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            <p>JES is the flagship journal of The Electrochemical Society. Published continuously from 1902 to the present, JES remains one of the most highly-cited journals in electrochemistry and solid-state science and technology.</p>
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Mark Wightman and Christian Amatore</option><option value="/collections/1945-7111_focus_issue_165_15_Y15">Focus Issue on Electrocatalysis – In Honor of Radoslav Adzic</option><option value="/collections/1945-7111_focus_issue_165_4_Y5">Focus Issue on Processes at the Semiconductor–Solution Interface</option><option value="/collections/1945-7111_focus_issue_165_6_Y7">Focus Issue on Proton Exchange Membrane Fuel Cell (PEMFC) Durability</option><option value="/collections/1945-7111_focus_issue_165_8_Y9">Focus Issue on Ubiquitous Sensors and Systems for IoT</option><option value="/collections/1945-7111_focus_issue_164_1_Y1">Focus Issue of Selected Papers from IMLB 2016 with Invited Papers Celebrating 25
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                    Open all abstracts<span class="offscreen-hidden">,&nbsp;in this tab</span></button></p><!--    articleEntryList start--><ul class="art-list"><li class="art-list-item reveal-container reveal-closed"><div class="eyebrow"><span class="offscreen-hidden">The following article is </span><span class="red">Open access</span></div><a href="/article/10.1149/2.0411609jes" class="art-list-item-title event_main-link">Calendar Aging of Lithium-Ion Batteries</a><p class="small art-list-item-meta">Peter Keil <em>et al</em> 2016 <em>J. Electrochem. Soc.</em> <b>163</b> A1872 </p><div class="art-list-item-tools small wd-abstr-upper"><a href="/article/10.1149/2.0411609jes/meta" class="mr-2 mb-0 nowrap event_mini-link" data-event-action="View article"><span class="icon-article"></span>View article<span class="offscreen-hidden">,&nbsp;Calendar Aging of Lithium-Ion Batteries</span></a><a href="/article/10.1149/2.0411609jes/pdf" class="mr-2 mb-0 nowrap event_mini-link" data-event-action="PDF"><span class="icon-file-pdf"></span>PDF<span class="offscreen-hidden">,&nbsp;Calendar Aging of Lithium-Ion Batteries</span></a><button type="button" class="reveal-trigger mr-2 nowrap"><svg aria-hidden="true" class="fa-icon fa-icon--left fa-icon--flip" role="img" focusable="false" xmlns="http://www.w3.org/2000/svg" viewBox="0 0 320 512"><!--caret-down--><!--!Font Awesome Free 6.5.1 by @fontawesome - https://fontawesome.com License - https://fontawesome.com/license/free Copyright 2024 Fonticons, Inc.--><path d="M137.4 374.6c12.5 12.5 32.8 12.5 45.3 0l128-128c9.2-9.2 11.9-22.9 6.9-34.9s-16.6-19.8-29.6-19.8L32 192c-12.9 0-24.6 7.8-29.6 19.8s-2.2 25.7 6.9 34.9l128 128z"/></svg><span class="reveal-trigger-label" data-reveal-text="Open abstract" data-reveal-label-alt="Close abstract" data-link-purpose-append="Calendar Aging of Lithium-Ion Batteries" data-link-purpose-append-open="Calendar Aging of Lithium-Ion Batteries">Open abstract</span></button></div><div class="reveal-content"><div class="article-text view-text-small"><p>In this study, the calendar aging of lithium-ion batteries is investigated at different temperatures for 16 states of charge (SoCs) from 0 to 100%. Three types of 18650 lithium-ion cells, containing different cathode materials, have been examined. Our study demonstrates that calendar aging does not increase steadily with the SoC. Instead, plateau regions, covering SoC intervals of more than 20%–30% of the cell capacity, are observed wherein the capacity fade is similar. Differential voltage analyses confirm that the capacity fade is mainly caused by a shift in the electrode balancing. Furthermore, our study reveals the high impact of the graphite electrode on calendar aging. Lower anode potentials, which aggravate electrolyte reduction and thus promote solid electrolyte interphase growth, have been identified as the main driver of capacity fade during storage. In the high SoC regime where the graphite anode is lithiated more than 50%, the low anode potential accelerates the loss of cyclable lithium, which in turn distorts the electrode balancing. Aging mechanisms induced by high cell potential, such as electrolyte oxidation or transition-metal dissolution, seem to play only a minor role. To maximize battery life, high storage SoCs corresponding to low anode potential should be avoided.</p></div><div class="art-list-item-tools small wd-abstr-lower"><a class="mr-2" href="https://doi.org/10.1149/2.0411609jes">https://doi.org/10.1149/2.0411609jes</a></div></div></li><li class="art-list-item reveal-container reveal-closed"><div class="eyebrow"><span class="offscreen-hidden">The following article is </span><span class="red">Open access</span></div><a href="/article/10.1149/1945-7111/abae37" class="art-list-item-title event_main-link">Degradation of Commercial Lithium-Ion Cells as a Function of Chemistry and Cycling Conditions</a><p class="small art-list-item-meta">Yuliya Preger <em>et al</em> 2020 <em>J. Electrochem. Soc.</em> <b>167</b> 120532 </p><div class="art-list-item-tools small wd-abstr-upper"><a href="/article/10.1149/1945-7111/abae37/meta" class="mr-2 mb-0 nowrap event_mini-link" data-event-action="View article"><span class="icon-article"></span>View article<span class="offscreen-hidden">,&nbsp;Degradation of Commercial Lithium-Ion Cells as a Function of Chemistry and Cycling Conditions</span></a><a href="/article/10.1149/1945-7111/abae37/pdf" class="mr-2 mb-0 nowrap event_mini-link" data-event-action="PDF"><span class="icon-file-pdf"></span>PDF<span class="offscreen-hidden">,&nbsp;Degradation of Commercial Lithium-Ion Cells as a Function of Chemistry and Cycling Conditions</span></a><button type="button" class="reveal-trigger mr-2 nowrap"><svg aria-hidden="true" class="fa-icon fa-icon--left fa-icon--flip" role="img" focusable="false" xmlns="http://www.w3.org/2000/svg" viewBox="0 0 320 512"><!--caret-down--><!--!Font Awesome Free 6.5.1 by @fontawesome - https://fontawesome.com License - https://fontawesome.com/license/free Copyright 2024 Fonticons, Inc.--><path d="M137.4 374.6c12.5 12.5 32.8 12.5 45.3 0l128-128c9.2-9.2 11.9-22.9 6.9-34.9s-16.6-19.8-29.6-19.8L32 192c-12.9 0-24.6 7.8-29.6 19.8s-2.2 25.7 6.9 34.9l128 128z"/></svg><span class="reveal-trigger-label" data-reveal-text="Open abstract" data-reveal-label-alt="Close abstract" data-link-purpose-append="Degradation of Commercial Lithium-Ion Cells as a Function of Chemistry and Cycling Conditions" data-link-purpose-append-open="Degradation of Commercial Lithium-Ion Cells as a Function of Chemistry and Cycling Conditions">Open abstract</span></button></div><div class="reveal-content"><div class="article-text view-text-small"><p>Energy storage systems with Li-ion batteries are increasingly deployed to maintain a robust and resilient grid and facilitate the integration of renewable energy resources. However, appropriate selection of cells for different applications is difficult due to limited public data comparing the most commonly used off-the-shelf Li-ion chemistries under the same operating conditions. This article details a multi-year cycling study of commercial LiFePO<sub>4</sub> (LFP), LiNi<sub>x</sub>Co<sub>y</sub>Al<sub>1−x−y</sub>O<sub>2</sub> (NCA), and LiNi<sub>x</sub>Mn<sub>y</sub>Co<sub>1−x−y</sub>O<sub>2</sub> (NMC) cells, varying the discharge rate, depth of discharge (DOD), and environment temperature. The capacity and discharge energy retention, as well as the round-trip efficiency, were compared. Even when operated within manufacturer specifications, the range of cycling conditions had a profound effect on cell degradation, with time to reach 80% capacity varying by thousands of hours and cycle counts among cells of each chemistry. The degradation of cells in this study was compared to that of similar cells in previous studies to identify universal trends and to provide a standard deviation for performance. All cycling files have been made publicly available at batteryarchive.org, a recently developed repository for visualization and comparison of battery data, to facilitate future experimental and modeling efforts.</p></div><div class="art-list-item-tools small wd-abstr-lower"><a class="mr-2" href="https://doi.org/10.1149/1945-7111/abae37">https://doi.org/10.1149/1945-7111/abae37</a></div></div></li><li class="art-list-item reveal-container reveal-closed"><div class="eyebrow"><span class="offscreen-hidden">The following article is </span><span class="red">Open access</span></div><a href="/article/10.1149/1945-7111/aea1c1" class="art-list-item-title event_main-link">Physics-Based Parameterization of a High-Power Silicon–Graphite Lithium-Ion Battery: Electrochemical Model of the Molicel P45B Cell</a><p class="small art-list-item-meta">Edmund J. F. Dickinson, <em>et al</em> 2026 <em>J. Electrochem. Soc.</em> <b>173</b> 190507 </p><div class="art-list-item-tools small wd-abstr-upper"><a href="/article/10.1149/1945-7111/aea1c1/meta" class="mr-2 mb-0 nowrap event_mini-link" data-event-action="View article"><span class="icon-article"></span>View article<span class="offscreen-hidden">,&nbsp;Physics-Based Parameterization of a High-Power Silicon–Graphite Lithium-Ion Battery: Electrochemical Model of the Molicel P45B Cell</span></a><a href="/article/10.1149/1945-7111/aea1c1/pdf" class="mr-2 mb-0 nowrap event_mini-link" data-event-action="PDF"><span class="icon-file-pdf"></span>PDF<span class="offscreen-hidden">,&nbsp;Physics-Based Parameterization of a High-Power Silicon–Graphite Lithium-Ion Battery: Electrochemical Model of the Molicel P45B Cell</span></a><button type="button" class="reveal-trigger mr-2 nowrap"><svg aria-hidden="true" class="fa-icon fa-icon--left fa-icon--flip" role="img" focusable="false" xmlns="http://www.w3.org/2000/svg" viewBox="0 0 320 512"><!--caret-down--><!--!Font Awesome Free 6.5.1 by @fontawesome - https://fontawesome.com License - https://fontawesome.com/license/free Copyright 2024 Fonticons, Inc.--><path d="M137.4 374.6c12.5 12.5 32.8 12.5 45.3 0l128-128c9.2-9.2 11.9-22.9 6.9-34.9s-16.6-19.8-29.6-19.8L32 192c-12.9 0-24.6 7.8-29.6 19.8s-2.2 25.7 6.9 34.9l128 128z"/></svg><span class="reveal-trigger-label" data-reveal-text="Open abstract" data-reveal-label-alt="Close abstract" data-link-purpose-append="Physics-Based Parameterization of a High-Power Silicon–Graphite Lithium-Ion Battery: Electrochemical Model of the Molicel P45B Cell" data-link-purpose-append-open="Physics-Based Parameterization of a High-Power Silicon–Graphite Lithium-Ion Battery: Electrochemical Model of the Molicel P45B Cell">Open abstract</span></button></div><div class="reveal-content"><div class="article-text view-text-small"><p>A comprehensive, teardown-led parameterization is developed for an electrochemical model of the Molicel P45B, a 4.5 Ah high-power lithium-ion cell with 21700 cylindrical form factor. Parameters are supplied in BPX JSON format, supporting Single Particle Model (SPM) and Doyle-Fuller-Newman (DFN) “Newman-style” models. In continuation of the authors’ previous dissemination of an equivalent circuit model (ECM) of the same cell, detailed insights into the cell’s internal design are presented and compared to prior studies; this includes cell overall design and bill-of-materials, electrode masses and dimensions, and active material morphology and chemistry. The negative electrode is a graphite–SiO<i><sub>x</sub></i> blend and, by contrast to legacy parameterization work, is described in the model using separately parameterized graphite and Si additive components which contribute in parallel to electrode charge capacity and current. Further, the Si-containing additive is described by an empirical, electrode-specific hysteresis model. Critical reported parameters utilize tuning for best predictive description of full cell voltage measurements, with comparison to values obtained from electrochemical measurements on harvested electrode samples from teardown. The parameterization is validated holistically using application-relevant pulse and continuous-current data, across the full operating envelope of temperature, state-of-charge, and operating current.</p><h2 id="artAbst2" class="collapse-blocked"></h2><p>
<span style="display: none;">figure placeholder</span>
</p><h2 id="artAbst3" class="collapse-blocked">Abstract</h2><p>
<ul><li><p>Open-source electrochemical parameter set for the Molicel P45B cell.</p></li><li><p>RMS voltage error &lt;25 mV for industry-specific validation (eVTOL, WLTP).</p></li><li><p>Resolved negative electrode blend: graphite and silicon-containing components.</p></li><li><p>Post-teardown characterization, comparing half-cell and full cell cycling data.</p></li><li><p>Simulations reproducible in PyBaMM with included Battery Parameter eXchange file.</p></li></ul></p></div><div class="art-list-item-tools small wd-abstr-lower"><a class="mr-2" href="https://doi.org/10.1149/1945-7111/aea1c1">https://doi.org/10.1149/1945-7111/aea1c1</a></div></div></li><li class="art-list-item reveal-container reveal-closed"><div class="eyebrow"><span class="offscreen-hidden">The following article is </span><span class="red">Open access</span></div><a href="/article/10.1149/1945-7111/ad6cbd" class="art-list-item-title event_main-link">The Operation Window of Lithium Iron Phosphate/Graphite Cells Affects their Lifetime</a><p class="small art-list-item-meta">Eniko S. Zsoldos <em>et al</em> 2024 <em>J. Electrochem. Soc.</em> <b>171</b> 080527 </p><div class="art-list-item-tools small wd-abstr-upper"><a href="/article/10.1149/1945-7111/ad6cbd/meta" class="mr-2 mb-0 nowrap event_mini-link" data-event-action="View article"><span class="icon-article"></span>View article<span class="offscreen-hidden">,&nbsp;The Operation Window of Lithium Iron Phosphate/Graphite Cells Affects their Lifetime</span></a><a href="/article/10.1149/1945-7111/ad6cbd/pdf" class="mr-2 mb-0 nowrap event_mini-link" data-event-action="PDF"><span class="icon-file-pdf"></span>PDF<span class="offscreen-hidden">,&nbsp;The Operation Window of Lithium Iron Phosphate/Graphite Cells Affects their Lifetime</span></a><button type="button" class="reveal-trigger mr-2 nowrap"><svg aria-hidden="true" class="fa-icon fa-icon--left fa-icon--flip" role="img" focusable="false" xmlns="http://www.w3.org/2000/svg" viewBox="0 0 320 512"><!--caret-down--><!--!Font Awesome Free 6.5.1 by @fontawesome - https://fontawesome.com License - https://fontawesome.com/license/free Copyright 2024 Fonticons, Inc.--><path d="M137.4 374.6c12.5 12.5 32.8 12.5 45.3 0l128-128c9.2-9.2 11.9-22.9 6.9-34.9s-16.6-19.8-29.6-19.8L32 192c-12.9 0-24.6 7.8-29.6 19.8s-2.2 25.7 6.9 34.9l128 128z"/></svg><span class="reveal-trigger-label" data-reveal-text="Open abstract" data-reveal-label-alt="Close abstract" data-link-purpose-append="The Operation Window of Lithium Iron Phosphate/Graphite Cells Affects their Lifetime" data-link-purpose-append-open="The Operation Window of Lithium Iron Phosphate/Graphite Cells Affects their Lifetime">Open abstract</span></button></div><div class="reveal-content"><div class="article-text view-text-small"><p>Lithium iron phosphate (LFP) battery cells are ubiquitous in electric vehicles and stationary energy storage because they are cheap and have a long lifetime. This work compares LFP/graphite pouch cells undergoing charge-discharge cycles over five state of charge (SOC) windows (0%–25%, 0%–60%, 0%–80%, 0%–100%, and 75%–100%). Cycling LFP cells across a lower average SOC results in less capacity fade than cycling across a higher average SOC, regardless of depth of discharge. The primary capacity fade mechanism is lithium inventory loss due to: lithiated graphite reactivity with electrolyte, which increases incrementally with SOC, and lithium alkoxide species causing iron dissolution and deposition on the negative electrode at high SOC which further accelerates lithium inventory loss. Our results show that even low voltage LFP systems (3.65 V) have a tradeoff between average SOC and lifetime. Operating LFP cells at lower average SOC can extend their lifetime substantially in both EV and grid storage applications.</p></div><div class="art-list-item-tools small wd-abstr-lower"><a class="mr-2" href="https://doi.org/10.1149/1945-7111/ad6cbd">https://doi.org/10.1149/1945-7111/ad6cbd</a></div></div></li><li class="art-list-item reveal-container reveal-closed"><div class="eyebrow"><span class="offscreen-hidden">The following article is </span><span class="red">Open access</span></div><a href="/article/10.1149/1945-7111/ab9050" class="art-list-item-title event_main-link">Development of Experimental Techniques for Parameterization of Multi-scale Lithium-ion Battery Models</a><p class="small art-list-item-meta">Chang-Hui Chen <em>et al</em> 2020 <em>J. Electrochem. Soc.</em> <b>167</b> 080534 </p><div class="art-list-item-tools small wd-abstr-upper"><a href="/article/10.1149/1945-7111/ab9050/meta" class="mr-2 mb-0 nowrap event_mini-link" data-event-action="View article"><span class="icon-article"></span>View article<span class="offscreen-hidden">,&nbsp;Development of Experimental Techniques for Parameterization of Multi-scale Lithium-ion Battery Models</span></a><a href="/article/10.1149/1945-7111/ab9050/pdf" class="mr-2 mb-0 nowrap event_mini-link" data-event-action="PDF"><span class="icon-file-pdf"></span>PDF<span class="offscreen-hidden">,&nbsp;Development of Experimental Techniques for Parameterization of Multi-scale Lithium-ion Battery Models</span></a><button type="button" class="reveal-trigger mr-2 nowrap"><svg aria-hidden="true" class="fa-icon fa-icon--left fa-icon--flip" role="img" focusable="false" xmlns="http://www.w3.org/2000/svg" viewBox="0 0 320 512"><!--caret-down--><!--!Font Awesome Free 6.5.1 by @fontawesome - https://fontawesome.com License - https://fontawesome.com/license/free Copyright 2024 Fonticons, Inc.--><path d="M137.4 374.6c12.5 12.5 32.8 12.5 45.3 0l128-128c9.2-9.2 11.9-22.9 6.9-34.9s-16.6-19.8-29.6-19.8L32 192c-12.9 0-24.6 7.8-29.6 19.8s-2.2 25.7 6.9 34.9l128 128z"/></svg><span class="reveal-trigger-label" data-reveal-text="Open abstract" data-reveal-label-alt="Close abstract" data-link-purpose-append="Development of Experimental Techniques for Parameterization of Multi-scale Lithium-ion Battery Models" data-link-purpose-append-open="Development of Experimental Techniques for Parameterization of Multi-scale Lithium-ion Battery Models">Open abstract</span></button></div><div class="reveal-content"><div class="article-text view-text-small"><p>Presented here, is an extensive 35 parameter experimental data set of a cylindrical 21700 commercial cell (LGM50), for an electrochemical pseudo-two-dimensional (P2D) model. The experimental methodologies for tear-down and subsequent chemical, physical, electrochemical kinetics and thermodynamic analysis, and their accuracy and validity are discussed. Chemical analysis of the LGM50 cell shows that it is comprised of a NMC 811 positive electrode and bi-component Graphite-SiO<sub>x</sub> negative electrode. The thermodynamic open circuit voltages (OCV) and lithium stoichiometry in the electrode are obtained using galvanostatic intermittent titration technique (GITT) in half cell and three-electrode full cell configurations. The activation energy and exchange current coefficient through electrochemical impedance spectroscopy (EIS) measurements. Apparent diffusion coefficients are estimated using the Sand equation on the voltage transient during the current pulse; an expansion factor was applied to the bi-component negative electrode data to reflect the average change in effective surface area during lithiation. The 35 parameters are applied within a P2D model to show the fit to experimental validation LGM50 cell discharge and relaxation voltage profiles at room temperature. The accuracy and validity of the processes and the techniques in the determination of these parameters are discussed, including opportunities for further modelling and data analysis improvements.</p></div><div class="art-list-item-tools small wd-abstr-lower"><a class="mr-2" href="https://doi.org/10.1149/1945-7111/ab9050">https://doi.org/10.1149/1945-7111/ab9050</a></div></div></li><li class="art-list-item reveal-container reveal-closed"><div class="eyebrow"><span class="offscreen-hidden">The following article is </span><span class="red">Open access</span></div><a href="/article/10.1149/1945-7111/ad14d0" class="art-list-item-title event_main-link">Lithium-Ion Cells in Automotive Applications: Tesla 4680 Cylindrical Cell Teardown and Characterization</a><p class="small art-list-item-meta">Manuel Ank <em>et al</em> 2023 <em>J. Electrochem. Soc.</em> <b>170</b> 120536 </p><div class="art-list-item-tools small wd-abstr-upper"><a href="/article/10.1149/1945-7111/ad14d0/meta" class="mr-2 mb-0 nowrap event_mini-link" data-event-action="View article"><span class="icon-article"></span>View article<span class="offscreen-hidden">,&nbsp;Lithium-Ion Cells in Automotive Applications: Tesla 4680 Cylindrical Cell Teardown and Characterization</span></a><a href="/article/10.1149/1945-7111/ad14d0/pdf" class="mr-2 mb-0 nowrap event_mini-link" data-event-action="PDF"><span class="icon-file-pdf"></span>PDF<span class="offscreen-hidden">,&nbsp;Lithium-Ion Cells in Automotive Applications: Tesla 4680 Cylindrical Cell Teardown and Characterization</span></a><button type="button" class="reveal-trigger mr-2 nowrap"><svg aria-hidden="true" class="fa-icon fa-icon--left fa-icon--flip" role="img" focusable="false" xmlns="http://www.w3.org/2000/svg" viewBox="0 0 320 512"><!--caret-down--><!--!Font Awesome Free 6.5.1 by @fontawesome - https://fontawesome.com License - https://fontawesome.com/license/free Copyright 2024 Fonticons, Inc.--><path d="M137.4 374.6c12.5 12.5 32.8 12.5 45.3 0l128-128c9.2-9.2 11.9-22.9 6.9-34.9s-16.6-19.8-29.6-19.8L32 192c-12.9 0-24.6 7.8-29.6 19.8s-2.2 25.7 6.9 34.9l128 128z"/></svg><span class="reveal-trigger-label" data-reveal-text="Open abstract" data-reveal-label-alt="Close abstract" data-link-purpose-append="Lithium-Ion Cells in Automotive Applications: Tesla 4680 Cylindrical Cell Teardown and Characterization" data-link-purpose-append-open="Lithium-Ion Cells in Automotive Applications: Tesla 4680 Cylindrical Cell Teardown and Characterization">Open abstract</span></button></div><div class="reveal-content"><div class="article-text view-text-small"><p>Battery research depends upon up-to-date information on the cell characteristics found in current electric vehicles, which is exacerbated by the deployment of novel formats and architectures. This necessitates open access to cell characterization data. Therefore, this study examines the architecture and performance of first-generation Tesla 4680 cells in detail, both by electrical characterization and thermal investigations at cell-level and by disassembling one cell down to the material level including a three-electrode analysis. The cell teardown reveals the complex cell architecture with electrode disks of hexagonal symmetry as well as an electrode winding consisting of a double-sided and homogeneously coated cathode and anode, two separators and no mandrel. A solvent-free anode fabrication and coating process can be derived. Energy-dispersive X-ray spectroscopy as well as differential voltage, incremental capacity and three-electrode analysis confirm a NMC811 cathode and a pure graphite anode without silicon. On cell-level, energy densities of 622.4 Wh/L and 232.5 Wh/kg were determined while characteristic state-of-charge dependencies regarding resistance and impedance behavior are revealed using hybrid pulse power characterization and electrochemical impedance spectroscopy. A comparatively high surface temperature of ∼70 °C is observed when charging at 2C without active cooling. All measurement data of this characterization study are provided as open source.</p></div><div class="art-list-item-tools small wd-abstr-lower"><a class="mr-2" href="https://doi.org/10.1149/1945-7111/ad14d0">https://doi.org/10.1149/1945-7111/ad14d0</a></div></div></li><li class="art-list-item reveal-container reveal-closed"><a href="/article/10.1149/1.2113792" class="art-list-item-title event_main-link">A General Energy Balance for Battery Systems</a><p class="small art-list-item-meta">D. Bernardi <em>et al</em> 1985 <em>J. Electrochem. Soc.</em> <b>132</b> 5 </p><div class="art-list-item-tools small wd-abstr-upper"><a href="/article/10.1149/1.2113792/meta" class="mr-2 mb-0 nowrap event_mini-link" data-event-action="View article"><span class="icon-article"></span>View article<span class="offscreen-hidden">,&nbsp;A General Energy Balance for Battery Systems</span></a><a href="/article/10.1149/1.2113792/pdf" class="mr-2 mb-0 nowrap event_mini-link" data-event-action="PDF"><span class="icon-file-pdf"></span>PDF<span class="offscreen-hidden">,&nbsp;A General Energy Balance for Battery Systems</span></a><button type="button" class="reveal-trigger mr-2 nowrap"><svg aria-hidden="true" class="fa-icon fa-icon--left fa-icon--flip" role="img" focusable="false" xmlns="http://www.w3.org/2000/svg" viewBox="0 0 320 512"><!--caret-down--><!--!Font Awesome Free 6.5.1 by @fontawesome - https://fontawesome.com License - https://fontawesome.com/license/free Copyright 2024 Fonticons, Inc.--><path d="M137.4 374.6c12.5 12.5 32.8 12.5 45.3 0l128-128c9.2-9.2 11.9-22.9 6.9-34.9s-16.6-19.8-29.6-19.8L32 192c-12.9 0-24.6 7.8-29.6 19.8s-2.2 25.7 6.9 34.9l128 128z"/></svg><span class="reveal-trigger-label" data-reveal-text="Open abstract" data-reveal-label-alt="Close abstract" data-link-purpose-append="A General Energy Balance for Battery Systems" data-link-purpose-append-open="A General Energy Balance for Battery Systems">Open abstract</span></button></div><div class="reveal-content"><div class="article-text view-text-small"><p>A general energy balance for battery systems has been developed. This equation is useful for estimating cell thermal characteristics. Reliable predictions of cell temperature and heat‐generation rate are required for the design and thermal management of battery systems. The temperature of a cell changes as a result of electrochemical reactions, phase changes, mixing effects, and joule heating. The equation developed incorporates these effects in a complete and general manner. Simplifications and special cases are discussed. The results of applying the energy balance to a mathematical model of the <span xmlns:xlink="http://www.w3.org/1999/xlink" class="inline-eqn"><span class="mml"><span class="texImage"><img src="data:image/png;base64,iVBORw0KGgoAAAANSUhEUgAAAAEAAAABCAQAAAC1HAwCAAAAC0lEQVR42mNkYAAAAAYAAjCB0C8AAAAASUVORK5CYII=" data-src="https://content.cld.iop.org/journals/1945-7111/132/1/5/revision1/jes_132_1_5ieqn1.jpg" style="max-width: 100%;" alt="Equation or symbol description not available" align="top" role="math"></img></span><math xmlns="http://www.w3.org/1998/Math/MathML"><mi>LiAl</mi><mo>/</mo><mi>FeS</mi></math></span></span> cell discharged through two different reaction mechanisms are given as examples. The examples illustrate how the energy equation may be applied to a specific system to examine the relative contributions corresponding to the terms in the equation. The examples show that the processes involved in cell heat generation may be complex and that the application of a sufficiently general energy equation is advantageous.</p></div><div class="art-list-item-tools small wd-abstr-lower"><a class="mr-2" href="https://doi.org/10.1149/1.2113792">https://doi.org/10.1149/1.2113792</a></div></div></li><li class="art-list-item reveal-container reveal-closed"><a href="/article/10.1149/1.1837571" class="art-list-item-title event_main-link">Phospho‐olivines as Positive‐Electrode Materials for Rechargeable Lithium Batteries</a><p class="small art-list-item-meta">A. K. Padhi <em>et al</em> 1997 <em>J. Electrochem. Soc.</em> <b>144</b> 1188 </p><div class="art-list-item-tools small wd-abstr-upper"><a href="/article/10.1149/1.1837571/meta" class="mr-2 mb-0 nowrap event_mini-link" data-event-action="View article"><span class="icon-article"></span>View article<span class="offscreen-hidden">,&nbsp;Phospho‐olivines as Positive‐Electrode Materials for Rechargeable Lithium Batteries</span></a><a href="/article/10.1149/1.1837571/pdf" class="mr-2 mb-0 nowrap event_mini-link" data-event-action="PDF"><span class="icon-file-pdf"></span>PDF<span class="offscreen-hidden">,&nbsp;Phospho‐olivines as Positive‐Electrode Materials for Rechargeable Lithium Batteries</span></a><button type="button" class="reveal-trigger mr-2 nowrap"><svg aria-hidden="true" class="fa-icon fa-icon--left fa-icon--flip" role="img" focusable="false" xmlns="http://www.w3.org/2000/svg" viewBox="0 0 320 512"><!--caret-down--><!--!Font Awesome Free 6.5.1 by @fontawesome - https://fontawesome.com License - https://fontawesome.com/license/free Copyright 2024 Fonticons, Inc.--><path d="M137.4 374.6c12.5 12.5 32.8 12.5 45.3 0l128-128c9.2-9.2 11.9-22.9 6.9-34.9s-16.6-19.8-29.6-19.8L32 192c-12.9 0-24.6 7.8-29.6 19.8s-2.2 25.7 6.9 34.9l128 128z"/></svg><span class="reveal-trigger-label" data-reveal-text="Open abstract" data-reveal-label-alt="Close abstract" data-link-purpose-append="Phospho‐olivines as Positive‐Electrode Materials for Rechargeable Lithium Batteries" data-link-purpose-append-open="Phospho‐olivines as Positive‐Electrode Materials for Rechargeable Lithium Batteries">Open abstract</span></button></div><div class="reveal-content"><div class="article-text view-text-small"><p>Reversible extraction of lithium from <span xmlns:xlink="http://www.w3.org/1999/xlink" class="inline-eqn"><span class="mml"><span class="texImage"><img src="data:image/png;base64,iVBORw0KGgoAAAANSUhEUgAAAAEAAAABCAQAAAC1HAwCAAAAC0lEQVR42mNkYAAAAAYAAjCB0C8AAAAASUVORK5CYII=" data-src="https://content.cld.iop.org/journals/1945-7111/144/4/1188/revision1/jes_144_4_1188ieqn1.jpg" style="max-width: 100%;" alt="Equation or symbol description not available" align="top" role="math"></img></span><math xmlns="http://www.w3.org/1998/Math/MathML"><msub><mi>LiFePO</mi><mrow><mn>4</mn></mrow></msub></math></span></span> (triphylite) and insertion of lithium into <span xmlns:xlink="http://www.w3.org/1999/xlink" class="inline-eqn"><span class="mml"><span class="texImage"><img src="data:image/png;base64,iVBORw0KGgoAAAANSUhEUgAAAAEAAAABCAQAAAC1HAwCAAAAC0lEQVR42mNkYAAAAAYAAjCB0C8AAAAASUVORK5CYII=" data-src="https://content.cld.iop.org/journals/1945-7111/144/4/1188/revision1/jes_144_4_1188ieqn2.jpg" style="max-width: 100%;" alt="Equation or symbol description not available" align="top" role="math"></img></span><math xmlns="http://www.w3.org/1998/Math/MathML"><msub><mi>FePO</mi><mrow><mn>4</mn></mrow></msub></math></span></span> at 3.5 V <i>vs.</i> lithium at 0.05 mA/cm<sup>2</sup> shows this material to be an excellent candidate for the cathode of a low‐power, rechargeable lithium battery that is inexpensive, nontoxic, and environmentally benign. Electrochemical extraction was limited to ∼0.6 Li/formula unit; but even with this restriction the specific capacity is 100 to 110 mAh/g. Complete extraction of lithium was performed chemically; it gave a new phase, <span xmlns:xlink="http://www.w3.org/1999/xlink" class="inline-eqn"><span class="mml"><span class="texImage"><img src="data:image/png;base64,iVBORw0KGgoAAAANSUhEUgAAAAEAAAABCAQAAAC1HAwCAAAAC0lEQVR42mNkYAAAAAYAAjCB0C8AAAAASUVORK5CYII=" data-src="https://content.cld.iop.org/journals/1945-7111/144/4/1188/revision1/jes_144_4_1188ieqn3.jpg" style="max-width: 100%;" alt="Equation or symbol description not available" align="top" role="math"></img></span><math xmlns="http://www.w3.org/1998/Math/MathML"><msub><mi>FePO</mi><mrow><mn>4</mn></mrow></msub></math></span></span>, isostructural with heterosite, <span xmlns:xlink="http://www.w3.org/1999/xlink" class="inline-eqn"><span class="mml"><span class="texImage"><img src="data:image/png;base64,iVBORw0KGgoAAAANSUhEUgAAAAEAAAABCAQAAAC1HAwCAAAAC0lEQVR42mNkYAAAAAYAAjCB0C8AAAAASUVORK5CYII=" data-src="https://content.cld.iop.org/journals/1945-7111/144/4/1188/revision1/jes_144_4_1188ieqn4.jpg" style="max-width: 100%;" alt="Equation or symbol description not available" align="top" role="math"></img></span><math xmlns="http://www.w3.org/1998/Math/MathML"><msub><mi>Fe</mi><mrow><mn>0.65</mn></mrow></msub><msub><mi>Mn</mi><mrow><mn>0.35</mn></mrow></msub><msub><mo>PO</mo><mrow><mn>4</mn></mrow></msub></math></span></span>. The <span xmlns:xlink="http://www.w3.org/1999/xlink" class="inline-eqn"><span class="mml"><span class="texImage"><img src="data:image/png;base64,iVBORw0KGgoAAAANSUhEUgAAAAEAAAABCAQAAAC1HAwCAAAAC0lEQVR42mNkYAAAAAYAAjCB0C8AAAAASUVORK5CYII=" data-src="https://content.cld.iop.org/journals/1945-7111/144/4/1188/revision1/jes_144_4_1188ieqn5.jpg" style="max-width: 100%;" alt="Equation or symbol description not available" align="top" role="math"></img></span><math xmlns="http://www.w3.org/1998/Math/MathML"><msub><mi>FePO</mi><mrow><mn>4</mn></mrow></msub></math></span></span> framework of the ordered olivine <span xmlns:xlink="http://www.w3.org/1999/xlink" class="inline-eqn"><span class="mml"><span class="texImage"><img src="data:image/png;base64,iVBORw0KGgoAAAANSUhEUgAAAAEAAAABCAQAAAC1HAwCAAAAC0lEQVR42mNkYAAAAAYAAjCB0C8AAAAASUVORK5CYII=" data-src="https://content.cld.iop.org/journals/1945-7111/144/4/1188/revision1/jes_144_4_1188ieqn6.jpg" style="max-width: 100%;" alt="Equation or symbol description not available" align="top" role="math"></img></span><math xmlns="http://www.w3.org/1998/Math/MathML"><msub><mi>LiFePO</mi><mrow><mn>4</mn></mrow></msub></math></span></span> is retained with minor displacive adjustments. Nevertheless the insertion/extraction reaction proceeds via a two‐phase process, and a reversible loss in capacity with increasing current density appears to be associated with a diffusion‐limited transfer of lithium across the two‐phase interface. Electrochemical extraction of lithium from isostructural <span xmlns:xlink="http://www.w3.org/1999/xlink" class="inline-eqn"><span class="mml"><span class="texImage"><img src="data:image/png;base64,iVBORw0KGgoAAAANSUhEUgAAAAEAAAABCAQAAAC1HAwCAAAAC0lEQVR42mNkYAAAAAYAAjCB0C8AAAAASUVORK5CYII=" data-src="https://content.cld.iop.org/journals/1945-7111/144/4/1188/revision1/jes_144_4_1188ieqn7.jpg" style="max-width: 100%;" alt="Equation or symbol description not available" align="top" role="math"></img></span><math xmlns="http://www.w3.org/1998/Math/MathML"><msub><mi>LiMPO</mi><mrow><mn>4</mn></mrow></msub></math></span></span> (M = Mn, Co, or Ni) with an <span xmlns:xlink="http://www.w3.org/1999/xlink" class="inline-eqn"><span class="mml"><span class="texImage"><img src="data:image/png;base64,iVBORw0KGgoAAAANSUhEUgAAAAEAAAABCAQAAAC1HAwCAAAAC0lEQVR42mNkYAAAAAYAAjCB0C8AAAAASUVORK5CYII=" data-src="https://content.cld.iop.org/journals/1945-7111/144/4/1188/revision1/jes_144_4_1188ieqn8.jpg" style="max-width: 100%;" alt="Equation or symbol description not available" align="top" role="math"></img></span><math xmlns="http://www.w3.org/1998/Math/MathML"><msub><mi>LiClO</mi><mrow><mn>4</mn></mrow></msub></math></span></span> electrolyte was not possible; but successful extraction of lithium from <span xmlns:xlink="http://www.w3.org/1999/xlink" class="inline-eqn"><span class="mml"><span class="texImage"><img src="data:image/png;base64,iVBORw0KGgoAAAANSUhEUgAAAAEAAAABCAQAAAC1HAwCAAAAC0lEQVR42mNkYAAAAAYAAjCB0C8AAAAASUVORK5CYII=" data-src="https://content.cld.iop.org/journals/1945-7111/144/4/1188/revision1/jes_144_4_1188ieqn9.jpg" style="max-width: 100%;" alt="Equation or symbol description not available" align="top" role="math"></img></span><math xmlns="http://www.w3.org/1998/Math/MathML"><msub><mi>LiFe</mi><mrow><mn>1</mn><mo>−</mo><mi>x</mi></mrow></msub><msub><mi>Mn</mi><mrow><mi>x</mi></mrow></msub><msub><mo>PO</mo><mrow><mn>4</mn></mrow></msub></math></span></span> was accomplished with maximum oxidation of the <span xmlns:xlink="http://www.w3.org/1999/xlink" class="inline-eqn"><span class="mml"><span class="texImage"><img src="data:image/png;base64,iVBORw0KGgoAAAANSUhEUgAAAAEAAAABCAQAAAC1HAwCAAAAC0lEQVR42mNkYAAAAAYAAjCB0C8AAAAASUVORK5CYII=" data-src="https://content.cld.iop.org/journals/1945-7111/144/4/1188/revision1/jes_144_4_1188ieqn10.jpg" style="max-width: 100%;" alt="Equation or symbol description not available" align="top" role="math"></img></span><math xmlns="http://www.w3.org/1998/Math/MathML"><msup><mi>Mn</mi><mrow><mn>3</mn><mo>+</mo></mrow></msup><mo>/</mo><msup><mi>Mn</mi><mrow><mn>2</mn><mo>+</mo></mrow></msup></math></span></span> occurring at <i>x</i> = 0.5. The <span xmlns:xlink="http://www.w3.org/1999/xlink" class="inline-eqn"><span class="mml"><span class="texImage"><img src="data:image/png;base64,iVBORw0KGgoAAAANSUhEUgAAAAEAAAABCAQAAAC1HAwCAAAAC0lEQVR42mNkYAAAAAYAAjCB0C8AAAAASUVORK5CYII=" data-src="https://content.cld.iop.org/journals/1945-7111/144/4/1188/revision1/jes_144_4_1188ieqn11.jpg" style="max-width: 100%;" alt="Equation or symbol description not available" align="top" role="math"></img></span><math xmlns="http://www.w3.org/1998/Math/MathML"><msup><mi>Fe</mi><mrow><mn>3</mn><mo>+</mo></mrow></msup><mo>/</mo><msup><mi>Fe</mi><mrow><mn>2</mn><mo>+</mo></mrow></msup></math></span></span> couple was oxidized first at 3.5 V followed by oxidation of the <span xmlns:xlink="http://www.w3.org/1999/xlink" class="inline-eqn"><span class="mml"><span class="texImage"><img src="data:image/png;base64,iVBORw0KGgoAAAANSUhEUgAAAAEAAAABCAQAAAC1HAwCAAAAC0lEQVR42mNkYAAAAAYAAjCB0C8AAAAASUVORK5CYII=" data-src="https://content.cld.iop.org/journals/1945-7111/144/4/1188/revision1/jes_144_4_1188ieqn12.jpg" style="max-width: 100%;" alt="Equation or symbol description not available" align="top" role="math"></img></span><math xmlns="http://www.w3.org/1998/Math/MathML"><msup><mi>Mn</mi><mrow><mn>3</mn><mo>+</mo></mrow></msup><mo>/</mo><msup><mi>Mn</mi><mrow><mn>2</mn><mo>+</mo></mrow></msup></math></span></span> couple at 4.1 V <i>vs.</i> lithium. The <span xmlns:xlink="http://www.w3.org/1999/xlink" class="inline-eqn"><span class="mml"><span class="texImage"><img src="data:image/png;base64,iVBORw0KGgoAAAANSUhEUgAAAAEAAAABCAQAAAC1HAwCAAAAC0lEQVR42mNkYAAAAAYAAjCB0C8AAAAASUVORK5CYII=" data-src="https://content.cld.iop.org/journals/1945-7111/144/4/1188/revision1/jes_144_4_1188ieqn13.jpg" style="max-width: 100%;" alt="Equation or symbol description not available" align="top" role="math"></img></span><math xmlns="http://www.w3.org/1998/Math/MathML"><msup><mi>Fe</mi><mrow><mn>3</mn><mo>+</mo></mrow></msup><mo>‐</mo><mo>O</mo><mo>‐</mo><msup><mi>Mn</mi><mrow><mn>2</mn><mo>+</mo></mrow></msup></math></span></span> interactions appear to destabilize the <span xmlns:xlink="http://www.w3.org/1999/xlink" class="inline-eqn"><span class="mml"><span class="texImage"><img src="data:image/png;base64,iVBORw0KGgoAAAANSUhEUgAAAAEAAAABCAQAAAC1HAwCAAAAC0lEQVR42mNkYAAAAAYAAjCB0C8AAAAASUVORK5CYII=" data-src="https://content.cld.iop.org/journals/1945-7111/144/4/1188/revision1/jes_144_4_1188ieqn14.jpg" style="max-width: 100%;" alt="Equation or symbol description not available" align="top" role="math"></img></span><math xmlns="http://www.w3.org/1998/Math/MathML"><msup><mi>Mn</mi><mrow><mn>2</mn><mo>+</mo></mrow></msup></math></span></span> level and stabilize the <span xmlns:xlink="http://www.w3.org/1999/xlink" class="inline-eqn"><span class="mml"><span class="texImage"><img src="data:image/png;base64,iVBORw0KGgoAAAANSUhEUgAAAAEAAAABCAQAAAC1HAwCAAAAC0lEQVR42mNkYAAAAAYAAjCB0C8AAAAASUVORK5CYII=" data-src="https://content.cld.iop.org/journals/1945-7111/144/4/1188/revision1/jes_144_4_1188ieqn15.jpg" style="max-width: 100%;" alt="Equation or symbol description not available" align="top" role="math"></img></span><math xmlns="http://www.w3.org/1998/Math/MathML"><msup><mi>Fe</mi><mrow><mn>3</mn><mo>+</mo></mrow></msup></math></span></span> level so as to make the <span xmlns:xlink="http://www.w3.org/1999/xlink" class="inline-eqn"><span class="mml"><span class="texImage"><img src="data:image/png;base64,iVBORw0KGgoAAAANSUhEUgAAAAEAAAABCAQAAAC1HAwCAAAAC0lEQVR42mNkYAAAAAYAAjCB0C8AAAAASUVORK5CYII=" data-src="https://content.cld.iop.org/journals/1945-7111/144/4/1188/revision1/jes_144_4_1188ieqn16.jpg" style="max-width: 100%;" alt="Equation or symbol description not available" align="top" role="math"></img></span><math xmlns="http://www.w3.org/1998/Math/MathML"><msup><mi>Mn</mi><mrow><mn>3</mn><mo>+</mo></mrow></msup><mo>/</mo><msup><mi>Mn</mi><mrow><mn>2</mn><mo>+</mo></mrow></msup></math></span></span> energy accessible.</p></div><div class="art-list-item-tools small wd-abstr-lower"><a class="mr-2" href="https://doi.org/10.1149/1.1837571">https://doi.org/10.1149/1.1837571</a></div></div></li><li class="art-list-item reveal-container reveal-closed"><div class="eyebrow"><span class="offscreen-hidden">The following article is </span><span class="red">Open access</span></div><a href="/article/10.1149/1945-7111/ac6d13" class="art-list-item-title event_main-link">Review—“Knees” in Lithium-Ion Battery Aging Trajectories</a><p class="small art-list-item-meta">Peter M. Attia <em>et al</em> 2022 <em>J. Electrochem. Soc.</em> <b>169</b> 060517 </p><div class="art-list-item-tools small wd-abstr-upper"><a href="/article/10.1149/1945-7111/ac6d13/meta" class="mr-2 mb-0 nowrap event_mini-link" data-event-action="View article"><span class="icon-article"></span>View article<span class="offscreen-hidden">,&nbsp;Review—“Knees” in Lithium-Ion Battery Aging Trajectories</span></a><a href="/article/10.1149/1945-7111/ac6d13/pdf" class="mr-2 mb-0 nowrap event_mini-link" data-event-action="PDF"><span class="icon-file-pdf"></span>PDF<span class="offscreen-hidden">,&nbsp;Review—“Knees” in Lithium-Ion Battery Aging Trajectories</span></a><button type="button" class="reveal-trigger mr-2 nowrap"><svg aria-hidden="true" class="fa-icon fa-icon--left fa-icon--flip" role="img" focusable="false" xmlns="http://www.w3.org/2000/svg" viewBox="0 0 320 512"><!--caret-down--><!--!Font Awesome Free 6.5.1 by @fontawesome - https://fontawesome.com License - https://fontawesome.com/license/free Copyright 2024 Fonticons, Inc.--><path d="M137.4 374.6c12.5 12.5 32.8 12.5 45.3 0l128-128c9.2-9.2 11.9-22.9 6.9-34.9s-16.6-19.8-29.6-19.8L32 192c-12.9 0-24.6 7.8-29.6 19.8s-2.2 25.7 6.9 34.9l128 128z"/></svg><span class="reveal-trigger-label" data-reveal-text="Open abstract" data-reveal-label-alt="Close abstract" data-link-purpose-append="Review—“Knees” in Lithium-Ion Battery Aging Trajectories" data-link-purpose-append-open="Review—“Knees” in Lithium-Ion Battery Aging Trajectories">Open abstract</span></button></div><div class="reveal-content"><div class="article-text view-text-small"><p>Lithium-ion batteries can last many years but sometimes exhibit rapid, nonlinear degradation that severely limits battery lifetime. In this work, we review prior work on “knees” in lithium-ion battery aging trajectories. We first review definitions for knees and three classes of “internal state trajectories” (termed snowball, hidden, and threshold trajectories) that can cause a knee. We then discuss six knee “pathways”, including lithium plating, electrode saturation, resistance growth, electrolyte and additive depletion, percolation-limited connectivity, and mechanical deformation—some of which have internal state trajectories with signals that are electrochemically undetectable. We also identify key design and usage sensitivities for knees. Finally, we discuss challenges and opportunities for knee modeling and prediction. Our findings illustrate the complexity and subtlety of lithium-ion battery degradation and can aid both academic and industrial efforts to improve battery lifetime.</p></div><div class="art-list-item-tools small wd-abstr-lower"><a class="mr-2" href="https://doi.org/10.1149/1945-7111/ac6d13">https://doi.org/10.1149/1945-7111/ac6d13</a></div></div></li><li class="art-list-item reveal-container reveal-closed"><a href="/article/10.1149/1.2085971" class="art-list-item-title event_main-link">Polymer Electrolyte Fuel Cell Model</a><p class="small art-list-item-meta">T. E. Springer <em>et al</em> 1991 <em>J. Electrochem. Soc.</em> <b>138</b> 2334 </p><div class="art-list-item-tools small wd-abstr-upper"><a href="/article/10.1149/1.2085971/meta" class="mr-2 mb-0 nowrap event_mini-link" data-event-action="View article"><span class="icon-article"></span>View article<span class="offscreen-hidden">,&nbsp;Polymer Electrolyte Fuel Cell Model</span></a><a href="/article/10.1149/1.2085971/pdf" class="mr-2 mb-0 nowrap event_mini-link" data-event-action="PDF"><span class="icon-file-pdf"></span>PDF<span class="offscreen-hidden">,&nbsp;Polymer Electrolyte Fuel Cell Model</span></a><button type="button" class="reveal-trigger mr-2 nowrap"><svg aria-hidden="true" class="fa-icon fa-icon--left fa-icon--flip" role="img" focusable="false" xmlns="http://www.w3.org/2000/svg" viewBox="0 0 320 512"><!--caret-down--><!--!Font Awesome Free 6.5.1 by @fontawesome - https://fontawesome.com License - https://fontawesome.com/license/free Copyright 2024 Fonticons, Inc.--><path d="M137.4 374.6c12.5 12.5 32.8 12.5 45.3 0l128-128c9.2-9.2 11.9-22.9 6.9-34.9s-16.6-19.8-29.6-19.8L32 192c-12.9 0-24.6 7.8-29.6 19.8s-2.2 25.7 6.9 34.9l128 128z"/></svg><span class="reveal-trigger-label" data-reveal-text="Open abstract" data-reveal-label-alt="Close abstract" data-link-purpose-append="Polymer Electrolyte Fuel Cell Model" data-link-purpose-append-open="Polymer Electrolyte Fuel Cell Model">Open abstract</span></button></div><div class="reveal-content"><div class="article-text view-text-small"><p>We present here an isothermal, one‐dimensional, steady‐state model for a complete polymer electrolyte fuel cell (PEFC) with a 117 Nafion® membrane. In this model we employ water diffusion coefficients electro‐osmotic drag coefficients, water sorption isotherms, and membrane conductivities, all measured in our laboratory as functions of membrane water content. The model predicts a net‐water‐per‐proton flux ratio of 0.2 <span xmlns:xlink="http://www.w3.org/1999/xlink" class="inline-eqn"><span class="mml"><span class="texImage"><img src="data:image/png;base64,iVBORw0KGgoAAAANSUhEUgAAAAEAAAABCAQAAAC1HAwCAAAAC0lEQVR42mNkYAAAAAYAAjCB0C8AAAAASUVORK5CYII=" data-src="https://content.cld.iop.org/journals/1945-7111/138/8/2334/revision1/jes_138_8_2334ieqn1.jpg" style="max-width: 100%;" alt="Equation or symbol description not available" align="top" role="math"></img></span><math xmlns="http://www.w3.org/1998/Math/MathML"><msub><mo>H</mo><mrow><mn>2</mn></mrow></msub><mo>O</mo><mo>/</mo><msup><mo>H</mo><mrow><mo>+</mo></mrow></msup></math></span></span> under typical operating conditions, which is much less than the measured electro‐osmotic drag coefficient for a fully hydrated membrane. It also predicts an increase in membrane resistance with increased current density and demonstrates the great advantage of a thinner membrane in alleviating this resistance problem. Both of these predictions were verified experimentally under certain conditions.</p></div><div class="art-list-item-tools small wd-abstr-lower"><a class="mr-2" href="https://doi.org/10.1149/1.2085971">https://doi.org/10.1149/1.2085971</a></div></div></li></ul><!--    articleEntryList end--></div></div></div><!-- End Most read tabpanel --><!-- Start Latest tabpanel --><div tabindex="0"
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                    Open all abstracts<span class="offscreen-hidden">,&nbsp;in this tab</span></button></p><!--    articleEntryList start--><ul class="art-list"><li class="art-list-item reveal-container reveal-closed"><div class="eyebrow"><span class="offscreen-hidden">The following article is </span><span class="red">Open access</span></div><a href="/article/10.1149/1945-7111/aeab15" class="art-list-item-title event_main-link">In Situ and Operando Neutron Powder Diffraction of Na<i><sub>x</sub></i>NiO<sub>2</sub>: A Case Study for Sodium-Ion Batteries</a><p class="small art-list-item-meta">James M. A. Steele <em>et al</em> 2026 <em>J. Electrochem. Soc.</em> <b>173</b> 200513 </p><div class="art-list-item-tools small wd-abstr-upper"><a href="/article/10.1149/1945-7111/aeab15/meta" class="mr-2 mb-0 nowrap event_mini-link" data-event-action="View article"><span class="icon-article"></span>View article<span class="offscreen-hidden">,&nbsp;In Situ and Operando Neutron Powder Diffraction of NaxNiO2: A Case Study for Sodium-Ion Batteries</span></a><a href="/article/10.1149/1945-7111/aeab15/pdf" class="mr-2 mb-0 nowrap event_mini-link" data-event-action="PDF"><span class="icon-file-pdf"></span>PDF<span class="offscreen-hidden">,&nbsp;In Situ and Operando Neutron Powder Diffraction of NaxNiO2: A Case Study for Sodium-Ion Batteries</span></a><button type="button" class="reveal-trigger mr-2 nowrap"><svg aria-hidden="true" class="fa-icon fa-icon--left fa-icon--flip" role="img" focusable="false" xmlns="http://www.w3.org/2000/svg" viewBox="0 0 320 512"><!--caret-down--><!--!Font Awesome Free 6.5.1 by @fontawesome - https://fontawesome.com License - https://fontawesome.com/license/free Copyright 2024 Fonticons, Inc.--><path d="M137.4 374.6c12.5 12.5 32.8 12.5 45.3 0l128-128c9.2-9.2 11.9-22.9 6.9-34.9s-16.6-19.8-29.6-19.8L32 192c-12.9 0-24.6 7.8-29.6 19.8s-2.2 25.7 6.9 34.9l128 128z"/></svg><span class="reveal-trigger-label" data-reveal-text="Open abstract" data-reveal-label-alt="Close abstract" data-link-purpose-append="In Situ and Operando Neutron Powder Diffraction of NaxNiO2: A Case Study for Sodium-Ion Batteries" data-link-purpose-append-open="In Situ and Operando Neutron Powder Diffraction of NaxNiO2: A Case Study for Sodium-Ion Batteries">Open abstract</span></button></div><div class="reveal-content"><div class="article-text view-text-small"><p>Neutron powder diffraction (NPD) is a non-destructive technique uniquely suited to investigating industrially relevant sodium-ion cathode materials. Unlike X–ray diffraction, it offers excellent contrast between neighbouring transition metal ions and is sensitive to lighter elements such as O/Na, which are key to revealing superstructural orderings characteristic of sodium cathodes. However, in situ/operando NPD battery studies are hindered by sample quantity requirements, and lack of suitable sample environments. Using a cell developed at ISIS Neutron and Muon Source, we observed no detrimental effects from prolonged vacuum exposure required for Time-of-Flight NPD. We collect/analyse data in two modes: operando<i>,</i> in which the electrochemical structural evolution is tracked, and in situ, wherein higher signal-to-noise data is collected during voltage holds, for phase-pure samples at set voltage cutoffs. Using Na<sub><i>x</i></sub>NiO<sub>2</sub> as a model system, we present a methodology to account for the complex background profile characteristic of electrochemical environments enabling, for the first time, quantitative Rietveld refinements against in situ electrochemical NPD, and providing a systematic framework for future studies. Structural models are refined against in situ data and benchmarked against combined refinement of ex situ SXRD/NPD measurements. This work unlocks potential for previously inaccessible insights into structure-property relationships and degradation, helping to facilitate the development of next-generation cathodes with enhanced useful lifetime, capacity, and performance.</p><h2 id="artAbst2" class="collapse-blocked"></h2><p><span style="display: none;">figure placeholder</span></p><h2 id="artAbst3" class="collapse-blocked">Highlights</h2><p><ul><li><p>Case study for neutron diffraction on battery cathode materials during operation</p></li><li><p>Complex electrochemical cell background accounted for via post-cycling measurement</p></li><li><p>Quantitative Rietveld refinement provided insight into structural phase transitions</p></li></ul></p></div><div class="art-list-item-tools small wd-abstr-lower"><a class="mr-2" href="https://doi.org/10.1149/1945-7111/aeab15">https://doi.org/10.1149/1945-7111/aeab15</a></div></div></li><li class="art-list-item reveal-container reveal-closed"><a href="/article/10.1149/1945-7111/aeaf86" class="art-list-item-title event_main-link">Successful Scale-Up of Solid Oxide Cell Manufacturing through Multilayer Water-Based Pre-Industrial Tape Casting</a><p class="small art-list-item-meta">Violeta Ureña-Torres <em>et al</em> 2026 <em>J. Electrochem. Soc.</em> <b>173</b> 204505 </p><div class="art-list-item-tools small wd-abstr-upper"><a href="/article/10.1149/1945-7111/aeaf86/meta" class="mr-2 mb-0 nowrap event_mini-link" data-event-action="View article"><span class="icon-article"></span>View article<span class="offscreen-hidden">,&nbsp;Successful Scale-Up of Solid Oxide Cell Manufacturing through Multilayer Water-Based Pre-Industrial Tape Casting</span></a><a href="/article/10.1149/1945-7111/aeaf86/pdf" class="mr-2 mb-0 nowrap event_mini-link" data-event-action="PDF"><span class="icon-file-pdf"></span>PDF<span class="offscreen-hidden">,&nbsp;Successful Scale-Up of Solid Oxide Cell Manufacturing through Multilayer Water-Based Pre-Industrial Tape Casting</span></a><button type="button" class="reveal-trigger mr-2 nowrap"><svg aria-hidden="true" class="fa-icon fa-icon--left fa-icon--flip" role="img" focusable="false" xmlns="http://www.w3.org/2000/svg" viewBox="0 0 320 512"><!--caret-down--><!--!Font Awesome Free 6.5.1 by @fontawesome - https://fontawesome.com License - https://fontawesome.com/license/free Copyright 2024 Fonticons, Inc.--><path d="M137.4 374.6c12.5 12.5 32.8 12.5 45.3 0l128-128c9.2-9.2 11.9-22.9 6.9-34.9s-16.6-19.8-29.6-19.8L32 192c-12.9 0-24.6 7.8-29.6 19.8s-2.2 25.7 6.9 34.9l128 128z"/></svg><span class="reveal-trigger-label" data-reveal-text="Open abstract" data-reveal-label-alt="Close abstract" data-link-purpose-append="Successful Scale-Up of Solid Oxide Cell Manufacturing through Multilayer Water-Based Pre-Industrial Tape Casting" data-link-purpose-append-open="Successful Scale-Up of Solid Oxide Cell Manufacturing through Multilayer Water-Based Pre-Industrial Tape Casting">Open abstract</span></button></div><div class="reveal-content"><div class="article-text view-text-small"><p>The scale-up of solid oxide cells (SOCs) manufacturing is critical for its industrial implementation. However, it presents significant challenges, including obtaining defect-free, dimensionally uniform layers and reproducible microstructure, controlling slurry properties, and minimizing resource consumption and waste generation. This work details the successful transition of a half-cell fabrication route (Ni-YSZ/YSZ) from laboratory scale to a pre-industrial roll-to-roll system, representing one of the first demonstrations of water-based multilayer casting at this scale. The scale-up was performed using water-based slurries as a feasible alternative to conventional organic-based systems, by carefully adjusting both slurry preparation and deposition parameters (i.e. gap, casting speed and drying temperature). While implementing pre-industrial fabrication, reduced slurry viscosity, sample reproducibility and appropriate microstructure were observed, resulting in maintained electrochemical performance (0.38 ± 0.02 and 0.42 ± 0.04 W cm<sup>−2</sup>, using LSM-YSZ oxygen electrode). In addition, the optimized multilayer deposition resulted in fivefold increase in production capacity, from ∼ 30 to &gt; 150 half-cells per week, as well as cost-efficient material utilization (from 3.5 to 0.7 € material cost per half-cell). These findings demonstrate the feasibility of high-throughput water-based SOCs manufacturing by a more sustainable process and offer a pathway toward the cost-effective production of next-generation energy technologies.</p><h2 id="artAbst2" class="collapse-blocked"></h2><p><span style="display: none;">figure placeholder</span></p><h2 id="artAbst3" class="collapse-blocked">Highlights</h2><p><ul><li><p>Pre-industrial scale solid oxide half-cells fabricated via roll-to-roll tape casting</p></li><li><p>Water-based multilayer processing enables sustainable and scalable manufacturing</p></li><li><p>Defect-free, uniform tapes with enhanced microstructural homogeneity were obtained</p></li><li><p>Reduced polarization resistance and sustained power density at pre-industrial scale</p></li><li><p>Fivefold increase in production capacity with significant material cost reduction</p></li></ul></p></div><div class="art-list-item-tools small wd-abstr-lower"><a class="mr-2" href="https://doi.org/10.1149/1945-7111/aeaf86">https://doi.org/10.1149/1945-7111/aeaf86</a></div></div></li><li class="art-list-item reveal-container reveal-closed"><a href="/article/10.1149/1945-7111/aeadd5" class="art-list-item-title event_main-link">Evaporation-Regulated Direct Ink Writing of Porous Composite Separators for High-Performance Lithium-Ion Batteries</a><p class="small art-list-item-meta">Jiacun Lu <em>et al</em> 2026 <em>J. Electrochem. Soc.</em> <b>173</b> 200512 </p><div class="art-list-item-tools small wd-abstr-upper"><a href="/article/10.1149/1945-7111/aeadd5/meta" class="mr-2 mb-0 nowrap event_mini-link" data-event-action="View article"><span class="icon-article"></span>View article<span class="offscreen-hidden">,&nbsp;Evaporation-Regulated Direct Ink Writing of Porous Composite Separators for High-Performance Lithium-Ion Batteries</span></a><a href="/article/10.1149/1945-7111/aeadd5/pdf" class="mr-2 mb-0 nowrap event_mini-link" data-event-action="PDF"><span class="icon-file-pdf"></span>PDF<span class="offscreen-hidden">,&nbsp;Evaporation-Regulated Direct Ink Writing of Porous Composite Separators for High-Performance Lithium-Ion Batteries</span></a><button type="button" class="reveal-trigger mr-2 nowrap"><svg aria-hidden="true" class="fa-icon fa-icon--left fa-icon--flip" role="img" focusable="false" xmlns="http://www.w3.org/2000/svg" viewBox="0 0 320 512"><!--caret-down--><!--!Font Awesome Free 6.5.1 by @fontawesome - https://fontawesome.com License - https://fontawesome.com/license/free Copyright 2024 Fonticons, Inc.--><path d="M137.4 374.6c12.5 12.5 32.8 12.5 45.3 0l128-128c9.2-9.2 11.9-22.9 6.9-34.9s-16.6-19.8-29.6-19.8L32 192c-12.9 0-24.6 7.8-29.6 19.8s-2.2 25.7 6.9 34.9l128 128z"/></svg><span class="reveal-trigger-label" data-reveal-text="Open abstract" data-reveal-label-alt="Close abstract" data-link-purpose-append="Evaporation-Regulated Direct Ink Writing of Porous Composite Separators for High-Performance Lithium-Ion Batteries" data-link-purpose-append-open="Evaporation-Regulated Direct Ink Writing of Porous Composite Separators for High-Performance Lithium-Ion Batteries">Open abstract</span></button></div><div class="reveal-content"><div class="article-text view-text-small"><p>Commercial polyolefin separators exhibit limited electrolyte wettability and thermal dimensional stability, while conventional fabrication methods provide limited control over pore structure. Herein, direct ink writing (DIW) was coupled with evaporation-induced phase separation to fabricate porous PVDF-HFP/Al<sub>2</sub>O<sub>3</sub> composite separators for liquid-electrolyte lithium-ion batteries. The shear-thinning, predominantly elastic ink enabled stable extrusion and shape retention. Compared with doctor-bladed DB-PA prepared using the same composition and drying conditions, DIW promoted an interconnected sponge-like pore network through multidirectional DMF evaporation and limited ingress of atmospheric moisture. Printing speed governed separator morphology and electrochemical performance. The optimized PA-8 separator, printed at 8 mm s<sup>−1</sup>, achieved a porosity of 65.37%, electrolyte uptake of 203.94%, ionic conductivity of 1.38 mS cm<sup>−1</sup>, and lithium-ion transference number of 0.82. It retained 62.33% of its original area after treatment at 180 °C. LiFePO<sub>4</sub>||Li cells using PA-8 delivered 120.52 mAh g<sup>−1</sup> at 5 C and retained 95.41% capacity after 200 cycles at 1 C, outperforming Celgard 2500 (106.60 mAh g<sup>−1</sup> and 87.63%, respectively). These results demonstrate that DIW-assisted phase separation enables controllable porous separators with improved electrolyte affinity, ion transport, thermal stability, and cell performance.</p><h2 id="artAbst2" class="collapse-blocked"></h2><p><span style="display: none;">figure placeholder</span></p></div><div class="art-list-item-tools small wd-abstr-lower"><a class="mr-2" href="https://doi.org/10.1149/1945-7111/aeadd5">https://doi.org/10.1149/1945-7111/aeadd5</a></div></div></li><li class="art-list-item reveal-container reveal-closed"><a href="/article/10.1149/1945-7111/aeb164" class="art-list-item-title event_main-link">Fluorine-Reduced Hückel Anions Electrolytes in Lithium–Sulfur Batteries with Novel UIO-66-NH<sub>2</sub>—Modified Cathodes</a><p class="small art-list-item-meta">Maciej Smoliński <em>et al</em> 2026 <em>J. Electrochem. Soc.</em> <b>173</b> 200511 </p><div class="art-list-item-tools small wd-abstr-upper"><a href="/article/10.1149/1945-7111/aeb164/meta" class="mr-2 mb-0 nowrap event_mini-link" data-event-action="View article"><span class="icon-article"></span>View article<span class="offscreen-hidden">,&nbsp;Fluorine-Reduced Hückel Anions Electrolytes in Lithium–Sulfur Batteries with Novel UIO-66-NH2—Modified Cathodes</span></a><a href="/article/10.1149/1945-7111/aeb164/pdf" class="mr-2 mb-0 nowrap event_mini-link" data-event-action="PDF"><span class="icon-file-pdf"></span>PDF<span class="offscreen-hidden">,&nbsp;Fluorine-Reduced Hückel Anions Electrolytes in Lithium–Sulfur Batteries with Novel UIO-66-NH2—Modified Cathodes</span></a><button type="button" class="reveal-trigger mr-2 nowrap"><svg aria-hidden="true" class="fa-icon fa-icon--left fa-icon--flip" role="img" focusable="false" xmlns="http://www.w3.org/2000/svg" viewBox="0 0 320 512"><!--caret-down--><!--!Font Awesome Free 6.5.1 by @fontawesome - https://fontawesome.com License - https://fontawesome.com/license/free Copyright 2024 Fonticons, Inc.--><path d="M137.4 374.6c12.5 12.5 32.8 12.5 45.3 0l128-128c9.2-9.2 11.9-22.9 6.9-34.9s-16.6-19.8-29.6-19.8L32 192c-12.9 0-24.6 7.8-29.6 19.8s-2.2 25.7 6.9 34.9l128 128z"/></svg><span class="reveal-trigger-label" data-reveal-text="Open abstract" data-reveal-label-alt="Close abstract" data-link-purpose-append="Fluorine-Reduced Hückel Anions Electrolytes in Lithium–Sulfur Batteries with Novel UIO-66-NH2—Modified Cathodes" data-link-purpose-append-open="Fluorine-Reduced Hückel Anions Electrolytes in Lithium–Sulfur Batteries with Novel UIO-66-NH2—Modified Cathodes">Open abstract</span></button></div><div class="reveal-content"><div class="article-text view-text-small"><p>Lithium–sulfur (Li–S) batteries are considered a promising alternative to lithium-ion cells; however, their implementation remains limited by several challenges. This research investigates two key strategies for improving Li–S batteries: 1) cathode engineering through the application of a novel modified UIO-66-NH<sub>2</sub> metal organic framework (MOF) in order to enhance the electrochemical performance by introducing a framework structure; the development of entirely fluorine-free cathodes fabricated by a dry processing method using water as the only solvent; and 2) electrolyte optimization using novel Hückel anion-based lithium salts, including fluorine-free structures. Optimization of the cathode composition—supported by electrochemical evaluation of MOF impact, sulfur loading, E/S ratio, and conductive additives—enabled the identification of the best-performing cathode configuration. In the second part of the study, the new electrolyte salts were evaluated. All four Hückel salts—lithium 4,5-dicyano-2-(trifluoromethyl)imidazolide (LiTDI), lithium 4,5-dicyano-2-(pentafluoroethyl)imidazolide (LiPDI), lithium 4,5-dicyano-2-(n-heptafluoropropyl)imidazolide (LiHDI), and lithium 2,4,5-tricyanoimidazolide (LiTIM)—outperformed the reference salt LiTFSI in most cases. The results demonstrate that MOF-based cathodes enhance sulfur utilization and cycling stability compared with previously reported carbon-sulfur cathodes (capacities higher up to 235.5%), while Hückel anion electrolytes affect polysulfide shuttle reactions relative to the benchmark LiTFSI-based electrolyte and improve coulombic efficiency. The combined application of both strategies yields performance improvements than either modification alone. This work establishes a design framework linking cathode architecture with electrolyte composition, resulting in advanced Li–S battery systems with reduced fluorine content.</p><h2 id="artAbst2" class="collapse-blocked"></h2><p><span style="display: none;">figure placeholder</span></p></div><div class="art-list-item-tools small wd-abstr-lower"><a class="mr-2" href="https://doi.org/10.1149/1945-7111/aeb164">https://doi.org/10.1149/1945-7111/aeb164</a></div></div></li><li class="art-list-item reveal-container reveal-closed"><a href="/article/10.1149/1945-7111/aeb336" class="art-list-item-title event_main-link">In Situ High-Speed AFM Observation of Long-Term Cu Electrodeposition</a><p class="small art-list-item-meta">Yen Chieh Cheng <em>et al</em> 2026 <em>J. Electrochem. Soc.</em> <b>173</b> 202503 </p><div class="art-list-item-tools small wd-abstr-upper"><a href="/article/10.1149/1945-7111/aeb336/meta" class="mr-2 mb-0 nowrap event_mini-link" data-event-action="View article"><span class="icon-article"></span>View article<span class="offscreen-hidden">,&nbsp;In Situ High-Speed AFM Observation of Long-Term Cu Electrodeposition</span></a><a href="/article/10.1149/1945-7111/aeb336/pdf" class="mr-2 mb-0 nowrap event_mini-link" data-event-action="PDF"><span class="icon-file-pdf"></span>PDF<span class="offscreen-hidden">,&nbsp;In Situ High-Speed AFM Observation of Long-Term Cu Electrodeposition</span></a><button type="button" class="reveal-trigger mr-2 nowrap"><svg aria-hidden="true" class="fa-icon fa-icon--left fa-icon--flip" role="img" focusable="false" xmlns="http://www.w3.org/2000/svg" viewBox="0 0 320 512"><!--caret-down--><!--!Font Awesome Free 6.5.1 by @fontawesome - https://fontawesome.com License - https://fontawesome.com/license/free Copyright 2024 Fonticons, Inc.--><path d="M137.4 374.6c12.5 12.5 32.8 12.5 45.3 0l128-128c9.2-9.2 11.9-22.9 6.9-34.9s-16.6-19.8-29.6-19.8L32 192c-12.9 0-24.6 7.8-29.6 19.8s-2.2 25.7 6.9 34.9l128 128z"/></svg><span class="reveal-trigger-label" data-reveal-text="Open abstract" data-reveal-label-alt="Close abstract" data-link-purpose-append="In Situ High-Speed AFM Observation of Long-Term Cu Electrodeposition" data-link-purpose-append-open="In Situ High-Speed AFM Observation of Long-Term Cu Electrodeposition">Open abstract</span></button></div><div class="reveal-content"><div class="article-text view-text-small"><p>Understanding how electrodeposition morphology evolves during nonequilibrium growth is essential for clarifying anomalous kinetic roughening, yet this relationship remains difficult to establish because most previous studies rely on ex situ measurements. Here, in situ high-speed atomic force microscopy (HS-AFM) was combined with dynamic scaling analysis to track the long-term evolution of Cu electrodeposition on highly oriented pyrolytic graphite and correlate real-space morphology with multiscale surface roughening. The applied cathodic potential systematically governed deposit evolution. At −0.6 V, relatively isolated deposits persisted, whereas denser deposits developed at −0.7 V. At −0.8 V, continued vertical growth was accompanied by second-layer formation and the development of coarse three-dimensional deposits with pronounced height contrast. Dynamic scaling analysis at −0.8 V revealed anomalous roughening, characterized by persistent time-dependent local surface width, distinct temporal evolution at local and larger lateral length scales, and rapid expansion of laterally correlated structures. These results directly link nanoscale deposit evolution with anomalous roughening during Cu electrodeposition and demonstrate that cathodic potential effectively regulates both morphology and roughening dynamics. The combination of operando HS-AFM and dynamic scaling provides a useful framework for investigating nonequilibrium electrochemical growth.</p><h2 id="artAbst2" class="collapse-blocked"></h2><p><span style="display: none;">figure placeholder</span></p></div><div class="art-list-item-tools small wd-abstr-lower"><a class="mr-2" href="https://doi.org/10.1149/1945-7111/aeb336">https://doi.org/10.1149/1945-7111/aeb336</a></div></div></li></ul><!--    articleEntryList end--></div></div></div><!-- End Latest tabpanel --><!-- Express Letters tabpanel --><!-- Express Letters tabpanel --><!-- Start Review tabpanel --><div tabindex="0"
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                    Open all abstracts<span class="offscreen-hidden">,&nbsp;in this tab</span></button></p><!--    articleEntryList start--><ul class="art-list"><li class="art-list-item reveal-container reveal-closed"><a href="/article/10.1149/1945-7111/aead2e" class="art-list-item-title event_main-link">Effect of Fabrication Parameters and Modification Strategies on the Performance of PbO<sub>2</sub> Anode: A Review</a><p class="small art-list-item-meta">Md. Mahboob Alam and Asok Adak 2026 <em>J. Electrochem. Soc.</em> <b>173</b> 193502 </p><div class="art-list-item-tools small wd-abstr-upper"><a href="/article/10.1149/1945-7111/aead2e/meta" class="mr-2 mb-0 nowrap event_mini-link" data-event-action="View article"><span class="icon-article"></span>View article<span class="offscreen-hidden">,&nbsp;Effect of Fabrication Parameters and Modification Strategies on the Performance of PbO2 Anode: A Review</span></a><a href="/article/10.1149/1945-7111/aead2e/pdf" class="mr-2 mb-0 nowrap event_mini-link" data-event-action="PDF"><span class="icon-file-pdf"></span>PDF<span class="offscreen-hidden">,&nbsp;Effect of Fabrication Parameters and Modification Strategies on the Performance of PbO2 Anode: A Review</span></a><button type="button" class="reveal-trigger mr-2 nowrap"><svg aria-hidden="true" class="fa-icon fa-icon--left fa-icon--flip" role="img" focusable="false" xmlns="http://www.w3.org/2000/svg" viewBox="0 0 320 512"><!--caret-down--><!--!Font Awesome Free 6.5.1 by @fontawesome - https://fontawesome.com License - https://fontawesome.com/license/free Copyright 2024 Fonticons, Inc.--><path d="M137.4 374.6c12.5 12.5 32.8 12.5 45.3 0l128-128c9.2-9.2 11.9-22.9 6.9-34.9s-16.6-19.8-29.6-19.8L32 192c-12.9 0-24.6 7.8-29.6 19.8s-2.2 25.7 6.9 34.9l128 128z"/></svg><span class="reveal-trigger-label" data-reveal-text="Open abstract" data-reveal-label-alt="Close abstract" data-link-purpose-append="Effect of Fabrication Parameters and Modification Strategies on the Performance of PbO2 Anode: A Review" data-link-purpose-append-open="Effect of Fabrication Parameters and Modification Strategies on the Performance of PbO2 Anode: A Review">Open abstract</span></button></div><div class="reveal-content"><div class="article-text view-text-small"><p>Lead dioxide (PbO<sub>2</sub>) has been used to treat organic pollutants in wastewater because of its high oxidation efficiency, high oxidation potential, and good corrosion resistance. The performance of the PbO<sub>2</sub> anode depends on its morphological, crystallographic, and electrochemical properties, which are influenced by the fabrication parameters, such as current density, Pb<sup>2+</sup> concentration, time, and temperature. This review presents a comprehensive discussion on the influence of these fabrication parameters on properties of the PbO<sub>2</sub> anode, including crystallite size, surface morphology, coating thickness, phase composition, crystal orientation, electrochemically active surface area, charge-transfer behavior, and oxygen evolution potential. Interlayer modification and active-layer doping have improved coating compactness, electron-transfer kinetics, reactive oxygen species generation, and pollutant mineralization efficiency of the PbO<sub>2</sub> anode. Hydroxyl radicals have been the dominant oxidizing species in the electrochemical oxidation system. Sulfate radicals provided an additional oxidation pathway in persulfate and peroxymonosulfate-assisted systems. During prolonged operation, lead leakage, reduced lifetime, and changes in properties have been found to degrade the anode’s overall performance. Thus, this work presents a comprehensive understanding of how fabrication parameters influence PbO<sub>2</sub> anode performance and offers valuable insights into the design of highly efficient and stable electrodes for advanced electrochemical wastewater treatment applications.</p><h2 id="artAbst2" class="collapse-blocked"></h2><p><span style="display: none;">figure placeholder</span></p><h2 id="artAbst3" class="collapse-blocked">Highlights</h2><p><ul><li><p>Fabrication parameters control PbO<sub>2</sub> morphology, crystallinity, and electrochemistry</p></li><li><p>Current density controls crystal growth, OEP, and electrochemical activity</p></li><li><p>Interlayer engineering improves adhesion, electron transfer, and anode lifetime</p></li><li><p>Active-layer doping enhances OEP, ROS generation, and pollutant degradation</p></li><li><p>Lead leakage and coating deterioration remain key barriers to long-term stability</p></li></ul></p></div><div class="art-list-item-tools small wd-abstr-lower"><a class="mr-2" href="https://doi.org/10.1149/1945-7111/aead2e">https://doi.org/10.1149/1945-7111/aead2e</a></div></div></li><li class="art-list-item reveal-container reveal-closed"><a href="/article/10.1149/1945-7111/aea1c0" class="art-list-item-title event_main-link">Data-Driven Advances in Electrochemical Energy and Sensing: Artificial Intelligence Approaches from Concept to Application</a><p class="small art-list-item-meta">Sourav Ghosh and Barkha Rani 2026 <em>J. Electrochem. Soc.</em> <b>173</b> 183502 </p><div class="art-list-item-tools small wd-abstr-upper"><a href="/article/10.1149/1945-7111/aea1c0/meta" class="mr-2 mb-0 nowrap event_mini-link" data-event-action="View article"><span class="icon-article"></span>View article<span class="offscreen-hidden">,&nbsp;Data-Driven Advances in Electrochemical Energy and Sensing: Artificial Intelligence Approaches from Concept to Application</span></a><a href="/article/10.1149/1945-7111/aea1c0/pdf" class="mr-2 mb-0 nowrap event_mini-link" data-event-action="PDF"><span class="icon-file-pdf"></span>PDF<span class="offscreen-hidden">,&nbsp;Data-Driven Advances in Electrochemical Energy and Sensing: Artificial Intelligence Approaches from Concept to Application</span></a><button type="button" class="reveal-trigger mr-2 nowrap"><svg aria-hidden="true" class="fa-icon fa-icon--left fa-icon--flip" role="img" focusable="false" xmlns="http://www.w3.org/2000/svg" viewBox="0 0 320 512"><!--caret-down--><!--!Font Awesome Free 6.5.1 by @fontawesome - https://fontawesome.com License - https://fontawesome.com/license/free Copyright 2024 Fonticons, Inc.--><path d="M137.4 374.6c12.5 12.5 32.8 12.5 45.3 0l128-128c9.2-9.2 11.9-22.9 6.9-34.9s-16.6-19.8-29.6-19.8L32 192c-12.9 0-24.6 7.8-29.6 19.8s-2.2 25.7 6.9 34.9l128 128z"/></svg><span class="reveal-trigger-label" data-reveal-text="Open abstract" data-reveal-label-alt="Close abstract" data-link-purpose-append="Data-Driven Advances in Electrochemical Energy and Sensing: Artificial Intelligence Approaches from Concept to Application" data-link-purpose-append-open="Data-Driven Advances in Electrochemical Energy and Sensing: Artificial Intelligence Approaches from Concept to Application">Open abstract</span></button></div><div class="reveal-content"><div class="article-text view-text-small"><p>The intersection of machine learning (ML) and electrochemical research is catalyzing transformative advancements in energy storage and conversion technologies. This review critically examines the role of ML and deep learning (DL) in optimizing electrochemical systems, focusing on batteries, supercapacitors, fuel cells, and sensors. ML-driven approaches facilitate accelerated material discovery, precise property predictions, and enhanced device performance monitoring, surpassing conventional trial-and-error methodologies. Integrating computational materials science, including density functional theory (DFT) and molecular dynamics (MD), with ML enables predictive modeling of electrochemical processes at an unprecedented scale. However, challenges such as data heterogeneity, model interpretability, and computational cost continue to limit widespread adoption. This review identifies key strategies to overcome these barriers, including establishing standardized data repositories, developing hybrid physics-informed ML models, and implementing explainable AI (XAI) for enhanced model transparency. By addressing these challenges, ML has the potential to drive the next wave of breakthroughs in electrochemical energy storage and conversion, accelerating the transition toward a sustainable and energy-secure future.</p><h2 id="artAbst2" class="collapse-blocked"></h2><p><span style="display: none;">figure placeholder</span></p></div><div class="art-list-item-tools small wd-abstr-lower"><a class="mr-2" href="https://doi.org/10.1149/1945-7111/aea1c0">https://doi.org/10.1149/1945-7111/aea1c0</a></div></div></li><li class="art-list-item reveal-container reveal-closed"><a href="/article/10.1149/1945-7111/ae9c71" class="art-list-item-title event_main-link">Mass Transport and Transmembrane Electric Potential in Multi-Ionic Systems: From Entropy and Nernst–Planck to Hodgkin–Huxley</a><p class="small art-list-item-meta">Nikolai M. Kocherginsky 2026 <em>J. Electrochem. Soc.</em> <b>173</b> 176503 </p><div class="art-list-item-tools small wd-abstr-upper"><a href="/article/10.1149/1945-7111/ae9c71/meta" class="mr-2 mb-0 nowrap event_mini-link" data-event-action="View article"><span class="icon-article"></span>View article<span class="offscreen-hidden">,&nbsp;Mass Transport and Transmembrane Electric Potential in Multi-Ionic Systems: From Entropy and Nernst–Planck to Hodgkin–Huxley</span></a><a href="/article/10.1149/1945-7111/ae9c71/pdf" class="mr-2 mb-0 nowrap event_mini-link" data-event-action="PDF"><span class="icon-file-pdf"></span>PDF<span class="offscreen-hidden">,&nbsp;Mass Transport and Transmembrane Electric Potential in Multi-Ionic Systems: From Entropy and Nernst–Planck to Hodgkin–Huxley</span></a><button type="button" class="reveal-trigger mr-2 nowrap"><svg aria-hidden="true" class="fa-icon fa-icon--left fa-icon--flip" role="img" focusable="false" xmlns="http://www.w3.org/2000/svg" viewBox="0 0 320 512"><!--caret-down--><!--!Font Awesome Free 6.5.1 by @fontawesome - https://fontawesome.com License - https://fontawesome.com/license/free Copyright 2024 Fonticons, Inc.--><path d="M137.4 374.6c12.5 12.5 32.8 12.5 45.3 0l128-128c9.2-9.2 11.9-22.9 6.9-34.9s-16.6-19.8-29.6-19.8L32 192c-12.9 0-24.6 7.8-29.6 19.8s-2.2 25.7 6.9 34.9l128 128z"/></svg><span class="reveal-trigger-label" data-reveal-text="Open abstract" data-reveal-label-alt="Close abstract" data-link-purpose-append="Mass Transport and Transmembrane Electric Potential in Multi-Ionic Systems: From Entropy and Nernst–Planck to Hodgkin–Huxley" data-link-purpose-append-open="Mass Transport and Transmembrane Electric Potential in Multi-Ionic Systems: From Entropy and Nernst–Planck to Hodgkin–Huxley">Open abstract</span></button></div><div class="reveal-content"><div class="article-text view-text-small"><p>A new equation for transmembrane electric potential for a system of several ions with different charges is suggested. This potential is determined by a system of Nernst–Planck equations for each of ions simultaneously. We explain why the experimental slope of <span xmlns:xlink="http://www.w3.org/1999/xlink" class="inline-eqn"><span class="tex"><span class="texImage"><img src="data:image/png;base64,iVBORw0KGgoAAAANSUhEUgAAAAEAAAABCAQAAAC1HAwCAAAAC0lEQVR42mNkYAAAAAYAAjCB0C8AAAAASUVORK5CYII=" data-src="https://content.cld.iop.org/journals/1945-7111/173/17/176503/revision2/jesae9c71ieqn1.gif" style="max-width: 100%;" alt="${\psi _{\text{e}}} = f(\ln {c_i})$" align="top" role="math"></img></span><script type="math/tex">{\psi _{\text{e}}} = f(\ln {c_i})</script></span></span> may change from <span xmlns:xlink="http://www.w3.org/1999/xlink" class="inline-eqn"><span class="tex"><span class="texImage"><img src="data:image/png;base64,iVBORw0KGgoAAAANSUhEUgAAAAEAAAABCAQAAAC1HAwCAAAAC0lEQVR42mNkYAAAAAYAAjCB0C8AAAAASUVORK5CYII=" data-src="https://content.cld.iop.org/journals/1945-7111/173/17/176503/revision2/jesae9c71ieqn2.gif" style="max-width: 100%;" alt="$2RT/F$" align="top" role="math"></img></span><script type="math/tex">2RT/F</script></span></span> to 0 and even change its sign for multicomponent systems, and a more general equation is given. Ohm’s law for partial electric current of each ion is not valid anymore. Problems with the semi-empirical Nikolsky–Eisenman equation for experiments with solid membranes and multivalent ions disappear. This equation may be used for solutions with Ca<sup>2+</sup>and other multicharged ions. Moreover, Cl<sup>−</sup> concentrations in the donor and acceptor solutions change their places in the nominator and denominator of final equation. At zero total current a gradient of one ion concentration may lead to coupled co- or counter-transport of another ion in a membrane, leading to both electrogenic and electrically silent transport. Instead of Hodgkin–Huxley a new model is suggested to describe mutual influence of transported K<sup>+</sup> and Na<sup>+</sup> ions, important in explanation of an action potential. Previously, in N.M. Kocherginsky <i>Physicochemical Mechanics with Applications in Physics, Chemistry, Membranology and Biology</i>, p. 376 Cambridge University Press, (2024), electrochemical electrode reactions and Butler–Volmer equation, multi component diffusion, thermodiffusion, and also surface tension-related phenomena were described.</p><h2 id="artAbst2" class="collapse-blocked"></h2><p><span style="display: none;">figure placeholder</span></p></div><div class="art-list-item-tools small wd-abstr-lower"><a class="mr-2" href="https://doi.org/10.1149/1945-7111/ae9c71">https://doi.org/10.1149/1945-7111/ae9c71</a></div></div></li><li class="art-list-item reveal-container reveal-closed"><a href="/article/10.1149/1945-7111/aea059" class="art-list-item-title event_main-link">Detection and Prevention Technologies for Lithium-Ion Battery Thermal Runaway</a><p class="small art-list-item-meta">Yuansheng Xu <em>et al</em> 2026 <em>J. Electrochem. Soc.</em> <b>173</b> 170520 </p><div class="art-list-item-tools small wd-abstr-upper"><a href="/article/10.1149/1945-7111/aea059/meta" class="mr-2 mb-0 nowrap event_mini-link" data-event-action="View article"><span class="icon-article"></span>View article<span class="offscreen-hidden">,&nbsp;Detection and Prevention Technologies for Lithium-Ion Battery Thermal Runaway</span></a><a href="/article/10.1149/1945-7111/aea059/pdf" class="mr-2 mb-0 nowrap event_mini-link" data-event-action="PDF"><span class="icon-file-pdf"></span>PDF<span class="offscreen-hidden">,&nbsp;Detection and Prevention Technologies for Lithium-Ion Battery Thermal Runaway</span></a><button type="button" class="reveal-trigger mr-2 nowrap"><svg aria-hidden="true" class="fa-icon fa-icon--left fa-icon--flip" role="img" focusable="false" xmlns="http://www.w3.org/2000/svg" viewBox="0 0 320 512"><!--caret-down--><!--!Font Awesome Free 6.5.1 by @fontawesome - https://fontawesome.com License - https://fontawesome.com/license/free Copyright 2024 Fonticons, Inc.--><path d="M137.4 374.6c12.5 12.5 32.8 12.5 45.3 0l128-128c9.2-9.2 11.9-22.9 6.9-34.9s-16.6-19.8-29.6-19.8L32 192c-12.9 0-24.6 7.8-29.6 19.8s-2.2 25.7 6.9 34.9l128 128z"/></svg><span class="reveal-trigger-label" data-reveal-text="Open abstract" data-reveal-label-alt="Close abstract" data-link-purpose-append="Detection and Prevention Technologies for Lithium-Ion Battery Thermal Runaway" data-link-purpose-append-open="Detection and Prevention Technologies for Lithium-Ion Battery Thermal Runaway">Open abstract</span></button></div><div class="reveal-content"><div class="article-text view-text-small"><p>The rapid popularization of lithium-ion batteries (LIBs) in vehicles and energy storage brings frequent thermal runaway safety accidents, which severely restrict industrial development. Thermal runaway originates from multi-stage exothermic chain reactions inside cells and is the most dangerous battery failure mode. Based on domestic and international research, this paper systematically elaborates LIB thermal runaway reaction mechanisms, root inducements, advanced early warning technologies and battery thermal management strategies. The collaborative application of early warning and thermal management systems can effectively suppress thermal runaway initiation and propagation. Finally, the existing technical bottlenecks and future intelligent integrated development directions are prospected.</p><h2 id="artAbst2" class="collapse-blocked"></h2><p><span style="display: none;">figure placeholder</span></p><h2 id="artAbst3" class="collapse-blocked">Highlights:</h2><p><ul><li><p>This paper conducts a systematic review that integrates the precursor mechanisms, detection technologies and prevention strategies of battery thermal runaway.</p></li><li><p>It thoroughly analyzes the synergistic coupling effect of multi-signal fusion detection and thermal runaway suppression technologies.</p></li><li><p>The core technical bottlenecks of early warning systems are summarized, and prospective research directions are put forward.</p></li><li><p>A novel integrated framework is proposed to realize the collaborative deployment of detection and protection functions within battery management system (BMS).</p></li></ul></p></div><div class="art-list-item-tools small wd-abstr-lower"><a class="mr-2" href="https://doi.org/10.1149/1945-7111/aea059">https://doi.org/10.1149/1945-7111/aea059</a></div></div></li><li class="art-list-item reveal-container reveal-closed"><a href="/article/10.1149/1945-7111/ae9646" class="art-list-item-title event_main-link">Recent Advances in Electrochemical Sensors for Aflatoxin B1 Detection</a><p class="small art-list-item-meta">Amed Gallegos-Tabanico <em>et al</em> 2026 <em>J. Electrochem. Soc.</em> <b>173</b> 167504 </p><div class="art-list-item-tools small wd-abstr-upper"><a href="/article/10.1149/1945-7111/ae9646/meta" class="mr-2 mb-0 nowrap event_mini-link" data-event-action="View article"><span class="icon-article"></span>View article<span class="offscreen-hidden">,&nbsp;Recent Advances in Electrochemical Sensors for Aflatoxin B1 Detection</span></a><a href="/article/10.1149/1945-7111/ae9646/pdf" class="mr-2 mb-0 nowrap event_mini-link" data-event-action="PDF"><span class="icon-file-pdf"></span>PDF<span class="offscreen-hidden">,&nbsp;Recent Advances in Electrochemical Sensors for Aflatoxin B1 Detection</span></a><button type="button" class="reveal-trigger mr-2 nowrap"><svg aria-hidden="true" class="fa-icon fa-icon--left fa-icon--flip" role="img" focusable="false" xmlns="http://www.w3.org/2000/svg" viewBox="0 0 320 512"><!--caret-down--><!--!Font Awesome Free 6.5.1 by @fontawesome - https://fontawesome.com License - https://fontawesome.com/license/free Copyright 2024 Fonticons, Inc.--><path d="M137.4 374.6c12.5 12.5 32.8 12.5 45.3 0l128-128c9.2-9.2 11.9-22.9 6.9-34.9s-16.6-19.8-29.6-19.8L32 192c-12.9 0-24.6 7.8-29.6 19.8s-2.2 25.7 6.9 34.9l128 128z"/></svg><span class="reveal-trigger-label" data-reveal-text="Open abstract" data-reveal-label-alt="Close abstract" data-link-purpose-append="Recent Advances in Electrochemical Sensors for Aflatoxin B1 Detection" data-link-purpose-append-open="Recent Advances in Electrochemical Sensors for Aflatoxin B1 Detection">Open abstract</span></button></div><div class="reveal-content"><div class="article-text view-text-small"><p>Aflatoxin B1 (AFB1), the most toxic and carcinogenic toxin produced by Aspergillus flavus and Aspergillus parasiticus, poses a major risk to food safety and public health due to its frequent occurrence in cereals and derived products. Conventional detection methods, including High-Performance Liquid Chromatography (HPLC) and Enzyme-Linked Immunosorbent Assay (ELISA), provide high sensitivity but are costly, time-consuming, and unsuitable for on-site use. Currently, no effective method exists to reduce aflatoxin levels in food and feed, thus early detection remains the only viable strategy for managing contamination. This review highlights advances in electrochemical sensors as promising alternatives, emphasizing the role of nanostructured materials, electrode surface modifications, and molecular recognition strategies such as aptamers, molecularly imprinted polymers, and antibodies. Challenges like matrix effects, sensor stability, and reproducibility are discussed, alongside future perspectives toward portable, reliable, and cost-effective detection platforms.</p><h2 id="artAbst2" class="collapse-blocked"></h2><p><span style="display: none;">figure placeholder</span></p></div><div class="art-list-item-tools small wd-abstr-lower"><a class="mr-2" href="https://doi.org/10.1149/1945-7111/ae9646">https://doi.org/10.1149/1945-7111/ae9646</a></div></div></li></ul><!--    articleEntryList end--></div></div></div><!-- End Review tabpanel --><!-- Start Featured tabpanel --><!-- End Featured tabpanel --><!-- Start Editor's chocie tabpanel --><div tabindex="0"
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                    Open all abstracts<span class="offscreen-hidden">,&nbsp;in this tab</span></button></p><!--    articleEntryList start--><ul class="art-list"><li class="art-list-item reveal-container reveal-closed"><div class="eyebrow"><span class="offscreen-hidden">The following article is </span><span class="red">Open access</span></div><a href="/article/10.1149/1945-7111/aeaf1a" class="art-list-item-title event_main-link">Editors’ Choice—Regulation of the Groove Profile in Jet Electrochemical Machining by Using an Embedded Auxiliary Electrode</a><p class="small art-list-item-meta">Xindi Wang <em>et al</em> 2026 <em>J. Electrochem. Soc.</em> <b>173</b> 193503 </p><div class="art-list-item-tools small wd-abstr-upper"><a href="/article/10.1149/1945-7111/aeaf1a/meta" class="mr-2 mb-0 nowrap event_mini-link" data-event-action="View article"><span class="icon-article"></span>View article<span class="offscreen-hidden">,&nbsp;Editors’ Choice—Regulation of the Groove Profile in Jet Electrochemical Machining by Using an Embedded Auxiliary Electrode</span></a><a href="/article/10.1149/1945-7111/aeaf1a/pdf" class="mr-2 mb-0 nowrap event_mini-link" data-event-action="PDF"><span class="icon-file-pdf"></span>PDF<span class="offscreen-hidden">,&nbsp;Editors’ Choice—Regulation of the Groove Profile in Jet Electrochemical Machining by Using an Embedded Auxiliary Electrode</span></a><button type="button" class="reveal-trigger mr-2 nowrap"><svg aria-hidden="true" class="fa-icon fa-icon--left fa-icon--flip" role="img" focusable="false" xmlns="http://www.w3.org/2000/svg" viewBox="0 0 320 512"><!--caret-down--><!--!Font Awesome Free 6.5.1 by @fontawesome - https://fontawesome.com License - https://fontawesome.com/license/free Copyright 2024 Fonticons, Inc.--><path d="M137.4 374.6c12.5 12.5 32.8 12.5 45.3 0l128-128c9.2-9.2 11.9-22.9 6.9-34.9s-16.6-19.8-29.6-19.8L32 192c-12.9 0-24.6 7.8-29.6 19.8s-2.2 25.7 6.9 34.9l128 128z"/></svg><span class="reveal-trigger-label" data-reveal-text="Open abstract" data-reveal-label-alt="Close abstract" data-link-purpose-append="Editors’ Choice—Regulation of the Groove Profile in Jet Electrochemical Machining by Using an Embedded Auxiliary Electrode" data-link-purpose-append-open="Editors’ Choice—Regulation of the Groove Profile in Jet Electrochemical Machining by Using an Embedded Auxiliary Electrode">Open abstract</span></button></div><div class="reveal-content"><div class="article-text view-text-small"><p>Jet electrochemical machining (Jet-ECM) is a promising approach for fabricating micro-meso structures such as grooves on difficult-to-machine materials. However, the electric field distribution within the machining gap usually follows a Gaussian distribution, leading to U-shaped profiles which is difficult to alter merely by adjusting the processing parameters. This limitation hinders the application expansion of the method. To realize controllable regulation of groove cross-sectional profiles, a novel machining method is proposed in this study. An auxiliary electrode is fixed at the central position of the tubular cathode via a dedicated fixture. With the machining voltage between the workpiece and the cathode maintained constant, the potential of the auxiliary electrode is adjustable. Simulation results demonstrate that applying different potentials to the auxiliary electrode significantly alters the electric field conditions, including current lines and the current density distribution on the workpiece, thereby changing the groove cross-sectional profile. In groove machining experiments conducted at a machining voltage of 15 V, the groove cross-sectional profile sequentially transforms from V-shape to U-shape and finally to W-shape as the auxiliary electrode potential is gradually increased from 0 V to 20 V. This confirms that the groove profile can be effectively regulated by the proposed method.</p><h2 id="artAbst2" class="collapse-blocked"></h2><p><span style="display: none;">figure placeholder</span></p><h2 id="artAbst3" class="collapse-blocked">Highlights:</h2><p>1. An embedded auxiliary is introduced into jet electrochemical machining.</p><p>2. The application of the auxiliary electrode can alter the electric field.</p><p>3. The cross-sectional profile can be regulated by changing the electrode potential.</p></div><div class="art-list-item-tools small wd-abstr-lower"><a class="mr-2" href="https://doi.org/10.1149/1945-7111/aeaf1a">https://doi.org/10.1149/1945-7111/aeaf1a</a></div></div></li><li class="art-list-item reveal-container reveal-closed"><div class="eyebrow"><span class="offscreen-hidden">The following article is </span><span class="red">Open access</span></div><a href="/article/10.1149/1945-7111/ae60a9" class="art-list-item-title event_main-link">Editors’ Choice—Understanding the Role of Multivalency in Chloride-Based Electrolytes for Efficient Iron Electrosynthesis</a><p class="small art-list-item-meta">William Lvovich <em>et al</em> 2026 <em>J. Electrochem. Soc.</em> <b>173</b> 082502 </p><div class="art-list-item-tools small wd-abstr-upper"><a href="/article/10.1149/1945-7111/ae60a9/meta" class="mr-2 mb-0 nowrap event_mini-link" data-event-action="View article"><span class="icon-article"></span>View article<span class="offscreen-hidden">,&nbsp;Editors’ Choice—Understanding the Role of Multivalency in Chloride-Based Electrolytes for Efficient Iron Electrosynthesis</span></a><a href="/article/10.1149/1945-7111/ae60a9/pdf" class="mr-2 mb-0 nowrap event_mini-link" data-event-action="PDF"><span class="icon-file-pdf"></span>PDF<span class="offscreen-hidden">,&nbsp;Editors’ Choice—Understanding the Role of Multivalency in Chloride-Based Electrolytes for Efficient Iron Electrosynthesis</span></a><button type="button" class="reveal-trigger mr-2 nowrap"><svg aria-hidden="true" class="fa-icon fa-icon--left fa-icon--flip" role="img" focusable="false" xmlns="http://www.w3.org/2000/svg" viewBox="0 0 320 512"><!--caret-down--><!--!Font Awesome Free 6.5.1 by @fontawesome - https://fontawesome.com License - https://fontawesome.com/license/free Copyright 2024 Fonticons, Inc.--><path d="M137.4 374.6c12.5 12.5 32.8 12.5 45.3 0l128-128c9.2-9.2 11.9-22.9 6.9-34.9s-16.6-19.8-29.6-19.8L32 192c-12.9 0-24.6 7.8-29.6 19.8s-2.2 25.7 6.9 34.9l128 128z"/></svg><span class="reveal-trigger-label" data-reveal-text="Open abstract" data-reveal-label-alt="Close abstract" data-link-purpose-append="Editors’ Choice—Understanding the Role of Multivalency in Chloride-Based Electrolytes for Efficient Iron Electrosynthesis" data-link-purpose-append-open="Editors’ Choice—Understanding the Role of Multivalency in Chloride-Based Electrolytes for Efficient Iron Electrosynthesis">Open abstract</span></button></div><div class="reveal-content"><div class="article-text view-text-small"><p>This study investigates aqueous electrolytes for efficient iron electrodeposition directly from Fe<sup>3+</sup> at ambient temperature. Concentrated lithium chloride (LiCl) based electrolytes were found to stabilize the Fe<sup>3+</sup> in the electrolyte, suppress parasitic hydrogen evolution and suppress redox shuttling of intermediate Fe<sup>2+</sup>, thus promoting efficient iron electrodeposition. These attributes collectively enabled high Coulombic efficiencies (&gt;75%) at high current densities (&gt;200 mA cm<sup>−2</sup>). Furthermore, detailed investigation revealed that increasing the LiCl concentration increased the electrolyte viscosity and decreased the Fe<sup>2+</sup> out-diffusion rate while also suppressing the activity of water. Sufficiently high LiCl concentrations (&gt;7 M) thus provide a window of current densities in which elevated Coulombic efficiencies can be achieved. Overall, this paper develops an understanding of the effects of electrolyte composition on the competition between Fe electrodeposition, hydrogen co-evolution, and intermediate Fe<sup>2+</sup> out-diffusion for efficient Fe metal electrosynthesis.</p><h2 id="artAbst2" class="collapse-blocked"></h2><p><span style="display: none;">figure placeholder</span></p></div><div class="art-list-item-tools small wd-abstr-lower"><a class="mr-2" href="https://doi.org/10.1149/1945-7111/ae60a9">https://doi.org/10.1149/1945-7111/ae60a9</a></div></div></li><li class="art-list-item reveal-container reveal-closed"><div class="eyebrow"><span class="offscreen-hidden">The following article is </span><span class="red">Open access</span></div><a href="/article/10.1149/1945-7111/ae17eb" class="art-list-item-title event_main-link">Editors’ Choice—Modeling of Multistage Redox-Mediated Electrodialysis for Volatile Fatty Acids Fractionation</a><p class="small art-list-item-meta">Riccardo Candeago <em>et al</em> 2025 <em>J. Electrochem. Soc.</em> <b>172</b> 113503 </p><div class="art-list-item-tools small wd-abstr-upper"><a href="/article/10.1149/1945-7111/ae17eb/meta" class="mr-2 mb-0 nowrap event_mini-link" data-event-action="View article"><span class="icon-article"></span>View article<span class="offscreen-hidden">,&nbsp;Editors’ Choice—Modeling of Multistage Redox-Mediated Electrodialysis for Volatile Fatty Acids Fractionation</span></a><a href="/article/10.1149/1945-7111/ae17eb/pdf" class="mr-2 mb-0 nowrap event_mini-link" data-event-action="PDF"><span class="icon-file-pdf"></span>PDF<span class="offscreen-hidden">,&nbsp;Editors’ Choice—Modeling of Multistage Redox-Mediated Electrodialysis for Volatile Fatty Acids Fractionation</span></a><button type="button" class="reveal-trigger mr-2 nowrap"><svg aria-hidden="true" class="fa-icon fa-icon--left fa-icon--flip" role="img" focusable="false" xmlns="http://www.w3.org/2000/svg" viewBox="0 0 320 512"><!--caret-down--><!--!Font Awesome Free 6.5.1 by @fontawesome - https://fontawesome.com License - https://fontawesome.com/license/free Copyright 2024 Fonticons, Inc.--><path d="M137.4 374.6c12.5 12.5 32.8 12.5 45.3 0l128-128c9.2-9.2 11.9-22.9 6.9-34.9s-16.6-19.8-29.6-19.8L32 192c-12.9 0-24.6 7.8-29.6 19.8s-2.2 25.7 6.9 34.9l128 128z"/></svg><span class="reveal-trigger-label" data-reveal-text="Open abstract" data-reveal-label-alt="Close abstract" data-link-purpose-append="Editors’ Choice—Modeling of Multistage Redox-Mediated Electrodialysis for Volatile Fatty Acids Fractionation" data-link-purpose-append-open="Editors’ Choice—Modeling of Multistage Redox-Mediated Electrodialysis for Volatile Fatty Acids Fractionation">Open abstract</span></button></div><div class="reveal-content"><div class="article-text view-text-small"><p>Production of volatile fatty acids (VFAs) from biomass fermentation is a promising pathway for sustainable chemical production. A central challenge is cost-effective recovery and fractionation of VFAs from fermentation broths. Redox-mediated electrodialysis (redox-ED) can be an energy efficient technique for VFA separation, replacing water splitting with redox-reactions. However, the low selectivity between VFAs of different lengths (separation factors &lt;3) obtained using commercially-available anion-exchange membranes limits the final product purity for industrial use. Cascaded operation can overcome these material limitations and increase product purity, yet multistage redox-ED can be complex and has not been extensively explored for selective ion separations. Here, we developed a physics-based model of redox-ED using finite elements to simulate the separation of a ternary carboxylic acid feed (propionic, butyric, and hexanoic) and evaluated five different multistage architectures including series, parallel, co-current, and counter-current setups. The single-stage, two-dimensional steady-state model captured the effect of the flow-field, concentration, and potential gradients, yielding reasonable agreement with experimental data. We then investigated the tradeoff between number of stages, product purity, and productivity, and assessed the impact of membrane selectivity. In sum, cascaded redox-ED with reflux simultaneously improved product purity and productivity, while series or equivalent single-stage architectures presented a tradeoff between VFA purity and productivity.</p><h2 id="artAbst2" class="collapse-blocked"></h2><p><span style="display: none;">figure placeholder</span></p></div><div class="art-list-item-tools small wd-abstr-lower"><a class="mr-2" href="https://doi.org/10.1149/1945-7111/ae17eb">https://doi.org/10.1149/1945-7111/ae17eb</a></div></div></li><li class="art-list-item reveal-container reveal-closed"><div class="eyebrow"><span class="offscreen-hidden">The following article is </span><span class="red">Open access</span></div><a href="/article/10.1149/1945-7111/adc553" class="art-list-item-title event_main-link">Editors’ Choice—Rapid Deactivation Convolutes Electrochemical CO<sub>2</sub> Reduction Selectivity Measurements on Gold Rotating Ring Disk Electrodes</a><p class="small art-list-item-meta">Maria Kelly <em>et al</em> 2025 <em>J. Electrochem. Soc.</em> <b>172</b> 046503 </p><div class="art-list-item-tools small wd-abstr-upper"><a href="/article/10.1149/1945-7111/adc553/meta" class="mr-2 mb-0 nowrap event_mini-link" data-event-action="View article"><span class="icon-article"></span>View article<span class="offscreen-hidden">,&nbsp;Editors’ Choice—Rapid Deactivation Convolutes Electrochemical CO2 Reduction Selectivity Measurements on Gold Rotating Ring Disk Electrodes</span></a><a href="/article/10.1149/1945-7111/adc553/pdf" class="mr-2 mb-0 nowrap event_mini-link" data-event-action="PDF"><span class="icon-file-pdf"></span>PDF<span class="offscreen-hidden">,&nbsp;Editors’ Choice—Rapid Deactivation Convolutes Electrochemical CO2 Reduction Selectivity Measurements on Gold Rotating Ring Disk Electrodes</span></a><button type="button" class="reveal-trigger mr-2 nowrap"><svg aria-hidden="true" class="fa-icon fa-icon--left fa-icon--flip" role="img" focusable="false" xmlns="http://www.w3.org/2000/svg" viewBox="0 0 320 512"><!--caret-down--><!--!Font Awesome Free 6.5.1 by @fontawesome - https://fontawesome.com License - https://fontawesome.com/license/free Copyright 2024 Fonticons, Inc.--><path d="M137.4 374.6c12.5 12.5 32.8 12.5 45.3 0l128-128c9.2-9.2 11.9-22.9 6.9-34.9s-16.6-19.8-29.6-19.8L32 192c-12.9 0-24.6 7.8-29.6 19.8s-2.2 25.7 6.9 34.9l128 128z"/></svg><span class="reveal-trigger-label" data-reveal-text="Open abstract" data-reveal-label-alt="Close abstract" data-link-purpose-append="Editors’ Choice—Rapid Deactivation Convolutes Electrochemical CO2 Reduction Selectivity Measurements on Gold Rotating Ring Disk Electrodes" data-link-purpose-append-open="Editors’ Choice—Rapid Deactivation Convolutes Electrochemical CO2 Reduction Selectivity Measurements on Gold Rotating Ring Disk Electrodes">Open abstract</span></button></div><div class="reveal-content"><div class="article-text view-text-small"><p>Voltammetric measurements of electrochemical CO<sub>2</sub> reduction reaction (CO<sub>2</sub>RR) selectivity on rotating ring disk electrodes (RRDE) are a rapid and sensitive method for quantifying an electrocatalyst’s selectivity, i.e. faradaic efficiency (FE). This method has been applied to polycrystalline Au electrocatalysts where a Au disk electrode catalyzes both the CO<sub>2</sub>RR and hydrogen evolution reaction while the concentric Au ring electrode selectively senses CO by oxidizing CO back to CO<sub>2</sub>. Such measurements enabled fundamental mechanistic studies but suffer from poor inter-laboratory reproducibility. This work identifies causes of variability in RRDE selectivity measurements by comparing protocols with different electrochemical methods, reagent purities, and glassware cleaning procedures. We observed FE<sub>CO</sub> decrease by 56% during 5 min chronoamperometry measurements, a phenomenon that is not readily apparent in voltammetric scans due to their dynamic nature. Electroplating of electrolyte impurities onto the disk and ring surfaces were identified as a major contributor to Au deactivation. Additionally, the oxygen reduction reaction may lead to higher disk currents in inadequately purged electrolytes, causing an apparent underestimation of FE<sub>CO</sub> at low overpotentials. Lastly, we propose operational bounds for CO<sub>2</sub>RR selectivity measurements on Au using the RRDE method and provide suggestions on steps for improving the accuracy of this technique.</p><h2 id="artAbst2" class="collapse-blocked"></h2><p><span style="display: none;">figure placeholder</span></p></div><div class="art-list-item-tools small wd-abstr-lower"><a class="mr-2" href="https://doi.org/10.1149/1945-7111/adc553">https://doi.org/10.1149/1945-7111/adc553</a></div></div></li><li class="art-list-item reveal-container reveal-closed"><div class="eyebrow"><span class="offscreen-hidden">The following article is </span><span class="red">Open access</span></div><a href="/article/10.1149/1945-7111/adbd7d" class="art-list-item-title event_main-link">Editors’ Choice—Molten Salt Electrolysis in Chloride Melts for Energy-Efficient Iron Metal Production</a><p class="small art-list-item-meta">Anar Badalbayli <em>et al</em> 2025 <em>J. Electrochem. Soc.</em> <b>172</b> 032508 </p><div class="art-list-item-tools small wd-abstr-upper"><a href="/article/10.1149/1945-7111/adbd7d/meta" class="mr-2 mb-0 nowrap event_mini-link" data-event-action="View article"><span class="icon-article"></span>View article<span class="offscreen-hidden">,&nbsp;Editors’ Choice—Molten Salt Electrolysis in Chloride Melts for Energy-Efficient Iron Metal Production</span></a><a href="/article/10.1149/1945-7111/adbd7d/pdf" class="mr-2 mb-0 nowrap event_mini-link" data-event-action="PDF"><span class="icon-file-pdf"></span>PDF<span class="offscreen-hidden">,&nbsp;Editors’ Choice—Molten Salt Electrolysis in Chloride Melts for Energy-Efficient Iron Metal Production</span></a><button type="button" class="reveal-trigger mr-2 nowrap"><svg aria-hidden="true" class="fa-icon fa-icon--left fa-icon--flip" role="img" focusable="false" xmlns="http://www.w3.org/2000/svg" viewBox="0 0 320 512"><!--caret-down--><!--!Font Awesome Free 6.5.1 by @fontawesome - https://fontawesome.com License - https://fontawesome.com/license/free Copyright 2024 Fonticons, Inc.--><path d="M137.4 374.6c12.5 12.5 32.8 12.5 45.3 0l128-128c9.2-9.2 11.9-22.9 6.9-34.9s-16.6-19.8-29.6-19.8L32 192c-12.9 0-24.6 7.8-29.6 19.8s-2.2 25.7 6.9 34.9l128 128z"/></svg><span class="reveal-trigger-label" data-reveal-text="Open abstract" data-reveal-label-alt="Close abstract" data-link-purpose-append="Editors’ Choice—Molten Salt Electrolysis in Chloride Melts for Energy-Efficient Iron Metal Production" data-link-purpose-append-open="Editors’ Choice—Molten Salt Electrolysis in Chloride Melts for Energy-Efficient Iron Metal Production">Open abstract</span></button></div><div class="reveal-content"><div class="article-text view-text-small"><p>This study explores chloride molten salt electrolysis (CMSE) as a promising route for energy-efficient iron metal (Fe) production. Moderate temperature (500 °C) LiCl-KCl molten salts offer excellent thermodynamic stability, high ionic conductivity and diffusivity, and high solubility for FeCl<sub>3</sub>, thereby enabling efficient Fe metal extraction at high electrowinning rates. Here, we demonstrate the two essential steps for converting taconite ore into Fe metal. First, Fe<sub>2</sub>O<sub>3</sub> from taconite pellets was selectively leached in HCl yielding a high-purity FeCl<sub>3</sub> aqueous solution, while the gangue components settled at the bottom. Then, anhydrous FeCl<sub>3</sub> was electrolyzed in a LiCl-KCl eutectic molten salt at 500 °C at high current density (1 A cm<sup>−2</sup>) and at high Coulombic efficiency (&gt;85%). Analysis of the electrowon Fe deposits revealed dendritic structures with purity of &gt;99 wt%, which could be further improved to nearly 100 wt% through arc re-melting. CMSE offers low specific energy consumption (3.7 kWhr kg<sup>−1</sup>), competitive with H<sub>2</sub>-DRI and other electrolytic approaches being pursued globally. Our findings underscore the potential of CMSE as an energy-efficient route for electrosynthesis of Fe metal.</p></div><div class="art-list-item-tools small wd-abstr-lower"><a class="mr-2" href="https://doi.org/10.1149/1945-7111/adbd7d">https://doi.org/10.1149/1945-7111/adbd7d</a></div></div></li></ul><!--    articleEntryList end--></div></div></div><!-- End Editor's chocie tabpanel --><!-- Start AM tabpanel --><div tabindex="0"
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                         style="display: none;"><!--    accepted manuscript listing start--><p id="jnl-issue-disp-links" class="cf"><button data-reveal-label-alt="Close all abstracts" class="reveal-all-trigger mr-2 small"
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               data-link-purpose-append-open="in this tab">Open all abstracts<span class="offscreen-hidden">,&nbsp;in this tab</span></button></p><!-- Start AM list content --><ul class="art-list" id="wd-jnl-issue-art-list"><li class="art-list-item reveal-container reveal-closed"><div class="eyebrow"><span class="offscreen-hidden">The following article is </span><span class="red">Open access</span></div><a href="/article/10.1149/1945-7111/aeb7d2" class="art-list-item-title event_main-link">Free Ionomer Controls Adsorption in Electrolyzer Inks</a><p class="small art-list-item-meta">Degirmenci et al&nbsp;</p><div class="art-list-item-tools small wd-abstr-upper"><a href="/article/10.1149/1945-7111/aeb7d2/meta" class="mr-2 mb-0 nowrap event_mini-link" data-event-action="View article"><span class="icon-article"></span>View accepted manuscript<span class="offscreen-hidden">,&nbsp;Free Ionomer Controls Adsorption in Electrolyzer Inks</span></a><a href="/article/10.1149/1945-7111/aeb7d2/pdf" class="mr-2 mb-0 nowrap event_mini-link" data-event-action="PDF"><span class="icon-file-pdf"></span>PDF<span class="offscreen-hidden">,&nbsp;Free Ionomer Controls Adsorption in Electrolyzer Inks</span></a><button type="button" class="reveal-trigger mr-2 nowrap"><svg aria-hidden="true" class="fa-icon fa-icon--left fa-icon--flip" role="img" focusable="false" xmlns="http://www.w3.org/2000/svg" viewBox="0 0 320 512"><!--caret-down--><!--!Font Awesome Free 6.5.1 by @fontawesome - https://fontawesome.com License - https://fontawesome.com/license/free Copyright 2024 Fonticons, Inc.--><path d="M137.4 374.6c12.5 12.5 32.8 12.5 45.3 0l128-128c9.2-9.2 11.9-22.9 6.9-34.9s-16.6-19.8-29.6-19.8L32 192c-12.9 0-24.6 7.8-29.6 19.8s-2.2 25.7 6.9 34.9l128 128z"/></svg><span class="reveal-trigger-label" data-reveal-text="Open abstract" data-reveal-label-alt="Close abstract" data-link-purpose-append="Free Ionomer Controls Adsorption in Electrolyzer Inks" data-link-purpose-append-open="Free Ionomer Controls Adsorption in Electrolyzer Inks">Open abstract</span></button></div><div class="reveal-content"><div class="article-text view-text-small">
						<p>The ionomer/catalyst interface in proton-exchange-membrane water-electrolyzer (PEMWE) anode catalyst layers governs multi-species transport and reaction kinetics, and originates from ionomer adsorption onto catalyst particles during ink formation. These inks contain iridium oxide (IrOx) catalyst and PEM ionomer (typically perfluorosulfonic acid, PFSA) dispersed in water:alcohol solvent mixtures, deposited to form the catalyst layer upon solvent evaporation. Despite the importance of ink formulation controlling ionomer adsorption, a systematic investigation spanning industrially relevant formulations (including concentrated inks used in roll-to-roll manufacturing) is missing. Here, we investigate the influence of IrOx concentration, ionomer-to-catalyst (I:C) ratio, and solvent composition on PFSA adsorption using thermal gravimetric analysis. PFSA adsorption is independent of IrOx concentration, being instead determined by free-ionomer concentration and solvent identity, across both dilute and concentrated inks. We further show that I:C ratio is a poor descriptor, with free-ionomer weight percentage providing a more meaningful metric that collapses adsorption data onto a single isotherm. In water-rich solvents, adsorption is primarily limited by electrostatic repulsion, whereas, in alcohol-rich solvents, solvation forces and surface-coverage effects dominate. We additionally characterize ink stability (sedimentation, x-ray scattering) and single-cell performance. These results extend to PFSA-based catalyst inks (including high-surface-area carbons), offering practical implications for ink formulation across deposition methods.</p>
					</div><div class="art-list-item-tools small wd-abstr-lower"><a class="mr-2" href="https://doi.org/10.1149/1945-7111/aeb7d2">https://doi.org/10.1149/1945-7111/aeb7d2</a></div></div></li><li class="art-list-item reveal-container reveal-closed"><div class="eyebrow"><span class="offscreen-hidden">The following article is </span><span class="red">Open access</span></div><a href="/article/10.1149/1945-7111/aeb765" class="art-list-item-title event_main-link">Resolving Electron-Transfer Heterogeneity in Electrochemical Aptamer-Based Sensors by Distribution of Capacitance Timescales</a><p class="small art-list-item-meta">Lansdorp et al&nbsp;</p><div class="art-list-item-tools small wd-abstr-upper"><a href="/article/10.1149/1945-7111/aeb765/meta" class="mr-2 mb-0 nowrap event_mini-link" data-event-action="View article"><span class="icon-article"></span>View accepted manuscript<span class="offscreen-hidden">,&nbsp;Resolving Electron-Transfer Heterogeneity in Electrochemical Aptamer-Based Sensors by Distribution of Capacitance Timescales</span></a><a href="/article/10.1149/1945-7111/aeb765/pdf" class="mr-2 mb-0 nowrap event_mini-link" data-event-action="PDF"><span class="icon-file-pdf"></span>PDF<span class="offscreen-hidden">,&nbsp;Resolving Electron-Transfer Heterogeneity in Electrochemical Aptamer-Based Sensors by Distribution of Capacitance Timescales</span></a><button type="button" class="reveal-trigger mr-2 nowrap"><svg aria-hidden="true" class="fa-icon fa-icon--left fa-icon--flip" role="img" focusable="false" xmlns="http://www.w3.org/2000/svg" viewBox="0 0 320 512"><!--caret-down--><!--!Font Awesome Free 6.5.1 by @fontawesome - https://fontawesome.com License - https://fontawesome.com/license/free Copyright 2024 Fonticons, Inc.--><path d="M137.4 374.6c12.5 12.5 32.8 12.5 45.3 0l128-128c9.2-9.2 11.9-22.9 6.9-34.9s-16.6-19.8-29.6-19.8L32 192c-12.9 0-24.6 7.8-29.6 19.8s-2.2 25.7 6.9 34.9l128 128z"/></svg><span class="reveal-trigger-label" data-reveal-text="Open abstract" data-reveal-label-alt="Close abstract" data-link-purpose-append="Resolving Electron-Transfer Heterogeneity in Electrochemical Aptamer-Based Sensors by Distribution of Capacitance Timescales" data-link-purpose-append-open="Resolving Electron-Transfer Heterogeneity in Electrochemical Aptamer-Based Sensors by Distribution of Capacitance Timescales">Open abstract</span></button></div><div class="reveal-content"><div class="article-text view-text-small">
						<p>Distribution of timescales methods have become powerful tools for extracting hidden kinetic processes from electrochemical impedance spectra. Their physical interpretation, however, depends critically on matching the assumed mathematical model to the underlying physical electrochemical system. Here, we show that the Distribution of Capacitive Times (DCT) model is well-matched to the physics of surface-immobilized redox systems, enabling electron-transfer rate heterogeneity to be resolved. This makes electrochemical aptamer-based (EAB) sensors a natural system for DCT analysis, as their surface-tethered redox reporters can occupy distinct molecular states with different electron-transfer kinetics. Applying DCT to a vancomycin EAB biosensor reveals two distinct electron-transfer populations whose respective rates remain nearly constant as a function of vancomycin concentration. In contrast, their relative occupancies evolve with changing target concentration, demonstrating that the sensor’s response arises from redistribution between states rather than from a continuously varying electron-transfer rate. Analysis of the population amplitudes is consistent with a biophysical model in which approximately one-third of the surface-bound aptamers do not respond to target, suggesting an area that can be explored to improve the performance of such sensors. These results demonstrate that DCT analysis can uncover mechanistic insights in surface-immobilized redox systems that are inaccessible to conventional impedance analysis.</p>
					</div><div class="art-list-item-tools small wd-abstr-lower"><a class="mr-2" href="https://doi.org/10.1149/1945-7111/aeb765">https://doi.org/10.1149/1945-7111/aeb765</a></div></div></li><li class="art-list-item reveal-container reveal-closed"><div class="eyebrow"><span class="offscreen-hidden">The following article is </span><span class="red">Open access</span></div><a href="/article/10.1149/1945-7111/aeb766" class="art-list-item-title event_main-link">Part II. Matched Asymptotics Analysis for a Lithium-Ion Battery with a Torn Negative-Electrode Tab Elucidating the Impact of Free-Electrolyte Reservoirs on Lithium Plating Initiation During Discharge</a><p class="small art-list-item-meta">Baker et al&nbsp;</p><div class="art-list-item-tools small wd-abstr-upper"><a href="/article/10.1149/1945-7111/aeb766/meta" class="mr-2 mb-0 nowrap event_mini-link" data-event-action="View article"><span class="icon-article"></span>View accepted manuscript<span class="offscreen-hidden">,&nbsp;Part II. Matched Asymptotics Analysis for a Lithium-Ion Battery with a Torn Negative-Electrode Tab Elucidating the Impact of Free-Electrolyte Reservoirs on Lithium Plating Initiation During Discharge</span></a><a href="/article/10.1149/1945-7111/aeb766/pdf" class="mr-2 mb-0 nowrap event_mini-link" data-event-action="PDF"><span class="icon-file-pdf"></span>PDF<span class="offscreen-hidden">,&nbsp;Part II. Matched Asymptotics Analysis for a Lithium-Ion Battery with a Torn Negative-Electrode Tab Elucidating the Impact of Free-Electrolyte Reservoirs on Lithium Plating Initiation During Discharge</span></a><button type="button" class="reveal-trigger mr-2 nowrap"><svg aria-hidden="true" class="fa-icon fa-icon--left fa-icon--flip" role="img" focusable="false" xmlns="http://www.w3.org/2000/svg" viewBox="0 0 320 512"><!--caret-down--><!--!Font Awesome Free 6.5.1 by @fontawesome - https://fontawesome.com License - https://fontawesome.com/license/free Copyright 2024 Fonticons, Inc.--><path d="M137.4 374.6c12.5 12.5 32.8 12.5 45.3 0l128-128c9.2-9.2 11.9-22.9 6.9-34.9s-16.6-19.8-29.6-19.8L32 192c-12.9 0-24.6 7.8-29.6 19.8s-2.2 25.7 6.9 34.9l128 128z"/></svg><span class="reveal-trigger-label" data-reveal-text="Open abstract" data-reveal-label-alt="Close abstract" data-link-purpose-append="Part II. Matched Asymptotics Analysis for a Lithium-Ion Battery with a Torn Negative-Electrode Tab Elucidating the Impact of Free-Electrolyte Reservoirs on Lithium Plating Initiation During Discharge" data-link-purpose-append-open="Part II. Matched Asymptotics Analysis for a Lithium-Ion Battery with a Torn Negative-Electrode Tab Elucidating the Impact of Free-Electrolyte Reservoirs on Lithium Plating Initiation During Discharge">Open abstract</span></button></div><div class="reveal-content"><div class="article-text view-text-small">
						<p>In Part 1 of this work [J. Electrochem. Soc., 173 (2026) 100506], a perturbation analysis was introduced to describe how lithium plating can occur during discharge in a two-cell stack featuring a broken negative-electrode tab. Assuming a large electrolyte reservoir adjacent to the cell stack, we demonstrated that current flows through the reservoir from the functioning cell into the tab-compromised cell, leading to plating during cell discharge. Because this reservoir also supplies excess electrolyte over the battery's operational life, which can be consumed over time if there is electrolyte decomposition upon cell cycling, its thickness represents a key design parameter. In this work, matched asymptotic expansions are employed to determine how small the reservoir thickness must be to hinder current flow and delay the onset of plating following a tab failure. Our results indicate that preventing plating during discharge of a cell with a torn negative-electrode tab requires a reservoir thickness so small that it precludes maintaining any significant supply of excess electrolyte, leading to so-called dry-cell constructions.</p>
					</div><div class="art-list-item-tools small wd-abstr-lower"><a class="mr-2" href="https://doi.org/10.1149/1945-7111/aeb766">https://doi.org/10.1149/1945-7111/aeb766</a></div></div></li><li class="art-list-item reveal-container reveal-closed"><a href="/article/10.1149/1945-7111/aeb767" class="art-list-item-title event_main-link">Glyoxime Substituent Effects on Electrocatalytic Dehalogenation by Heterobinuclear Ruthenium(II)–Cobaloxime Complexes</a><p class="small art-list-item-meta">Pizarro et al&nbsp;</p><div class="art-list-item-tools small wd-abstr-upper"><a href="/article/10.1149/1945-7111/aeb767/meta" class="mr-2 mb-0 nowrap event_mini-link" data-event-action="View article"><span class="icon-article"></span>View accepted manuscript<span class="offscreen-hidden">,&nbsp;Glyoxime Substituent Effects on Electrocatalytic Dehalogenation by Heterobinuclear Ruthenium(II)–Cobaloxime Complexes</span></a><a href="/article/10.1149/1945-7111/aeb767/pdf" class="mr-2 mb-0 nowrap event_mini-link" data-event-action="PDF"><span class="icon-file-pdf"></span>PDF<span class="offscreen-hidden">,&nbsp;Glyoxime Substituent Effects on Electrocatalytic Dehalogenation by Heterobinuclear Ruthenium(II)–Cobaloxime Complexes</span></a><button type="button" class="reveal-trigger mr-2 nowrap"><svg aria-hidden="true" class="fa-icon fa-icon--left fa-icon--flip" role="img" focusable="false" xmlns="http://www.w3.org/2000/svg" viewBox="0 0 320 512"><!--caret-down--><!--!Font Awesome Free 6.5.1 by @fontawesome - https://fontawesome.com License - https://fontawesome.com/license/free Copyright 2024 Fonticons, Inc.--><path d="M137.4 374.6c12.5 12.5 32.8 12.5 45.3 0l128-128c9.2-9.2 11.9-22.9 6.9-34.9s-16.6-19.8-29.6-19.8L32 192c-12.9 0-24.6 7.8-29.6 19.8s-2.2 25.7 6.9 34.9l128 128z"/></svg><span class="reveal-trigger-label" data-reveal-text="Open abstract" data-reveal-label-alt="Close abstract" data-link-purpose-append="Glyoxime Substituent Effects on Electrocatalytic Dehalogenation by Heterobinuclear Ruthenium(II)–Cobaloxime Complexes" data-link-purpose-append-open="Glyoxime Substituent Effects on Electrocatalytic Dehalogenation by Heterobinuclear Ruthenium(II)–Cobaloxime Complexes">Open abstract</span></button></div><div class="reveal-content"><div class="article-text view-text-small">
						<p>A family of heterobinuclear ruthenium(II)-cobaloxime complexes of general formula [Ru(bpy)2(5py-bpy)Co(XgH)2Cl]2+, where XgH represents dimethylglyoximato (dmgH), methylphenylglyoximato (mpgH), or diphenylglyoximato (dpgH), was prepared and investigated for electrocatalytic reductive dehalogenation of organohalides. The Ru-containing axial metalloligand remained constant, while the substituents of the equatorial glyoximato ligands were systematically varied. Cyclic voltammetry revealed cathodic waves assigned to the Co(II)/Co(I) process at -1.49, -1.30, and -1.18 V vs Fc/Fc+ for Ru-Co(dmgH), Ru-Co(mpgH), and Ru-Co(dpgH), respectively. Addition of hexachloroethane (HCA) or trans-1,2-dibromocyclohexane (1,2-DBCH) produced concentration-dependent cathodic current enhancements consistent with reaction of electrogenerated Co(I) with the organohalides. Foot-of-the-wave analysis provided apparent bimolecular catalytic rate constants, with Ru-Co(dmgH) exhibiting the highest values: (3.00 ± 0.55) × 105 M-1 s-1 for HCA and (3.48 ± 0.06) × 105 M-1 s-1 for 1,2-DBCH. Despite having the most negative Co(II)/Co(I) potential, Ru-Co(dmgH) showed the highest apparent catalytic activity toward both substrates, while the phenyl-substituted derivatives were markedly less active toward 1,2-DBCH. Comparison with mononuclear cobaloximes indicates that the Ru-containing metalloligand does not uniformly enhance activity, and that dehalogenation reflects a balance among Co(I) accessibility, reduced-state reactivity, and substrate accessibility.</p>
					</div><div class="art-list-item-tools small wd-abstr-lower"><a class="mr-2" href="https://doi.org/10.1149/1945-7111/aeb767">https://doi.org/10.1149/1945-7111/aeb767</a></div></div></li><li class="art-list-item reveal-container reveal-closed"><a href="/article/10.1149/1945-7111/aeb62f" class="art-list-item-title event_main-link">Regulation of Ion Concentration and Deposit Shape in Liquid-Mask Electrodeposition with Bipolar Pulse Current</a><p class="small art-list-item-meta">He et al&nbsp;</p><div class="art-list-item-tools small wd-abstr-upper"><a href="/article/10.1149/1945-7111/aeb62f/meta" class="mr-2 mb-0 nowrap event_mini-link" data-event-action="View article"><span class="icon-article"></span>View accepted manuscript<span class="offscreen-hidden">,&nbsp;Regulation of Ion Concentration and Deposit Shape in Liquid-Mask Electrodeposition with Bipolar Pulse Current</span></a><a href="/article/10.1149/1945-7111/aeb62f/pdf" class="mr-2 mb-0 nowrap event_mini-link" data-event-action="PDF"><span class="icon-file-pdf"></span>PDF<span class="offscreen-hidden">,&nbsp;Regulation of Ion Concentration and Deposit Shape in Liquid-Mask Electrodeposition with Bipolar Pulse Current</span></a><button type="button" class="reveal-trigger mr-2 nowrap"><svg aria-hidden="true" class="fa-icon fa-icon--left fa-icon--flip" role="img" focusable="false" xmlns="http://www.w3.org/2000/svg" viewBox="0 0 320 512"><!--caret-down--><!--!Font Awesome Free 6.5.1 by @fontawesome - https://fontawesome.com License - https://fontawesome.com/license/free Copyright 2024 Fonticons, Inc.--><path d="M137.4 374.6c12.5 12.5 32.8 12.5 45.3 0l128-128c9.2-9.2 11.9-22.9 6.9-34.9s-16.6-19.8-29.6-19.8L32 192c-12.9 0-24.6 7.8-29.6 19.8s-2.2 25.7 6.9 34.9l128 128z"/></svg><span class="reveal-trigger-label" data-reveal-text="Open abstract" data-reveal-label-alt="Close abstract" data-link-purpose-append="Regulation of Ion Concentration and Deposit Shape in Liquid-Mask Electrodeposition with Bipolar Pulse Current" data-link-purpose-append-open="Regulation of Ion Concentration and Deposit Shape in Liquid-Mask Electrodeposition with Bipolar Pulse Current">Open abstract</span></button></div><div class="reveal-content"><div class="article-text view-text-small">
						<p>This study proposes a bipolar pulse current (BPC)-assisted liquid-mask electrodeposition method to improve deposit flatness by regulating interfacial ion transport. Numerical simulations were employed to analyze Cu2+ concentration fields, time-averaged deposition rates, and thickness evolution in direct current, single pulse current (SPC), and BPC modes. The results show that SPC with pulse period of 100 ms and duty cycle of 25% alleviates concentration polarization and reduces non-uniform growth, yet residual profile unevenness persists due to the lack of an active leveling mechanism. BPC further refines the deposit profile through reverse anodic dissolution, where the morphology depends not only on the reverse-to-forward charge ratio λ, but also on the distribution of reverse charge between current amplitude and pulse duration. At identical λ values, low-current/long-duration combinations cause more pronounced edge recession and may extend excessive dissolution toward the deposit center. Among the conditions tested, the optimal flatness was achieved at reverse current of 0.2 mA and reverse duty cycle of 15% (λ=0.30), yielding an edge-to-center height difference of 2.1 μm and a surface roughness of 0.29 μm. Using these optimized parameters, a continuous 3000 μm long copper line was fabricated, demonstrating the feasibility of the proposed strategy for continuous-path deposition.</p>
					</div><div class="art-list-item-tools small wd-abstr-lower"><a class="mr-2" href="https://doi.org/10.1149/1945-7111/aeb62f">https://doi.org/10.1149/1945-7111/aeb62f</a></div></div></li></ul><!-- End AM list content --><p><a href="/journal/1945-7111/acceptedmanuscripts/1">More Accepted manuscripts</a></p><!--    accepted manuscript listing end--></div></div></div><!-- End AM tabpanel --><!-- Start Trending tabpanel --><div tabindex="0"
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                    Open all abstracts<span class="offscreen-hidden">,&nbsp;in this tab</span></button></p><!--    articleEntryList start--><ul class="art-list"><li class="art-list-item reveal-container reveal-closed"><div class="eyebrow"><span class="offscreen-hidden">The following article is </span><span class="red">Open access</span></div><a href="/article/10.1149/1945-7111/aeab15" class="art-list-item-title event_main-link">In Situ and Operando Neutron Powder Diffraction of Na<i><sub>x</sub></i>NiO<sub>2</sub>: A Case Study for Sodium-Ion Batteries</a><p class="small art-list-item-meta">James M. A. Steele <em>et al</em> 2026 <em>J. Electrochem. Soc.</em> <b>173</b> 200513 </p><div class="art-list-item-tools small wd-abstr-upper"><a href="/article/10.1149/1945-7111/aeab15/meta" class="mr-2 mb-0 nowrap event_mini-link" data-event-action="View article"><span class="icon-article"></span>View article<span class="offscreen-hidden">,&nbsp;In Situ and Operando Neutron Powder Diffraction of NaxNiO2: A Case Study for Sodium-Ion Batteries</span></a><a href="/article/10.1149/1945-7111/aeab15/pdf" class="mr-2 mb-0 nowrap event_mini-link" data-event-action="PDF"><span class="icon-file-pdf"></span>PDF<span class="offscreen-hidden">,&nbsp;In Situ and Operando Neutron Powder Diffraction of NaxNiO2: A Case Study for Sodium-Ion Batteries</span></a><button type="button" class="reveal-trigger mr-2 nowrap"><svg aria-hidden="true" class="fa-icon fa-icon--left fa-icon--flip" role="img" focusable="false" xmlns="http://www.w3.org/2000/svg" viewBox="0 0 320 512"><!--caret-down--><!--!Font Awesome Free 6.5.1 by @fontawesome - https://fontawesome.com License - https://fontawesome.com/license/free Copyright 2024 Fonticons, Inc.--><path d="M137.4 374.6c12.5 12.5 32.8 12.5 45.3 0l128-128c9.2-9.2 11.9-22.9 6.9-34.9s-16.6-19.8-29.6-19.8L32 192c-12.9 0-24.6 7.8-29.6 19.8s-2.2 25.7 6.9 34.9l128 128z"/></svg><span class="reveal-trigger-label" data-reveal-text="Open abstract" data-reveal-label-alt="Close abstract" data-link-purpose-append="In Situ and Operando Neutron Powder Diffraction of NaxNiO2: A Case Study for Sodium-Ion Batteries" data-link-purpose-append-open="In Situ and Operando Neutron Powder Diffraction of NaxNiO2: A Case Study for Sodium-Ion Batteries">Open abstract</span></button></div><div class="reveal-content"><div class="article-text view-text-small"><p>Neutron powder diffraction (NPD) is a non-destructive technique uniquely suited to investigating industrially relevant sodium-ion cathode materials. Unlike X–ray diffraction, it offers excellent contrast between neighbouring transition metal ions and is sensitive to lighter elements such as O/Na, which are key to revealing superstructural orderings characteristic of sodium cathodes. However, in situ/operando NPD battery studies are hindered by sample quantity requirements, and lack of suitable sample environments. Using a cell developed at ISIS Neutron and Muon Source, we observed no detrimental effects from prolonged vacuum exposure required for Time-of-Flight NPD. We collect/analyse data in two modes: operando<i>,</i> in which the electrochemical structural evolution is tracked, and in situ, wherein higher signal-to-noise data is collected during voltage holds, for phase-pure samples at set voltage cutoffs. Using Na<sub><i>x</i></sub>NiO<sub>2</sub> as a model system, we present a methodology to account for the complex background profile characteristic of electrochemical environments enabling, for the first time, quantitative Rietveld refinements against in situ electrochemical NPD, and providing a systematic framework for future studies. Structural models are refined against in situ data and benchmarked against combined refinement of ex situ SXRD/NPD measurements. This work unlocks potential for previously inaccessible insights into structure-property relationships and degradation, helping to facilitate the development of next-generation cathodes with enhanced useful lifetime, capacity, and performance.</p><h2 id="artAbst2" class="collapse-blocked"></h2><p><span style="display: none;">figure placeholder</span></p><h2 id="artAbst3" class="collapse-blocked">Highlights</h2><p><ul><li><p>Case study for neutron diffraction on battery cathode materials during operation</p></li><li><p>Complex electrochemical cell background accounted for via post-cycling measurement</p></li><li><p>Quantitative Rietveld refinement provided insight into structural phase transitions</p></li></ul></p></div><div class="art-list-item-tools small wd-abstr-lower"><a class="mr-2" href="https://doi.org/10.1149/1945-7111/aeab15">https://doi.org/10.1149/1945-7111/aeab15</a></div></div></li><li class="art-list-item reveal-container reveal-closed"><div class="eyebrow"><span class="offscreen-hidden">The following article is </span><span class="red">Open access</span></div><a href="/article/10.1149/1945-7111/aeb444" class="art-list-item-title event_main-link">Localized Corrosion Susceptibility of Hypoeutectic Al–Ce Alloy Castings</a><p class="small art-list-item-meta">A. C. Abraham <em>et al</em> 2026 <em>J. Electrochem. Soc.</em> <b>173</b> 201502 </p><div class="art-list-item-tools small wd-abstr-upper"><a href="/article/10.1149/1945-7111/aeb444/meta" class="mr-2 mb-0 nowrap event_mini-link" data-event-action="View article"><span class="icon-article"></span>View article<span class="offscreen-hidden">,&nbsp;Localized Corrosion Susceptibility of Hypoeutectic Al–Ce Alloy Castings</span></a><a href="/article/10.1149/1945-7111/aeb444/pdf" class="mr-2 mb-0 nowrap event_mini-link" data-event-action="PDF"><span class="icon-file-pdf"></span>PDF<span class="offscreen-hidden">,&nbsp;Localized Corrosion Susceptibility of Hypoeutectic Al–Ce Alloy Castings</span></a><button type="button" class="reveal-trigger mr-2 nowrap"><svg aria-hidden="true" class="fa-icon fa-icon--left fa-icon--flip" role="img" focusable="false" xmlns="http://www.w3.org/2000/svg" viewBox="0 0 320 512"><!--caret-down--><!--!Font Awesome Free 6.5.1 by @fontawesome - https://fontawesome.com License - https://fontawesome.com/license/free Copyright 2024 Fonticons, Inc.--><path d="M137.4 374.6c12.5 12.5 32.8 12.5 45.3 0l128-128c9.2-9.2 11.9-22.9 6.9-34.9s-16.6-19.8-29.6-19.8L32 192c-12.9 0-24.6 7.8-29.6 19.8s-2.2 25.7 6.9 34.9l128 128z"/></svg><span class="reveal-trigger-label" data-reveal-text="Open abstract" data-reveal-label-alt="Close abstract" data-link-purpose-append="Localized Corrosion Susceptibility of Hypoeutectic Al–Ce Alloy Castings" data-link-purpose-append-open="Localized Corrosion Susceptibility of Hypoeutectic Al–Ce Alloy Castings">Open abstract</span></button></div><div class="reveal-content"><div class="article-text view-text-small"><p>Hypoeutectic Al–Ce alloys provide improved mechanical strength retention at elevated temperatures relative to other Al alloy cast alloys. However, broader applications, particularly those related to automotive assembly, require demonstrated aqueous corrosion performance. The purpose of this work was to determine the localized corrosion susceptibility of a hypoeutectic Al-6Ce alloy, relative to a hypoeutectic Al–Si alloy (A356), in NaCl (aq). Conventional electrochemical polarization and bulk immersion (ASTM G110) testing, coupled with scanning electron microscopy were used for this purpose. The Al-6Ce alloy exhibited significantly lower localized corrosion susceptibility as determined by ASTM G110 testing. Electrochemical polarization measurements reveal that the lower susceptibility is likely related to the micro-galvanic coupling between the anodic Al<sub>11</sub>Ce<sub>3</sub> eutectic phase and the adjacent cathodic primary Al dendritic phase, which is not sufficiently polarizing to induce passivity breakdown of the anodic Al<sub>11</sub>Ce<sub>3</sub> eutectic phase. The implications of the results are discussed within the context of materials performance in automotive applications.</p><h2 id="artAbst2" class="collapse-blocked"></h2><p><span style="display: none;">figure placeholder</span></p></div><div class="art-list-item-tools small wd-abstr-lower"><a class="mr-2" href="https://doi.org/10.1149/1945-7111/aeb444">https://doi.org/10.1149/1945-7111/aeb444</a></div></div></li><li class="art-list-item reveal-container reveal-closed"><div class="eyebrow"><span class="offscreen-hidden">The following article is </span><span class="red">Open access</span></div><a href="/article/10.1149/1945-7111/aeb7d2" class="art-list-item-title event_main-link">Free Ionomer Controls Adsorption in Electrolyzer Inks</a><p class="small art-list-item-meta">Maximilian Enis Degirmenci <em>et al</em> 2026 <em>J. Electrochem. Soc.</em> <b></b>  </p><div class="art-list-item-tools small wd-abstr-upper"><a href="/article/10.1149/1945-7111/aeb7d2/meta" class="mr-2 mb-0 nowrap event_mini-link" data-event-action="View article"><span class="icon-article"></span>View article<span class="offscreen-hidden">,&nbsp;Free Ionomer Controls Adsorption in Electrolyzer Inks</span></a><a href="/article/10.1149/1945-7111/aeb7d2/pdf" class="mr-2 mb-0 nowrap event_mini-link" data-event-action="PDF"><span class="icon-file-pdf"></span>PDF<span class="offscreen-hidden">,&nbsp;Free Ionomer Controls Adsorption in Electrolyzer Inks</span></a><button type="button" class="reveal-trigger mr-2 nowrap"><svg aria-hidden="true" class="fa-icon fa-icon--left fa-icon--flip" role="img" focusable="false" xmlns="http://www.w3.org/2000/svg" viewBox="0 0 320 512"><!--caret-down--><!--!Font Awesome Free 6.5.1 by @fontawesome - https://fontawesome.com License - https://fontawesome.com/license/free Copyright 2024 Fonticons, Inc.--><path d="M137.4 374.6c12.5 12.5 32.8 12.5 45.3 0l128-128c9.2-9.2 11.9-22.9 6.9-34.9s-16.6-19.8-29.6-19.8L32 192c-12.9 0-24.6 7.8-29.6 19.8s-2.2 25.7 6.9 34.9l128 128z"/></svg><span class="reveal-trigger-label" data-reveal-text="Open abstract" data-reveal-label-alt="Close abstract" data-link-purpose-append="Free Ionomer Controls Adsorption in Electrolyzer Inks" data-link-purpose-append-open="Free Ionomer Controls Adsorption in Electrolyzer Inks">Open abstract</span></button></div><div class="reveal-content"><div class="article-text view-text-small"><p>The ionomer/catalyst interface in proton-exchange-membrane water-electrolyzer (PEMWE) anode catalyst layers governs multi-species transport and reaction kinetics, and originates from ionomer adsorption onto catalyst particles during ink formation. These inks contain iridium oxide (IrOx) catalyst and PEM ionomer (typically perfluorosulfonic acid, PFSA) dispersed in water:alcohol solvent mixtures, deposited to form the catalyst layer upon solvent evaporation. Despite the importance of ink formulation controlling ionomer adsorption, a systematic investigation spanning industrially relevant formulations (including concentrated inks used in roll-to-roll manufacturing) is missing. Here, we investigate the influence of IrOx concentration, ionomer-to-catalyst (I:C) ratio, and solvent composition on PFSA adsorption using thermal gravimetric analysis. PFSA adsorption is independent of IrOx concentration, being instead determined by free-ionomer concentration and solvent identity, across both dilute and concentrated inks. We further show that I:C ratio is a poor descriptor, with free-ionomer weight percentage providing a more meaningful metric that collapses adsorption data onto a single isotherm. In water-rich solvents, adsorption is primarily limited by electrostatic repulsion, whereas, in alcohol-rich solvents, solvation forces and surface-coverage effects dominate. We additionally characterize ink stability (sedimentation, x-ray scattering) and single-cell performance. These results extend to PFSA-based catalyst inks (including high-surface-area carbons), offering practical implications for ink formulation across deposition methods.</p></div><div class="art-list-item-tools small wd-abstr-lower"><a class="mr-2" href="https://doi.org/10.1149/1945-7111/aeb7d2">https://doi.org/10.1149/1945-7111/aeb7d2</a></div></div></li><li class="art-list-item reveal-container reveal-closed"><div class="eyebrow"><span class="offscreen-hidden">The following article is </span><span class="red">Open access</span></div><a href="/article/10.1149/1945-7111/aeae76" class="art-list-item-title event_main-link">A Particle-Based Model for Optimization of Lithium-Ion Battery Electrodes</a><p class="small art-list-item-meta">Giuliano Lombardo <em>et al</em> 2026 <em>J. Electrochem. Soc.</em> <b>173</b> 200510 </p><div class="art-list-item-tools small wd-abstr-upper"><a href="/article/10.1149/1945-7111/aeae76/meta" class="mr-2 mb-0 nowrap event_mini-link" data-event-action="View article"><span class="icon-article"></span>View article<span class="offscreen-hidden">,&nbsp;A Particle-Based Model for Optimization of Lithium-Ion Battery Electrodes</span></a><a href="/article/10.1149/1945-7111/aeae76/pdf" class="mr-2 mb-0 nowrap event_mini-link" data-event-action="PDF"><span class="icon-file-pdf"></span>PDF<span class="offscreen-hidden">,&nbsp;A Particle-Based Model for Optimization of Lithium-Ion Battery Electrodes</span></a><button type="button" class="reveal-trigger mr-2 nowrap"><svg aria-hidden="true" class="fa-icon fa-icon--left fa-icon--flip" role="img" focusable="false" xmlns="http://www.w3.org/2000/svg" viewBox="0 0 320 512"><!--caret-down--><!--!Font Awesome Free 6.5.1 by @fontawesome - https://fontawesome.com License - https://fontawesome.com/license/free Copyright 2024 Fonticons, Inc.--><path d="M137.4 374.6c12.5 12.5 32.8 12.5 45.3 0l128-128c9.2-9.2 11.9-22.9 6.9-34.9s-16.6-19.8-29.6-19.8L32 192c-12.9 0-24.6 7.8-29.6 19.8s-2.2 25.7 6.9 34.9l128 128z"/></svg><span class="reveal-trigger-label" data-reveal-text="Open abstract" data-reveal-label-alt="Close abstract" data-link-purpose-append="A Particle-Based Model for Optimization of Lithium-Ion Battery Electrodes" data-link-purpose-append-open="A Particle-Based Model for Optimization of Lithium-Ion Battery Electrodes">Open abstract</span></button></div><div class="reveal-content"><div class="article-text view-text-small"><p>For the optimization of electrode structures, a predictive modeling framework is desirable. So-called first-principles models address this requirement by incorporating experimentally characterized material properties. Together with a fully resolved digital representation of the electrode structure, first-principles models provide excellent prediction accuracy and remain predictive for changing geometries. However, their high computational cost makes them unsuitable for electrode optimization. To overcome this limitation, we employ a previously derived 1D particle-based model which reduces the fully resolved model across two scales: porous electrode level and particle level. The model combines effective transport properties at the porous electrode level with a time-dependent, particle-based description that accounts for single-particle morphology. We present a workflow for the full parameterization of the 1D particle-based model using a graphite half-cell. Material properties and the reconstructed electrode structure are obtained from experimental characterization, from which the effective transport properties can be derived. The particle-based properties are obtained from fully resolved first-principles simulations of single particles. Validation of the 1D particle-based model indicates prediction errors comparable to or lower than those of the P2D model. Due to its first-principles-based parameters, which incorporate real particle morphology without empirical fitting, the proposed framework is well-suited for predictive optimization of electrode structures.</p><h2 id="artAbst2" class="collapse-blocked"></h2><p><span style="display: none;">figure placeholder</span></p><h2 id="artAbst3" class="collapse-blocked">Highlights</h2><p><ul><li><p>First-principles modeling enables predictive optimization of electrode structure</p></li><li><p>Model reduction is applied at two scales: porous electrode and individual particle</p></li><li><p>Imaging and experiments allow model parameterization without empirical fitting</p></li><li><p>First-principles, single-particle simulation captures effect of real particle shape</p></li><li><p>Prediction errors are comparable to or lower than those of the state-of-the-art</p></li></ul></p></div><div class="art-list-item-tools small wd-abstr-lower"><a class="mr-2" href="https://doi.org/10.1149/1945-7111/aeae76">https://doi.org/10.1149/1945-7111/aeae76</a></div></div></li><li class="art-list-item reveal-container reveal-closed"><div class="eyebrow"><span class="offscreen-hidden">The following article is </span><span class="red">Open access</span></div><a href="/article/10.1149/1945-7111/aeb335" class="art-list-item-title event_main-link">Probing The Limits Of Closing The H<sub>2</sub> And O<sub>2</sub> Molar Flow Balance In PEM Water Electrolysis</a><p class="small art-list-item-meta">Ricardo Duarte <em>et al</em> 2026 <em>J. Electrochem. Soc.</em> <b>173</b> 204503 </p><div class="art-list-item-tools small wd-abstr-upper"><a href="/article/10.1149/1945-7111/aeb335/meta" class="mr-2 mb-0 nowrap event_mini-link" data-event-action="View article"><span class="icon-article"></span>View article<span class="offscreen-hidden">,&nbsp;Probing The Limits Of Closing The H2 And O2 Molar Flow Balance In PEM Water Electrolysis</span></a><a href="/article/10.1149/1945-7111/aeb335/pdf" class="mr-2 mb-0 nowrap event_mini-link" data-event-action="PDF"><span class="icon-file-pdf"></span>PDF<span class="offscreen-hidden">,&nbsp;Probing The Limits Of Closing The H2 And O2 Molar Flow Balance In PEM Water Electrolysis</span></a><button type="button" class="reveal-trigger mr-2 nowrap"><svg aria-hidden="true" class="fa-icon fa-icon--left fa-icon--flip" role="img" focusable="false" xmlns="http://www.w3.org/2000/svg" viewBox="0 0 320 512"><!--caret-down--><!--!Font Awesome Free 6.5.1 by @fontawesome - https://fontawesome.com License - https://fontawesome.com/license/free Copyright 2024 Fonticons, Inc.--><path d="M137.4 374.6c12.5 12.5 32.8 12.5 45.3 0l128-128c9.2-9.2 11.9-22.9 6.9-34.9s-16.6-19.8-29.6-19.8L32 192c-12.9 0-24.6 7.8-29.6 19.8s-2.2 25.7 6.9 34.9l128 128z"/></svg><span class="reveal-trigger-label" data-reveal-text="Open abstract" data-reveal-label-alt="Close abstract" data-link-purpose-append="Probing The Limits Of Closing The H2 And O2 Molar Flow Balance In PEM Water Electrolysis" data-link-purpose-append-open="Probing The Limits Of Closing The H2 And O2 Molar Flow Balance In PEM Water Electrolysis">Open abstract</span></button></div><div class="reveal-content"><div class="article-text view-text-small"><p>A deeper fundamental understanding of hydrogen and oxygen production, transport, and reaction rates within polymer electrolyte membrane water electrolysis (PEMWE) systems is needed to better optimize membrane design and improve commercial viability. This work closes the molar flow balance of hydrogen and oxygen leaving operating PEMWE cells through quantification of anode and cathode exhaust flows. It quantifies recombination reactions occurring within the cell and probes the measurement accuracy of these measurements through observed standard deviation and error propagation theory. Through rigorous effort, we have shown the ability to close the molar flow balance to within + /− 0.5% of the total cell current, a value that enables accurate quantification of hydrogen recovery efficiency for cathode pressures up to 30 bar and current densities up to 4 A cm<sup>−2</sup>. Recombined and lost hydrogen have also been quantified from these measurements but with higher measurement uncertainty. The cell performance values reported, and the techniques used to obtain them will be of significant value in optimizing membrane design for PEMWE operation.</p><h2 id="artAbst2" class="collapse-blocked"></h2><p><span style="display: none;">figure placeholder</span></p></div><div class="art-list-item-tools small wd-abstr-lower"><a class="mr-2" href="https://doi.org/10.1149/1945-7111/aeb335">https://doi.org/10.1149/1945-7111/aeb335</a></div></div></li><li class="art-list-item reveal-container reveal-closed"><div class="eyebrow"><span class="offscreen-hidden">The following article is </span><span class="red">Open access</span></div><a href="/article/10.1149/1945-7111/aeb765" class="art-list-item-title event_main-link">Resolving Electron-Transfer Heterogeneity in Electrochemical Aptamer-Based Sensors by Distribution of Capacitance Timescales</a><p class="small art-list-item-meta">Bob Lansdorp <em>et al</em> 2026 <em>J. Electrochem. Soc.</em> <b></b>  </p><div class="art-list-item-tools small wd-abstr-upper"><a href="/article/10.1149/1945-7111/aeb765/meta" class="mr-2 mb-0 nowrap event_mini-link" data-event-action="View article"><span class="icon-article"></span>View article<span class="offscreen-hidden">,&nbsp;Resolving Electron-Transfer Heterogeneity in Electrochemical Aptamer-Based Sensors by Distribution of Capacitance Timescales</span></a><a href="/article/10.1149/1945-7111/aeb765/pdf" class="mr-2 mb-0 nowrap event_mini-link" data-event-action="PDF"><span class="icon-file-pdf"></span>PDF<span class="offscreen-hidden">,&nbsp;Resolving Electron-Transfer Heterogeneity in Electrochemical Aptamer-Based Sensors by Distribution of Capacitance Timescales</span></a><button type="button" class="reveal-trigger mr-2 nowrap"><svg aria-hidden="true" class="fa-icon fa-icon--left fa-icon--flip" role="img" focusable="false" xmlns="http://www.w3.org/2000/svg" viewBox="0 0 320 512"><!--caret-down--><!--!Font Awesome Free 6.5.1 by @fontawesome - https://fontawesome.com License - https://fontawesome.com/license/free Copyright 2024 Fonticons, Inc.--><path d="M137.4 374.6c12.5 12.5 32.8 12.5 45.3 0l128-128c9.2-9.2 11.9-22.9 6.9-34.9s-16.6-19.8-29.6-19.8L32 192c-12.9 0-24.6 7.8-29.6 19.8s-2.2 25.7 6.9 34.9l128 128z"/></svg><span class="reveal-trigger-label" data-reveal-text="Open abstract" data-reveal-label-alt="Close abstract" data-link-purpose-append="Resolving Electron-Transfer Heterogeneity in Electrochemical Aptamer-Based Sensors by Distribution of Capacitance Timescales" data-link-purpose-append-open="Resolving Electron-Transfer Heterogeneity in Electrochemical Aptamer-Based Sensors by Distribution of Capacitance Timescales">Open abstract</span></button></div><div class="reveal-content"><div class="article-text view-text-small"><p>Distribution of timescales methods have become powerful tools for extracting hidden kinetic processes from electrochemical impedance spectra. Their physical interpretation, however, depends critically on matching the assumed mathematical model to the underlying physical electrochemical system. Here, we show that the Distribution of Capacitive Times (DCT) model is well-matched to the physics of surface-immobilized redox systems, enabling electron-transfer rate heterogeneity to be resolved. This makes electrochemical aptamer-based (EAB) sensors a natural system for DCT analysis, as their surface-tethered redox reporters can occupy distinct molecular states with different electron-transfer kinetics. Applying DCT to a vancomycin EAB biosensor reveals two distinct electron-transfer populations whose respective rates remain nearly constant as a function of vancomycin concentration. In contrast, their relative occupancies evolve with changing target concentration, demonstrating that the sensor’s response arises from redistribution between states rather than from a continuously varying electron-transfer rate. Analysis of the population amplitudes is consistent with a biophysical model in which approximately one-third of the surface-bound aptamers do not respond to target, suggesting an area that can be explored to improve the performance of such sensors. These results demonstrate that DCT analysis can uncover mechanistic insights in surface-immobilized redox systems that are inaccessible to conventional impedance analysis.</p></div><div class="art-list-item-tools small wd-abstr-lower"><a class="mr-2" href="https://doi.org/10.1149/1945-7111/aeb765">https://doi.org/10.1149/1945-7111/aeb765</a></div></div></li><li class="art-list-item reveal-container reveal-closed"><div class="eyebrow"><span class="offscreen-hidden">The following article is </span><span class="red">Open access</span></div><a href="/article/10.1149/1945-7111/aeb766" class="art-list-item-title event_main-link">Part II. Matched Asymptotics Analysis for a Lithium-Ion Battery with a Torn Negative-Electrode Tab Elucidating the Impact of Free-Electrolyte Reservoirs on Lithium Plating Initiation During Discharge</a><p class="small art-list-item-meta">Daniel R. Baker and Mark Verbrugge 2026 <em>J. Electrochem. Soc.</em> <b></b>  </p><div class="art-list-item-tools small wd-abstr-upper"><a href="/article/10.1149/1945-7111/aeb766/meta" class="mr-2 mb-0 nowrap event_mini-link" data-event-action="View article"><span class="icon-article"></span>View article<span class="offscreen-hidden">,&nbsp;Part II. Matched Asymptotics Analysis for a Lithium-Ion Battery with a Torn Negative-Electrode Tab Elucidating the Impact of Free-Electrolyte Reservoirs on Lithium Plating Initiation During Discharge</span></a><a href="/article/10.1149/1945-7111/aeb766/pdf" class="mr-2 mb-0 nowrap event_mini-link" data-event-action="PDF"><span class="icon-file-pdf"></span>PDF<span class="offscreen-hidden">,&nbsp;Part II. Matched Asymptotics Analysis for a Lithium-Ion Battery with a Torn Negative-Electrode Tab Elucidating the Impact of Free-Electrolyte Reservoirs on Lithium Plating Initiation During Discharge</span></a><button type="button" class="reveal-trigger mr-2 nowrap"><svg aria-hidden="true" class="fa-icon fa-icon--left fa-icon--flip" role="img" focusable="false" xmlns="http://www.w3.org/2000/svg" viewBox="0 0 320 512"><!--caret-down--><!--!Font Awesome Free 6.5.1 by @fontawesome - https://fontawesome.com License - https://fontawesome.com/license/free Copyright 2024 Fonticons, Inc.--><path d="M137.4 374.6c12.5 12.5 32.8 12.5 45.3 0l128-128c9.2-9.2 11.9-22.9 6.9-34.9s-16.6-19.8-29.6-19.8L32 192c-12.9 0-24.6 7.8-29.6 19.8s-2.2 25.7 6.9 34.9l128 128z"/></svg><span class="reveal-trigger-label" data-reveal-text="Open abstract" data-reveal-label-alt="Close abstract" data-link-purpose-append="Part II. Matched Asymptotics Analysis for a Lithium-Ion Battery with a Torn Negative-Electrode Tab Elucidating the Impact of Free-Electrolyte Reservoirs on Lithium Plating Initiation During Discharge" data-link-purpose-append-open="Part II. Matched Asymptotics Analysis for a Lithium-Ion Battery with a Torn Negative-Electrode Tab Elucidating the Impact of Free-Electrolyte Reservoirs on Lithium Plating Initiation During Discharge">Open abstract</span></button></div><div class="reveal-content"><div class="article-text view-text-small"><p>In Part 1 of this work [J. Electrochem. Soc., 173 (2026) 100506], a perturbation analysis was introduced to describe how lithium plating can occur during discharge in a two-cell stack featuring a broken negative-electrode tab. Assuming a large electrolyte reservoir adjacent to the cell stack, we demonstrated that current flows through the reservoir from the functioning cell into the tab-compromised cell, leading to plating during cell discharge. Because this reservoir also supplies excess electrolyte over the battery's operational life, which can be consumed over time if there is electrolyte decomposition upon cell cycling, its thickness represents a key design parameter. In this work, matched asymptotic expansions are employed to determine how small the reservoir thickness must be to hinder current flow and delay the onset of plating following a tab failure. Our results indicate that preventing plating during discharge of a cell with a torn negative-electrode tab requires a reservoir thickness so small that it precludes maintaining any significant supply of excess electrolyte, leading to so-called dry-cell constructions.</p></div><div class="art-list-item-tools small wd-abstr-lower"><a class="mr-2" href="https://doi.org/10.1149/1945-7111/aeb766">https://doi.org/10.1149/1945-7111/aeb766</a></div></div></li><li class="art-list-item reveal-container reveal-closed"><div class="eyebrow"><span class="offscreen-hidden">The following article is </span><span class="red">Open access</span></div><a href="/article/10.1149/1945-7111/aeb574" class="art-list-item-title event_main-link">Electrolyte Volume and Pore Filling Ratio Evolution during Calendar Aging of 4695 Lithium-Ion Batteries</a><p class="small art-list-item-meta">Cara Zimmermann <em>et al</em> 2026 <em>J. Electrochem. Soc.</em> <b></b>  </p><div class="art-list-item-tools small wd-abstr-upper"><a href="/article/10.1149/1945-7111/aeb574/meta" class="mr-2 mb-0 nowrap event_mini-link" data-event-action="View article"><span class="icon-article"></span>View article<span class="offscreen-hidden">,&nbsp;Electrolyte Volume and Pore Filling Ratio Evolution during Calendar Aging of 4695 Lithium-Ion Batteries</span></a><a href="/article/10.1149/1945-7111/aeb574/pdf" class="mr-2 mb-0 nowrap event_mini-link" data-event-action="PDF"><span class="icon-file-pdf"></span>PDF<span class="offscreen-hidden">,&nbsp;Electrolyte Volume and Pore Filling Ratio Evolution during Calendar Aging of 4695 Lithium-Ion Batteries</span></a><button type="button" class="reveal-trigger mr-2 nowrap"><svg aria-hidden="true" class="fa-icon fa-icon--left fa-icon--flip" role="img" focusable="false" xmlns="http://www.w3.org/2000/svg" viewBox="0 0 320 512"><!--caret-down--><!--!Font Awesome Free 6.5.1 by @fontawesome - https://fontawesome.com License - https://fontawesome.com/license/free Copyright 2024 Fonticons, Inc.--><path d="M137.4 374.6c12.5 12.5 32.8 12.5 45.3 0l128-128c9.2-9.2 11.9-22.9 6.9-34.9s-16.6-19.8-29.6-19.8L32 192c-12.9 0-24.6 7.8-29.6 19.8s-2.2 25.7 6.9 34.9l128 128z"/></svg><span class="reveal-trigger-label" data-reveal-text="Open abstract" data-reveal-label-alt="Close abstract" data-link-purpose-append="Electrolyte Volume and Pore Filling Ratio Evolution during Calendar Aging of 4695 Lithium-Ion Batteries" data-link-purpose-append-open="Electrolyte Volume and Pore Filling Ratio Evolution during Calendar Aging of 4695 Lithium-Ion Batteries">Open abstract</span></button></div><div class="reveal-content"><div class="article-text view-text-small"><p>Electrolyte depletion is a key driver of late-life rollover in lithium-ion batteries. However, quantitative tracking of electrolyte evolution during calendar aging remains challenging. In this study, the electrochemical aging behavior, electrolyte volume, pore volume, and pore filling ratio (PFR) evolution of automotive prototype 4695 cells (Ni-rich NMC || graphite–Si/C) are investigated during 300 days of accelerated storage at 55 °C &amp; 100% SoC, 55 °C &amp; 80% SoC, and 45 °C &amp; 100% SoC. A combined approach employing periodic moment-of-inertia measurements, CT-derived jelly-roll geometry analysis, porosity measurements, and degradation-mode analysis is applied. Elevated-temperature storage results in enhanced capacity fade and resistance growth, while storage at both high temperature and high SoC additionally promotes cathode-related degradation and conducting salt depletion. In contrast, all storage conditions exhibit similar electrolyte volume losses and PFR reductions at 100% SoC. The electrolyte consumption rate, defined as electrolyte volume loss per C/20 capacity loss, is highest at 45 °C, indicating that capacity fade at 55 °C involves a larger contribution from degradation mechanisms not associated with electrolyte consumption. Consequently, electrolyte volume loss and PFR evolution cannot be directly correlated with capacity fade during calendar aging.</p></div><div class="art-list-item-tools small wd-abstr-lower"><a class="mr-2" href="https://doi.org/10.1149/1945-7111/aeb574">https://doi.org/10.1149/1945-7111/aeb574</a></div></div></li><li class="art-list-item reveal-container reveal-closed"><div class="eyebrow"><span class="offscreen-hidden">The following article is </span><span class="red">Open access</span></div><a href="/article/10.1149/1945-7111/aeb575" class="art-list-item-title event_main-link">Investigation of the Local Cathode Potential Evolution during Start-up by Means of Embedded Reference Electrodes in a PEM Fuel Cell</a><p class="small art-list-item-meta">Dietmar Gerteisen <em>et al</em> 2026 <em>J. Electrochem. Soc.</em> <b></b>  </p><div class="art-list-item-tools small wd-abstr-upper"><a href="/article/10.1149/1945-7111/aeb575/meta" class="mr-2 mb-0 nowrap event_mini-link" data-event-action="View article"><span class="icon-article"></span>View article<span class="offscreen-hidden">,&nbsp;Investigation of the Local Cathode Potential Evolution during Start-up by Means of Embedded Reference Electrodes in a PEM Fuel Cell</span></a><a href="/article/10.1149/1945-7111/aeb575/pdf" class="mr-2 mb-0 nowrap event_mini-link" data-event-action="PDF"><span class="icon-file-pdf"></span>PDF<span class="offscreen-hidden">,&nbsp;Investigation of the Local Cathode Potential Evolution during Start-up by Means of Embedded Reference Electrodes in a PEM Fuel Cell</span></a><button type="button" class="reveal-trigger mr-2 nowrap"><svg aria-hidden="true" class="fa-icon fa-icon--left fa-icon--flip" role="img" focusable="false" xmlns="http://www.w3.org/2000/svg" viewBox="0 0 320 512"><!--caret-down--><!--!Font Awesome Free 6.5.1 by @fontawesome - https://fontawesome.com License - https://fontawesome.com/license/free Copyright 2024 Fonticons, Inc.--><path d="M137.4 374.6c12.5 12.5 32.8 12.5 45.3 0l128-128c9.2-9.2 11.9-22.9 6.9-34.9s-16.6-19.8-29.6-19.8L32 192c-12.9 0-24.6 7.8-29.6 19.8s-2.2 25.7 6.9 34.9l128 128z"/></svg><span class="reveal-trigger-label" data-reveal-text="Open abstract" data-reveal-label-alt="Close abstract" data-link-purpose-append="Investigation of the Local Cathode Potential Evolution during Start-up by Means of Embedded Reference Electrodes in a PEM Fuel Cell" data-link-purpose-append-open="Investigation of the Local Cathode Potential Evolution during Start-up by Means of Embedded Reference Electrodes in a PEM Fuel Cell">Open abstract</span></button></div><div class="reveal-content"><div class="article-text view-text-small"><p>Air-air start-up (SU) events in proton exchange membrane fuel cells generate cathode potential overshoots exceeding 1.4 V, driving degradation through carbon corrosion and platinum dissolution. While the reverse-current mechanism is established, the influence of system-level pre-conditioning parameters on spatially resolved cathode potential transients remains insufficiently understood. This study employs a segmented along-the-channel cell with ten air-flushed reference electrodes to measure local cathode potentials during air-air SU events. Hydrogen flow rate and pre-conditioning parameters such as anode/cathode humidity and purge duration are investigated. Increasing hydrogen flow from 0.125 to 4 nL/min reduces SU duration (276 to 163 ms) and peak overshoot (1.56 to 1.45 V), though the effect does not scale linearly with residence time, indicating electrochemical process dominance. Anode humidity exerts minimal influence when the cathode remains fully humidified. In contrast, cathode dehydration fundamentally alters transient behavior: peak overshoots at the anode outlet decrease, while inlet segments develop pronounced overshoots with markedly slower decay rates. This is attributed to increased ohmic resistance and reduced double-layer capacitance under dehydrated conditions. The findings reveal that cathode hydration critically governs SU-induced degradation and that dehydration strategies may prolong exposure to corrosive potentials, providing guidance for optimizing shutdown protocols in automotive applications.</p></div><div class="art-list-item-tools small wd-abstr-lower"><a class="mr-2" href="https://doi.org/10.1149/1945-7111/aeb575">https://doi.org/10.1149/1945-7111/aeb575</a></div></div></li><li class="art-list-item reveal-container reveal-closed"><div class="eyebrow"><span class="offscreen-hidden">The following article is </span><span class="red">Open access</span></div><a href="/article/10.1149/1945-7111/aeb578" class="art-list-item-title event_main-link">Cell Format Dependent Cyclic and Calendar Aging of Lithium-Ion Cells: A Comparison of Coin and Pouch Cells</a><p class="small art-list-item-meta">Kai Büscher <em>et al</em> 2026 <em>J. Electrochem. Soc.</em> <b></b>  </p><div class="art-list-item-tools small wd-abstr-upper"><a href="/article/10.1149/1945-7111/aeb578/meta" class="mr-2 mb-0 nowrap event_mini-link" data-event-action="View article"><span class="icon-article"></span>View article<span class="offscreen-hidden">,&nbsp;Cell Format Dependent Cyclic and Calendar Aging of Lithium-Ion Cells: A Comparison of Coin and Pouch Cells</span></a><a href="/article/10.1149/1945-7111/aeb578/pdf" class="mr-2 mb-0 nowrap event_mini-link" data-event-action="PDF"><span class="icon-file-pdf"></span>PDF<span class="offscreen-hidden">,&nbsp;Cell Format Dependent Cyclic and Calendar Aging of Lithium-Ion Cells: A Comparison of Coin and Pouch Cells</span></a><button type="button" class="reveal-trigger mr-2 nowrap"><svg aria-hidden="true" class="fa-icon fa-icon--left fa-icon--flip" role="img" focusable="false" xmlns="http://www.w3.org/2000/svg" viewBox="0 0 320 512"><!--caret-down--><!--!Font Awesome Free 6.5.1 by @fontawesome - https://fontawesome.com License - https://fontawesome.com/license/free Copyright 2024 Fonticons, Inc.--><path d="M137.4 374.6c12.5 12.5 32.8 12.5 45.3 0l128-128c9.2-9.2 11.9-22.9 6.9-34.9s-16.6-19.8-29.6-19.8L32 192c-12.9 0-24.6 7.8-29.6 19.8s-2.2 25.7 6.9 34.9l128 128z"/></svg><span class="reveal-trigger-label" data-reveal-text="Open abstract" data-reveal-label-alt="Close abstract" data-link-purpose-append="Cell Format Dependent Cyclic and Calendar Aging of Lithium-Ion Cells: A Comparison of Coin and Pouch Cells" data-link-purpose-append-open="Cell Format Dependent Cyclic and Calendar Aging of Lithium-Ion Cells: A Comparison of Coin and Pouch Cells">Open abstract</span></button></div><div class="reveal-content"><div class="article-text view-text-small"><p>Coin cells are widely used for the development of new materials before validation in application oriented formats. However, electrochemical results differ between cell formats. The origins of these format dependent aging are still under discussion. Here, the aging behaviour of coin and pouch cells (NMC811 || graphite or graphite + 10% SiOx) assembled with identical electrodes, separators and electrolytes is compared.&amp;#xD;Unlike pouch cells, coin cells consistently exhibit accelerated capacity loss during cyclic aging (20 °C, 40 °C and 60 °C) and calendar aging at 0% and 100% state of charge. The discrepancy between coin and pouch cells during cyclic aging increases with temperature. The results reveal an additional temperature  and time dependent, but potential- and cycle independent aging mechanism in coin cells, reducing transferability between the two formats. Several factors, including pressure, electrolyte amount, additive amount, lithium plating and resistance, were excluded as the main origin.&amp;#xD;Instead, ion chromatography–mass spectrometry reveals an increased difluorophosphate concentration in the coin cell electrolyte, indicating enhanced LiPF₆ hydrolysis, most probably caused by insufficient hermetic sealing of the coin cell housing. Sealing such coin cells in an additional pouch bag suppresses hydrolysis and improves comparability between coin and pouch cells, particularly at higher temperature.</p></div><div class="art-list-item-tools small wd-abstr-lower"><a class="mr-2" href="https://doi.org/10.1149/1945-7111/aeb578">https://doi.org/10.1149/1945-7111/aeb578</a></div></div></li></ul><!--    articleEntryList end--><p><a href="/nsearch?currentPage=1&amp;terms=&amp;nextPage=2&amp;previousPage=-1&amp;searchDatePeriod=anytime&amp;journals=1945-7111&amp;accessType=open-access&amp;orderBy=newest&amp;pageLength=20">More Open Access articles</a></p></div></div></div><!-- End Open Access tabpanel --><!-- Start Spotlights tabpanel --><!-- End Spotlights tabpanel --><!-- MostCited tabpanel --><div tabindex="0"
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                    Open all abstracts<span class="offscreen-hidden">,&nbsp;in this tab</span></button></p><!--    articleEntryList start--><ul class="art-list"><li class="art-list-item reveal-container reveal-closed"><a href="/article/10.1149/1.1856988" class="art-list-item-title event_main-link">Trends in the Exchange Current for Hydrogen Evolution</a><p class="small art-list-item-meta">J. K. Nørskov <em>et al</em> 2005 <em>J. Electrochem. Soc.</em> <b>152</b> J23 </p><div class="art-list-item-tools small wd-abstr-upper"><a href="/article/10.1149/1.1856988/meta" class="mr-2 mb-0 nowrap event_mini-link" data-event-action="View article"><span class="icon-article"></span>View article<span class="offscreen-hidden">,&nbsp;Trends in the Exchange Current for Hydrogen Evolution</span></a><a href="/article/10.1149/1.1856988/pdf" class="mr-2 mb-0 nowrap event_mini-link" data-event-action="PDF"><span class="icon-file-pdf"></span>PDF<span class="offscreen-hidden">,&nbsp;Trends in the Exchange Current for Hydrogen Evolution</span></a><button type="button" class="reveal-trigger mr-2 nowrap"><svg aria-hidden="true" class="fa-icon fa-icon--left fa-icon--flip" role="img" focusable="false" xmlns="http://www.w3.org/2000/svg" viewBox="0 0 320 512"><!--caret-down--><!--!Font Awesome Free 6.5.1 by @fontawesome - https://fontawesome.com License - https://fontawesome.com/license/free Copyright 2024 Fonticons, Inc.--><path d="M137.4 374.6c12.5 12.5 32.8 12.5 45.3 0l128-128c9.2-9.2 11.9-22.9 6.9-34.9s-16.6-19.8-29.6-19.8L32 192c-12.9 0-24.6 7.8-29.6 19.8s-2.2 25.7 6.9 34.9l128 128z"/></svg><span class="reveal-trigger-label" data-reveal-text="Open abstract" data-reveal-label-alt="Close abstract" data-link-purpose-append="Trends in the Exchange Current for Hydrogen Evolution" data-link-purpose-append-open="Trends in the Exchange Current for Hydrogen Evolution">Open abstract</span></button></div><div class="reveal-content"><div class="article-text view-text-small"><p>A density functional theory database of hydrogen chemisorption energies on close packed surfaces of a number of transition and noble metals is presented. The bond energies are used to understand the trends in the exchange current for hydrogen evolution. A volcano curve is obtained when measured exchange currents are plotted as a function of the calculated hydrogen adsorption energies and a simple kinetic model is developed to understand the origin of the volcano. The volcano curve is also consistent with Pt being the most efficient electrocatalyst for hydrogen evolution. © 2005 The Electrochemical Society. All rights reserved.</p></div><div class="art-list-item-tools small wd-abstr-lower"><a class="mr-2" href="https://doi.org/10.1149/1.1856988">https://doi.org/10.1149/1.1856988</a></div></div></li><li class="art-list-item reveal-container reveal-closed"><a href="/article/10.1149/1.2358294" class="art-list-item-title event_main-link">Comment on “Trends in the Exchange Current for Hydrogen Evolution” [<i>J. Electrochem. Soc.</i>, 152, J23 (2005)]</a><p class="small art-list-item-meta">Wolfgang Schmickler and Sergio Trasatti 2006 <em>J. Electrochem. Soc.</em> <b>153</b> L31 </p><div class="art-list-item-tools small wd-abstr-upper"><a href="/article/10.1149/1.2358294/meta" class="mr-2 mb-0 nowrap event_mini-link" data-event-action="View article"><span class="icon-article"></span>View article<span class="offscreen-hidden">,&nbsp;Comment on “Trends in the Exchange Current for Hydrogen Evolution” [J. Electrochem. Soc., 152, J23 (2005)]</span></a><a href="/article/10.1149/1.2358294/pdf" class="mr-2 mb-0 nowrap event_mini-link" data-event-action="PDF"><span class="icon-file-pdf"></span>PDF<span class="offscreen-hidden">,&nbsp;Comment on “Trends in the Exchange Current for Hydrogen Evolution” [J. Electrochem. Soc., 152, J23 (2005)]</span></a><button type="button" class="reveal-trigger mr-2 nowrap"><svg aria-hidden="true" class="fa-icon fa-icon--left fa-icon--flip" role="img" focusable="false" xmlns="http://www.w3.org/2000/svg" viewBox="0 0 320 512"><!--caret-down--><!--!Font Awesome Free 6.5.1 by @fontawesome - https://fontawesome.com License - https://fontawesome.com/license/free Copyright 2024 Fonticons, Inc.--><path d="M137.4 374.6c12.5 12.5 32.8 12.5 45.3 0l128-128c9.2-9.2 11.9-22.9 6.9-34.9s-16.6-19.8-29.6-19.8L32 192c-12.9 0-24.6 7.8-29.6 19.8s-2.2 25.7 6.9 34.9l128 128z"/></svg><span class="reveal-trigger-label" data-reveal-text="Open abstract" data-reveal-label-alt="Close abstract" data-link-purpose-append="Comment on “Trends in the Exchange Current for Hydrogen Evolution” [J. Electrochem. Soc., 152, J23 (2005)]" data-link-purpose-append-open="Comment on “Trends in the Exchange Current for Hydrogen Evolution” [J. Electrochem. Soc., 152, J23 (2005)]">Open abstract</span></button></div><div class="reveal-content"><div class="article-text view-text-small"><p>We compare the adsorption energies calculated by Nørskov  et al. with data derived from experimental values; except for Ni and Co, which absorb hydrogen strongly, there is a linear relation. We discuss the model proposed by these authors in the light of extensive previous work and of experimental data and find it overly simplistic.</p></div><div class="art-list-item-tools small wd-abstr-lower"><a class="mr-2" href="https://doi.org/10.1149/1.2358294">https://doi.org/10.1149/1.2358294</a></div></div></li><li class="art-list-item reveal-container reveal-closed"><div class="eyebrow"><span class="offscreen-hidden">The following article is </span><span class="red">Open access</span></div><a href="/article/10.1149/2.1441707jes" class="art-list-item-title event_main-link">Review—SEI: Past, Present and Future</a><p class="small art-list-item-meta">E. Peled and S. Menkin 2017 <em>J. Electrochem. Soc.</em> <b>164</b> A1703 </p><div class="art-list-item-tools small wd-abstr-upper"><a href="/article/10.1149/2.1441707jes/meta" class="mr-2 mb-0 nowrap event_mini-link" data-event-action="View article"><span class="icon-article"></span>View article<span class="offscreen-hidden">,&nbsp;Review—SEI: Past, Present and Future</span></a><a href="/article/10.1149/2.1441707jes/pdf" class="mr-2 mb-0 nowrap event_mini-link" data-event-action="PDF"><span class="icon-file-pdf"></span>PDF<span class="offscreen-hidden">,&nbsp;Review—SEI: Past, Present and Future</span></a><button type="button" class="reveal-trigger mr-2 nowrap"><svg aria-hidden="true" class="fa-icon fa-icon--left fa-icon--flip" role="img" focusable="false" xmlns="http://www.w3.org/2000/svg" viewBox="0 0 320 512"><!--caret-down--><!--!Font Awesome Free 6.5.1 by @fontawesome - https://fontawesome.com License - https://fontawesome.com/license/free Copyright 2024 Fonticons, Inc.--><path d="M137.4 374.6c12.5 12.5 32.8 12.5 45.3 0l128-128c9.2-9.2 11.9-22.9 6.9-34.9s-16.6-19.8-29.6-19.8L32 192c-12.9 0-24.6 7.8-29.6 19.8s-2.2 25.7 6.9 34.9l128 128z"/></svg><span class="reveal-trigger-label" data-reveal-text="Open abstract" data-reveal-label-alt="Close abstract" data-link-purpose-append="Review—SEI: Past, Present and Future" data-link-purpose-append-open="Review—SEI: Past, Present and Future">Open abstract</span></button></div><div class="reveal-content"><div class="article-text view-text-small"><p>The Solid-Electrolyte-Interphase (SEI) model for non-aqueous alkali-metal batteries constitutes a paradigm change in the understanding of lithium batteries and has thus enabled the development of safer, durable, higher-power and lower-cost lithium batteries for portable and EV applications. Prior to the publication of the SEI model (1979), researchers used the Butler-Volmer equation, in which a direct electron transfer from the electrode to lithium cations in the solution is assumed. The SEI model proved that this is a mistaken concept and that, in practice, the transfer of electrons from the electrode to the solution in a lithium battery, must be prevented, since it will result in fast self-discharge of the active materials and poor battery performance. This model provides [E. Peled, in “Lithium Batteries,” J.P. Gabano (ed), Academic Press, (1983), E. Peled, <i>J. Electrochem. Soc.</i>, <b>126</b>, 2047 (1979).] new equations for: electrode kinetics (i<sub>o</sub> and b), anode corrosion, SEI resistivity and growth rate and irreversible capacity loss of lithium-ion batteries. This model became a cornerstone in the science and technology of lithium batteries. This paper reviews the past, present and the future of SEI batteries.</p></div><div class="art-list-item-tools small wd-abstr-lower"><a class="mr-2" href="https://doi.org/10.1149/2.1441707jes">https://doi.org/10.1149/2.1441707jes</a></div></div></li><li class="art-list-item reveal-container reveal-closed"><div class="eyebrow"><span class="offscreen-hidden">The following article is </span><span class="red">Open access</span></div><a href="/article/10.1149/2.0021707jes" class="art-list-item-title event_main-link">Oxygen Release and Its Effect on the Cycling Stability of LiNi<sub>x</sub>Mn<sub>y</sub>Co<sub>z</sub>O<sub>2</sub> (NMC) Cathode Materials for Li-Ion Batteries</a><p class="small art-list-item-meta">Roland Jung <em>et al</em> 2017 <em>J. Electrochem. Soc.</em> <b>164</b> A1361 </p><div class="art-list-item-tools small wd-abstr-upper"><a href="/article/10.1149/2.0021707jes/meta" class="mr-2 mb-0 nowrap event_mini-link" data-event-action="View article"><span class="icon-article"></span>View article<span class="offscreen-hidden">,&nbsp;Oxygen Release and Its Effect on the Cycling Stability of LiNixMnyCozO2 (NMC) Cathode Materials for Li-Ion Batteries</span></a><a href="/article/10.1149/2.0021707jes/pdf" class="mr-2 mb-0 nowrap event_mini-link" data-event-action="PDF"><span class="icon-file-pdf"></span>PDF<span class="offscreen-hidden">,&nbsp;Oxygen Release and Its Effect on the Cycling Stability of LiNixMnyCozO2 (NMC) Cathode Materials for Li-Ion Batteries</span></a><button type="button" class="reveal-trigger mr-2 nowrap"><svg aria-hidden="true" class="fa-icon fa-icon--left fa-icon--flip" role="img" focusable="false" xmlns="http://www.w3.org/2000/svg" viewBox="0 0 320 512"><!--caret-down--><!--!Font Awesome Free 6.5.1 by @fontawesome - https://fontawesome.com License - https://fontawesome.com/license/free Copyright 2024 Fonticons, Inc.--><path d="M137.4 374.6c12.5 12.5 32.8 12.5 45.3 0l128-128c9.2-9.2 11.9-22.9 6.9-34.9s-16.6-19.8-29.6-19.8L32 192c-12.9 0-24.6 7.8-29.6 19.8s-2.2 25.7 6.9 34.9l128 128z"/></svg><span class="reveal-trigger-label" data-reveal-text="Open abstract" data-reveal-label-alt="Close abstract" data-link-purpose-append="Oxygen Release and Its Effect on the Cycling Stability of LiNixMnyCozO2 (NMC) Cathode Materials for Li-Ion Batteries" data-link-purpose-append-open="Oxygen Release and Its Effect on the Cycling Stability of LiNixMnyCozO2 (NMC) Cathode Materials for Li-Ion Batteries">Open abstract</span></button></div><div class="reveal-content"><div class="article-text view-text-small"><p>Layered LiNi<sub>x</sub>Mn<sub>y</sub>Co<sub>z</sub>O<sub>2</sub> (NMC) is a widely used class of cathode materials with LiNi<sub>1/3</sub>Mn<sub>1/3</sub>Co<sub>1/3</sub>O<sub>2</sub> (NMC111) being the most common representative. However, Ni-rich NMCs are more and more in the focus of current research due to their higher specific capacity and energy. In this work we will compare LiNi<sub>1/3</sub>Mn<sub>1/3</sub>Co<sub>1/3</sub>O<sub>2</sub> (NMC111), LiNi<sub>0.6</sub>Mn<sub>0.2</sub>Co<sub>0.2</sub>O<sub>2</sub> (NMC622), and LiNi<sub>0.8</sub>Mn<sub>0.1</sub>Co<sub>0.1</sub>O<sub>2</sub> (NMC811) with respect to their cycling stability in NMC-graphite full-cells at different end-of-charge potentials. It will be shown that stable cycling is possible up to 4.4 V for NMC111 and NMC622 and only up to 4.0 V for NMC811. At higher potentials, significant capacity fading was observed, which was traced back to an increase in the polarization of the NMC electrode, contrary to the nearly constant polarization of the graphite electrode. Furthermore, we show that the increase in the polarization occurs when the NMC materials are cycled up to a high-voltage feature in the dq/dV plot, which occurs at ∼4.7 V vs. Li/Li<sup>+</sup> for NMC111 and NMC622 and at ∼4.3 V vs. Li/Li<sup>+</sup> for NMC811. For the latter material, this feature corresponds to the H2 → H3 phase transition. Contrary to the common understanding that the electrochemical oxidation of carbonate electrolytes causes the CO<sub>2</sub> and CO evolution at potentials above 4.7 V vs. Li/Li<sup>+</sup>, we believe that the observed CO<sub>2</sub> and CO are mainly due to the chemical reaction of reactive lattice oxygen with the electrolyte. This hypothesis is based on gas analysis using On-line Electrochemical Mass Spectrometry (OEMS), by which we prove that all three materials release oxygen from the particle surface and that the oxygen evolution coincides with the onset of CO<sub>2</sub> and CO evolution. Interestingly, the onsets of oxygen evolution for the different NMCs correlate well with the high-voltage redox feature at ∼4.7 V vs. Li/Li<sup>+</sup> for NMC111 and NMC622 as well as at ∼4.3 V vs. Li/Li<sup>+</sup> for NMC811. To support this hypothesis, we show that no CO<sub>2</sub> or CO is evolved for the LiNi<sub>0.43</sub>Mn<sub>1.57</sub>O<sub>4</sub> (LNMO) spinel up to 5 V vs. Li/Li<sup>+</sup>, consistent with the absence of oxygen release. Lastly, we demonstrate by the use of <sup>13</sup>C labeled conductive carbon that it is the electrolyte rather than the conductive carbon which is oxidized by the released lattice oxygen. Taking these findings into consideration, a mechanism is proposed for the reaction of released lattice oxygen with ethylene carbonate yielding CO<sub>2</sub>, CO, and H<sub>2</sub>O.</p></div><div class="art-list-item-tools small wd-abstr-lower"><a class="mr-2" href="https://doi.org/10.1149/2.0021707jes">https://doi.org/10.1149/2.0021707jes</a></div></div></li><li class="art-list-item reveal-container reveal-closed"><a href="/article/10.1149/1.1393348" class="art-list-item-title event_main-link">High Capacity Anode Materials for Rechargeable Sodium‐Ion Batteries</a><p class="small art-list-item-meta">D. A. Stevens and J. R. Dahn 2000 <em>J. Electrochem. Soc.</em> <b>147</b> 1271 </p><div class="art-list-item-tools small wd-abstr-upper"><a href="/article/10.1149/1.1393348/meta" class="mr-2 mb-0 nowrap event_mini-link" data-event-action="View article"><span class="icon-article"></span>View article<span class="offscreen-hidden">,&nbsp;High Capacity Anode Materials for Rechargeable Sodium‐Ion Batteries</span></a><a href="/article/10.1149/1.1393348/pdf" class="mr-2 mb-0 nowrap event_mini-link" data-event-action="PDF"><span class="icon-file-pdf"></span>PDF<span class="offscreen-hidden">,&nbsp;High Capacity Anode Materials for Rechargeable Sodium‐Ion Batteries</span></a><button type="button" class="reveal-trigger mr-2 nowrap"><svg aria-hidden="true" class="fa-icon fa-icon--left fa-icon--flip" role="img" focusable="false" xmlns="http://www.w3.org/2000/svg" viewBox="0 0 320 512"><!--caret-down--><!--!Font Awesome Free 6.5.1 by @fontawesome - https://fontawesome.com License - https://fontawesome.com/license/free Copyright 2024 Fonticons, Inc.--><path d="M137.4 374.6c12.5 12.5 32.8 12.5 45.3 0l128-128c9.2-9.2 11.9-22.9 6.9-34.9s-16.6-19.8-29.6-19.8L32 192c-12.9 0-24.6 7.8-29.6 19.8s-2.2 25.7 6.9 34.9l128 128z"/></svg><span class="reveal-trigger-label" data-reveal-text="Open abstract" data-reveal-label-alt="Close abstract" data-link-purpose-append="High Capacity Anode Materials for Rechargeable Sodium‐Ion Batteries" data-link-purpose-append-open="High Capacity Anode Materials for Rechargeable Sodium‐Ion Batteries">Open abstract</span></button></div><div class="reveal-content"><div class="article-text view-text-small"><p>Electrochemical techniques have been used to study the reversible insertion of sodium into hard‐carbon host structures at room temperature. In this paper we compare these results with those for lithium insertion in the same materials and demonstrate the presence of similar alkali metal insertion mechanisms in both cases. Despite the gravimetric capacities being lower for sodium than lithium insertion, we have achieved a reversible sodium capacity of 300 mAh/g, close to that for lithium insertion in graphitic carbon anode materials. Such materials may therefore be useful as anodes in rechargeable sodium‐ion batteries. © 2000 The Electrochemical Society. All rights reserved.</p></div><div class="art-list-item-tools small wd-abstr-lower"><a class="mr-2" href="https://doi.org/10.1149/1.1393348">https://doi.org/10.1149/1.1393348</a></div></div></li><li class="art-list-item reveal-container reveal-closed"><a href="/article/10.1149/1.3515880" class="art-list-item-title event_main-link">A Critical Review of Thermal Issues in Lithium-Ion Batteries</a><p class="small art-list-item-meta">Todd M. Bandhauer <em>et al</em> 2011 <em>J. Electrochem. Soc.</em> <b>158</b> R1 </p><div class="art-list-item-tools small wd-abstr-upper"><a href="/article/10.1149/1.3515880/meta" class="mr-2 mb-0 nowrap event_mini-link" data-event-action="View article"><span class="icon-article"></span>View article<span class="offscreen-hidden">,&nbsp;A Critical Review of Thermal Issues in Lithium-Ion Batteries</span></a><a href="/article/10.1149/1.3515880/pdf" class="mr-2 mb-0 nowrap event_mini-link" data-event-action="PDF"><span class="icon-file-pdf"></span>PDF<span class="offscreen-hidden">,&nbsp;A Critical Review of Thermal Issues in Lithium-Ion Batteries</span></a><button type="button" class="reveal-trigger mr-2 nowrap"><svg aria-hidden="true" class="fa-icon fa-icon--left fa-icon--flip" role="img" focusable="false" xmlns="http://www.w3.org/2000/svg" viewBox="0 0 320 512"><!--caret-down--><!--!Font Awesome Free 6.5.1 by @fontawesome - https://fontawesome.com License - https://fontawesome.com/license/free Copyright 2024 Fonticons, Inc.--><path d="M137.4 374.6c12.5 12.5 32.8 12.5 45.3 0l128-128c9.2-9.2 11.9-22.9 6.9-34.9s-16.6-19.8-29.6-19.8L32 192c-12.9 0-24.6 7.8-29.6 19.8s-2.2 25.7 6.9 34.9l128 128z"/></svg><span class="reveal-trigger-label" data-reveal-text="Open abstract" data-reveal-label-alt="Close abstract" data-link-purpose-append="A Critical Review of Thermal Issues in Lithium-Ion Batteries" data-link-purpose-append-open="A Critical Review of Thermal Issues in Lithium-Ion Batteries">Open abstract</span></button></div><div class="reveal-content"><div class="article-text view-text-small"><p>Lithium-ion batteries are well-suited for fully electric and hybrid electric vehicles due to their high specific energy and energy density relative to other rechargeable cell chemistries. However, these batteries have not been widely deployed commercially in these vehicles yet due to safety, cost, and poor low temperature performance, which are all challenges related to battery thermal management. In this paper, a critical review of the available literature on the major thermal issues for lithium-ion batteries is presented. Specific attention is paid to the effects of temperature and thermal management on capacity/power fade, thermal runaway, and pack electrical imbalance and to the performance of lithium-ion cells at cold temperatures. Furthermore, insights gained from previous experimental and modeling investigations are elucidated. These include the need for more accurate heat generation measurements, improved modeling of the heat generation rate, and clarity in the relative magnitudes of the various thermal effects observed at high charge and discharge rates seen in electric vehicle applications. From an analysis of the literature, the requirements for lithium-ion thermal management systems for optimal performance in these applications are suggested, and it is clear that no existing thermal management strategy or technology meets all these requirements.</p></div><div class="art-list-item-tools small wd-abstr-lower"><a class="mr-2" href="https://doi.org/10.1149/1.3515880">https://doi.org/10.1149/1.3515880</a></div></div></li><li class="art-list-item reveal-container reveal-closed"><a href="/article/10.1149/1.1850854" class="art-list-item-title event_main-link">The Impact of Elastic Deformation on Deposition Kinetics at Lithium/Polymer Interfaces</a><p class="small art-list-item-meta">Charles Monroe and John Newman 2005 <em>J. Electrochem. Soc.</em> <b>152</b> A396 </p><div class="art-list-item-tools small wd-abstr-upper"><a href="/article/10.1149/1.1850854/meta" class="mr-2 mb-0 nowrap event_mini-link" data-event-action="View article"><span class="icon-article"></span>View article<span class="offscreen-hidden">,&nbsp;The Impact of Elastic Deformation on Deposition Kinetics at Lithium/Polymer Interfaces</span></a><a href="/article/10.1149/1.1850854/pdf" class="mr-2 mb-0 nowrap event_mini-link" data-event-action="PDF"><span class="icon-file-pdf"></span>PDF<span class="offscreen-hidden">,&nbsp;The Impact of Elastic Deformation on Deposition Kinetics at Lithium/Polymer Interfaces</span></a><button type="button" class="reveal-trigger mr-2 nowrap"><svg aria-hidden="true" class="fa-icon fa-icon--left fa-icon--flip" role="img" focusable="false" xmlns="http://www.w3.org/2000/svg" viewBox="0 0 320 512"><!--caret-down--><!--!Font Awesome Free 6.5.1 by @fontawesome - https://fontawesome.com License - https://fontawesome.com/license/free Copyright 2024 Fonticons, Inc.--><path d="M137.4 374.6c12.5 12.5 32.8 12.5 45.3 0l128-128c9.2-9.2 11.9-22.9 6.9-34.9s-16.6-19.8-29.6-19.8L32 192c-12.9 0-24.6 7.8-29.6 19.8s-2.2 25.7 6.9 34.9l128 128z"/></svg><span class="reveal-trigger-label" data-reveal-text="Open abstract" data-reveal-label-alt="Close abstract" data-link-purpose-append="The Impact of Elastic Deformation on Deposition Kinetics at Lithium/Polymer Interfaces" data-link-purpose-append-open="The Impact of Elastic Deformation on Deposition Kinetics at Lithium/Polymer Interfaces">Open abstract</span></button></div><div class="reveal-content"><div class="article-text view-text-small"><p>Past theories of electrode stability assume that the surface tension resists the amplification of surface roughness at cathodes and show that instability at lithium/liquid interfaces cannot be prevented by surface forces alone [Electrochim. Acta, <b>40</b>, 599 (1995)]. This work treats interfacial stability in lithium/polymer systems where the electrolyte is solid. Linear elasticity theory is employed to compute the additional effect of bulk mechanical forces on electrode stability. The lithium and polymer are treated as Hookean elastic materials, characterized by their shear moduli and Poisson’s ratios. Two-dimensional displacement distributions that satisfy force balances across a periodically deforming interface are derived; these allow computation of the stress and surface-tension forces. The incorporation of elastic effects into a kinetic model demonstrates regimes of electrolyte mechanical properties where amplification of surface roughness can be inhibited. For a polymer material with Poisson’s ratio similar to poly(ethylene oxide), interfacial roughening is mechanically suppressed when the separator shear modulus is about twice that of lithium. © 2005 The Electrochemical Society. All rights reserved.</p></div><div class="art-list-item-tools small wd-abstr-lower"><a class="mr-2" href="https://doi.org/10.1149/1.1850854">https://doi.org/10.1149/1.1850854</a></div></div></li><li class="art-list-item reveal-container reveal-closed"><div class="eyebrow"><span class="offscreen-hidden">The following article is </span><span class="red">Open access</span></div><a href="/article/10.1149/1945-7111/ab9050" class="art-list-item-title event_main-link">Development of Experimental Techniques for Parameterization of Multi-scale Lithium-ion Battery Models</a><p class="small art-list-item-meta">Chang-Hui Chen <em>et al</em> 2020 <em>J. Electrochem. Soc.</em> <b>167</b> 080534 </p><div class="art-list-item-tools small wd-abstr-upper"><a href="/article/10.1149/1945-7111/ab9050/meta" class="mr-2 mb-0 nowrap event_mini-link" data-event-action="View article"><span class="icon-article"></span>View article<span class="offscreen-hidden">,&nbsp;Development of Experimental Techniques for Parameterization of Multi-scale Lithium-ion Battery Models</span></a><a href="/article/10.1149/1945-7111/ab9050/pdf" class="mr-2 mb-0 nowrap event_mini-link" data-event-action="PDF"><span class="icon-file-pdf"></span>PDF<span class="offscreen-hidden">,&nbsp;Development of Experimental Techniques for Parameterization of Multi-scale Lithium-ion Battery Models</span></a><button type="button" class="reveal-trigger mr-2 nowrap"><svg aria-hidden="true" class="fa-icon fa-icon--left fa-icon--flip" role="img" focusable="false" xmlns="http://www.w3.org/2000/svg" viewBox="0 0 320 512"><!--caret-down--><!--!Font Awesome Free 6.5.1 by @fontawesome - https://fontawesome.com License - https://fontawesome.com/license/free Copyright 2024 Fonticons, Inc.--><path d="M137.4 374.6c12.5 12.5 32.8 12.5 45.3 0l128-128c9.2-9.2 11.9-22.9 6.9-34.9s-16.6-19.8-29.6-19.8L32 192c-12.9 0-24.6 7.8-29.6 19.8s-2.2 25.7 6.9 34.9l128 128z"/></svg><span class="reveal-trigger-label" data-reveal-text="Open abstract" data-reveal-label-alt="Close abstract" data-link-purpose-append="Development of Experimental Techniques for Parameterization of Multi-scale Lithium-ion Battery Models" data-link-purpose-append-open="Development of Experimental Techniques for Parameterization of Multi-scale Lithium-ion Battery Models">Open abstract</span></button></div><div class="reveal-content"><div class="article-text view-text-small"><p>Presented here, is an extensive 35 parameter experimental data set of a cylindrical 21700 commercial cell (LGM50), for an electrochemical pseudo-two-dimensional (P2D) model. The experimental methodologies for tear-down and subsequent chemical, physical, electrochemical kinetics and thermodynamic analysis, and their accuracy and validity are discussed. Chemical analysis of the LGM50 cell shows that it is comprised of a NMC 811 positive electrode and bi-component Graphite-SiO<sub>x</sub> negative electrode. The thermodynamic open circuit voltages (OCV) and lithium stoichiometry in the electrode are obtained using galvanostatic intermittent titration technique (GITT) in half cell and three-electrode full cell configurations. The activation energy and exchange current coefficient through electrochemical impedance spectroscopy (EIS) measurements. Apparent diffusion coefficients are estimated using the Sand equation on the voltage transient during the current pulse; an expansion factor was applied to the bi-component negative electrode data to reflect the average change in effective surface area during lithiation. The 35 parameters are applied within a P2D model to show the fit to experimental validation LGM50 cell discharge and relaxation voltage profiles at room temperature. The accuracy and validity of the processes and the techniques in the determination of these parameters are discussed, including opportunities for further modelling and data analysis improvements.</p></div><div class="art-list-item-tools small wd-abstr-lower"><a class="mr-2" href="https://doi.org/10.1149/1945-7111/ab9050">https://doi.org/10.1149/1945-7111/ab9050</a></div></div></li><li class="art-list-item reveal-container reveal-closed"><a href="/article/10.1149/1.1379565" class="art-list-item-title event_main-link">The Mechanisms of Lithium and Sodium Insertion in Carbon Materials</a><p class="small art-list-item-meta">D. A. Stevens and J. R. Dahn 2001 <em>J. Electrochem. Soc.</em> <b>148</b> A803 </p><div class="art-list-item-tools small wd-abstr-upper"><a href="/article/10.1149/1.1379565/meta" class="mr-2 mb-0 nowrap event_mini-link" data-event-action="View article"><span class="icon-article"></span>View article<span class="offscreen-hidden">,&nbsp;The Mechanisms of Lithium and Sodium Insertion in Carbon Materials</span></a><a href="/article/10.1149/1.1379565/pdf" class="mr-2 mb-0 nowrap event_mini-link" data-event-action="PDF"><span class="icon-file-pdf"></span>PDF<span class="offscreen-hidden">,&nbsp;The Mechanisms of Lithium and Sodium Insertion in Carbon Materials</span></a><button type="button" class="reveal-trigger mr-2 nowrap"><svg aria-hidden="true" class="fa-icon fa-icon--left fa-icon--flip" role="img" focusable="false" xmlns="http://www.w3.org/2000/svg" viewBox="0 0 320 512"><!--caret-down--><!--!Font Awesome Free 6.5.1 by @fontawesome - https://fontawesome.com License - https://fontawesome.com/license/free Copyright 2024 Fonticons, Inc.--><path d="M137.4 374.6c12.5 12.5 32.8 12.5 45.3 0l128-128c9.2-9.2 11.9-22.9 6.9-34.9s-16.6-19.8-29.6-19.8L32 192c-12.9 0-24.6 7.8-29.6 19.8s-2.2 25.7 6.9 34.9l128 128z"/></svg><span class="reveal-trigger-label" data-reveal-text="Open abstract" data-reveal-label-alt="Close abstract" data-link-purpose-append="The Mechanisms of Lithium and Sodium Insertion in Carbon Materials" data-link-purpose-append-open="The Mechanisms of Lithium and Sodium Insertion in Carbon Materials">Open abstract</span></button></div><div class="reveal-content"><div class="article-text view-text-small"><p>In this paper, we compare the interactions of lithium and sodium with a range of carbon materials in electrochemical cells. Through wide angle <i>in situ</i> X-ray scattering studies, we demonstrate that both lithium and sodium can be inserted into the interlayer space in disordered carbon materials. This insertion process is accompanied by an increase in the interlayer spacing in these materials. Small-angle <i>in situ</i> scattering studies are presented to clearly show the insertion of lithium and sodium into nanopores within disordered hard carbons. We also show that very little, if any, sodium can be inserted into graphitic materials in contrast to the large capacity seen for lithium insertion. © 2001 The Electrochemical Society. All rights reserved.</p></div><div class="art-list-item-tools small wd-abstr-lower"><a class="mr-2" href="https://doi.org/10.1149/1.1379565">https://doi.org/10.1149/1.1379565</a></div></div></li><li class="art-list-item reveal-container reveal-closed"><a href="/article/10.1149/1.3483106" class="art-list-item-title event_main-link">Hydrogen Oxidation and Evolution Reaction Kinetics on Platinum: Acid vs Alkaline Electrolytes</a><p class="small art-list-item-meta">Wenchao Sheng <em>et al</em> 2010 <em>J. Electrochem. Soc.</em> <b>157</b> B1529 </p><div class="art-list-item-tools small wd-abstr-upper"><a href="/article/10.1149/1.3483106/meta" class="mr-2 mb-0 nowrap event_mini-link" data-event-action="View article"><span class="icon-article"></span>View article<span class="offscreen-hidden">,&nbsp;Hydrogen Oxidation and Evolution Reaction Kinetics on Platinum: Acid vs Alkaline Electrolytes</span></a><a href="/article/10.1149/1.3483106/pdf" class="mr-2 mb-0 nowrap event_mini-link" data-event-action="PDF"><span class="icon-file-pdf"></span>PDF<span class="offscreen-hidden">,&nbsp;Hydrogen Oxidation and Evolution Reaction Kinetics on Platinum: Acid vs Alkaline Electrolytes</span></a><button type="button" class="reveal-trigger mr-2 nowrap"><svg aria-hidden="true" class="fa-icon fa-icon--left fa-icon--flip" role="img" focusable="false" xmlns="http://www.w3.org/2000/svg" viewBox="0 0 320 512"><!--caret-down--><!--!Font Awesome Free 6.5.1 by @fontawesome - https://fontawesome.com License - https://fontawesome.com/license/free Copyright 2024 Fonticons, Inc.--><path d="M137.4 374.6c12.5 12.5 32.8 12.5 45.3 0l128-128c9.2-9.2 11.9-22.9 6.9-34.9s-16.6-19.8-29.6-19.8L32 192c-12.9 0-24.6 7.8-29.6 19.8s-2.2 25.7 6.9 34.9l128 128z"/></svg><span class="reveal-trigger-label" data-reveal-text="Open abstract" data-reveal-label-alt="Close abstract" data-link-purpose-append="Hydrogen Oxidation and Evolution Reaction Kinetics on Platinum: Acid vs Alkaline Electrolytes" data-link-purpose-append-open="Hydrogen Oxidation and Evolution Reaction Kinetics on Platinum: Acid vs Alkaline Electrolytes">Open abstract</span></button></div><div class="reveal-content"><div class="article-text view-text-small"><p>The kinetics of the hydrogen oxidation reaction (HOR) and hydrogen evolution reaction (HER) on polycrystalline platinum [Pt(pc)] and high surface area carbon-supported platinum nanoparticles (Pt/C) were studied in 0.1 M KOH using rotating disk electrode (RDE) measurements. After corrections of noncompensated solution resistance from ac impedance spectroscopy and of hydrogen mass transport in the HOR branch, the kinetic current densities were fitted to the Butler–Volmer equation using a transfer coefficient of <span xmlns:xlink="http://www.w3.org/1999/xlink" class="inline-eqn"><span class="mml"><span class="texImage"><img src="data:image/png;base64,iVBORw0KGgoAAAANSUhEUgAAAAEAAAABCAQAAAC1HAwCAAAAC0lEQVR42mNkYAAAAAYAAjCB0C8AAAAASUVORK5CYII=" data-src="https://content.cld.iop.org/journals/1945-7111/157/11/B1529/revision1/jes_157_11_B1529ieqn1.jpg" style="max-width: 100%;" alt="Equation or symbol description not available" align="top" role="math"></img></span><math xmlns="http://www.w3.org/1998/Math/MathML"><mrow><mi>α</mi><mo>=</mo><mn>0.5</mn></mrow></math></span></span>, from which HOR/HER exchange current densities on Pt(pc) and Pt/C were obtained, and the HOR/HER mechanisms in alkaline solution were discussed. Unlike the HOR/HER rates on Pt electrodes in alkaline solution, the HOR/HER rates on a Pt electrode in 0.1 M <span xmlns:xlink="http://www.w3.org/1999/xlink" class="inline-eqn"><span class="mml"><span class="texImage"><img src="data:image/png;base64,iVBORw0KGgoAAAANSUhEUgAAAAEAAAABCAQAAAC1HAwCAAAAC0lEQVR42mNkYAAAAAYAAjCB0C8AAAAASUVORK5CYII=" data-src="https://content.cld.iop.org/journals/1945-7111/157/11/B1529/revision1/jes_157_11_B1529ieqn2.jpg" style="max-width: 100%;" alt="Equation or symbol description not available" align="top" role="math"></img></span><math xmlns="http://www.w3.org/1998/Math/MathML"><mrow><msub><mrow><mtext>HClO</mtext></mrow><mrow><mn>4</mn></mrow></msub></mrow></math></span></span> were limited entirely by hydrogen diffusion, which renders the quantification of the HOR/HER kinetics impossible by conventional RDE measurements. The simulation of the hydrogen anode performance based on the specific exchange current densities of the HOR/HER at <span xmlns:xlink="http://www.w3.org/1999/xlink" class="inline-eqn"><span class="mml"><span class="texImage"><img src="data:image/png;base64,iVBORw0KGgoAAAANSUhEUgAAAAEAAAABCAQAAAC1HAwCAAAAC0lEQVR42mNkYAAAAAYAAjCB0C8AAAAASUVORK5CYII=" data-src="https://content.cld.iop.org/journals/1945-7111/157/11/B1529/revision1/jes_157_11_B1529ieqn3.jpg" style="max-width: 100%;" alt="Equation or symbol description not available" align="top" role="math"></img></span><math xmlns="http://www.w3.org/1998/Math/MathML"><mrow><mn>80</mn><mo>°</mo><mi>C</mi></mrow></math></span></span> illustrates that in addition to the oxygen reduction reaction cell voltage loss on the cathode, the slow HOR kinetics are projected to cause significant anode potential losses in alkaline fuel cells for low platinum loadings (<span xmlns:xlink="http://www.w3.org/1999/xlink" class="inline-eqn"><span class="mml"><span class="texImage"><img src="data:image/png;base64,iVBORw0KGgoAAAANSUhEUgAAAAEAAAABCAQAAAC1HAwCAAAAC0lEQVR42mNkYAAAAAYAAjCB0C8AAAAASUVORK5CYII=" data-src="https://content.cld.iop.org/journals/1945-7111/157/11/B1529/revision1/jes_157_11_B1529ieqn4.jpg" style="max-width: 100%;" alt="Equation or symbol description not available" align="top" role="math"></img></span><math xmlns="http://www.w3.org/1998/Math/MathML"><mrow><mo></mo><mn>130</mn><mspace></mspace><mtext>mV</mtext></mrow></math></span></span> at <span xmlns:xlink="http://www.w3.org/1999/xlink" class="inline-eqn"><span class="mml"><span class="texImage"><img src="data:image/png;base64,iVBORw0KGgoAAAANSUhEUgAAAAEAAAABCAQAAAC1HAwCAAAAC0lEQVR42mNkYAAAAAYAAjCB0C8AAAAASUVORK5CYII=" data-src="https://content.cld.iop.org/journals/1945-7111/157/11/B1529/revision1/jes_157_11_B1529ieqn5.jpg" style="max-width: 100%;" alt="Equation or symbol description not available" align="top" role="math"></img></span><math xmlns="http://www.w3.org/1998/Math/MathML"><mrow><mn>0.05</mn><mspace></mspace><msub><mrow><mtext>mg</mtext></mrow><mrow><mtext>Pt</mtext></mrow></msub><mo>/</mo><msubsup><mrow><mtext>cm</mtext></mrow><mrow><mtext>anode</mtext></mrow><mrow><mn>2</mn></mrow></msubsup></mrow></math></span></span> and <span xmlns:xlink="http://www.w3.org/1999/xlink" class="inline-eqn"><span class="mml"><span class="texImage"><img src="data:image/png;base64,iVBORw0KGgoAAAANSUhEUgAAAAEAAAABCAQAAAC1HAwCAAAAC0lEQVR42mNkYAAAAAYAAjCB0C8AAAAASUVORK5CYII=" data-src="https://content.cld.iop.org/journals/1945-7111/157/11/B1529/revision1/jes_157_11_B1529ieqn6.jpg" style="max-width: 100%;" alt="Equation or symbol description not available" align="top" role="math"></img></span><math xmlns="http://www.w3.org/1998/Math/MathML"><mrow><mn>1.5</mn><mspace></mspace><mi>A</mi><mo>/</mo><msubsup><mrow><mtext>cm</mtext></mrow><mrow><mtext>anode</mtext></mrow><mrow><mn>2</mn></mrow></msubsup></mrow></math></span></span>), contrary to what is reported for proton exchange membrane fuel cells.</p></div><div class="art-list-item-tools small wd-abstr-lower"><a class="mr-2" href="https://doi.org/10.1149/1.3483106">https://doi.org/10.1149/1.3483106</a></div></div></li></ul><!--    articleEntryList end--></div></div></div><!-- End Featured tabpanel --></div><!-- End Article listing tabs --><!--  Start of google banners in the middle.  --><section aria-label="Main column advert"><div class="ad-iframe-wrap"><div id='div-gpt-ad-1562594774007-0' style='width: 728px; height: 90px; display: block;'><script>
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