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run-001 | T01 | Li-ion | non-aqueous | coin cell, micrometric silicon electrode against lithium metal | half cell | coin (CR2032) | micrometric silicon Ev-Nano® | anode | null | null | 1 M LiPF6 EC:DEC (1:1 by volume) | null | Celgard® 2400 + membrane poreuse Viledon® | null | Not reported | 0.005 V | 1.2 V | Li metal | C/20 | 1 | lithiation capacity (first discharge) 3700 mAh.g-1; delithiation capacity recovered on charge ~300 mAh.g-1; C 3600 mAh.g-1; particle size ~5 µm | Mechanical failure | Pulverisation of the active material during lithiation probably disconnected the particles from the electronic network. | Suggested by the author | We built a CR2032 coin half cell with a micrometric commercial silicon electrode (Ev-Nano, ~5 µm particles) against lithium metal. The electrode was 65:25:10 silicon : carbon fibres : CMC, cast from an aqueous ink onto 10 µm copper foil, dried and calendered, at about 1.5 mg/cm² of silicon. We used 1 M LiPF6 in EC:DEC ... | Compréhension des mécanismes de (dé)lithiation et de dégradation d'électrodes de silicium pour accumulateur Li-ion et étude de facteurs influents | Etienne Radvanyi | 2,014 | PhD (doctorat) | Université de Grenoble | France | https://theses.hal.science/tel-01127946 |
run-002 | T01 | Li-ion | non-aqueous | coin cell vs Li metal, β-type regime (full lithiation, delithiation capacity limited to 1200 mAh/g) | half cell | pile bouton | nanometric silicon | anode | null | null | 1 M LiPF6 EC:DEC (1:1 by volume) + none | null | Not reported | null | Not reported | 0.005 V | 1.2 V | Li metal | C/20 | Unclear (degradation after 160 cycles; exact failure cycle not stated) | exchanged capacity 1200 mAh.g-1; composition Li2,5Si ↔ Li3,75Si; sudden capacity drop ~160 cycles | Degradation | Performance loss when cycling in the β domain against lithium metal is attributed more to the cell set-up than to intrinsic silicon-electrode deterioration. | Suggested by the author | We cycled a nanometric silicon electrode against lithium metal in a coin cell, in 1 M LiPF6 in EC:DEC (1:1 by volume) with no additive. The electrode was 65:25:10 silicon : carbon fibres : CMC, cast from an aqueous ink onto 10 µm copper foil and calendered, at about 1.5 mg/cm² of silicon. At C/20 we lithiated fully dow... | Compréhension des mécanismes de (dé)lithiation et de dégradation d'électrodes de silicium pour accumulateur Li-ion et étude de facteurs influents | Etienne Radvanyi | 2,014 | PhD (doctorat) | Université de Grenoble | France | https://theses.hal.science/tel-01127946 |
run-003 | T02 | Li-S | non-aqueous | rate capability test with equal charge and discharge currents | half cell | Not reported | S-on-NwC composite electrode | cathode | null | null | Not reported | null | Not reported | null | Not reported | Not reported | Not reported | Not reported | 2C | Unclear (rate raised every 5 cycles; shorted at 2C, exact cycle not given) | charge current density 14 mA cm-2; cathode areal capacity 7.18 mAh cm-2 | Short circuit | Charging at 2C imposed a high current density of 14 mA cm-2, which caused severe dendrite formation at the lithium electrode. | Stated by the author | We ran a rate-capability test on an S-on-NwC cathode (80/10/10, 4.66 mg of sulfur/cm², 7.18 mAh/cm²) against a lithium electrode. Charge and discharge currents were equal, and we stepped the C-rate up every five cycles. When we charged at 2C, a current density of 14 mA/cm², the cell short-circuited. The high charging c... | Lithium/Sulfur batteries : development and understanding of the working mechanisms | Sylwia Walus | 2,015 | PhD (doctorat) | Université Grenoble Alpes | France | https://theses.hal.science/tel-01212711 |
run-004 | T02 | Li-S | non-aqueous | Li2S electrode vs Li coin cell, cell 1 of two cells aimed to be identical | half cell | coin | Li2S/SuperP/PVdF electrode (as-received commercial Li2S) | cathode | null | null | 1 M LiTFSI TEGDME/DIOX 1:1 vol + LiNO3 (0.1M) | null | Viledon + Celgard2400 | null | room temperature | 1.7 V | 3 V | Li+/Li | C/10 | 1 | null | Did not work in that regime | Probably the Li2S failed to activate because the potential limit set for the first step was too low. | Suggested by the author | We built two Li2S half coin cells meant to be identical. They used 70/20/10 Li2S/Super P/PVdF electrodes made from as-received commercial Li2S at 0.89 mg/cm², against lithium in 1 M LiTFSI + 0.1 M LiNO3 in TEGDME/DIOX (1:1 by volume), with Viledon and Celgard 2400 separators. We cycled them at room temperature at C/10 ... | Lithium/Sulfur batteries : development and understanding of the working mechanisms | Sylwia Walus | 2,015 | PhD (doctorat) | Université Grenoble Alpes | France | https://theses.hal.science/tel-01212711 |
run-005 | T03 | Li-ion | non-aqueous | silicon nanowires in a half cell against Li metal (cycling 2) | half cell | Not reported | silicon nanowires | anode | null | null | 1 M LiPF6 EC-DMC + FEC 5% | null | Celgard (polypropylene) + Whatman (glass fibre) | null | Not reported | 20 mV | 2 V | Li metal | 1C | Unclear (cycling ended after 600 cycles (run 2, with FEC); failure cycle unspecified) | lithiation capacity limit 900 mAh.g-1; number of cycles at end of cycling 600 cycles; electrode thickness at end of cycling 16 µm; capacity recovered at 1C at end of cycling 14 % of maximum capacity | Mechanical failure | Cracks severed some nanowires, disconnecting their tips from the current collector, which may partly explain the active-material loss seen in the electrochemical curves. | Suggested by the author | We grew Si nanowires directly on the current collector by CVD (VLS growth), with no binder or additives. We cycled them in a half cell against Li metal in 1 M LiPF6 in EC-DMC with 5 % FEC, with Celgard and glass fibre separators. We ran them at 1C between 20 mV and 2 V, with lithiation capped at 900 mAh/g. As cycling w... | Etude de nanofils de silicium comme matériau d'électrode négative de batterie lithium-ion | Leveau Lucie | 2,015 | PhD (doctorat) | Ecole Polytechnique | France | https://theses.hal.science/tel-01234963 |
run-006 | T04 | Not reported | non-aqueous | Type-2016 coin cell with 10 wt% DBA containing electrolyte, galvanostatic cycling | half cell | Type-2016 coin cell | LiNi0.5Co0.2Mn0.3O2 | cathode | null | null | 1 M LiPF6 EC: EMC 1:1 wt% + 10 wt% DBA | null | Not reported | null | Not reported | Not reported | Not reported | Not reported | 1C | Unclear (no cycle count given; cell could not cycle normally) | capacity lowest capacity | Did not work in that regime | DBA clearly causes a significant rise in cell impedance. | Stated by the author | We assembled Type-2016 coin half cells with an NCM523 cathode and a Li metal disk anode, using 1 M LiPF6 in EC:EMC (1:1 wt%) with 10 wt% DBA added to the electrolyte. After a 2-hour rest we cycled them at 1C. The 10 wt% DBA cell had the lowest capacity and could not be charged and discharged normally. DBA significantly... | Using Amines and Alkanes as Thermal-Runaway Retardants for Lithium-Ion Battery | Shi, Yang | 2,016 | PhD | University of California, San Diego | United States | https://escholarship.org/uc/item/0kr2m740 |
run-007 | T05 | Li-O2 | non-aqueous | Li/2 M LiNO3 in TEGDME/Csp/O2 cell | full cell | custom-built pressurized Swagelok-type Li-O2 cell | Csp air electrode (Carbon Super P) | cathode | null | null | 2 M LiNO3 TEGDME | null | glass fiber (Whatman GF/D) | null | 25 °C | Not reported | Not reported | Li+/Li0 | 50 mA/gC | 15 | negative electrode Li; limited capacity 1000 mAh/gC | Contamination | Gas evolution was very low (> 4 e⁻/gas). | Stated by the author | We cycled a Li-O2 cell with a Li negative electrode and a Carbon Super P air electrode (Csp with 10 wt % PTFE, drop-cast on stainless steel mesh). The electrolyte was 2 M LiNO3 in TEGDME on glass fibre separators, and the cell was a pressurized Swagelok-type cell held at 25 °C. We ran it at 50 mA/gC with the capacity l... | Study and improvement of non-aqueous Lithium-Air batteries via the development of a silicon-based anode | Florent Lepoivre | 2,016 | PhD (doctorat) | Université Pierre et Marie Curie - Paris VI | France | https://theses.hal.science/tel-01474849 |
run-008 | T05 | Li-O2 | non-aqueous | Li | Csp | O2; 0.5 M LiTFSI + 10 mM LiI in DME | full cell | custom-built pressurized Swagelok-type Li-O2 cell | Csp air electrode (Carbon Super P) | cathode | null | null | 0.5 M LiTFSI DME + LiI (10 mM) | null | glass fiber (Whatman GF/D) | null | 25 °C | Not reported | Not reported | Li+/Li0 | 50 mA/gcarbon | Unclear (cycle count not given; cell died after 550 h on test) | negative electrode Li; time to cell death 550 h; capacity limit 1000 mAh/gcarbon | Contamination | Major parasitic reactions caused the failure. | Stated by the author | We cycled a Li-O2 cell with a Li negative electrode and a Carbon Super P air electrode (10 wt % PTFE, on stainless steel mesh) in 0.5 M LiTFSI in DME with 10 mM LiI. The cell was a pressurized Swagelok-type cell with glass fibre separators, held at 25 °C. We ran it at 50 mA/gcarbon with the capacity limited to 1000 mAh... | Study and improvement of non-aqueous Lithium-Air batteries via the development of a silicon-based anode | Florent Lepoivre | 2,016 | PhD (doctorat) | Université Pierre et Marie Curie - Paris VI | France | https://theses.hal.science/tel-01474849 |
run-009 | T05 | Li-O2 | non-aqueous | LixSi // Csp // O2 cell, 2 M LiNO3 in DMA | full cell | pressurized three-electrode cell | LixSi (prelithiated Si|SiO2/Csp/CMC [2:1:1] electrode) | anode | SiO2 surface layer | null | 2 M LiNO3 DMA | null | glass fiber (Whatman GF/D) | null | 25 °C | Not reported | Not reported | Li ring reference electrode | 50 µA/gcarbon | 1–5 | positive electrode Csp (10 % PTFE onto SS mesh, ~ 0.4 mg of Csp); LixSi capacity ~1.55 mAh; capacity limit 1000 mAh/gcarbon; available anode capacity at end of discharge #2 5 %; Si electrode pretreatment 20 h plating sequence | Contamination | Rapid delithiation probably stems from parasitic reactions in the formatting cycles, where LiNO3 in the DMA electrolyte favours Li2O SEI formation on the LixSi anode. | Suggested by the author | We built a LixSi-O2 full cell in a pressurized three-electrode cell with a Li ring reference, using 2 M LiNO3 in DMA on glass fibre separators. The anode was a Si|SiO2/Csp/CMC (2:1:1) electrode made from 100 nm Si particles, given a 20 h plating treatment and prelithiated by galvanostatic discharge to 0 V (about 1.55 m... | Study and improvement of non-aqueous Lithium-Air batteries via the development of a silicon-based anode | Florent Lepoivre | 2,016 | PhD (doctorat) | Université Pierre et Marie Curie - Paris VI | France | https://theses.hal.science/tel-01474849 |
run-010 | T05 | Li-O2 | non-aqueous | LixSi // Csp // O2 cell, 0.5 M LiTFSI in TEGDME | full cell | pressurized three-electrode cell | LixSi (prelithiated Si|SiO2/Csp/CMC [2:1:1] electrode) | anode | SiO2 surface layer | null | 0.5 M LiTFSI TEGDME | null | glass fiber (Whatman GF/D) | null | 25 °C | Not reported | Not reported | Li ring reference electrode | 50 µA/gcarbon | 1–5 | positive electrode Csp (10 % PTFE onto SS mesh, ~ 0.4 mg of Csp); LixSi capacity ~1.55 mAh; capacity limit 1000 mAh/gcarbon; available anode capacity at end of discharge #2 28 %; Si electrode pretreatment 20 h plating sequence | Contamination | In the TEGDME-based system, cycle life is limited by side reactions at the air electrode, such as carbon corrosion. | Suggested by the author | We built a LixSi-O2 full cell in a pressurized three-electrode cell with a Li ring reference, using 0.5 M LiTFSI in TEGDME on glass fibre separators. The anode was a Si|SiO2/Csp/CMC (2:1:1) electrode made from 100 nm Si particles, given a 20 h plating treatment and prelithiated by galvanostatic discharge to 0 V (about ... | Study and improvement of non-aqueous Lithium-Air batteries via the development of a silicon-based anode | Florent Lepoivre | 2,016 | PhD (doctorat) | Université Pierre et Marie Curie - Paris VI | France | https://theses.hal.science/tel-01474849 |
run-011 | T05 | Li-O2 | non-aqueous | Ohara cell: LixSi | LP30 + 10 % FEC | LATP | 0.5 M LiTFSI in TEGDME | Csp | O2 | full cell | two-compartment Ohara cell with pressurized gas reservoir | LixSi (prelithiated Si|SiO2/Csp/CMC electrode) | anode | SiO2 surface layer | null | 1 M LiPF6 ethylene carbonate / dimethyl carbonate [1:1] weight ratio + FEC (10 %) | null | Unclear (separator material not given; wetted with LP30 + 10 % FEC) | null | 25 °C | 0.5 V | Not reported | Not reported | 50 µA/gcarbon | 3 | cathode-side electrolyte 0.5 M LiTFSI in TEGDME; solid electrolyte interlayer LICGS, LATP-type, 200 µm thick, Ohara Inc.; LixSi capacity ~1.5 mAh; capacity limit 1000 mAh/gcarbon | Contamination | Li-consuming side reactions, not offset by the high LixSi electrode loading, raised the anode potential and so dropped the full-cell voltage. | Stated by the author | We built a LixSi-O2 cell in a two-compartment Ohara cell with a pressurized gas reservoir. The lower compartment held a prelithiated Si|SiO2/Csp/CMC electrode made from 100 nm Si and discharged to 0 V (about 1.5 mAh), with a separator soaked in LP30 (1 M LiPF6 in EC/DMC) plus 10 % FEC. A 200 µm LATP-type solid electrol... | Study and improvement of non-aqueous Lithium-Air batteries via the development of a silicon-based anode | Florent Lepoivre | 2,016 | PhD (doctorat) | Université Pierre et Marie Curie - Paris VI | France | https://theses.hal.science/tel-01474849 |
run-012 | T06 | Li-metal | solid state | PEO-b-PSTFSI BCE-lithium symmetric cell | symmetric cell | pouch | PEO-b-PSTFSI (Si-EO) single-ion diblock copolymer electrolyte | solid electrolyte | null | null | null | PEO-b-PSTFSI (Si-EO) | null | Not reported | 90 °C | null | null | null | 0.175 mA.cm-2 | 37 | charge passed 197 C.cm-2; pre-conditioning cycles 15 cycles; pre-conditioning current density 0.02 mA.cm-2; ionic conductivity during cycling ~2.7e-05 S.cm-1; Rel ~240 Ω.cm2; interface resistance after charge, first cycle 1263 Ω.cm-2; interface resistance after charge, last cycle 970 Ω.cm-2; transference number 1; thic... | Short circuit | The short circuit was probably caused by local variations in current density, which may stem from varying SEI properties. | Suggested by the author | We made a single-ion diblock copolymer electrolyte, PEO-b-PSTFSI, by anionic polymerization and melt-pressed it into a membrane (typically 50–100 µm thick). We sandwiched it between 150 µm Li chips, pre-pressed at room temperature, in a symmetric pouch cell. At 90 °C, after 15 pre-conditioning cycles at 0.02 mA cm-2, w... | Study of a buffer layer based on block copolymer electrolytes, between the lithium metal and a ceramic electrolyte for aqueous Lithium-air battery | Louise Frenck | 2,016 | PhD (doctorat) | Université Grenoble Alpes | France | https://theses.hal.science/tel-01532066 |
run-013 | T07 | Zn-air | aqueous | in-operando Zn-air cell, zinc tip anode and carbon cathode with a micro porous hydrophilic polypropylene membrane separator between them | half cell | in-situ cell inside a 6 mm wide Kapton® polyimide tube | zinc | anode | null | null | 5 M KOH water | null | hydrophilic microporous polypropylene membrane; mean pore size 0.5 µm, thickness 100 µm | null | room temperature | Not reported | Not reported | Not reported | 10 mA | 2 | ZnO concentration 0.15 M; current density 20 mA/cm2; half cycle duration 15 min; time to first (intermittent) short circuit, into first dissolution step 240 s; time to complete short circuit, into second deposition step 656 s | Short circuit | Detached dendrites built up on the membrane and created an electron-conducting path linking anode and counter electrode, short-circuiting the cell. | Stated by the author | We ran an in-operando Zn-air half cell inside a 6 mm Kapton tube with 5 M KOH and 0.15 M ZnO in water. The anode was a Zn rod machined to a ~200 µm tip, facing a carbon counter electrode across a microporous hydrophilic polypropylene membrane (0.5 µm pores, 100 µm thick). At room temperature we applied 10 mA (about 20 ... | Advanced 3D Imaging and Quantification of Battery Materials | Biton, Moshiel | 2,017 | PhD | Imperial College London | United Kingdom | https://doi.org/10.25560/45350 |
run-014 | T08 | Li-ion | non-aqueous | 5 nm Al2O3 coated 1-mm thick LFP electrode against lithium | half cell | Not reported | LiFePO4 | cathode | alumina (Al2O3) | null | 1 M LiPF6 EC: DMC (1:1 wt.%) | null | Not reported | null | Not reported | Not reported | Not reported | Not reported | C/20 | 20 | Al2O3 thickness 5 nm; porosity 44 %; average pore size 12 µm; discharge capacity at 20th cycle 18 mAh/g; capacity retention 13 %; columbic efficiency 69 % | Interfacial failure | The thick insulating layer is thought to raise charge-transfer resistance, blocking lithium-ion diffusion across the active material/electrolyte interface. | Suggested by the author | We made a 1-mm thick LiFePO4 electrode with 10 wt.% carbon by spark plasma sintering, giving 44% porosity and an average pore size of 12 µm. We then coated it throughout with 5 nm of Al2O3 by atomic layer deposition. We cycled it in a half cell against lithium in 1 M LiPF6 in EC:DMC (1:1 wt.%) at C/20. By the 20th cycl... | Thick binder free electrodes for Li-ion battery using Spark Plasma Sintering and templating approach | Rakesh Elango | 2,018 | PhD (doctorat) | Université de Picardie Jules Verne | France | https://theses.hal.science/tel-03647555 |
run-015 | T08 | Na-ion | non-aqueous | NVPF/Na | half cell | Not reported | Na3V2(PO4)2F3 (NVPF) | cathode | carbon | null | 1 M NaPF6 EC: DMC (1:1) + 3% Fluoroethylene carbonate (FEC) | null | 2 layers of glass fiber separators | null | Not reported | 2.5 V | 4.3 V | Na | C/20 | 2 | porosity 43 %; pore size 5–10 µm; electrode thickness 0.75 mm; first discharge capacity 113 mAh/g; first-cycle areal capacity 19.6 mAh/cm2; repetitive cells failing the same way 2 cells | Short circuit | Dendrites formed on the sodium metal anode. | Stated by the author | We built a Na3V2(PO4)2F3 (NVPF) / sodium metal half cell using a thick electrode of sol-gel carbon-coated NVPF, made by spark plasma sintering with NaCl templating (50:40:10 vol.% NVPF:NaCl:carbon). The electrode was about 0.75 mm thick with 43% porosity. The electrolyte was 1 M NaPF6 in EC:DMC (1:1) with 3% FEC, with ... | Thick binder free electrodes for Li-ion battery using Spark Plasma Sintering and templating approach | Rakesh Elango | 2,018 | PhD (doctorat) | Université de Picardie Jules Verne | France | https://theses.hal.science/tel-03647555 |
run-016 | T08 | Li-ion | non-aqueous | Sn-Sb/Li | half cell | Not reported | Sn-Sb alloy (SnSb) | anode | null | null | 1 M LiPF6 EC: DMC (1:1 wt.%) | null | 2 layers of glass fiber separator | null | Not reported | 0.01 V | 1 V | metallic lithium | C/20 | 2 | electrode thickness 0.65 mm; porosity 51 %; first-cycle discharge capacity 714 mAh/g; first-cycle areal capacity 46.2 mAh/cm2; cells showing the same failure 2 cells | Interfacial failure | An unstable SEI layer formed because discharge was carried down to a low potential near zero. | Stated by the author | We ball-milled Sn and Sb powders (1:1 molar) into an SnSb alloy and mixed it with NaCl and sp-carbon (50:40:10 vol.%). We spark plasma sintered the mix at 350 °C under 10 kN for 5 min in Ar, giving a 0.65 mm thick electrode with 51% porosity and a loading of 228 mg/cm2. We tested it in a half cell against metallic lith... | Thick binder free electrodes for Li-ion battery using Spark Plasma Sintering and templating approach | Rakesh Elango | 2,018 | PhD (doctorat) | Université de Picardie Jules Verne | France | https://theses.hal.science/tel-03647555 |
run-017 | T09 | Li-ion | non-aqueous | V7/1.2k/PG electrode vs Li metal foil, 2325 coin cell | half cell | 2325 coin cell | V7 Si alloy (3M V7 alloy) | anode | null | null | 1 M LiPF6 EC:DEC:FEC, volume ratio 3:6:1 | null | two layers of Celgard-2301 and one layer of BMF (polypropylene blown microfiber separator) | null | Not reported | 0.005 V | 0.9 V | Li/Li+ | C/5 | Unclear (no failure cycle; ~10% initial discharge capacity retained over 100 cycles) | binder NaPAA, MW 1.2k; slurry solvent propylene glycol (PG); D50 12.15 µm; discharge capacity retention ~10 %; test length 100 cycles | Mechanical failure | Binder was lost because the slurry viscosity was low, compromising V7 electrode mechanical integrity and causing poor cycling. | Stated by the author | We made V7 Si-alloy electrodes (D50 12.15 µm) with 1.2k molecular weight NaPAA binder at 9:1 by weight, using propylene glycol as the slurry solvent. We mixed the slurry in a planetary mill and coated it onto Cu foil at about 2 mg/cm2 of active material. We tested the electrodes in 2325 coin half cells against Li metal... | Binder Effects on Si-Alloy Electrode Performance | Wei, Congxiao | 2,019 | MSc | Dalhousie University | Canada | https://hdl.handle.net/10222/80012 |
run-018 | T10 | Li-ion | non-aqueous | Li//LCO cells | half cell | coin cells | LCO-5 (stoichiometric LCO, (Li/Co)th = 0.98) | cathode | null | null | 1 M LiPF6 EC:DEC:DMC | null | Not reported | null | Not reported | 3 V | 4.8 V | Li+/Li | C/20 | Unclear (cells died fast cycling to 4.8 V; no data past cycle 10) | no data after cycle 10; coin cells were assembled for each test 3–4 | Degradation | The rapid cell death may be linked to structural instability within the high-voltage operating window. | Suggested by the author | We cycled stoichiometric LiCoO2 (LCO-5, Li/Co 0.98, made by a solid-state route) in Li//LCO coin cells with a pure lithium counter electrode and 1 M LiPF6 in EC:DEC:DMC. The electrodes were 90:5:5 wt% LCO:C:PVDF, cast from an NMP slurry onto 30 µm aluminium at about 10 mg/cm2 and dried overnight under vacuum at 120 °C.... | Investigation of structural failure mechanisms of LiCoO2 at high voltage and material optimization through aluminum doping | Marie Duffiet | 2,019 | PhD (doctorat) | Université de Bordeaux | France | https://theses.hal.science/tel-03259019 |
run-019 | T11 | Zn-MnO2 | non-aqueous | fully printed MnO2 cathode | 4-layer printed 0.3m [EMIM]+[OTf]− GPE (90µm) | printed Zn anode (final cells) | full cell | coin (2032) | printed γ-MnO2 cathode (ball-milled and sieved) | cathode | null | null | 0.3 m Zn(OTf)2 [EMIM]+[OTf]− ionic liquid in PVDF-HFP gel | null | 4-layer printed PVDF-HFP gel polymer electrolyte (no separate separator) | null | Not reported | 1 V | 1.8 V | full-cell voltage | Not reported | Not reported | discharge/charge current (final cells) 100 µA; GPE thickness 90 µm; GPE layers 4 | Short circuit | Cells displayed evidence of electrical shorts through the gel polymer electrolyte (GPE), with potentials falling to nearly zero at failure. | Stated by the author | We fully printed Zn-MnO2 cells in 2032 coin cells with a ball-milled, sieved γ-MnO2 cathode (81 wt% MnO2, 12 wt% AB, 7 wt% PVDF-HFP), four printed layers of PVDF-HFP gel electrolyte of 0.3 m Zn(OTf)2 in [EMIM]+[OTf]− (about 90 µm), and a printed Zn anode. We cycled them between 1.0 and 1.8 V at 100 µA. The cells that f... | Optimization and Characterization of a Layer-by-Layer, Fully Printed, Secondary Zn-MnO2 Battery with an Ionic Liquid Gel Polymer Electrolyte for Internet of Things Applications | Kim, Bernard Jeongkyu | 2,019 | PhD | University of California, Berkeley | United States | https://escholarship.org/uc/item/9sm9j0j2 |
run-020 | T12 | Li-metal | solid state | Cu/Li/LLZO/LLZO+LCO (collecteur feuille d’or) | full cell | pouch cell | LiCoO2 (LCO) | cathode | null | null | null | LLZO, pellet densified by CUC (1.1 mm, 96%) | densified LLZO pellet | Not reported | 60 °C | Not reported | 4.4 V | Not reported | C/50 | 1 | carbon black (Super P®) 2 wt%; LCO areal loading ~7 mg/cm2; positive electrode compaction pressure 50 MPa; applied current 18 µA; internal resistance at 60 °C 20 kΩ; time before reaching the upper limit 2 minutes | Did not work in that regime | The positive electrode was indeed the source of the failure. | Stated by the author | We built an all-solid-state Cu/Li/LLZO/LLZO+LCO full cell on a densified LLZO pellet (1.1 mm, 96 % dense) that already carried the Li metal. It used a gold foil as the positive collector and was sealed under vacuum in a pouch. For the positive composite we made an ink of 70 wt% ball-milled commercial LCO and 30 wt% LLZ... | Batterie tout solide pour application automobile : processus de mise en forme et étude des interfaces | Ognjen Hajndl | 2,019 | PhD (doctorat) | Université Grenoble Alpes | France | https://theses.hal.science/tel-02171564 |
run-021 | T12 | Li-metal | solid state | Au / LCO+LLZO / LLZO / Li / Cu | full cell | pouch cell | LCO | cathode | null | null | null | LLZO (layer densified by CUC in one step with the composite) | Not reported | Not reported | 25 °C | Not reported | 4.6 V | Not reported | C/167 | 1 | applied current 20 µA; current density 18 µA/cm2; time before the potential drop 4 heures; exchanged capacity 77 µAh; LCO areal loading (assumed) ~19 mg/cm2; total resistance at 25 °C ~40 kΩ; Constant applied pressure (CUC) 126 MPa | Short circuit | A lithium dendrite most likely formed. | Suggested by the author | We densified a 50/50 LLZO/LCO composite (100 mg) between two LLZO layers in one step (126 MPa, 800 °C for 20 min). We then abraded the top layer and pressed a gold foil onto it at 74 MPa, and sealed the finished Au / LCO+LLZO / LLZO / Li / Cu full cell under vacuum in a pouch. Its total resistance at 25 °C was about 40... | Batterie tout solide pour application automobile : processus de mise en forme et étude des interfaces | Ognjen Hajndl | 2,019 | PhD (doctorat) | Université Grenoble Alpes | France | https://theses.hal.science/tel-02171564 |
run-022 | T13 | Li-metal | solid state | Li || Co400p-SO3 + DMPEG || Li | symmetric cell | coin | Co400p-SO3 + DMPEG | solid electrolyte | null | null | null | Co400p-SO3 + DMPEG | Not reported | Not reported | 80 °C | null | null | null | 0.2 mA.cm-2 | Unclear (cycle count not given; short circuit followed instability at 0.2 mA.cm-2) | stable up to 400 h; DMPEG content 36 wt.%; EO/Li 23; DMPEG MW 1000 g/mol; thickness 100–120 µm; membrane casting cast into membrane from a solution of 0.2 g copolymer in DMSO, dried under vacuum at 80 °C for 48 h | Short circuit | The cell lost stability and polarized once the current density reached 0.2 mA.cm-2. | Stated by the author | We made the Co400p-SO3 copolymer by a two-step polycondensation. We cast the lithiated polymer from DMSO into 100–120 µm membranes, dried them under vacuum at 80 °C for 48 h, and added 36 wt.% DMPEG (1000 g/mol, EO/Li = 23). We tested the membrane in a symmetric Li || Co400p-SO3 + DMPEG || Li coin cell at 80 °C, steppi... | Development and characterization of safety and versatile electrolytes for lithium and post lithium batteries | Hoang Phuong Khanh Ngo | 2,019 | PhD (doctorat) | Université Grenoble Alpes | France | https://theses.hal.science/tel-02475732 |
run-023 | T14 | Li-ion | Not reported | NbSnSb/LiCoO2 full cell | full cell | Not reported | NbSnSb | anode | null | null | Not reported | Not reported | Not reported | Not reported | 25 °C | Not reported | Not reported | Not reported | 81 mA.g-1NbSnSb | Unclear (capacity dropped sharply beyond 60 cycles; exact failure cycle not given) | positive electrode LiCoO2; positive electrode potential > 5 V | Interfacial failure | Lithium, limited to the amount supplied by the initial LiCoO2, was probably trapped continuously in the SEI on the NbSnSb electrode during cycling. | Suggested by the author | We cycled a full cell of mechanically milled NbSnSb against LiCoO2 at 25 °C, at 81 mA/g of NbSnSb. It held about 500 mAh/g for around 55 cycles. Beyond about 60 cycles, the faradaic efficiency fell and the capacity dropped drastically, while the positive electrode potential kept climbing to above 5 V. We think lithium,... | Batteries à forte densité d'énergie utilisant un électrolyte gélifié, présentant une longue durée de vie et une sécurité renforcée | Gaël Coquil | 2,019 | PhD (doctorat) | Université Montpellier | France | https://theses.hal.science/tel-02475734 |
run-024 | T14 | Li-ion | non-aqueous | antimony electrode / 5% POE 40% LiPF6 membrane / lithium electrode, two-electrode Swagelok | half cell | two-electrode Swagelok | Sb | anode | null | null | 1 M LiPF6 EC : PC : 3DMC + 5 % FEC + 1 % VC | null | gelled polymer membrane (separator and electrolyte) | null | 25 °C | 0 V | 1.5 V | Li+/Li | C/10 | Not reported | gelled polymer electrolyte 5% POE 40% LiPF6; current density 22 mA.g-1Sb | Did not work in that regime | Room-temperature ionic conductivity of the polymer electrolytes seems too low for efficient Li+ migration at the applied current densities. | Suggested by the author | We tested a 5% POE 40% LiPF6 gelled polymer electrolyte membrane, acting as both separator and electrolyte, between an antimony electrode and lithium in a two-electrode Swagelok cell. The liquid electrolyte was 1 M LiPF6 in EC:PC:3DMC + 5% FEC + 1% VC. The antimony electrode was 70% active material, 12% CMC, 9% carbon ... | Batteries à forte densité d'énergie utilisant un électrolyte gélifié, présentant une longue durée de vie et une sécurité renforcée | Gaël Coquil | 2,019 | PhD (doctorat) | Université Montpellier | France | https://theses.hal.science/tel-02475734 |
run-025 | T14 | Li-ion | non-aqueous | antimony electrode / 5% POE 60% LiPF6 membrane / lithium electrode, two-electrode Swagelok | half cell | two-electrode Swagelok | Sb | anode | null | null | 1 M LiPF6 EC : PC : 3DMC + 5 % FEC + 1 % VC | null | gelled polymer membrane (separator and electrolyte) | null | 25 °C | 0 V | 1.5 V | Li+/Li | C/10 | Not reported | gelled polymer electrolyte 5% POE 60% LiPF6; current density 22 mA.g-1Sb | Did not work in that regime | Room-temperature ionic conductivity of the polymer electrolytes seems too low for efficient Li+ migration at the applied current densities. | Suggested by the author | We tested a 5% POE 60% LiPF6 gelled polymer electrolyte membrane, acting as both separator and electrolyte, between an antimony electrode and lithium in a two-electrode Swagelok cell. The liquid electrolyte was 1 M LiPF6 in EC:PC:3DMC + 5% FEC + 1% VC. The antimony electrode was 70% active material, 12% CMC, 9% carbon ... | Batteries à forte densité d'énergie utilisant un électrolyte gélifié, présentant une longue durée de vie et une sécurité renforcée | Gaël Coquil | 2,019 | PhD (doctorat) | Université Montpellier | France | https://theses.hal.science/tel-02475734 |
run-026 | T14 | Li-ion | non-aqueous | antimony electrode / 5% POE 40% LiPF6 membrane / lithium electrode, two-electrode Swagelok | half cell | two-electrode Swagelok | Sb | anode | null | null | 1 M LiPF6 EC : PC : 3DMC + 5 % FEC + 1 % VC | null | gelled polymer membrane (separator and electrolyte) | null | 60 °C | 0 V | 1.5 V | Li+/Li | C/10 | 1 | gelled polymer electrolyte 5% POE 40% LiPF6; current density 22 mA.g-1Sb | Did not work in that regime | May stem from reduction and/or a specific degradation of the polymer, the material's low ionic conductivity, or a poor electrode–electrolyte interface. | Suggested by the author | We tested a 5% POE 40% LiPF6 gelled polymer electrolyte membrane, acting as both separator and electrolyte, between an antimony electrode and lithium in a two-electrode Swagelok cell. The liquid electrolyte was 1 M LiPF6 in EC:PC:3DMC + 5% FEC + 1% VC. The antimony electrode was 70% active material, 12% CMC, 9% carbon ... | Batteries à forte densité d'énergie utilisant un électrolyte gélifié, présentant une longue durée de vie et une sécurité renforcée | Gaël Coquil | 2,019 | PhD (doctorat) | Université Montpellier | France | https://theses.hal.science/tel-02475734 |
run-027 | T14 | Li-ion | non-aqueous | antimony electrode / 5% POE 60% LiPF6 membrane / lithium electrode, two-electrode Swagelok | half cell | two-electrode Swagelok | Sb | anode | null | null | 1 M LiPF6 EC : PC : 3DMC + 5 % FEC + 1 % VC | null | gelled polymer membrane (separator and electrolyte) | null | 60 °C | 0 V | 1.5 V | Li+/Li | C/10 | 3 | gelled polymer electrolyte 5% POE 60% LiPF6; current density 22 mA.g-1Sb | Interfacial failure | Attributed to a resistive passivation layer forming on the negative electrode, probably via secondary polymer-chain cross-linking, which irreversibly trapped Li+ and blocked cycling. | Suggested by the author | We tested a 5% POE 60% LiPF6 gelled polymer electrolyte membrane, acting as both separator and electrolyte, between an antimony electrode and lithium in a two-electrode Swagelok cell. The liquid electrolyte was 1 M LiPF6 in EC:PC:3DMC + 5% FEC + 1% VC. The antimony electrode was 70% active material, 12% CMC, 9% carbon ... | Batteries à forte densité d'énergie utilisant un électrolyte gélifié, présentant une longue durée de vie et une sécurité renforcée | Gaël Coquil | 2,019 | PhD (doctorat) | Université Montpellier | France | https://theses.hal.science/tel-02475734 |
run-028 | T14 | Li-ion | non-aqueous | three-electrode Swagelok, LiCoO2 (working) / polymer electrolyte 5% POE 60% LiPF6 / graphite (counter), lithium reference | full cell | three-electrode Swagelok | LiCoO2 | cathode | null | null | 1 M LiPF6 EC : PC : 3DMC + 5 % FEC + 1 % VC | null | 5% POE 60% LiPF6 polymer electrolyte, deposited on the positive electrode | null | 25 °C | 3 V | 4.2 V | Li+/Li | C/20 | 1 | negative electrode graphite (90% graphite / 10% PVDF, copper current collector); reference electrode lithium; current density 14 mA.g-1LiCoO2 | Interfacial failure | Attributed to a resistive passivation layer forming on the negative electrode, probably via secondary polymer-chain cross-linking, which irreversibly trapped Li+ and blocked cycling. | Suggested by the author | We assembled a three-electrode Swagelok full cell with a LiCoO2 working electrode, a graphite counter electrode and a lithium reference. The electrodes were separated by a 5% POE 60% LiPF6 gelled polymer electrolyte deposited on the positive electrode, and the liquid electrolyte was 1 M LiPF6 in EC:PC:3DMC + 5% FEC + 1... | Batteries à forte densité d'énergie utilisant un électrolyte gélifié, présentant une longue durée de vie et une sécurité renforcée | Gaël Coquil | 2,019 | PhD (doctorat) | Université Montpellier | France | https://theses.hal.science/tel-02475734 |
run-029 | T15 | Li-ion | non-aqueous | Li2TiS3 (unpressed) electrode half cell vs Li+/Li | half cell | coin cell | Li2TiS3 (disordered rocksalt) | cathode | null | null | 1 M LiPF6 EC:PC:DMC 1:1:3 by volume | null | Unclear (Celgard® 2400 (polypropylene) and Viledon® (polyolefin), Φ 16.5 mm; arrangement not given) | null | 22 °C | 1.5 V | 3 V | Li+/Li | C/10 | Unclear (capacity faded quickly after 3 cycles; total cycle count not given) | null | Contamination | A reaction between sulfur and the electrolyte may explain the short cycle life of these Li2TiS3 cells. | Suggested by the author | We made Li2TiS3 by dry mechanochemical synthesis (20 h planetary ball milling), coated it as an 80:10:10 slurry in the glovebox, and left the electrodes unpressed. We cycled them in coin half cells against Li foil in 1 M LiPF6 in EC:PC:DMC (1:1:3 by volume) at C/10 between 1.5 and 3 V vs Li+/Li, at 22 °C. The cells los... | Synthesis and characterization of new positive electrode materials for Li-ion high energy applications | Yagmur Celasun | 2,020 | PhD (doctorat) | Université Grenoble Alpes [2020-....] | France | https://theses.hal.science/tel-03080208 |
run-030 | T15 | Li-ion | non-aqueous | Li2TiSe2S electrode half cell vs Li+/Li, coin cell | half cell | coin cell | Li2TiSe2S (Se-substituted disordered rocksalt Li2TiS3) | cathode | null | null | 1 M LiPF6 EC:PC:DMC 1:1:3 by volume | null | Unclear (Celgard® 2400 (polypropylene) and Viledon® (polyolefin), Φ 16.5 mm; arrangement not given) | null | 22 °C | 1.5 V | 3 V | Li+/Li | C/10 | 2 | capacity retained at end of 2nd cycle 80 % | Contamination | Changes in electrode morphology and Tix(Se-S)y impurities point to possible parasitic reactions during discharge. | Suggested by the author | We made Li2TiSe2S by wet mechanochemical synthesis, milling Li2S, Ti and Se in anhydrous hexane at 510 rpm for 20 h. We coated it as an 80:10:10 slurry on Al foil in the glovebox and pressed the electrodes at 10 tons. We cycled coin half cells against Li foil in 1 M LiPF6 in EC:PC:DMC (1:1:3 by volume) at C/10 between ... | Synthesis and characterization of new positive electrode materials for Li-ion high energy applications | Yagmur Celasun | 2,020 | PhD (doctorat) | Université Grenoble Alpes [2020-....] | France | https://theses.hal.science/tel-03080208 |
run-031 | T16 | Li-ion | solid state | LFP/GPE/LTO full cell | full cell | coin (CR2032) | PEGDA/PC/LiTFSI gel polymer electrolyte, composition C5 (20/50/30 wt%) with 2 wt% LiBOB | solid electrolyte | null | null | null | UV-crosslinked PEGDA/PC/LiTFSI GPE, C5 (20/50/30 wt%) + 2 wt% LiBOB | none | Not reported | Not reported | 1.2 V | 2.4 V | LTO | 0.1 C | 1–10 | discharge capacity over 10 cycle 10 mAh/g; 1st cycle discharge capacity 69 mAh/g; coulombic efficiency 77 %; room temperature ionic conductivity 0.0024 S/cm; preparation atmosphere ambient-conditions, without the inert atmosphere | Degradation | Gel polymer electrolyte breakdown caused the capacity fade, as LSV measurement of its electrochemical stability window showed. | Stated by the author | We assembled an LFP/GPE/LTO full cell in a CR2032 coin cell without a separator. A UV-crosslinked PEGDA/PC/LiTFSI gel polymer electrolyte, composition C5 (20/50/30 wt%) with 2 wt% LiBOB, served as both electrolyte and separator. The 80:10:10 electrodes were doctor-bladed with a 120 μm spacer, and we prepared the electr... | Development of Stable Gel Polymer and Flame-Resistant Electrolytes Towards Enabling the Assembling of Lithium-Ion Batteries Under Open-Air Conditions | Lee, Seungjin | 2,020 | PhD | University of California, Riverside | United States | https://escholarship.org/uc/item/37w1m4kp |
run-032 | T17 | Li-ion | solid state | In | LPS | LZO-coated NMC/LPS/CNF composite cathode, custom pressure cell | full cell | custom-made pressure cell (PEEK cylinder, 8 mm inner diameter, stainless-steel rod current collectors) | LiNi0.5Mn0.3Co0.2O2 (NMC) | cathode | amorphous Li-Zr-oxide (LZO), Li2O–ZrO2, 6 - 8 nm | null | null | amorphous 75Li2S-25P2S5 (LPS) | cold-pressed LPS electrolyte layer (35 mg) | ~5 MPa | Not reported | Unclear (two references given: 1.4 V vs. In, 2 V vs. Li/Li+) | 3.7 V | In | 0.05 mA/cm2 | 30–40 | discharge capacity after drop < 20 mAh g-1; capacity after re-pressing at 300 MPa ~80 mAh g-1; RMF after 50 cycles 3283 Ω; void volume after 50 cycles 12.41 % of total volume; contact loss area after 50 cycles 10.4 % of total cathode surface area; cathode particle size ~12 µm; cathode composite mass ~5 mg; top-of-charg... | Mechanical failure | This result shows unambiguously that mechanical degradation contributes in a major way to capacity fade in ASSB cycling. | Stated by the author | We built In | LPS | NMC532 solid-state full cells in a custom PEEK pressure cell, with a cold-pressed composite cathode of NMC532 coated with 6 to 8 nm of amorphous Li-Zr-oxide, 75Li2S-25P2S5 (LPS) and carbon nanofiber (60:35:5) on a cold-pressed LPS separator. We cycled them at 0.05 mA/cm2 up to 3.7 V vs. In under abo... | Improving the Energy Density and Cycling Stability of All-Solid-State Batteries | Shi, Tan | 2,020 | PhD | University of California, Berkeley | United States | https://escholarship.org/uc/item/75s4q169 |
run-033 | T18 | Li-metal | solid state | Li-SEO-Li symmetric cell | symmetric cell | polypropylene-lined aluminum pouch | lithium metal foil | anode | null | null | null | nanostructured PS-b-PEO (SEO) block copolymer with dissolved LiTFSI | null | Not reported | 90 °C | Not reported | Not reported | Not reported | 0.32 mA cm-2 | null | polymer SEO(115-172); conditioning cycles 14 cycles; polarization direction one direction; time to failure (Fig. 2.1a cell) ~17 h; time to failure (Fig. 2.5a cell) 0.7 h; Cd (Fig. 2.4b cell) 18.7 C cm-2; average Cd (Table 2.2) 7.18 C cm-2 | Short circuit | The cells failed by short circuit as lithium protrusions grew. | Stated by the author | We made Li|SEO|Li symmetric cells by pressing three layers of lithium foil onto nickel foil at 130 MPa. The electrolyte was a nanostructured polystyrene-block-poly(ethylene oxide) block copolymer, SEO(115-172), with dissolved LiTFSI, and each cell was vacuum-sealed in a polypropylene-lined aluminum pouch. After 14 cond... | Lithium Electrodeposition through Rigid Block Copolymer Electrolytes | Maslyn, Jacqueline Avery | 2,020 | PhD | University of California, Berkeley | United States | https://escholarship.org/uc/item/823727zm |
run-034 | T19 | Li-ion | non-aqueous | Swagelok cell; TiS3 powder electrode with 20 wt% Csp, ground by hand | half cell | Swagelok | TiS3 | cathode | null | null | 1 M LiPF6 ethylene carbonate/dimethyl carbonate in 1:1 weight ratio | null | Whatman GF/D borosilicate glass fiber membrane | null | Not reported | 1.7 V | 3 V | Li | C/20 | 1–25 | capacity ~370 mAh·g−1 | Degradation | Capacity faded quickly because the S²⁻/S₂²⁻ redox is structurally irreversible and kinetically slow. | Stated by the author | We made TiS3 by reacting TiS2 or Ti powder with sulfur (20 wt% excess) in a vacuum-sealed quartz tube at 550 °C for one week. We hand-ground the powder with 20 wt% Csp and cycled it in a Swagelok half cell against metallic Li, using LP30 in a Whatman GF/D glass fibre separator and about 10 mg/cm² of active material. We... | Exploration of ionic conductors and Li-rich sulfides for all-solid-state batteries | Sujoy Saha | 2,020 | PhD (doctorat) | Sorbonne Université | France | https://theses.hal.science/tel-03153280 |
run-035 | T19 | Li-ion | non-aqueous | Li1.13Ti0.57Fe0.3S2 /Li half-cell | half cell | Swagelok | Li1.13Ti0.57Fe0.3S2 | cathode | null | null | 1 M LiPF6 ethylene carbonate/dimethyl carbonate in 1:1 weight ratio | null | Whatman GF/D borosilicate glass fiber membrane | null | Not reported | Not reported | 4.5 V | Li | C/20 | Not reported | cell failure voltage > 3.8 V | Contamination | Failure resulted from decomposition of the sample, or from parasitic reactions or similar side processes. | Stated by the author | We made Li1.13Ti0.57Fe0.3S2 by reacting Li2S, TiS2 and FeS in vacuum-sealed quartz tubes at 750 °C, then hand-ground it for 5 min with 20 wt% Super-P. We cycled it in a Swagelok half cell against Li, using LP30 in a Whatman GF/D separator and about 10 mg/cm² of active material. To widen the voltage range, we charged it... | Exploration of ionic conductors and Li-rich sulfides for all-solid-state batteries | Sujoy Saha | 2,020 | PhD (doctorat) | Sorbonne Université | France | https://theses.hal.science/tel-03153280 |
run-036 | T20 | Li-S | solid state | mLi2S(LiI)-mLPSC-C|mLPSC|In-Li | half cell | Not reported | LiI-coated micron-sized Li2S agglomerates (mLi2S(LiI)) | cathode | LiI | null | null | micron-sized Li6PS5Cl (mLPSC) | null | 2 MPa | Not reported | Not reported | Not reported | In-Li | 0.033 mA cm-2 | 1 | charge capacity 900 mA h g-1; LiI-Li2S molar ratio 1:3 | Interfacial failure | Approaching 900 mA h g-1, the potential passed LPSC (2.1 V vs. In-Li) and LiI (2.3 V vs. In-Li) oxidation potentials, forming low-conductivity, impedance-raising species. | Stated by the author | We built an all-solid-state mLi2S(LiI)-mLPSC-C|mLPSC|In-Li cell. The cathode was micron-sized Li2S agglomerates coated with LiI, made by dissolving LiI and Li2S (1:3 molar) in ethanol and evaporating at 300 °C, then hand-mixed with micron-sized Li6PS5Cl and carbon. We used 12.5 mg of this mixture against In-Li foil und... | Towards High Energy Density Anode-less Lithium Metal Batteries: A Study of Lithium Dendrites Suppression and Elimination | Wang, Chao | 2,021 | PhD | Delft University of Technology | Netherlands | https://doi.org/10.4233/uuid:79489c85-e9be-41ff-b79a-10d2b974fc94 |
run-037 | T21 | Li-S | non-aqueous | Li||S cells, operando EIS during galvanostatic discharge | full cell | coin (2032 type) | sulfur-carbon (S-C) composite (sulfur in integrated ketjen black) | cathode | null | null | 0.2 M LiTFSI DOL/DME with 50/50 vol. ratio + LiNO3, 1.5 wt.% | null | Celgard® 2400 | null | Not reported | 1.7 V | 2.8 V | Li/Li+ | 16 mA g-1 | Not reported | E/S mass ratio 2.4; binder PVP; cathode sulfur areal loading ~6 mg cm-2; capacity at termination 200 mAh g-1; peak charge transfer resistance Rct 1691 ohms; peak interphase resistance Rint 320 ohms | Interfacial failure | Discharge stopped early because of the high charge-transfer resistance (Rct), probably caused by slow Li-ion transport across the interface. | Stated by the author | We built Li||S 2032 coin cells with a sulfur/integrated ketjen black composite cathode (about 6 mg/cm2 sulfur, PVP binder) on Al foil against Li foil, with a Celgard 2400 separator and 0.2 M LiTFSI in DOL/DME (50/50 vol.) with 1.5 wt% LiNO3 at an electrolyte-to-sulfur mass ratio of 2.4. We discharged them at 16 mA/g be... | Understanding the Electrode Electrolyte Interphase for Metal Sulfur Batteries | Zhao, Yifan | 2,021 | PhD | University of California, Riverside | United States | https://escholarship.org/uc/item/84s5m2st |
run-038 | T22 | Li-ion | non-aqueous | NMC 811(non-calendered)/Gr pouch cell | full cell | pouch | NMC 811 (non-calendered electrode) | cathode | null | null | 1 M LiPF6 EC/DEC/EMC 1:1:1 vol. + 0.2M LDFP (LiPO2F2, 1.92 wt.%) | null | Not reported | null | 55 °C | 2.8 V | 4.3 V | Li/Li+ | C/4 | Unclear (failure cycle not given; ~65% capacity left after 110 cycles) | capacity retention ~65 %; behaving similarly up to 30 cycles | Mechanical failure | A reaction with the interphase, yielding LDFP, is thought to cause grain decohesion and loss of contact in the positive electrode. | Suggested by the author | We cycled non-calendered NMC 811/graphite pouch full cells (90 wt.% NMC 811, 6 wt.% C45 carbon black, 4 wt.% PVDF) at 55 °C, at C/4 between 2.8 and 4.3 V. The electrolyte was 1 M LiPF6 in EC/DEC/EMC (1:1:1 vol.) with 0.2 M LDFP (LiPO2F2, 1.92 wt.%). For the first 30 cycles they behaved like the cells without LDFP. Afte... | Nickel-rich NMC materials for lithium-ion batteries : surface reactivity and gas production | Ana Cristina Martinez Maciel | 2,021 | PhD (doctorat) | Université de Picardie Jules Verne | France | https://theses.hal.science/tel-03617814 |
run-039 | T23 | Li-ion | non-aqueous | half cell vs lithium metal, Whatman glass fibre separator, electrolyte EC:PC:3DMC; 5% FEC | half cell | Not reported | SC100 (Si@C, 15 wt% C) | anode | PDA-derived nitrogen-doped disordered carbon | null | EC : PC : 3DMC + 5% FEC | null | Whatman glass fibre | null | Not reported | 0.01 V | 1.5 V | Li+/Li | 500 mA.g-1 | ~20 | initial capacity ~3100 mAh.g-1; stabilised capacity 750 mAh.g-1; carbon content 15 wt%; first formation cycle 100 mA.g-1; floating 0.01 V | Mechanical failure | The fade reflects cracks forming in the electrode film because the volume changes of Li-Si alloying were not damped enough. | Stated by the author | We made a half cell against lithium metal with SC100: core-shell Si@C nanoparticles carrying 15 wt% of nitrogen-doped disordered carbon, a ~5 nm layer derived from polydopamine. We grew the polydopamine on silicon nanoparticles in Tris buffer for 24 h and then annealed under Ar/H2. The electrode was 70 wt% active mater... | Particules core-shell à base de silicium comme matériaux d'anode pour batteries Li-ion | Bastien Rage | 2,021 | PhD (doctorat) | Université Montpellier | France | https://theses.hal.science/tel-03630057 |
run-040 | T23 | Li-ion | non-aqueous | half cell vs lithium metal, Whatman glass fibre separator, electrolyte EC:PC:3DMC; 5% FEC | half cell | Not reported | Si@C-8 wt% carbon | anode | carbon layer (8 wt% C) | null | EC : PC : 3DMC + 5% FEC | null | Whatman glass fibre | null | Not reported | 0.01 V | 1.5 V | Not reported | 500 mA.g-1 | ~20 | stabilised capacity 250 mAh.g-1; carbon content 8 wt%; first formation cycle 100 mA.g-1 | Mechanical failure | The fade reflects cracks forming in the electrode film because the volume changes of Li-Si alloying were not damped enough. | Stated by the author | We made a half cell against lithium metal with core-shell Si@C nanoparticles carrying 8 wt% carbon. The electrode was 70 wt% active material, 18 wt% C65 carbon and 12 wt% CMC, with a Whatman glass fibre separator and EC:PC:3DMC + 5% FEC. After a first cycle at 100 mA/g we cycled at 500 mA/g between 0.01 and 1.5 V. The ... | Particules core-shell à base de silicium comme matériaux d'anode pour batteries Li-ion | Bastien Rage | 2,021 | PhD (doctorat) | Université Montpellier | France | https://theses.hal.science/tel-03630057 |
run-041 | T23 | Li-ion | non-aqueous | half cell vs lithium metal, Whatman glass fibre separator, electrolyte EC:PC:3DMC; 5% FEC | half cell | Not reported | SC100 (Si@C, 15 wt% C) | anode | PDA-derived nitrogen-doped disordered carbon | null | EC : PC : 3DMC + 5% FEC | null | Whatman glass fibre | null | Not reported | 0.01 V | 1.5 V | Li+/Li | 500 mA.g-1 | ~40 | first discharge capacity 1450 mAh.g-1; stabilised capacity before the drop 1000 mAh.g-1; final capacity 200 mAh.g-1; carbon content 15 wt%; basis for capacity calculation 88 wt% electrode film | Mechanical failure | The carbon coatings broke down as a result of the silicon's volume changes. | Stated by the author | We made a half cell against lithium metal with SC100: core-shell Si@C nanoparticles with 15 wt% nitrogen-doped carbon from polydopamine (Tris buffer, 24 h, then annealed under Ar/H2). This time the electrode had only 30 wt% active material, with 29 wt% C65, 29 wt% VGCF carbon fibres and 12 wt% CMC. We used a Whatman gl... | Particules core-shell à base de silicium comme matériaux d'anode pour batteries Li-ion | Bastien Rage | 2,021 | PhD (doctorat) | Université Montpellier | France | https://theses.hal.science/tel-03630057 |
run-042 | T23 | Li-ion | non-aqueous | half cell vs lithium metal (protocol of Ch. 2, § 6.1) | half cell | Not reported | Si@Cp-4 | anode | PDA-derived amorphous carbon (HCl treated) | null | EC : PC : 3DMC + 5% FEC | null | Whatman glass fibre | null | Not reported | 0.01 V | 1.5 V | Li+/Li | 500 mA.g-1 | about twenty cycles | total discharge capacity (1st cycle) 2520 mAh.g-1; stabilised capacity 1000 mAh.g-1; HCl concentration of the acid treatment 8 M; presence of chlorine chlorine from the hydrochloric acid treatment; premier cycle d’activation 100 mA.g-1 | Mechanical failure | Conventionally attributed to electrode-film cracking caused by poor absorption of the silicon's volume changes. | Suggested by the author | We made a half cell against lithium metal with Si@Cp-4. These are Si@C-Co-4 particles (dopamine plus CoCl2, heat-treated under hydrogenated argon) etched in 8 M HCl, which left an amorphous carbon shell and some residual chlorine. The electrode was 70 wt% active material, 18 wt% C65 carbon and 12 wt% CMC, with a Whatma... | Particules core-shell à base de silicium comme matériaux d'anode pour batteries Li-ion | Bastien Rage | 2,021 | PhD (doctorat) | Université Montpellier | France | https://theses.hal.science/tel-03630057 |
run-043 | T24 | Li-metal | solid state | symmetric cell Li(M) coated Li2S / Li6PS5Cl / Li(M) coated Li2S | symmetric cell | PMMA die, 10 mm diameter | Li(M) | anode | Li2S | null | null | Li6PS5Cl (Ampcera) | null | ~6.7 MPa | Not reported | null | null | null | 50 µA.cm-2 | Unclear (cycle count not given; cell short-circuited instantly) | coating solution concentration 0.5 M; current densities tested 50–350 µA.cm-2 | Short circuit | Caused by the Li2S coating's poor mechanical hold on the Li metal. | Stated by the author | We assembled a symmetric Li/Li6PS5Cl/Li cell whose Li electrodes (scraped, laminated Li on Cu) were coated with Li2S by slow evaporation of a 0.5 M Li2S solution in DME. The electrolyte was 100 mg of Li6PS5Cl pressed at 250 MPa in a 10 mm PMMA die. The cell was held at about 6.7 MPa by the clamping vice during testing.... | Étude de la stabilité des interfaces dans les batteries tout-solide au lithium | Cédric Barcha | 2,021 | PhD (doctorat) | Université de Picardie Jules Verne | France | https://theses.hal.science/tel-03945249 |
run-044 | T25 | aqueous Zn battery | aqueous | Zn/Li2SO4-ZnSO4/γ’-V2O5 system | half cell | two-electrode split cell (MTI company) | γ’-V2O5 | cathode | null | null | 3.5 (ZnSO4) + 2.5 (Li2SO4) mole L-1 ZnSO4 + Li2SO4 distilled water | null | AGM (Absorptive Glass Mat NSG Corporation) | null | Not reported | 1 V | 1.6 V | Not reported | C/5 | Unclear (failure cycle not given; capacities reported at cycles 10 and 100) | initial discharge and charge capacity 120 mAh g-1; discharge capacity after 10 cycles 60 mAh g-1; discharge capacity after 100 cycles 40 mAh g-1; pH 4 | Degradation | The capacity fade is possibly linked to dissolution of the γ’-V2O5 active material. | Suggested by the author | We made γ’-V2O5 by a polyol route and cast it on carbon paper (90 wt% active material, 6 wt% PVDF, 4 wt% Ketjen black; about 5 mg/cm2). We used it as the positive electrode of a two-electrode split cell against zinc foil, with an AGM separator and an aqueous electrolyte of 3.5 M ZnSO4 and 2.5 M Li2SO4 at pH 4. We cycle... | Electrochemical properties of vanadium oxide-based cathode materials for Li/Na-ion batteries and aqueous rechargeable zinc batteries | Dauren Batyrbekuly | 2,021 | PhD (doctorat) | Université Paris-Est Créteil Val-de-Marne - Paris 12; Nazarbayev University | France | https://theses.hal.science/tel-04071118 |
run-045 | T26 | Li-ion | non-aqueous | Li∣Si Swagelok-type half cells | half cell | Swagelok-type | Si nanoparticles | anode | null | null | 3.2 m LiFSI C3mpyrFSI (N-propyl-N-methylpyrrolidinium FSI ionic liquid) | null | 25 µm microporous polypropylene membrane (Celgard 3501) and borosilicate glass-fiber (Whatman GF/A) | null | 50 °C | 0.01 V | 1 V | Li | C/10 | Unclear (cycle count not given; rapid fading set in after about 60 cycles) | onset of rapid capacity fading ~60 cycles; specific capacity after 100 cycles 1160 mAhg−1; Formation steps C/40 and C/20 | Interfacial failure | Possibly linked to electrolyte degradation after prolonged cycling, which may alter its intrinsic transport properties, lead to an SEI that is more blocking, or both. | Suggested by the author | We cycled a Li|Si half cell in a Swagelok-type fitting. The Si nanoparticle electrode (71:7:11:9:2 wt%) was mixed as an aqueous slurry in a planetary ball mill and tape-cast onto 25 μm copper foil at about 1.0 mg cm-2. It faced a 0.75 mm Li foil counter electrode, with a Celgard 3501 membrane and a GF/A glass-fibre sep... | Lithium-ion batteries based on silicon anode and ionic liquid electrolytes | Khryslyn Arano | 2,021 | PhD (doctorat) | Université de Nantes; Deakin university (Geelong, Australie) | France | https://theses.hal.science/tel-05324716 |
run-046 | T27 | Li-S | non-aqueous | FeNC@S | Li metal CR2032 coin cell | Not reported | coin (CR2032) | FeNC@S | cathode | null | null | 1 M LiTFSI DOL-DME mixture (1:1, v/v) + 0.2 M LiNO3 | null | Not reported | null | Not reported | 1.6 V | 3 V | Li+/Li | C/10 | ~40 | E/S 9 mL g-1; negative electrode Li metal | Short circuit | The cell suffered internal short circuits linked to lithium dendrite formation and growth. | Stated by the author | We made FeNC by a sacrificial ZIF-8 metal–organic framework route with heat treatment at 1050 °C in Ar and impregnated it with sulfur at 160 °C under N2. We doctor-bladed an 80:10:10 wt% FeNC@S:PVDF:Super P slurry onto carbon-coated Al foil at 3.7 mg cm-2 and dried it at 40 °C. We assembled CR2032 coin cells with Li me... | Design and characterization of novel sulfur host materials for Lithium-sulfur batteries | Sajad Rahimi | 2,022 | PhD (doctorat) | Université Grenoble Alpes [2020-....] | France | https://theses.hal.science/tel-04048676 |
run-047 | T28 | Mg-ion | non-aqueous | Mg3Bi2/Mo6S8 full cell | full cell | coin cell (2032) | Mg3Bi2 | anode | null | null | 0.8 M Mg(TFSI)2 DME | null | glass fiber (Whatman GF/A) | null | Not reported | Not reported | Not reported | Not reported | C/10 | Unclear (fully failed by cycle 20; exact failure cycle not given) | cycles to 50% of initial capacity 13; cycles to complete failure 20; N/P ratio 60; positive electrode Mo6S8 film | Degradation | Possible reasons are bismuth dissolving and migrating to the opposite electrode, or Mg3Bi2 reacting more strongly with the Mg(TFSI)2-in-DME electrolyte. | Suggested by the author | We cycled a Mg3Bi2 | Mo6S8 full cell in a 2032 coin cell with 0.8 M Mg(TFSI)2 in DME at C/10. We made the Mg3Bi2 by mechanical alloying (5 h at 875 rpm) and formed it into a self-standing electrode of 70% alloy, 20% carbon (C65:VGCF 1:1) and 10% PTFE, punched into 8 mm discs. The cell had a large magnesium excess (N/P ... | Alloys for magnesium batteries : from bulk electrode to surface protection | Clément Pechberty | 2,022 | PhD (doctorat) | Université de Montpellier | France | https://theses.hal.science/tel-05425509 |
run-048 | T28 | Mg-ion | non-aqueous | full-cell Mg2Sn/Mo6S8 with an optimized negative electrode | full cell | coin cell (2032) | Mg2Sn (film formulation) | anode | null | null | 0.5 M Mg(TFSI)2 DME | null | glass fiber (Whatman GF/A) | null | 40 °C | Not reported | Not reported | Not reported | C/10 | Unclear (fully failed by cycle 30; exact failure cycle not given) | cycles to complete failure 30; N/P 15; average loading 1.5 mgalloy.cm-2; positive electrode Mo6S8 | Degradation | It is reasonable to assume a lower alloy loading offsets the active-material loss over a shorter span of cycles. | Suggested by the author | We cycled a full cell of a Mg2Sn film electrode against Mo6S8 at 40 °C in a 2032 coin cell, with 0.5 M Mg(TFSI)2 in DME at C/10 and two Whatman GF/A glass fibre separators. The negative electrode was 70% mechanically alloyed Mg2Sn, 25% carbon and 5% PAN, cast from NMP onto 10 µm carbon-coated aluminium foil. It had an ... | Alloys for magnesium batteries : from bulk electrode to surface protection | Clément Pechberty | 2,022 | PhD (doctorat) | Université de Montpellier | France | https://theses.hal.science/tel-05425509 |
run-049 | T28 | Mg-metal | non-aqueous | symmetric cell of treated Mg after 15 min of soaking in 10 mM Bi(OTf)3/DME | symmetric cell | coin cell (2032) | magnesium foil | anode | Bi (from 10 mM Bi(OTf)3/DME, 15 min immersion) | null | 0.5 M Mg(TFSI)2 DME | null | glass fiber (Whatman GF/A) | null | Not reported | Not reported | Not reported | Not reported | 50 µA.cm-2 | Unclear (short circuit after roughly 120 h; number of cycles not given) | time to failure ~120 h; sweep duration 30 min | Short circuit | Probably, low current density lets plating build large magnesium islands on uncoated regions, which more readily bridge the electrodes across the separator. | Suggested by the author | We ran a Mg|Mg symmetric 2032 coin cell with 7 mm magnesium discs. We scratched the discs, dipped them for 15 min in 10 mM Bi(OTf)3 in DME to leave a bismuth coating, dried them for 30 min and rinsed them with DME. The electrolyte was 0.5 M Mg(TFSI)2 in DME with two Whatman GF/A separators, and we polarised the cell at... | Alloys for magnesium batteries : from bulk electrode to surface protection | Clément Pechberty | 2,022 | PhD (doctorat) | Université de Montpellier | France | https://theses.hal.science/tel-05425509 |
run-050 | T28 | Mg-metal | non-aqueous | symmetric cell of Mg after 2 h of soaking in 10 mM saturated Bi(OTf)3/DME | symmetric cell | coin cell (2032) | magnesium foil | anode | Bi (from 10 mM Bi(OTf)3/DME, 2 h immersion) | null | 0.5 M Mg(TFSI)2 DME | null | glass fiber (Whatman GF/A) | null | Not reported | Not reported | Not reported | Not reported | 50 µA.cm-2 | Unclear (short circuit after roughly 160 h; number of cycles not given) | time to failure ~160 h | Short circuit | The lack of alloy formation at the surface and the highly dendritic morphology seen with the bismuth layer may account for the failure. | Suggested by the author | We ran a Mg|Mg symmetric 2032 coin cell with magnesium electrodes soaked for 2 h in saturated 10 mM Bi(OTf)3 in DME. We cycled it in 0.5 M Mg(TFSI)2 in DME at 50 µA/cm² with two Whatman GF/A separators. It was unstable, like the cell with the shorter treatment, and short-circuited after about 160 h of cycling. We think... | Alloys for magnesium batteries : from bulk electrode to surface protection | Clément Pechberty | 2,022 | PhD (doctorat) | Université de Montpellier | France | https://theses.hal.science/tel-05425509 |
run-051 | T29 | Li-ion | Unclear (only δ phase–electrolyte reaction mentioned; battery state not given) | Not reported | half cell | Not reported | Li3FeN2 synthesized with Fe Goodfellow at 750°C for 12 hours | anode | null | null | Unclear (electrolyte mentioned (reacts with δ phase); molarity not specified) Unclear (electrolyte mentioned (reacts with δ phase); salt not specified) Unclear (electrolyte mentioned (reacts with δ phase); solvent not specified) | null | Not reported | null | Not reported | 0.9 V | 1.6 V | Li+/Li | C/10 | 2 | capacity decline over 60 cycles 10 % | Contamination | Experimental results point to an irreversible chemical reaction involving the δ phase. | Stated by the author | We synthesized Li3FeN2 from Goodfellow Fe mixed with Li3N (20% excess), pressed into a pellet and heated at 750 °C for 12 h under N2 with no annealing, and tested it as a Li-ion negative electrode in a half cell. We cycled it galvanostatically at C/10 between 0.9 and 1.6 V vs Li+/Li. Capacity dropped by 14% at the seco... | Structure and Electrochemistry of Lithiated Transition Metal (Mn, Fe, Ni) Nitrides as Materials for Negative Electrode of Lithium Ion Battery | Zhou, Yanlong | 2,022 | PhD (doctorat) | Université Paris-Est Créteil Val-de-Marne - Paris 12 | France | https://theses.hal.science/tel-04740699 |
run-052 | T29 | Li-ion | non-aqueous | CR2032 coin cells like previously described in chapter 2 | half cell | coin (CR2032) | Li3FeN2 (LFN) synthesized with Fe Prolabo at 720°C for 12 hours | anode | null | null | 1 mol L-1 LiPF6 EC : DMC : DEC (1: 1 :1, v) | null | Not reported | null | Not reported | 0.9 V | 1.6 V | Li+/Li | C/10 | 2 | efficiency of first cycle ~90 %; capacity at 10th cycle 100 mAh g-1 | Degradation | Capacity was unexpectedly retained better at higher current rates, which might stem from Fe4+ possibly being unstable in the system. | Suggested by the author | We made Li3FeN2 by solid-state reaction of an Fe and Li3N pellet (1:1.2) at 720 °C for 12 hours under N2. We turned it into dry-processed electrodes of 70% Li3FeN2, 22% carbon black and 8% PTFE. We tested these in CR2032 coin half cells against lithium with 1 mol L-1 LiPF6 in EC:DMC:DEC (1:1:1 by volume), cycling at C/... | Structure and Electrochemistry of Lithiated Transition Metal (Mn, Fe, Ni) Nitrides as Materials for Negative Electrode of Lithium Ion Battery | Zhou, Yanlong | 2,022 | PhD (doctorat) | Université Paris-Est Créteil Val-de-Marne - Paris 12 | France | https://theses.hal.science/tel-04740699 |
run-053 | T29 | Li-ion | Unclear (state not given; source only points to earlier-described procedures) | two-electrode coin cell (CR2025) | half cell | coin cell (CR2025) | Li7MnN4 delithiated with benzoyl chloride (1.5BC, 0.3M, 24h) | anode | null | null | Unclear (molarity not given; only earlier procedures referenced) Unclear (salt not given; only earlier procedures referenced) Unclear (solvent not given; only earlier procedures referenced) | null | Unclear (separator not given; only earlier procedures referenced) | null | Not reported | Not reported | Not reported | Li+/Li | C/20 | Unclear (cycle count not given; later cycles showed poor cycle life) | first oxidation efficiency 50 %; OCV of delithiated material 1.72 V | Degradation | The delithiation conditions were overly harsh, causing irreversible active-material loss and a large quantity of dead mass. | Stated by the author | We chemically delithiated Li7MnN4 (made at 750 °C for 12 h) with benzoyl chloride in acetonitrile (1.5 BC : 1 LMN, 0.3 M, 24 h), which gave a delithiated powder with an OCV of 1.72 V. We made it into an electrode with carbon black and tested it at C/20 in a two-electrode CR2025 coin cell. The first reduction gave a far... | Structure and Electrochemistry of Lithiated Transition Metal (Mn, Fe, Ni) Nitrides as Materials for Negative Electrode of Lithium Ion Battery | Zhou, Yanlong | 2,022 | PhD (doctorat) | Université Paris-Est Créteil Val-de-Marne - Paris 12 | France | https://theses.hal.science/tel-04740699 |
run-054 | T30 | Li-ion | solid state | NMC622/C-Li3InCl6/VGCF | C-Li6PS5Cl | Li0.5In/C-Li6PS5Cl (hetero-structure) | full cell | cylindrical polyetherimide (PEI) body; stainless steel pistons (×2), 8 mm diameter | NMC622 | cathode | Li2O-ZrO2 | null | null | C-Li3InCl6 (solvent-free) in cathode composite; C-Li6PS5Cl separator and anode composite | C-Li6PS5Cl | 1 ton/cm2 | room temperature | 2.1 V | 3.6 V | LiIn/In | C/20 | Unclear (failure cycle not given; 50% capacity loss after 20 cycles) | capacity decay 50 %; cell polarization nearly 4-fold increase; cathode loading 16–20 mg/cm2 | Interfacial failure | The degradation arises because Li3InCl6 is chemically unstable against sulfide solid electrolytes, which forms a passivation interlayer. | Stated by the author | We built an all-solid-state cell with a hand-ground composite cathode of Li2O-ZrO2-coated NMC622, solvent-free made C-Li3InCl6 and VGCF (70:30:5 by weight, 16–20 mg/cm2). The separator was C-Li6PS5Cl and the anode a Li0.5In/C-Li6PS5Cl composite, in a PEI cell body with 8 mm stainless steel pistons under 1 ton/cm2. We c... | In search of the best solid electrolyte-layered oxide pair in all-solid-state batteries | Tuncay Koç | 2,022 | PhD (doctorat) | Sorbonne Université | France | https://theses.hal.science/tel-04137255 |
run-055 | T30 | Li-ion | solid state | NMC622/W-β-Li3PS4/VGCF | W-β-Li3PS4 | Li0.5In/W-β-Li3PS4 | full cell | cylindrical polyetherimide (PEI) body; stainless steel pistons (×2), 8 mm diameter | NMC622 | cathode | Li2O-ZrO2 | null | null | W-β-Li3PS4 (solvent-based) in cathode composite, separator and anode composite | W-β-Li3PS4 | 1 ton/cm2 | room temperature | 2.1 V | 3.6 V | LiIn/In | C/20 | Unclear (failure cycle not given; 71.5% capacity retained after 20 cycles) | capacity decay to 71.5 %; cell polarization 2-fold growth; cathode loading 16–20 mg/cm2 | Degradation | The rapid decay is attributed to carbon driving electrochemical degradation of the solid electrolyte. | Suggested by the author | We built an all-solid-state cell with a hand-ground composite cathode of Li2O-ZrO2-coated NMC622, solvent-based W-β-Li3PS4 and VGCF (70:30:5 by weight, 16–20 mg/cm2). W-β-Li3PS4 was also the separator and part of the Li0.5In composite anode, in a PEI cell body with 8 mm stainless steel pistons under 1 ton/cm2. We cycle... | In search of the best solid electrolyte-layered oxide pair in all-solid-state batteries | Tuncay Koç | 2,022 | PhD (doctorat) | Sorbonne Université | France | https://theses.hal.science/tel-04137255 |
run-056 | T30 | Li-ion | solid state | NMC622/W-Li3InCl6/VGCF | C-Li6PS5Cl | Li0.5In/C-Li6PS5Cl (hetero-structure) | full cell | cylindrical polyetherimide (PEI) body; stainless steel pistons (×2), 8 mm diameter | NMC622 | cathode | Li2O-ZrO2 | null | null | W-Li3InCl6 (water-assisted) in cathode composite; C-Li6PS5Cl separator and anode composite | C-Li6PS5Cl | 1 ton/cm2 | room temperature | 2.1 V | 3.6 V | LiIn/In | C/20 | Unclear (failure cycle not given; 50% loss of initial capacity after 20 cycles) | decay of initial cycle 50 %; cathode loading 16–20 mg/cm2 | Interfacial failure | The degradation arises because Li3InCl6 is chemically unstable against sulfide solid electrolytes, which forms a passivation interlayer. | Stated by the author | We built an all-solid-state full cell with Li3InCl6 only in the cathode. The cathode composite was Li2O-ZrO2-coated NMC622, water-assisted Li3InCl6 (W-Li3InCl6) and VGCF at 70:30:5 by weight, hand-ground for 10 minutes in an agate mortar. It was paired with a C-Li6PS5Cl separator and a Li0.5In/C-Li6PS5Cl anode composit... | In search of the best solid electrolyte-layered oxide pair in all-solid-state batteries | Tuncay Koç | 2,022 | PhD (doctorat) | Sorbonne Université | France | https://theses.hal.science/tel-04137255 |
run-057 | T30 | Li-ion | solid state | NMC622/W-Li3InCl6/VGCF | W-β-Li3PS4 | Li0.5In/W-β-Li3PS4 | full cell | cylindrical polyetherimide (PEI) body; stainless steel pistons (×2), 8 mm diameter | NMC622 | cathode | Li2O-ZrO2 | null | null | W-Li3InCl6 in cathode composite; W-β-Li3PS4 separator and anode composite | W-β-Li3PS4 | 1 ton/cm2 | room temperature | 2.1 V | 3.6 V | LiIn/In | C/20 | Unclear (failure cycle not given; capacity fell by 88.3% after 20 cycles) | capacity decay 88.3 % | Interfacial failure | The degradation arises because Li3InCl6 is chemically unstable against sulfide solid electrolytes, which forms a passivation interlayer. | Stated by the author | We built an all-solid-state full cell with a cathode composite of Li2O-ZrO2-coated NMC622, water-assisted Li3InCl6 (W-Li3InCl6) and VGCF at 70:30:5 by weight, hand-ground for 10 minutes in an agate mortar. It used a W-β-Li3PS4 separator and a Li0.5In/W-β-Li3PS4 anode composite. We cycled it in a cylindrical PEI cell wi... | In search of the best solid electrolyte-layered oxide pair in all-solid-state batteries | Tuncay Koç | 2,022 | PhD (doctorat) | Sorbonne Université | France | https://theses.hal.science/tel-04137255 |
run-058 | T30 | Li-ion | solid state | coated-NMC622:Li3InCl6:VGCF | 10 nm-Li3PO4-coated Li6PS5Cl | Li6PS5Cl:Li0.5In | full cell | cylindrical polyetherimide (PEI) body; stainless steel pistons (×2), 8 mm diameter | NMC622 | cathode | Zr-based coating | null | null | Li3InCl6 in cathode composite; 10 nm Li3PO4-coated Li6PS5Cl separator; Li6PS5Cl in anode composite | 10 nm-Li3PO4-coated Li6PS5Cl | 1 t/cm2 | room temperature | 2.1 V | Unclear (upper cut-off unspecified; one of 3.6/3.7/3.8/3.9 V vs. LiIn/In) | LiIn/In | Not reported | 1 | coating layer thickness 10 nm; Li3PO4 deposition method atomic layer deposition (ALD) | Did not work in that regime | Caused by a higher cell resistance that came with the thicker coating layer. | Stated by the author | We built an all-solid-state full cell from three parts: a Zr-coated NMC622:Li3InCl6:VGCF cathode composite, a Li6PS5Cl separator coated with a 10 nm Li3PO4 layer by atomic layer deposition, and a Li6PS5Cl:Li0.5In anode composite. It was held in a cylindrical PEI cell with two 8 mm stainless steel pistons under 1 t/cm2.... | In search of the best solid electrolyte-layered oxide pair in all-solid-state batteries | Tuncay Koç | 2,022 | PhD (doctorat) | Sorbonne Université | France | https://theses.hal.science/tel-04137255 |
run-059 | T31 | Li-ion | non-aqueous | Swagelok half cell; Li metal as both counter and reference electrode | half cell | Swagelok | nanometric crystalline silicon (d ~150 nm) | anode | null | null | 1 M LiPF6 EC/DMC=50/50 (v/v) + 10% FEC | null | two glass microfibre membranes (GF/D, Whatman) and one Celgard 2500 | null | room temperature | 0.005 V | 1 V | Li+/Li | C/20 | 2 | liant AT-Ti(OiPr)4_Propanol; capacity at second cycle 1500 mAh/gsi; first-cycle coulombic efficiency 41 % | Mechanical failure | Poor cohesion or adhesion leads to active-material disconnection, usually most visible as a lower second-cycle discharge capacity, as observed here. | Suggested by the author | We made a Swagelok half cell with a nanometric crystalline silicon electrode (about 150 nm) against lithium metal, which served as both counter and reference electrode. The binder was a tannic acid–Ti(OiPr)4 coordination compound synthesised in propan-1-ol. The electrode was 75:10:15 Si : carbon : binder at 1.7 mg/cm².... | Optimisation d’électrodes de silicium pour batteries lithium-ion : nouveaux liants moléculaires et revêtements de coordination | Nassima Kana | 2,022 | PhD (doctorat) | Nantes Université | France | https://theses.hal.science/tel-04343685 |
run-060 | T31 | Li-ion | non-aqueous | half cell; Li metal as both counter and reference electrode | half cell | Swagelok | nanometric crystalline silicon (d ~150 nm) | anode | null | null | 1 M LiPF6 EC/DMC 1/1 v/v + 10%FEC | null | Two Whatman glass fibre separators | null | room temperature | 0.005 V | 1 V | Li+/Li | C/10 | Unclear (below 750 mAh/gSi at 65 cycles; failure cycle not given) | liant acide tannique 5%; capacity at 65 cycles < 750 mAh/gSi; first-cycle coulombic efficiency 57 % | Mechanical failure | Attributed to the electrodes having too little mechanical cohesion to allow complete delithiation. | Suggested by the author | We built Swagelok half cells of nanometric crystalline silicon (about 150 nm) against lithium metal, with only 5% tannic acid binder in an 85/10/5 formulation at 2 mg/cm². The components were mixed in a planetary mill at 500 rpm for 1 h and doctor-bladed onto copper foil. The electrolyte was 300 µl of 1 M LiPF6 in EC/D... | Optimisation d’électrodes de silicium pour batteries lithium-ion : nouveaux liants moléculaires et revêtements de coordination | Nassima Kana | 2,022 | PhD (doctorat) | Nantes Université | France | https://theses.hal.science/tel-04343685 |
run-061 | T32 | Li-ion | non-aqueous | operando ATR-FTIR cell | half cell | specially designed half-cell (Figure 2-11) | 2%B – aSi0.8(CH3)0.2:H | anode | null | boron | 1 M LiPF6 EC: DMC (1:1) + 5%FEC | null | Not reported | null | Not reported | 125 mV | Not reported | Li/Li+ | ~23 μA/cm2 | 1 | thickness 30 nm; plateau potential < 100 mV; expected lithiation duration ~1.5–2 hours | Did not work in that regime | Caused by the 2%B – aSi0.8(CH3)0.2:H film being highly resistive. | Stated by the author | We deposited a 30 nm film of boron-doped methylated amorphous silicon, 2%B – aSi0.8(CH3)0.2:H, by PECVD on a c-Si substrate. We lithiated it in our operando ATR-FTIR half cell against lithium foil, using 1 M LiPF6 in EC:DMC (1:1) with 5% FEC at about 23 µA/cm2. The first lithiation should have lasted about 1.5–2 hours.... | Methylated amorphous silicon for Li-ion batteries | Ngoc Tram Phung | 2,023 | PhD (doctorat) | Institut Polytechnique de Paris | France | https://theses.hal.science/tel-04532178 |
run-062 | T33 | Li-ion | solid state | SE-free electrode configuration, LTS (100%) | Li6PS5Cl | LiIn : Li6PS5Cl | half cell | custom-built two-electrode cell | O3-LixTiS2 (pristine LTS) | cathode | null | null | null | Li6PS5Cl | Li6PS5Cl | 100 MPa | RT | 1.8 V | 2.6 V | Li+/Li | C/60 | 1 | null | Did not work in that regime | Li+ ions show restricted apparent diffusion. | Stated by the author | We built an all-solid-state cell with a solid-electrolyte-free positive electrode of 100% pristine O3-LixTiS2, made by solid-state synthesis at 800 °C from Ti and Li2S in evacuated quartz tubes, with a Li6PS5Cl separator and a LiIn:Li6PS5Cl counter electrode in a homemade two-electrode cell, at about 12 mg of active ma... | Engineering Strategies to Improve All-Solid-State Battery Performance under Low-Pressure Conditions | Hennequart, Benjamin | 2,023 | PhD (doctorat) | Sorbonne Université | France | https://theses.hal.science/tel-04524445 |
run-063 | T33 | Li-ion | solid state | pouch cell with aluminium disk and tabs | half cell | pouch cell | NMC622 | cathode | null | null | null | LYBC separator film with thin LPSCl layer; Li3InCl6 in cathode composite | LYBC film fibrillated with 0.2 wt.% PTFE, with thin LPSCl layer | 0.1 MPa | RT | 2.1 V | 3.6 V | Li+/LiIn | C/20 | 1 | disk diameter 13 mm; stack densification pressure 400 MPa | Interfacial failure | The weak performance was attributed mainly to inadequate contact at the current collectors. | Suggested by the author | We built a 13 mm solid-state half cell in a pouch with an aluminium disk and tabs: an NMC622:Li3InCl6:VGCF (66.5:28.5:5) working electrode at 4.5 mg NMC/cm2, a Li3YBr2Cl4 (LYBC) separator film fibrillated with 0.2 wt% PTFE plus a thin LPSCl layer, and a LiIn:LPSCl counter electrode, with the whole stack densified at 40... | Engineering Strategies to Improve All-Solid-State Battery Performance under Low-Pressure Conditions | Hennequart, Benjamin | 2,023 | PhD (doctorat) | Sorbonne Université | France | https://theses.hal.science/tel-04524445 |
run-064 | T34 | Na-ion | solid state | NASICON ASSB micro-battery on heating and biasing MEMS chip, operando SEM cyclic voltammetry | symmetric cell | micro-battery (total length of 60 µm) | NVP | cathode | Not reported | null | null | NZSP | Not reported | Not reported | 200 °C | 0 V | 5 V | Not reported | Not reported | 1 | scan rate 0.5 mV.s-1; electrolyte layer thickness 18 µm; number of CV cycles 5 | Did not work in that regime | The micro-batteries' low electronic conductivity may also have contributed. | Suggested by the author | We extracted a symmetric NVP|NZSP|NVP micro-battery from an SPS-assembled pellet using a TEM technique. It was about 60 µm long with an 18 µm electrolyte layer, and its electrodes were NVP : NZSP : C = 42.5 : 42.5 : 15 by mass. We mounted it on a heating and biasing MEMS chip for operando SEM and ran five cyclic voltam... | Exploring the Potential of NASICON as an Efficient Solid-State Electrolyte for Sodium-Based Solid State Batteries | Mahayoni, Eunike | 2,023 | PhD (doctorat) | Université de Picardie Jules Verne | France | https://theses.hal.science/tel-05674137 |
run-065 | T34 | Na-ion | solid state | NASICON micro-battery, operando SEM cyclic voltammetry | symmetric cell | micro-battery | NVP | cathode | Not reported | null | null | Unclear (not named here; electrolyte's Na also fully migrated to anode) | Not reported | Not reported | 200 °C | Not reported | 3 V | Not reported | Not reported | 5 | scan rate 0.5 mV.s-1; cycle at which subtle peak appeared 4 | Degradation | The micro-batteries' low electronic conductivity may also have contributed. | Suggested by the author | We cycled a second symmetric NVP|NZSP|NVP micro-battery, cut from the same battery as the first (electrodes NVP : NZSP : C = 42.5 : 42.5 : 15 by mass). We ran cyclic voltammetry under operando SEM at 200 °C, up to 3 V at 0.5 mV/s. A faint redox peak appeared on the fourth cycle, but the current response increased signi... | Exploring the Potential of NASICON as an Efficient Solid-State Electrolyte for Sodium-Based Solid State Batteries | Mahayoni, Eunike | 2,023 | PhD (doctorat) | Université de Picardie Jules Verne | France | https://theses.hal.science/tel-05674137 |
run-066 | T35 | Li-metal | solid state | NCM811|PPL|Li mettery (PPL-mettery), uniaxial tensile deformed | full cell | mettery (AA5052-H111 aluminium alloy sheets as casing and current collectors) | PPL electrolyte | solid electrolyte | null | null | null | PPL electrolyte | Not reported | Unclear (normal contact pressure applied; magnitude not stated) | 25 °C | 2.8 V | 4.3 V | Not reported | 2 C | Unclear (no failure cycle given; 39.8% capacity retained after 100 cycles) | tensile strain 15 %; activation 0.1C for the first three cycles; capacity retention 39.8 %; lithium metal foil thickness 100 μm | Mechanical failure | Mainly due to PPL electrolyte micro-cracks, which obstruct ion transport paths and reduce ionic conductivity. | Stated by the author | We built an NCM811|PPL|Li mettery, using AA5052-H111 aluminium alloy sheets as both casing and current collectors. NCM811 slurry was coated directly on one sheet, 100 μm lithium foil went on the other, and a solid-state PPL electrolyte sat between them. We stretched it uniaxially to 15% tensile strain and activated it ... | Development of formable metal batteries (Mettery) | Yu, Xiangnan | 2,023 | PhD | Imperial College London | United Kingdom | https://doi.org/10.25560/126839 |
run-067 | T35 | Li-metal | Unclear (quasi-solid-state PPL+FEC electrolyte noted; overall cell state not specified) | NCM811|PPL+FEC|Li mettery (PPL+FEC-mettery), tensile strain 0.5% | full cell | mettery | PPL electrolyte | solid electrolyte | null | null | Not reported | PPL electrolyte | Not reported | Not reported | 25 °C | 2.8 V | 4.3 V | Not reported | 1 C | 252 | FEC content 1 μL/cm2; tensile strain 0.5 %; activation 0.1C for the first three cycles | Short circuit | The larger amount of liquid FEC added (1 μL/cm2) would reduce the PPL+FEC electrolyte's mechanical strength, making a short circuit occur more readily. | Stated by the author | We built an NCM811|PPL+FEC|Li mettery, adding 1 μL/cm2 of liquid FEC to the solid-state PPL electrolyte during assembly, and deformed it to 0.5% tensile strain. After three activation cycles at 0.1C, we cycled it at 1C between 2.8 and 4.3 V at 25 °C. It delivered an initial specific capacity of 162.4 mAh g-1 and short-... | Development of formable metal batteries (Mettery) | Yu, Xiangnan | 2,023 | PhD | Imperial College London | United Kingdom | https://doi.org/10.25560/126839 |
run-068 | T36 | Li-metal | solid state | Li/Li7P3S11/Li | symmetric cell | pouch | Li7P3S11 | solid electrolyte | null | null | null | Li7P3S11 | null | 1.1 MPa | 22 °C | Not reported | Not reported | Not reported | 0.1 mA.cm-2 | Unclear (cycle count not given; shorted after roughly 300 h) | time to failure ~300 h; areal lithium capacity 1 mAh.cm-2; electrolyte mass 150 mg | Short circuit | Thought to be either different intrinsic mechanical properties (more or less brittle and/or rigid) or the nature and properties of the lithium/electrolyte interphase layers. | Suggested by the author | We assembled an all-solid-state Li/Li7P3S11/Li symmetric pouch cell. The Li7P3S11 was made by ball-milling 70 mol% Li2S with 30 mol% P2S5, then crystallised by heat treatment. We densified 150 mg of it in a 13 mm die at 75 MPa for 30 s, 225 MPa for 5 min and 375 MPa for 5 min, then pressed 100 μm thick, 12 mm lithium d... | All-solid-state lithium - sulfur batteries with sulfide solid electrolyte | Marine Soler | 2,023 | PhD (doctorat) | Université Grenoble Alpes [2020-....] | France | https://theses.hal.science/tel-04204591 |
run-069 | T36 | Li-metal | solid state | Li/Li6PS5Cl/Li | symmetric cell | pouch | Li6PS5Cl | solid electrolyte | null | null | null | Li6PS5Cl | null | 1.1 MPa | 22 °C | Not reported | Not reported | Not reported | 0.1 mA.cm-2 | Unclear (cycle count not given; abrupt overpotential rise near 4400 h) | time to failure ~4400 h; areal lithium capacity 1 mAh.cm-2 | Interfacial failure | The lithium is thought to have eventually lost contact with the electrolyte. | Suggested by the author | We assembled an all-solid-state Li/Li6PS5Cl/Li symmetric pouch cell using commercial Li6PS5Cl. The electrolyte was densified in a 13 mm die at 75 MPa for 30 s, 225 MPa for 5 min and 375 MPa for 5 min, and 100 μm thick, 12 mm lithium discs were then pressed on at 75 MPa for 3 s. We cycled it galvanostatically at 0.1 mA ... | All-solid-state lithium - sulfur batteries with sulfide solid electrolyte | Marine Soler | 2,023 | PhD (doctorat) | Université Grenoble Alpes [2020-....] | France | https://theses.hal.science/tel-04204591 |
run-070 | T36 | Li-S | solid state | InLi/Li6PS5Cl/(KBC-S-Li6PS5Cl) | full cell | Sphere Energy ASC-A (fixed thickness) | KBC-S-Li6PS5Cl composite (KB:S8:Li6PS5Cl 1:2:3) | cathode | null | null | null | Li6PS5Cl | null | 50 MPa | 22 °C | 1.5 V | 2.7 V | Li+/Li | C/50 | Unclear (cycle count not given; cycling delivered zero or near-zero capacity) | cell capacity 4.46 mAh; anode lithium content 34.3 %at | Did not work in that regime | Probably, 50 MPa was insufficient pressure for the cell to function correctly. | Suggested by the author | We assembled an all-solid-state Li-S cell, InLi/Li6PS5Cl/(KBC-S-Li6PS5Cl), in a fixed-thickness ASC-A pressure device at an initial pressure of 50 MPa. The cathode composite was Ketjenblack:S8:Li6PS5Cl at 1:2:3 by mass, made by impregnating sulfur at 140 °C into a Ketjenblack EC600/phenolic resin matrix. The InLi anode... | All-solid-state lithium - sulfur batteries with sulfide solid electrolyte | Marine Soler | 2,023 | PhD (doctorat) | Université Grenoble Alpes [2020-....] | France | https://theses.hal.science/tel-04204591 |
run-071 | T37 | Li-ion | non-aqueous | graphite/NCM811 cells | full cell | coin (2032) | NCM811 | cathode | null | null | 1 M LiPF6 EC/EMC 30:70wt% | null | Celgard | null | 25 °C | 2.5 V | 4.2 V | full cell voltage (graphite negative electrode) | 1C | Unclear (cycle count not given; cell could not cycle at all) | spacer configuration single 0.5 mm spacer; electrolyte volume 60 µL | Did not work in that regime | Because internal pressure was low, the components did not contact the cell on both sides. | Stated by the author | We assembled a graphite/NCM811 full cell in a 2032 coin cell with a single 0.5 mm spacer. It had a Celgard separator, cast electrodes and 60 µL of LP57 electrolyte (1 M LiPF6 in EC/EMC 30:70 wt%). It was to be cycled between 2.5 and 4.2 V at 1C and 25 °C, but it was unable to cycle at all. The low internal pressure mea... | Unraveling Degradation Patterns in Li-ion Batteries through Electrochemical Analysis Procedures | Valentin Meunier | 2,023 | PhD (doctorat) | Sorbonne Université | France | https://theses.hal.science/tel-04347681 |
run-072 | T37 | Li-ion | non-aqueous | graphite/LNO full cells | full cell | coin (2032) | LiNiO2 | cathode | null | null | 1 M LiPF6 EC:EMC 30:70wt% | null | Celgard 2500 (polypropylene), single layer | null | 25 °C | 2.5 V | 4.8 V | full cell voltage (graphite negative electrode) | C/2 | Unclear (total cycles not given; 55% loss measured after 6th control cycle) | capacity loss 55 %; knee point present; LAM 27.8 %; control cycle rate C/20; N/P ratio 1.5; electrolyte volume 30 μL | Degradation | Most of the degradation came from cycling up to a high cut-off voltage of 4.8 V. | Stated by the author | We cycled a graphite/LiNiO2 full cell in a 2032 coin cell. The positive electrode was 92 wt% LiNiO2, 4 wt% PVDF and 4 wt% Super C45 carbon, cast and calendered, and balanced at N/P 1.5. It had a single Celgard 2500 polypropylene separator and 30 μL of LP57 electrolyte (1 M LiPF6 in EC:EMC 30:70 wt%). We cycled it at C/... | Unraveling Degradation Patterns in Li-ion Batteries through Electrochemical Analysis Procedures | Valentin Meunier | 2,023 | PhD (doctorat) | Sorbonne Université | France | https://theses.hal.science/tel-04347681 |
run-073 | T37 | Li-ion | non-aqueous | graphite/NMC811 cells | full cell | coin (2032) | NMC811 | cathode | null | null | 5 M LiFSI DMC + none | null | Celgard 3501 (coated polypropylene) | null | 25 °C | 2.5 V | 4.3 V | full cell voltage (graphite negative electrode) | 1C | 250 | capacity retention 70 %; LAM NE 33 %; estimated Li plating onset 51 cycles; cathode areal capacity 1 mAh.cm-2; N/P 1.27; electrolyte volume 31.2 μL | Contamination | DMC undergoes anodic decomposition during charge; Li+ intercalation into graphite alone cannot fully offset the extra capacity from this oxidation, so Li plates. | Stated by the author | We cycled a graphite/NMC811 full cell in a 2032 coin cell with a high-concentration electrolyte of 5 M LiFSI in DMC and no additive. The NMC811 electrode was 95 wt% NMC811, 3 wt% C65 carbon black and 2 wt% PVDF on aluminium foil at 1.0 mAh cm-2, with N/P 1.27, a Celgard 3501 separator and 31.2 μL of electrolyte. We cyc... | Unraveling Degradation Patterns in Li-ion Batteries through Electrochemical Analysis Procedures | Valentin Meunier | 2,023 | PhD (doctorat) | Sorbonne Université | France | https://theses.hal.science/tel-04347681 |
run-074 | T37 | Li-ion | non-aqueous | graphite/NMC811 cells | full cell | coin (2032) | NMC811 | cathode | null | null | Unclear (salt molarity not given; only LiFSI:DMC:TTE molar ratio 1:2:3 reported) LiFSI DMC:TTE (LiFSI:DMC:TTE molar ratio 1:2:3) + trimethylphosphite (TMP) | null | Celgard 3501 (coated polypropylene) | null | 25 °C | 2.5 V | 4.3 V | full cell voltage (graphite negative electrode) | 1C | 255 | additive concentration 2 wt%; N/P 1.27 | Interfacial failure | TMP oxidizes on the positive electrode and builds a thick, resistive CEI that harms cell performance. | Stated by the author | We cycled a graphite/NMC811 full cell in a 2032 coin cell with a localised high-concentration electrolyte (LiFSI:DMC:TTE at a 1:2:3 molar ratio) containing 2 wt% trimethylphosphite (TMP) as a CEI additive. The NMC811 electrode was 95:3:2 NMC811:C65:PVDF on aluminium foil, with N/P 1.27 and a Celgard 3501 separator. We ... | Unraveling Degradation Patterns in Li-ion Batteries through Electrochemical Analysis Procedures | Valentin Meunier | 2,023 | PhD (doctorat) | Sorbonne Université | France | https://theses.hal.science/tel-04347681 |
run-075 | T37 | Li-ion | non-aqueous | graphite/NMC811 cells | full cell | coin (2032) | NMC811 | cathode | null | null | Unclear (salt molarity not given; only LiFSI:DMC:TTE molar ratio 1:2:3 reported) LiFSI DMC:TTE (LiFSI:DMC:TTE molar ratio 1:2:3) + none | null | Celgard 3501 (coated polypropylene) | null | 25 °C | 2.5 V | 4.5 V | full cell voltage (graphite negative electrode) | 1C | <= 410 | CE drop 98 %; LAM PE -23 %; N/P 1.27 | Degradation | Lithium is thought to be unable to reinsert properly into the NMC as discharge ends. | Suggested by the author | We cycled a graphite/NMC811 full cell in a 2032 coin cell with bare localised high-concentration electrolyte (LiFSI:DMC:TTE at 1:2:3 molar, no additives). The NMC811 electrode was 95:3:2 NMC811:C65:PVDF on aluminium foil, with N/P 1.27 and a Celgard 3501 separator. We cycled it at 1C and 25 °C between 2.5 and 4.5 V. Th... | Unraveling Degradation Patterns in Li-ion Batteries through Electrochemical Analysis Procedures | Valentin Meunier | 2,023 | PhD (doctorat) | Sorbonne Université | France | https://theses.hal.science/tel-04347681 |
run-076 | T38 | Na-ion | non-aqueous | 18650 NVPF-HC cell | full cell | 18650 | Na3V2(PO4)2F3 (NVPF) | cathode | carbon coating | null | 1 M NaPF6 EC-PC-DMC (1:1:1 by volume) + none | null | Not reported | null | 55 °C | Not reported | Not reported | Not reported | C/5 | 28 | time to CID break ~10 days; internal pressure ~15 bars; capacity retention at failure 93 % | Mechanical failure | The pressure rise is attributed to gaseous by-products formed by parasitic reactions involving the electrolyte. | Suggested by the author | We filled an 18650 NVPF|hard carbon Na-ion cell, with carbon-coated NVPF, with 1 M NaPF6 in EC-PC-DMC (1:1:1 by volume) and no electrolyte additive. Formation and cycling were done at 55 °C at C/5 (1C = 128 mAh/g). After about 10 days (28 cycles), the current interrupt device broke and the cell stopped working. The int... | Achieving Na-ion Battery Advancements Through Decoding Degradation Pathways and Electrolyte Engineering | Parth Desai | 2,023 | PhD (doctorat) | Sorbonne Université | France | https://theses.hal.science/tel-04543545 |
run-077 | T38 | Na-ion | non-aqueous | NVPF|HC full cell in coin-type 2032 cell | full cell | coin-type 2032 | Na3V2(PO4)2F3 (NVPF) | cathode | Not reported | null | 1 M NaPF6 EC-PC-DMC (1:1:1 by volume) + 0.5 wt% NaODFB + 3 wt% VC | null | Not reported | null | 55 °C | 2 V | 4.3 V | full cell voltage | C/5 | Unclear (failure cycle not given; fast fade began after 20 cycles) | storage at 100% state of charge 1 week at 4.3 V, 55°C, after cycle 10; negative electrode hard carbon (HC) | Contamination | Electrolyte oxidation added surplus Na+ inventory, which raised capacity at first and then led to rapid capacity loss. | Stated by the author | We assembled an NVPF|hard carbon Na-ion full cell in a 2032 coin cell, with electrodes at 94:3:3 active material:PVDF:conductive carbon. The electrolyte was 1 M NaPF6 in EC-PC-DMC (1:1:1 by volume) containing 0.5 wt% NaODFB and 3 wt% VC. We cycled it at 55 °C between 2 and 4.3 V, first for 10 cycles at C/5, then stored... | Achieving Na-ion Battery Advancements Through Decoding Degradation Pathways and Electrolyte Engineering | Parth Desai | 2,023 | PhD (doctorat) | Sorbonne Université | France | https://theses.hal.science/tel-04543545 |
run-078 | T39 | Li-metal | solid state | TiS2/Argyrodite/Li0 | full cell | SPHERE ASC-AD | TiS2 | cathode | null | null | null | argyrodite | argyrodite, 35 mg | 45 MPa | 20 °C | Not reported | Not reported | Not reported | C/50 | 4 | reversible capacity 30 mAh.g-1; positive electrode mass 10 mg | Short circuit | Probably caused by dendrite formation or lithium creep, both promoted by the applied pressure. | Suggested by the author | We built an all-solid-state TiS2/argyrodite/Li cell in a SPHERE ASC-AD holder under 45 MPa. It had 10 mg of positive electrode made from commercial TiS2, a 35 mg argyrodite separator and a Li metal negative electrode. We cycled it at C/50 at 20 °C. It gave a reversible capacity of about 30 mAh/g with a large irreversib... | Étude des interfaces électrodes / électrolyte dans des accumulateurs tout-solide et tout-sulfure au lithium | Mathieu Caspar | 2,023 | PhD (doctorat) | Université de Pau et des Pays de l'Adour | France | https://theses.hal.science/tel-04709439 |
run-079 | T39 | Li-metal | solid state | all-solid-state cell, argyrodite separator ~80 mg (~1 mm), Li0 Ø 6 mm × 220 µm, SPHERE ASC-AD cell | full cell | SPHERE ASC-AD | Li0 (lithium metal) | anode | null | null | null | argyrodite | argyrodite, ~80 mg (~1 mm) | 48 MPa | 20 °C | Not reported | Not reported | Not reported | Not reported | Unclear (cycle count not given; shorts occurred before or during cycling) | Masse d’argyrodite ~80 mg; Li diameter 6 mm; Li thickness 220 µm; Masse Li 3.3 mg; CCMI rate 100 %; Effectif 2 cellules | Short circuit | The lithium creep phenomenon can trigger short circuits of mechanical origin. | Suggested by the author | We assembled two all-solid-state cells in SPHERE ASC-AD holders under 48 MPa at 20 °C. Each had an argyrodite separator of about 80 mg (about 1 mm thick) and a thick Li metal negative electrode, 6 mm across and 220 µm thick (3.3 mg). Both cells short-circuited, some before cycling started and some during it. We think t... | Étude des interfaces électrodes / électrolyte dans des accumulateurs tout-solide et tout-sulfure au lithium | Mathieu Caspar | 2,023 | PhD (doctorat) | Université de Pau et des Pays de l'Adour | France | https://theses.hal.science/tel-04709439 |
run-080 | T40 | Li-metal | solid state | symmetrical Li/LAGP/Li cell | symmetric cell | Not reported | LAGP | solid electrolyte | null | null | null | LAGP | null | Unclear (no controlled pressure applied; pressure value not given) | Unclear (no temperature control applied; operating value not given) | Not reported | 10 V | Not reported | 80 µA.cm-2 | Unclear (cycle count not given; polarised to 10 V by 60 h) | time to 10 V 60 hours; current step duration 1 hour | Mechanical failure | The cell failed mainly because pores and interphase formation led to high cell polarization. | Stated by the author | We cycled a symmetric Li/LAGP/Li cell with an LAGP pellet sintered at 680 °C, without controlling the temperature or the pressure. We applied alternating one-hour current steps at 80 µA/cm², the low current density in our series, and stopped at 10 V. The cell polarised up to 10 V after 60 hours of cycling. When we open... | Study of all-solid-state Li-ion batteries based on LAGP electrolyte using multiscale imaging techniques | Sorina Crețu | 2,023 | PhD (doctorat) | Université de Picardie Jules Verne | France | https://theses.hal.science/tel-05635675 |
run-081 | T40 | Li-metal | solid state | symmetrical Li/LAGP/Li cell | symmetric cell | Not reported | LAGP | solid electrolyte | null | null | null | LAGP | null | Unclear (no controlled pressure applied; pressure value not given) | Unclear (no temperature control applied; operating value not given) | Not reported | 10 V | Not reported | 120 µA.cm-2 | Unclear (cycle count not given; hit 10 V just after 30 h) | time to 10 V ~30 hours; current step duration 1 hour | Mechanical failure | Failure came mainly from hot spots of locally elevated current density inside the cell, which set off Li filament growth. | Stated by the author | We cycled a symmetric Li/LAGP/Li cell with an LAGP pellet sintered at 680 °C, without controlling the temperature or the pressure. We applied alternating one-hour current steps at 120 µA/cm², our medium current density, and stopped at 10 V. During cycling we saw voltage spikes and asymmetry between the two electrodes, ... | Study of all-solid-state Li-ion batteries based on LAGP electrolyte using multiscale imaging techniques | Sorina Crețu | 2,023 | PhD (doctorat) | Université de Picardie Jules Verne | France | https://theses.hal.science/tel-05635675 |
run-082 | T40 | Li-metal | solid state | symmetrical Li/LAGP/Li cell | symmetric cell | Not reported | LAGP | solid electrolyte | null | null | null | LAGP | null | Unclear (no controlled pressure applied; pressure value not given) | Unclear (no temperature control applied; operating value not given) | Not reported | 10 V | Not reported | 160 µA.cm-2 | Unclear (cycle count not given; hit 10 V just after 27 h) | time to 10 V ~27 hours; current step duration 1 hour | Mechanical failure | Failure came mainly from hot spots of locally elevated current density inside the cell, which set off Li filament growth. | Stated by the author | We cycled a symmetric Li/LAGP/Li cell with an LAGP pellet sintered at 680 °C, without controlling the temperature or the pressure. We applied alternating one-hour current steps at 160 µA/cm², our high current density, and stopped at 10 V. The cell reached 10 V after about 27 hours. X-ray CT and SEM afterwards showed de... | Study of all-solid-state Li-ion batteries based on LAGP electrolyte using multiscale imaging techniques | Sorina Crețu | 2,023 | PhD (doctorat) | Université de Picardie Jules Verne | France | https://theses.hal.science/tel-05635675 |
run-083 | T40 | Li-metal | solid state | enhanced LiFePO4/LAGP/Li metal battery | full cell | Not reported | LiFePO4 | cathode | Not reported | null | null | LAGP | null | Not reported | 100 °C | Not reported | Not reported | Not reported | C/40 | Unclear (cycle count not given; performance worsened further after 7 cycles) | charge capacity in the first cycle 56 mAh.g-1; first discharge capacity relative to charge capacity ~60 %; onset of high voltage fluctuations 3 cycle; solid electrolyte thickness ~200–400 µm; pressure applied on each layer before sintering 5 t | Mechanical failure | Because LAGP is very rigid, dendrite growth caused a huge number of cracks. | Stated by the author | We built our optimised all-solid-state LiFePO4/LAGP/Li metal cell. The positive electrode was 30 % LiFePO4, 60 % LAGP and 10 % carbon black, mixed by SPEX for 30 min. We pressed each layer at 5 t and made the LFP/LAGP half battery by SPS at 680 °C, with an LAGP layer about 200 µm thick. We cycled it at 100 °C at C/40. ... | Study of all-solid-state Li-ion batteries based on LAGP electrolyte using multiscale imaging techniques | Sorina Crețu | 2,023 | PhD (doctorat) | Université de Picardie Jules Verne | France | https://theses.hal.science/tel-05635675 |
run-084 | T41 | Li-ion | aqueous | LiFePO4 vs. TiS2 full cell | full cell | coin cell | LiFePO4 | cathode | carbon coating | null | 21 m LiTFSI water | null | Not reported | null | Not reported | Not reported | Not reported | Not reported | C/10 | 1 | electrode mass balancing 0.8; balancing in capacity 0.56; potentiostatic step at end of each charge/discharge 30 min; negative electrode TiS2 | Contamination | Failure attributed to persistent parasitic reactions in the cell. | Stated by the author | We cycled a carbon-coated LiFePO4 vs TiS2 full coin cell in aqueous 21 m LiTFSI. The electrode mass balancing was 0.8 (0.56 in capacity), and we held a 30-minute potentiostatic step at the end of each charge and discharge. At C/10 the cell failed after just one cycle. We attribute the failure to parasitic reactions tha... | Understanding degradation in water-in-salt batteries | Célia Doublet | 2,024 | PhD (doctorat) | Université Grenoble Alpes [2020-....] | France | https://theses.hal.science/tel-05140586 |
run-085 | T41 | Li-ion | aqueous | LiFePO4 vs. TiS2 full cell | full cell | coin cell | LiFePO4 | cathode | carbon coating | null | 21 m LiTFSI water | null | Not reported | null | Not reported | Not reported | Not reported | Not reported | C/2 | Unclear (ceased working after 33 cycles; exact failure criterion not given) | cycles before it stopped working 33 cycles; electrode mass balancing 0.8; balancing in capacity 0.56; potentiostatic step at end of each charge/discharge 30 min; negative electrode TiS2 | Contamination | Failure attributed to persistent parasitic reactions in the cell. | Stated by the author | We cycled a carbon-coated LiFePO4 vs TiS2 full coin cell at C/2 in aqueous 21 m LiTFSI. The electrode mass balancing was 0.8 (0.56 in capacity), and we held a 30-minute potentiostatic step at the end of each charge and discharge. The coulombic efficiency was erratic, and the cell stopped working after 33 cycles. We att... | Understanding degradation in water-in-salt batteries | Célia Doublet | 2,024 | PhD (doctorat) | Université Grenoble Alpes [2020-....] | France | https://theses.hal.science/tel-05140586 |
run-086 | T42 | Na-ion | solid state | Na9Sn4 | SSE | Sn half cell with NYZC separator | half cell | 10 mm PEEK die with two Ti plungers | Sn | anode | null | null | null | Na2.25Y0.25Zr0.75Cl6 (NYZC) | NYZC solid electrolyte pellet | Not reported | Not reported | Unclear (lower voltage cutoff not given; sodiation stopped at 95% theoretical capacity) | 2 V | Not reported | 0.16 mA∙cm-2 | 1 | SSE pellet pressing pressure 370 MPa; SSE separator thickness ~500 μm; interphase layer thickness 90 μm; interfacial resistance increase during sodiation ~9000 Ω | Interfacial failure | An electron-conducting layer formed at the NYZC–Sn interphase, driving fast, ongoing NYZC consumption and thickening of the interlayer. | Stated by the author | We built a solid-state Na9Sn4 | NYZC | Sn half cell in a 10 mm PEEK die with two Ti plungers, using a roughly 500 µm Na2.25Y0.25Zr0.75Cl6 (NYZC) separator pellet pressed at 370 MPa and a Sn electrode slurry-cast on Al foil (99.5:0.5 Sn:PVDF). We cycled it once at 0.16 mA/cm2, sodiating the Sn to 95% of its theoretical ... | Enabling an Anode-Free Sodium All-Solid-State Battery | Deysher, Grayson | 2,024 | PhD | University of California, San Diego | United States | https://escholarship.org/uc/item/189840j0 |
run-087 | T43 | Li-ion | non-aqueous | Si+Gr/LFP full cells | full cell | Swagelok | Si/Gr blend electrode (Si nanoparticles + SFG6 graphite, 50:50) | anode | null | null | 3.2 m LiFSI P1222FSI (triethyl(methyl)phosphonium bis(fluorosulfonyl)imide) ionic liquid | null | Celgard 3501 membrane + borosilicate glass-fiber separator (Whatman GF/D) | null | 50 °C | 1.5 V | 4 V | Not reported | C/5 | Unclear (cycle count not given; 48% capacity retained at 100 cycles) | capacity retention 48 %; cycles before capacity fade accelerates 40 cycles; initial coulombic efficiency (CE) 87 %; negative electrode capacity utilized ~77 %; cumulative ICL after 100 cycles ~1000 mAh g-1; cyclable lithium lost to the SEI on the anode ~60 %; N/P capacity ratio 1.1–1.2; anode Si/Gr loading 3–3.5 mg cm-... | Mechanical failure | Attributed to Si nanoporosification and disconnection of particles within the Si/graphite blend anode, which depleted the LFP cathode's lithium inventory over prolonged cycling. | Suggested by the author | We built a Si/graphite | LFP full cell in a Swagelok fitting. The negative electrode was a 50:50 blend of Si nanoparticles and SFG6 graphite with GM15 and a partially lithiated PAA binder (Si:Gr:GM15:PAA 43:43:4:10), tape-cast from a ball-milled aqueous slurry onto Cu foil at 3.0-3.5 mg cm-2 (5.9-6.9 mAh cm-2). The LFP... | Characterization and understanding of the SEI in Li-ion batteries based on silicon and ionic liquid | Boluwatife Igbaroola | 2,024 | PhD (doctorat) | Nantes Université | France | https://theses.hal.science/tel-04994352 |
run-088 | T44 | Li-ion | non-aqueous | Graphite / NMC 811 full cell | full cell | pouch | graphite GHDR 15-4 (Imerys), electrode n°7-G | anode | carbon coating | null | 1 M LiPF6 DMC:EC:EMC 1:1:1 (vol.) + 10% FEC + 2% VC | null | trilayer (PP/PE/PP) Celgard® M2000 | null | 23 °C | 2.7 V | 4.2 V | cell voltage (full cell) | C/3 (charge) / C/2 (discharge) | Unclear (below 80% capacity within only 40 cycles; total cycles not given) | areal loading (negative electrode) 12.9 mg.cm-2; porosity 36 %; electrode parameters (Table 12, no. 7-G) Dispermat, GHDR, DS 0,9, CMC 20 000 0,0, CMC/Liant 0,66, NTC 0,00, Super P 0,0, QX2/Graphite 0,0, vitesse 0,8 m/min; tortuosity 2.4; positive electrode NMC 811 from Targray KY181; formation temperature 60 °C; pressi... | Degradation | The capacity fade is thought to stem mainly from loss of active material, along with SEI thickening. | Suggested by the author | We built three graphite/NMC811 pouch full cells with a 10.24 cm² active area. The negative electrode used carbon-coated GHDR 15-4 graphite with no conductive additive, coated and then calendered to 12.9 mg/cm², 36% porosity and a tortuosity of 2.4. The positive electrode was 96.5 wt% NMC811 (Targray KY181). The electro... | Influence du procédé de fabrication d’électrodes de batterie sur les caractéristiques d’électrodes et les performances électrochimiques | Jean-Baptiste Guy | 2,024 | PhD (doctorat) | Université Grenoble Alpes [2020-....] | France | https://theses.hal.science/tel-05120632 |
run-089 | T45 | Li-ion | non-aqueous | Si-GS/P / Li half cell in a 12.5 mm Swagelok cell | half cell | Swagelock | Si-GS/P (porous solar-grade silicon) | anode | null | Unclear (p-type wafers; dopant element and concentration not given) | 1 M LiPF6 EC/DMC (LP30) | null | papier Whatman C90 | null | Not reported | 1 mV | 1 V | Li/Li+ | C/9 | Unclear (cycle life given as 53 cycles; exact failure cycle not stated) | lifetime 53 cycles; emergence of the 0.44 V peak (onset of the capacity drop) 50 cycle; capacity 2700 mAh/g; capacity retention threshold 80 % | Degradation | This correlation suggests Li15Si4 formation might underlie the capacity loss in both cases (PAA and CMC binders). | Suggested by the author | We made a 12.5 mm Swagelok half cell against pure lithium with porous solar-grade silicon. To make it, we electrochemically etched p-type polycrystalline solar-grade wafers, detached the porous layer electrochemically and ball-milled it. The electrode was 140 mg Si, 45 mg GNP and 15 mg PAA binder, with the pH brought t... | Élaboration d'une nouvelle architecture pour anodes en silicium poreux dans les batteries lithium-ion, intégrant une approche économique et écologique via l'utilisation de silicium grade solaire | Sofiane Abdelouhab | 2,024 | PhD (doctorat) | Université de Sherbrooke (Québec, Canada) | France | https://theses.hal.science/tel-05553249 |
run-090 | T46 | Li-S | solid state | Li2S full cell using CNT cathode with Li3PS4 surface coating, with PEO–LLZTO composite solid electrolyte membrane | full cell | coin | Li2S (CNT cathode) | cathode | Li3PS4 layer | null | null | PEO–LLZTO composite solid electrolyte membrane | PEO-LLZTO solid electrolyte separator | Not reported | 60 °C | 1 V | 3.5 V | Not reported | 0.1 C | Unclear (short circuit soon after 30 stable cycles; exact cycle not given) | current density 30 μA cm⁻²; Li2S loading 0.2 mg cm⁻²; Li3PS4 layer thickness ~3 μm; densification treatment none; stable cycling before short circuit 30 cycles; anode Ag-decorated Li anode | Short circuit | Probably caused by the tip effect: cathode surface irregularities locally raise current density, which triggers lithium dendrite growth in this sheet-type ASSB configuration. | Suggested by the author | We assembled an all-solid-state Li2S full coin cell with a CNT cathode, a PEO–LLZTO composite solid electrolyte separator and an Ag-decorated lithium anode. The cathode carried a ~3 µm spray-printed Li3PS4 surface layer. The Li2S was ~10 nm nanoparticles made by LiEt3BH reduction. The cathode ink was spray-printed on a... | Thin-film technology for flexible sulfide-based all-solid-state lithium batteries | Lilin Wu | 2,025 | PhD (doctorat) | Université de Rennes | France | https://theses.hal.science/tel-05534586 |
run-091 | T47 | Li-metal | non-aqueous | Li/PIL/Cu cells | half cell | coin (CR2032) | Li metal | anode | null | null | 1 M LiFSI Pyr13FSI/PDDAFSI (60:40 wt%) | null | PIL infiltrated Celgard separator | null | 40 °C | Not reported | 1.5 V | Not reported | 0.2 mA/cm2 | > 40 | areal capacity per cycle 1 mAh/cm2; Li reservoir plating 3 mAh/cm2; time at onset of diverging voltage trace > 400 hour | Degradation | The 1M PIL has a low transference number and low carrier concentration, so it develops gradients induced by ion depletion. | Stated by the author | We assembled a Li||Cu CR2032 coin cell with a 250 µm Li disc and a Celgard separator infiltrated with a PIL gel electrolyte of 1 M LiFSI in Pyr13FSI/PDDAFSI (60:40 wt%). We first plated a 3 mAh/cm2 Li reservoir at 0.2 mA/cm2. We then plated and stripped at 0.2 mA/cm2 and 1 mAh/cm2 per cycle at 40 °C, with a 1.5 V cutof... | Optimizing Electrode-Electrolyte Interfaces in Lithium Batteries | Karanth, Pranav | 2,025 | PhD | Delft University of Technology | Netherlands | https://doi.org/10.4233/uuid:62918903-e42d-4d9a-9599-d0a1cfde3ef0 |
run-092 | T48 | Li-ion | solid state | NMC-HE PVDF 7 wt.%/LPSCl/InLi cell | half cell | Not reported | NMC622 | cathode | Not reported | Not reported | null | LPSCl | LPSCl pellet (no binder) | 50 MPa | 25 °C | 2.1 V | 3.9 V | InLi+/InLi | C/10 | Unclear (cycle count not given; capacity fell steeply over the first few cycles) | binder PVDF-1 (HE PVDF-1 7 wt.% catholyte); initial specific capacity 181 mAh.g-1; specific capacity after 50 cycles 59 mAh.g-1 | Degradation | Possibly an insulating compound forming, the composite electrode cracking so that ion and electron pathways became more tortuous, and/or NMC particles losing contact. | Suggested by the author | We tested an all-solid-state half cell with a composite cathode of NMC622, LPSCl and the HE PVDF-1 7 wt.% catholyte (NMC/LPSCl/PVDF-1 70/28/2 wt.%). The cathode was dry-mixed in a mortar and pressed at 250 MPa, with an NMC loading of 14.5 mg cm-2. The cell had a binder-free LPSCl pellet separator and an InLi counter el... | Role of binder in the engineering of all-solid batteries | Lucas Trassart | 2,025 | PhD (doctorat) | Université Grenoble Alpes [2020-....] | France | https://theses.hal.science/tel-05320949 |
run-093 | T48 | Li-ion | solid state | NMC-HE PVDF 30 wt%/LPSCl/InLi cell | half cell | Not reported | NMC622 | cathode | Not reported | Not reported | null | LPSCl | LPSCl pellet (no binder) | 50 MPa | 25 °C | 2.1 V | 3.9 V | InLi+/InLi | C/10 | Unclear (cycle count not given; NMC apparently inactive after 10 cycles) | binder PVDF-1 (HE PVDF-1 30 wt.% catholyte); initial specific capacity 146 mAh.g-1; specific capacity after 50 cycles 30 mAh.g-1 | Degradation | The irregular capacity trend across cycling in the cell using HE PVDF-1 30 wt.% catholyte may indicate contact problems. | Suggested by the author | We tested an all-solid-state half cell with a composite cathode of NMC622, LPSCl and the HE PVDF-1 30 wt.% catholyte (NMC/LPSCl/polymer 70/21/9 wt.%). The cathode was dry-mixed in a mortar and pressed at 250 MPa, with an NMC loading of 14.5 mg cm-2. The cell had a binder-free LPSCl pellet separator and an InLi counter ... | Role of binder in the engineering of all-solid batteries | Lucas Trassart | 2,025 | PhD (doctorat) | Université Grenoble Alpes [2020-....] | France | https://theses.hal.science/tel-05320949 |
run-094 | T49 | Li-ion | solid state | Li2.07Ni0.62N composite | Li6PS5Br | Li half-cell | half cell | CR2032 coin-cell | Li2.07Ni0.62N | anode | null | null | null | Li6PS5Br | null | Not reported | Not reported | 0.02 V | 1 V | Li+/Li | C/25 | Unclear (cycle count not given; 99 ± 1% efficiency sustained for 17 cycles) | current density 8 mA g-1; stable galvanostatic profile (cycles) 1–16; reversible gravimetric capacity before drop 150 mAh g-1; solid electrolyte synthesis ball-milled | Interfacial failure | Failure may eventually stem from by-products of argyrodite degradation piling up at the nitride interface. | Suggested by the author | We built an all-solid-state Li2.07Ni0.62N composite | Li6PS5Br | Li half cell in a CR2032 coin cell. The working electrode was a hand-ground composite of 45 wt.% Li2.07Ni0.62N, 5 wt.% CVGF and 50 wt.% ball-milled Li6PS5Br, at an active loading of about 5 mg cm-2. We cycled it at C/25 (8 mA g-1) between 0.02 and 1 V. It... | Development of new electrolytes for all-solid state Li-ion batteries | Yaxin Qu | 2,025 | PhD (doctorat) | Université Paris-Est Créteil Val-de-Marne - Paris 12 | France | https://theses.hal.science/tel-05517445 |
run-095 | T49 | Li-ion | solid state | NMC composite | Li5.6PS4.6Br1.4 | Li-In half-cell | half cell | CR2032 coin-cell | NMC622 | cathode | null | null | null | Li5.6PS4.6Br1.4 | null | Not reported | Not reported | 2.6 V | 4.3 V | Li+/Li | 9 mA g-1 | 27–40 | discharge capacity before drop 142 mAh g-1; discharge capacity at 40th cycle 80 mAh·g-1; Li-In alloy formation pre-treatment temperature 50 °C | Mechanical failure | The capacity fade at cycle 30 is probably due to a different factor: volume change of the NMC cathode over cycling. | Suggested by the author | We tested an all-solid-state NMC622 composite | Li5.6PS4.6Br1.4 | Li-In half cell in a CR2032 coin cell. The cathode was a hand-ground composite of 68 wt.% NMC622, 2 wt.% CVGF and 30 wt.% argyrodite, and the cell was kept at 50 °C overnight to form the Li-In alloy. We cycled it at 9 mA g-1 between 2.6 and 4.3 V vs Li+/... | Development of new electrolytes for all-solid state Li-ion batteries | Yaxin Qu | 2,025 | PhD (doctorat) | Université Paris-Est Créteil Val-de-Marne - Paris 12 | France | https://theses.hal.science/tel-05517445 |
End of preview. Expand in Data Studio
Failed Battery Runs from PhD Theses
Battery experiments that failed, with the conditions they ran under and the reason the researcher gave.
Papers report the experiments that worked. The cells that shorted, cracked or faded mostly stay in the lab, and the most complete public record of them is the PhD thesis, which documents a whole project, including the runs that never reached a paper. This is a curated sample of 100 failed runs from 50 battery theses, shared for evaluation. Each run is recorded with its cell, materials and test conditions, how it failed, and the cause the author gave.
Thesis, to failed run, to test conditions, to failure mode and stated cause.
At a glance
| Failed runs | 100 |
| Theses | 50 |
| Thesis years | 2014 to 2026 |
| Solid-state runs | 39 |
| Cause stated outright by the author | 48 |
| Cause suggested by the author | 52 |
| Failure mode | Runs |
|---|---|
| Mechanical failure | 21 |
| Short circuit | 19 |
| Degradation | 18 |
| Interfacial failure | 16 |
| Contamination | 14 |
| Did not work in that regime | 12 |
One run
An all-solid-state NMC622 cell with a halide catholyte and a sulfide separator, which failed at the interface between the two electrolytes.
run_id run-054
battery_state solid state
cell NMC622/C-Li3InCl6/VGCF | C-Li6PS5Cl | Li0.5In/C-Li6PS5Cl (hetero-structure)
cell_type full cell
active_material NMC622
coating Li2O-ZrO2
solid_electrolyte C-Li3InCl6 (solvent-free) in cathode composite; C-Li6PS5Cl separator and anode composite
stack_pressure 1 ton/cm2
temperature room temperature
voltage_lower 2.1 V
voltage_upper 3.6 V
voltage_reference LiIn/In
c_rate_or_current C/20
cycle_number Unclear (failure cycle not given; 50% capacity loss after 20 cycles)
failure_mode Interfacial failure
failure_reason The degradation arises because Li3InCl6 is chemically unstable against sulfide solid electrolytes, which forms a passivation interlayer.
reason_given_as Stated by the author
thesis_year 2022
institution Sorbonne Université
The full record (records.jsonl) also carries the remaining conditions, the basis of each value (stated in the thesis or inferred from it), and a short summary of the run.
What a run carries
- The cell and its format, the active material with any coating or dopant, and the electrolyte, liquid or solid
- Test conditions, including temperature, voltage window and reference, C-rate or current, cycle number and stack pressure
- Other values the thesis records for the run, such as capacities before and after the failure
- The failure mode, and the cause in the author's own reasoning, marked as stated outright or suggested
- A short summary of the run, and the thesis it came from with a link
Every condition is in one of four states. It has a value, it is not reported in the thesis, it is mentioned without a usable value (marked Unclear, with a note), or it does not apply to the cell (n/a). Nothing is filled in from general knowledge.
How the runs were chosen
Each thesis was read by a language model, which recorded every condition together with the passage it came from. A second model then judged each run, and a final independent check confirmed it. A run is included only when the failing cell is the subject of the experiment, not a baseline the author improved on, and when the author gives a cause. No thesis contributes more than six runs, so runs from one thesis often form a series in which one condition changes.
Text and sources
No thesis text is reproduced. Conditions are recorded as facts, and summaries and causes are written in our own words. Values from French-language theses are translated, and thesis titles are kept as published. Every run links to its thesis.
Limits
Theses report failures unevenly, so the mix of failure modes reflects what authors chose to write up rather than how often each failure happens. The cause is the author's explanation and has not been tested independently. Most runs come from French theses, because French repositories deposit full theses openly.
Files
| File | What |
|---|---|
runs.csv |
One row per run, 33 columns, shown in the viewer |
records.jsonl |
The same runs as structured records, with the basis of each condition |
Beyond this sample
The full set is larger, and the same method extends to more theses and to other experimental domains. For access, other domains, or records in a different format, contact andre.mizoguchi@mail.mcgill.ca.
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