Classifications

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  • C04B41/00—After-treatment of mortars, concrete, artificial stone or ceramics; Treatment of natural stone
  • C04B41/009—After-treatment of mortars, concrete, artificial stone or ceramics; Treatment of natural stone characterised by the material treated
• • B—PERFORMING OPERATIONS; TRANSPORTING
  • B05—SPRAYING OR ATOMISING IN GENERAL; APPLYING FLUENT MATERIALS TO SURFACES, IN GENERAL
  • B05D—PROCESSES FOR APPLYING FLUENT MATERIALS TO SURFACES, IN GENERAL
  • B05D5/00—Processes for applying liquids or other fluent materials to surfaces to obtain special surface effects, finishes or structures
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  • C04B35/00—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
  • C04B35/515—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on non-oxide ceramics
  • C04B35/52—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on non-oxide ceramics based on carbon, e.g. graphite
  • C04B35/521—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on non-oxide ceramics based on carbon, e.g. graphite obtained by impregnation of carbon products with a carbonisable material
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  • C04B35/00—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
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  • C04B35/56—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on non-oxide ceramics based on carbides or oxycarbides
  • C04B35/565—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on non-oxide ceramics based on carbides or oxycarbides based on silicon carbide
  • C04B35/573—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on non-oxide ceramics based on carbides or oxycarbides based on silicon carbide obtained by reaction sintering or recrystallisation
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  • C04B35/00—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
  • C04B35/622—Forming processes; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
  • C04B35/626—Preparing or treating the powders individually or as batches ; preparing or treating macroscopic reinforcing agents for ceramic products, e.g. fibres; mechanical aspects section B
  • C04B35/628—Coating the powders or the macroscopic reinforcing agents
  • C04B35/62844—Coating fibres
  • C04B35/62857—Coating fibres with non-oxide ceramics
  • C04B35/6286—Carbides
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  • C04B35/00—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
  • C04B35/622—Forming processes; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
  • C04B35/626—Preparing or treating the powders individually or as batches ; preparing or treating macroscopic reinforcing agents for ceramic products, e.g. fibres; mechanical aspects section B
  • C04B35/628—Coating the powders or the macroscopic reinforcing agents
  • C04B35/62844—Coating fibres
  • C04B35/62857—Coating fibres with non-oxide ceramics
  • C04B35/62873—Carbon
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  • C04B35/00—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
  • C04B35/622—Forming processes; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
  • C04B35/626—Preparing or treating the powders individually or as batches ; preparing or treating macroscopic reinforcing agents for ceramic products, e.g. fibres; mechanical aspects section B
  • C04B35/628—Coating the powders or the macroscopic reinforcing agents
  • C04B35/62894—Coating the powders or the macroscopic reinforcing agents with more than one coating layer
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  • C04B35/00—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
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  • C04B35/626—Preparing or treating the powders individually or as batches ; preparing or treating macroscopic reinforcing agents for ceramic products, e.g. fibres; mechanical aspects section B
  • C04B35/628—Coating the powders or the macroscopic reinforcing agents
  • C04B35/62897—Coatings characterised by their thickness
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  • C04B35/00—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
  • C04B35/71—Ceramic products containing macroscopic reinforcing agents
  • C04B35/78—Ceramic products containing macroscopic reinforcing agents containing non-metallic materials
  • C04B35/80—Fibres, filaments, whiskers, platelets, or the like
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  • C04B41/00—After-treatment of mortars, concrete, artificial stone or ceramics; Treatment of natural stone
  • C04B41/45—Coating or impregnating, e.g. injection in masonry, partial coating of green or fired ceramics, organic coating compositions for adhering together two concrete elements
  • C04B41/52—Multiple coating or impregnating multiple coating or impregnating with the same composition or with compositions only differing in the concentration of the constituents, is classified as single coating or impregnation
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  • C04B41/00—After-treatment of mortars, concrete, artificial stone or ceramics; Treatment of natural stone
  • C04B41/80—After-treatment of mortars, concrete, artificial stone or ceramics; Treatment of natural stone of only ceramics
  • C04B41/81—Coating or impregnation
  • C04B41/89—Coating or impregnation for obtaining at least two superposed coatings having different compositions
• • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
  • F16—ENGINEERING ELEMENTS AND UNITS; GENERAL MEASURES FOR PRODUCING AND MAINTAINING EFFECTIVE FUNCTIONING OF MACHINES OR INSTALLATIONS; THERMAL INSULATION IN GENERAL
  • F16D—COUPLINGS FOR TRANSMITTING ROTATION; CLUTCHES; BRAKES
  • F16D69/00—Friction linings; Attachment thereof; Selection of coacting friction substances or surfaces
  • F16D69/02—Composition of linings ; Methods of manufacturing
  • F16D69/023—Composite materials containing carbon and carbon fibres or fibres made of carbonizable material
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  • C04B2111/00—Mortars, concrete or artificial stone or mixtures to prepare them, characterised by specific function, property or use
  • C04B2111/00241—Physical properties of the materials not provided for elsewhere in C04B2111/00
  • C04B2111/00362—Friction materials, e.g. used as brake linings, anti-skid materials
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  • C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
  • C04B2235/02—Composition of constituents of the starting material or of secondary phases of the final product
  • C04B2235/30—Constituents and secondary phases not being of a fibrous nature
  • C04B2235/38—Non-oxide ceramic constituents or additives
  • C04B2235/3817—Carbides
  • C04B2235/3826—Silicon carbides
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  • C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
  • C04B2235/02—Composition of constituents of the starting material or of secondary phases of the final product
  • C04B2235/30—Constituents and secondary phases not being of a fibrous nature
  • C04B2235/48—Organic compounds becoming part of a ceramic after heat treatment, e.g. carbonising phenol resins
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  • C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
  • C04B2235/02—Composition of constituents of the starting material or of secondary phases of the final product
  • C04B2235/50—Constituents or additives of the starting mixture chosen for their shape or used because of their shape or their physical appearance
  • C04B2235/52—Constituents or additives characterised by their shapes
  • C04B2235/5208—Fibers
  • C04B2235/5216—Inorganic
  • C04B2235/524—Non-oxidic, e.g. borides, carbides, silicides or nitrides
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  • C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
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• • 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
  • Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
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  • Y10T428/00—Stock material or miscellaneous articles
  • Y10T428/249921—Web or sheet containing structurally defined element or component
  • Y10T428/249924—Noninterengaged fiber-containing paper-free web or sheet which is not of specified porosity

Definitions

• the present invention relates to C / C-SiC composite materials, that is to say having a carbon fiber reinforcement densified by a mixed carbon-silicon carbide matrix for friction elements such as brake discs and / or brake pads.
• the preforms are made from felts or basic fibrous textures such as fabrics, braids, knits, unidirectional layers of son, strands or cables, or complexes formed of several unidirectional layers superimposed with different directions and linked together by light needling.
• the bonding can be carried out by needling carried out individually on each layer, for example as described in document US-A-4,790,052.
• the base felts or textures used are made of carbon fibers or carbon precursor, the transformation of the precursor 0 being in the latter case carried out by heat treatment after preparation of the preform.
• Densification by the carbon matrix is carried out by chemical infiltration in the vapor phase or by the liquid route.
• Chemical vapor infiltration consists of placing the preform
• the gas phase usually comprises one or more hydrocarbons, for example methane, giving pyrolytic carbon by decomposition
• Carbon densification by the liquid route consists in impregnating the preform with a carbon precursor in the liquid state, for example a resin with a non-zero coke content, and in transforming the precursor into carbon by heat treatment.
• a carbon precursor for example a resin with a non-zero coke content
• the object of the present invention is to provide friction elements made of C / C-SiC composite, the cost and performance of which make them suitable for being used for brakes of railway vehicles or series or competition passenger cars, or still utility or industrial vehicles such as trucks.
• the invention aims to provide friction elements which provide regular and reproducible braking efficiency, under conditions of intense braking or not, and in a dry or wet environment.
• the present invention also aims to provide friction elements which wear slightly and are capable of being used in friction against materials of different natures.
• a friction element having at least one rubbing face and made of a composite material comprising a carbon fiber reinforcement and a matrix having at least one carbon phase and one phase.
• a friction element in which, at least in the vicinity of the or each rubbing face, the matrix comprises: a first phase containing pyrocarbon obtained by chemical vapor infiltration, in the vicinity of the fibers of the reinforcement, a second phase refractory obtained at least in part by pyrolysis from a liquid precursor, and a silicon carbide phase.
• Such a friction element may constitute a brake disc, or at least a brake disc friction lining, in a disc brake of a railway vehicle, a brake of a passenger car of series or competition cars, or a brake of industrial or utility vehicle.
• pyrocarbon phase is understood here to mean a pyrolytic carbon phase obtained by chemical vapor infiltration using one or more gaseous carbon precursors.
• refractory phase is meant here a carbon or ceramic phase.
• the composite material consists, by volume, of
• the matrix phase obtained by chemical vapor infiltration forms on the fibers a continuous coating of pyrocarbon of constant thickness and, at least initially, non-cracked. Pyrocarbon, by completely covering the fibers, can protect them during the formation of the silicon carbide matrix phase.
• the pyrocarbon obtained by chemical vapor infiltration has a fairly high thermal conductivity and provides the composite material with minimal thermomechanical properties making it possible in particular to fulfill the heat sink function in order to remove the calories generated by friction.
• the first matrix phase may comprise one or more layers of a material capable of protecting the pyrocarbon, as well as the underlying carbon fibers, against oxidation.
• An oxidation protection material capable of being deposited by chemical vapor infiltration is silicon carbide, a ternary Si-BC system or boron carbide.
• This material can be chosen from precursors of self-healing glass, that is to say, capable, after oxidation, of forming a glass which, on passing to a pasty state at the temperature of use of the friction element, clogs cracks appearing in the first matrix phase.
• Temperature gradient processes can be implemented by inductive coupling between an inductor and an armature located on one side of the preform to be densified or by direct coupling between an inductor and the preform.
• the isothermal and pressure gradient processes can be carried out by imposing a path on the precursor gas phase of the matrix either with directed flow under isobaric conditions, as described in French patent application 2 733 254, or with forced flow, as described in the international patent application WO 96/15288.
• the vaporized film processes consist of immersing the preform in a bath and heating the preform to a temperature such that a film of precursor vapor is formed in contact with the preform, the infiltration then taking place in the vapor phase, as described for example in US Patent 4,472,454.
• the second phase of carbon or ceramic matrix can be formed by a resin or pitch coke or by a ceramic residue of pyrolysis of ceramic precursor.
• Carbon precursor resins in the liquid state are chosen, for example, from thermosetting resins, such as phenolic, furan or epoxy resins, thermoplastic resins, pitches, or combinations thereof.
• Precursors of ceramic in the liquid state are for example polycarbosilane or polysilazane resins or their combinations.
• a matrix phase obtained by the liquid route, such as a resin coke has a relatively low thermal conductivity. This allows, from the start of braking, to reach a relatively high local temperature at the level of the friction face.
• the C / C-SiC composites have a coefficient of friction which is relatively low when cold, and higher when hot. A rapid transition to a high coefficient of friction then makes it possible to obtain good braking efficiency from very low speeds as well as in wet braking conditions.
• the refractory phase obtained by the liquid route represents only a part of the matrix, not in contact with the fibers, and does not unacceptably penalize the heat sink function.
• the second phase of the matrix is in the form of carbon pools or ceramics which lodge in the heart of the pores remaining after formation of the first matrix phase. This results in an increased possibility of closing the porosity with the silicon carbide of the last matrix phase. This closure of the porosity makes it possible to avoid the influence of a humid environment on the tribological properties.
• solid fillers for example a carbon powder or a ceramic powder, or a powder of a material for protection against oxidation.
• the solid charges can be introduced in the form of a suspension in the liquid precursor.
• the silicon carbide matrix phase is effective in reducing wear. It gives in particular to the composite material an increased hardness which makes it possible to associate it in friction with a wide range of different materials.
• the presence of SiC provides dry efficiency from the lowest braking energies.
• SiC provides increased resistance to oxidation, forming a barrier against ambient oxygen, at the heart of the composite material, and sealing off the porosity, at least to a large extent.
• the matrix has a silicon carbide phase which may be present only over a limited depth from the or each rubbing face.
• the core of the disc can be at least partially formed of composite material in which the matrix does not include a silicon carbide phase.
• the absence of silicon carbide phase gives the core less rigidity and preserves good mechanical behavior of the core of the disc for resuming braking forces which are generally transmitted by mechanical connection at the level of the inner or outer crown of the soul.
• a friction element according to the invention in the form of a friction lining, or wear lining, fixed on a metal disc core.
• the friction lining may have a silicon carbide phase throughout its thickness or over a limited depth from the rubbing face.
• the invention also aims to provide a method of manufacturing a friction element made of C / C-SiC composite material, a method of the type comprising the development of a carbon fiber preform having an accessible internal porosity and the densification of the preform by a matrix having at least one carbon phase and one silicon carbide phase.
• the densification of the preform comprises: a first chemical vapor infiltration step in order to fill between 10% and 55% of the volume of the preform with a first matrix phase containing pyrocarbon and forming a coating continuous on carbon fibers; a second stage of densification by impregnating the partially densified preform with a composition containing a precursor of refractory material in the liquid state and transformation of the precursor by heat treatment; and a third step of forming a silicon carbide matrix phase at least in the vicinity of the or each rubbing face.
• a first phase of matrix containing pyrocarbon and at least one layer of material for protection against oxidation can be formed by chemical vapor infiltration.
• the second densification step is carried out by impregnating the partially densified preform with a composition containing a precursor in the liquid state comprising at least one of the compounds chosen from resins and pitches giving a residue of carbon by pyrolysis and the resins giving a ceramic residue by pyrolysis.
• the composition may also contain suspended solid fillers such as carbon powders, ceramic powders or a material for protection against oxidation.
• a high temperature heat treatment is carried out after the second densification step and before the formation of the silicon carbide matrix phase.
• This heat treatment carried out at a temperature between approximately 1800 ° C. and approximately 2850 ° C., makes it possible to improve the thermal properties of the final material, in particular the thermal conductivity, and this in particular when the second matrix phase is made of carbon.
• the silicon carbide matrix phase can be formed in different ways:
• - siliciding by introducing silicon in the molten state and reacting it with carbon from at least one of the first two matrix phases; - siliciding by infiltration with a silicon carrier gas or by silicon vapor at high temperature, typically more than 1800 ° C; - siliciding by introducing solid charges in the form of silicon powder and heat treatment to react the silicon with carbon from the matrix;
• siliciding this is advantageously carried out simultaneously on several densified preforms, by having several densified preforms alternating with silicon sources comprising a majority phase based on silicon and a minority phase capable of forming a retention structure and draining the molten silicon, and heating to a temperature above the melting temperature of the silicon, so that, from each source, the molten silicon can migrate within the or each adjacent densified preform.
• silicon sources comprising a majority phase based on silicon and a minority phase capable of forming a retention structure and draining the molten silicon, and heating to a temperature above the melting temperature of the silicon, so that, from each source, the molten silicon can migrate within the or each adjacent densified preform.
• This process has the advantage of allowing control of the degree of siliciding.
• the quantity of silicon introduced into a densified preform through the or each rubbing face is determined as a function of a desired depth of siliciding, so as to form a matrix phase of silicon carbide over a depth limited from of the or each rubbing face.
• FIG. 2A, 2B and 2C are very schematic views of the microstructure of the composite material at different stages of the production of a friction element; and - Figures 3 and 4 show curves representing the variation of the coefficient of friction over time during tests of a friction element according to the invention, for different sliding speeds, different braking pressures, and in environments dry and wet.
• a friction element in the form of a brake disc made of C / C-SiC composite material it being understood that other types of friction elements can be made of the same material, such as brake pads and friction linings fixed on one side or both sides of disc cores with one or two rubbing faces.
• the production of a brake disc comprises (FIG. 1): - the preparation of an annular fibrous preform 10 made of carbon fibers,
• the fibrous preform 10 is produced by superimposing layers or strata of a fibrous texture 12 or of several different textures, and bonding the strata together by needling.
• the fibrous texture 12 can be constituted by a felt, a fabric, a knitted fabric, a unidirectional ply of threads, cables or strands, or a complex formed by several unidirectional plies superimposed with different directions and linked together by light needling.
• the different layers or strata are stacked and needled one by one as described in particular in document US-A-4,790,052, each needling pass being carried out with surface density of needle strokes and penetration depth of the needles substantially constant, in order to obtain a substantially uniform needling volume density.
• the fibrous texture 12 is made of carbon fibers or of carbon precursor fibers, for example of preoxidized polyacrylonitrile fibers. In the latter case, the transformation of the precursor into carbon is carried out by heat treatment carried out on the fibrous texture before or after preparation of the preform.
• An annular preform can be obtained by stacking and needling the flat layers and cutting the preform by punching at the end of the needling process. It is also possible to use precut annular strata. These methods are well known, so there is no need to describe them here in detail.
• the volume ratio of carbon fibers in the preform is preferably on average between about 15% and 35%.
• fiber volume ratio is understood here to mean the fraction of the apparent volume of the preform actually occupied by the fibers. It will be noted that the volume content of fibers may be lower in the vicinity of the rubbing faces, for example be lowered up to 10%, in comparison with the part of preform corresponding to the core of the disc. A too low volume rate of fibers at the level of the core of the disc penalizes the fibrous reinforcement function, therefore the mechanical properties of the core of the composite disc obtained, while a too high volume rate of fibers leads to a reduction in the porosity detrimental to densification.
• the preform therefore has an internal porosity of between 65% and 85% by volume and, in particular due to the method of production, this porosity is open, that is to say accessible from the outside.
• solid fillers can be introduced into the preform to occupy approximately 2 to 10% of the volume of the preform.
• These solid charges are in the form of refractory powder, that is to say carbon powder or ceramic powder.
• the first densification step is carried out by placing the preform in a chamber of a chemical vapor infiltration installation by isothermal-isobaric process.
• a reaction gaseous phase is introduced into the chamber where temperature and pressure conditions are established which favor the diffusion of the gaseous phase within the porosity of the preform, and the deposition of the matrix material on the fibers by reaction. of the gas phase in contact with the surface of the fibers.
• a pyrolytic carbon deposit is typically obtained from a gas phase comprising one or more hydrocarbons, for example methane.
• the temperature in the enclosure is typically maintained at a value between 950 ° C and 1150 ° C and the pressure between 1 kPa and 3 kPa.
• annular preforms are arranged in the chamber of the chemical vapor infiltration installation to be treated simultaneously.
• An example of loading several preforms into stacks, with a directed flow of the gaseous phase, is described in the French patent application No. 2,733,254 already cited.
• vapor infiltration processes can be used, for example temperature gradient processes, such as for example heating the preform by direct inductive coupling, pressure gradient processes, or vaporized film process.
• Chemical vapor infiltration leads to the formation of a continuous pyrolytic carbon coating 15 individually sheathing the fibers 14 (FIG. 2A).
• This first phase of densification of the preform is continued until preferably filling between 10% and 55% approximately of the volume of the preform with pyrocarbon.
• the quantity of pyrocarbon deposited on the fibers must be sufficient to give the disc the thermal conduction capacity required to ensure the functions of heat sink and mechanical strength.
• the quantity of pyrocarbon deposited must remain limited in order to allow sufficient porosity to remain in order to continue densification.
• the first densification step can also comprise the formation of one or more layers of material for protection against oxidation, covering the pyrocarbon or interspersed with layers of pyrocarbon.
• the material for protection against oxidation deposited by chemical vapor infiltration can be silicon carbide, boron carbide, or a ternary compound Si-BC.
• a material is chosen which, in an oxidizing medium, forms a self-healing glass at the temperature of use of the brake disc.
• the second densification step is carried out by the liquid route, impregnating the partially densified preform with a carbon or ceramic precursor in the liquid state and transforming the precursor by heat treatment.
• a carbon precursor is typically a resin having a non-zero coke content (the coke content being the percentage of carbon residue obtained after carbonization relative to the initial mass of the resin), or even a pitch.
• Resins which can be used are in particular thermosetting resins such as phenolic, furan and epoxy resins, thermoplastic resins, pitches or combinations thereof.
• a ceramic precursor is typically a resin such as a polycarbosilane or polysilazane resin or a combination thereof.
• the impregnation is carried out for example by immersing the preform in a bath of an impregnation composition formed by the resin possibly added with a solvent.
• the impregnation can be carried out under pressure or under vacuum in order to promote the penetration of the impregnation composition to the core of the remaining porosity of the preform.
• the impregnated preform is dried and then, after crosslinking of the resin, is subjected to a pyrolysis treatment while being brought to a temperature of approximately 900 ° C. to 1000 ° C.
• the second densification step is carried out in one or more successive impregnation-carbonization cycles, so as to fill approximately between 4% and 40% of the volume of the preform by the refractory matrix phase.
• the quantity of carbon or ceramic obtained by the liquid route must be sufficient to have, in the final composite material, a refractory matrix phase of low thermal conductivity promoting a rapid transition to a high coefficient of friction.
• a sufficient residual accessible internal porosity to allow the formation of the silicon carbide matrix phase.
• the refractory material obtained by the liquid route is carbon. It is in the form of clusters 16 of resin coke or pitch housed in the pores 17 of the partially densified preform (FIG. 2B).
• solid charges can be introduced in suspension in the liquid precursor.
• These solid fillers consist for example of a carbon powder, a ceramic powder, or a powder of material for protection against oxidation such as a self-healing glass precursor.
• a heat treatment at a temperature of between approximately 1800 ° C. and 2850 ° C. can be carried out immediately after the second matrix phase has been formed, in particular when the latter is made of carbon, in order to improve the thermal conductivity of the material.
• the silicon carbide matrix phase can be obtained by siliciding the preform, that is to say by introducing molten silicon or in the form of vapor within the remaining accessible porosity and reaction of the silicon with the pyrocarbon of the first matrix phase and with carbon from the second matrix phase.
• Different known siliciding techniques can be used, for example by immersion in a molten silicon bath or by connecting the densified preform to a molten silicon bath by a drain bringing the silicon to the preform by capillary action.
• a stack siliciding process of the type described in the above-mentioned French patent application No. 95 13458 is used.
• the silicon sources 18 consist of a majority phase of silicon, or based on silicon, for example in the form of powder, and of a minority phase capable of forming a structure for retaining and draining the molten silicon.
• the minority phase is for example a rigid honeycomb structure such as a honeycomb structure 18a whose cells are filled with powdered silicon 18b.
• the minority phase may consist of a three-dimensional network with high porosity, such as a felt formed from short fibers, or a non-rigid cellular texture, such as a foam, the minority phase extending throughout the volume. from the silicon source.
• the siliciding treatment is carried out by bringing the stack of preforms 10 ′ and silicon sources 18 to a temperature for example between 1410 ° C. and 1600 ° C., under a reduced pressure, for example less than 50 kPa, and under an atmosphere. neutral, for example under argon or under vacuum.
• the silicon contained in the sources 18 reaches its melting point, it migrates to the adjacent preforms through their surfaces in contact with the sources 18. From a source 18, this migration takes place by gravity towards a preform 10 ' located below and by capillary action towards a preform 10 'situated above.
• the molten silicon infiltrating into the remaining porosity of the densified preforms 10 ′ forms silicon carbide (SiC) 19 by reaction with carbon, both the pyrocarbon 15 and that 16 obtained by liquid means (FIG. 2c).
• SiC silicon carbide
• An SiC layer is thus formed up to the heart of the densified preform, the porosity of the latter not being closed.
• This layer depending on the remaining porosity of the densified preform, before siliciding, can have a thickness of a few microns to more than 10 microns, if the source of silicon is sufficient. In this way, the disc obtained is provided with internal protection against oxidation by SiC 19 forming a barrier against oxygen from the surrounding medium.
• the SiC gives the latter hardness and resistance to wear. It will also be noted that, by reaction of the silicon with the pyrocarbon which covers the surface of the pores 17 as well as with the carbon of the grains 16 which partially occupy these same pores, the SiC obtained 19 leads to at least partial sealing of the pores, therefore sealing of the composite material. This results in less influence in a humid environment.
• the disc obtained 20 is machined to its final dimensions, in particular by rectification of its rubbing face or faces and formation at its periphery, or on its internal surface, of notches (not shown) making it possible to connect the disc 20 with a member of which it is integral in rotation.
• the machining of the disc can be carried out before siliciding.
• the faces of the silicon sources 18 used then have shapes complementary to those of the faces of the discs.
• the siliciding treatment is carried out so as to occupy between 10 and 35% of the volume of the preform densified with silicon carbide. Porosity residual of the densified preform is preferably reduced to a value of less than 10% by volume after siliciding.
• the disc 20 obtained then comprises, in volume:
• Such a material has a very low density, between 1,600 and 2,100 kg / m ⁇ , a coefficient of thermal expansion less than 2.10-6 p ar o j and a thermal diffusivity greater than that of steels.
• the friction levels are stable and reproducible, without sudden discontinuity and without significant influence of the surrounding stresses.
• Chemical vapor infiltration of SiC is a well known process, the gaseous precursor usually being methyltrichlorosilane (MTS).
• MTS methyltrichlorosilane
• the process can be carried out under isothermal-isobaric conditions, or with a temperature gradient or with a pressure gradient.
• the densified preform can be heated by direct coupling between the preform and an inductor.
• Charges can be inserted by vacuum impregnation with a suspension of SiC powder in a liquid. It can be supplemented by a final stage of chemical vapor infiltration.
• Discs and pads for rail vehicle disc brakes are made as follows.
• the fibrous preforms are produced by needling superimposed layers of carbon fiber felt and cutting of the preforms so as to obtain annular disc preforms with a thickness equal to 60 mm, an internal diameter equal to 235 mm and an external diameter equal to 660 mm, and parallelepipedal preforms of pads of dimensions 15 mm x 8 mm x 40 mm.
• the volume rates of fibers in the preforms are equal to 25%
• a first stage of densification of the preforms by chemical vapor infiltration is carried out from a gas phase consisting of a mixture of natural gas and propane, the temperature being maintained at approximately 1000 ° C. and the pressure at approximately 1.3 kPa. Chemical vapor infiltration is continued until filling approximately 42% of the volume of the preforms with pyrocarbon.
• the partially densified preforms are impregnated with a furan resin, then heat treated, in order to form a second phase of resin coke matrix.
• the impregnation is carried out under vacuum by immersion in a resin bath. After drying and crosslinking of the resin, it is charred at a temperature of 900 ° C.
• the resin impregnation is carried out so as to obtain a resin coke occupying 17% of the volume of the preforms.
• the preforms thus densified with carbon have an accessible residual porosity of approximately 16% by volume.
• the siliciding is carried out by the stack siliciding method described in the aforementioned French patent application No. 95 13458.
• the quantity of molten silicon introduced into the densified preforms is chosen so as to obtain a SiC matrix phase representing approximately 20% by volume of the siliconized composite material, which corresponds to a deposit of SiC of more than 10 microns thick.
• the friction elements (discs and pads) thus obtained have a density of approximately 1,950 kg / nv, and a final porosity of approximately 10% and their constitution, in volume, is as follows: - approximately 25% of fibers of carbon,
• a brake made up of a disc and pads thus produced is tested on a dry braking bench, with sliding speeds variable between 5 and 100 m / s.
• the coefficient of friction is measured for different sliding speeds and at different times of the test.
• the hatched area shows the domain in which all the measured values lie. The braking efficiency is therefore substantially unchanged in a wide range of sliding speeds.
• a similar brake is tested in dry braking at an imposed constant sliding speed of 20 m / s. After running in for 3 min with the application of a braking pressure of 0.55 MPa, the coefficient of friction is measured when three braking pressures are applied equal to 0.25 MPa, 0.55 MPa and 1 MPa respectively steps of 3 min duration.
• Curve A in Figure 4 shows the variation of the braking coefficient measured as a function of time.
• a similar brake is tested under the same conditions with the exception of the environment which is humid, the brake being permanently sprayed with water.
• the curve B in FIG. 4 shows the variation of the braking coefficient measured as a function of time.
• Curves A and B show the excellent behavior of the friction elements in siliconized C-C composite produced in accordance with the invention.
• the coefficient of friction is remarkably stable, for different braking pressures, and, on the other hand, practically identical values are measured in dry environment and in humid environment. Thus, constant braking efficiency is provided under these different conditions of use.
• Discs for high-end series passenger vehicle disc brakes are produced as follows.
• the fiber preforms are produced by needling superimposed layers of carbon fiber felt and cutting of the preforms so as to obtain annular disk preforms with a thickness equal to 35 mm, an internal diameter equal to 160 mm and an external diameter equal to 360 mm.
• the volume content of fibers in the preforms is 22%.
• a first stage of chemical vapor infiltration is carried out by alternating deposits of layers of pyrocarbon and deposits of thin layers (thickness of about 0.5 micron) of boron carbide B4C, up to filling 40% of the volume. initial preforms.
• the partially densified preforms are impregnated with a phenolic resin and then heat treated at 900 ° C. in order to form a second phase of resin coke matrix.
• the impregnation is carried out so as to fill approximately 18% of the volume of the preforms with resin coke, so that the residual porosity of the preforms is approximately 10% by volume.
• the siliciding is carried out as in Example 1, but over a limited thickness from each rubbing face, using silicon sources voluntarily containing an insufficient quantity of silicon to carry out core siliciding.
• the discs obtained have a variable composition:
• the composition, by volume is 22% of carbon fibers, 25% of pyrocarbon / B4C, 5% of resin coke and approximately 33% of SiC, the porosity residual being around 7%, - in the rest of the disc, in particular in the central part of the core, the composition, by volume, is 22% of fiber content, 40% of pyrocarbon / B4C, 18% of coke of resin and approximately 0% of silicon carbide, the residual porosity being 10%.
• the discs obtained have a lower apparent density, of the order of
• the fibrous preforms are produced by needling superimposed layers of carbon fiber felt and cutting the preforms so as to obtain annular disc preforms with a thickness equal to 32 mm, an internal diameter equal to 180 mm and an external diameter equal to 320 mm.
• the volume content of fibers in the preforms is equal to 30%.
• a first chemical vapor infiltration step is carried out to form a pyrocarbon matrix phase occupying 30% of the volume of the preform.
• the partially densified preforms are impregnated with a polycarbosilane resin and then heat treated to form a second phase of SiC matrix consisting of a pyrolysis residue and occupying 12% of the volume of the preform.
• the preforms thus densified are machined and a silicon carbide matrix phase is introduced by chemical vapor infiltration under isothermal-isobaric conditions until occupying 20% of the volume of the preforms by SiC.
• the residual porosity of the discs obtained is 8% by volume.
• the discs obtained have a lower apparent density, but tribological properties comparable to those of the discs of set 1, in the wear parts.
• Fibrous preforms are produced by needling superimposed layers of carbon fiber felt and cutting of the preforms so as to obtain annular preforms in which the volume content of fibers is equal to 23%.
• a first chemical vapor infiltration step is carried out to form a pyrocarbon matrix phase occupying 45% of the volume of the preform.
• the partially densified preforms are impregnated with a phenolic resin and then heat treated at 900 ° C. in order to form a second phase of resin coke matrix occupying 10% of the volume of the preform.
• the preforms thus densified are heat treated at 2800 ° C., in order to improve the thermal conductivity of the carbon phases of the matrix.
• a third step of chemical vapor infiltration is carried out to form a matrix phase of silicon carbide (SiC) occupying 15% of the volume of the preform.
• the discs obtained have excellent tribological properties.

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• 1996
  • 1996-10-14 EP EP96402184A patent/EP0835853A1/fr not_active Withdrawn
• 1997
  • 1997-10-14 WO PCT/FR1997/001831 patent/WO1998016484A1/fr not_active Ceased
  • 1997-10-14 UA UA99042046A patent/UA54452C2/uk unknown
  • 1997-10-14 DE DE69726604T patent/DE69726604T3/de not_active Expired - Lifetime
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