Method of forming Ceramic matrix composites using modified hydrogen silsesquioxane resin

Abstract: Disclosed are novel ceramic matrix composites in which coated refractory fibers are imbedded in a ceramic matrix derived from a modified hydrogen silsesquioxane resin.

Description: The present invention provides a method of forming fiber-reinforced ceramic matrix composites using modified hydrogen silsesquioxane resin as a matrix for refractory fibers. These composites are formed into complex shapes which have good oxidation resistance at high temperatures, strength and toughness. Ceramic matrix composites and methods for their production are well known in the art. For instance, several recent articles such as Mah et al., Ceramic Bulletin, Vol. 66, No. 2 (1987), and Schioler et al., Ceramic Bulletin, Vol. 65, No. 2 (1986), describe various matrices and fibers used in ceramic matrix composites as well as a variety of processing techniques used for their production. The composite materials and methods described therein, however, differ from those claimed herein. Similarly, Chi et al. in US Patents 4,460,639 and 4,460,640 and Haluska in US Patent 4,460,630 disclose ceramic matrix composites and their methods of manufacture. It is taught therein that organosilsesquioxanes, organopolysiloxanes and polysilazanes, respectively, are used as matrix precursors in polymer infiltration processes. Those patents, however, do not describe the use of hydrogen silsesquioxane resin (H-resin) as a polymeric matrix precursor. H-resin is also known in the art. For instance, US Patent 3,615,272 reveals the production of soluble H-resin by the hydrolysis and condensation of a silane in a sulfuric acid medium. Similarly, US Patent 4,756,977 teaches the use of H-resin to form protective ceramic coatings on electronic devices. Those patents, however, do not describe modification of the H-resin nor the use of the resin as a matrix precursor in ceramic matrix composites. US-A-5 318 930 discloses a fiber reinforced glass composite having a refractory fiber in a matrix of a black glass ceramic. WO 93/14040 discloses a fiber reinforced glass composite having a carbon-coated refractory fiber in a matrix of a black glass ceramic. However, neither of these documents describes the use of a hydrogen silsesquioxane resin (H-resin) as a polymeric matrix precursor. We have unexpectedly found that modified H-resins can be used to prepare ceramic matrix composites with excellent mechanical properties. The present invention introduces a method of forming a fiber-reinforced ceramic matrix composite comprising a ceramic matrix comprising silicon, carbon and oxygen having a char stoichiometry of SiO y C z , wherein y = 1.2 to 1.6, z = 0.2-0.6, and within the ceramic matrix, a refractory fiber coated with a material which provides an interface between the refractory fiber and the ceramic matrix, which method comprises (a) impregnating an assembly of refractory fibers having an interfacial coating thereon with a preceramic matrix mixture comprising modified hydrogen silsesquioxane resin of the structure (HSi0 1.5 ) x (R 1 R 2 R 3 SiO 0.5 ) y , wherein R 1 , R 2 and R 3 are independently selected from hydrogen, alkyls and aryls, x is 0.25 to 0.99, y is 0.75 to 0.01 and x + y = 1.0, and having a number average molecular weight (Mn) in the range of between 500 to 2500; (b) forming the impregnated assembly of fibers into the desired shape; (c) curing the formed impregnated assembly of fibers; and (d) heating the cured impregnated assembly of fibers of (c) to a temperature of at least 1000°C. in an inert atmosphere for a time effective to convert the modified hydrogen silsesquioxane resin to a ceramic. Our invention is based on the discovery that ceramic matrix composites are formed using modified H-resin as the matrix precursor. This was particularly unexpected since H-resin does not have carbon in its repeating units and high carbon levels were previously believed essential in the fabrication of desirable composites. We have now found that composites containing small amounts of carbon have surprisingly excellent strength and toughness even at elevated temperatures in air. The refractory fibers which may be used in this invention comprise any high-modulus fibers which are compatible with the modified H-resin, matrices and any of the fiber coatings described herein and which can also withstand polymer infiltration processing. Many of these fibers are known in the art and are commercially available. Examples of suitable fibers include those of silicon carbide, silicon nitride, silicon carbide deposited on a carbon core, aluminum borate, aluminum oxide, silicon oxide, silicon carbide containing titanium, silicon oxycarbides, silicon oxycarbonitrides, carbon and the like. Generally, such fibers should have a modulus greater than 100 GPa, preferably greater than 150 GPa. These fibers may contain any desirable number of filaments per tow and have a diameter in the range of 5 to 500 micrometers. Examples of specific fibers include silicon carbide fibers with a diameter in the range of 10-20 micrometers manufactured by Nippon Carbon and sold under the name "Nicalon™"; fibers comprising silicon carbide deposited on a carbon core with a diameter of 143 micrometers manufactured by Avco and designated "SCS-6"; alumina-boria-silica fibers with a diameter of 10-12 micrometers manufactured by 3M and sold under the names "Nextel™ 312", "Nextel™ 440" and "Nextel™ 480"; Al 2 O 3 fibers with a diameter of 20 micrometers manufactured by Du Pont under the designation "FP"; SiO 2 fibers with a diameter of 8-10 micrometers manufactured by J. P. Stevens; Al 2 O 3 -SiO 2 fibers with a diameter in the range of 9-17 micrometers manufactured by Sumitomo; silicon carbide fibers containing titanium with a diameter in the range of 8-10 micrometers manufactured by Ube and sold under the name "Tyranno™"; silicon carbide fiber with a diameter in the range of 6-10 micrometers manufactured by Avco; silicon oxycarbonitride fibers with a diameter in the range of 10-15 micrometers manufactured by Dow Corning designated "MPDZ" and "HPZ"; silicon carbide fibers with a diameter in the range of 10-15 micrometers manufactured by Dow Corning designated "MPS"; silicon nitride fibers such as those produced by Tonen or Rhone Poulenc, Al 2 O 3 -ZrO 2 fibers with a diameter of 20 micrometers manufactured by Du Pont and Designated "PRD-166" and crystalline silicon carbide fibers produced by Dow Corning. Although any of the above fibers are functional, those preferred herein comprise ceramic fibers of silicon, carbon, nitrogen and/or oxygen. Especially preferred are "Nicalon™" silicon oxycarbide fibers and crystalline silicon carbide fibers. These fibers may be used in nearly any length and may be arranged in the matrix in nearly any manner desired. Generally, the fibers are essentially continuous and are either aligned unidirectionally, woven as a 2-dimensional fabric or shaped as a 3-dimensional reinforced preform. Such versatility in architecture is another advantage of the present composite system over prior art composites. The fibers of this invention may also be provided with a coating to toughen the composite by preventing bonding and chemical reactions between the fibers and the matrix. This allows our fibers to debond and pullout under stress such that our composite does not undergo catastrophic failure as demonstrated by traditional ceramic monoliths. Generally, any interfacial coating which has the above effect and which is compatible with the fiber and the matrix may be used herein. These include, for example, coatings of carbon, boron nitride, silicon carbide, silicon nitride, aluminum nitride and their combinations. Such coatings and methods for their deposition are well known in the art. For instance, US Patent 4,885,199 shows the application of various interfacial coatings such as carbon on ceramic fibers. US Patent 4,642,271 claims the chemical vapor deposition of boron nitride on fibers. EPA 90311185.4 describes the application of B-N-C coatings on fibers. Additionally, it is noted that certain fibers, when heated in the matrix, form in-situ interfacial layers such as carbon or boron nitride which may also serve the same purpose as those described above. The coatings of our invention are generally used in thicknesses which allow the fibers to debond and pullout under stress. Although the thickness is dependent on coating quality, typical thicknesses are generally in the range of 0.05 to 1.0 micrometer. Especially preferred in the present invention is the use of boron nitride coatings or coating combinations which contain boron nitride. We have found that when fibers with such coatings are incorporated within the matrix of the present invention, they will possess novel long-term stability at elevated temperatures in air. This is particularly unexpected in the art since boron nitride coated fibers are generally known to undergo oxidative degradation under such conditions. Thus, the composites of the present invention retain their properties under conditions which adversely affect the prior art composites. The matrix precursor material to be used herein is modified H-resin. H-resin is formed by the hydrolysis or partial hydrolysis of HSiX 3 , wherein X is a hydrolyzable substituent. Exemplary hydrolyzable substituents include halogens such as chlorine, fluorine and bromine; and hydrocarbonoxy groups such as alkoxy or acyloxy. The resultant resins have the formula HSi(OH) x (x) y O z/2 , in which each X is a hydrolyzable substituent as defined above, x = 0-2, y = 0-2, z = 1-3, x + y + z = 3. As such, these resins may be fully condensed (HSiO 3/2 ) n or they may be only partially hydrolyzed (i.e., containing some Si-X) and/or partially condensed (i.e., containing some Si-OH). Although not represented by this structure, these resins may contain a small number (e.g., less than 10%) of silicon atoms which have either 0 or 2 hydrogen atoms attached thereto due to various factors involved in their formation or handling. Methods for producing H-resin are known in the art. For example, it is known to hydrolyze an alkoxy or acyloxy silane with water in an acidic, alcoholic hydrolysis medium. Similarly, US Patent 3,615,272 produces a nearly fully condensed H-resin (which may contain up to 100-300 ppm silanol) by a process comprising hydrolyzing trichlorosilane in a benzenesulfonic acid hydrate hydrolysis medium and then washing the resultant resin with water or aqueous sulfuric acid. Additionally, US Patent 5,010,159 claims an alternative method comprising hydrolyzing hydridosilanes in an arylsulfonic acid hydrate hydrolysis medium to form a resin which is then contacted with a neutralizing agent. The H-resin used in this invention is generally modified to render it more useful in the formation of ceramic composites. Without modification, H-resin has a broad molecular weight range which can lead to a wide variability in the physical properties of the resin which, in turn, lead to variability in processing. Additionally, the broad molecular weight range of the resin can lead to decreased ceramic yields due to vaporization of low molecular weight species. Therefore, we have developed a method for tailoring the molecular weight distribution of the resin to eliminate these problems. This tailoring affords one the ability to make resins having, for instance, the appropriate rheological properties needed for ceramic fabrication techniques such as cloth lay-up of ceramic matrix composites, resin transfer molding (RTM) of ceramic matrix composites and reinfiltration of porous ceramic bodies. Similarly, the modification renders the resin curable under moderate conditions such as mild heat, radiation, curing catalysts or curing agents. This curability is essential to the invention to increase the ceramic yield and to inhibit the composite from delaminating during pyrolysis. Generally, the H-resin modification is performed by endcapping the resin with a material containing Si-C and Si-H bonds. Examples of such materials are those generally encompassed by the structure (R 1 R 2 R 3 Si) 2 O wherein R 1 , R 2 and R 3 are independently selected from hydrogen, alkyls such as methyl, ethyl and propyl or aryls such as phenyl. Specific compounds include tetramethyldisiloxane and hexamethyldisiloxane. The endcapping and molecular weight control is generally accomplished by redistribution under acid/water conditions in the presence of the endcapping agent. The ratio of the H-resin to endcapping agent in this reaction is used to tailor the molecular weight of the resin. Generally, the molar ratio of H-resin to endcapping agent is in the range of 10:1 to 1:10. The expression "modified H-resin", therefore, is used to describe these endcapped resins which are curable and have tailored molecular weights. Preferably, the number average molecular weight (Mn) for these materials are in the range of 500 to 2500. The modified H-resin has the structure (HSiO 1.5 ) x (R 1 R 2 R 3 SiO 0.5 ) y , wherein R 1 , R 2 and R 3 are independently selected from hydrogen, alkyls and aryls, x is 0.25 to 0.99, y is 0.01 to 0.75 and x + y = 1.0. Preferably, R 1 , R 2 and R 3 are independently selected from hydrogen and methyl, x is 0.5 to 0.99, y is 0.01 to 0.5 and x + y = 1.0. More preferably, the modified H-resin has the structure (HSiO 1.5 ) x (Me 2 HSiO 0.5 ) y , wherein x is 0.5 to 0.99, y is 0.01 to 0.5 and x + y = 1.0. When the resultant H-resin is pyrolyzed, the char composition has a stoichiometry of approximately SiO y C Z , wherein y = 1.2 to 1.6 and z = 0.2 to 0.6. Although not wishing to be bound by theory, it is thought that when a composite incorporating such a resin is heated in an oxidizing environment, the surfaces of the composite exposed to the environment form in-situ silica (SiO 2 ) coatings. These coatings seal the exposed surface and protect the matrix and the interfacial coating on the fiber from further oxidation when subsequently heated in an oxidizing environment. In addition to the above fibers and matrices, the composites of the present invention may also contain fillers. Fillers are used herein to decrease the amount of matrix shrinkage which occurs on pyrolysis so that the resultant composites have lower porosity. Suitable fillers are known in the art and include, for example, powders, whiskers or particulates of Al 2 O 3 , SiO 2 , other metal oxides, silicon carbide, silicon nitride, silicon hexaboride, aluminum nitride, boron nitride and the like. The preferred fillers to be used herein are boron nitride, silicon carbide, silicon nitride and aluminum nitride. Such fillers are generally included in amounts up to 80 volume percent based on the volume of modified H-resin material. The composites of this invention may also contain materials which assist in curing (crosslinking) the H-resin. These curing agents may be activated by heating the green body containing the curing agent to temperatures in the range of 50-300°C. (i.e., the activation of a free radical precursor) or they may be crosslinked at room temperature. Curing agents are well known in the art. Examples include free radical precursors such as organic peroxides (dibenzoyl peroxide, bis- p -chlorobenzol peroxide, bis-2,4-dichlorobenzol peroxide, di- t -butyl peroxide, dicumyl peroxide, t -butyl perbenzoate, 2,5-bis( t -butylperoxy)-2,3-dimethylhexane and t -butyl peracetate); and platinum-containing curing agents such as platinum metal, H 2 PtCl 6 and ((C 4 H 9 ) 3 P) 2 PtCl 2 . Other conventional curing agents known in the art may also be used. The curing agent is present in an effective amount, i.e. an amount sufficient to induce crosslinking in the H-resin. Normally, however, the peroxide curing agent will be present at 0.1 to 5.0 weight percent based on the weight of the compound to be cured, with the preferred amount being 2.0 weight percent. When platinum-containing curing agents are used, the amount will normally be such that platinum is present at 1 to 1000 ppm based on the weight of the compound to be cured with the preferred amount being 50 to 150 ppm platinum. Examples of crosslinking agents include, for example, polyfunctional organosilicon compounds such as silanes, silazanes or siloxanes. The preferred crosslinking agents are organosilicon compounds with Si-H or Si-Vi functional bonds. The composites herein are produced by polymer infiltration. This process comprises first impregnating the coated fibers with a liquid preceramic mixture comprising the modified H-resin and, if desired, fillers. This preceramic mixture is formed by either a solution or melt route. In the solution route, the modified H-resin and fillers are mixed in an organic solvent. The preferred solvents are those with a low vaporization point (such as lower than 125°C.) at atmospheric pressure to facilitate removal from the impregnated fibers and those with less than 1 percent by weight water. Examples of suitable organic solvents include aliphatic hydrocarbons such as hexane or heptane and aromatic hydrocarbons such as benzene or toluene. The concentration of H-resin in solution can be varied over a wide range with higher concentrations generally resulting in larger amounts of the preceramic polymer impregnating the fiber. Preferably, concentrations in the range of 30 to 60 weight percent are employed herein. In the melt route, the modified H-resin is heated to a temperature above its melting point yet below its curing temperature in an inert environment to form the preceramic mixture. Fillers may also be mixed in the molten polymer if desired. The fibers are then impregnated with the preceramic mixture by any convenient means. For instance, the fibers can be immersed in the mixture, sprayed with the mixture or held under a stream of the mixture. The impregnated fibers can additionally be manipulated to uniformly distribute the matrix mixture in the fibers. Following impregnation, any excess matrix mixture on the fibers is allowed to drain off. If the solution route to the preceramic mixture is used, the solvent is allowed to evaporate. Generally, any practical method such as air evaporation at room temperature or the use of vacuum or mild heat can be used. The resultant fibers which have been impregnated and the solvent evaporated are commonly called a "pre-preg". If the melt method to the preceramic mixture is used, the impregnated fibers are merely cooled to form the "pre-preg". Alternatively, however, the melt impregnated fibers may be formed prior to cooling by a process such as filament winding or pulltrusion. When these formed fibers are cooled, they can be immediately cured and fired as set forth below. The prepregs formed above may, optionally, be partially cured so that they will hold the shape imparted in a subsequent step. This partial curing, also called "B-staging", is generally accomplished by heating in air at a temperature in the range of 50 to 150°C. for 2 minutes to 4 hours. Generally, heating at 100°C. for 10 to 15 minutes is sufficient. This heating may be conducted by any appropriate means, but the use of an air convection oven or similar equipment is usually sufficient. Care should be taken during this curing step to avoid temperature and time combinations which result in excessive curing such that flowability of the resin in the later molding or pressing steps is significantly reduced. The prepreg is then subjected to externally applied pressure while heating to form the composite into the desired shape and cause uniformity of resin about the fibers. Generally, this is accomplished by pressing the prepreg into a mold at a temperature and pressure which allows the resin to flow throughout the mold. The pressing conditions generally used include temperatures in the range of 60 to 300°C., pressures in the range of 0.07 to 175 kg/cm 2 and times in the range of 2 minutes to 6 hours. Pressing at 175°C., 14-28 kg/cm 2 and 30 to 180 minutes generally provides satisfactory results. Temperatures and pressures which result in resin being forced out of the mold should be avoided. It should be noted that if a 3-dimensional (3-D) shape is desired, the above steps are often altered. To manufacture 3-D objects by this process, one generally first forms the fiber into the desired shape and then impregnates the formed fiber with the polymer mixture. The impregnated fibers are then pressed, cured and fired as above. The formed prepreg is next infusibilized (cured) to insure complete or nearly complete crosslinking such that deformation on pyrolysis will not occur. Any schedule which produces the desired result may be used so long as the temperature does not cause ceramification. A preferred schedule comprises heating at less than 5°C./minute to 285°C. and then holding for 16 hours. This curing step may be performed in the mold under pressure or it may be accomplished in a conventional oven under nitrogen without any applied pressure. The pressed and cured product (green composite or molded part) is then slowly fired in a furnace to a temperature of at least 1000°C. in an inert atmosphere or vacuum until the product ceramifies. It is preferred that the green composite be fired at a temperature of 1200°C. By slow firing, it is meant that the composites are heated in a slow (e.g., 2°C./min), stepwise or linear fashion until the majority of any higher boiling volatiles present escape the composite after which time the temperature can be quickly raised to the ultimate firing temperature. For example, the temperature for most composites should be raised to near 300°C. and the heating slowly continued until a temperature of 800°C. is reached after which the temperature can be raised rather quickly to the ultimate firing temperature. After completion of the firing process the composite is cooled. At least the initial cooling should also be under an inert atmosphere. When cooled, the resulting material is a uniform, hard, strong fiber reinforced composite. The volume percentage of fibers in the resulting composite can vary over a wide range depending on the desired use. Generally, it is preferred that 10 to 65 volume percent of the composite is fiber. The composites formed by the above process are generally quite porous. Since it may be preferred to produce dense objects (which have higher strength), it is within the scope of this invention to reimpregnate the composites formed above. This is accomplished by merely impregnating the composite with the preceramic matrix mixture (without fillers) as described above (by either the solution or melt route), curing the reimpregnated composite and then firing. This "reimpregnation" can be repeated until products with the desired density and strength are achieved. The composites herein have many desirable properties such as good oxidation resistance at high temperatures, high strength and toughness and a wide range of dielectric properties. For instance, the four-point flexural strength of the composites measured at room temperature and at temperatures up to 1100°C. in air generally exceed 2100 kg/cm 2 and often exceed 3500 kg/cm 2 . Similarly, the tangent modulus of these composites often exceed 700,000 kg/cm 2 . The following non-limiting examples are provided so that one skilled in the art might better understand the invention. Throughout this specification, "Me" represents a methyl group, "Ph" represents a phenyl group and "Vi" represents a vinyl group. All reactions were carried out in an argon atmosphere in laboratory glassware. H-resin was obtained from Dow Corning Corporation and was produced by the method of US Patent 3,615,272. (Me 2 HSi) 2 O was purchased from Huls Systems. Trifluromethaneacetic acid was purchased from Aldrich Chemical. All NMR spectra were recorded on a Varian™ VXR200T spectrometer. Solution spectra were recorded in CDCl 3 in a 5 mm switchable probe ( 1 H, 399.95 MHz) or a 16 mm Si-free probe ( 29 Si, 79.46 MHz) and referenced to internal CDCl 3 (7.25 ppm, 1 H) or TMS (0 ppm). The integrals were normalized and calculated relative to the siloxane species. Chromium acetylacetonate (0.02 M) was added for the 29 Si spectra to ensure quantitative acquisition. Gel permeation chromatography (GPC) data were obtained on a Waters™ GPC equipped with a model 600E systems controller, a model 490 UV and model 410 Differential Defractometer detectors interfaced to a Digital™ Professional 380 computer employing Waters™ 'Expert' software; all values are relative to polystyrene standards. Carbon, hydrogen and nitrogen analysis were done on a Control Equipment Corporation 240-XA Elemental Analyzer. Oxygen analyses were done on a Leco™ Oxygen Analyzer equipped with an Oxygen Determinator 316 (Model 783700) and an Electrode Furnace EF100. Silicon was determined by a fusion technique which consisted of converting the silicon material to soluble forms of silicon and analyzing the solute for total silicon by atomic absorption spectrometry. All furnace firings were done in a Lindberg tube furnace, Model 54233 equipped with a Eurotherm controller. Example 1 Preparation of (HSiO 1.5 ) 0.90 (Me 2 HSiO 0.5 ) 0.10 Polymer Synthesis A toluene solution (approximately 20% by weight solids) of H-resin, 265 g (53 g of H-resin), was placed in a 500 mL three necked round bottom flask fitted with an overhead stirrer, thermometer and condenser under argon. To this solution were added 67 g of (Me 2 HSiO) 2 , one equivalent of (Me 2 HSiO) 0.5 , 1 g of trifluoroacetic acid and 1 g of water. The resulting solution was refluxed 24 hours. The reaction was cooled and 1 g of CaCO 3 and 5 g of water were added to neutralize the acid. The flask was fitted with a Dean Stark trap and the water was removed by azetroping dry over an 8 hour period. The reaction was cooled and 5 g of Me 2 HSiCl added and allowed to stir overnight. The polymer was isolated by filtration through a 1.0 micrometer membrane and by removing the solvent in vacuo at 50°C. The polymer was characterized by GPC molecular weight analysis: Mw=5,809; Mn=1,222 and z=4.75. 1 H NMR showed a broad singlet 4.8 ppm (1 H, Me 2 HSiO 0.5 ), a broad multiplet at 4.4 ppm (9 H, HSiO 1.5 ) and a broad singlet at 0.3 ppm (6.2 H, (Me) 2 HSiO 0.5 ). Crosslinking and Conversion to a Ceramic A sample of the above resin, 4.0 g, was blended with 1.0 g of vinyl functional siloxane fluid of the formula (MeSiO 1.5 ) 0.10 (MeViSiO) 0.90 and 0.05 g of dicumuyl peroxide. The above mixture was heated to 150°C. under Ar to afford a brittle solid in 99% yield. An aliquot of this cured material was then weighed in an alumina boat and transferred to a Lindberg tube furnace. The furnace was continuously purged with argon and the sample heated to 1200°C. at 10°C./minute and held at temperature for 1 hour before cooling back to ambient temperatures. The ceramic yield was 85.3% and the ceramic analysis was C:9.3; Si:43.9; 0:40.95. Oxidation of the Ceramic The above ceramic was ground in a synthetic sapphire mortar and pestle to a fine powder. An aliquot of this powder was then weighed in an alumina boat and transferred to a Lindberg tube furnace. The sample was heated to 1000°C. at 10°C./minute in flowing air and held at temperature for 10 hours before cooling back to ambient temperatures. The % weight change was found to be 0.5% and the material had the following ceramic analysis of C:8.3; Si:37.5; 0:41.95. Example 2 Preparation of (HSiO 1.5 ) 0.65 (Me 2 HSiO 0.5 ) 0.35 Polymer Synthesis A toluene solution (approximately 20% by weight solids) of H-resin, 650 g (130 g of H-resin), was placed in a 1 L three necked round bottom flask fitted with an overhead stirrer, thermometer and condenser under argon. To this solution were added 160 g of (Me 2 HSiO) 2 , 2.38 equivalents of (Me 2 HSiO) 0.5 , 2.5 g of trifluoroacetic acid and 2.5 g of water. The resulting solution was refluxed 48 hours. The reaction was cooled and 2.5 g of CaCO 3 and 10 g of water were added to neutralize the acid. The flask was fitted with a Dean Stark trap and the water was removed by azetroping dry over an 24 h period. The polymer was isolated by filtration through a 1.0 micrometer membrane and by removing the solvent in vacuo at 50°C. The yield was 222 g. The polymer was characterized by GPC molecular weight analysis: Mw=4,269; Mn=1,407 and z=3.03. 1 H NMR showed a broad singlet 4.7 ppm (3.5 H, Me 2 HSiO 0.5 ), a broad multiplet at 4.4 ppm (6.5 H, HSiO 1.5 ) and a broad singlet at 0.2 ppm (12.5 H, (Me) 2 HSiO 0.5 ). 29 Si NMR showed a broad doublet at -4.0 ppm (1 Si, (Me) 2 HSiO 0.5 ) and a broad doublet at -85 ppm (1.68 Si, HSiO 1.5 ). Crosslinking and Conversion to a Ceramic A sample of the above resin, 4.0 g, was blended with 1.0 g of vinyl functional siloxane fluid of the formula (MeSiO 1.5 ) 0.10 (MeViSiO) 0.90 and 0.05 g of dicumuyl peroxide. The above mixture was heated to 150°C. under Ar to afford a brittle solid in 99% yield. An aliquot of this cured material was then weighed in an alumina boat and transferred to a Lindberg tube furnace. The furnace was continuously purged with argon and the sample heated to 1200°C. at 10°C./minute and held at temperature for 1 hour before cooling back to ambient temperatures. The ceramic yield was 71.2% and the ceramic analysis was C:15.1; Si:45.5; O:33.4. Oxidation of the Ceramic The above ceramic was ground in a synthetic sapphire mortar and pestle to a fine powder. An aliquot of this powder was then weighed in an alumina boat and transferred to a Lindberg tube furnace. The sample was heated to 1000°C. at 10°C./minute in flowing air and held at temperature for 10 hours before cooling back to ambient temperatures. The % weight change was found to be +1.1 % and the material had the following ceramic analysis C:11.9; Si:42.5; O:37.5. Example 3 Preparation of (HSiO 1.5 ) 0.92 (Me 2 HSiO 0.5 ) 0.08 Polymer Synthesis A toluene solution (approximately 40% by weight solids) of H-resin (Mw=9,667; Mn=1200; z=8.05), 358 g (143 g of H-resin), was placed in a 1 L three necked round bottom flask fitted with an overhead stirrer, thermometer and condenser under argon. To this solution were added 20.1 g of (Me 2 HSiO) 2 , 0.3 equivalents of (Me 2 HSiO) 0.5 , 2.0 g of trifluoroacetic acid and 2.0 g of water. The resulting solution was refluxed 40 hours. The reaction was cooled and 2.0 g of CaCO 3 and 10 g of water were added to neutralize the acid. The flask was fitted with a Dean Stark trap and the water was removed by azetroping dry over an 24 hour period. The polymer was isolated by filtration through a 1.0 micrometer membrane and by removing the solvent in vacuo at 50°C. The yield was 160 g. The polymer has a Tg of 29°C and was characterized by GPC molecular weight analysis: Mw=29,010; Mn=1,653 and z=17.74. 29 Si NMR showed a broad doublet at -3.0 ppm (1 Si, (Me) 2 HSiO 0.5 ) and a broad doublet at -85 ppm (11.12 Si, HSiO 1.5 ). As a test of the stability of this polymer, the GPC molecular weight was measured twice a week for 3 weeks after which time it was apparent that the molecular weight of the polymer was drifting upwards and the polymer was becoming less soluble and leading to gelation. Crosslinking and Conversion to a Ceramic A sample of the above resin, 4.0 g, was blended with 1.0 g of vinyl functional siloxane fluid of the formula (MesiO 1.5 ) 0.10 (MeViSiO) 0.90 and 0.05 g of dicumuyl peroxide. The above mixture was heated to 150°C. under Ar to afford a brittle solid in 99% yield. An aliquot of this cured material was then weighed in an alumina boat and transferred to a Lindberg tube furnace. The furnace was continuously purged with argon and the sample heated to 1200°C. at 10°C./minute and held at temperature for 1 hour before cooling back to ambient temperatures. The ceramic yield was 88.7% and the ceramic analysis was C:6.93; Si:46.3; O:42.5. Oxidation of the Ceramic The above ceramic was ground in a synthetic sapphire mortar and pestle to a fine powder. An aliquot of this powder was then weighed in an alumina boat and transferred to a Lindberg tube furnace. The sample was heated to 1000°C. at 10°C./minute in flowing air and held at temperature for 10 hours before cooling back to ambient temperatures. The % weight change was found to be +1.1 % and the material had the following ceramic analysis C:5.6; Si:44.2; O:45.2. Example 4 Preparation of (HSiO 1.5 ) 0.92 (Me 2 HSiO 0.5 ) 0.08 Polymer Synthesis A toluene solution (approximately 18% by weight solids) of H-resin (Mw=9,667; Mn=1200; z=8.05), 796 g (143 g of H-resin), was placed in a 1 L three necked round bottom flask fitted with an overhead stirrer, thermometer and condenser under argon. To this solution were added 20.1 g of (Me 2 HSiO) 2 , 0.3 equivalents of (Me 2 HSiO) 0.5 , 2.0 g of trifluoroacetic acid and 2.0 g of water. The resulting solution was was refluxed 40 hours. The reaction was cooled and 2.0 g of CaCO 3 and 10 g of water were added to neutralize the acid. The flask was fitted with a Dean Stark trap and the water was removed by azetroping dry over a 24 hour period. The polymer was isolated by filtration through a 1.0 micrometer membrane and by removing the solvent in vacuo at 50°C. The yield was 179 g. The polymer has a Tg of -39°C. and was characterized by GPC molecular weight analysis: Mw=9,194; Mn=1,338 and z=6.87. 29 Si NMR showed a broad doublet at -3.0 ppm (1 Si, (Me) 2 HSiO 0.5 ) and a broad doublet at -85 ppm (12.175 Si, HSiO 1.5 ). As a test of the stability of this polymer, the GPC molecular weight was measured twice a week for 6 weeks after which time it was apparent that the molecular weight of the polymer was not changing at all, indicating that the material was not gelling. Crosslinking and Conversion to a Ceramic A sample of the above resin, 4.0 g, was blended with 1.0 g of vinyl functional siloxane fluid of the formula (MeSiO 1.5 ) 0.10 (MeViSiO) 0.90 and 0.05 g of dicumuyl peroxide. The above mixture was heated to 150°C. under Ar to afford a brittle solid in 99% yield. An aliquot of this cured material was then weighed in an alumina boat and transferred to a Lindberg tube furnace. The furnace was continuously purged with argon and the sample heated to 1200°C. at 10°C./minute and held at temperature for 1 hour before cooling back to ambient temperatures. The ceramic yield was 89.6% and the ceramic analysis was C:10.17; Si:48.7; O:35.8. Oxidation of the Ceramic The above ceramic was ground in a synthetic sapphire mortar and pestle to a fine powder. An aliquot of this powder was then weighed in an alumina boat and transferred to a Lindberg tube furnace. The sample was heated to 1000°C. at 10°C./minute in flowing air and held at temperature for 10 hours before cooling back to ambient temperatures. The % weight change was found to be +0.8 % and the material had the following ceramic analysis C:9.08; Si:42.3; O:40.3. Example 5 Preparation of (HSiO 1.5 ) 0.92 (Me 2 HSiO 0.5 ) 0.08 Polymer Synthesis A toluene solution (approximately 18% by weight solids) of H-resin, 796 g (143 g of H-resin), was placed in a 1 L three necked round bottom flask fitted with an overhead stirrer, thermometer and condenser under argon. To this solution were added 20.1 g of (Me 2 HSiO) 2 , 0.3 equivalents of (Me 2 HSiO) 0.5 , 2.0 g of trifluoroacetic acid and 2.0 g of water. The resulting solution was refluxed 40 hours. The reaction was cooled and 2.0 g of CaCO 3 and 10 g of water were added to neutralize the acid. The flask was fitted with a Dean Stark trap and the water was removed by azetroping dry over a 24 hour period. The polymer was isolated by filtration through a 1.0 micrometer membrane and by removing the solvent in vacuo at 50°C. The yield was 160 g. The polymer had a Tg of 29°C. and was characterized by GPC molecular weight analysis: Mw=29,010 and Mn=1,635. 29 Si NMR showed a broad doublet at -3.0 ppm (1 Si, (Me) 2 HSiO 0.5 ) and a broad doublet at -85 ppm (12.175 Si, HSiO 1.5 ). Crosslinking and Conversion to a Ceramic A sample of the above resin, 4.0 g, was blended with 1.0 g of vinyl functional siloxane fluid of the formula (MeSiO 1.5 ) 0.10 (MeViSiO) 0.90 and 0.05 g of dicumuyl peroxide. The above mixture was heated to 150°C. under Ar to afford a brittle solid in 99% yield. An aliquot of this cured material was then weighed in an alumina boat and transferred to a Lindberg tube furnace. The furnace was continuously purged with argon and the sample heated to 1200°C. at 10°C./minute and held at temperature for 1 hour before cooling back to ambient temperatures. The ceramic yield was 89% and the ceramic analysis was C:6.93; Si:46.3; O:42.5. Oxidation of the Ceramic The above ceramic was ground in a synthetic sapphire mortar and pestle to a fine powder. An aliquot of this powder was then weighed in an alumina boat and transferred to a Lindberg tube furnace. The sample was heated to 1000°C. at 10°C./minute in flowing air and held at temperature for 10 hours before cooling back to ambient temperatures. The % weight change was found to be +1.1 % and the material had the following ceramic analysis C:5.57; Si:44.2; O:45.2. Example 6 Preparation of (HSiO 1.5 ) 0.63 (Me 2 HSiO 0.5 ) 0.37 Polymer Synthesis A toluene solution (approximately 18% by weight solids) of H-resin, 650 g (117 g of H-resin), was placed in a 1 L three necked round bottom flask fitted with an overhead stirrer, thermometer and condenser under argon. To this solution were added 160 g of (Me 2 HSiO) 2 , 2.4 equivalents of (Me 2 HSiO) 0.5 , 2.0 g of trifluoroacetic acid and 2.0 g of water. The resulting solution was refluxed 48 hours. The reaction was cooled and 2.0 g of CaCO 3 and 10 g of water were added to neutralize the acid. The flask was fitted with a Dean Stark trap and the water was removed by azetroping dry over an 24 hour period. The polymer was isolated by filtration through a 1.0 micrometer membrane and by removing the solvent in vacuo at 50°C. The yield was 70 g. The polymer has a Tg of -22°C. and was characterized by GPC molecular weight analysis: Mw=4,269 and Mn=1,407. 29 Si NMR showed a broad doublet at -4.0 ppm ((Me) 2 HSiO 0.5 ) and a broad doublet at -85 ppm (HSiO 1.5 ). Crosslinking and Conversion to a Ceramic A sample of the above resin, 4.0 g, was blended with 1.0 g of vinyl functional siloxane fluid of the formula (MeSiO 1.5 ) 0.10 (MeViSiO) 0.90 and 0.05 g of dicumuyl peroxide. The above mixture was heated to 150°C. under Ar to afford a brittle solid in 99% yield. An aliquot of this cured material was then weighed in an alumina boat and transferred to a Lindberg tube furnace. The furnace was continuously purged with argon and the sample heated to 1200°C. at 10°C./minute and held at temperature for 1 hour before cooling back to ambient temperatures. The ceramic yield was 71.2% and the ceramic analysis was C:15.1; Si:45.5; O:33.4. Oxidation of the Ceramic The above ceramic was ground in a synthetic sapphire mortar and pestle to a fine powder. An aliquot of this powder was then weighed in an alumina boat and transferred to a Lindberg tube furnace. The sample was heated to 1000°C. at 10°C./minute in flowing air and held at temperature for 10 hours before cooling back to ambient temperatures. The % weight change was found to be +1.1 % and the material had the following ceramic analysis C:11.9; Si:42.5; O:37.5. Example 7 Composite Fabrication A slurry of 12.1 g of silicon nitride in 36.2 g of an 18 wt % solution of the modified H-resin of Example 5 (9 g), 7.2 g of vinyl functional siloxane fluid of the formula (MeSiO 1.5 ) 0.10 (MeViSiO) 0.90 and 0.4 g of Lupersol 101® (2,5-bis(t-butylperoxy)-2,3-dimethylhexane) were used to impregnate a 15 cm X 15 cm piece of heat treated, BN coated Ceramic Grade, 8 harness satin weave Nicalon® cloth (10 g). The cloth was then cut into six sheets of 5 cm X 7.5 cm, stacked, vacuum bagged, heated to 118°C. for 2 minutes before applying 14 kg/cm 2 for 30 minutes, heated further to 194°C., 278°C. then 166°C. The resultant cured plate had a thickness of 0.35 mm/ply and a weight of 16.66 g. The plate was pyrolyzed to 1200°C. under an inert atmosphere. After pyrolysis, the composite was densified to 5% open porosity by 5 reinfiltration cycles comprising impregnation with a 80:20 mixture of the modified H-resin polymer of Example 6 : vinyl functional siloxane fluid of the formula (MeSiO 1.5 ) 0.10 (MeViSiO) 0.90 with 1 part Lupersol 101® followed by pyrolysis to 1200°C. under argon. Testing of the composite in a 3 point flexural test gave a strength of 1596 kg/cm 2 and a flexural modulus of 511,000 kg/cm 2 . Example 8 Composite Fabrication A slurry of 16.7 g of silicon nitride in a toluene solution (50 g) of the modified H-resin (40 g) of Example 5, 10 g of vinyl functional siloxane fluid of the formula (MeSiO 1.5 ) 0.10 (MeViSiO) 0.90 and 0.5 g of dicumuyl peroxide were used to impregnate a 21.6 cm X 31.7 cm piece of heat treated, BN coated Ceramic Grade, 8 hardness satin weave Nicalon® cloth (10 g). The cloth was then cut into six sheets of 10 cm X 10 cm, stacked, vacuum bagged, heated to 250°C. over 3.5 hours and held at temperature for 6 hours. The resultant cured plate had a thickness of 0.38 mm/ply and a weight of 45.8 g. The plate was pyrolyzed to 1200°C. under an inert atmosphere. The pyrolyzed plate had a thickness of 0.35 mm/ply, a weight of 44.78 g, an apparent porosity of 21.1 % and a density of 1.95 g/cm 3 . The composite was densified to 5% open porosity by 5 reinfiltration cycles comprising impregnation with an 80:20 mixture of the modified H-resin polymer of Example 6 : vinyl functional siloxane fluid of the formula (MeSiO 1.5 ) 0.10 (MeViSiO) 0.90 with 1 part Lupersol 101® followed by pyrolysis to 1200°C. under argon. Testing of the composite in a 3 point flexural test gave a strength of 1820 kg/cm 2 . A test sample of this composite was oxidized at 1100°C. for 50 hours and had a weight change of +0.19% and gave a flexural strength of 1645 kg/cm 2 . Example 9 Composite Fabrication A slurry of 16.7 g of silicon carbide in a toluene solution (50 g) of the modified H-resin (40 g) of Example 5, 10 g of vinyl functional siloxane fluid of the formula (MeSiO 1.5 ) 0.10 (MeViSiO) 0.90 and 0.5 g of dicumuyl peroxide were used to impregnate a 21.6 cm X 31.7 cm piece of heat treated, BN coated Ceramic Grade, 8 hardness satin weave Nicalon® cloth (10 g). The cloth was then cut into six sheets of 10 cm X 10 cm, stacked, vacuum bagged, heated to 97°C. over 10 minutes where pressure was applied and the temperature was held for 1 hour. It was then heated to 247°C. over 4.5 hours and held at this temperature for 6 hours. The resultant cured plate had a thickness of 0.35 mm/ply and a weight of 40.17 g. The plate was pyrolyzed to 1200°C. under an inert atmosphere. The pyrolyzed plate had a thickness of 0.33 mm/ply, a weight of 39.34 g, an apparent porosity of 21.1 % and a density of 1.97 g/cm 3 . The composite was densified to 5% open porosity by 5 reinfiltration cycles comprising impreganation with a 80:20 mixture of the modified H-resin polymer of Example 6 : vinyl functional siloxane fluid of the formula (MeSiO 1.5 ) 0.10 (MeViSiO) 0.90 with 1 part Lupersol 101® followed by pyrolysis to 1200°C. under argon. Testing of the composite in a 3 point flexural test gave a strength of 2540 kg/cm 2 . A test sample of this composite was oxidized at 1100°C. for 50 hours and had a weight change of +0.19% and gave a flexural strength of 1876 kg/cm 2 . Example 10 Composite Fabrication A slurry of 25 g of silicon nitride in a toluene solution (75 g) of the modified H-resin (60 g) of Example 5, 15 g of vinyl functional siloxane fluid of the formula (MeSiO 1.5 ) 0.10 (MeViSiO) 0.90 and 0.7 g of dicumuyl peroxide were used to impregnate a 21 cm X 31.7 cm piece of heat treated, BN coated Ceramic Grade, 8 hardness satin weave Nicalon® cloth (10 g). The cloth was then cut into six sheets of 10 cm X 10 cm stacked, vacuum bagged, heated to 247°C. over 3.5 hours and held at this temperature for 6 hours. The cured plate was cut into 1.2 cm X 6.7 cm test samples. The test samples were pyrolyzed to 1200°C. under an inert atmosphere. The pyrolyzed plates had an apparent porosity of 21.1 % and a density of 1.95 g/cm 3 . The composite was densified by 4 reinfiltration cycles comprising impreganation with a 80:20 mixture of the modified H-resin polymer of Example 6 : vinyl functional siloxane fluid of the formula (MeSiO 1.5 ) 0.10 (MeViSiO) 0.90 with 1 part Lupersol 101® followed by pyrolysis to 1200°C. under argon. After the first cycle, the porosity was found to be 13.5 % and the test sample had a flexural strength of 1323 kg/cm 2 . After two cycles, the porosity was found to be 8 % and the test sample had a flexural strength of 1778 kg/cm 2 . After three cycles the porosity was found to be 6.2 % and the test sample had a flexural strength of 1771 kg/cm 2 . After four cycles the porosity was found to be 4.9% and the test sample had a flexural strength of 1288 kg/cm 2 .

Claims: A method of forming a fiber-reinforced ceramic matrix composite comprising a ceramic matrix comprising silicon, carbon and oxygen having a char stoichiometry of SiO y C z , wherein y = 1.2 to 1.6, z = 0.2-0.6, and within the ceramic matrix, a refractory fiber coated with a material which provides an interface between the refractory fiber and the ceramic matrix, which method comprises (a) impregnating an assembly of refractory fibers having an interfacial coating thereon with a preceramic matrix mixture comprising modified hydrogen silsesquioxane resin of the structure (HSi0 1.5 ) x (R 1 R 2 R 3 SiO 0.5 ) y , wherein R 1 , R 2 and R 3 are independently selected from hydrogen, alkyls and aryls, x is 0.25 to 0.99, y is 0.75 to 0.01 and x + y = 1.0, and having a number average molecular weight (Mn) in the range of between 500 to 2500; (b) forming the impregnated assembly of fibers into the desired shape; (c) curing the formed impregnated assembly of fibers; and (d) heating the cured impregnated assembly of fibers of (c) to a temperature of at least 1000°C. in an inert atmosphere for a time effective to convert the modified hydrogen silsesquioxane resin to a ceramic. The method of claim 1, wherein the preceramic matrix mixture additionally comprises a solvent and the solvent is evaporated from the impregnated fibers prior to step (b). The method of claim 1 or 2, wherein the impregnated assembly of fibers of step (a) are cured prior to forming them into the desired shape in step (b). The method of any of claims 1 to 3, wherein the forming in step (b) is accomplished by pressing the impregnated assembly of fibers of step (a) into a mold at a temperature in the range of 60 to 300°C., a pressure in the range of 0.07 to 175 kg/cm 2 and for a time in the range of 2 minutes to 4 hours. The method of any of claims 1 to 4, wherein the composite of step d is subjected to step (a), (c) and (d) at least one more time. The method of any of claims 1 to 5, wherein the preceramic matrix mixture additionally comprises a material which assists in curing the modified hydrogen silsesquoixane resin. The method of any of claims 1 to 6, wherein the refractory fiber comprises silicon and carbon. The method of any of claims 1 to 7, wherein the fiber coating is selected from carbon, boron, boron nitride, silicon carbide, silicon nitride, aluminum nitride and combinations thereof. The method of any of claims 1 to 8, wherein 20 to 65 percent by volume of the composite comprises fiber. The method of any of claims 1 to 9, wherein the composite has less than 10% open porosity. The method of any of claims 1 to 10, wherein the matrix also comprises fillers selected from boron nitride, silicon carbide, silicon nitride, silicon hexaboride, boron carbide, titanium boride, boron, titanium carbide and aluminum nitride.

Inventors: ZANK GREGG ALAN, ZANK, GREGG ALAN
Applicants: DOW CORNING, DOW CORNING CORPORATION
Application year: 1996
Main classification: C04B35
IPC codes: C03C14, C04B35