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Triweekly Patent Update – 2025-05-20 – Free Version

  • Lithium-ion batteries – electrolytes – solid & semi-solid

  • ALL-SOLID-STATE CELL
    Applicant: TOYOTA MOTOR / US 2025125490 A1

    All-solid-state cells with sulfide electrolyte and lithium metal negative electrodes were constructed. Cells with 0.25 vol% Sn in the first solid electrolyte layer exhibit a charging capacity of 1.65 mAh/cm2 when charged between 3.0 V and 4.2 V at 3 mA/cm2. This optimal cell included an Mg layer (thickness: 1000 nm) deposited on the Ni foil current collector and a Sn layer (thickness: 100 nm) between the Mg layer and the first solid electrolyte layer.
    The outstanding performance is attributed to the optimal metal phase proportion that allows for effective trapping of lithium dendrites while maintaining good ionic conductivity. The Li2S ∙ P2S5 ∙ LiI solid electrolyte serves as both the first and second solid electrolyte layers, with only the first layer containing the dispersed Sn phase.
    When charged, an alloy of Sn and Li forms in the first solid electrolyte layer, functioning as a protective layer that prevents decomposition of the sulfide solid electrolyte, resulting in superior cycling characteristics without short circuits.
    The Figure below shows a schematic cross-sectional view of an all-solid-state cell with the following layers: 1: negative electrode current collector (Ni foil), 2: metal layer (Mg metal), 3A: first solid electrolyte layer (containing Sn metal phase), 3B: second solid electrolyte layer (Li2S ∙ P2S5 ∙ LiI), 4: positive electrode active material layer, 5: positive electrode current collector, 10: all-solid-state cell, DT: thickness direction.

    Patent Image, Toyota Motor

    This work illustrates how the presence of Sn and Mg at the lithium metal / sulfide electrolyte interface reduces the risk of lithium dendrite formation while charging all-solid-state lithium metal cells with sulfide electrolytes.

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  • Lithium-ion batteries – negative electrode (excluding Li metal electrodes)

  • Silicon-carbon negative electrode material and preparation method thereof
    Applicant: Contemporary Amperex Technology Co., Ltd. (CATL) / CN 119852338 A

    A silicon-carbon negative electrode material was prepared by a two-step process. In the first step, porous carbon was heated (500°C, 2 h, under Ar, rotary kiln) to remove adsorbed oxygen. After vacuum evacuation to 1×10-5 Pa and argon purging, monosilane and argon (volume ratio 1:4) were introduced to form silicon-carbon particles with 200 Pa micropositive pressure, with the kiln rotating at 40 Hz.
    In the second step, the temperature was raised to 600°C and a gas mixture of acetylene, methane, and argon (volume ratio 2:1:7) was introduced at 0.2 kPa pressure (40 Hz rotation).
    The resulting material exhibits a high-valence silicon content of 15.2% in the region extending 10 nm inward from the surface, 7.4% at 10-20 nm depth, and 2.9% at 20-30 nm depth, as determined by X-ray photoelectron spectroscopy (XPS) depth profiling using argon ion etching. XPS analysis also confirms the distribution of low-valence silicon (binding energy 98-102 eV) and high-valence silicon (binding energy 102-106 eV, see Figure).
    In contrast, the XPS spectrum of the comparative example processed at 200°C exhibits a much higher proportion of high-valence silicon, with the high-valence silicon peak (102-106 eV) being more prominent relative to the low-valence silicon peak (98-102 eV).
    The resulting material exhibits a discharge capacity of 1,984 mAh/g and a first cycle efficiency of 93.8% in half-cell tests. In contrast, the comparative example processed at 200°C exhibits a lower discharge capacity of 1,766 mAh/g, a reduced first cycle efficiency of 83.5% in half-cells.
    强度: intensity
    低价硅: low-valence silicon
    高价硅: high-valence silicon
    基线: baseline
    电子结合能: electron binding energy (eV)

    Patent Image, CATL

    The difference in silicon valence states between samples can potentially be explained by oxidation mechanisms. Low-valence silicon (0 to 2+ oxidation states) represents silicon species like elemental Si (0) and partially oxidized silicon, while high-valence silicon (3+ to 4+ oxidation states) presumably consists of silicon oxide species like SiO2. When processed at insufficient temperatures (200°C), oxygen from residual gases in the reaction vessel or from the carbon framework itself might react with deposited silicon, forming silicon oxides. At the optimal temperature (600°C), the carbon coating deposition rate is presumably higher and more uniform, creating a protective layer that effectively prevents silicon oxidation.
    XPS measurements in Si-carbon composite materials might also explain electrochemical differences in other Si-carbon materials that appear similar in terms of other characterization methods (such as Si content & crystallinity, particle size distribution, BET specific surface area).

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  • Lithium-ion batteries – positive electrode

  • ANIONIC REDOX HIGH ENERGY CATHODES
    Applicant: WILDCAT DISCOVERY TECHNOLOGIES / TIANJIN B & M SCIENCE TECHNOLOGY / WO 2025065466 A1

    Li1.15Mn0.6Ni0.225O2 was doped with tungsten and coated with lithium borate (LBO). The core material was prepared by ball milling lithium, manganese, and nickel precursors (selected from Mn2O3, Mn3O4, Ni(OH)2, Li2CO3) in a planetary mill using zirconia media (5 mm size, 6 h). The milled precursors were annealed (870°C, 10 h, air) to form the lithium-rich manganese nickel oxide material.
    For tungsten doping, the precursors were modified to achieve a composition of Li1.15Mn0.596Ni0.224W0.005O2 (W-containing precursor not identified). The lithium borate coating was applied by ball-milling H3BO3 (1 mol%) with the active material in ethanol/water (7:3 by mass) using Teflon milling media. The solid content was maintained at 25 mass%. The resulting mixture was dried (90°C, 2 h) and annealed (500°C, 5 h, air) to form the LBO coating.
    For comparison, an uncoated (pristine) Li1.15Mn0.6Ni0.225O2 material, a material with only LBO coating (1 mol%), and a material with only Nb2O5 coating (2 mol%) were prepared using similar procedures. The Nb2O5 coating was applied using Nb(OC2H5)5 as the precursor.
    The coated and uncoated materials were used to prepare cathodes (90 mass% active material, 5 mass% Super C65 carbon black, 5 mass% PVDF) with a loading of 11.1 mg/cm2. Full cells were assembled with graphite anodes and tested with a standard electrolyte (EC/EMC/LiPF6, 2% FEC, 6% DEC, 2 mass% tris(trimethylsilyl) phosphite).
    As shown in Figure below, the W-doped LBO-coated material exhibits the best performance, maintaining a cycling capacity above 190 mAh/g after 200 cycles. The LBO-coated and Nb2O5-coated materials exhibit similar performance with capacities around 185 mAh/g after 200 cycles, while the uncoated pristine material rapidly degrades to below 100 mAh/g after approximately 150 cycles.

    Patent Image, Wildcat Discovery Technologies / Tianjin B&M Science Technology

    This work illustrates how the combination of tungsten doping and lithium borate coating improves the cycling stability of LRLO (Li-rich layered oxide) active materials.

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  • Fuel cells (PEMFC / SOFC / PAFC / AEMFC) – electrochemically active materials

  • Fuel cell membrane electrode, preparation method thereof and fuel cell
    Applicant: Weishi Energy Technology / CN 119852456 A

    A PEMFC electrode was prepared with a cathode catalyst layer comprising three sequentially arranged layers (first, second, and third catalyst layers), with the first catalyst layer adjacent to the proton exchange membrane. Each catalyst layer independently contains catalyst and ionomer, with the first catalyst layer containing hydrophilic nanoparticles and the third catalyst layer containing hydrophobic nanoparticles.
    The hydrophilic nanoparticles in the first catalyst layer includes TiO2 nanoparticles with a specific surface area of 100-400 m2/g. The mass ratio of hydrophilic nanoparticles to catalyst is 0.05-0.8:1.
    The second catalyst layer contains only catalyst and ionomer without any additional nanoparticles, serving as a transition layer between the hydrophilic first layer and the hydrophobic third layer. The Pt loading in the second layer is 0.05-0.15 mg/cm2, similar to the other catalyst layers.
    The hydrophobic nanoparticles in the third catalyst layer include PTFE nanoparticles with a specific surface area of 100-400 m2/g. The mass ratio of hydrophobic nanoparticles to catalyst is 0.02-0.40:1.
    The catalyst used in all three layers is TEC10E50E (Tanaka Precious Metals) consisting of 50.5% Pt supported on 49.5% carbon black. This commercial Pt/C catalyst was used in its as-received state without further modification. In the experimental examples, the catalyst was dispersed in water and mixed with isopropanol and Nafion D2020 ionomer solution (20% solid content) to form the catalyst ink for each layer.
    This design results in a hydrophilic-to-hydrophobic gradient from the membrane side outward, improving both proton conduction near the membrane and formation of capillary force gradients in catalyst layer pores, facilitating oxygen transport and liquid water removal, thereby enhancing fuel cell power density.
    The electrode layers were applied sequentially by ultrasonic spray-coating onto a Gore proton exchange membrane (12 μm thickness), with each layer dried (70°C, 5 min) before applying the next layer. The anode catalyst layer was applied to the opposite side of the membrane with a Pt loading of 0.05 mg/cm2.
    As shown in the Figure, the polarization curve comparison between Example 1 (with the three-layer gradient design) and Comparative Example 1 (conventional catalyst layer) demonstrates significant performance improvements across the entire current density range. The performance enhancement is particularly pronounced at high current densities, indicating improved mass transport capabilities of the gradient cathode structure.
    对比例1: comparative example 1
    实施例1: example 1
    电压(V): voltage (V)
    电流密度(A/cm2): current density (A/cm2)

    Patent Image, Weishi Energy Technology

    This work illustrates how a gradient structure in the cathode catalyst layer of a PEMFC can improve performance, through the selective incorporation of TiO2 and PTFE nanoparticles.

  • The premium version includes another two patent discussions, plus an Excel list with 50-100 commercially relevant recent patent families.
  • Triweekly patent lists for other categories (Excel files are included for premium users)

  • - Lithium metal batteries (excluding Li-S, Li-Air): XLSX
  • - Lithium-air batteries: XLSX
  • - Lithium-ion batteries – electrolytes – liquid: XLSX
  • - Lithium-ion batteries – separators: XLSX
  • - Lithium-sulfur batteries: XLSX
  • - Na-ion batteries: XLSX
  • Prior patent updates

  • 2025-04-29
  • 2025-04-08
  • 2025-03-18
  • 2025-02-25
  • 2025-02-04

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