DE4012229A1 - FIBER-REINFORCED CERAMIC BASE MATERIAL COMPONENT COMPONENT AND METHOD FOR THE PRODUCTION THEREOF - Google Patents

Abstract

A fibre reinforced composite member is made by interspersing a matrix mixture slurry formed from a ceramic matrix precursor, a liquid compatible with the precursor and ceramic discontinuous material comprising particles about reinforcing fibres to provide a prepreg preform, which is heated in an oxidizing atmosphere to a temperature at which the precursor is transformed to a ceramic phase which bonds said ceramic particles into a matrix about the fibres. The member may be an airfoil shaped strut (10) useful in a gas turbine engine hot section, which is made by disposition of plies 22, formed from said matrix mixture slurry and fibres, e.g. fabric about forming blocks 24, the assembly being placed within forming dies (26A, 26B) and pressure being applied while the assembly is heated. The resulting preform is sintered in a furnace to a consolidation temperature. <IMAGE>

Description

This invention relates to ceramic composite components and process for the preparation, and, in particular in one Mold, ceramic fiber reinforced ceramic matrix composite material components.

This application is related to the one filed simultaneously Patent application entitled "Compressed component and Method and Preform for Production "(Applicant's abstract) 12 662.5-13DV-09 230), for which the priority of the US application Serial No. 3 41 001 of 14 April 1989 has been.

The use of ceramic in the form of at high temperature in operation, such as in components for power generating devices, including vehicle engines, Gas turbines, etc. is in terms of low Weight and strength of certain ceramics at high Temperatures attractive. A typical component is a gas turbo engine brace. However, they are monolithic  ceramic structures without reinforcement brittle. Such components without support from additional incorporated, reinforcing Structures do not meet the requirements regarding their reliability for such demanding Use.

In an attempt to overcome this deficiency became certain Break Resistant Ceramic Base Material Composites mentioned. These contain incorporated fibers of various types Size and different types, for example long fibers or filaments, short or cut fibers, whiskers, etc. All these types are here for simplicity referred to as "fibers". Some fibers were with certain Coated materials that have been applied to the occurrence strong reactions between amplification and prevent the base material. However, some are Coatings of carbon, or carbon species, or of other material that will oxidize if it is in a exposed to elevated operating temperature of the air becomes. The inclusion of such fibers within the ceramic Base material was made to brittle fracture behavior to resist.

A problem with the use of such oxidizing Fibers, such as carbon, as reinforcement in ceramic composites is that the system at the use can become environmental and stable: cracks in the ceramic matrix, even microcracks, the Oxidizable fiber available for contact with atmospheric oxygen at elevated operating temperatures, as in hot sections of power generating machinery occur. Such oxidation of reinforcing fibers weakens or destroys the fibrous structure or its function, causing too  an unwalked weakening of the structural component leads.

Another problem concerns the fact that high sintering temperatures for ceramic particles around reinforcing fibers around the type of fibers that can be used to restrict. For example, many fibers deteriorate above about 1000 ° C, considerably below that for the ceramic Particles required sintering temperatures.

In short, the present invention provides in one form a method for producing a stable in its environment, fiber reinforced ceramic matrix composite component, containing oxidation-stable reinforcing fibers, for example, ceramic fibers, and one around the fiber mixed basic substance. The term "oxidation stable", such as as used herein in terms of fibers, means fibers, which essentially no extensive oxidation and / or no environmental degradation under intended operating conditions the temperatures of the atmosphere, such as Air, suffer. The matrix is a mixture of which contains ceramic particles, together by a ceramic Phase connected.

In the process form, the present invention provides a ceramic base precursor, which on heating converted into a ceramic phase, mixed in one substantially uniform distribution in a slurry a basic mix of discontinuous material, containing ceramic particles in a liquid, which is compatible with the precursor. This slurry is around the oxidation-stable fibers around as a basic mass mixture to create a prepreg preform which in an oxidizing atmosphere, such as in  Air is heated, at a processing temperature, at least when for the conversion of the precursor into a ceramic Phase required temperature and lower than that which leads to a degradation of the ceramic in the preform will lead. By the present invention, such Temperature in the range of about 600 ° to 1000 ° C lie. Such heating converts the ceramic precursor, as by decomposition, into a ceramic phase to, for example, amorphous or crystalline form, which the ceramic particles from the slurry into a ceramic matrix around the fibers binds. Because the Components of this reinforced ceramic matrix composite component stabilized in an oxidizing atmosphere are, preferably substantially all ceramic Oxides are interconnected, the component is environmentally stable and of high strength and high resistance to breakage.

FIG. 1 is a graphical comparison of the fracture resistance values of a non-reinforced matrix, another reinforced matrix, and a composite, reinforced member of the present invention. FIG .

FIG. 2 is a fragmentary perspective sectional view of a portion of a gas turbocharged brace. FIG .

Fig. 3 is a fragmentary schematic sectional view of layers of ceramic matrix composite material disposed about forming blocks.

Fig. 4 is a fragmentary perspective sectional view of the component of Fig. 3 arranged in fitting fittings.

Break-resistant, fiber-reinforced ceramic base material composites provide the designer of high-temperature components  for power-generating machines, such as Components for car engines, turbo engines, etc., an opportunity to specify stable, lightweight components. However, certain such composites are environmental unstable by occurrence of cracks, which oxidizable Expose parts of the air. In addition, certain known perform Machinings to an undesirable degree of porosity in the product. Likewise, the types of fibers that are sintered in the be included ceramic reinforced composites can, limited, based on the required relative high sintering temperatures and a fiber deterioration temperature, lower than the required sintering temperature.

The present invention provides an improved method to avoid such known problems and to manufacture an environmentally stable reinforced ceramic matrix compound component high strength and high breakage resistance at lower processing temperatures. A the main basis for the invention is the provision of ingredients which are at a lower temperature can be stabilized; and after a stabilizing Heating a product which is a component which preferably substantially all ceramic oxides with each other connected. The use of such ingredients eliminates the possibility of component degradation when used as a result of oxidation.

Typical of the ceramic particles as they are for the ceramic Basic materials used are the oxides of such elements as Al, Si, Ca, Hf, B, Ti, Y and Zr, and their mixtures and combinations. Such commercial available materials include Al₂O₃, SiO₂, CaO, ZrO₂, HfO₂, BN, TiO₂, 3Al₂O₃ · 2SiO₂, V₂O₃ CaO · Al₂O₃ and various clays  and glass fritters. Ceramic particle sizes in the range between about 75 microns to 0.2 microns (75 microns to 0.2 microns) in the Diameters were considered as a basic material component in the Evaluation of the present invention examined. A form The present invention addresses the fact that each of these ceramics when used as a structure when firing up to an elevated compression temperature will shrink. For example, an alumina shape a linear shrinkage in the range of about 3 to 4% at 1400 ° C.

In connection with the present invention, a Variety of ceramic precursors rated both as a basic mass precursor as well as an infiltrant precursor, as will be described later can be. The use of such a precursor as a binder in combination with the ceramic particles allows the development of a stable composite at a significantly lower processing temperature. such Precursors, for example, by decomposition in the Heating in a ceramic phase can go for the Practical implementation of parts of the present invention in solid or liquid form, or mixtures thereof. In general, they are called organometallic, sol Classified gels or metal salts. Included in the Evaluation were the following ceramic precursors: polycarbosilanes, Silicones, metal salts (including vinylic Polysilanes, dimethylsiloxane and hafnium oxychloride), silica and alumina sol, aluminum isopropoxide, monoaluminum phosphate and other phosphates. The following Table I shows specific forms of such precursors.  

Table I

Ceramic precursors

According to the inventive method is discontinuous Material containing the ceramic particles, the ceramic precursor and optionally a binder, in a liquid for providing a slurry Base material mixture dispersed. The term "discontinuous Material "as used herein is intended to be powder, Particles, small chips, flakes of material, whiskers, etc. mean. A characteristic of the liquid of the slurry is that they are compatible with the ceramic Precursor and preferably a solvent therefor is, and for the binder, if used has been. This allows a substantially uniform Distribution of precursor in the slurry, along with the ceramic particles and optionally binders for Provision of the base material mixture. For example the liquid may be aqueous or organic depending on from the precursor or the mixture of precursors and optionally binder. The precursor becomes preferably, as already stated, in the liquid solve, which acts as a solvent in this case. typical, used as solvent organic liquids include ethyl alcohol, trichloroethane, methyl alcohol, toluene and methyl ethyl ketone, which binders, the polymers and / or infiltrants allow themselves in a solution dissolve. The amount of solvent required depends on the solubility and saturation limit of the binder / polymers and the desired viscosity of the slurry from. The preferred limits are in the range of 20 to 30 weight percent solvent. Additional solvent amounts are only used to vaporize the excess Solvent prolonged drying times condition.

With regard to the ceramic particles in the slurry  It has been found that such particles are in the range of more than 40% by weight up to about 90% by weight the sum of ceramic particles and precursor should be. At 40 weight percent or less is insufficient Ceramic present in the composite component to create a base material around the reinforcing fibers, which leads to too high a porosity; at a larger one Value as about 90% by weight is insufficient Binding of the ceramic particles to the reinforcing fibers around through the converted precursor ceramic phase. The preferred range for the ceramic particles in the sum of particles and precursors is 50 to 80 weight percent, and more specifically about 70 to 80 weight percent.

It was found that the ceramic precursor in the slurry the base material mixture in an amount of about 10 to 40 weight percent of the sum of precursor and ceramic particles should be included, preferably in an amount from 10 to 30 weight percent, to adequate flow and binding sure. Less than about 10 weight percent provides insufficient ceramic phase for flow and interconnection the ceramic particles after the precursor decomposition heating; greater than about 40 weight percent the decomposition of the precursor leads to excess Porosity in the base material phase.

The remainder of the slurry is generally the liquid. However, such other materials, such as binders, may be used and plasticizer, commonly referred to herein as a "binder", the temporarily to hold together an uncured Base material can be used in the slurry be included. Binder for holding the preform before heating to the processing temperature can be up  about 20 percent by weight of the sum of the ceramic particles, of the precursor and the binder. A larger than this amount becomes too high a porosity to lead. Examples of such evaluated binders and plasticizers (and a source of supply) are Prestolines Master Mix (P.B.S. Chemical), Cellulose ethers (Dow Chemical), Polyvinyl butyral (Monsanto), butyl benzyl phthalate (Monsanto), Polyalkylene glycol (Union Carbide) and polyethylene glycol (Union Carbide). Also used binding systems were Epoxy resins, for example, multipurpose epoxy resins by Ciba-Geigy, Silicones, for example polysiloxanes (GE), RTV (GE) and polycarbosilane (Union Carbide). Contain after Requirements were dispersants, such as glycerol trioleate, marine oil, Adipate polyester, sodium polyacrylate and phosphate ester. If Epoxy resin as a bonding system with the above preferred precursor and ceramic range used, the epoxy was about 1 to 10 weight percent, with respect to the mixture of Precursor and ceramic particles.

In connection with the present invention have been a variety of ceramic reinforcing fibers including those in the Table II below, together with their coefficients of thermal expansion (CTE) shown, rated:

reinforcing fibers Type CTE × 10 ^-6 per ° C A. Monofilaments Sapphire 7-9 Avco SCS-6 4.8 Sigma 4.8 B. Roving / yarn @ Nextel 440 4.4 Nextel 480 4.4 Sumitomo 8.8 DuPont FP 7.0 DuPont PRD-166 9.0 UBE 3.1 Nicolon 3.1 carbon 0 C. Cut fibers / whiskers @ Nextel 440 4.4 Saffil® 8.0

In a evaluated in connection with the present invention Example 1 contained the masterbatch blend slurry Al₂O₃ particles in the size range of about 0.2 to 50 microns (0.2 to 50 microns) as ceramic particles, a commercially as RTV silicone available as the ceramic precursor and as Bisphenol on the Mark located epoxy resin as a binder. In this typical mixture, the content of Al₂O₃  70 to 80 weight percent of silicone 10 to 30 weight percent and at epoxy 1 to 10 weight percent of the sum of Al₂O₃, silicone and binder. This was the mix Combination solvent trichloroethane and ethanol as the Liquid in an amount of about 20 to 30 weight percent, the remainder, 70 to 80 percent by weight, the above mixture to ceramic, precursor and binder was to the base material slurry to deliver.

In an example 2 was a combination of ceramic precursors contain. Such a mixture contained 70 to 80 Weight percent Al₂O₃ as the ceramic particles, 5 to 15 weight percent Silicone and 5 to 15 weight percent aluminum isopropoxide as the ceramic precursors, and, as the binder, Epoxy in an amount of 1 to 10 weight percent the sum of the ceramic particles, the precursor and the Binder. In the mixture was the combination solvent Trichloroethane and ethanol as the liquid in one Amount of about 20 to 30 weight percent, with the remainder, 70 up to 80% by weight, the mixture of ceramics, precursors and binder was added to the stock slurry deliver.

In one form of the process of the present invention has been each of the masterbatch mix slurries of the above Examples 1 and 2 around reinforcing ceramic fibers around in the shape of a tissue is mixed. In these examples were the reinforcing fibers from the Sumitomo yarn referred to above or roving, contained in the range of 20 up to 40% by volume of the component. In other forms and examples Both the reinforcing ceramic fibers were wound filament. In the present invention, it has been recognized that the reinforcing fibers in the range of about 10 to 50 volume percent  of the component, and preferably 30 to 40 vol%, are included. Less than 10 volume percent provides insufficient Reinforcement strength, and at more than about 50 volume percent the fibers are too tight for their arrangement subdivided the adequate base material around.

After allowing the prepreg to dry to the majority To evaporate the solvent, the thus formed Molded prepreg layers and pressed into a component, such as using compression molding, or a Autoclave, using temperature and pressure as this The person skilled in the art is known and practiced technically. Subsequently the component was in a fixed preform format cooled.

The preform was then processed at a processing temperature Range from 600 ° to 1000 ° C instead of the usual in known methods much higher sintering temperature, for example in the range of about 1300 ° to 1650 ° C, heated. This Heating is used to remove organic compounds, such as the temporary binder, and for conversion of the ceramic precursor into a ceramic bonding phase or phases carried out by decomposition. By the practice of the present invention under Inclusion of a binding precursor with the ceramic particles the processing temperature can be in a much lower Held as the area for sintering together the ceramic particles around the reinforcing fibers is needed around. Likewise, the invention allows the use of fibers otherwise known in the higher Sintered temperatures degraded or thermochemically damaged would.  

In the above Examples 1 and 2, the heating was applied to the Processing temperature in the range of about 600 ° to 800 ° C. carried out. Such heating results in a ceramic base material of ceramic particles, together connected by a ceramic phase or phases. In general the base material has an open porosity in the range of about 5 to 30 volume percent.

In another embodiment, the present invention concludes Invention Additional Levels of Reduction or Elimination such porosity. In such an embodiment becomes additional ceramic precursor in liquid Form, or usually in high concentration in one Liquid dispersed on the ceramic described above Applied base material and into the porosity infiltrated. For example, the base material in the dipped liquid ceramic precursor infiltrants and a vacuum applied to the penetration of the precursor to facilitate in the pores. After drying is heated the infiltrated base material as described above, heated around the infiltrated base material as described above, around the infiltrated ceramic precursor into a ceramic phase or -phasen and thereby a certain porosity to eliminate. Such a pore infiltration and Heating transfer can be repeated if desired, around the porosity in the base material to a desired one To reduce or eliminate scale.

The diagrammatic comparison of FIG. 1 illustrates a stress versus strain curve showing the resistance to breakage and toughness of the component made in accordance with the present invention. The data shown in this Figure 1 was obtained by examination at room temperature. The specimens used were rectangular test bars measuring 0.5 "x 6" x 0.1 "(12.7 mm x 152.4 mm x 2.54 mm).

The measured values represented by the curve 1 were obtained from the examination of a test piece obtained from the mixture of the above Example 1 as described without spreading the slurry around the reinforcing fibers. The material in the curve 1 is a monolithic matrix of ceramic particles, ceramic precursor and epoxy binder which is low in strength and catastrophically fails in a brittle manner. Monolithic ceramics of this type are not viable candidates for endangered forms in engineering applications due to their intolerance to imperfections and subsequent low toughness.

The measurement results shown by the curve 2 of Fig. 1 were obtained by examining a sample of the same size and shape as that used for the measurement results of the curve 1 prepared from the same mixture. However, the mixture was distributed around a reinforcing fiber fabric of Sumitomo yarn contained in an amount of about 30 volume percent of the component. The material in Curve 2 is a ceramic composite in which the same monolithic matrix material of Curve 1 was incorporated over and around the fiber reinforcements. The material had high strength because the load was now transferred to the high strength fibers and the material had good break and toughness. This type of composite behavior allows a part to have a prolonged life after incipient onset of fracture.

As can be seen from FIG. 1, the reinforced ceramic-base material composite component of curve 2 is significantly stronger and closer than that of curve 1 .

For comparison purposes, in Fig. 1, a curve 3 is given, which represents the use of sapphire-reinforcing fibers in a base material of Al₂O₃ and sintered at about 1450 ° to 1500 ° C, considerably above the temperature performance of the fibers indicated in Table II. No precursor was included in such a composite consisting of 55% by volume of aluminum silicate and 45% by volume of sapphire fibers. Accordingly, this mixture required the use of the sintering solidification temperature, significantly higher than the treatment temperature used in the process of the invention, generally about 600 ° to 1000 ° C. The material in curve 3 has a higher strength than curve 2 with tough behavior. These improved properties represent the benefits of using a higher strength reinforcing fiber with a thermally compatible base material to allow the stress from the base material to be transferred to the fiber in an efficient manner.

As can be seen from the comparison of Curve 2 representing the present invention and Curve 3 representing a part made by a variety of methods, the present invention provides a high strength, tough, reinforced ceramic composite made without a densification process ultra-high temperature. This is accomplished in the present invention by the use of a ceramic precursor which decomposes at a lower temperature to a ceramic phase which joins the ceramic particles and the reinforcing fibers together to form a composite part.

Typical of components that can be made in accordance with the present invention is a wing-like brace, useful in a hot section of a gas turbomachine, and shown in the fragmentary perspective sectional view of Fig. 2. The brace, generally indicated at 10 , includes a brace Bracing body 12 with a profile leading edge 14 and a profile trailing edge 16 . The strut 10 is sometimes referred to as a hollow strut because of the presence of a plurality of cavities 18 therein separated by fins 20 .

The brace 10 can be made by providing a plurality of layers, such as sipes, discs, bands, etc., made as described above. The fragmentary sectional view of FIG. 3 is schematic and representative of the arrangement of such layers, identified at 22 , around forming blocks 24 , such as aluminum, as an initial formation of the preform configuration of a portion of the brace of FIG. 2 in relation to the shape of FIG finished brace. In reality, each layer will have a thickness for this component, depending on fiber and shape, as known to those skilled in the art. For example, typical caliper dimensions range from about 0.008 to 0.020 inches (0.2032 to 0.508 mm). However, as is known to those skilled in the art, the number of layers actually required to produce such a laminated structure is much greater than the layers shown in FIG. 3 for the sake of simplicity. Additional individual fibers 25 are interposed between the layers within potential interstices between the layers at the curvature portions of the edges of the pore reduction blocks 24 .

After formation of the component of Fig. 3, assembled around the Formierblöcke 24, the assembly is placed for the purpose of lamination of the component in a suitable product preform within suitably shaped mating forming dies 26 A and 26 B in Fig. 4. Typically, a pressure, represented by arrows 28 , in the range of about 150 to 1000 pounds per square inch (10.34 to 68.95 bar) is applied to the component while it is being heated, for example in the range of 150 ° to 400 ° F (65.56 ° to 204.44 ° C) for an adequate time to allow proper lamination to occur. Such a temperature is not sufficient to allow the densification of the construction materials to occur.

After lamination, the preform thus formed is removed from the forming molds and the forming blocks are removed. The preform is then placed in an oven and heated to a temperature below 1000 ° C in a controlled manner to remove binder and plasticizer and then heated to a processing temperature at which no fiber degradation occurs, such as 1000 ° C or above to sinter the preform into a substantially dense ceramic matrix composite article of FIG. 2.

The simultaneously filed, related patent application with entitled "Compressed component and method and preform for the production "(Appl. No .: 12 662.5-13DV-09 230) which is expressly referred to, speaks that Problem of shrinkage of compacted ceramic particles and the resulting porosity. According to the invention the above-mentioned application becomes such Counteracted shrinkage by mixing with the ceramic  Particles before compaction particles of an inorganic Filler mixes, which has a net expansion of the ceramic particles during heating to the densification temperature having. Examined in the rating of this invention are the inorganic filler materials of pale-like crystal form, which in the following Table III are identified.

Table III

Filler materials

Such filler materials may be in a form of the present Invention used to during the heating Porosity formed on the processing temperature counteract. The proportion of the filler in the above Mixture is chosen so that the expansion of the filler any such porosity, however generated, counteracts.  

When the inorganic filler of the related application is in the base material blend of the present invention the ceramic particles and the precursor, and optionally of the binder, may contain such a filler in an amount of, for example, up to about 50% by weight the sum of the ceramic, the precursor, the optionally contained binder and the filler, be included. The proportion is selected so that the expansion the filler counteracts the porosity. Such Porosity could be due to the shrinkage of the ceramic Particles, but occurs mainly in the lower processing temperature of the transfer or the volume change of materials during heating the preform of the present invention in an oxidizing Atmosphere, as described herein. Typically, the porosity controlling mixture becomes the ceramic particles and the filler 50 to 93 weight percent ceramic particles and 7 to 50% by weight of inorganic Be filler, wherein the porositätssteuernde mixture more than 40% by weight up to about 90% by weight the base material mixture of particles, precursor and optionally represents binder. Preferred as inorganic filler materials are those which in the above Table III and the one lath-like Have crystal form. In particular, it has been found that pyrophyllite and wollastonite as fillers especially are usable. Likewise, reinforcing fibers increase which expand relative to the base material mixture, as stated in the disclosure of the expressly drawn related application, the ability of processing the preform at ambient pressure.

The present invention has been described in connection with typical,  although not limiting examples and embodiments from their related data. however it is for a person skilled in the art readily recognize that the present invention a multitude of modifications and variations within the scope of the following claims.

For all patents cited in the present specification and publications are expressly incorporated by reference and the disclosure of all these publications by this reference in its entirety in the present Registration integrated.

Claims (20)

A process for producing a fiber-reinforced ceramic base composite component characterized in that it comprises the steps of:
Providing a ceramic base precursor that converts to a ceramic phase upon heating, a liquid compatible with the precursor and ceramic discontinuous material containing particles,
Mixing together the ceramic base precursor, the liquid and the discontinuous material into a masterbatch slurry in which the ceramic particles and the precursor are substantially evenly distributed,
Providing a plurality of oxidation-stable reinforcing fibers,
Mixing the base material mixture slurry around the fibers to provide a prepreg preform,
Heating the preform in an oxidizing atmosphere at a processing temperature of at least one temperature required to convert the precursor to a ceramic phase and below a temperature that results in degradation of the ceramic in the preform ceramic substrate precursor ceramic phase precursor bonding ceramic particles from the slurry into a ceramic matrix material around the fibers and providing an environmentally stable, high strength, high strength, crack resistant ceramic base material fiber reinforced composite component. A method according to claim 1, characterized in that the base material mixture slurry contains:

• a) ceramic particles ranging from greater than 40 weight percent to about 90 weight percent of the sum of the ceramic particles and the ceramic precursor, and
• b) ceramic precursor in the range of about 10 to 40 weight percent of said sum, and wherein the reinforcing fibers are about 10 to 50 volume percent of the composite component.

3. The method according to claim 2, characterized that the reinforcing fibers are ceramic fibers are. 4. The method according to claim 2, characterized that the prepreg preform in air at a processing temperature in the range of about 600 ° is heated to 1000 ° C. 5. The method according to claim 2, characterized that a binder provided and in the slurry in the range of up to about 20% by weight the sum of the ceramic particles, the ceramic Precursors and the binder is included. 6. The method according to claim 5, characterized in that the base material mixture slurry contains:
70 to 80 weight percent of the sum of the ceramic particles, the ceramic precursor and the binder, wherein the ceramic particles 50 to 80 weight percent, the ceramic precursor 10 to 30 weight percent and the binder 1 to 20 weight percent of the sum, and
20 to 30 percent by weight of the liquid as an organic liquid. 7. The method according to claim 2, characterized that the ceramic precursor a Material is selected from the group consisting of organometallic, Sol gels, metal salts and their mixtures, and the ceramic particles contain material selected from the group consisting of oxides of Al, Si, Ca, Hf, B, Ti, Y, Zf and their mixtures and combinations. 8. The method according to claim 1, characterized that a variety of fibers in Form of a layer are provided, and the base material mixture around the fibers around in the Layer is mixed to provide a prepreg layer. 9. The method according to claim 8, characterized that a variety of prepreg layers laminated to a prepreg preform before heating are. 10. The method of claim 1 for the production of the composite component in a higher density, thereby characterized in that after heating the preform in an oxidizing atmosphere for the conversion of the  Ceramic base precursor in a ceramic phase of Composite component exposed to a Keramikinfiltrant precursor which is the open structure in the component infiltrated and then the infiltrated component in an oxidizing atmosphere is heated to the infiltrated Ceramic infiltrant precursor in a ceramic phase convert. 11. The method according to claim 1, characterized that the base material mix slurry except the ceramic particles a particulate contains inorganic filler, which has a net expansion with respect to the ceramic particles, when heated to the processing temperature, the proportion of the inorganic filler in the base material mixture is selected so that the expansion of the Filler in the preform during heating to the Processing temperature counteracts generated porosity. 12. A method according to claim 11, in which the base material mixture slurry contains a binder, characterized in that it comprises:

• (a) ceramic particles ranging from greater than 40 weight percent to about 90 weight percent of the sum of the ceramic particles, the ceramic precursor, the inorganic binder and the filler,
• (b) ceramic precursor in the range of about 10 to 40 percent by weight of said sum,
• (c) binders in the range of up to about 20% by weight of said sum, and
• (d) inorganic filler in the range of up to about 50 percent by weight of said sum.

13. The method according to claim 12, characterized in that

• (a) the ceramic particles are in the range of about 50 to 80 percent by weight of said sum,
• (b) the ceramic precursor is in the range of about 10 to 30 percent by weight of said sum,
• (c) the binder is in the range of about 1 to 20 percent by weight of said sum, and
• (d) the inorganic filler is in the range of about 7 to 50 percent by weight of said sum.

A fiber reinforced composite member of improved environmental resistance and improved combination of high strength and high fracture resistance, characterized in that it contains:
A variety of reinforcing fibers,
a ceramic matrix containing ceramic particles mixed around the reinforcing fibers, and
a ceramic bonding phase which bonds the ceramic particles and the reinforcing fibers together. 15. Component according to claim 14, characterized that the reinforcing fibers about 10 to 50 percent by volume of the component amount. 16. Component according to claim 14, characterized that containing the plurality of layers ceramic bonded ceramic particles and reinforcing Fibers are connected together. 17. Component according to claim 14, characterized that the reinforcing fibers are ceramic  are, and thus a ceramic base material, ceramic fiber reinforced Composite component, determine. 18. Component according to claim 14, characterized that he is in the ceramic base material contains a filler of an inorganic material, which has a crystal form of pale-like type. 19. Component according to claim 14, characterized in that the ceramic particles are in the range of about 7 to 50 weight percent of the sum of the ceramic particles and the ceramic bonding phase,
the ceramic bonding phase is in the range of about 1 to 20 percent by weight of said sum, and
the reinforcing fibers are in the range of about 10 to 50 volume percent of the component. 20. Component according to claim 19, characterized that is a filler of inorganic Material with a crystal form of pale type in the Range of about 7 to 50 percent by weight of the sum of the ceramic Particles, the ceramic bonding phase and the Filler is included.