Search Images Maps Play YouTube News Gmail Drive More »
Sign in
Screen reader users: click this link for accessible mode. Accessible mode has the same essential features but works better with your reader.

Patents

  1. Advanced Patent Search
Publication numberUS3738906 A
Publication typeGrant
Publication dateJun 12, 1973
Filing dateAug 21, 1970
Priority dateAug 21, 1970
Also published asCA953743A, CA953743A1, DE2141331A1
Publication numberUS 3738906 A, US 3738906A, US-A-3738906, US3738906 A, US3738906A
InventorsE Olcott
Original AssigneeAtlantic Res Corp
Export CitationBiBTeX, EndNote, RefMan
External Links: USPTO, USPTO Assignment, Espacenet
Pyrolytic graphite silicon carbide microcomposites
US 3738906 A
Abstract  available in
Images(2)
Previous page
Next page
Claims  available in
Description  (OCR text may contain errors)

United States Olcott atet 1 PYROLYTIC GRAPHITE-SILICON CARBIDE MICROCOMPOSITES Eugene L. Olcott, Falls Church, Va.

[73] Assignee: Atlantic Research Corporation,

Alexandria, Va.

22 Filed: Aug. 21, 11970 21 Appl. No.: 65,899

[75] Inventor:

[52] US. Cl. 161/168, 117/46, 117/106,

156/166, 161/57,161/l43,264/79, 161/60 [51] Int. Cl B3211 5/08 [58]' Field of Search 161/69, 162, 168-170,

16l/l76,188; l17/46,106, 119,118; 252/504, 516; 23/208; 264/29, 81, 85; 156/166 Primary Examiner-William A. Powell Attorney-Tipton D. Jennings [57] ABSTRACT A rigid pyrolytic graphite microcomposite material comprising a matrix of pyrolytic graphite containing embedded therein codeposited crystalline silicon carbide comprising aciculae oriented approximately perpendicular to the a-b plane of the crystallite layers of the pyrolytic graphite. The SiC comprises at least about June 12, 1973 5 volume percent of the microcomposite material, preferably at least about 10 volume percent.

A method for making said microcomposite material comprising pyrolyzing a mixture of methyl trichlorosilane and a hydrocarbon gas at temperatures of about 2800F to 4000F, preferably about 3200F to 3800F and, thereby codepositing pyrolytic graphite and SiC.

A rigid composite pyrolytic graphite article comprising a matrix of the above microcomposite material containing embedded therein at least one reinforcing refractory filament or strand layer. The refractory filament or strand layer comprises a plurality of unidirectional and substantially parallel, laterally spaced, individual, continuous'refractory filaments or strands. The microcomposite matrix is nucleated from each of the individual refractory filaments or strands and interconnected to form a continuous matrix phase surrounding and interconnecting the individual filaments or strands comprising the embedded filament or strand layer.

A method for making said rigid pyrolytic graphite article comprising winding a continuous, individual, refractory filament or strand around a shaped form and simultaneously pyrolyzing a mixture of methyl trichlorosilane and a hydrocarbon gas onto the filament or strand at about the point of winding contact to nucleate pyrolytic graphite and SiC from the filament or strand, winding additional turns of the filament or strand around the form, each additional turn being spaced from previously wound turns and, as each of the additional turns is wound, simultaneously pyrolyzing the mixture of methyl trichlorosilane and hydrocarbon gas thereon at about the point of winding contact and on the codeposited pyrolytic graphite and SiC nucleated from previously wound turns.

8 Claims, 7 Drawing Figures PMENTED JUN l 73 sum 2 or g PYROLYTIC GRAPHITE-SILICON CARBIDE MICROCOMPOSITES BACKGROUND OF THE INVENTION The superior high temperature and erosion resistant properties of rigid pyrolytic graphite materials are well known. These properties make the material particularly useful as liners for chambers or vessels subject to such conditions, as rocket nozzle inserts, and the like.

Pyrolytic graphite, however, does have certain disadvantageous properties stemming from its particular crystallite structure and from its tendency to oxidize, particularly at high temperatures in an oxidizing atmosphere.

Pyrolytic graphite is normally produced by the pyrolysis of a carbonaceous gas, such as methane or propane, onto a heated substrate. Flat, hexagonal crystallitesoriented parallel to the substrate surface are deposited in layers which build up into an essentially laminar structure. The pyrolytic graphite crystal is considerably wider in its flat or a-b plane than along its thickness dimension or c-axis. As a result, pyrolytic graphite is highly anisotropic in many of its properties, including strength, heat conductivity and thermal expansion, with attendant difficulties .in practical use. As an example, the material has an exceedingly high coefficient of thermal expansion in the thickness or c-axis direction and a relatively low coefficient in the a-b direction. As a result, it is exceedingly difficult to match a pyrolytic graphite liner or insert with a suitable backing material which can avoid separation during thermal cycling. Because of its weakness in the c-direction, due to its flat, plate-like and, thereby, laminar microstructure, pyrolytic graphite tends to delaminate under high stresses.

The embedding within the laminar pyrolytic graphite crystallite structure of aciculae of crystalline SiC'which are oriented in the c-direction, as compared to the planar orientation of the layers of the pyrolytic graphite in the a-b direction, advantageously reduces the anisotropy of the graphite and reduces the tendency of the graphite to delaminate. Additionally, it substantially improves oxidation resistance since, unlike carbon which oxidizes to a gas, silicon oxidizes to SiO, which fuses to form a protective coating. Improved oxidationresistance is particularly important if the pyrolytic graphite is exposed to high temperature oxidative atmospheres.

The production of SiC films and coatings, for example, on flexible metalfilaments such as tungsten, by vapor phase pyrolysis-of a silane, such as SiI-h, SiCl., SiHCl,, (Cl- 9 5i or Ch5SiCl with or without added hydrocarbon gas, is well known, the objective generally being the production of pure SiC. The pyrolysis temperatures employed are generally below the optimum temperatures for producing pyrolytic graphite.

Yajima et al pyrolyzed a mixture of SiC], and propane under vacuum. Maximum SiC production of up to 4 weight percent was obtained at temperatures of about 1,400C to 1,500C and dropped to as little as 0.02 to 0.03 weight percent at temperatures of about 2,000C. Since SiC is considerably denser than pyrolytic graphite, the volume percent of SiC was substantially smaller.

None of the referenced art discloses the pyrolytic graphite-SiC microcomposite of this invention or the process for making it.

Copending applications Ser. No. 592,846 new U.S. Pat. No. 3,629,049 and 870,948 disclose rigid pyrolytic graphite articles comprising a matrix of pyrolytic graphite containing embedded therein at least one reinforcing layer consisting of a plurality of unidirectional and substantially parallel, laterally spaced, individual, continuous carbon strands. The matrix comprises crystallite layers of pyrolytic graphite nucleated from each of the individual carbon strands and interconnected to form a continuous phase surrounding and interconnecting the individual strands comprising the embedded strand layers. By conforming the crystallite pyrolytic graphite layers to embedded strand surfaces instead of to the surface of a conventional base substrate, anisotropy of the pyrolytic graphite and its attendant disadvantages are substantially reduced.

Utilization of the codeposited pyrolytic graphite-SiC microcomposite of the present invention in place of the pyrolytic graphite matrix disclosed in said copending applications provides further improvement in isotropy and improves oxidation resistance.

Seishi Yajima et al., Journal of Materials Science 4 (1969) Pp. 16-423 and 424-431, and Chemical Abstracts, 1970, 7, p. 69, disclose a structure comprising flake-like single crystals of SiC dispersed in amatrix of pyrolytic graphite and oriented parallel to theplanes-of the graphite. The crystallite size of the SiC was about 200 A. thick (c-direction) and about 2,000 A, in diameter (a-b direction). Since the single SiC crystals of the Yajima et al structures are essentially flat and oriented in the same planar direction as the pyrolytic graphite, they cannot have any substantial effect on the anisotropy or delamination characteristics of the latter.

The object of the invention is to provide a rigid pyrolytic graphite-SiC microcomposite having substantially lower anisotropy than pyrolytic graphite and improved SUMMARY OF THE INVENTION Broadly, the invention comprises rigid microcomposite pyrolytic graphite materials containing codeposited andembedded therein crystalline SiC comprising aciculae, 'the longitudinal axes of which are oriented approximately perpendicular to the a-b or flat plane of thepyrolytic graphite crystallite layers. The microcomposite is a two-phase system since the pyrolytic graphite and SiC are mutually insoluble.

The codeposition of aciculae of SiC within a matrix of pyrolytic graphite in such manner that the longitudinalaxes of the aciculae are oriented approximately in the c-direction relative to the a-b plane of the pyrolytic graphite provides asubstantial dimension in the thickness or c-direction which considerably reduces the anisotropy normally characteristic of pyrolytic graphite alone. This results in substantially increased strength in the thickness dimension and improvement in other properties, such as thermal 1 expansion. Additionally,

the perpendicularly embedded SiC aciculae interrupt the laminar pattern of the pyrolytic graphite and thus reduce its tendency to delaminate. Since SiC is considerably harder than pyrolytic graphite, the presence of the former in the microcomposite also improves erosion-resistance, as well as the oxidation resistance of the graphite.

The composite pyrolytic graphite-SiC material may be prepared by pyrolyzing a mixture of methyl trichlorosilane and a hydrocarbon gas onto a heated substrate at temperatures of about 2,800F to 4,000F, preferably about 3,200F to 3,800F. in a suitable furnace in accordance with procedures otherwise well known in the production of pyrolytic graphite.

The invention additionally comprises rigid composite articles comprising the aforedescribed pyrolytic graphite-SiC microcomposite containing embedded therein at least one reinforcing layer of a plurality of unidirectional and substantially parallel, laterally spaced, individual, continuous refractory filaments or strands. The pyrolytic graphite-SiC is nucleated from each of the individual refractory filaments or strands and is interconnected to form a continuous matrix phase surrounding and interconnecting the individual filaments or strands comprising the embedded filament or strand layer.

Nucleation and growth of the pyrolytic graphite-SiC microcomposite from the embedded plurality of refractory filaments or strands further reduces and interrupts the laminar character of the pyrolytic graphite portion of the composite material and thereby further reduces anisotropy and delamination tendency. Additionally,

the reinforcing refractory filaments or strands increase the strength of the composite article in the direction of filament or strand orientation.

The rigid reinforced composite pyrolytic graphite- SiC articles can be made by progressively positioning a continuous, individual refractory filament or strand onto a shaped form and simultaneously pyrolyzing a mixture of methyl trichlorosilane and a hydrocarbon gas onto the filament or strand at about the point of positioning contact to nucleate pyrolytic graphite and silicon carbide from the filament or strand, progressively positioning additional filament or strand laterally spaced from previously positioned filament or strand and, as the additional filament or strand is positioned, simultaneously pyrolyzing the mixture of methyl trichlorosilane and hydrocarbon gas thereon at about the point of positioning contact and on the codeposited pyrolytic graphite and SiC nucleated from previously psitioned filament or strand. The pyrolysis temperature should be about 2,800F to 4,000F, preferably about 3,200F to 3,800F.

DRAWINGS FIG. 1 is a photomicrograph at a magnification of I50 of a crosssection of a sample of the pyrolytic graphite-SiC microcomposite of the invention.

FIG. 2 is a photomicrograph of the same section at a magnification of 600. 7

FIG. 3 is a schematic illustration of apparatus for practicing this invention. I

FIG. 4 is a schematic illustration'of a rigid filamentor strand-reinforced pyrolytic graphite-SiC composite according to this invention.

FIGS. 5 and 6 are schematic representations of modified apparatus suitable for use in preparing the filamentor strand-reinforced composites.

FIG. 7 .schematically illustrates an alternative arrangement of reinforcing strands.

DETAILED DESCRIPTION The amount of SiC should be at least about 5 percent, preferably at least about 10 percent, by volume of the microcomposite. Depending upon the desired properties for a particular application, the percent of SiC can be as high as or even 95. In general, the preferred range is about 10 to 50 volume percent, with the pyrolytic graphite making up the remainder.

In some applications, it may be desirable to use a microcomposite of graded relative pyrolytic graphite and SiC composition. For example, the outermost portion of the microcomposite can have a higher SiC content to minimize oxidative surface erosion. Such graded variations in the relative amounts of the codeposited pyrolytic graphite and SiC can readily be achieved by varying respective flow rates of the methyl trichlorosilane and hydrocarbon gas and/or other processing variables in the codeposition process.

The photomicrographs of FIGS. 1 and 2 at lSOX and 600x magnification respectively, clearly show the SiC, a large proportion of which is in the form of needle-like aciculae of SiC oriented substantially perpendicularly to the codeposited laminar layers of pyrolytic graphite, which forms an embedding matrix. The volume percent in the photographed sample is about 20 percent.

The microcomposite can be made by vapor phase pyrolysis of a mixture of methyl trichlorosilane and a hydrocarbon gas onto a heated substrate at a temperature of about 2,8004,000F, preferably about 3,200-3,800F. An inert diluent gas, such as argon, nitrogen, helium, hydrogen, and mixtures thereof is generally desirable, with some or all of the gas used to aspirate the liquid methyl trichlorosilane. Mixtures of hydrogen with argon, helium or nitrogen has been found particularly effective in obtaining good aciculae crystalline SiC formation. The process can be carried out in a conventional furnace and related equipment at reduced or atmospheric pressures. Atmospheric pressure is generally preferred because of the excellent results obtained and the convenience.

The relative flow rates of the methyl trichlorosilane and hydrocarbon gas vary generally with the desired microcomposite composition. In general, the silane may be introduced at a weight percent flow rate of about 5 to 75 percent, preferably about 15 to 50 percent and the hydrocarbon gas at a weight percent flow rate of about 25 to percent, preferably about 15 to 50 percent.

The. hydrocarbon gas can be any of those generally employed in producing pyrolytic graphite by vapor phase deposition, such as the lower alkanes, e.g. methane, ethane, and propane; ethylene; acetylene; and

mixtures thereof. Methane is preferred.

EXAMPLE I A cylindrical graphite substrate was seated in a 4 inch Perenny resistance furnace and heated to 3,400F. A mixture ofmethyl trichlorosilane, methane, argon and hydrogen were injected into one end of the graphite cylinderuThe methyl trichlorosilane was entrained for injection by bubbling argon through a container of the liquid methyl trichlorosilane. Flow rates were: argon l3 std. cu. ft/hr; hydrogen l0 std. cu. ft/hr; methane 2.0 std. cu. ft/hr.

Total methyl trichlorosilane consumed was 85 gm.

Pyrolytic deposition was continued for 1 hour.

The thickness of the formed microcomposite and the relative amounts of the codeposited pyrolytic graphite and silicon carbide varied with distance from theinjection nozzle. The thickest portion of the microcomposite formed was 26 mils and contained about 75 volume percent of needle-like crystalline aciculae of silicon carbide embedded in laminar layers of pyrolytic graphitef The volume percent of silicon carbide decreased with increasing distance from the injector. The photomicrographs of FIGS. 1 and 2 were made with a sample taken from a downstream portion having a silicon carbide volume percent of about 20.

The rigid microcomposite cylinder formed by the above procedure was sound and showed no signs of delamination after cooling.

EXAMPLE II A run was made under conditions substantially the same as in Example I except that the pyrolysis tempera ture was maintained at 3,600F.

Results were substantially similar except that at the point of maximum deposition, the relative volumes of the SiC aciculae and the pyrolytic graphite were 85 and percent and then decreased with increasing distance from the injector.

The rigid microcomposite cylinder was sound. and showed no signs of delamination after cooling.

EXAMPLE III A pyrolytic graphite-SiC microcomposite was deposited'on a 1-inch diameter disc in a manner similar to. the procedure used in the preceding examples except that no hydrogen was used and a 1-inch disc substrate was centered at right angles to the injector so that a substantially uniform microcomposite was formed over the face of the disc. A

To determine oxidation resistance, the resulting pyrolytic graphite-SiC microcomposite disc and a disc of the same size and substrate coated with an equal thickness of pyrolytic graphite were heated to about 3,000F

in a highly oxidizing oxyacetylene flame for three min- \utes. The pyrolytic graphite coating was fully pene- I'ated and almost completely burned away whereas the yr'olytic graphite-SiC coating eroded only on the surface-with almost half of the thickness remaining intact.

EXAMPLE IV Several pyrolytic graphite and pyrolytic graphite-SiC microcomposite deposition runs were made on ATJ graphite discs which have a higher coefficient of thermal expansion than pyrolytic graphite in its a-b plane.

By cross-sectioning of the deposits, it was determined.

The method can be practiced with apparatus such as that schematically illustrated in FIG. 3. As shown therein, a continuous, individual refractory filament or strand, as for example carbon strand, 1, is fed through a guide tube 2, and connected to a mandrel 3, disposed in chamber 4. To prevent oxidation of the carbonaceous gas, atmospheric oxygen is removed and continuously excluded from the chamber by evacuation and/or purging with inert gases such as helium or nitrogen. The strand is heated to and maintained at a temperature sufficient to pyrolyze the methyl trichlorosilane and hydrocarbon gases by induction, radiant, or resistance heating means, not shown. The mandrel is rotated and moved longitudinally relative to the strand guide tube 2, by means not shown. In this manner, spaced turns of strand are progressively positioned on the mandrel. As the strand is wound, the methyl trichlorosilane, hydrocarbon and carrier gas mixture are fed through tube 5, to impinge upon the strand at about the point of winding contact, Pyrolysis of the methyl trichlorosilane and hydrocarbon gas occurs and a pyrolytic graphite-SiC microcomposite matrix is nucleated from the heated strand substrate. As winding continues, the microcomposite is simultaneously deposited on thestrand being wound and on the matrix deposited on previously wound strands. Thus, the strands are not only individually enveloped in a microcomposite matrix but are interconnected and bonded to each other by the matrix. The winding is continued to produce a composite article such as schematically illustrated in FIG. 4. As shown, the article comprises one or more spaced, reinforcing strand layers 6, each of which comprises a plurality of spaced strands 1, disposed in and interconnected by a pyrolytic graphite-SiC microcomposite matrix 7, composed of graphite crystallite layers 8 containing embedded, perpendicularly oriented, codeposited aciculae of SiC.

As shown, the crystallite layers of the pyrolytic graphite in the microcomposite matrix are oriented in conformity to surfaces of the strands and are, therefore, aligned around the strands and in the direction of strand orientation, thereby maximizing strength of the pyrolytic graphite component in that direction. Furthermore, the embedded strands significantly reinforce the microcomposite-strand composite in the direction of strand orientation.

Since the orientation of the pyrolytic graphite crystallite layers conforms to the strand surfaces rather than the base or mandrel substrate surface of the composite, the pyrolytic graphite component of the microcomposite does not have the continuous laminar structure characteristic of conventional pyrolytic graphite. This, together with the embedded codeposited SiC aciculae, further tends to prevent propagation of cracks and delaminations. Composite strength in the thickness direction is also further significantly improved by the increased degree of crystallite layer alignment in that direction. In addition, the marked disparity in thermal expansion in the a-b and c directions characteristic of conventional pyrolytic graphite is further reduced.

The strands also prevent delamination failures by restricting the thickness of laminar pyrolytic graphite component growth units nucleated from these strands. It is known that growth units less than 0.05 inches thick are less subject to delamination. Since, in the composition of this invention, the thickness of laminar pyrolytic graphite component units is generally about one-half the distance between the strands; preferred unit size is obtained by spacing the strands less than 0.1 inch of each other. 7

The process for composite fabrication can be practiced with individual strands, as in the embodiment described, or with multi-strand structures, such as a plurality of laterally spaced, unidirectionally oriented individual strands, or with woven cloths or tapes comprising strands oriented in both warp and woof direction. When using multi-strand structures to prepare a composite, it is preferred simultaneously to impinge the reactive gas mixture on both sides of the strand structure as it is progressively laid down to ensure that the gas penetrates between the strands to effect the highest degree of lateral bonding. This can be accomplished by apparatus such as schematically illustrated in FIG. 5, wherein gas injector channels 9, feed gas into contact with spaced strands 1, or by apparatus as shown in FIG. 6, wherein woven refractory cloth 11 and gas are both fed through guide channel 10.

When the method is practiced with woven fabrics, little matrix bond is obtained between strands where warp and woof intercross since it is difficult for the reaction gas mixture to penetrate between the touching strands. It is, therefore, preferred that all strands in each reinforcing strand layer in the composite be sub stantially unidirectionally oriented Such orientation eliminates weaknesses which result from the absence of a matrix bond at points of strand to strand contact. In composites having multiple reinforcing strand layers, the direction of strand orientation can be varied in dif: ferent reinforcing layers as shown, for example, in FIG. 7. Thus composites having desired directional strength characteristics can readily be prepared.

This invention can, of course, be practiced by positioning strand on a variety of shaped forms to produce articles having the desired configuration. The strand can be progressively positioned on the shaped form by any desired technique. However, winding is preferred for reasons of simplicity. It will be understood from the foregoing discussion that the term progressively" positioning connotes a gradual laying down of strand to continuously and progressively increase the area of strand contact with the shaped form rather than effecting overall lateral strand contact as by stacking". This permits matrix formation between strands as they are positioned and eliminates the necessity of forcing the feed gas mixture between prepositioned strands.

When the invention is practiced with strands, such as carbon yarns, which comprise a multiplicity of fibers which have been spun or otherwise incorporated to form the continuous strand, the pyrolytic graphite-Sic microcomposite may, in some instances be deposited on fibers or fuzz protruding from the strand rather than directly on the base strand. Therefore, in order to obtain optimum lateral bonding of strands by the matrix, it may be desirable to minimize such protrusions as, for example, by mechanically removing them with a scraper blade as the matrix is built up or by utilizing strands precoated with pyrolytic graphite to provide a smooth surface.

Although this invention has been described with reference to illustrative embodiments thereof, it will be apparent to those skilled in the art that the principles of this invention can be embodied in other forms but within the scope of the claims.

I claim:

1. Pyrolytic graphite microcomposite comprising pyrolytic graphite containing embedded therein codeposited silicon carbide comprising aciculae of silicon carbide, the longitudinal axes of said aciculae being aligned in the c-direction relative to the a-b plane of the associated pyrolytic graphite crystalline, said silicon carbide comprising at least about 5 percent by volume of said microcomposite.

2. The microcomposite of claim 1 in which the silicon carbide comprises at least 10 percent by volume.

3. The microcomposite of claim 1 including a graphite substrate onto which said pyrolytic graphite and silicon carbide are codeposited.

4. The microcomposite of claim 1 in which the silicon carbide comprises between about 10 to 50 percent by volume of said microcomposite.

5. The microcomposite of claim 4 having a graded pyrolytic graphite and silicon carbide composition, in which the relative amounts of each ingredient vary with distance from the surface of the microcomposite.

6. The microcomposite of claim 4 including a graphite substrate onto which said pyrolytic graphite and silicon carbide are codeposited.

7. The microcomposite of claim 1 having a graded pyrolytic graphite and silicon carbide composition, in which the relative amounts of each ingredient vary with distance from the surface of the microcomposite, the silicon carbide being in a range between about 5 to percent by volume.

8. The microcomposite of claim 7 including a graphite substrate onto which said pyrolytic graphite and silicon carbide are codeposited.

UNITED STATES PATENT OFFICE CERTIFICATE OF CURREQHQN Patent No. 3 738,906 Dated June 12,- 1973 Inventor s 6116 Lo V It is certified that error appears in the above-identified patent .and that said Letters Patent are hereby corrected as shown below:

C01. 5, line 7, "75" should read 25 Col. 5, 1ines25 and 26, "85 and 15 should read 15 and 85 Claim 1, col. 8, line 28, "crystalline" should read crystallite (sEAL) Attest:

GIBSON JR. C. MARSHALL DANN McCOY M.

Commissioner of Patents ffAttesting Officer FORM powso (169) uscoMM-oc eoave-pas U.S GOVERNMENT PRINTING OFFICE: [969 0"366-334

Referenced by
Citing PatentFiling datePublication dateApplicantTitle
US3885073 *Apr 12, 1973May 20, 1975Atlantic Res CorpPre-stressed pyrolytic graphite-refractory carbide microcomposites
US3897582 *Jan 26, 1973Jul 29, 1975Atlantic Res CorpBraking elements
US3900668 *Oct 30, 1972Aug 19, 1975Atlantic Res CorpInternal components for gas turbines of pyrolytic graphite silicon carbide codeposit
US3900675 *Apr 24, 1973Aug 19, 1975Atlantic Res CorpRocket nozzle comprising pyrolytic graphite-silicon carbide microcomposite inserts
US3924034 *Nov 27, 1972Dec 2, 1975Atlantic Res CorpProcess of making pyrolytic graphite-silicon carbide microcomposites
US3935354 *Nov 27, 1972Jan 27, 1976Olcott Eugene LShaped articles of pyrolytic graphite-silicon carbide microcomposites
US4127659 *Jan 26, 1977Nov 28, 1978Avco CorporationSilicon carbide filaments and method
US4329743 *Apr 27, 1979May 18, 1982College Of Medicine And Dentistry Of New JerseyBio-absorbable composite tissue scaffold
US4340619 *Jan 15, 1981Jul 20, 1982Dow Corning CorporationProcess for the preparation of poly(disilyl)silazane polymers and the polymers therefrom
US4341965 *Mar 27, 1981Jul 27, 1982Agency Of Industrial Science & TechnologyComposite electrode and insulating wall elements for magnetohydrodynamic power generating channels characterized by fibers in a matrix
US4404153 *Aug 10, 1981Sep 13, 1983Dow Corning CorporationProcess for the preparation of poly(disilyl)silazane polymers and the polymers therefrom
US4411027 *Feb 23, 1982Oct 25, 1983University Of Medicine And Dentistry Of New JerseyBio-absorbable composite tissue scaffold
US4512038 *Apr 6, 1981Apr 23, 1985University Of Medicine And Dentistry Of New JerseyBio-absorbable composite tissue scaffold
US4560589 *Sep 19, 1983Dec 24, 1985Shin-Etsu Chemical Co., Ltd.Method for providing a coating layer of silicon carbide on substrate surface
US4613522 *Sep 29, 1982Sep 23, 1986Avco CorporationOxidation resistant carbon-carbon composites
US4668583 *Nov 13, 1984May 26, 1987Hi-Shear CorporationRefractory coating
US4700823 *Mar 28, 1980Oct 20, 1987Eaton CorporationClutch with pyrolytic carbon friction material
US5049393 *Jun 30, 1988Sep 17, 1991Baylor College Of MedicineAnti-thrombogenic elastomer and objects and prostheses made therefrom
US5084151 *Feb 14, 1990Jan 28, 1992Sorin Biomedica S.P.A.Method and apparatus for forming prosthetic device having a biocompatible carbon film thereon
US5370684 *Aug 18, 1992Dec 6, 1994Sorin Biomedica S.P.A.Prosthesis of polymeric material coated with biocompatible carbon
US5387247 *Jan 3, 1990Feb 7, 1995Sorin Biomedia S.P.A.Prosthetic device having a biocompatible carbon film thereon and a method of and apparatus for forming such device
US5421896 *Sep 26, 1994Jun 6, 1995Fujitsu LimitedGraphite heater for molecular beam source of carbon
US7632309 *Dec 13, 1999Dec 15, 2009St. Jude Medical, Inc.Pyrolytic carbon and metal/metalloid carbide composites
US20130197659 *Apr 21, 2011Aug 1, 2013Sandvik Intellectual Property AbJoint prosthesis
Classifications
U.S. Classification428/212, 273/DIG.230, 428/357, 428/293.7, 428/367, 427/249.16, 156/166, 264/29.5, 427/223
International ClassificationC01B31/00, C04B35/52, C04B35/83
Cooperative ClassificationY10S273/23, C04B35/522, C01B31/00, C04B35/565, C04B35/83
European ClassificationC01B31/00, C04B35/83, C04B35/52G, C04B35/565