JPH08175879A - Ceramic fiber-based composite material - Google Patents

Abstract

PURPOSE: To obtain the subject composite material esp. excellent in oxidation resistance and improved in mechanical strength and breaking energy. CONSTITUTION: This composite material 1a is made up of ceramic matrix 2a and ceramic fibers 3a, wherein a layer 5a containing at least one compound selected from Si-N-O, Si=C-O and Si-Ti-C-O compounds lies at the interface between the matrix 2a and the ceramic fiber 3a. The interfacial layer is pref. made up from a sintered compact of a ceramic precursor polymer such as polysilazane, polycarbosilane or polytitanocarbosilane. The thickness of the layer 5a is pref. set at a level <=10% of the diameter of the ceramic fiber 3a. Furthermore, it is preferable that a slidable layer 4 consisting of carbon and/or baron nitride be provided between the ceramic fiber 3a and the interfacial layer 5a.

Description

Detailed Description of the Invention

[0001]

BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a ceramic-based fiber composite material, and more particularly to a ceramic-based fiber composite material having excellent oxidation resistance and improved strength and fracture resistance.

[0002]

2. Description of the Related Art Generally, a ceramic sintered body has little strength decrease up to a high temperature, and has various characteristics such as hardness, electric insulation, wear resistance, heat resistance, corrosion resistance, and lightness as compared with conventional metal materials. Since it is excellent, it is used in a wide range of fields as electronic materials and structural materials such as heavy electric equipment parts, aircraft parts, automobile parts, electronic devices, precision machine parts, and semiconductor device materials.

However, the ceramics sintered body is weaker in tensile stress than in compression, and has a defect of so-called brittleness, in which fracture progresses at a stretch under tensile stress. For this reason, in order to enable the application of the ceramic component to the site where high reliability is required, it is strongly required to increase the toughness and increase the fracture energy of the ceramic sintered body.

That is, gas turbine parts, aircraft parts,
For ceramic structural parts such as ceramic structural parts used for automobile parts that require high reliability in addition to heat resistance and high temperature strength, fiber, whiskers, plates, particles and other reinforcing materials made of inorganic substances and metals are used as matrix materials. Researches for practical use of ceramic composite material (CMC) parts in which the toughness value, the fracture energy value, etc. are increased by dispersing and compounding in a sintered body are being promoted in domestic and overseas research institutions.

However, in the ceramic-based fiber composite material in which the fibers are simply dispersed and composited in the matrix sintered body as described above, when the fibers and the ceramic matrix react with each other at the interface to firmly bond them, the strength increases. However, once a crack is generated, the fibers are insufficiently prevented from propagating the crack, and the composite material is instantly destroyed. On the contrary, when the bonding force at the interface between the fiber and the ceramic matrix is too weak, the interface peels off before the matrix breaks, and sufficient strength cannot be obtained.

As a means for solving the above problems, a composite material has been developed in which a slip layer made of carbon (C), boron nitride (BN) or the like is formed on the surface of a fiber. This slip layer is formed on the fiber surface by carbon (C) or boron nitride (B).
N) or the like by a chemical vapor deposition method (CVD method) or a physical vapor deposition method (P
It is formed by coating with the VD method).

By forming this sliding layer, the bonding strength between the fiber and the ceramic matrix is optimized. Then, sufficient strength is maintained, and after the matrix is broken, the fibers are pulled out, and metastable breakage proceeds.

[0008]

However, in the composite material in which the sliding layer is formed of carbon or BN, the low oxidation resistance of carbon and BN poses a problem when used at high temperature.

Further, after the initial destruction of the composite material, when the ceramic fibers are exposed to the surface in an oxidizing atmosphere at a high temperature, the sliding layer made of C or BN is rapidly oxidized, and the function as a sliding layer is obtained. There was a drawback that it would be lost. Therefore, the effect of preventing cracks from progressing in the composite material when used at high temperature is still insufficient, and there is a problem that strength and fracture energy are reduced.

The present invention has been made to solve the above problems, and an object of the present invention is to provide a ceramic-based fiber composite material having excellent oxidation resistance, improved strength and breaking energy.

[0011]

In order to achieve the above object, the inventors of the present invention prepared a composite material by forming various substances on the surface of a fiber, and the interfacial substance has high temperature strength characteristics of the composite material. A comparative study was conducted on the effects on the fracture energy. As a result, when an interface layer of a certain thickness consisting of a ceramic precursor polymer sintered body is integrally formed on the fiber surface and the fiber is compounded into a ceramic matrix to form a composite material, high temperature conditions are used. For the first time, a composite material having a high fracture energy was obtained. In addition to the above-mentioned interfacial layer, a slip layer composed of C or BN is formed between the interfacial layer and the ceramic fiber to form a multiple structure at the interface between the matrix and the fiber, whereby peeling at the interface or pulling of the fiber It was also found that, as a result of the removal mechanism becoming more complicated and the fracture resistance increasing as compared with the conventional one, a composite material having excellent fracture energy can be obtained.
The present invention has been completed based on the above findings.

That is, the ceramic-based fiber composite material according to the present invention is a ceramic-based fiber composite material obtained by compounding ceramic fibers in a ceramic matrix, and is a Si-N-O compound, a Si-C-O compound and a Si-Ti compound. An interface layer containing at least one of the —C—O compounds is formed at the interface between the ceramic matrix and the ceramic fibers.

Further, Si--N--O compound, Si--C--O
Compound and at least one of Si-Ti-C-O compound
The interfacial layer containing the seed is polysilazane, polycarbosilane,
It is characterized by comprising a sintered body of a ceramic precursor polymer such as polytitanocarbosilane. Further, the thickness of the formed interface layer is 10% or less of the diameter of the ceramic fiber. Further, it is preferable to form a sliding layer made of at least one of carbon (C) and boron nitride (BN) between the ceramic fiber and the interface layer.

Here, various ceramics sintered bodies can be used as the ceramics constituting the matrix of the above ceramic-based fiber composite material. For example, silicon carbide (SiC), aluminum nitride (AlN), silicon nitride ( Si ₃ N ₄ ), non-oxide ceramics sintered body such as boron nitride (BN), alumina (Al ₂ O ₃ ), zirconia (ZrO ₂ ), titania (TiO ₂ ), mullite (3Al ₂ O _3).・ 2SiO ₂ ) and beryllia (Be)
O), cordierite, zircon, sialon, spinel (MgAl ₂ O ₄ ) and other oxide-based ceramic raw materials are used alone or in combination of two or more. Particularly, as the sialon, one having a composition formula: Si _6-z Al _z O _z N _8-z (where 0 <z ≦ 4.5) is preferably used. Also,
If necessary, a sintering aid or additive such as yttrium oxide, alumina, cerium oxide, magnesium carbonate, calcium carbonate or silica is added to the ceramic raw material powder for forming the sintered body. It is also possible to form the matrix by reaction sintering.

The ceramic fibers arranged in the matrix are compounded in a predetermined amount in order to enhance the toughness of the composite material. The material of the fibers is not particularly limited, and the same ceramic fibers as the constituent material of the matrix can be used. Specific examples of such ceramic fibers include silicon carbide fibers (SiC, Si
-CO, Si-Ti-CO, etc.), SiC-coated fiber (core wire is C, for example), alumina fiber, zirconia fiber,
Carbon fiber, boron fiber, silicon nitride fiber, Si ₃ N ₄
Coated fiber (core C, for example) and mullite (3Al _{2
O 3 · 2SiO 2 ~2Al 2 O} 3 · SiO 2) has fibers, it may use at least one selected from these.

The diameter and the length of the fiber have a great influence on the arrangement of the fiber in the molded body, the volume fraction, and the strength characteristics of the composite material. In the present invention, the diameter is 3 to.
Short fibers or continuous fibers having a length of 150 μm and a length of 0.1 mm or more are used. When the diameter is less than 3 μm, the size is less than the particle size of the matrix, the composite effect is small, and the diameter is
With thick fibers exceeding 50 μm, stress due to the difference in thermal expansion is likely to occur at the interface between the fibers and the matrix, and cracks or the like are likely to occur in the matrix. In either case, it is difficult to significantly improve the composite effect of the fibers. Become. When the length of the fiber is less than 0.1 mm, the effect of suppressing the progress of cracks is small and the effect of improving the toughness is also small.

That is, by using fibers having a diameter of 3 to 150 μm and a length of 0.1 mm or more, it is possible to significantly improve the composite effect of the fibers while maintaining good shape imparting performance. Become. However, if the content of such fibers is less than 5%, the composite effect is reduced, so the content of fibers is preferably 5% or more.

On the surface of the fiber, a Si--N--O compound,
An interface layer containing at least one of a Si—C—O compound and a Si—Ti—C—O compound is integrally formed. The above Si-N-O compound, Si-C-O compound and Si-
The Ti—C—O compound is slightly inferior in heat resistance to C and BN, but is excellent in oxidation resistance, and is extremely effective as a stable interface substance for improving the corrosion resistance and fracture energy of the composite material.

The Si--N--O compound, the Si--C--O compound and the Si--Ti--C--O compound constituting the interface layer are, for example, ceramics such as polysilazane, polycarbosilane and polytitanocarbosilane, respectively. It is obtained by using a precursor polymer as a starting material, applying the solution to the surface of the ceramic fiber, and then firing it in a temperature range of 500 to 1100 ° C. in a non-oxidizing atmosphere such as nitrogen gas.

Since the above-mentioned ceramics precursor polymer has a property of being easily decomposed in air, it is desirable to carry out the coating operation and the firing operation on the fiber surface in an atmosphere of an inert gas such as nitrogen gas or Ar gas. .

The thickness of the interface layer is set to 10% or less of the diameter of the ceramic fiber used. Since the interface layer is more fragile than the fibers and the matrix itself, if the thickness exceeds 10% of the fiber diameter, the strength characteristics and fracture energy of the composite material will decrease. Therefore, although the thickness of the interface layer is set within the above range, it is practically 0.2
The range of up to 5 μm is preferred.

In order to prevent the reaction between the fibers and the interface layer or to improve the slippage at the interface between the fibers and the fibers, a slipping layer having a thickness of about 1 to 5 μm may be formed on the surface of the ceramic fiber. This sliding layer is formed by coating the surface of the fiber with carbon (C) or boron nitride (BN).

By the above-mentioned sliding layer, ceramic fibers and
The strength with the interface layer is optimized, and due to this optimum strength, the holding strength after initial fracture can be kept high, and a composite material having a high toughness value can be obtained.

Further, by forming the composite interface by forming the interface layer and the slip layer made of C or BN into a multiple structure, debonding (debonding) and slipping (pullout) occur at many points of the composite interface, Since the cumulative and complicated fracture mechanism is formed, the fracture energy of the composite material can be further improved.

The fiber having an interface layer and, if necessary, a slip layer, has a fiber volume ratio (Vf) with respect to the whole composite material.
Is added at a rate of 5% or more. However, if the added amount exceeds 50%, it becomes difficult to uniformly arrange the matrix around each fiber, and the strength characteristics of the composite material are rapidly deteriorated due to the occurrence of defects such as voids. Therefore, the preferable addition amount is 20 in which the combined effect appears.
-40% by volume.

In addition, by exposing a matrix single layer having a thickness of 200 μm or more, which is composed of only a matrix, integrally on the entire surface of the composite material and the interface portion between the fiber and the matrix is not exposed on the surface, the fiber is exposed. It is possible to prevent oxidative deterioration and strength reduction due to. Further, it is possible to prevent deterioration of the slip function due to the oxidation of C and BN components constituting the slip layer formed on the fiber surface, and it is possible to effectively prevent the deterioration of the high temperature strength of the composite material. By forming the matrix single layer to a thickness of 500 μm or less, the strength reduction preventing function can be sufficiently exerted.

The flat plate-shaped ceramic-based fiber composite material in which a plurality of fiber layers are laminated and arranged in the matrix is manufactured as follows, for example. That is, inside and around each fiber layer formed by weaving ceramic fibers,
It is manufactured by stacking ceramic raw material powders in a predetermined ratio and molding, and then sintering the resulting molded body in a non-oxidizing atmosphere by hot pressing, atmospheric pressure sintering, or reaction sintering. .

On the other hand, a ceramic-based fiber composite material having a complicated shape such as a turbine rotor blade, instead of a flat plate shape, is manufactured by the following method, for example. That is, a fiber is knitted to form a preformed body (preform) close to the shape of the final part, and the preformed body is impregnated with a ceramics slurry serving as a matrix to form a formed body. It is manufactured by main sintering. It is also possible to manufacture the above matrix by a reaction sintering method.

[0029]

The ceramic-based fiber composite material having the above structure is excellent in oxidation resistance and contains at least one of Si—N—O compound, Si—C—O compound and Si—Ti—C—O compound. Since the interface layer is formed between the ceramic fiber and the matrix, it is possible to effectively prevent the reaction between the fiber and the matrix in the manufacturing process of the composite material, and prevent the embrittlement of the composite material due to the sticking of both. can do. In addition, when stress is applied to the composite material, debonding of the fiber and matrix occurs in the interface layer, which exerts the effect of increasing the crack propagation resistance, but does not reduce the initial fracture strength of the composite material. Is retained. Further, after the initial fracture, the fibers are pulled out to improve the toughness of the composite material. At this time, since the interface layer increases the slip resistance between the fiber and the matrix, the fracture energy of the composite material can be significantly improved.

Further, since the Si--N--O compound and the like which compose the interface layer have excellent oxidation resistance as compared with C and BN, when the fiber is exposed on the surface of the composite material or the initial fracture occurs. Even if the fiber is exposed later, the interface layer is less likely to deteriorate, and the function of protecting the fiber is maintained. Therefore, even when the composite material is used in an oxidizing atmosphere at a high temperature, the strength and the fracture energy value are not significantly reduced, and particularly excellent durability as a high temperature structural part material is exhibited.

Further, by forming the composite interface by forming the interface layer and the slip layer made of C or BN into a multiple structure, peeling (debonding) and slipping (pullout) occur at many points of the composite interface, Since the cumulative and complicated fracture mechanism is formed, the fracture energy of the composite material can be further improved.

[0032]

DETAILED DESCRIPTION OF THE PREFERRED EMBODIMENTS An embodiment of the present invention will be described below with reference to the accompanying drawings.

Examples 1 to 7 SiC continuous fibers having a diameter of 15 μm (trade name: Nicalon, manufactured by Nippon Carbon Co., Ltd.) were prepared as ceramic fibers for Examples 1 to 7. Of these SiC continuous fibers, as shown in Table 1, a 0.4 μm thick carbon (C) sliding layer is formed on the surface of the SiC continuous fibers for Examples 2 and 6 by the CVD method. The thickness of the SiC continuous fiber surface for Example 4 was 0.4 using the CVD method.
A sliding layer made of μm boron nitride (BN) was formed.

Next, a xylene solution of polysilazane (manufactured by Tonen Co., Ltd.) as a ceramic precursor polymer was added to the SiC continuous fibers for Examples 1, 2 and 7 in which a slipping layer was formed, if necessary, in a nitrogen atmosphere. And then baked at a temperature of 600 [deg.] C. in a nitrogen atmosphere to give Si-N-O having a thickness of 0.6 [mu] m (Examples 1 and 2) or 3 [mu] m (Example 7).
An interface layer of the compound was formed.

On the other hand, xylene solution of polycarbosilane as a ceramics precursor polymer (manufactured by Nippon Carbon Co., Ltd.) was added to the SiC continuous fibers for Examples 3 and 4 in which a slipping layer was formed if necessary in a nitrogen atmosphere. After coating in the same manner, baking at a temperature of 600 ° C. in a nitrogen atmosphere also gives a thickness of 0.6.
An interface layer consisting of a μm Si—C—O compound was formed.

On the other hand, to the SiC continuous fibers for Examples 5 and 6 in which a slipping layer was formed as needed, a xylene solution of polytitanocarbosilane as a ceramic precursor polymer (manufactured by Ube Industries, Ltd.) was added with nitrogen. After applying in the atmosphere,
Similarly, it was fired in a nitrogen atmosphere at a temperature of 600 ° C. to a thickness of 0.
An interface layer of 6 μm Si-Ti-CO compound was formed.

The SiC continuous fibers for Examples 1 to 7 in which the various interface layers and, if necessary, the slip layer are formed as described above are woven in a two-dimensional direction to form a plain weave cloth. One sheet is laminated and each of Examples 1 to 7 is formed.
A preform for use was manufactured.

On the other hand, by dispersing SiC powder (average particle size 5 μm) as an aggregate and graphite powder (average particle size 1 μm) as a carbon source corresponding to 20% by weight of the amount of SiC powder in a solvent. A low viscosity raw material slurry was prepared. Next, the above-mentioned low-viscosity raw material slurry was impregnated into each of the above-mentioned preforms by using a pressure casting method to obtain each fiber-containing ceramics form. The impregnated amount of the raw material slurry is shown in Table 1.
As shown in, the fiber volume ratio (Vf) in the densified composite material sintered body was set to 30%.

Then, the fiber-containing ceramics compact is placed in an alumina board filled with 1.2 times as much Si powder as necessary for silicifying the fiber-containing ceramics compact, and placed in an Ar gas atmosphere. By maintaining the temperature at 1430 ° C. for 4 hours in the adjusted firing furnace, the fiber-containing ceramics compact is subjected to reaction sintering while impregnating with molten Si to form a dense matrix made of a SiC sintered compact. S formed according to each of Examples 1 to 7
An iC-based fiber composite material was prepared.

As shown in FIG. 1, the composite material 1 according to the above Examples 1, 3, 5, and 7 has a structure in which the SiC continuous fibers 3 are dispersed and composited in the matrix 2 made of the SiC reaction sintered body. Further, on the surface of each SiC continuous fiber 3, Si-
An interface layer 5 made of an N—O compound or the like is integrally formed.

On the other hand, the composite material 1 according to Examples 2, 4 and 6
As shown in FIG. 2, a has a structure in which a continuous SiC fiber 3a is dispersed and composited in a matrix 2a made of a SiC reaction sintered body. A sliding layer 4 made of C or BN and an interface layer 5a made of a Si—N—O compound or the like are formed between the SiC continuous fibers 3a and the matrix 2a so as to have a multiple structure.

Comparative Example 1 On the other hand, a composite material according to Comparative Example 1 using a SiC sintered body as a matrix was prepared in the same manner as in Example 1 except that the interface layer was not formed.

Comparative Example 2 An interface layer was not formed on the surface of SiC continuous fiber, and the thickness was 0.4 μm.
A composite material according to Comparative Example 2 having a SiC sintered body as a matrix was prepared in the same manner as in Example 1 except that m of carbon (C) was coated.

Comparative Example 3 A thickness of 0.4 μm was obtained without forming an interface layer on the surface of SiC continuous fiber.
A composite material according to Comparative Example 3 using a SiC sintered body as a matrix was prepared in the same manner as in Example 1 except that m m boron nitride (BN) was coated.

In order to evaluate the fracture characteristics of each of the composite materials according to Examples 1 to 7 and Comparative Examples 1 to 3 prepared as described above, a bending test piece was cut out from each composite material and subjected to room temperature (R
T: 25 ° C.) and high temperature (1300 ° C.) three-point bending strength, fracture energy and oxidation resistance were measured. Here, the fracture energy value of each test piece was calculated by integrating the fracture energy from the shape of the stress-strain curve, setting Comparative Example 3 as the reference value 1, and calculating the magnification against the reference value and displaying each as a relative value. . Oxidation resistance was evaluated by the weight increase due to the oxidation of the test piece of each composite material after keeping it in the air at 1450 ° C. for 500 hours. Is less than 0.1% and less than 1%, and x indicates a weight increase of 1% or more. The measurement evaluation results are shown in Table 1 below.

[0046]

[Table 1]

As is clear from the results shown in Table 1, according to the ceramic-based fiber composite material according to the present example in which the interface layer made of Si—N—O compound or the like having excellent oxidation resistance is formed, It was possible to effectively prevent the reaction with the matrix, prevent the embrittlement of the composite material due to the reaction sticking of both, and obtain the composite material with high fracture energy.

In addition, in the composite materials according to Examples 2, 4 and 6 in which, in addition to the above-mentioned interface layer, the sliding layers made of C or BN were double formed, peeling and fiber pull-out occurred at the composite interface, It was confirmed that the fracture energy of the composite material is further improved due to the cumulative and complicated fracture mechanism.

It was found that in the composite material according to Example 7 in which the thickness of the interface layer was as large as 20% of the fiber diameter, the strength and the breaking energy were relatively lowered.

On the other hand, in the composite material according to Comparative Example 1 in which the slip layer and the interface layer were not formed, the fiber and the matrix were fixed and brittle fracture occurred. Further, in the composite material according to Comparative Example 2 in which the slip layer made of C was formed, Si was used.
Since the reaction-bonded SiC matrix in which the fiber and the matrix are strongly bonded to each other is formed by reacting with, the three-point bending strength is relatively large, but brittle fracture occurs. Further, in the composite material of Comparative Example 3 in which only the sliding layer made of BN was formed,
Although some strength characteristics can be obtained, oxidation resistance is inferior, and in the bending test at high temperature, there is a problem that the oxidation energy value rapidly deteriorates from the part where the fiber is exposed after the initial fracture, and the fracture energy value easily deteriorates. It was found to be unsuitable as a part material.

In the above embodiment, the case where the reaction-sintered SiC matrix is formed as the ceramic matrix is exemplified, but Si ₃ N ₄ , sialon, AlN, Al ₂ O ₃ , ZrO is used as the matrix.
Similar complex effects were obtained when ₂ , ₂ , SiO ₂ , mullite and spinel were formed.

[0052]

As described above, according to the ceramic-based fiber composite material of the present invention, Si--N--O compound, Si
-C-O compound and Si-Ti-C-O compound, at least one kind of which has an excellent oxidation resistance is formed between the ceramic fiber and the matrix, and therefore, in the manufacturing process of the composite material. The reaction between the fiber and the matrix can be effectively prevented, and the embrittlement of the composite material due to the sticking of the both can be prevented. In addition, when stress is applied to the composite material, debonding of the fiber and matrix occurs in the interface layer, which exerts the effect of increasing the crack propagation resistance, but does not reduce the initial fracture strength of the composite material. Is retained. Further, after the initial fracture, the fibers are pulled out to improve the toughness of the composite material. At this time, since the interface layer increases the slip resistance between the fiber and the matrix, the fracture energy of the composite material can be significantly improved.

Further, since the Si--N--O compound and the like which compose the interface layer have excellent oxidation resistance as compared with C and BN, when the fiber is exposed on the surface of the composite material or the initial fracture occurs. Even if the fiber is exposed later, the interface layer is less likely to deteriorate, and the function of protecting the fiber is maintained. Therefore, even when the composite material is used in an oxidizing atmosphere at a high temperature, the strength and the fracture energy value are not significantly reduced, and particularly excellent durability as a high temperature structural part material is exhibited.

Further, by forming the composite interface by forming the interfacial layer and the slip layer made of C or BN into a multiple structure, delamination (debonding) and slip (pullout) occur at many points of the composite interface, Since the cumulative and complicated fracture mechanism is formed, the fracture energy of the composite material can be further improved.

[Brief description of drawings]

FIG. 1 is a sectional view of an essential part showing an embodiment of a ceramic-based fiber composite material according to the present invention.

FIG. 2 is a sectional view of an essential part showing another embodiment of the ceramic-based fiber composite material according to the present invention.

[Explanation of symbols]

1,1a Ceramics-based fiber composite material (SiC-based fiber composite material) 2,2a Ceramics matrix (SiC reaction sintering matrix) 3,3a Ceramics fiber (SiC continuous fiber) 4 Sliding layer 5,5a Interface layer

Claims (5)

[Claims] 1. A ceramic matrix fiber composite material obtained by compounding ceramic fibers in a ceramic matrix, comprising at least one of Si—N—O compound, Si—C—O compound and Si—Ti—C—O compound. A ceramic-based fiber composite material, characterized in that an interface layer containing the same is formed at the interface between the ceramic matrix and the ceramic fiber. 2. The interface layer containing at least one of Si—N—O compound, Si—C—O compound and Si—Ti—C—O compound is made of polysilazane, polycarbosilane, polytitanocarbosilane or the like. The ceramic-based fiber composite material according to claim 1, which is composed of a sintered body of a ceramic precursor polymer. 3. The ceramic-based fiber composite material according to claim 1, wherein the thickness of the formed interface layer is 10% or less of the diameter of the ceramic fiber. 4. The ceramic-based fiber composite according to claim 1, wherein a sliding layer made of at least one of carbon (C) and boron nitride (BN) is formed between the ceramic fiber and the interface layer. material. 5. The main component of the ceramic matrix is:
Silicon Carbide (SiC), Silicon Nitride (Si ₃ N ₄ ), Sialon (Si _6-z Al _z O _z N _8-z (0 <z ≦ 4.
5)), aluminum nitride (AlN), alumina (Al
₂ O ₃ ), zirconia (ZrO ₂ ), silica (Si
O ₂ ), mullite (3Al ₂ O ₃ .2SiO ₂ ), and spinel (MgAl ₂ O ₄ ) at least one kind, The ceramic base fiber composite material according to claim 1.