WO2021098820A1 - 预锂化聚苯硫醚、聚苯硫醚固态电解质膜、电池极片、准固态锂离子电池及其制造方法 - Google Patents

预锂化聚苯硫醚、聚苯硫醚固态电解质膜、电池极片、准固态锂离子电池及其制造方法 Download PDF

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WO2021098820A1
WO2021098820A1 PCT/CN2020/130376 CN2020130376W WO2021098820A1 WO 2021098820 A1 WO2021098820 A1 WO 2021098820A1 CN 2020130376 W CN2020130376 W CN 2020130376W WO 2021098820 A1 WO2021098820 A1 WO 2021098820A1
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polyphenylene sulfide
powder
lithium
solid
ptfe
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PCT/CN2020/130376
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English (en)
French (fr)
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周海涛
高宏权
伍建春
俞崇晨
刘孟豪
侯栋
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江苏大学
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Priority claimed from CN201911149824.4A external-priority patent/CN111004404B/zh
Priority claimed from CN201911394880.4A external-priority patent/CN111018061B/zh
Priority claimed from CN202010084430.1A external-priority patent/CN111342121B/zh
Priority claimed from CN202010573661.9A external-priority patent/CN111864272B/zh
Application filed by 江苏大学 filed Critical 江苏大学
Priority to US17/413,960 priority Critical patent/US11289737B2/en
Publication of WO2021098820A1 publication Critical patent/WO2021098820A1/zh

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    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
    • H01M10/00—Secondary cells; Manufacture thereof
    • H01M10/05—Accumulators with non-aqueous electrolyte
    • H01M10/056—Accumulators with non-aqueous electrolyte characterised by the materials used as electrolytes, e.g. mixed inorganic/organic electrolytes
    • H01M10/0564—Accumulators with non-aqueous electrolyte characterised by the materials used as electrolytes, e.g. mixed inorganic/organic electrolytes the electrolyte being constituted of organic materials only
    • H01M10/0565—Polymeric materials, e.g. gel-type or solid-type
    • C—CHEMISTRY; METALLURGY
    • C08—ORGANIC MACROMOLECULAR COMPOUNDS; THEIR PREPARATION OR CHEMICAL WORKING-UP; COMPOSITIONS BASED THEREON
    • C08G—MACROMOLECULAR COMPOUNDS OBTAINED OTHERWISE THAN BY REACTIONS ONLY INVOLVING UNSATURATED CARBON-TO-CARBON BONDS
    • C08G75/00—Macromolecular compounds obtained by reactions forming a linkage containing sulfur with or without nitrogen, oxygen, or carbon in the main chain of the macromolecule
    • C08G75/02—Polythioethers
    • C—CHEMISTRY; METALLURGY
    • C08—ORGANIC MACROMOLECULAR COMPOUNDS; THEIR PREPARATION OR CHEMICAL WORKING-UP; COMPOSITIONS BASED THEREON
    • C08G—MACROMOLECULAR COMPOUNDS OBTAINED OTHERWISE THAN BY REACTIONS ONLY INVOLVING UNSATURATED CARBON-TO-CARBON BONDS
    • C08G75/00—Macromolecular compounds obtained by reactions forming a linkage containing sulfur with or without nitrogen, oxygen, or carbon in the main chain of the macromolecule
    • C08G75/02—Polythioethers
    • C08G75/0204—Polyarylenethioethers
    • C—CHEMISTRY; METALLURGY
    • C08—ORGANIC MACROMOLECULAR COMPOUNDS; THEIR PREPARATION OR CHEMICAL WORKING-UP; COMPOSITIONS BASED THEREON
    • C08G—MACROMOLECULAR COMPOUNDS OBTAINED OTHERWISE THAN BY REACTIONS ONLY INVOLVING UNSATURATED CARBON-TO-CARBON BONDS
    • C08G75/00—Macromolecular compounds obtained by reactions forming a linkage containing sulfur with or without nitrogen, oxygen, or carbon in the main chain of the macromolecule
    • C08G75/02—Polythioethers
    • C08G75/0204—Polyarylenethioethers
    • C08G75/025—Preparatory processes
    • C08G75/0254—Preparatory processes using metal sulfides
    • C—CHEMISTRY; METALLURGY
    • C08—ORGANIC MACROMOLECULAR COMPOUNDS; THEIR PREPARATION OR CHEMICAL WORKING-UP; COMPOSITIONS BASED THEREON
    • C08G—MACROMOLECULAR COMPOUNDS OBTAINED OTHERWISE THAN BY REACTIONS ONLY INVOLVING UNSATURATED CARBON-TO-CARBON BONDS
    • C08G75/00—Macromolecular compounds obtained by reactions forming a linkage containing sulfur with or without nitrogen, oxygen, or carbon in the main chain of the macromolecule
    • C08G75/14—Polysulfides
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
    • H01M10/00—Secondary cells; Manufacture thereof
    • H01M10/05—Accumulators with non-aqueous electrolyte
    • H01M10/052—Li-accumulators
    • H01M10/0525—Rocking-chair batteries, i.e. batteries with lithium insertion or intercalation in both electrodes; Lithium-ion batteries
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
    • H01M2300/00—Electrolytes
    • H01M2300/0017—Non-aqueous electrolytes
    • H01M2300/0065—Solid electrolytes
    • H01M2300/0082—Organic polymers
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
    • H01M2300/00—Electrolytes
    • H01M2300/0085—Immobilising or gelification of electrolyte
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
    • Y02E—REDUCTION OF GREENHOUSE GAS [GHG] EMISSIONS, RELATED TO ENERGY GENERATION, TRANSMISSION OR DISTRIBUTION
    • Y02E60/00—Enabling technologies; Technologies with a potential or indirect contribution to GHG emissions mitigation
    • Y02E60/10—Energy storage using batteries
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
    • Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
    • Y02P70/00—Climate change mitigation technologies in the production process for final industrial or consumer products
    • Y02P70/50—Manufacturing or production processes characterised by the final manufactured product

Definitions

  • the invention relates to a pre-lithiated polyphenylene sulfide, polyphenylene sulfide solid electrolyte membrane, battery pole piece, high-safety high-volume energy density quasi-solid lithium ion battery and a manufacturing method thereof, and belongs to new energy material and device manufacturing technology field.
  • solid-state lithium-ion batteries have attracted more and more attention from industry and academia due to their excellent safety performance and potential high energy density.
  • the power density of solid-state lithium-ion batteries is very low, which greatly limits its commercial promotion and application.
  • the key issue that urgently needs a breakthrough is the development of a new type of solid electrolyte material with high conductivity and excellent processing performance.
  • Current inorganic ceramic / glass electrolytes such as Li 5 La 3 Zr 2 O 12 , Li 3x La 2 / 3x TiO 3, and sulfide electrolyte lithium ion conductivity due up 10 -4 ⁇ 10 -2 S cm - 1.
  • the current traditional pole piece manufacturing process uses a solvent-containing wet coating process. This method has the inherent defects of high porosity, low conductivity, and low load, making it impossible to manufacture thick pole pieces. This limits the further increase in the energy density of lithium batteries.
  • the present invention provides a pre-lithiated polyphenylene sulfide, polyphenylene sulfide solid electrolyte membrane, battery pole pieces, high-volume energy-density quasi-solid-state lithium ion battery with high safety and long life and the same
  • the manufacturing method the solid solubility of lithium in the pre-lithiated polyphenylene sulfide solid electrolyte membrane material prepared by this method is high, and the chloride ion in the membrane material is effectively bound, making it an excellent conductor of single lithium ion;
  • the battery pole piece does not rely on solvents, the load is large, and the thickness is uniform and controllable; the manufactured quasi-solid lithium-ion battery has a simplified assembly process, high safety, long life, high volume energy density, convenient electrolyte infiltration, and easy manufacturing area Large, thin blade battery.
  • a method for manufacturing pre-lithiated polyphenylene sulfide with high lithium solid solubility which is characterized in that it comprises the following steps:
  • NMP N-methylpyrrolidone
  • p-DCB 1,4-dichlorobenzene
  • chloride ion complexing agent in the mixed powder, add chloride ion complexing agent, stir evenly, and place in a closed reactor, react at 150-250 °C for 80-200 minutes, and then After washing and drying, pre-lithiated polyphenylene sulfide with high lithium solid solubility is obtained.
  • Li 2 S is formed by a high-temperature reaction of metallic lithium powder and sulfur powder or formed by a carbothermal reduction reaction of lithium sulfate (Li 2 SO 4 ).
  • the molar ratio of NMP, lithium sulfide Li 2 S, and lithium hydroxide LiOH is 1-5:1:0.05-0.2.
  • the molar ratio of Li 2 S to p-DCB is 1.3-0.8:1.
  • the method of evaporation or sublimation is hot-air drying method, rotary evaporation method, freeze-drying method, which retains the solid phase components to the maximum extent and only removes NMP and H 2 O.
  • chloride ion complexing agent is an organic non-metal ion complexing agent, preferably calixarene crown ether, caliximidazole, calixpyrrole, and calixarene.
  • the added amount of the chloride ion complexing agent is 0.01-0.2 times that of p-DCB.
  • the weight percentage of the pre-lithiated polyphenylene sulfide powder is 80%-97%.
  • the pre-lithiated polyphenylene sulfide prepared by the method for preparing the pre-lithiated polyphenylene sulfide with high lithium solid solubility.
  • the method for preparing an isotropic polyphenylene sulfide solid electrolyte membrane is characterized in that the pre-lithiated polyphenylene sulfide powder and polytetrafluoroethylene (PTFE) are exposed to the temperature condition in which the polytetrafluoroethylene is glassy.
  • the mixer is evenly mixed, and supersonic gas is used for air grinding, so that the molecular chain of PTFE is extended and opened, and physical adhesion is formed between the pre-lithiated polyphenylene sulfide powder and no chemical reaction occurs; then it passes through the extruder.
  • the gas in the powder is removed to form a continuous cake-like broadband, and then the continuous cake-like broadband is made into a pre-lithiated polyphenylene sulfide film by a hot roll at a temperature of less than 150°C, and then rolled; prepared into polyphenylene sulfide Solid electrolyte membrane.
  • the pre-lithiated polyphenylene sulfide powder is the pre-lithiated polyphenylene sulfide according to claim 9; the air milling is to first preheat the powder to 40-50° C., and directional drawing the PTFE The equipment uses supersonic jet gas to jet and draw PTFE.
  • the directional drawing of PTFE is that the PTFE in the powder is preheated by the supersonic jet gas to form a viscous fluid state, and the PTFE viscous fluid is ejected through a small nozzle to form a supersonic jet fluid under pressure.
  • the mixed powder is sucked in through the venturi structure and collected in the volute cavity.
  • the collected material becomes a spatial network of loose agglomerates.
  • the temperature of the pre-lithiated polyphenylene sulfide powder and PTFE is controlled to be below 10°C during the uniform mixing process in the mixer; the mixing time in the mixer is 0.5-4 hours.
  • the pre-lithiated polyphenylene sulfide film material after hot pressing also includes the following treatment processes:
  • Two or more sheets of pre-lithiated polyphenylene sulfide one-time lamination membrane materials are hot-pressed and composited into a defect-free high-density solid electrolyte membrane; or:
  • Two heated fluorine rubber modules are used to heat the pre-lithiated polyphenylene sulfide membrane material at 150-230°C for 1-10 seconds, so that the microcracks and holes of the pre-lithiated polyphenylene sulfide membrane material can be healed.
  • a defect-free high-density solid electrolyte membrane is made.
  • the polyphenylene sulfide solid electrolyte membrane is prepared by the preparation method of the polyphenylene sulfide solid electrolyte membrane.
  • the method for preparing high-load battery pole pieces is characterized in that the conductive carbon material is mixed with the positive electrode material and the negative electrode material of the lithium ion battery respectively in a mixer; and then separately with the PTFE powder under the temperature condition that the PTFE is glassy. Mix uniformly, use supersonic jet gas to extend and open the molecular chain of PTFE, and form physical adhesion with the mixed powder of conductive carbon material and lithium-ion battery cathode and anode materials, and no chemical reaction occurs; it is made under high temperature and heat pressure.
  • the film-forming material D is then thermally composited with the single-sided heat collector of the perforated current collector by a hot-pressing composite process to form a single-sided loaded positive electrode thick electrode and a single-sided loaded negative electrode thick electrode.
  • the weight percentage of the positive electrode material or negative electrode material of the lithium ion battery and the carbon material is 50%-95%: 50%-5%.
  • the weight percentage of the mixed powder of the PTFE powder and the conductive carbon material, the positive or negative electrode material of the lithium ion battery is 3%-15%: 85%-97%.
  • the hot pressing temperature is 150-250°C.
  • the rolling temperature is 120-220°C.
  • the current collector and a piece of film material D are unrolled at the same speed and enter two relatively rotating hot roller presses.
  • the width of the roll gap and the pressure are controlled so that the film material D can just be compounded on the current collector, so as to avoid excessive deformation of the film due to excessive roller pressure and breakage of the current collector.
  • the use of supersonic jet gas to extend and open the molecular chain of PTFE is to first preheat the powder to 40-50°C, and use supersonic jet gas jet drawing in the PTFE directional drawing equipment, the PTFE directional drawing ,
  • the PTFE in the powder forms a viscous fluid state after being preheated by the supersonic jet gas.
  • the PTFE viscous fluid is sprayed out through a small nozzle to form a supersonic jet fluid, and the mixed powder is sucked in through the venturi structure. , It is collected in the volute cavity, and the collected materials become loose agglomerates of spatial network.
  • the conductive carbon material is one or a mixture of super-P, acetylene black, activated carbon, artificial graphite, and high-purity graphite;
  • the current collector is a stainless steel foil coated with carbon protection and perforated , Aluminum foil or copper foil.
  • the single-side-loaded positive electrode thick electrode and the single-side-loaded negative electrode thick electrode prepared by the preparation method of any one of claims 16-22 are used as the positive pole piece and the negative electrode, respectively Pole piece, assembling a quasi-solid lithium-ion battery, stack the positive pole piece, polyphenylene sulfide solid electrolyte and negative pole piece in sequence, and the unloaded side of the positive pole piece and negative pole piece face outward; Perform hot pressing and compounding at ⁇ 150°C to form a "sandwich" structure of the composite sheet. After the composite sheet is encapsulated by a packaging film, it is vacuum injected and heat sealed into the shell.
  • a plurality of composite sheet layers are stacked together using a laminator, the positive electrode current collector is bonded to the positive current collector, the negative electrode current collector is bonded to the negative current collector, and the lugs are welded, and then The composite sheet is encapsulated by packaging film.
  • the packaging film is an insulating flexible packaging film, preferably an aluminum plastic film, a polyimide film, or a plastic film.
  • the high-safety, high-volume energy density quasi-solid-state lithium ion battery is prepared by the method for manufacturing a high-safety, high-volume energy density quasi-solid-state lithium-ion battery.
  • the present invention has the following beneficial effects:
  • Polyphenylene sulfide is used as the carrier of the solid electrolyte, which has good thermal stability, is not easy to burn, has high safety, and has a long life.
  • the traditional pre-lithiated polyphenylene sulfide solid electrolyte is prepared by the method of salivation molding. During the recrystallization process of the salivation molding, the crystal orientation exists, which will cause the anisotropy of the lithium ion transmission performance, and the lithium ion in the horizontal film direction
  • the electrical conductivity is 1 to 2 orders of magnitude greater than the electrical conductivity in the direction perpendicular to the film.
  • the pre-lithiated polyphenylene sulfide powder is mixed with PTFE to form agglomerates in the PTFE directional drawing equipment.
  • the PTFE is preheated by the jet gas to form a viscous fluid state, and the PTFE viscous fluid passes through under pressure.
  • the small nozzles form a supersonic jet fluid ejection, suck electrode material powder through the venturi tube structure, fill it in the PTFE fiber cluster, and collect it in the volute cavity. The collected material becomes a spatial network of loose agglomerates.
  • the molecular chain of the long-chain PTFE stretches and opens, and the functionalized organic powder is physically adhered to the PTFE molecular chain; the gas discharged from the powder through the extruder is made into a continuous cake-like broadband, and the cake-like broadband is in the physical and chemical properties of the organic powder. Change the temperature below ( ⁇ 150°C) to form a film through hot pressing.
  • PTFE has a high compression ratio, high molecular weight, and long chain segments; during the preparation process, the pre-lithiated polyphenylene sulfide powder and PTFE are fully adhered to the molecular chain of PTFE during air milling to achieve uniform mixing.
  • the functionalized powder is wrapped by the adhesion between PTFE molecular chains in the process of forming a continuous cake-like broadband through an extruder.
  • the continuous cake-shaped broadband can be preformed first, which can effectively remove the air in the loose powder after air milling, which is beneficial to the formation of a continuous uniform film.
  • the manufacturing process does not use high temperature, the processing temperature is always below the temperature at which the physical and chemical properties of the organic powder changes, and the manufacturing process does not use additives such as solvents, which avoids functional damage caused by the dissolution of the powder.
  • the membrane material manufacturing process will not recrystallize the functionalized powder, will not appear anisotropy, and it is easy to manufacture dense membrane materials, especially for organic solid electrolyte membranes, which can ensure that the membrane materials have excellent performance in all directions. Ionic conductivity characteristics.
  • the whole process is a physical process.
  • the pre-lithiated polyphenylene sulfide powder will not undergo chemical reactions, and its physical and chemical properties will not change. Therefore, the prepared functional membrane material has ideal catalytic, metal ion exchange or proton exchange properties. .
  • the pre-lithiated polyphenylene sulfide solid electrolyte in the present invention adopts a low-temperature non-damage manufacturing method, and the lithium ion conductivity of the membrane material does not produce anisotropy. Therefore, the present invention is particularly suitable for pre-lithiated polyphenylene sulfide powders that are not suitable for film formation by injection molding or salivation, or the effects of high temperature or solvents will damage the function of organic powders, or produce anisotropic effects in film formation.
  • LiOH is first added for better dehydration of the system .
  • the reaction between Li 2 S and p-DCB is a nucleophilic substitution reaction, and aprotic polarity is conducive to the occurrence of the reaction, but H 2 O can have a solvation effect with Li 2 S, thereby weakening its nucleophilic effect and reducing monomer reactivity.
  • Better dehydration can increase the yield of the linear crystallization region of polyphenylene sulfide, while the ratio of The linear region can ensure that there are a large number of fast migration channels for lithium ions in the structure.
  • the solvent and water are directly evaporated or sublimated to realize the conversion of the product to the reactant in one step, and realize the nano-level mixing of polyphenylene sulfide and lithium salt in situ, which promotes the subsequent high-temperature solid solution reaction fully.
  • Polyphenylene sulfide with high crystallinity has high hardness and high strength, and it is difficult to break. It is difficult to prepare nano-level polyphenylene sulfide powder. Simply mixing and heating polyphenylene sulfide powder and lithium salt will cause uneven reaction. Low solid solubility and low conductivity.
  • the added chloride ion complexing agent can effectively separate lithium ions and chloride ions, promote the capture of lithium ions by the sulfur sites on the polyphenylene sulfide chain, and increase the solid solubility of lithium, thereby increasing the pre-lithiation polyphenylene sulfide The conductivity.
  • the chloride ion complexing agent due to the pinning effect of the chloride ion complexing agent on the chloride ion, under the action of the electric field, only the lithium ion can undergo directional migration in the crystal structure of the pre-lithiated polyphenylene sulfide, while the chloride ion cannot move.
  • the pinning effect of the chloride ion complexing agent on the chloride ion can also prevent the chloride ion from participating in the electrochemical reaction, corroding the current collector, and causing the capacity of the battery to decrease.
  • the manufacturing equipment used in the prelithiation method is simple and convenient to operate, and the whole process does not pollute the environment.
  • the recovered NMP can be reused after purification, and the cleaning filtrate is an excess LiCl solution, which also has a high recovery value.
  • Two or more functional membranes are combined by hot pressing to form a lithium ion solid electrolyte membrane material, which can not only increase the strength, toughness and flatness of the membrane material, but also eliminate the voids, cracks, and uneven thickness of the membrane material to the greatest extent.
  • the functional defects of the membrane material especially to prevent the precipitation of metal dendrites on the surface of the battery caused by the uneven thickness of the membrane material during the cycle.
  • the invention can continuously roll-to-roll to produce micron-level organic membrane materials.
  • the manufacturing equipment used in the manufacturing method is simple and convenient to operate, a solvent-free drying process, low energy consumption, no secondary pollution during use, and convenient cleaning.
  • the method for preparing high-load battery pole pieces of the present invention has a large load of electrode active material, uniform and controllable thickness, high strength, good corrosion resistance, and high conductivity. , Can realize thick film load on various current collectors.
  • the purpose of the single-sided load and perforation of the current collector is to ensure a good penetration of the electrolyte.
  • the manufacturing equipment used in the manufacturing method is simple and convenient to operate, does not cause secondary pollution during use, and is convenient to clean. It is a true ion sieve cathode with easy processing, corrosion resistance, stable structure, long life, suitable raw material cost and strong practicability.
  • the volume of the active material load is greatly increased by 30% to 50%; the two current collectors are attached to the gap and the pores on the current collector are the infiltration channels of the electrolyte.
  • the solid electrolyte does not require infiltration compared with the traditional polymer diaphragm, the overall injection volume of the battery is greatly reduced, and there is no fluid electrolyte inside the battery; and the solid electrolyte It contains lithium, the content of toxic fluorine-containing lithium salt in the electrolyte is also greatly reduced, and the battery is more environmentally friendly; the high-temperature decomposition temperature of pre-lithiated polyphenylene sulfide membrane with high lithium solid solubility is much higher than that of traditional polymers The decomposition temperature of the diaphragm and the safety performance are further improved.
  • the single-piece “sandwich” structure composite sheet made by hot pressing, the battery pole piece and solid electrolyte are bonded into a whole, it has good flexibility, is not easy to move under repeated bending, and can be made Ultra-thin flexible quasi-solid battery used in wearable electronic devices.
  • Polyphenylene sulfide solid electrolyte itself has good flame-retardant properties and good thermal stability. It can not be decomposed at 400°C, the amount of electrolyte is greatly reduced, the combustibles inside the battery are also reduced, and the battery safety performance is improved. , It can be punctured without burning or exploding.
  • FIG. 1 is a process flow diagram of the manufacturing method of the quasi-solid-state lithium ion battery with high safety and high volume energy density according to the present invention.
  • Figure 2 is a schematic diagram of a perforated carbon-coated current collector.
  • Fig. 3 is a schematic diagram of a single-sided load electrode after the electrode film and the perforated carbon-coated current collector are thermally combined.
  • Figure 4 is a schematic diagram of the "sandwich" structure of the composite sheet.
  • Figure 5 is a schematic diagram of the battery stack and the electrolyte infiltration channel.
  • Fig. 6 is a schematic diagram of the structure of five "sandwich" structured composite sheet laminates.
  • Figure 7 shows the charge and discharge curves of LiNi 0.5 Co 0.2 Mn 0.3 O 2 /graphite quasi-solid battery at room temperature 25°C and different current densities.
  • Figure 8 is a cycle diagram of LiNi 0.5 Co 0.2 Mn 0.3 O 2 /graphite quasi-solid battery at room temperature 25°C and 1C.
  • Figure 9 shows the charging and discharging curves of LiCoO 2 /Li 4 Ti 5 O 12 quasi-solid battery at room temperature of 25°C and different current densities.
  • the quasi-solid lithium-ion battery of the present invention is composed of a "sandwich" structure composite sheet layer. According to the battery capacity design requirements, the number of sheets is determined and stacked together. Two adjacent perforated current collectors form Electrolyte penetration path.
  • the "sandwich" structure composite sheet layer is formed by a single-sided load positive electrode thick electrode, a solid electrolyte and a single-sided load negative electrode thick electrode through hot pressing.
  • the single-sided load positive electrode thick electrode adopts a manufacturing method that does not rely on solvents.
  • a variety of carbon materials, electrode active materials and PTFE are preheated in supersonic jet gas, PTFE is oriented drawing, and the molecular chain of PTFE is expanded and opened.
  • the solid electrolyte is pre-lithiated polyphenylene sulfide film material with high lithium solid solubility, high lithium solid solubility pre-lithiated polyphenylene sulfide powder and PTFE, and supersonic jet gas is used in the PTFE directional drawing equipment Jet-drawing, extruding and exhausting to form a cake, which is made into pre-lithiated polyphenylene sulfide film after one-time rolling and multi-layer film composite rolling.
  • PTFE is used as the polymer binder. Because PTFE powder has a high compression ratio, high molecular weight, and long chain segments, it can quickly unfold molecular chains and form a spatial network under supersonic air grinding to adhere and wrap the powder. , Is conducive to the uniform distribution and adhesion of the powder, and is more conducive to film formation.
  • the prepared pre-lithiated polyphenylene sulfide solid electrolyte membrane material has a high solid solubility of lithium, and the chloride ion in the membrane material is effectively bound, making it an excellent conductor of a single lithium ion; the prepared battery pole pieces are not Relying on solvents, large load capacity, large uniformity and controllable thickness; the manufactured quasi-solid lithium-ion battery has a simplified assembly process, has the characteristics of high safety, long life, high volume energy density, convenient electrolyte infiltration, easy to manufacture, large area and thin thickness Blade battery.
  • FIG. 1 The overall process flow of the manufacturing method of the quasi-solid-state lithium ion battery with high safety and high volume energy density according to the present invention is shown in FIG. 1, and will be described in detail below with reference to embodiments.
  • NMP N-methylpyrrolidone
  • lithium sulfide Li 2 S Li 2 S
  • lithium hydroxide LiOH in a ratio of 3:1:0.1 according to the amount of substances in an autoclave with stirring function, and raise the temperature to 200°C Dehydrate at high temperature for 4 hours to obtain a dehydration system;
  • the dehydration system is cooled to 100° C., and 1,4-dichlorobenzene (p-DCB) is added, and the amount ratio of the substance to Li 2 S is 1:1.
  • the reaction was carried out at 220°C for 130 minutes to obtain a mixed slurry.
  • the amount of HCl and LiOH are the same, just to neutralize LiOH, and use the method of evaporation or sublimation to remove NMP and H 2 O in the mixed slurry B, and the mixed slurry Of NMP and H 2 O to obtain a dry mixed powder.
  • the powder obtained after the above reaction is stirred and washed with deionized water for a certain period of time and then filtered.
  • the filter cake is washed and dried again to obtain a pre-lithiated polyphenylene sulfide with high lithium solid solubility as the final product.
  • the pre-lithiated polyphenylene sulfide powder and PTFE powder are mixed according to the weight percentage of 94%: 6%, and the PTFE in the mixture is preheated and dried by compressed air at 50°C with an air flow rate of supersonic speed in the PTFE directional drawing equipment. Spray wire drawing to form a spatial network of loose micelles and collect them.
  • the powder is made into a continuous cake-like broadband through an extruder, and then a film is pressed by a hot roll press for multiple composite rolls.
  • the final thickness of the film is 35 ⁇ m, and the lithium ion conductivity of the prepared film is 7*10 -4 S ⁇ cm -1 .
  • a V-type mixer In a low-temperature cold storage at 5°C, use a V-type mixer to mix the PTFE granular powder and the above-mentioned mixed powder A at a weight percentage of 6%:94%, and mix for 2 hours until uniform to obtain powder B; use air flow rate
  • the PTFE in powder B is sprayed and drawn by preheated dry compressed air at a supersonic speed of 50°C in a PTFE directional drawing equipment to form a spatial network of loose micelles, which are collected to obtain mixed powder C and ground mixed powder C It is discharged and collected with the air flow; the mixed powder C is rolled by a hot roller press twice to form a film, and the hot pressing temperature is 180°C.
  • the thickness of the positive electrode film is about 500 micrometers, and the thickness of the negative electrode film is about 300 micrometers; after the second rolling, the thickness of the positive electrode film is about 250 micrometers, and the thickness of the negative electrode film is about 120 micrometers.
  • the positive electrode LiNi 0.5 Co 0.2 Mn 0.3 O 2 film and the negative electrode graphite film were thermally composited on the perforated carbon-coated aluminum foil or perforated carbon-coated copper foil through a hot-pressing composite roll at a temperature of 160°C, respectively, to form a single-sided loaded LiNi 0.5 Co 0.2 Mn 0.3 O 2 positive electrode thick electrode, single-sided graphite negative electrode thick electrode.
  • the single-sided thick LiNi 0.5 Co 0.2 Mn 0.3 O 2 positive electrode was used as the positive pole piece, and the single-sided graphite negative thick electrode was used as the negative pole piece.
  • the positive pole piece and pre-lithiated polyphenylene sulfide with high lithium solid solubility were used as the positive pole piece.
  • the membrane material and the negative pole piece are stacked in sequence, and the unloaded side of the positive pole piece and the negative pole piece are facing outwards; the hot-pressing compound is performed at 100°C to form a "sandwich" structure composite sheet layer, as shown in Figure 4. Show.
  • NMP N-methylpyrrolidone
  • Li 2 S lithium sulfide Li 2 S
  • lithium hydroxide Li(OH) Li(OH)
  • NMP N-methylpyrrolidone
  • p-DCB 1,4-dichlorobenzene
  • the amount of HCl and LiOH are the same, just to neutralize LiOH, and use evaporation or sublimation to remove NMP and H 2 O in the mixed slurry. NMP and H 2 O to obtain dry mixed powder.
  • cup imidazole the amount of which is 0.05 of p-DCB, stir it evenly, and place it in a closed reaction kettle and keep it at 210°C for 160 minutes to obtain a powder.
  • the powder obtained after the above reaction is stirred and washed with deionized water for a certain period of time and then filtered. The filter cake is washed and dried again to obtain a pre-lithiated polyphenylene sulfide with high lithium solid solubility as the final product.
  • the pre-lithiated polyphenylene sulfide powder and PTFE powder are mixed at a weight percentage of 94%: 6%, and the mixture is preheated and dried by compressed air at 50°C with an air flow rate of supersonic speed in the PTFE directional drawing equipment.
  • PTFE is sprayed and drawn to form a spatial network of loose micelles and collected.
  • the powder is made into a continuous cake-like broadband through an extruder, and then a film is pressed by a hot roller pressing machine several times with a composite roller.
  • the final thickness of the film is 52 ⁇ m, and the lithium ion conductivity of the prepared film is 1*10 -3 S ⁇ cm -1 .
  • LiCoO 2 is used as the positive electrode active material
  • Li 4 Ti 5 O 12 is used as the negative electrode active material, respectively, with artificial graphite, activated carbon, and acetylene black according to the weight percentage of 89%: 6%: 4%: 1%.
  • the thickness of the positive electrode film is about 450 micrometers, and the thickness of the negative electrode film is about 550 micrometers; after the second rolling, the thickness of the positive electrode film is about 220 micrometers, and the thickness of the negative electrode film is about 300 micrometers.
  • the aluminum foil is used as the current collector, after being coated with carbon and punched, as shown in Figure 2.
  • the positive electrode LiCoO 2 film or the negative electrode Li 4 Ti 5 O 12 film is thermally composited on the single side of the perforated carbon-coated aluminum foil through a hot pressing composite roll at a temperature of 160°C, as shown in Figure 3, to form a single-sided loaded LiCoO 2 positive electrode thickness Electrode, single-sided load Li 4 Ti 5 O 12 negative electrode thick electrode.
  • the single-sided LiCoO 2 thick positive electrode was used as the positive pole piece, and the single-sided Li 4 Ti 5 O 12 thick negative electrode was used as the negative pole piece.
  • the positive pole piece and the pre-lithiated polyphenylene sulfide film with high lithium solid solubility were used as the negative pole piece.
  • the material and the negative pole piece are stacked in sequence, and the unloaded side of the positive pole piece and the negative pole piece are facing outwards; the hot-pressing compound is performed at 100°C to form a "sandwich" structure composite sheet layer, as shown in Figure 4. .
  • NMP N-methylpyrrolidone
  • Li 2 S lithium sulfide Li 2 S
  • lithium hydroxide Li(OH) Li(OH)
  • NMP N-methylpyrrolidone
  • p-DCB 1,4-dichlorobenzene
  • the amount of HCl and LiOH are the same, just to neutralize LiOH, and use evaporation or sublimation to remove NMP and H 2 O in the mixed slurry. NMP and H 2 O to obtain dry mixed powder.
  • the mixed powder add cup pyrrole, the amount of which is 0.2 of p-DCB, stir it evenly, and place it in a closed reaction kettle and keep it at 210°C for 160 minutes to obtain a powder.
  • the powder obtained after the above reaction is stirred and washed with deionized water for a certain period of time and then filtered. The filter cake is washed and dried again to obtain a pre-lithiated polyphenylene sulfide with high lithium solid solubility as the final product.
  • the pre-lithiated polyphenylene sulfide powder and PTFE powder are mixed at a weight percentage of 94%: 6%, and the mixture is preheated and dried by compressed air at 50°C with an air flow rate of supersonic speed in the PTFE directional drawing equipment.
  • PTFE is sprayed and drawn to form a spatial network of loose micelles and collected.
  • the powder is made into a continuous cake-like broadband through an extruder, and then the film is pressed by a hot roller press for multiple composite rolls.
  • the final thickness of the film is 37 ⁇ m, and the lithium ion conductivity of the prepared film is 8.2*10 -4 S ⁇ cm -1 .
  • LiNi 1.5 Mn 0.5 O 4 was used as the positive electrode active material, and Li 4 Ti 5 O 12 was used as the negative electrode active material, respectively with artificial graphite, activated carbon, and acetylene black at a weight percentage of 89%: 6%: 4%: 1%.
  • VC type high-efficiency asymmetric mixer mixes evenly to obtain powder.
  • the thickness of the positive electrode film is about 500 micrometers, and the thickness of the negative electrode film is about 500 micrometers; after the second rolling, the thickness of the positive electrode film is about 280 micrometers, and the thickness of the negative electrode film is about 280 micrometers.
  • the positive electrode graphite film was thermally composited on one side of the perforated carbon-coated aluminum foil, and the thermal composite rolling temperature was 160°C.
  • LiNi1.5Mn0.5O4 positive electrode single-sided pole piece, Li4Ti5O12 negative electrode and high lithium solid solubility pre-lithiated polyphenylene sulfide film material are stacked together, and the load surface of the positive and negative electrodes are coated. The material is separated, the unloaded side of the current collector is facing outwards, and it is hot-pressed and composited at 110°C to form a "sandwich" structure composite sheet, as shown in Figure 4.

Abstract

提供一种预锂化聚苯硫醚、聚苯硫醚固态电解质膜、电池极片、准固态锂离子电池及其制造方法，包括采用不依赖溶剂的方法制备各向同性的聚苯硫醚固态电解质，制造高负载电池极片和组装准固态锂离子电池三个步骤。活性物质负载的体积占比提高到30％～50％；聚苯硫醚固态电解质本身具有很好的阻燃特性和良好的热稳定性，减少了电解液注液量，电解液用量大幅减少，也减少了电池内部可燃物，提高的电池安全性能。固态电解质含锂，电解液中的有毒的含氟锂盐含量也大幅减少。经过热压后电池极片和固态电解质粘合为一个整体，在反复弯折下不易错动，可作为超薄柔性准固态电池，用于可穿戴电子设备中。

Description

预锂化聚苯硫醚、聚苯硫醚固态电解质膜、电池极片、准固态锂离子电池及其制造方法 技术领域
本发明涉及一种预锂化聚苯硫醚、聚苯硫醚固态电解质膜、电池极片、高安全性高体积能量密度准固态锂离子电池及其制造方法，属于新能源材料和器件制造技术领域。
背景技术
首先，固态锂离子电池以其卓越的安全性能和潜在的高能量密度，越来越受到工业界和学术界的关注。然而，固态锂离子的电池的功率密度很低，极大限制了其商业推广和应用。迫切需要突破的关键问题就是开发新型的具有高电导率和优良加工性能的固态电解质材料。当前无机陶瓷/玻璃电解质，如Li 5La 3Zr 2O 12、Li 3xLa 2/3-xTiO 3，和硫化物电解质因其锂离子电导率可达10 -4～10 -2S cm -1，受到了广泛的关注，但是该类材料机械加工性能差、成膜困难，特别是硫化物电解质加工环境要求极为苛刻，工程化和商业化还需要很长的路要走。另外一种是有机电解质，如PEO、PVDF等，容易加工成膜，可以卷对卷的进行加工生产，但该类的有机电解质的电导率较低，只有10 -8～10 -5S cm -1，室温下无法正常应用，同样限制了该类材料的进一步大规模推广。
其次，当前传统的极片制造工艺采用了含有溶剂的湿法涂布工艺，该方法存在孔隙率高、电导率低、负载量低的先天性缺陷，无法实现厚极片的制造。限制了锂电池能量密度的进一步提高。
再次，当前叠片式锂电池制造过程中，为了实现高体积利用率，采用了薄片设计，极片面积增大，厚度减薄，但由于采用了传统的不含预制锂盐的隔膜，使得电解液的浸润过程困难，容易造成电解液和锂盐分布不均，对电池性能造成影响。
发明内容
为克服现有技术的缺陷，本发明提供一种预锂化聚苯硫醚、聚苯硫醚固态电解质膜、电池极片、高安全性长寿命的高体积能量密度准固态锂离子电池及其制造方法，该方法所制备的预锂化聚苯硫醚固态电解质膜材中锂的固溶度高，且膜材中的氯离子被有效束缚，使其成为单一锂离子的优良导体；所制备的电池极片不依赖溶剂、负载量大、厚度均一可控；所制造的准固态锂离子电池装配工艺简化，具有高安全性长寿命高体积能量密度的特点，电解液浸润便利，易制造面积大，厚度薄的刀片式电池。
一种高锂固溶度的预锂化聚苯硫醚的制造方法，其特征在于，包括以下步骤：
将N-甲基吡咯酮(NMP)、硫化锂Li 2S、氢氧化锂LiOH置于有搅拌功能的高压反应釜中，并升温到150-250℃高温脱水2-5h后，降温至100℃，加入1,4-二氯苯(p-DCB)，在150-250℃下反应80-200分钟；滴加与LiOH的物质的量相同的盐酸，中和LiOH，并采用蒸发或升华的办法除去NMP和H 2O，得到干燥混合粉料；在混合粉料中，加入氯离子络合剂，搅拌均匀，并置于密闭反应釜中，在150-250℃下反应80-200分钟，再经洗涤、干燥，得到高锂固溶度的预锂化聚苯硫醚。
进一步地，所述的Li 2S为金属锂粉和硫粉高温反应生成或硫酸锂(Li 2SO 4)碳热还原反应生成。
进一步地，所述的NMP、硫化锂Li 2S、氢氧化锂LiOH的摩尔配比为1-5：1：0.05-0.2。
进一步地，所述Li 2S与p-DCB的摩尔配比为1.3-0.8：1。
进一步地，所述蒸发或升华的办法为热风烘干法、旋转蒸发法、冷冻干燥法，最大限度保留固相成分，仅去除NMP和H 2O。
进一步地，所述的氯离子络合剂为有机无金属离子络合剂，优选为杯芳冠醚、杯咪唑、杯吡咯、杯芳烃。
进一步地，所述的氯离子络合剂添加的物质的量为p-DCB的0.01-0.2倍。
进一步地，步骤1)中所制备的聚苯硫醚固态电解质中，预锂化聚苯硫醚粉料所占的重量百分比为80％-97％。
所述高锂固溶度的预锂化聚苯硫醚制备方法制备的预锂化聚苯硫醚。
各向同性的聚苯硫醚固态电解质膜的制备方法，其特征在于，将预锂化聚苯硫醚粉料与聚四氟乙烯(PTFE)于聚四氟乙烯呈玻璃态的温度条件下在混合机中混合均匀，使用超音速气体进行空气研磨，使得PTFE的分子链延展打开，并与预锂化聚苯硫醚粉料之间形成物理粘连，且不发生化学反应；再经过挤出机排除粉体中的气体制成连续饼状宽带，然后将连续饼状宽带采用温度低于150℃的热辊压制成预锂化聚苯硫醚膜材，并收卷；制备成聚苯硫醚固态电解质膜。
进一步地，所述预锂化聚苯硫醚粉料为权利要求9所述的预锂化聚苯硫醚；所述空气研磨是首先将粉料预热到40-50℃，在PTFE定向拉丝设备中采用超音速射流气体对PTFE喷射拉丝。
进一步地，所述的PTFE定向拉丝，为粉料中的PTFE在经超音速射流气体预热后形成粘流态，PTFE粘流体在加压条件下，通过细小喷嘴构成超音速射流流体喷出，通过文丘里管结构吸入混合粉料，在蜗壳型腔中进行收集，收集的物料成为空间网状疏松团聚体。
进一步地，预锂化聚苯硫醚粉料和PTFE在混料机中混合均匀的过程中温度控制在10℃以 下；混料机中混料时间为0.5-4小时。
进一步地，预锂化聚苯硫醚压膜膜材热压后还包括以下处理过程：
将两张或多张预锂化聚苯硫醚一次压膜膜材经过热压复合成无缺陷高致密固态电解质膜；或者：
采用两个加热的氟橡胶模块将预锂化聚苯硫醚膜材在150-230℃下热压1-10s，使得预锂化聚苯硫醚一次压膜膜材的微裂纹、孔洞愈合，制成无缺陷高致密固态电解质膜。
所述聚苯硫醚固态电解质膜的制备方法制备的聚苯硫醚固态电解质膜。
高负载电池极片的制备方法，其特征在于，将导电碳材料分别与锂离子电池正极材料、负极材料，在混料机中混合均匀；再分别与PTFE粉体在PTFE呈玻璃态的温度条件下混合均匀，使用超音速射流气体使PTFE的分子链延展打开，分别同导电碳材料与锂离子电池正极、负极材料的混合粉体形成物理粘连，且不发生化学反应；在高温热压下制成膜材D，再采用热压复合工艺将膜材D与经过打孔的集流体的单面热复合，制成单面负载正极厚电极、单面负载负极厚电极。
进一步地，锂离子电池正极材料或负极材料与碳材料的重量百分比为50％-95％：50％-5％。
进一步地，PTFE粉体与导电碳材料、锂离子电池正极或负极材料的混合粉料的重量百分比为3％-15％：85％-97％。
进一步地，热压温度为150-250℃。
进一步地，将膜材D与集流体热复合时的辊压温度为120-220℃，集流体和一张膜材D经同速放卷，进入两个相对转动的热辊压机，通过调节辊缝宽度，控制压力，使得膜材D刚好能够复合在集流体上即可，避免因辊压力过大导致膜材形变过大，拉断集流体。
进一步地，所述使用超音速射流气体使PTFE的分子链延展打开是首先将粉料预热到40-50℃，在PTFE定向拉丝设备中使用超音速射流气体喷射拉丝，所述的PTFE定向拉丝，为粉料中的PTFE在经超音速射流气体预热后形成粘流态，PTFE粘流体在加压条件下，通过细小喷嘴构成超音速射流流体喷出，通过文丘里管结构吸入混合粉料，在蜗壳型腔中进行收集，收集的物料成为空间网状疏松团聚体。
进一步地，所述导电碳材料为super-P、乙炔黑、活性碳、人造石墨、高纯石墨中的一种或几种的混合物；所述的集流体为涂碳保护并打孔的不锈钢箔、铝箔或铜箔。
一种高安全性高体积能量密度准固态锂离子电池的制造方法，其特征在于，包括以下步骤：
利用权利要求15制备的聚苯硫醚固态电解质膜作为电解质，权利要求16-22任一项所述制备方法制备的单面负载正极厚电极、单面负载负极厚电极分别作为正极极片、负极极片， 组装准固态锂离子电池，将正极极片、聚苯硫醚固态电解质和负极极片依次叠在一起，且正极极片、负极极片的集流体未负载的一面向外；在80～150℃进行热压复合，形成“三明治”结构的复合片层，采用包装膜将复合片层封装后，真空注液，热封入壳。
进一步地，在封装之前，将多个复合片层采用叠片机叠在一起，正极集流体与正极集流体相贴合，负极集流体与负极集流体相贴合，极耳部分进行焊接，再采用包装膜将复合片层封装。
进一步地，所述的包装膜是绝缘的柔性封装膜，优选为铝塑膜、聚酰亚胺膜、塑料膜。
所述高安全性高体积能量密度准固态锂离子电池的制造方法制备的高安全性高体积能量密度准固态锂离子电池。
与现有技术相比，本发明的有益效果：
(1)采用聚苯硫醚作为固态电解质的载体，热稳定性好，不易燃烧，安全性高，寿命长。
(2)消除了固态电解质中锂离子传输性能的各向异性
传统的预锂化聚苯硫醚固态电解质是采用流涎成型的方式制备，在流涎成型的再结晶过程中，存在晶体取向，会造成锂离子传输性能的各向异性，其水平膜方向的锂离子电导率比垂直膜方向的电导率大1到2个数量级。
本发明通过将预锂化聚苯硫醚粉料与PTFE混合后在PTFE定向拉丝设备中进行物料造团，PTFE经射流气体预热后形成粘流态，PTFE粘流体在加压条件下，通过细小喷嘴构成超音速射流流体喷出，通过文丘里管结构吸入电极材料粉体，在PTFE纤维簇中进行填充，在蜗壳型腔中进行收集，收集的物料成为空间网状疏松团聚体。长链的PTFE的分子链延展打开，功能化有机粉体物理粘连在PTFE分子链上；在经过挤出机排出粉体中的气体制成连续饼状宽带，饼状宽带在有机粉体物化性质改变温度以下(<150℃)经过热压制成膜。PTFE高压缩比，且分子量高，链段长；在制备的过程中，预锂化聚苯硫醚粉料与PTFE在空气研磨是充分粘附到PTFE的分子链上，实现均匀混合。再经挤出机制成连续饼状宽带的过程中PTFE分子链之间黏连将功能化粉体包裹起来。同时经过首先预制成连续饼状宽带，能够有效排除空气研磨后疏松粉体中的空气，有利于连续均匀膜的形成。该制造过程不采用高温，加工温度始终在有机粉体物化性质改变温度以下，制造过程不采用溶剂等助剂，避免了粉料溶解造成的功能破坏。膜材制造过程不会出现功能化粉体的重结晶，不会出现各向异性，并且容易制造致密的膜材，特别对于有机的固态电解质膜，可以确保膜材在各个方向上均具有优异的离子电导特性。整个过程均为物理过程，预锂化聚苯硫醚粉料不会发生化学反应，其物理化学性质不发生改变，因此所制备的功能膜材料具有理想的催化、金属离子交换或质子交换的性能。
即：本发明中的预锂化聚苯硫醚固态电解质采用采用低温无损伤制造方法，膜材的锂离 子电导率不产生各向异性。因此，本发明尤其适用于预锂化聚苯硫醚粉料不宜通过注塑或流涎等方法成膜，或高温或溶剂的影响会损坏有机粉体的功能，或在制膜中产生各向异性影响到膜材性能的膜材料的制备。
3)聚苯硫醚的预锂化过程中，实现了锂离子与聚苯硫醚纳米级的均匀混合，提高了锂离子迁移通道、锂的固溶度，提高了预锂化聚苯硫醚的电导率。
聚苯硫醚的预锂化中，首先加入LiOH，其目的是为了体系更好的脱水，Li 2S与p-DCB的反应是亲核取代反应，非质子极性有利于反应的发生，但是H 2O可以与Li 2S发生溶剂化效应，从而减弱其亲核作用，降低了单体反应活性，更好的脱水能够提高聚苯硫醚的线性结晶区的产率，而足够高比率的线性区可以确保结构中存在大量的锂离子快速迁移通道。然后，将溶剂和水直接蒸发或升华，一步实现生成物到反应物的转换，并原位实现聚苯硫醚和锂盐的纳米级混合，促进了后续的高温固溶反应充分。高结晶度的聚苯硫醚硬度高强度大，很难破碎，很难制备纳米级聚苯硫醚粉料，简单将聚苯硫醚粗粉和锂盐混合加热，会造成反应不均，锂固溶度低，电导率低。再次，加入的氯离子络合剂可以有效分离锂离子和氯离子，促进聚苯硫醚链上的硫位对锂离子的俘获，提高锂的固溶度，从而提高预锂化聚苯硫醚的电导率。同时，由于氯离子络合剂对氯离子的钉扎作用，使得预锂化聚苯硫醚在电场的作用下，仅有锂离子可以在其晶结构中发生定向迁移，而氯离子无法移动，使其成为单一锂离子的优良导体，进一步提高了预锂化聚苯硫醚的锂离子电导率。氯离子络合剂对氯离子的钉扎作用还可以防止氯离子参与到电化学反应中，腐蚀集流体，造成电池的容量衰减。
同时，该预锂化方法使用的制造设备操作简单方便，全过程对环境无污染，回收的NMP经过纯化可以重复利用，清洗滤液为过量的LiCl溶液，同样具有较高的回收价值。
4)两层或多层功能膜经热压复合形成锂离子固态电解质膜材，不仅能增加膜材的强度、韧性、平整度，并最大限度消除膜材的空隙、裂纹、厚度不均一等损害膜材功能的缺陷，尤其防止因膜材厚度不均造成的电池在循环过程中表面金属枝晶析出。本发明可连续的卷对卷制得微米级的有机膜材。同时，所述制造方法使用的制造设备操作简单方便，无溶剂干燥过程，能耗低，且使用过程中不会造成二次污染，清理方便。
5)高负载电池极片制造不依赖溶剂，具有优良的实用性.
与目前使用的湿法涂布极片相比，本发明中农用于制备高负载电池极片的方法，电极活性物质负载量大、厚度均一可控、强度大、耐蚀性好、电导率高，能在各式各样的集流体上实现厚膜负载。集流体单面负载并打孔其目的是确保电解液有很好的渗透。同时，所述制造方法使用的制造设备简单操作方便，且使用过程中不会造成二次污染，清洗方便。是真正意义上的易加工、耐腐蚀、结构稳定、长寿命、原材料费用适宜且实用性强的离子筛阴极。
6)本发明中准固态锂离子电池的制造过程中，活性物质负载的体积占比大幅提高30％到50％；两集流体贴合缝隙和集流体上的孔道为电解液的浸润通道，可以更好的实现厚电极负载的电解液润湿；由于固态电解质同传统的聚合物隔膜相比，不需要浸润，大幅减少了电池的整体注液量，电池内部无流动性电解液；且固态电解质本身含锂，电解液中的有毒的含氟锂盐含量也大幅减少，电池更加环境友好；高锂固溶度的预锂化聚苯硫醚膜材的高温分解温度远远高于传统聚合物隔膜的分解温度，安全性能进一步提高。
7)经过热压后制成的单片“三明治”结构复合片层，其电池极片和固态电解质粘合成为一个整体，具有很好的柔性，在反复弯折下不易错动，可以做成超薄柔性准固态电池，用于可穿戴电子设备中。
8)聚苯硫醚固态电解质本身具有很好的阻燃特性和良好的热稳定性，可以做到400℃不分解，电解液用量大幅减少，也减少了电池内部可燃物，提高的电池安全性能，可以做到穿刺不燃烧、不爆炸。
附图说明
图1为本发明所述高安全性高体积能量密度准固态锂离子电池的制造方法的工艺流程图。
图2为打孔涂碳集流体的示意图。
图3为电极膜和打孔涂碳集流体热复合后的单面负载电极示意图。
图4为“三明治”结构复合片层的结构示意图。
图5为电池叠片和电解液浸润通道示意图。
图6为5个“三明治”结构复合片层叠片的结构示意图。
图7为LiNi 0.5Co 0.2Mn 0.3O 2/石墨准固态电池在室温25℃，不同电流密度下的充放电曲线。
图8为LiNi 0.5Co 0.2Mn 0.3O 2/石墨准固态电池在室温25℃，1C下的循环图。
图9为LiCoO 2/Li 4Ti 5O 12准固态电池在室温25℃，不同电流密度下的充放电曲线。
图中：
1-打孔涂炭层，2-打孔集流体，3-厚电极膜，301-正极厚电极膜，302-负极厚电极膜，4-预锂化聚苯硫醚固态电解质，5-电解质浸润通道。
具体实施方式
为使本发明的技术方案更加清楚，下面将对本发明的技术方案进行清楚、完整地描述，显然，所描述的实施例是本发明一部分实施例，而不是全部的实施例。
本发明所述的准固态锂离子电池是由“三明治”结构复合片层组成，根据电池容量设计 需求，确定片层数量，并叠片在一起的，两个相贴的打孔集流体形成了电解液渗透路径。所述的“三明治”结构复合片层是由单面负载正极厚电极，固态电解质和单面负载负极厚电极经过热压后形成的。所述的单面负载正极厚电极，采用了不依赖溶剂的制造方法，多种碳材料、电极活性物质和PTFE在超音速射流气体预热，PTFE定向拉丝，PTFE的分子链延展打开，再经多步辊压成膜，最后同打孔涂碳集流体热压复合。所述的固态电解质为高锂固溶度的预锂化聚苯硫醚膜材，高锂固溶度预锂化聚苯硫醚粉料和PTFE，在PTFE定向拉丝设备中使用超音速射流气体喷射拉丝，挤压排气成饼，经一次辊压和多层膜复合辊压后制成预锂化聚苯硫醚膜材。
选用PTFE作为聚合物粘接剂，由于PTFE粉料具有高压缩比，且分子量高，链段长，能在超音速空气研磨下，分子链迅速展开并形成空间网络状，将粉体粘附包裹，有利于粉体的均匀分布与粘附，更有利于成膜。
准固态锂离子电池的制造过程中的所有成膜步骤不依赖溶剂，极大简化了电池的制造工艺，并使得该工艺更加环境友好。所制备的预锂化聚苯硫醚固态电解质膜材中锂的固溶度高，且膜材中的氯离子被有效束缚，使其成为单一锂离子的优良导体；所制备的电池极片不依赖溶剂、负载量大、厚度大均一可控；所制造的准固态锂离子电池装配工艺简化，具有高安全性长寿命高体积能量密度的特点，电解液浸润便利，易制造面积大，厚度薄的刀片式电池。
本发明所述的高安全性高体积能量密度准固态锂离子电池的制造方法的整体工艺流程如图1所示，下面结合实施例具体说明。
实施例1：
(1)制备高锂固溶度的预锂化聚苯硫醚膜材：
将N-甲基吡咯酮(NMP)、硫化锂Li 2S、氢氧化锂LiOH，按照物质的量比为3：1：0.1，置于有搅拌功能的高压反应釜中，并升温到200℃高温脱水4小时，得到脱水体系；其次，将脱水体系降温至100℃，加入1,4-二氯苯(p-DCB)，同Li 2S的物质的量比为1：1。在220℃下反应130分钟，得到混合浆料。再次，在混合浆料中滴加定量盐酸，HCl与LiOH的物质的量相同，恰好中和LiOH，并采用蒸发或升华的办法除去混合浆料B中的NMP和H 2O，混合浆料中的NMP和H 2O,得到干燥混合粉料。在混合粉料中，加入杯芳冠醚，其物质的量为p-DCB的0.17，搅拌均匀，并置于密闭反应釜中，在210℃下保温160分钟，得到粉料。最后，将上述反应结束得到的粉料，用去离子水搅拌洗涤一定时间后过滤，滤饼再次洗涤、干燥，得到最终产物为高锂固溶度的预锂化聚苯硫醚。预锂化的聚苯硫醚粉体和PTFE粉料按照94％：6％的重量百分比混合，采用空气流速达到超音速的50℃预热干燥压缩空气在PTFE定向拉丝设备中将混合物中的PTFE喷射拉丝，形成空间网状疏松胶团，并收集。粉料经挤 出机制成连续饼状宽带，然后经热辊压机多次复合辊压制膜，膜材最终厚度为35μm，所制得的膜材的锂离子电导率均为7*10 -4S·cm -1。
(2)不依赖溶剂的方法制备高负载电池极片：
将LiNi 0.5Co 0.2Mn 0.3O 2作为正极活性材料，石墨作为负极活性材料，分别与人造石墨、活性碳、乙炔黑按照86％：7％：5％：2％的重量百分比，在VC型高效不对称混合机混合均匀得到粉料A。在5℃的低温冷库中，使用V型混合机将聚四氟乙烯颗粒粉体、上述混合粉料A按照6％：94％的重量百分比，混合2小时至均匀得到粉料B；采用空气流速达到超音速的50℃预热干燥压缩空气在PTFE定向拉丝设备中将粉料B中的PTFE喷射拉丝，形成空间网状疏松胶团，并收集，制得混粉C，研磨后的混粉C随气流排出并收集；混粉C经热辊压机辊压两次成膜，热压温度为180℃。经第一次辊压后，正极膜的厚度为500微米左右，负极膜的厚度为300微米左右；第二次辊压后正极膜的厚度为250微米左右，负极膜的厚度为120微米左右。将正极LiNi 0.5Co 0.2Mn 0.3O 2膜、负极石墨膜分别通过温度为160℃热压复合辊热复合在打孔涂碳铝箔或打孔涂碳铜箔的一面，分别制成单面负载LiNi 0.5Co 0.2Mn 0.3O 2正极厚电极、单面负载石墨负极厚电极。上述打孔涂碳铝箔或者打孔涂碳铜箔的结构如图2所示，制成的单面负载LiNi 0.5Co 0.2Mn 0.3O 2正极厚电极、单面负载石墨负极厚电极的结构如图3所示。
(3)组装准固态锂离子电池：
将单面负载LiNi 0.5Co 0.2Mn 0.3O 2正极厚电极作为正极极片，单面负载石墨负极厚电极作为负极极片，将正极极片、高锂固溶度的预锂化聚苯硫醚膜材、负极极片依次叠在一起，且正极极片、负极极片的集流体未负载的一面向外；在100℃进行热压复合，形成“三明治”结构复合片层，如图4所示。再将5个“三明治”结构复合片层采用叠片机叠在一起，如图5、图6所示，正极铝集流体与正极铝集流体相贴合，负极铜集流体与负极铜集流体相贴合。集流体上的孔道与两个集流体之间的缝隙形成电解液浸润通道5。极耳部分进行焊接，铝塑膜封装后，真空注碳酸酯类电解液，热封入壳。该准固态电池在室温25℃，不同电流密度下的充放电曲线如图7所示，该准固态电池1C下的循环性能如图8所示，500圈容量不衰减。针刺实验不发生起火爆炸。
实施例2：
(1)制备高锂固溶度的预锂化聚苯硫醚膜材：
将N-甲基吡咯酮(NMP)、硫化锂Li 2S、氢氧化锂Li(OH)，按照物质的量比为4：1：0.15，置于有搅拌功能的高压反应釜中，并升温到200℃高温脱水4小时，得到脱水体系；其次，将脱水体系降温至100℃，加入1,4-二氯苯(p-DCB)，同Li 2S的物质的量比为1：1.2。在220℃ 下反应130分钟，得到混合浆料。再次，在混合浆料中滴加定量盐酸，HCl与LiOH的物质的量相同，恰好中和LiOH，并采用蒸发或升华的办法除去混合浆料中的NMP和H 2O，混合浆料中的NMP和H 2O,得到干燥混合粉料。在混合粉料中，加入杯咪唑，其物质的量为p-DCB的0.05，搅拌均匀，并置于密闭反应釜中，在210℃下保温160分钟，得到粉料。最后，将上述反应结束得到的粉料，用去离子水搅拌洗涤一定时间后过滤，滤饼再次洗涤、干燥，得到最终产物为高锂固溶度的预锂化聚苯硫醚。将预锂化的聚苯硫醚粉体和PTFE粉料按照94％：6％的重量百分比混合，采用空气流速达到超音速的50℃预热干燥压缩空气在PTFE定向拉丝设备中将混合物中的PTFE喷射拉丝，形成空间网状疏松胶团，并收集。粉料经挤出机制成连续饼状宽带，然后经热辊压机多次复合辊压制膜，膜材最终厚度为52μm，所制得的膜材的锂离子电导率均为1*10 -3S·cm -1。
(2)不依赖溶剂的方法制备高负载电池极片：
将LiCoO 2作为正极活性材料，Li 4Ti 5O 12作为负极活性材料，分别与人造石墨、活性碳、乙炔黑按照89％：6％：4％：1％的重量百分比，在VC型高效不对称混合机混合均匀得到粉料A。在5℃的低温冷库中，使用V型混合机将聚四氟乙烯颗粒粉体、上述混合粉料A按照6％：94％的重量百分比，混合2小时至均匀得到粉料B；采用空气流速达到超音速的50℃预热干燥压缩空气在PTFE定向拉丝设备中将粉料B中的PTFE喷射拉丝，形成空间网状疏松胶团，并收集，制得混粉C；混粉C经热辊压机辊压两次成膜，热压温度为180℃。经第一次辊压后，正极膜的厚度为450微米左右，负极膜的厚度为550微米左右；第二次辊压后正极膜的厚度为220微米左右，负极膜的厚度为300微米左右。以铝箔为集流体，经过涂炭、打孔后，如图2所示。将正极LiCoO 2膜或负极Li 4Ti 5O 12膜分别通过温度为160℃热压复合辊热复合在打孔涂碳铝箔的单面，如图3所示，形成单面负载LiCoO 2正极厚电极、单面负载Li 4Ti 5O 12负极厚电极。
(3)组装准固态锂离子电池：
将单面负载LiCoO 2正极厚电极作为正极极片，单面负载Li 4Ti 5O 12负极厚电极作为负极极片，将正极极片、高锂固溶度的预锂化聚苯硫醚膜材、负极极片依次叠在一起，且正极极片、负极极片的集流体未负载的一面向外；在100℃进行热压复合，形成“三明治”结构复合片层，如图4所示。再将10个“三明治”结构复合片层采用叠片机叠在一起，正极铝集流体与正极铝集流体相贴合，负极铜集流体与负极铜集流体相贴合，如图5、图6所示。极耳部分进行焊接，铝塑膜封装后，真空注碳酸酯类电解液，热封入壳。该准固态电池在室温25℃，不同电流密度下的充放电曲线如图9所示。1C容量保持率高达90％。具有优秀的倍率性能。
实施例3：
(1)制备高锂固溶度的预锂化聚苯硫醚膜材：
将N-甲基吡咯酮(NMP)、硫化锂Li 2S、氢氧化锂Li(OH)，按照物质的量比为5：1：0.18，置于有搅拌功能的高压反应釜中，并升温到200℃高温脱水4小时，得到脱水体系；其次，将脱水体系降温至100℃，加入1,4-二氯苯(p-DCB)，同Li 2S的物质的量比为1：0.9。在220℃下反应130分钟，得到混合浆料。再次，在混合浆料中滴加定量盐酸，HCl与LiOH的物质的量相同，恰好中和LiOH，并采用蒸发或升华的办法除去混合浆料中的NMP和H 2O，混合浆料中的NMP和H 2O,得到干燥混合粉料。在混合粉料中，加入杯吡咯，其物质的量为p-DCB的0.2，搅拌均匀，并置于密闭反应釜中，在210℃下保温160分钟，得到粉料。最后，将上述反应结束得到的粉料，用去离子水搅拌洗涤一定时间后过滤，滤饼再次洗涤、干燥，得到最终产物为高锂固溶度的预锂化聚苯硫醚。将预锂化的聚苯硫醚粉体和PTFE粉料按照94％：6％的重量百分比混合，采用空气流速达到超音速的50℃预热干燥压缩空气在PTFE定向拉丝设备中将混合物中的PTFE喷射拉丝，形成空间网状疏松胶团，并收集。粉料经挤出机制成连续饼状宽带，然后经热辊压机多次复合辊压制膜，膜材最终厚度为37μm，所制得的膜材的锂离子电导率均为8.2*10 -4S·cm -1。
(2)不依赖溶剂的方法制备高负载电池极片：
将LiNi 1.5Mn 0.5O 4作为正极活性材料，Li 4Ti 5O 12作为负极活性材料，分别与人造石墨、活性碳、乙炔黑按照89％：6％：4％：1％的重量百分比，在VC型高效不对称混合机混合均匀得到粉料。在5℃的低温冷库中，使用V型混合机将聚四氟乙烯颗粒粉体、上述混合粉料A按照6％：94％的重量百分比，混合2小时至均匀得到粉料B；采用空气流速达到超音速的50℃预热干燥压缩空气在PTFE定向拉丝设备中将粉料B中的PTFE喷射拉丝，形成空间网状疏松胶团，并收集，制得混粉C；混粉C经热辊压机辊压两次成膜，热压温度为150℃。经第一次辊压后，正极膜的厚度为500微米左右，负极膜的厚度为500微米左右；第二次辊压后正极膜的厚度为280微米左右，负极膜的厚度为280微米左右。将正极石墨膜热复合在打孔涂碳铝箔的单面，热复合辊压温度为160℃。
(3)组装准固态锂离子电池：
将不依赖溶剂的高负载电池LiNi1.5Mn0.5O4正极单面极片、Li4Ti5O12负极和高锂固溶度的预锂化聚苯硫醚膜材，叠在一起，且正负极的负载面被膜材隔开，集流体未负载面向外，在110℃进行热压复合，形成“三明治”结构复合片层，如图4所示。再将15个“三明治”结构复合片层采用叠片机叠在一起，正极铝集流体与正极铝集流体相贴合，负极铜集流体与负极铜集流体相贴合，极耳部分进行焊接，铝塑膜封装后，真空注含LiTFSI和FEC的离子 液体电解液，热封入壳，制成高压钛酸锂准固态锂离子电池。

Claims (26)

  1. 一种高锂固溶度的预锂化聚苯硫醚的制造方法，其特征在于，包括以下步骤：
    将N-甲基吡咯酮(NMP)、硫化锂Li 2S、氢氧化锂LiOH置于有搅拌功能的高压反应釜中，并升温到150-250℃高温脱水2-5h后，降温至100℃，加入1,4-二氯苯(p-DCB)，在150-250℃下反应80-200分钟；滴加与LiOH的物质的量相同的盐酸，中和LiOH，并采用蒸发或升华的办法除去NMP和H 2O，得到干燥混合粉料；在混合粉料中，加入氯离子络合剂，搅拌均匀，并置于密闭反应釜中，在150-250℃下反应80-200分钟，再经洗涤、干燥，得到高锂固溶度的预锂化聚苯硫醚。
  2. 根据权利要求1所述的预锂化聚苯硫醚的制造方法，其特征在于，所述的Li 2S为金属锂粉和硫粉高温反应生成或硫酸锂(Li 2SO 4)碳热还原反应生成。
  3. 根据权利要求1所述的预锂化聚苯硫醚的制造方法，其特征在于，所述的NMP、硫化锂Li 2S、氢氧化锂LiOH的摩尔配比为1-5：1：0.05-0.2。
  4. 根据权利要求1所述的预锂化聚苯硫醚的制造方法，其特征在于，所述Li 2S与p-DCB的摩尔配比为1.3-0.8：1。
  5. 根据权利要求1所述的预锂化聚苯硫醚的制造方法，其特征在于，所述蒸发或升华的办法为热风烘干法、旋转蒸发法、冷冻干燥法，最大限度保留固相成分，仅去除NMP和H 2O。
  6. 根据权利要求1所述的预锂化聚苯硫醚的制造方法，其特征在于，所述的氯离子络合剂为有机无金属离子络合剂，优选为杯芳冠醚、杯咪唑、杯吡咯、杯芳烃。
  7. 根据权利要求1所述的预锂化聚苯硫醚的制造方法，其特征在于，所述的氯离子络合剂添加的物质的量为p-DCB的0.01-0.2倍。
  8. 根据权利要求1所述的预锂化聚苯硫醚的制造方法，其特征在于，步骤1)中所制备的聚苯硫醚固态电解质中，预锂化聚苯硫醚粉料所占的重量百分比为80％-97％。
  9. 权利要求1所述制备方法制备的预锂化聚苯硫醚。
  10. 各向同性的聚苯硫醚固态电解质膜的制备方法，其特征在于，将预锂化聚苯硫醚粉料与聚四氟乙烯(PTFE)于聚四氟乙烯呈玻璃态的温度条件下在混合机中混合均匀，使用超音速气体进行空气研磨，使得PTFE的分子链延展打开， 并与预锂化聚苯硫醚粉料之间形成物理粘连，且不发生化学反应；再经过挤出机排除粉体中的气体制成连续饼状宽带，然后将连续饼状宽带采用温度低于150℃的热辊压制成预锂化聚苯硫醚膜材，并收卷；制备成聚苯硫醚固态电解质膜。
  11. 根据权利要求10所述聚苯硫醚固态电解质膜的制备方法，其特征在于，所述预锂化聚苯硫醚粉料为权利要求9所述的预锂化聚苯硫醚；所述空气研磨是首先将粉料预热到40-50℃，在PTFE定向拉丝设备中采用超音速射流气体对PTFE喷射拉丝。
  12. 根据权利要求11所述的聚苯硫醚固态电解质膜的制造方法，其特征在于，所述的PTFE定向拉丝，为粉料中的PTFE在经超音速射流气体预热后形成粘流态，PTFE粘流体在加压条件下，通过细小喷嘴构成超音速射流流体喷出，通过文丘里管结构吸入混合粉料，在蜗壳型腔中进行收集，收集的物料成为空间网状疏松团聚体。
  13. 根据权利要求10所述聚苯硫醚固态电解质膜的制备方法，其特征在于，预锂化聚苯硫醚粉料和PTFE在混料机中混合均匀的过程中温度控制在10℃以下；混料机中混料时间为0.5-4小时。
  14. 根据权利要求10所述聚苯硫醚固态电解质膜的制备方法，其特征在于，预锂化聚苯硫醚压膜膜材热压后还包括以下处理过程：
    将两张或多张预锂化聚苯硫醚一次压膜膜材经过热压复合成无缺陷高致密固态电解质膜；或者：
    采用两个加热的氟橡胶模块将预锂化聚苯硫醚膜材在150-230℃下热压1-10s，使得预锂化聚苯硫醚一次压膜膜材的微裂纹、孔洞愈合，制成无缺陷高致密固态电解质膜。
  15. 权利要求10-14任一项所述制备方法制备的聚苯硫醚固态电解质膜。
  16. 高负载电池极片的制备方法，其特征在于，将导电碳材料分别与锂离子电池正极材料、负极材料，在混料机中混合均匀；再分别与PTFE粉体在PTFE呈玻璃态的温度条件下混合均匀，使用超音速射流气体使PTFE的分子链延展打开，分别同导电碳材料与锂离子电池正极、负极材料的混合粉体形成物理粘连，且不发生化学反应；在高温热压下制成膜材D，再采用热压复合工艺将膜材D与经过打孔的集流体的单面热复合，制成单面负载正极厚电极、单面负载负极厚电极。
  17. 根据权利要求16所述的高负载电池极片的制造方法，其特征在于，锂离子电池正极材料或负极材料与碳材料的重量百分比为50％-95％：50％-5％。
  18. 根据权利要求16所述的高负载电池极片的制造方法，其特征在于，PTFE粉体与导电碳材料、锂离子电池正极或负极材料的混合粉料的重量百分比为3％-15％：85％-97％。
  19. 根据权利要求16所述的高负载电池极片的制造方法，其特征在于，热压温度为150-250℃。
  20. 根据权利要求16所述的高负载电池极片的制造方法，其特征在于，将膜材D与集流体热复合时的辊压温度为120-220℃，集流体和一张膜材D经同速放卷，进入两个相对转动的热辊压机，通过调节辊缝宽度，控制压力，使得膜材D刚好能够复合在集流体上即可，避免因辊压力过大导致膜材形变过大，拉断集流体。
  21. 根据权利要求16所述的高负载电池极片的制造方法，其特征在于，所述使用超音速射流气体使PTFE的分子链延展打开是首先将粉料预热到40-50℃，在PTFE定向拉丝设备中使用超音速射流气体喷射拉丝，所述的PTFE定向拉丝，为粉料中的PTFE在经超音速射流气体预热后形成粘流态，PTFE粘流体在加压条件下，通过细小喷嘴构成超音速射流流体喷出，通过文丘里管结构吸入混合粉料，在蜗壳型腔中进行收集，收集的物料成为空间网状疏松团聚体。
  22. 根据权利要求16所述的高负载电池极片的制造方法，其特征在于，所述导电碳材料为super-P、乙炔黑、活性碳、人造石墨、高纯石墨中的一种或几种的混合物；所述的集流体为涂碳保护并打孔的不锈钢箔、铝箔或铜箔。
  23. 一种高安全性高体积能量密度准固态锂离子电池的制造方法，其特征在于，包括以下步骤：
    利用权利要求15制备的聚苯硫醚固态电解质膜作为电解质，权利要求16-22任一项所述制备方法制备的单面负载正极厚电极、单面负载负极厚电极分别作为正极极片、负极极片，组装准固态锂离子电池，将正极极片、聚苯硫醚固态电解质和负极极片依次叠在一起，且正极极片、负极极片的集流体未负载的一面向外；在80～150℃进行热压复合，形成“三明治”结构的复合片层，采用包装膜将复合片层封装后，真空注液，热封入壳。
  24. 根据权利要求23所述的高安全性高体积能量密度准固态锂离子电池的 制造方法，其特征在于，在封装之前，将多个复合片层采用叠片机叠在一起，正极集流体与正极集流体相贴合，负极集流体与负极集流体相贴合，极耳部分进行焊接，再采用包装膜将复合片层封装。
  25. 根据权利要求23所述的高安全性高体积能量密度准固态锂离子电池的制造方法，其特征在于，所述的包装膜是绝缘的柔性封装膜，优选为铝塑膜、聚酰亚胺膜、塑料膜。
  26. 根据权利要求23-25任一项所述的制造方法制备的高安全性高体积能量密度准固态锂离子电池。
PCT/CN2020/130376 2019-11-21 2020-11-20 预锂化聚苯硫醚、聚苯硫醚固态电解质膜、电池极片、准固态锂离子电池及其制造方法 WO2021098820A1 (zh)

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