U.S. patent number 3,738,906 [Application Number 05/065,899] was granted by the patent office on 1973-06-12 for pyrolytic graphite-silicon carbide microcomposites.
This patent grant is currently assigned to Atlantic Research Corporation. Invention is credited to Eugene L. Olcott.
United States Patent |
3,738,906 |
Olcott |
June 12, 1973 |
**Please see images for:
( Certificate of Correction ) ** |
PYROLYTIC GRAPHITE-SILICON CARBIDE MICROCOMPOSITES
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 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 2800.degree.F to 4000.degree.F, preferably about
3200.degree.F to 3800.degree.F 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.
Inventors: |
Olcott; Eugene L. (Falls
Church, VA) |
Assignee: |
Atlantic Research Corporation
(Alexandria, VA)
|
Family
ID: |
22065888 |
Appl.
No.: |
05/065,899 |
Filed: |
August 21, 1970 |
Current U.S.
Class: |
428/212; 156/166;
273/DIG.23; 428/367; 264/29.5; 427/223; 428/357; 427/249.16;
428/293.7 |
Current CPC
Class: |
C01B
32/00 (20170801); C04B 35/83 (20130101); C04B
35/522 (20130101); C04B 35/565 (20130101); Y10S
273/23 (20130101); Y10T 428/249929 (20150401); Y10T
428/29 (20150115); Y10T 428/24942 (20150115); Y10T
428/2918 (20150115) |
Current International
Class: |
C01B
31/00 (20060101); C04B 35/52 (20060101); C04B
35/83 (20060101); B32b 005/08 () |
Field of
Search: |
;161/69,162,168-170,176,188 ;117/46,106,119,118 ;252/504,516
;23/208 ;264/29,81,85 ;156/166 |
References Cited
[Referenced By]
U.S. Patent Documents
Primary Examiner: Powell; William A.
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 95 percent by volume.
8. The microcomposite of claim 7 including a graphite substrate
onto which said pyrolytic graphite and silicon carbide are
codeposited.
Description
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 crystallites oriented 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.sub.2 which fuses to form a protective
coating. Improved oxidation-resistance 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
metal filaments such as tungsten, by vapor phase pyrolysis of a
silane, such as SiH.sub.4, SiCl.sub.4, SiHCl.sub.3,
(CH.sub.3).sub.4 Si or Ch.sub.3 SiCl.sub.3 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.
Seishi Yajima et al., Journal of Materials Science 4 (1969) pp.
416-423 and 424-431, and Chemical Abstracts, 1970, 7, p. 69,
disclose a structure comprising flake-like single crystals of SiC
dispersed in a matrix of pyrolytic graphite and oriented parallel
to the planes 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.
Yajima et al pyrolyzed a mixture of SiCl.sub.4 and propane under
vacuum. Maximum SiC production of up to 4 weight percent was
obtained at temperatures of about 1,400.degree.C to 1,500.degree.C
and dropped to as little as 0.02 to 0.03 weight percent at
temperatures of about 2,000.degree.C. 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 now 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.
The object of the invention is to provide a rigid pyrolytic
graphite-SiC microcomposite having substantially lower anisotropy
than pyrolytic graphite and improved oxidation resistance.
Still another object is to provide a process for making said rigid
pyrolytic graphite-SiC microcomposite.
Another object is to provide rigid reinforced composite pyrolytic
graphite-SiC articles having additionally decreased anisotropy.
Still another object is to provide a process for making said rigid
reinforced composite pyrolytic graphite-SiC articles.
Other objects and advantages will become apparent from the
following description and drawings.
SUMMARY OF THE INVENTION
Broadly, the invention comprises rigid microcomposite pyrolytic
graphite materials containing codeposited and embedded therein
crystalline SiC comprising aciculae, the longitudinal axes of which
are oriented approximately perpendicular to the a-b or flat plane
of the pyrolytic 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 longitudinal axes of the aciculae
are oriented approximately in the c-direction relative to the a-b
plane of the pyrolytic graphite provides a substantial 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
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 2,800.degree.F
to 4,000.degree.F, preferably about 3,200.degree.F to
3,800.degree.F. 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 positioned filament or strand. The pyrolysis temperature
should be about 2,800.degree.F to 4,000.degree.F, preferably about
3,200.degree.F to 3,800.degree.F.
DRAWINGS
FIG. 1 is a photomicrograph at a magnification of 150 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.
FIG. 3 is a schematic illustration of apparatus for practicing this
invention.
FIG. 4 is a schematic illustration of a rigid filament- or
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 filament- or 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 90 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 150.times. and 600.times.
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
2,800.degree.-4,000.degree.F, preferably about
3,200.degree.-3,800.degree.F. 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 95 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 3,400.degree.F. A mixture of
methyl trichlorosilane, methane, argon and hydrogen were injected
into one end of the graphite cylinder. The methyl trichlorosilane
was entrained for injection by bubbling argon through a container
of the liquid methyl trichlorosilane. Flow rates were: argon -- 13
std. cu. ft/hr; hydrogen -- 10 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 the injection 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 graphite. 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 temperature was maintained at
3,600.degree.F.
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 15 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.
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 3,000.degree.F in a highly oxidizing oxyacetylene
flame for three minutes. The pyrolytic graphite coating was fully
penetrated and almost completely burned away whereas the pyrolytic
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 that all of the microcomposites were free from
delamination, whereas the pyrolytic graphite deposits showed major
delaminations between the deposit and the substrate.
The pyrolytic graphite-SiC microcomposites can be reinforced to
increase strength and further reduce anisotropy of the pyrolytic
graphite component by embedding at least one layer of a plurality
of unidirectional and substantially parallel, laterally spaced,
individual continuous, refractory filaments or strands in the
microcomposite by nucleating the codeposited pyrolytic graphite and
SiC from each of the filaments or strands to form a continuous
interconnecting matrix surrounding and interconnecting the
individual filaments or strands.
The strands or filaments can comprise any suitable refractory
material such as carbon in any suitable form including, for
example, pyrolyzed rayon and pyrolytic graphite; SiC-coated metal
filaments, such as tungsten; carbon alloyed with a metal, such as
Th, W, Ta, Mb, or Zr, in amounts, for example, up to about 20
percent by weight; boron filaments, and the like.
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 the
strand 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.
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 substantially
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
different 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.
* * * * *