KR20200045723A - Fabrication Method of Carbon Composite Using melt infiltration method - Google Patents

Abstract

According to the present invention, a carbon composite manufacturing method comprises: a step (a) of providing a carbon fiber preform; and a step (b) of filling the carbon fiber preform with a mixture containing heat-resistant ceramic particles having bimodal distribution and a carbon source, and heat-treating the mixture to densify the same.

Description

{Fabrication Method of Carbon Composite Using melt infiltration method}

The present invention relates to a method for producing a carbon composite material using a melt impregnation method, and in detail, to a method for producing a carbon composite material having improved strength.

Materials for use in the aerospace sector are materials that require high physical and chemical properties such as strength, modulus of elasticity, fracture toughness, oxidation resistance, and abrasion resistance. Accordingly, research has been conducted based on the complexization between various fibrous and matrix materials.

The preform used for this complexing is a fibrous reinforcing material shaped into a certain shape, and a fiber-based composite can be manufactured by forming and densifying carbon or high-temperature ceramic in the pores of the preform.

As proposed in Korean Patent Registration No. 0503499, as a method of manufacturing a preform, a fabric is fabricated in which fibers are two-dimensionally arranged by felt or weaving, which are irregularly arranged fibers, and then a binding force is provided in the thickness direction by needle punching. How to do is known.

However, when using an irregular fiber felt, needle punching is easily performed, but there is a limit to improving the fiber density. In addition, in the case of manufacturing a preform by laminating the fiber layers arranged regularly by weaving, there is a limit in strengthening the binding force between the fiber layers by needle punching as the fibers are damaged during needle punching.

Furthermore, in the case of using a high elasticity (high ductility) fiber layer for easy punching and strengthening the interlayer binding force during needle punching, interlayer peeling occurs due to a volume change occurring in the process of converting the high elastic fiber layer to carbon fiber after needle punching Thereby, there is a problem of deteriorating the mechanical properties of the preform.

Republic of Korea Registered Patent No. 0503499

It is an object of the present invention to provide a method for producing a carbon composite material having improved strength and improved interlayer binding.

Another object of the present invention is to provide a method for producing a carbon composite material having improved mechanical strength and improved heat resistance.

The method for manufacturing a carbon composite material according to the present invention comprises the steps of: a) providing a carbon fiber preform; And b) filling the carbon fiber preform with a mixture containing heat-resistant ceramic particles having a carbon source and a bimodal distribution, and heat-treating the resulting mixture to density.

In the method of manufacturing a carbon composite material according to an embodiment of the present invention, the step a) includes a coke-coated fiber sheet and a step of manufacturing a sheet laminate that is bound between sheets by needle punching. .

In the method for manufacturing a carbon composite material according to an embodiment of the present invention, the coke coated fiber sheet may include a coke coated carbon fiber sheet or a coke coated oxypan fiber sheet.

In the method for manufacturing a carbon composite material according to an embodiment of the present invention, the coke coated fiber sheet may be prepared by impregnating a fiber sheet in a phenol resin solution containing coke, an epoxy resin solution, or a mixed resin solution thereof. .

In the method for producing a carbon composite material according to an embodiment of the present invention, the volatile content of the coke may be 8 to 12% by weight.

In the method for producing a carbon composite material according to an embodiment of the present invention, the heat-resistant fiber sheet may contain 5 to 15% by weight of coke.

In the method for manufacturing a carbon composite material according to an embodiment of the present invention, in step b), the carbon source may be a pitch.

In the method for producing a carbon composite material according to an embodiment of the present invention, after step b), c) forming a surface coating layer comprising a heat-resistant ceramic having a bimodal particle size distribution on the surface of the densified carbon fiber preform Step; may further include.

In the method of manufacturing a carbon composite material according to an embodiment of the present invention, the heat-resistant ceramic may be one or more ceramics selected from carbide-based, boride-based, nitride-based, and silicide-based.

The present invention includes a carbon composite material produced by the above-described manufacturing method.

Carbon composite material according to an embodiment of the present invention, as the carbon fiber preform is produced by laminating coke-coated fiber sheets and mechanically binding the sheets to each other by needle punching, inter-sheet interfacial peeling is prevented and has strong binding force , There is an advantage that can improve the mechanical strength of the carbon composite material.

In addition, the carbon composite material according to an embodiment of the present invention is based on a carbon fiber preform-coated fiber sheet, so that the pitch is easily and homogeneously permeated into fine pores between fibers by coke to strongly bond between the preform and the matrix. It has the advantage of being able to manufacture a carbon composite material.

In addition, the method of manufacturing a carbon composite material according to an embodiment of the present invention is characterized by having improved strength by suppressing the propagation of cracks in the matrix by the matrix containing heat-resistant ceramic particles and carbon having a bimodal distribution.

The method for manufacturing the carbon composite material of the present invention will be described in detail. At this time, unless there are other definitions in the technical terms and scientific terms to be used, it means that those skilled in the art to which the present invention pertains have the meanings commonly understood, and unnecessarily obscure the subject matter of the present invention in the following description. Descriptions of possible known functions and configurations are omitted.

The method for manufacturing a carbon composite material according to the present invention comprises the steps of: a) providing a carbon fiber preform; And b) filling the carbon fiber preform with a mixture containing heat-resistant ceramic particles having a carbon source and a bimodal distribution, and heat-treating the resulting mixture to density.

In the method of manufacturing a carbon composite material according to the present invention, when the heat-resistant ceramic particles have a bimodal distribution, when the cracks generated in the carbon fiber composite propagate the matrix, the propagation of cracks is prevented by the ceramic particles having a relatively large particle diameter. As it becomes, it is advantageous because it can enhance the mechanical strength of the composite material. That is, when the crack tip of the generated and propagated crack reaches the ceramic particle having a relatively large particle size, the propagation path of the crack must be changed along the interface of the relatively large particle, so that the relatively coarse ceramic particle Can effectively suppress crack propagation, and the mechanical strength of the composite can be significantly increased by suppressing crack propagation.

In the method of manufacturing a carbon composite material according to an embodiment of the present invention, step a) includes a coke-coated fiber sheet and a step of manufacturing a sheet laminate that is bound between sheets by needle punching.

In this case, the coke-coated fiber sheet may include a coke-coated carbon fiber sheet or a coke-coated heat-resistant fiber sheet. The heat-resistant fiber of the coke-coated heat-resistant fiber sheet may be a polyacrylonitrile (PAN) -based fiber or a rayon-based fiber, and is preferably an oxi-PAN (Oxidized Polyacrylonitrile) fiber. Oxypan fiber has an excellent carbonization rate and is advantageous because it can be converted to carbon fiber having excellent specific strength and inelasticity during carbonization heat treatment. According to one advantageous example, the coke-coated heat-resistant fiber sheet can be a coke-coated oxypan fiber sheet. Coke coated on the heat-resistant fiber sheet can have stronger interfacial bonding force between the heat-resistant fiber sheet and the carbon fiber sheet, and can suppress swelling due to cohesiveness of the coke during carbonization. Interfacial peeling can be prevented, and a carbon fiber preform having improved strength can be produced. In addition, the coke coated on the heat-resistant fiber sheet easily improves the strength of the preform itself as well as the adhesion between the preform and the matrix by allowing the carbon source used for densification, especially the pitch, to easily penetrate the micropores between the fibers in the preform. Can increase the density of the carbon composite material.

Coke coated on a fiber sheet, advantageously a heat resistant fiber sheet, may have a volatile content of 8 to 12% by weight. When the coke has an volatile content of 8 to 12% by weight, the swelling phenomenon can be substantially completely suppressed by cohesiveness of the coke during carbonization, and it is advantageous because the sheets can be strongly bound. As is known, the volatile content of the coke can be controlled by adjusting the heat treatment temperature and time of the pitch, and as a specific example, the above-mentioned volatile content is obtained by heat treating the pitch at a temperature of 400 to 500 ° C for 1 to 3 hours. Coke can be produced.

The coke-coated heat-resistant fiber sheet may contain 5 to 15% by weight of coke, and this coke content improves the cohesion between sheets of the sheet laminate by coke and also provides a carbon source, especially pitch, even between the fine gaps of the fibers forming the preform. Is a content that allows homogeneous filling and at the same time a needle punching can be easily performed.

As described above, the sheet laminate may include a carbon fiber sheet, a heat-resistant fiber sheet, or a carbon fiber sheet and heat-resistant fiber sheet that are alternately stacked with each other. As described above, the carbon fiber sheet or the heat-resistant fiber sheet is coke coated. It may be, and according to an advantageous example, the sheet laminate may include an alternately laminated carbon fiber sheet and a coke coated heat resistant fiber sheet.

At this time, the coke-coated fiber sheet may be prepared by impregnating a fiber sheet in a phenol resin solution containing coke, an epoxy resin solution or a mixed resin solution thereof. When a) step is described in more detail on the basis of an advantageous example, step a) is performed by impregnating a heat-resistant fiber sheet in a phenol resin solution containing coke, an epoxy resin solution, or a mixed resin solution thereof, thereby forming a coke-coated heat-resistant fiber sheet. Manufacturing; A step of alternately laminating carbon fiber sheets and coke-coated heat-resistant fiber sheets and needle punching to produce mechanically bonded laminates; And preparing a carbon fiber preform by carbonization heat treatment of the laminate.

The carbon fiber sheet and the heat-resistant fiber sheet can be filament yarns or staple fibers independently of each other, and the carbon fiber sheet and the heat-resistant fiber sheet are independent of each other, such as woven fabrics, non-woven fabrics, knitted fabrics, multi-axis knitted fabrics, unidirectional array fabrics, or webs. (web) may be in the form, but is not limited thereto. In addition, the alternately stacked carbon fiber sheet may be a stacked sheet in which one or more carbon fiber sheets are stacked, and the alternating heat-resistant fiber sheet may also be stacked in one or more heat-resistant fiber sheets independently of the carbon fiber sheet. It may be a sheet, but is not limited thereto. In addition, the number of carbon fiber sheets contained in the laminate: the number of heat-resistant fiber sheets may be 1: 1 to 0.2, but is not limited thereto. When the carbon fiber sheet and the heat-resistant fiber sheet are alternately stacked, the stacking direction is 30 °, 45 °, 60 °, 90 °, 120 °, 135 when the other sheet is arranged based on the fiber alignment direction of one of the adjacent sheets. It can be stacked to be °, 150 ° or 180 °, and advantageously the fiber arrangement can be stacked such that they cross vertically or symmetrically. A preform having uniform mechanical properties may be manufactured through such lamination, but the present invention is not limited by a specific lamination direction. The thickness of the carbon fiber sheet and the heat-resistant fiber sheet may be 0.1 to 10 mm, respectively, and may be substantially 0.5 to 5 mm to improve productivity and to achieve stable interlayer bonding between needles during needle punching, but is not limited thereto. no.

The needle punching process may be a process in which the binding is imparted in the vertical direction between the fibers inside the laminate by vertically moving the needle in the thickness direction of the sheet laminate. Needles can be implemented by passing a plurality of needles fixed to the punching head for up and down movements through the guide plate and through the inside of the stack, and the needles have a barb or needle tip protruding from the side. It may be a fork (fork) shape, but is not limited thereto.

In addition, the stack of sheets during needle punching can be needle punched in a compressed state by a compression roller or a compression plate, which is advantageous for increasing the strength of the carbon fiber preform. As a specific example, the fiber density of the laminate mechanically bound by needle punching may be 0.2 to 0.6 g / cm ³ , but is not limited thereto.

The carbonization heat treatment of the laminate mechanically bound by needle punching may be performed at 500 to 2000 ° C. in an inert atmosphere (argon, nitrogen, helium or a mixed gas atmosphere thereof).

After step a), step b) for carbon fiber densification may be performed. In step b), the heat-resistant ceramic particles may have a particle size distribution of at least bimodal that satisfies relational expression 1 below. That is, the heat-resistant ceramic particles dispersed in the carbon source and filled in the preform may have a bimodal particle size distribution, and may satisfy relational expression 1 below.

(Relationship 1)

2 ≤ D ₂ / D ₁ ≤ 50

D ₁ is the center size of the peak with the smallest center size of the peak in the bimodal particle size distribution of the heat-resistant ceramic particles, and D ₂ is the center size of the peak with the largest center size of the peak in the same particle size distribution.

It can be located homogeneously dispersed in the preform, in order to improve the mechanical strength by suppressing crack propagation, D ₂ / D ₁ is preferably 2 to 50, advantageously 10 to 50, and the heat-resistant ceramic of D ₂ has a long and short axis ratio It is more advantageous that the (aspect ratio) is an elongated particle shape of 2 to 10. In this case, the particle size distribution of the heat-resistant ceramic belonging to D ₁ and / or D ₂ may mean a distribution of diameters converted into circles having the same area as one cross-sectional area based on random cross-sectional shapes of particles.

As a practical example, the coarse particles, which are particles belonging to D ₂ , may have an average particle diameter of 10 to 50 μm, D ₁ may have an average particle diameter satisfying 10 to 50 in relation 1, advantageously D ₂ / D ₁ have. In addition, in terms of maximizing a desired crack propagation inhibitory effect without contacting each other between coarse particles, the heat-resistant ceramic may have a weight ratio of fine particles belonging to D ₁ : coarse particles belonging to D ₂ to be 1: 0.05 to 0.4, and substantially It may be 0.1 to 0.3.

The heat-resistant ceramic particles may be carbide-based, boride-based, nitride-based and / or silicide-based. Specifically, the carbide system may be one or two or more selected from silicon carbide, hafnium carbide, tantalum carbide, tungsten carbide, and zirconium carbide. One or two or more may be selected from ride, vanadium boride and hafnium boride, and the nitride system may be one or two from silicon nitride, aluminum nitride, hafnium nitride, zirconium nitride and boronitride. More than one species may be selected, and the silicide system may be one or two or more selected from molybdenum silicide, zirconium silicide, tantalum silicide, and hafnium silicide, but the present invention is not limited by specific materials of heat-resistant ceramics.

The mixture of carbon source and heat-resistant ceramic particles used for densification may contain 30-50% by weight of heat-resistant ceramic particles and 70-50% by weight of carbon sources to obtain a significant mechanical strength enhancement effect by the ceramic particles.

Carbon sources used for densification may include pitch, phenol resin, epoxy resin, and the like, but in an advantageous example, the carbon source may be pitch, and the pitch may include isotropic pitch, mesoface pitch, or a mixture thereof. Pitch is more advantageous than other liquid carbon sources (for example, furan resin, phenol resin, etc.) in terms of high carbon yield, low viscosity, and excellent wettability, and is also easy to fine pores of carbon fiber preforms based on coke coated fiber sheets. It is advantageous to be able to soak. The softening point of the pitch may be 50 to 350 ° C, specifically 60 to 300 ° C, and more specifically 60 to 240 ° C, but is not limited thereto.

Thereafter, a heat treatment for carbonizing a carbon source, that is, as a representative example, a carbon source including a pitch may be pressure sintering, and may be specifically performed at 500 to 1500 ° C. under a pressure of 100 to 500 bar, but is not limited thereto.

After pressure sintering is performed (collectively referred to as primary densification), additional densification (collectively referred to as secondary densification) may be further performed to improve density, and secondary densification is performed using a pitch of a conventional liquid carbon source. The impregnation method, a gas phase infiltration method using a carbon source of the gas phase, or a pitch impregnation method and a gas phase infiltration method may be used. In detail, the pitch impregnation method may be performed by infiltrating a carbon source such as a phenolic resin, coal, or petroleum pitch into a primary density preform, followed by carbonization at a temperature of 500 to 1700 ° C. Independently, the gas phase infiltration method provides primary density by supplying C1 to C3 hydrocarbon gas such as methane and propane at a temperature higher than the thermal decomposition temperature of hydrocarbon gas (for example, 700 to 1500 ° C) to the primary density preform. Pyrolysis carbon may be directly deposited on the preform, but is not limited thereto.

In addition, before impregnating the carbon fiber preform with a mixture containing pitch and heat-resistant ceramic particles, forming a thermally decomposed carbon in the carbon fiber preform using a gas phase penetration method; after being performed, impregnation of the mixture may be performed. In this case, the carbon fibers of the carbon fiber preform can be protected by pyrolysis carbon.

In addition, after the thermal decomposition carbon is formed, a graphitization treatment for heat treatment at 2000 to 2500 ° C. for graphitization may be further performed, but the present invention is not limited thereto.

The manufacturing method according to an embodiment of the present invention may further include; after step b), forming a surface coating layer comprising a heat-resistant ceramic having a bimodal particle size distribution on the surface of the carbon fiber preform on which the matrix is formed.

The heat-resistant ceramic contained in the surface coating layer of the composite material may be carbide-based, boride-based, nitride-based and / or silicide-based. Specifically, the carbide system may be one or two or more selected from silicon carbide, hafnium carbide, tantalum carbide, tungsten carbide, and zirconium carbide. One or two or more may be selected from ride, vanadium boride and hafnium boride, and the nitride system may be one or two from silicon nitride, aluminum nitride, hafnium nitride, zirconium nitride and boronitride. More than one species may be selected, and the silicide system may be one or two or more selected from molybdenum silicide, zirconium silicide, tantalum silicide, and hafnium silicide, but the present invention is not limited by specific materials of heat-resistant ceramics.

The heat-resistant ceramic contained in the surface coating layer of the composite material may have a particle size distribution of at least bimodal that satisfies at least the following relationship (1).

(Relationship 1)

2 ≤ D ₂ / D ₁ ≤ 50

D ₁ is the center size of the peak with the smallest center size of the peak in the particle size distribution of bi-modal or more of the heat-resistant ceramic, and D ₂ is the center size of the peak with the largest center size of the peak in the same particle size distribution. Advantageously, D ₂ / D ₁ can be from 10 to 50.

When the heat-resistant ceramic has a bimodal distribution, when the thermal crack is generated and propagated in the coating layer due to a difference in the thermal expansion coefficient, the propagation of cracks is prevented by the ceramic particles having a relatively large particle diameter, and thus the mechanicality of the coating layer It is advantageous because it can enhance the strength and prevent crack propagation to the preform side filled with the matrix and / or the surface side of the coating layer. That is, when the crack tip of the crack generated and propagated in the coating layer reaches the ceramic particle having a relatively large particle size, the propagation path of the crack must be changed along the particle interface of the relatively large particle, so that Korean ceramic particles can effectively suppress crack propagation.

In terms of improving mechanical strength by suppressing crack propagation, D ₂ / D ₁ is preferably 2 to 50, and advantageously 5 to 50, and the heat resistant ceramic of D _{2 has} an aspect ratio of 2 to 10 It is more advantageous to have an elongated particle shape. In this case, the particle size distribution of the heat-resistant ceramic belonging to D ₁ and / or D ₂ may mean a distribution of diameters converted into circles having the same area as one cross-sectional area based on random cross-sectional shapes of particles. As a practical example, the coarse particles, which are particles belonging to D ₂ , may have an average particle diameter of 1 to 50 μm, and D ₁ may have an average particle diameter satisfying 5 to 50 in relation 1, advantageously D ₂ / D ₁ have. In addition, in terms of maximizing a desired crack propagation inhibitory effect without contacting each other between coarse particles, the heat-resistant ceramic may have a weight ratio of fine particles belonging to D ₁ : coarse particles belonging to D ₂ to be 1: 0.05 to 0.4, and substantially It may be 0.1 to 0.3.

In the step of forming the heat-resistant ceramic coating layer having a particle size distribution of bimodal or higher, the carbon preform (hereinafter, the densityd preform) filled with the matrix obtained in step b) and coarse particles, that is, the heat-resistant ceramic particles belonging to D ₂ and the binder Fixing the coarse particles on the densified preform surface by contacting a ceramic dispersion containing; And forming a surface coating layer by depositing a heat-resistant ceramic on the densified preform having coarse particles fixed on the surface. The contact between the ceramic dispersion and the densified preform can be performed using a method such as spraying, impregnation, or application, and the preform densified through the concentration of the ceramic particles in the ceramic dispersion, the amount of contact (the amount of application), the number of times of contact, etc. Of course, the density (number / unit area) of the ceramic particles located at can be adjusted. As a practical example, the ceramic dispersion is an organic binder, polyvinylidene fluoride, polyvinylidene fluoride-hexafluoropropylene copolymer, polyvinylidene fluoride-trichloroethylene copolymer, polymethylmethacrylate, polyacrylic Nitrile, polyvinylpyrrolidone, polyvinyl acetate, polyethylene-vinyl acetate copolymer, polyethylene oxide, cellulose acetate, cellulose acetate butyrate, cellulose acetate propionate, cyanoethyl pullulan, cyanoethyl polyvinyl alcohol, cyano 1 to 5 of noethyl cellulose, cyanoethyl sucrose, pullulan, carboxyl methyl cellulose, styrene-butadiene copolymer, acrylonitrile-styrene-butadiene copolymer, polyimide, polytetrafluoroethylene or mixtures thereof Can contain weight percent , But the invention is not limited to this. In addition, the ceramic dispersion may contain 10 to 30% by weight of ceramic particles, but is not limited thereto. At this time, the dispersion medium of the ceramic dispersion can be used as long as the organic binder is dissolved and is easily volatile removed.

Fine heat-resistant ceramics can be formed by depositing heat-resistant ceramics on a densified preform surface with coarse particles surface-fixed. The deposition of the heat-resistant ceramic uses a conventional vapor deposition method for producing a ceramic thin film, such as conventional chemical vapor deposition (CVD) such as plasma-assisted chemical vapor deposition, or conventional physical vapor deposition (PVD) such as sputtering. Of course, it can be performed. At this time, it is a matter of course that the organic binder remaining with the coarse particles on the surface of the preform densityd by plasma or heating during deposition can be carbonized or decomposed and removed. As an example of practical chemical vapor deposition using silicon carbide as an example, fine heat-resistant ceramic particles may be performed at 1100 to 1300 ° C using a silicon precursor gas such as methyltrichlorosilane (MTS), but the present invention is limited by these specific deposition conditions. It does not work.

The present invention includes a carbon composite material produced by the method for manufacturing the composite material described above.

The carbon composite material according to the present invention may have improved density and strength, and further, the carbon fiber preform may be densified with a composite matrix of heat-resistant ceramic particles and carbon having a bimodal distribution.

In addition, the carbon composite material according to an embodiment of the present invention is a densified preform; And a surface coating film including a heat-resistant ceramic having the above-described bimodal particle size distribution.

(Example 1)

The woven PAN-based carbon fiber sheet and the carbon fiber web were alternately stacked, but lamination was performed such that the fiber arrangement between the woven carbon fiber sheets adjacent to each other with the carbon fiber web interposed therebetween was laminated, and mechanical bonding was performed by binding by needle punching. To prepare a carbon fiber preform that is a laminated body (60 mm).

In order to densify (primary density) the prepared carbon fiber preform, a pitch containing 40% by weight of SiC particles is melted and vacuum-impregnated in the prepared carbon fiber preform, and re-impregnated at an atmospheric pressure of 350 ° C. to 300 bar. Pressure-sintered at 650 ° C. under pressure to prepare a primary density preform. At this time, the SiC particles mixed with the pitch were fine SiC particles having an average particle diameter of 2 μm: aspect ratio 4 and coarse SiC particles having an average particle diameter of 32 μm were mixed particles at a weight ratio of 1: 0.15.

Thereafter, the primary density preform was impregnated again with a melt pitch, followed by carbonization heat treatment at 1000 ° C. and graphitization treatment at 2100 ° C. twice to prepare a carbon fiber composite.

The carbon fiber composite material is impregnated into a dispersion containing 3% by weight of carboxyl methyl cellulose and 10% by weight of SiC powder (average particle size = 17 μm, aspect ratio = 2.4), recovered and dried to coarse SiC particles on the surface of the substrate Was placed. Subsequently, MTS (methyltrichlorosilane) and H ₂ mixed gas (H ₂ / TMS = 3) were supplied at a temperature of 1400 ° C. (800 sccm) to perform deposition, thereby preparing a 40 μm thick SiC coating film. As a result of observing the surface of the SiC coating film prepared through the scanning electron microscope, it was confirmed that the SiC grains of the angular shape having an average size of about 5 μm were formed by deposition, and the coarse particles per unit area occupied in the cross section of the coating film through the scanning electron microscope It was confirmed that the area (area by coarse particles / total cross-sectional area * 100) was about 8%.

The composite prepared in Example was maintained at 1000 ° C. in the air to test oxidation resistance, and as a result of measuring the mass loss after the oxidation resistance test, it was confirmed that the weight reduction of the composite prepared in Example was only about 17%. .

As described above, in the present invention, it has been described by specific matters and limited embodiments and drawings, which are provided to help the overall understanding of the present invention, but the present invention is not limited to the above embodiments, and the present invention Various modifications and variations are possible from those skilled in the art to those skilled in the art.

Therefore, the spirit of the present invention is limited to the described embodiments, and should not be determined, and all claims that are equivalent to or equivalent to the claims, as well as the claims described below, will belong to the scope of the spirit of the present invention. .

Claims (8)

a) providing a carbon fiber preform; And
b) filling the carbon fiber preform with a mixture containing heat-resistant ceramic particles having a carbon source and a bimodal distribution, and heat-treating the mixture to make it dense;
Method of manufacturing a carbon composite comprising a. According to claim 1,
Step a) is
A method of manufacturing a carbon composite comprising a; comprising a coke-coated fiber sheet and manufacturing a sheet laminate that is bound between sheets by needle punching. According to claim 2,
The coke-coated fiber sheet is a method for producing a carbon composite material produced by impregnating a fiber sheet in a phenolic resin solution, an epoxy resin solution or a mixed resin solution containing coke. According to claim 2,
The heat-resistant fiber sheet is a method for producing a carbon composite material containing 5 to 15% by weight of coke. According to claim 1,
In step b),
The carbon source is a method of manufacturing a pitch carbon composite material. According to claim 1,
After step b),
c) forming a surface coating layer comprising a heat-resistant ceramic having a bimodal particle size distribution on the surface of the densified carbon fiber preform; further comprising a method for producing a carbon composite material. The method of claim 6,
The heat-resistant ceramic is a method of manufacturing a carbon composite material that is at least one ceramic selected from carbide, boride, nitride and silicide. A carbon composite material produced by the manufacturing method according to any one of claims 1 to 7.