JP5052803B2 - Composite brake and method of manufacturing the same - Google Patents

Description

  The present invention relates to a composite brake that can be used as a sliding material or the like.

The inventors of the present application have already proposed a yarn assembly in which yarns containing at least a bundle of carbon fibers and a carbon component other than carbon fibers are combined three-dimensionally and integrated so as not to separate from each other, and this yarn Patent Documents 1 to 7 propose a fiber composite material including a matrix made of a SiC + Si-based material filled between adjacent yarns in an assembly. It is known that the materials disclosed in these patent documents have excellent characteristics as a sliding material, a brake material and the like.
JP 2000-81062 A JP 2000-52461 A JP-A-11-292626 WO99 / 19273 brochure JP 2000-351672 A JP 2001-192270 A JP 2002-179462 A

  However, although the fiber composite materials disclosed in the above Patent Documents 1 to 7 are excellent in various properties, the C constituting the basic skeleton exposed as a braking surface is particularly used under extremely severe conditions. When the area of the carbon fiber of the / C composite occupies a predetermined ratio or more, there is a possibility that a slight fluctuation occurs in the dynamic friction coefficient when used as a material such as a brake. However, there is a demand for reducing the fluctuation of the dynamic friction coefficient due to wear even if it is worn by use.

  The present invention has been made in order to reduce the fluctuation of the dynamic friction coefficient due to the above-described wear, and its purpose is to control the fluctuation of the dynamic friction coefficient within a range in which a problem does not substantially occur. To do.

  That is, basically, a yarn assembly in which yarns containing at least a bundle of carbon fibers and a carbon component other than carbon fibers are combined three-dimensionally and integrated so as not to separate from each other, and this yarn assembly A fiber composite material comprising a SiC + Si-based material or a matrix made of SiC, which is filled between adjacent yarns in the body, and even if the exposed surface is worn with use, the friction coefficient causes wear. The present invention has been completed by finding that the above-mentioned object can be achieved by using a fiber composite material in which the fluctuation of the dynamic friction coefficient due to the above does not substantially occur.

  In the present invention, the fact that fluctuation due to wear does not substantially occur in the dynamic friction coefficient means that the dynamic friction coefficient of the exposed surface falls within a specific range due to wear. The dynamic friction coefficient of the exposed surface that is the outermost surface must always be within this range. For this purpose, in any exposed surface (including the exposed surface when the product is manufactured), SiC + Si or SiC It has been found that the surface area occupied by is required to be 50% or less, preferably 40% or less, more preferably 40% or less and 15% or more of the total surface area. In order to ensure such a surface area ratio, for example, the fiber composite material manufactured based on Example 1 of the above-mentioned Patent Document 4 is used, and the equivalent diameter (short axis and long axis) of the used C / C fiber bundle is used. In consideration of the average) and the size of the final product itself, the ratio of the surface area composed of Si + SiC or SiC on the wear surface to the total surface area is 50% or less, preferably 40% or less, more preferably It has been found that the above-mentioned object can be achieved by cutting with an angle that is 40% or less and 15% or more, and the present invention has been completed based on this finding. In order for the exposed surface of the fiber composite material to satisfy the above-mentioned requirements, it is necessary to select the cutting angle and / or the axial direction of cutting in consideration of the thickness of the carbon fiber layer and the thickness of the matrix layer. In general, it is preferable to select an angle and / or direction which is preferable using a prototype sample, and to select based on the result. The axial direction of cutting is such that the ratio of the area of Si + SiC or SiC on the exposed surface formed by cutting to the total surface area on the exposed surface is 50% or less, preferably 40% or less, more preferably 40% or less. And if it is 15% or more, the fiber composite material that is a three-dimensional body can be in any of the longitudinal direction (Y-axis direction), the lateral direction (X-axis direction), or the vertical direction (Z-axis direction). It ’s okay. In the present specification, the cut-out angle and / or the cut-out axial direction may be collectively referred to as a cut-out angle.

  In the present invention, the basic fiber composite material may be manufactured in accordance with, for example, the description of Patent Document 4 described above, and the composite brake is obtained by converting the fiber composite material thus obtained into a desired SiC + Si or SiC. What is necessary is just to cut out with the angle that the area amount which occupies becomes 50% or less of the total area, preferably 40% or less, more preferably 40% or less and 15% or more. The cutting may be performed with a diamond saw, for example. If it exceeds 50%, squeal is likely to occur during braking, and the dynamic friction coefficient becomes too large, which is not preferable. On the other hand, if it is less than 15%, the variation of the friction coefficient particularly at the low temperature in the initial stage of braking becomes large, which causes an inconvenience that it is difficult to control.

  According to the present invention, even if wear occurs due to use, a composite brake can be obtained in which the dynamic friction coefficient of the surface that becomes the surface due to wear does not substantially vary.

  The composite brake of the present invention basically includes a yarn assembly in which yarns containing at least a bundle of carbon fibers and a carbon component other than carbon fibers are combined in a three-dimensional manner so as not to separate from each other. And a matrix made of a SiC + Si-based material filled between adjacent yarns in the yarn assembly.

  Thus, by using C / C composite as a base material, it is possible to impart toughness to the fiber composite material, so that it is excellent in impact resistance, light weight, high strength, high lubricity, and wear resistance. It can be. Therefore, the disadvantage of the low impact resistance of the SiC fiber reinforced Si-SiC composite can be overcome, and it can also be used for a structural material having a complicated shape or thin portion.

  Hereinafter, the fiber composite material which is a starting material of the composite brake according to the present invention will be described.

  The fiber composite material used in the present invention forms a flexible coating made of a plastic such as a thermoplastic resin at least around the carbon fiber bundle to obtain a flexible intermediate material, which is then made into a yarn shape, and then Depending on the case, a specific treatment of forming a sheet and laminating and heat forming is performed, so that carbon particles other than high-temperature molten Si and carbon fibers, organic binders, and plastic coatings are generated by thermal decomposition. It is presumed that carbon having high activity first contacts and reacts and does not directly contact the carbon fiber bundle, and the structure of the carbon fiber is not destroyed. Moreover, this fiber composite material has a microstructure in which a matrix made of SiC + Si-based material or SiC is filled between adjacent yarns in the yarn assembly.

  The sliding part of the brake member becomes a surface, and the surface has the same flat shape as the mold at the time of heat molding. In other words, when the yarn is made into a sheet shape, the surface of the mold and the sheet are almost parallel, and when the yarn is cut into a certain length and filled into the formwork, it is probable that the yarn will be arranged in a direction parallel to the mold surface. Become. Furthermore, the final material produced by this process is one in which the outer surface of the yarn is impregnated with Si and a part thereof is converted to SiC, and the yarn is not positively impregnated with Si. Accordingly, by adopting the structure described in the claims, it becomes difficult for each yarn fiber composed of carbon fiber bundle yarns to be detached from the yarn, and also has a necessary braking characteristic. In other words, the structure is excellent in wear characteristics and has dynamic friction characteristics, strength characteristics, and heat resistance characteristics necessary for a brake as described in Patent Documents 1, 2, 3, 4, 5, 6, and 7.

  In the present invention, the SiC + Si-based material is a general term for materials containing silicon and silicon carbide as main components. In the present invention, silicon is impregnated into a C / C composite or a molded body thereof. At this time, silicon reacts mainly with carbon components other than carbon fibers or residual carbon in the composite and is partially carbonized. Therefore, partly carbonized silicon is generated between the yarn assemblies. In this matrix, several intermediate phases can be included, ranging from a silicon phase in which substantially pure silicon remains to a substantially pure silicon carbide phase. That is, this matrix is typically composed of a silicon phase and a silicon carbide phase, but Si— in which the carbon content changes in a gradient manner based on silicon between the silicon phase and the silicon carbide phase. A SiC coexisting phase may be included. The SiC + Si-based material is a generic name for materials in which the carbon concentration is changed from 0 mol% to 50 mol% in such a Si-SiC series. Needless to say, Si may react with carbon containing free carbon and substantially no Si remains, and may be composed of SiC alone. Such a layer is referred to as SiC.

  This fiber composite material preferably comprises a silicon carbide phase in which the matrix is produced along the surface of the yarn. In this case, the strength of each yarn itself is further improved and it is difficult to break. Moreover, this fiber composite material preferably includes a silicon phase whose matrix is made of silicon, and a silicon carbide phase is generated between the silicon phase and the yarn. In this case, the surface of the yarn is strengthened by the silicon carbide phase, and the central portion of the matrix is made of the silicon phase having a relatively low hardness, so that the microscopic stress distribution is further promoted.

  The fiber composite material preferably has a gradient composition in which the silicon content increases as the matrix moves away from the surface of the yarn. In the fiber composite material, preferably, the yarn assembly includes a plurality of yarn arrays, and each yarn array is formed by two-dimensionally arranging a plurality of yarns substantially in parallel. Each yarn array is stacked to form a yarn assembly. As a result, the fiber composite material has a laminated structure in which a plurality of yarn arrays are laminated in one direction.

  In this case, it is particularly preferable that the longitudinal directions of the yarns in adjacent yarn arrays intersect each other. This further promotes stress dispersion. The longitudinal directions of the yarns in adjacent yarn arrays are particularly preferably orthogonal.

  Preferably, the matrix is continuous with each other in the fiber composite material to form a three-dimensional network structure. Particularly preferably in this case, the matrix is two-dimensionally arranged substantially parallel to each yarn array, and the matrices generated in each adjacent yarn array are continuous with each other, whereby the matrix is A three-dimensional lattice is formed.

  The carbon component other than carbon fiber in the yarn is preferably carbon powder, and particularly preferably graphitized carbon powder.

  1 is a schematic perspective view for explaining the concept of a yarn assembly, FIG. 2 (a) is a sectional view taken along the line IIa-IIa in FIG. 1, and FIG. 2 (b) is a sectional view taken along line IIb-IIb in FIG. It is line sectional drawing. FIG. 3 is a partially enlarged view of FIG.

  The skeleton of the fiber composite material 7 is constituted by a yarn assembly 6. The yarn assembly 6 is formed by stacking yarn arrays 1A, 1B, 1C, 1D, 1E, and 1F in the vertical direction. In each yarn array, each yarn 3 is arranged two-dimensionally, and the longitudinal direction of each yarn is substantially parallel. The longitudinal direction of each yarn in each yarn array adjacent to each other in the vertical direction is orthogonal. That is, the longitudinal directions of the yarns 2A of the yarn arrays 1A, 1C, and 1E are parallel to each other and orthogonal to the longitudinal direction of the yarns 2B of the yarn arrays 1B, 1D, and 1F.

  Each yarn is composed of a fiber bundle 3 composed of carbon fibers and carbon components other than carbon fibers. By stacking the yarn arrays, a three-dimensional lattice-shaped yarn assembly 6 is formed. Each yarn is crushed during a pressure forming process as described later, and has a substantially elliptical shape.

  3 (a) and 3 (b) are conceptual diagrams schematically illustrating the cut-out angle and / or the cut-out axial direction of the composite material brake according to the present invention. For example, FIG. 3A shows the SiC + Si depending on the cutting angle and / or the cutting axial direction when the fiber composite material having the cross-sectional structure shown in FIG. 2A is used as the cutting basic axis. The system material or SiC schematically explains the ratio of the exposed surface immediately after cutting out. For example, an object having a cross-sectional shape shown in FIG. 3A is cut along the cutting line IIIa-IIIa. By cutting in the axial direction, a ratio of (SiC + Si) / C of 25/75 is obtained, and when cutting in the Z-axis direction along the cutting line IIIc-IIIc, the ratio of (SiC + Si) / C is 50 / 50 can be obtained, and when it is cut obliquely in the Z-axis direction along the cutting line IIIb-IIIb, a (SiC + Si) / C ratio of 25/75 is obtained.

  FIG. 3B shows the SiC + Si depending on the cut-out angle and / or the cut-out axial direction when the fiber composite material having the cross-sectional structure shown in FIG. 2B is used as the cut-out basic axis. The material or SiC schematically explains the ratio of the exposed surface immediately after cutting, and for example, an object having the cross-sectional shape shown in FIG. 3B is cut along the cutting line IVa-IVa. By cutting in the axial direction, a ratio of (SiC + Si) / C is obtained as 0/100, and when cutting in the Z-axis direction along the cutting line IVc-IVc, the ratio of (SiC + Si) / C is 0. / 100 is obtained, and when it is cut in the Y-axis direction along the cutting line IVb-IVb, a (SiC + Si) / C ratio of 65/35 is obtained. As the composite material brake according to the present invention, in FIG. 3 (a), one cut along IIIa-IIIa and one cut along IIIc-IIIc are shown in FIG. 3 (b). And those cut along VIc-VIc. Thus, what was cut out to satisfy the above-described conditions exists, for example, in a state where the carbon fiber bundle 3 composed of the above-mentioned yarn, the silicon carbide phase 4, and the SiC + Si-based material phase 5 are exposed on the surface. . By comprising in this way, even if it is worn out as a result of use, the SiC + Si-based material phase or the SiC phase is constantly present in a state exposed on the surface, and the SiC + Si-based material phase or the SiC phase at a predetermined ratio. Will be present on the surface. Note that Si present on the surface usually reacts with nearby carbon over time to form silicon carbide.

  The fiber composite material that is the starting material for the composite material brake of the present invention may contain, for example, boron nitride, boron, copper, bismuth, titanium, chromium, tungsten, molybdenum, etc. Other elements other than carbon may be included. Since these substances have lubricity, the inclusion of the C / C composite in the base material can maintain the lubricity of the fiber even in the base material portion impregnated with the SiC + Si-based material. Decline can be prevented.

The fiber composite material which is a starting material for the composite brake of the present invention can be preferably produced by the following method. That is, a carbon fiber bundle is produced by including a powdery binder pitch and coke which finally become a matrix in a bundle of carbon fibers, and further containing a phenol resin powder or the like as necessary. A flexible coating made of a plastic such as a thermoplastic resin is formed around the carbon fiber bundle to obtain a flexible intermediate material. This flexible intermediate material is made into a yarn shape (see Japanese Patent Application No. 63-231791), and after a necessary amount is laminated, it is molded by hot pressing at 300 to 2000 ° C. and at Jojo to 500 kg / cm ^2. By doing, a molded object is obtained. Or this molded object is carbonized at 700-1200 degreeC as needed, and graphitized at 1500-3000 degreeC, and a sintered compact is obtained.

  Carbon fiber is made from petroleum pitch or coal tar pitch as raw material, and pitch-based carbon fiber and acrylonitrile (co) polymer fiber obtained by adjusting spinning pitch, melt spinning, infusibilization and carbonization are made flameproof and carbonized. Any of the obtained PAN-based carbon fibers may be used.

  As the organic binder necessary for forming the matrix, thermosetting resins such as phenol resins and epoxy resins and tar, pitch, etc. are used. These include cokes, metals, metal compounds, inorganic and organic compounds, and the like. May be. A part of the organic binder may be a carbon source.

  Next, the molded body or sintered body produced as described above and Si are held in a temperature range of 1100 to 1400 ° C. and a furnace pressure of 0.1 to 10 hPa for 1 hour or longer. Preferably, at this time, while flowing an inert gas of 0.1 NL per kg of the total weight of the compact or sintered body and Si (normal liter: 1200 ° C., equivalent to 5065 liter when the pressure is 0.1 hPa), A Si-SiC layer is formed on the surface of the compact or sintered body. Next, the temperature is raised to 1450 to 2500 ° C., preferably 1700 to 1800 ° C., and the SiC + Si-based material or SiC is melted and impregnated into the open pores of the molded body or sintered body. In this process, when a molded body is used, the molded body is also fired to produce a fiber composite material.

  The molded body or sintered body and Si are held at a temperature of 1100 to 1400 ° C. and a pressure of 0.1 to 10 hPa for 1 hour or more, and in that case, inert per 1 kg of the total weight of the molded body or sintered body and Si It is desirable to control the gas to flow at 0.1 NL or more, preferably 1 NL or more, more preferably 10 NL or more.

In this way, by forming an inert gas atmosphere at the time of firing (ie, before the melting and impregnation of Si), the generated gas such as CO accompanying the change of the inorganic polymer or inorganic material to ceramic is removed from the firing atmosphere. Further, by preventing contamination of the firing atmosphere from the outside by O ₂ or the like in the air, the porosity of the fiber composite material obtained by subsequently melting and impregnating Si can be kept low.

  Further, when Si is contacted and impregnated into the molded body or sintered body, the ambient temperature is raised to 1450 to 2500 ° C., preferably 1700 to 1800 ° C. In this case, the firing furnace pressure is preferably in the range of 0.1 to 10 hPa. Furthermore, the furnace atmosphere is preferably an inert gas or Ar gas.

  As described above, when a flexible intermediate material is used and combined with impregnation and melting of silicon, in the molded body or sintered body, elongated open pores remain in the gaps between the yarns, and silicon extends along the elongated open pores. It penetrates deeply into the sintered or molded body. In the process of permeation, silicon reacts with the carbon of the yarn and gradually carbonizes from the surface of the yarn to produce a fiber composite material that is a starting material of the present invention. The composite brake according to the present invention is obtained by cutting out the fiber composite material thus obtained at an angle such that the surface area occupied by the SiC + Si-based material or SiC is 50% or less of the total surface area.

Next, the present invention will be described in more detail using examples, but the present invention is not limited to these examples. The obtained composite brake was measured for the dynamic friction coefficient by the following method.
(Evaluation method of dynamic friction coefficient)

A test piece of 60 mm × 60 mm × 5 mm (thickness) is set on a jig and rotated, and the mating material (SUJ, 10 mm ball) is pressed against the test piece with a constant load Fp (N), and the friction force Fs ( N) was measured. The value of the dynamic friction coefficient was calculated by the following equation.
Friction coefficient μ = Fs / Fp

(Example)
By impregnating a phenolic resin with carbon fiber aligned in one direction, about 10,000 carbon long fibers having a diameter of 10 μm are bundled to obtain a fiber bundle (yarn), and this yarn is arranged as shown in FIG. A prepreg sheet was obtained. Next, 50 stages of this prepreg sheet were laminated and treated with a hot press at 180 ° C. and 10 kg / cm ² to cure the phenol resin. Subsequently, it baked at 2000 degreeC in nitrogen, and obtained the C / C composite. When the physical properties of the obtained C / C composite were measured by the method described in Patent Document 4, the density was 1.0 g / cm ³ and the open porosity was 50%.

  Next, the obtained C / C composite was erected in a carbon crucible filled with Si powder having a purity of 99.8% and an average particle diameter of 1 mm. Next, the carbon crucible was moved into the firing furnace. After processing the temperature in the firing furnace at 1300 ° C., the argon gas flow rate as an inert gas at 20 NL / min, the firing furnace pressure at 1 hPa, and the holding time for 4 hours, By raising the internal temperature to 1600 ° C., the C / C composite was impregnated with Si to produce a fiber composite material as a raw material. In this example, the entire C / C composite was changed to a fiber composite material.

The density, open porosity, interlaminar shear strength, compressive strength, and flexural modulus of the obtained fiber composite material were as follows.
Density (g / cm ² ): 2.2
Open porosity (%): 1-2
Compressive strength (MPa): 190
Flexural modulus (GPa): 40
Interlaminar shear strength (MPa): 22
Specific wear amount (mm ³ / (N / km)): 0.0
Dynamic friction coefficient (μ): 0.55
Self-healing property: 140/190
Oxidation resistance (%): 4

  This was fixed to a mounting table for cutting in the X-axis direction at an angle such that the proportion of SiC + Si in the cut surface was about 35%, and then cut using a diamond saw. The surface of what was cut out in this way was configured as schematically shown in FIG. 3, and the proportion of Si + SiC in the surface was 37% as measured by EDS surface elemental analysis. Moreover, the dynamic friction coefficient of this thing was 0.50. This was set in a Disk-on-Disk type abrasion tester, rotated 100 million times, and the dynamic friction coefficient of the surface exposed later was measured. The fluctuation of the dynamic friction coefficient was 0.55 ± 0.00. 05, in a range where there was substantially no variation. The ratio of SiC + Si in the exposed surface exposed as a result of wear was 27%, which was slightly decreased.

(Comparative example)
The fiber composite material itself obtained in the above example was cut out to have a predetermined thickness, subjected to a wear test under the same conditions, and then the dynamic friction coefficient of the exposed surface was measured. The previous coefficient of dynamic friction was 0.50, which was the same as that in the example, but it decreased significantly to 0.15 when the wear test was completed. When the area occupied by SiC and Si on the exposed surface of the substrate itself was determined, it was 8% when it was 39% at the start. Therefore, it is considered that a sufficient dynamic friction coefficient could not be shown.

  As described above, the composite brake of the present invention uses a fiber composite material as the material, and this fiber composite material has a base material composed of a C / C composite as a basic structure, and an SiC + Si-based material. Or because it has a structure impregnated with SiC, the impact resistance, light weight and high strength characteristic of C / C composite, and oxidation resistance, creep resistance and spalling resistance that are not characteristic of C / C composite It has both sex.

  Such characteristics do not fluctuate greatly depending on the angle of cutting, and in addition, the dynamic friction coefficient of the exposed surface that has been exposed due to wear is substantially unchanged from that immediately after production, so higher performance is required. The composite brake of the present invention is promising as a control material for high-speed mass transportation equipment.

It is a perspective view which shows typically the form of the yarn aggregate | assembly of a fiber composite material which is a manufacturing material of the composite material brake of this invention. It is the IIa-IIa sectional view taken on the line of FIG. 1 which shows typically the microstructure of the principal part of the fiber composite material which is a manufacturing material of this invention composite brake. It is the IIb-IIb sectional view taken on the line of FIG. 1 schematically showing the microstructure of the main part of the fiber composite material, which is a material for manufacturing the composite brake of the present invention. BRIEF DESCRIPTION OF THE DRAWINGS It is a conceptual diagram which illustrates typically the cut-out angle of the composite material brake which concerns on this invention, and / or the axial direction to cut out, and the IIIa-IIIa, IIIb-IIIb, and IIIc-IIIc line | wire in a figure are the respective cut-out directions typically It is a line shown. BRIEF DESCRIPTION OF THE DRAWINGS It is a conceptual diagram which illustrates typically the cut-out angle of the composite material brake which concerns on this invention, and / or the axial direction to cut out, and the IVa-IVa, IVb-IVb, and IVc-IVc line | wire in a figure is a pattern showing each cut-out direction It is a line shown.

Explanation of symbols

1A, 1B, 1C, 1D, 1E, 1F: yarn array, 2A, 2B: yarn, 3: carbon fiber bundle, 4, 4A, 4B: silicon carbide phase, 5, 5A, 5B: silicon phase, 6: yarn Aggregate 7: Fiber composite material.

Claims (7)

A yarn assembly in which yarns containing at least a bundle of carbon fibers and a carbon component other than carbon fibers are three-dimensionally combined and integrated so as not to separate from each other, and the adjacent yarns in this yarn assembly A composite material comprising a SiC + Si-based material or a matrix made of SiC, and the surface area occupied by the SiC + Si-based material or SiC in the exposed surface formed by cutting is the entire surface of the exposed surface. the cut-out surfaces to occupy 15 to 40% of the surface area and the exposed surface, or, even in the exposed surface coming exposed by abrasion by use, the total surface areas occupied by the SiC + Si based material or a SiC is exposed surface A composite brake that is 15-40% of the total.   The yarn assembly includes a plurality of yarn arrays, and each yarn array is formed by two-dimensionally arranging a plurality of the yarns substantially in parallel, and the yarn arrays are stacked. The composite brake according to claim 1, wherein the yarn assembly is configured. The composite material brake according to claim 1 or 2 , wherein longitudinal directions of the yarns in the adjacent yarn array bodies intersect each other.   The composite brake according to any one of claims 1 to 3, wherein the matrix forms a three-dimensional network structure by being continuous with each other in the fiber composite material. The matrices are two-dimensionally arranged substantially parallel to each yarn array, and the matrices generated in each adjacent yarn array are continuous with each other, whereby the matrix is three-dimensional. 5. A composite brake according to claim 4 forming a lattice.   A carbon fiber bundle is produced by including a powdery carbon component that finally becomes a matrix in the bundle of carbon fibers, and then a plastic film is formed around the carbon fiber bundle to form an intermediate material. After the intermediate material is made into a yarn shape and a predetermined amount is laminated, it is molded to obtain a molded body, or after the molded body is sintered to obtain a sintered body, the molded body or the sintered body and Si are obtained. The molded body or sintered body is maintained at a temperature of 1100 to 1400 ° C. in an inert gas atmosphere, and then the molded body or sintered body and Si are heated to a temperature of 1450 to 2500 ° C. The surface area occupied by the SiC + Si-based material or SiC in the exposed surface obtained by impregnating the SiC + Si-based material into the open pores of the fiber to obtain a fiber composite material and cutting out the fiber composite material is 15% of the total surface area of the exposed surface. Yarn assembly comprising three-dimensionally combined yarns containing at least a bundle of carbon fibers and a carbon component other than carbon fibers that are cut out at an angle of 40% and integrated so as not to separate from each other And a matrix made of SiC + Si-based material or SiC filled between the adjacent yarns in the yarn assembly, and the exposed surface is also exposed by wear due to use. The manufacturing method of the composite material brake which consists of a fiber composite material whose surface area which a SiC + Si type material or SiC occupies is 15 to 40% of the total surface area of this exposed surface also in the coming exposed surface. The molded body or sintered body and Si are held at a temperature of 1100 to 1400 ° C. and a pressure of 0.1 to 10 hPa for 1 hour or more, and at that time, per 1 kg of the total weight of the molded body or sintered body and Si The method for producing a composite brake according to claim 6 , wherein the inert gas is controlled to flow at 0.1 normal liter (NL) or more.

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