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  • H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
  • H01F1/00—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties
  • H01F1/01—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials
  • H01F1/03—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity
  • H01F1/12—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials
  • H01F1/34—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials non-metallic substances, e.g. ferrites
  • H01F1/342—Oxides
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  • H01G11/00—Hybrid capacitors, i.e. capacitors having different positive and negative electrodes; Electric double-layer [EDL] capacitors; Processes for the manufacture thereof or of parts thereof
  • H01G11/22—Electrodes
  • H01G11/30—Electrodes characterised by their material
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  • H01G11/44—Raw materials therefor, e.g. resins or coal
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  • H01G11/00—Hybrid capacitors, i.e. capacitors having different positive and negative electrodes; Electric double-layer [EDL] capacitors; Processes for the manufacture thereof or of parts thereof
  • H01G11/22—Electrodes
  • H01G11/30—Electrodes characterised by their material
  • H01G11/50—Electrodes characterised by their material specially adapted for lithium-ion capacitors, e.g. for lithium-doping or for intercalation
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  • 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
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  • H01M10/054—Accumulators with insertion or intercalation of metals other than lithium, e.g. with magnesium or aluminium
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  • H01M4/04—Processes of manufacture in general
  • H01M4/0471—Processes of manufacture in general involving thermal treatment, e.g. firing, sintering, backing particulate active material, thermal decomposition, pyrolysis
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  • H01M4/13—Electrodes for accumulators with non-aqueous electrolyte, e.g. for lithium-accumulators; Processes of manufacture thereof
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  • H01M4/13—Electrodes for accumulators with non-aqueous electrolyte, e.g. for lithium-accumulators; Processes of manufacture thereof
  • H01M4/139—Processes of manufacture
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  • H01M4/36—Selection of substances as active materials, active masses, active liquids
  • H01M4/48—Selection of substances as active materials, active masses, active liquids of inorganic oxides or hydroxides
  • H01M4/485—Selection of substances as active materials, active masses, active liquids of inorganic oxides or hydroxides of mixed oxides or hydroxides for inserting or intercalating light metals, e.g. LiTi2O4 or LiTi2OxFy
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  • H01M4/36—Selection of substances as active materials, active masses, active liquids
  • H01M4/58—Selection of substances as active materials, active masses, active liquids of inorganic compounds other than oxides or hydroxides, e.g. sulfides, selenides, tellurides, halogenides or LiCoFy; of polyanionic structures, e.g. phosphates, silicates or borates
  • H01M4/5825—Oxygenated metallic salts or polyanionic structures, e.g. borates, phosphates, silicates, olivines
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  • C08J2201/00—Foams characterised by the foaming process
  • C08J2201/04—Foams characterised by the foaming process characterised by the elimination of a liquid or solid component, e.g. precipitation, leaching out, evaporation
  • C08J2201/046—Elimination of a polymeric phase
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  • C08J9/00—Working-up of macromolecular substances to porous or cellular articles or materials; After-treatment thereof
  • C08J9/0061—Working-up of macromolecular substances to porous or cellular articles or materials; After-treatment thereof characterized by the use of several polymeric components
• • H—ELECTRICITY
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  • H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
  • H01F1/00—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties
  • H01F1/01—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials
  • H01F1/03—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity
  • H01F1/12—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials
  • H01F1/34—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials non-metallic substances, e.g. ferrites
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  • H01M2004/021—Physical characteristics, e.g. porosity, surface area
• • 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
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  • 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
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  • Y02E60/00—Enabling technologies; Technologies with a potential or indirect contribution to GHG emissions mitigation
  • Y02E60/13—Energy storage using capacitors
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  • 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 present invention relates to a method for preparing a particular polymeric composition that can be used to constitute a lithium-ion, sodium-ion or supercapacitor battery electrode or to exhibit magnetic properties, such a composition obtained by this method, a precursor mixture of this composition obtained by a first mixing step of this method, and this lithium-ion battery electrode or supercapacitor.
• the invention applies to all polymeric compositions comprising a very high level of filler (advantageously greater than 80% by weight or 60% by volume) and a controlled porosity depending on the application chosen, the filler being for example a material active inorganic for lithium-ion or sodium-ion battery electrode, porous carbon for supercapacitor electrode or magnetic inorganic filler.
• a solvent process is generally used to mix the various compounds (eg magnetic charge, surfactant, compatibilizer, binder) in order to obtain a dispersion or slurry. ) which, once dried, allows the obtaining of the magnetic material, as for example described in US-A1-2011/0018664. After coating this dispersion, a magnetic field is applied to orient the magnetic charges, the resulting coated film is dried, then it is cut to the desired shape and finally sintered to obtain the final material. For these magnetic applications, we rather search for a dense material in order to have the highest corresponding magnetic field possible.
• the electrodes are most often obtained by a method with organic or aqueous solvent comprising a step of dissolution or dispersion of the various compounds of the electrode including a polymeric binder in the solvent, followed by a step of spreading on a metal collector and finally a step of evaporation of the solvent.
• This method for example described in document US-B2-7 235 332 with an organic solvent, makes it possible to obtain a high porosity in the material, due to the space occupied by the solvent. This porosity is necessary for the impregnation of the electrode with an electrolyte, which makes it possible to ensure its operation.
• Another known method essentially for the incorporation of high magnetic charge rates to materials, consists in making a mold injection of a paste comprising the filler and a thermosetting resin precursor, as for example described in the US document. -A1 -2006/0280921, then baking the dough.
• the magnetic materials obtained have a high level of magnetic charges linked by a three-dimensional network. Nevertheless, these materials once cured are no longer convertible and have the disadvantage of requiring usually long process times due to the reaction of the resins.
• this type of process is highly dependent on the flow of the thermosetting precursors through the intergranular porosity (Darcy's law) and therefore on the viscosity of these precursors.
• Document US-A1 -2011 / 074531 describes, for example, the melting of materials containing a magnetic charge higher than 80%, via the functionalization of the surface of the charge by an epoxy oligomer, the use of a low molecular weight polymer chain (4 to 12 kmol / g) containing a hydrogen amine labile allowing crosslinking with the epoxy function, and the addition of a pentaerythritol type additive and a fatty acid.
• a major disadvantage of these methods of incorporation by the molten route of high levels of magnetic charges is the need to functionalize the surface of the charge and to use a binder of low molecular weight, typically less than 15 kmol / g, to avoid the problems induced by high molar masses and without compatibilization of the surface of the load, which include a considerable increase in the viscosity and therefore the pressures associated with the process and a significant abrasion of the equipment and raw materials in contact generated by the non-functionalized load due to its high concentration.
• the lithium-ion batteries consist of at least two faradic conducting electrodes of different polarities, the anode (usually made of graphite) and the cathode (usually an oxide of a transition metal), electrodes between which is located a separator consisting of an electrical insulator impregnated with an aprotic electrolyte based on Li + cations ensuring the ionic conductivity.
• the active material of a lithium-ion battery electrode allows a reversible insertion / deinsertion of lithium within the electrode, and the higher the mass fraction of this active material, the greater the capacitance of the electrode.
• the electrode must also contain an electrically conductive compound, such as carbon black and, to give it a sufficient mechanical cohesion, a polymeric binder.
• a lithium-ion battery is thus based on the reversible exchange of the lithium ion between the anode and the cathode during charging and discharge of the battery, and it has a high energy density for a very low mass thanks to the physical properties of lithium.
• compositions for this battery are each characterized by the presence of a crosslinked elastomeric binder and a non-volatile organic compound that can be used in the electrolyte solvent.
• This organic compound is present in the composition in a reduced mass fraction (typically less than 5%) and can be a carbonate of at least one olefin, e.g. ethylene carbonate.
• US-B1-7,820,328 has attempted to provide a solution to this problem by using, in conjunction with a polymeric binder and a conductive dilution charge, a low mass fraction of at most 5% of a sacrificial polymer. thermally decomposed to obtain an electrode incorporating an active material in a mass fraction of greater than 90%, but without exemplary embodiment detailing the process used (which can be indifferently implemented with or without a solvent).
• a major disadvantage of the process presented in the latter document lies in the difficulty of implementation of the electrodes in the case where they would be obtained by melting, as well as in their electrochemical capacity may be insufficient in a lithium-ion battery.
• An object of the present invention is therefore to design a melt manufacturing process which overcomes these disadvantages by allowing in particular a control of the porosity of the compositions obtained. according to the targeted applications, with incorporation of a very high mass rate of charges typically greater than 80%, without the need for functionalization of these charges.
• a hot active material and additives comprising a polymeric binder and a continuous sacrificial polymeric phase are mixed by hot melt and without solvent evaporation. so that the mass fraction in the mixture obtained of this phase is equal to or greater than 15%, then a polymer composition is obtained which can be used to constitute a lithium-ion, sodium-ion or supercapacitor battery electrode or to exhibit magnetic properties, with improved plasticization and fluidity during the implementation of the molten mixture despite the mass ratio of active material (s) very high in the composition, and obtaining a controlled porosity of the composition according to the desired application giving it, as appropriate, an electrode capacitance or satisfactory magnetic field properties.
• a method of preparation according to the invention of a polymeric composition that can be used to constitute a lithium-ion, sodium-ion or supercapacitor battery electrode or to exhibit magnetic properties thus comprises the following steps:
• composition which comprises the active material (s) with a mass ratio greater than 80%
• this method according to the invention is such that said sacrificial polymeric phase is used in step a) according to a mass fraction in said mixture which is equal to or greater than 15%.
• said sacrificial polymeric phase is used in step a) in a mass fraction in said mixture which is between 20% and 80% inclusive.
• the process of the invention makes it possible to incorporate, directly in the melt and by conventional plastic transformation techniques, very high levels of cumulative charges in the compositions obtained, greater than 80% by weight or even 60% in volume, which confer high performance electrochemical cells incorporating electrodes consisting of these compositions.
• the Applicant has thus been able to produce, in the molten state, materials which can be used in the state according to the chosen application which, after shaping and removal of the sacrificial phase, contain these very high charge levels without prior modification of the surface of the charges. use of a coupling agent.
• this method makes it possible to control the porosity within the composition by the quantity of sacrificial phase introduced as a function of the intended application by controlling it in terms of size, quantity and morphology of the pores, or even possibly eliminating this porosity, using a continuous sacrificial phase well chosen in its nature with respect to this melt process and the chosen application.
• An open porosity of dimensions for example less than 20 .mu.m, can be sought for electrode-type applications for sorbing an electrolyte.
• the porosity of the composition can be controlled (compromise density / magnetism), reduced or eliminated by compression to obtain a denser material. Indeed according to the chosen application, one can either decrease the density for an equivalent magnetic field or increase the magnetic field for a given volume by increasing the density. To obtain electrodes, it is also possible to compress the material to control its porosity.
• the mixing, dispersion and homogeneous distribution of the binder phase, the sacrificial phase and the active material (s) are ensured during the melt process.
• a possible crosslinking of the binder phase is possible to optimize the mechanical properties and cohesion of the composition, but is not necessary if a future transformation is envisaged.
• the method according to the invention provides short implementation times, typical of conventional plastic processing processes such as extrusion for example, and that the improved processability of the compositions of the present invention.
• the invention is maintained thereafter as long as no crosslinking has been performed.
• said sacrificial polymeric phase may be used in step a) in the form of granules of average size greater than 1 mm in number (ie not nanoparticles), and step a) is placed implemented in an internal mixer or in an extruder without macroseparation of phases between the binder phase and the sacrificial polymeric phase in said mixture, wherein the binder phase is homogeneously dispersed in the sacrificial polymeric phase which is continuous, or form a co-continuous phase with the latter.
• the sacrificial phase can be extracted by simple thermal decomposition or by any other method allowing its extraction without impacting the rest of the mixture.
• the sacrificial phase can also be directly extracted at the outlet of the die by decompression during the use of volatile compounds. It is preferable to use as the sacrificial material one or more polymers leaving little or no residue during its (their) decomposition. However, if such a polymer compatible with the final application is chosen as sacrificial phase, one can alternatively control its extraction and leave part of the sacrificial phase in the composition obtained.
• said sacrificial polymeric phase is removed substantially without residue or not in step b) via a thermal decomposition, the sacrificial phase having a thermal decomposition temperature of at least 20 ° lower C at a thermal decomposition temperature of the phase forming a binder.
• this sacrificial phase is preferably based on at least one sacrificial polymer chosen from carbonate polyalkenes, preferably polyethylenes carbonate and / or carbonate polypropylenes (nevertheless other polymers known to have a temperature can also be used. free of thermal degradation).
• said sacrificial polymeric phase is removed substantially without residue or not in step b) via extraction with a solvent and is based on at least one liquid-extractable sacrificial polymer and preferably selected from the group consisting of polyethylene glycols, polypropylene glycols and mixtures thereof (it should be noted that other bases of liquid extractable polymers, aqueous or organic base can also be used).
• photoacid generators as additives to aid the decomposition of sacrificial phases, eg for polypropylene carbonate (reference may be made to the article by Cupta M., Jayachandran P., Khol P., Photoacid generators for catalytic decomposition of polycarbonate, Journal of Applied Polymer Science, 2007, Vol 105, pp. 2655-2662).
• the use of these photoacids makes it possible to reduce the degradation temperatures after implementation of the cathode, in particular. They are therefore useful without being necessary to the invention.
• active material (s) usable (s) in the process of the invention and present (s) in the composition obtained in step b) according to a mass fraction preferably equal to or greater than 85% it is possible to use, depending on the desired application, a filler selected from the group consisting of:
• any magnetic inorganic fillers known to those skilled in the art such as ferrites Fe 2 O 3 and magnetic materials of Nd-Fe-B, Sm-Fe-N or cobalt-based type such as SmCo, in particular ,
• active inorganic fillers capable of allowing lithium insertion / deinsertion for the lithium-ion battery electrodes, comprising lithiated polyanionic compounds or complexes such as a phosphate of a lithiated metal M of formula LiMPO 4 coated with carbon (eg C-LiFePO 4 ), a lithium titanium oxide of formula Li 4 Ti 5 O 2 , or any other active material known to those skilled in the art for cathodes (eg LiCoO 2 , Li n0 4 LiNi 3 Mni / 3 Co 3 0 4 ) or anodes (eg graphite), and
• lithiated polyanionic compounds or complexes such as a phosphate of a lithiated metal M of formula LiMPO 4 coated with carbon (eg C-LiFePO 4 ), a lithium titanium oxide of formula Li 4 Ti 5 O 2 , or any other active material known to those skilled in the art for cathodes (eg LiCoO 2 , Li n0 4 LiN
• the charges comprising porous carbon for the electrodes of supercapacitors.
• Electroconductive inorganic fillers can be added together with others, for example in the context of electrodes for lithium-ion, sodium-ion or supercapacitor batteries, but also alone in the context of highly conductive applications, for conductivities greater than S / cm.
• conductive carbon black may be mentioned, but also graphite, graphene, carbon nanofibers, carbon nanotubes and a mixture thereof.
• binder polymer (s) ensuring the cohesion of the composition after use
• all the polymer bases can be used, subject to their ability to be processed by the molten route and, as previously mentioned, to their possible compatibilization with the chosen sacrificial phase.
• polyolefins, halogenated polymers, acrylic polymers, acrylates, methacrylates, vinyl acetates, polyethers, polyesters, polyamides, aromatic polymers and elastomers may be mentioned.
• said binder phase comprises at least one crosslinked elastomer or not, which is used in said mixture according to a mass fraction of between 1% and 12% and which is preferably selected from the group consisting of hydrogenated butadiene and acrylonitrile copolymers (HNBR), copolymers of ethylene and an acrylate, polyisoprenes and mixtures thereof.
• HNBR hydrogenated butadiene and acrylonitrile copolymers
• other elastomers of the rubber or thermoplastic elastomer type can be used.
• a binder ensuring a continuity of elastic properties over a temperature range of substantially -20 ° C to 80 ° C, hence the preferential use of elastomers such as HNBR or copolymers d ethylene and acrylate, in particular.
• compositions of the invention specific additives in order to improve or optimize their manufacturing process. It is also possible to add compounds that allow crosslinking of the binder as well as coagents capable of aiding in the crosslinking and homogenization thereof. For example, organic peroxides can be mentioned as a crosslinking agent and triallyl cyanurate as a coagent. It is also possible to use any compounds that make it possible to crosslink the binder, such as photoinitiators or sulfur compounds (typical of the crosslinking of rubbers by vulcanization).
• said composition obtained in step b) may have a volume porosity of between 30% and 70% and is adapted to constitute a lithium-ion, sodium-ion or supercapacitor battery electrode.
• the process may comprise between steps a) and b) a step of shaping by calendering said mixture obtained in step a), and said composition obtained in step b) is formed of a sheet of thickness between 50 ⁇ m and 150 ⁇ m.
• a polymeric composition according to the invention which can be used to constitute a lithium-ion, sodium-ion or supercapacitor or to present magnetic properties, is such that the composition is obtained by said method of the invention as defined above and may have said sacrificial phase in a mass fraction equal to or greater than 0.001% and for example between 0.01% and 10%.
• a polymeric mixture according to the invention which can be used to constitute a precursor of this composition (eg an electrode precursor) is such that this mixture is obtained by step a) of said process of the invention and comprises said sacrificial polymeric phase according to a mass fraction in this mixture equal to or greater than 15% and preferably inclusive between
• this mixture of the invention is further such that said binder phase is homogeneously dispersed in said continuous sacrificial polymeric phase, or forms a co-continuous phase therewith.
• a lithium-ion, sodium-ion or supercapacitor battery electrode according to the invention e.g. a cathode or anode
• a cathode or anode is such that it comprises a polymeric composition according to the invention as defined above.
• this electrode may be such that said composition further comprises an electrically conductive filler selected from the group consisting of carbon black, graphite, expanded graphite, carbon fibers, carbon nanotubes, graphene and mixtures thereof, said electrically conductive filler being present in the composition in a mass fraction of between 1% and 10%.
• an electrically conductive filler selected from the group consisting of carbon black, graphite, expanded graphite, carbon fibers, carbon nanotubes, graphene and mixtures thereof, said electrically conductive filler being present in the composition in a mass fraction of between 1% and 10%.
• the invention described in the present description can be applied to other fields than those mentioned above requiring high levels of inorganic fillers (metal, magnetic or other) and possibly a control of the porosity of the composition obtained, as for example for insulating screens between two diamagnetic. It is also possible, by replacing the magnetic charges by electroconductive charges, to use melt materials having very high electrical conductivities (greater than S / cm), porous or not depending on the desired application. A controlled and finely dispersed porosity allows a thermal or sound insulation, while having a high rate of charge. For example, high electrical conductivity effects combined with thermal insulation in the context of the Seebeck or Peltier effect and a thermoelectric generator can be advantageously obtained.
• a composition 1 of magnetic material was prepared according to the following formulations (expressed in mass and volume fractions), for the mixture before extraction of the sacrificial polymer and for the composition 1 obtained after this extraction.
• Composition 1 was prepared using an internal mixer at 60 ° C. HNBR and a portion of the polyethylene carbonate were first added to obtain a plasticized molten mixture. Then, the magnetic charges were gradually added with regular addition of the remaining polyethylene carbonate until a homogeneous mixture was obtained.
• the resulting mixture was then calendered in sheet form before being placed in an oven at 230 ° C. under air for 15 minutes. Finally, the resulting product was placed in a press at 150 ° C to re-densify the material forming this composition 1.
• composition 1 During the heat treatment, it was measured by mass difference removal of the polyethylene carbonate: 100% of the polyethylene carbonate initially incorporated in the mixture was thus decomposed. This leads to a decrease in density of composition 1 from 3 g / cm 3 to 2.4 g / cm 3 . After re-densification, a density of 3.7 g / cm 3 was obtained.
• this process for preparing composition 1 does not require the surface functionalization of the magnetic charges, which can be used as they are for the magnetic fields they generate in the final product thanks to the high quantities of charges (mass ratio of 95%) and the re-densification of the material after extraction of the sacrificial polymer.
• this method makes it possible to obtain an intense magnetic field in one direction, thanks to the presence of a relatively high proportion of sacrificial phase in the molten mixture (mass ratio of 20%) and to the fluidity of the mixture. Once charges are added and oriented, this extraction and re-densification can maintain this orientation and increase the density and therefore the intensity of the emitted field.
• a lithium ion battery cathode composition 2 was prepared according to the following formulations, for the mixture before extraction of the sacrificial polymer and for the composition 2 obtained after the extraction.
• Binder HNBR (Zetpol 2010L) 4.9 10.4 7.5 20.8
• Composition 2 was prepared using an internal mixer at 70 ° C. HNBR and a portion of the polyethylene carbonate were first added to obtain a plasticized melt blend. Then, the mineral fillers were gradually added with regular addition of the remaining polyethylene carbonate, until a homogeneous mixture was obtained.
• the resultant mixture was then calendered as a sheet to press in a press at 170 ° C for 15 minutes.
• a decomposition step of the sacrificial polymer was performed in an oven under air at 230 ° C. for 15 min. During the heat treatment, it was measured by mass difference removal of the polyethylene carbonate: 100% of the polyethylene carbonate initially incorporated in the mixture was thus decomposed. This led to a decrease in electrode density of 2.0 g / cm 3 to 1.3 g / cm 3 and a 50% volume porosity.
• the resulting composition 2 which is derived from a molten mixture comprising more than 30% by weight of sacrificial phase and which comprises 85% by weight of active material, can be used directly as a cathode.
• this composition 2 has been characterized in coin cell against Li metal. By setting a current equivalent to a charge / discharge rate of C / 5, a maximum discharge capacity of 115 mAh per gram of cathode (not including current collector mass) was obtained, which corresponds to a capacitance of 135 mAh per gram of C-LiFePO 4 .
• a lithium ion battery cathode composition 3 was prepared according to the following formulations (expressed in mass and volume fractions), for the mixture before extraction of the sacrificial polymer and for the composition 3 obtained after this extraction. Table 3:
• Composition 3 was prepared using an internal mixer at 80 ° C. HNBR and high molecular weight polypropylene carbonate were first added to obtain a plasticized molten mixture. Then, the mineral fillers were gradually added with regular addition of the low molecular weight polypropylene carbonate (preheating to about 60 ° C of the material may be necessary in order to reduce the viscosity and facilitate the addition), until to obtain a homogeneous mixture.
• the resultant mixture was then calendered as a sheet to press in a press at 170 ° C for 15 minutes.
• a decomposition step of the sacrificial polymer was performed in an oven under air at 230 ° C. for 45 minutes.
• the mass elimination of the polypropylene carbonates was measured by mass difference: 100% of the polypropylene carbonates initially incorporated in the mixture were thus decomposed. This led to a decrease in electrode density from 2.1 g / cm 3 to 1.6 g / cm 3 and a 40% volume porosity.
• the resulting composition 3 which comes from a molten mixture comprising more than 20% by weight of sacrificial phase and which comprises 85% by weight of active material, can be used directly as cathode. Indeed, it has been characterized in coin cell against Li metal. By setting a current equivalent to a charging and discharging rate of C / 5, a maximum discharge capacity of 123 mAh per gram of cathode (without including the mass of the current collector) was obtained, which corresponds to a capacitance of 145 mAh per gram of C-LiFePO 4 .
• a lithium ion battery cathode composition 4 was prepared according to the following formulations (expressed in mass and volume fractions), for the mixture before extraction of the sacrificial polymer and for the composition 4 obtained after this extraction.
• Composition 4 was prepared using a twin screw extruder equipped with three gravimetric feeders, a side feeder, a gear pump and a flat die. The various raw materials were distributed in these different gravimetric feeders. During the extrusion, the feed rates of the feeders were adjusted to obtain the desired composition 4. Using a specific screw profile, the raw materials were dispersed and melt homogenized in the twin-screw extruder. The gear pump and the flat die at the end of the extruder were used to shape the resulting mixture as a film directly deposited on a current collector. The resulting film was then heat treated at 230 ° C for 60 min. under air, in order to obtain the final composition 4.
• the resulting composition 4 which is derived from a molten mixture comprising more than 30% by weight of sacrificial phase and which comprises 90% by weight of active material, can be used directly as a cathode. Indeed, it has been characterized in coin cell against Li metal. By setting a current equivalent to a charging and discharging rate of C / 5, a maximum discharge capacity of 123 mAh per gram of cathode (without including the collector mass) was obtained, which corresponds to a capacity of 136 mAh. mAh per gram of C-LiFePO 4 .
• a lithium ion battery cathode composition was prepared according to the following formulations (expressed in mass and volume fractions), for the mixture before extraction of the sacrificial polymer and for the composition obtained after this extraction. Table 5:
• Composition 5 was prepared using a twin screw extruder equipped with three gravimetric feeders, a side feed, a gear pump and a flat die. The various raw materials were distributed in these different gravimetric feeders. During extrusion, the flow rates of the feeders were adjusted to obtain the desired composition. Using a specific screw profile, the raw materials were dispersed and melt homogenized in the twin-screw extruder. The gear pump and the flat die at the end of the extruder were used to shape the resulting mixture as a film directly deposited on a current collector. The resulting film was then heat treated at 230 ° C for 60 min. under air, in order to obtain the final composition.
• the mass removal of the polypropylene carbonate was measured by mass difference: 100% of the polypropylene carbonate incorporated in the mixture was thus decomposed. This led to a drop in electrode density of 2.1 g / cm 3 at 1.4 g / cm 3 and a 50% volume porosity.
• the resulting composition which is derived from a molten mixture comprising more than 30% by weight of sacrificial phase and which comprises 90% by weight of active material, can be used directly as a cathode. Indeed, it has been characterized in coin cell against Li metal.
• a lithium-ion battery cathode composition 6 was prepared according to the following formulations (expressed in mass and volume fractions), for the mixture before extraction of the sacrificial polymer and for the composition 6 obtained after this extraction.
• Composition 6 was prepared using an internal mixer at 70 ° C. HNBR and a portion of the polyethylene carbonate were first added to obtain a plasticized molten mixture. Then we added progressively the mineral fillers with regular addition of the remaining polyethylene carbonate, until a homogeneous mixture is obtained.
• the resultant mixture was then calendered as a sheet to press in a press at 170 ° C for 15 minutes.
• a decomposition step of the sacrificial polymer was performed in an oven under air at 240 ° C. for 30 minutes. During the heat treatment, it was measured by mass difference removal of the polyethylene carbonate: 100% of the polyethylene carbonate initially incorporated in the mixture was thus decomposed. This led to a volume porosity of 66%.
• the resulting composition 6 which is obtained from a molten mixture comprising 50% by mass of sacrificial phase and which comprises 85% by weight of active material, can be used directly as cathode. Indeed, it has been characterized in coin cell against Li metal. By setting a current equivalent to a charge / discharge rate of C / 5, a maximum discharge capacity of 109 mAh per gram of cathode (not including current collector mass) was obtained, which corresponds to a capacitance 128 mAh per gram of C-LiFePO 4 .
• This electrode was further compressed after degradation of the sacrificial phase, the resulting product still having the same final formulation as composition 6 and also being directly usable as a cathode. It was characterized as previously in a coin cell against Li metal, setting a current equivalent to a charge and discharge rate of C / 5, and a maximum discharge capacity of 106 mAh per gram of cathode was obtained. (Not including the mass of the collector), which corresponds to a capacity of 124 mAh per gram of C-LiFePO 4 .
• a "control" cathode composition for a lithium-ion battery was prepared according to the following formulations (expressed in mass and volume fractions), for the mixture before extraction of the sacrificial polymer and for the "control" composition obtained after this extraction.
• the "control" composition was prepared using an internal mixer at 70 ° C. HNBR and polyethylene carbonate were first added to obtain a plasticized melt blend. Then, some of the mineral fillers were gradually added. The remainder of the mineral fillers had to be added to an open mixer. Indeed, the complete addition of the charges in the internal mixer causes an abrasive burnout phenomenon.
• the resultant mixture was then calendered as a sheet to press in a press at 170 ° C for 15 minutes. Due to the high viscosity of the mixture, it was only possible to obtain a thickness of 280 ⁇ m in comparison with the 50 ⁇ m to 150 ⁇ m obtained in normal time with the method of the invention.
• a decomposition step of the sacrificial polymer was performed in an oven under air at 230 ° C. for 20 minutes. During the heat treatment, it was measured by mass difference removal of the polyethylene carbonate: 100% of the polyethylene carbonate initially incorporated in the mixture was thus decomposed. This led to a volume porosity of only 17.6%.
• the "control" composition obtained in a coin cell against Li metal has been characterized.
• a current equivalent to a charging and discharging rate of C / 5 By setting a current equivalent to a charging and discharging rate of C / 5, a maximum discharge capacity of 26 mAh per gram of cathode (without including the mass of the current collector) was obtained, which corresponds to a capacitance 30 mAh per gram of C-LiFePO.
• control composition which is derived from a melt containing only 10% by weight of sacrificial phase, in contrast to the amounts of at least 15% required in the melt blends of the present invention, is very difficult to achieve. enforce.
• this very low porosity "control" composition does not provide efficient electrochemical results due to the insufficient access of the electrolyte to the active ingredient that results (see capacity maximum discharge of only 26 mAh per gram of cathode), in particular contrary to Example 2 according to the invention characterized by the same mass ratio of final active ingredient (85%) but by the incorporation of a mass ratio clearly higher sacrificial phase (more than 30%) which provides a maximum discharge capacity of 115 mAh per gram of cathode.

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