U.S. patent application number 14/065461 was filed with the patent office on 2014-03-20 for method for producing tubular body.
This patent application is currently assigned to IBIDEN CO., LTD.. The applicant listed for this patent is IBIDEN CO., LTD.. Invention is credited to Takashi TAKAGI.
Application Number | 20140079879 14/065461 |
Document ID | / |
Family ID | 40671005 |
Filed Date | 2014-03-20 |
United States Patent
Application |
20140079879 |
Kind Code |
A1 |
TAKAGI; Takashi |
March 20, 2014 |
METHOD FOR PRODUCING TUBULAR BODY
Abstract
A method for producing a tubular body includes winding ceramic
fibers to form an aggregate with the ceramic fibers. The aggregate
has a tubular shape. Pyrolytic carbon is vapor deposited on the
aggregate to form a fiber-reinforced carbonaceous substrate. The
pyrolytic carbon positioned at least on an outer surface of the
fiber-reinforced carbonaceous substrate is converted to CVR-SiC by
reaction with an SiO gas to form an CVR-SiC layer. CVD-SiC is
deposited on a surface of the CVR-SiC layer after forming the
CVR-SiC layer. An amount of silicon decreases from a boundary
region to an inside of the fiber-reinforced carbonaceous
substrate.
Inventors: |
TAKAGI; Takashi; (Gifu,
JP) |
|
Applicant: |
Name |
City |
State |
Country |
Type |
IBIDEN CO., LTD. |
Ogaki-shi |
|
JP |
|
|
Assignee: |
IBIDEN CO., LTD.
Ogaki-shi
JP
|
Family ID: |
40671005 |
Appl. No.: |
14/065461 |
Filed: |
October 29, 2013 |
Related U.S. Patent Documents
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Application
Number |
Filing Date |
Patent Number |
|
|
12369391 |
Feb 11, 2009 |
8603579 |
|
|
14065461 |
|
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Current U.S.
Class: |
427/177 |
Current CPC
Class: |
Y02E 30/30 20130101;
Y02E 30/40 20130101; C04B 41/5059 20130101; C04B 41/52 20130101;
C23C 16/02 20130101; C04B 35/52 20130101; C04B 2235/614 20130101;
C04B 2235/94 20130101; G21C 21/02 20130101; C04B 2235/5244
20130101; C04B 41/89 20130101; C04B 41/009 20130101; G21C 3/07
20130101; G21C 3/00 20130101; C04B 41/87 20130101; C04B 35/806
20130101; Y10T 428/249939 20150401; C04B 41/5059 20130101; C04B
41/4529 20130101; C04B 41/4556 20130101; C04B 41/52 20130101; C04B
41/4529 20130101; C04B 41/4556 20130101; C04B 41/5059 20130101;
C04B 41/52 20130101; C04B 41/4531 20130101; C04B 41/5059 20130101;
C04B 41/009 20130101; C04B 35/52 20130101; C04B 41/009 20130101;
C04B 35/806 20130101 |
Class at
Publication: |
427/177 |
International
Class: |
G21C 3/00 20060101
G21C003/00; C23C 16/02 20060101 C23C016/02 |
Foreign Application Data
Date |
Code |
Application Number |
Feb 29, 2008 |
JP |
2008-050324 |
Claims
1. A method for producing a tubular body, comprising: winding
ceramic fibers to form an aggregate with the ceramic fibers, the
aggregate having a tubular shape; vapor depositing pyrolytic carbon
on the aggregate to form a fiber-reinforced carbonaceous substrate;
converting the pyrolytic carbon located at least on an outer
surface of the fiber-reinforced carbonaceous substrate to CVR-SiC
by reaction with an SiO gas to form an CVR-SiC layer; and
depositing CVD-SiC on a surface of the CVR-SiC layer after forming
the CVR-SiC layer, an amount of silicon decreasing from a boundary
region to an inside of the fiber-reinforced carbonaceous
substrate.
2. A method for producing a tubular body, comprising: weaving
strands including ceramic fibers to form an aggregate with the
ceramic fibers, the aggregate having a braid form which has a
hollow mesh body; vapor depositing pyrolytic carbon on the
aggregate to form a fiber-reinforced carbonaceous substrate;
converting the pyrolytic carbon positioned at least on an outer
surface of the fiber-reinforced carbonaceous substrate to CVR-SiC
by reaction with an SiO gas to form an CVR-SiC layer; and
depositing CVD-SiC on a surface of the CVR-SiC layer after forming
the CVR-SiC layer, an amount of silicon decreasing from a boundary
region to an inside of the fiber-reinforced carbonaceous
substrate.
3. The method according to claim 1, wherein a mass ratio of the
ceramic fibers to the fiber-reinforced carbonaceous substrate
ranges from about 10% to about 50%.
4. The method according to claim 1, wherein a thickness of the
fiber-reinforced carbonaceous substrate ranges from about 0.3 mm to
about 2 mm.
5. The method according to claim 1, wherein the tubular body is
used as a nuclear fuel cladding tube.
6. The method according to claim 1, wherein a thickness of the
fiber-reinforced carbonaceous substrate ranges from about 0.3 mm to
about 2 mm.
7. The method according to claim 1, wherein raw material for the
ceramic fibers includes ZrC.
8. The method according to claim 2, wherein a mass ratio of the
ceramic fibers to the fiber-reinforced carbonaceous substrate
ranges from about 10% to about 50%.
9. The method according to claim 2, wherein a thickness of the
fiber-reinforced carbonaceous substrate ranges from about 0.3 mm to
about 2 mm.
10. The method according to claim 2, wherein the tubular body is
used as a nuclear fuel cladding tube.
11. The method according to claim 2, wherein a thickness of the
fiber-reinforced carbonaceous substrate ranges from about 0.3 mm to
about 2 mm.
12. The method according to claim 2, wherein raw material for the
ceramic fibers includes ZrC.
Description
CROSS-REFERENCE TO RELATED APPLICATIONS
[0001] The present application is a divisional application of the
U.S. patent application Ser. No. 12/369,391, filed Feb. 11, 2009,
which claims priority under 35 U.S.C. .sctn.119 to Japanese Patent
Application No. 2008-050324, filed on Feb. 29, 2008. The contents
of these applications are incorporated herein by reference in their
entirety.
BACKGROUND OF THE INVENTION
[0002] 1. Field of the Invention
[0003] The present invention relates to a method for producing the
tubular body.
[0004] 2. Discussion of the Background
[0005] In many nuclear reactors today, nuclear fuel is contained in
a sealed metal tube called a "cladding tube", and this cladding
tube is generally made of a zirconium alloy or a steel alloy. The
cladding tube is designed so that any radioactive gas and solid
fission product are surely held in the tube and not released to a
coolant during normal operation or during a conceivable accident.
If the cladding tube is damaged, heat, hydrogen and ultimately the
fission product can be released to the coolant.
[0006] Problems with conventional cladding tube are known. For
example, the metal cladding tube is relatively soft, and may come
into contact with a fragment which sometimes flows into a cooling
system and contacts with fuel, so that the metal cladding tube
wears or corrodes. As a result, such wear or corrosion is likely to
lead to damage of a boundary wall of a metal containment, and
consequently to release of the fission product into the coolant.
Further, the metal cladding tube exothermicly react with hot water
of 1,000.degree. C. or higher to result in the addition of further
heat to fission product decay heat generated by the nuclear fuel.
This additional heat from the cladding further amplifies the
seriousness and duration period of an accident, for example, as
occurred at Three Mile Island.
[0007] JP-A-2008-501977 describes a multilayer ceramic tube
(cladding tube) including an inner layer of monolithic SiC; an
intermediate layer as a composite material in which SiC fibers are
surrounded by a SiC matrix; and an outer layer of SiC. The contents
of JP-A-2008-501977 are incorporated herein by reference in their
entirety.
[0008] However, in such a cladding tube composed of SiC as a whole,
the monolithic SiC layer is formed by Chemical Vapor Deposition
(CVD) or the like, and all of the inner layer, the intermediate
layer and the outer layer have high rigidity, so that particularly,
strain generated by an immediate change in temperature which occurs
at the start of an operation can develop into a crack penetrating
front to back sides of the cladding tube.
[0009] Further, in order to prevent such a problem, the
JP-A-2008-501977 proposes to provide each fiber with double
coatings including an inside pyrolytic carbon sublayer for
preventing the development of the crack and an outside SiC sublayer
for protecting carbon from an oxidizing environment. However, in
order to provide each fiber with the double coatings, film forming
has to be performed on a fiber surface in a state where each fiber
is dispersed. If each fiber can not be sufficiently dispersed, it
can be coated with only either one of the above-described
sublayers. Accordingly, the SiC fiber and the SiC matrix come into
contact with each other to cause that the pyrolytic carbon layer
would not sufficiently function.
[0010] Further, in JP-A-2008-501977, the SiC matrix is formed by
two processes of providing the SiC fiber surface with the coatings
and multistage treatment in which CVD or polymer
penetration/pyrolysis are repeated. Such a production method
requires repetition of treatment many times, resulting in
complicated processes.
SUMMARY OF THE INVENTION
[0011] According to an aspect of the present invention, a method
for producing a tubular body includes winding ceramic fibers to
form an aggregate with the ceramic fibers. The aggregate has a
tubular shape. Pyrolytic carbon is vapor deposited on the aggregate
to form a fiber-reinforced carbonaceous substrate. The pyrolytic
carbon positioned at least on an outer surface of the
fiber-reinforced carbonaceous substrate is converted to CVR-SiC by
reaction with an SiO gas to form an CVR-SiC layer. CVD-SiC is
deposited on a surface of the CVR-SiC layer after forming the
CVR-SiC layer. An amount of silicon decreases from a boundary
region to an inside of the fiber-reinforced carbonaceous
substrate.
[0012] According to another aspect of the present invention, a
method for producing a tubular body includes weaving strands
including ceramic fibers to form an aggregate with the ceramic
fibers. The aggregate has a braid form which has a hollow mesh
body. Pyrolytic carbon is vapor deposited on the aggregate to form
a fiber-reinforced carbonaceous substrate. The pyrolytic carbon
positioned at least on an outer surface of the fiber-reinforced
carbonaceous substrate is converted to CVR-SiC by reaction with an
SiO gas to form an CVR-SiC layer. CVD-SiC is deposited on a surface
of the CVR-SiC layer after forming the CVR-SiC layer. An amount of
silicon decreases from a boundary region to an inside of the
fiber-reinforced carbonaceous substrate.
BRIEF DESCRIPTION OF THE DRAWINGS
[0013] The above and other aspects of the present invention will
become more apparent and more readily appreciated from the
following description of exemplary embodiments of the present
invention taken in conjunction with the attached drawings, in
which:
[0014] FIG. 1 is a view schematically showing a section taken on a
plane parallel to a central axis of a tubular body in a state where
a nuclear fuel is covered with the tubular body used as a cladding
tube according to an exemplary embodiment;
[0015] FIG. 2 is a view schematically showing a section in an
arbitrary direction of a tubular body according to an exemplary
embodiment; and
[0016] FIG. 3 is a view schematically showing a section in an
arbitrary direction of tubular body according to another exemplary
embodiment of the present invention.
DESCRIPTION OF THE EMBODIMENTS
[0017] The embodiments will now be described with reference to the
accompanying drawings, wherein like reference numerals designate
corresponding or identical elements throughout the various
drawings.
[0018] The tubular body according to an exemplary embodiment of the
present invention usually has a cylindrical body opened at an end
portion, but may be closed at the end portion depending on the
design of the nuclear reactor. Hereinafter, there will be described
respective portions of the tubular body according to an exemplary
embodiment in detail.
[0019] The fiber-reinforced carbonaceous substrate is a tubular
body including an aggregate formed of ceramic fibers and a
carbonaceous material filled in interstices between the ceramic
fibers.
[0020] Herein, the carbonaceous material means a material
substantially composed of carbon, and may be pyrolytic carbon,
glassy carbon or the like. In particular, pyrolytic carbon is
preferred.
[0021] The pyrolytic carbon has good adhesion properties to ceramic
fibers, particularly to SiC fibers, and moreover, can provide a
high-purity carbonaceous material by using a high-purity raw
material. Chemical Vapor Infiltration (CVI) for vapor depositing
the pyrolytic carbon is performed on the aggregate, thereby being
able to form the fiber-reinforced carbonaceous substrate with the
carbonaceous material filled in the interstices between the ceramic
fibers. The CVI is a vacuum film forming method based on the same
principle as CVD.
[0022] The carbonaceous material of the fiber-reinforced
carbonaceous substrate is unnecessary to densely fill all the
interstices between the ceramic fibers of the aggregate, and may
fill only a surface layer of the aggregate, because even when only
the surface layer portion is densely filled, an anchor effect
between the SiC layer and the ceramic fibers can be sufficiently
obtained.
[0023] In the fiber-reinforced carbonaceous substrate, the mass
ratio of the ceramic fibers to the whole substrate is preferably
from about 10% to about 50%, and more preferably from about 20% to
about 30%. Less than about 10% of the ratio results in a decrease
in strength of the substrate, whereas exceeding about 50% of the
ratio causes difficulty to hold the ceramic fiber while being
compressed before the CVI treatment, resulting in easy deformation
in shape.
[0024] The thickness of the fiber-reinforced carbonaceous substrate
is preferably from about 0.3 mm to about 2 mm, and more preferably
from about 0.5 mm to about 1.2 mm. Less than about 0.3 mm of the
thickness may result in difficulty to have sufficient strength,
whereas exceeding about 2 mm of the thickness results in tendency
to fail to sufficiently transfer heat to the coolant.
[0025] The SiC layer means a layer substantially composed of SiC,
and usually means a layer containing SiC in an amount of 95% by
mass or more.
[0026] The SiC layer can be obtained by converting the carbonaceous
material on a surface of the fiber-reinforced carbonaceous
substrate to SiC by reaction with an SiO gas. The SiO gas is
obtained, for example, by disposing an silicon mixture of various
kinds such as Si powder-SiO.sub.2 powder, SiC powder-SiO.sub.2
powder or carbon powder-SiO.sub.2 powder as a source on a bottom of
a furnace, disposing the fiber-reinforced carbonaceous substrate
above it, and performing heat treatment at 1,300.degree. C. to
2,300.degree. C.
[0027] The SiC layer (CVR-SiC layer) thus obtained by the reaction
conversion has an unclear boundary between the SiC layer and the
fiber-reinforced carbonaceous substrate, and silicon atoms are
diffused from the boundary region to an inside of the
fiber-reinforced carbonaceous substrate (as shown in FIG. 2,
CVR-SiC forms the boundary region 7 and the SiC layer 8 in such a
manner that its density gradually increases from the inside of the
tube to the outside thereof). In other words, in the boundary
region between the fiber-reinforced carbonaceous substrate and the
SiC layer 8, the amount of silicon gradually increases from the
inside to the outside. In the case of the CVD-SiC layer formed by
CVD or the like, diffusion of silicon atoms from a boundary region
with the fiber-reinforced carbonaceous substrate to the inside of
the fiber-reinforced carbonaceous substrate is not observed.
[0028] SiC has a thermal expansion coefficient of 2 to 3 times that
of the pyrolytic carbon so that SiC has a problem of being easily
separable. However, the CVR-SiC layer is originally obtained by
converting the carbonaceous material to SiC, and has no clear
boundary with the carbonaceous material so that this configuration
has an advantage that interlayer separation is not likely to
occur.
[0029] Further, in use for cladding tubes for coolants such as
water and molten metal which have reactivity with carbon, an SiC
layer may be newly deposited on the surface of the SiC layer
according to the exemplary embodiment. Although a method for
depositing the SiC layer is not limited, it is preferred to form a
CVD-SiC layer by the CVD method. The CVD-SiC layer is higher in
density, so that it has low reactivity with a heating medium such
as cooling water or molten metal and has a high shielding effect.
Accordingly, the tubular body having a long life can be
provided.
[0030] Further, if the CVD-SiC layer is further laminated on the
surface of the cladding tube, the CVR-SiC layer and the CVD-SiC
layer on the surface thereof are formed of the same material at an
interface therebetween so that they are approximately equal in
thermal expansion and have strong adhesive force. Accordingly,
there is also an advantage that the SiC layer in which interlayer
separation is not likely to occur is obtained.
[0031] The thickness of the SiC layer according to the exemplary
embodiment is preferably from 10 .mu.m to 500 .mu.m, and more
preferably from 20 .mu.m to 100 .mu.m. With this range, the
advantages of the exemplary embodiment can be sufficiently
exhibited. However, less than 10 .mu.m of the thickness results in
the tendency of the carbonaceous material layer to expose by
abrasion, whereas exceeding 500 .mu.m of the thickness may result
in a decrease in the carbonaceous material of the fiber-reinforced
carbonaceous substrate.
[0032] If the CVD-SiC layer is further coated (laminated) on the
SiC layer according to the exemplary embodiment, the thickness
thereof is preferably from 2 .mu.m to 300 .mu.m, and more
preferably from 10 .mu.m to 100 .mu.m. In the case of less than 2
.mu.m, thin portions are liable to occur in the CVD-SiC layer to
cause failure to obtain a sufficient shielding effect. In the case
of exceeding 300 .mu.m, the dimension error due to unevenness in
thickness of the formed layer increases, and moreover, modifying
processing tends to become difficult because SiC is hard.
[0033] Raw materials for the ceramic fibers constituting the
aggregate include SiC, carbon, ZrC and the like. SiC is preferred
among these, and ZrC is particularly preferred in use for
ultrahigh-temperature gas reactors. These are difficult to react
with the coolant, and also have heat resistance.
[0034] Although the thickness of the ceramic fibers is not
particularly limited, the ceramic fibers having a diameter of 10
.mu.m to 20 .mu.m can be suitably used. As a strand, there can be
suitably utilized one composed of 100 to 1,000 fibers.
[0035] As for the aggregate constituting the fiber-reinforced
carbonaceous substrate of the tubular body according to the
exemplary embodiment, there is no particular limitation on its
structure, as long as it is formed in a tubular form (a tubular
shape). However, it is preferably formed by winding method using
strands of ceramic fibers, or by braiding strands into a hollow
braid mesh body. In the case of the braid, it is formed by weaving
strands composed of ceramic fibers so as to be aligned diagonally
to a central axis of an inner core die, or by triaxial weave using
strands parallel to the central axis.
[0036] According to the configuration as described above, the
ceramic fiber surface contacts with the carbonaceous material so
that a crack which occurs by thermal stress can be stopped at the
ceramic fiber surface. Accordingly, a crack penetrating from the
inside to outside of the tubular body is not likely to occur.
Moreover, pretreatment for providing each ceramic fiber with a
coating is unnecessary so that the process can be simplified.
Furthermore, a nuclear reactor can be operated at higher
temperature by improvement in performance of the tubular body so
that the nuclear reactor having high energy efficiency can be
provided, and the working life thereof can be prolonged.
[0037] In particular, the tubular body may have a simple structure
and be difficult to break in a high-temperature gas reactor using a
coolant having no fear of reacting with carbon, and the like.
[0038] The winding methods for forming the tubular body according
to the exemplary embodiment include a sheet winding method which
includes winding a sheet such as a woven fabric, and the like, as
well as a filament winding method which includes winding a
filament.
[0039] A method for producing the tubular body according to an
embodiment of the present invention will be described below in
detail (see FIG. 2).
(1) Aggregate Forming Step
[0040] The aggregate of the tubular body according to the exemplary
embodiment can be obtained by winding ceramic fibers around an
inner core die having a specific size by a method such as filament
winding or braiding.
[0041] In a braid form, it is particularly advantageous to
constitute the aggregate by triaxial weave including warp yarns and
two pairs of weft yarns rounded in the opposite direction to each
other. In the case of the triaxial weave, the warp yarns are added
as braces to the two pairs of weft yarns, thereby being able to
provide the tubular body which has high rigidity and in which
tension applied to the individual fibers is suppressed.
[0042] The ceramic fibers may be any fibers. For example,
High-Nicalon manufactured by Nippon Carbon Co., Ltd. can be
utilized as the SiC fibers. Although a material of the inner core
die is not particularly limited, it is advantageous to use an inner
core die made of graphite so as not to react in a CVD step
described later and the like.
[0043] In order to make it easy to perform mold release of the
aggregate, the inner core die is preferably coated with a release
agent. Although the kind of release agent is not particularly
limited, it is advantageous to use a graphite powder or
graphite-based release agent which makes easy mold release after
CVD and has no fear of impurity incorporation.
(2) Carbonaceous Material Forming Step
[0044] The carbonaceous materials include pyrolytic carbon obtained
by CVI, glassy carbon obtained by repeating impregnation of a resin
solution as a carbon precursor, followed by burning, and the like.
Among the above, the pyrolytic carbon obtained by CVI (CVD) is
particularly advantageous, because the high-purity carbonaceous
material is easily obtained by upgrading the purity of a raw
material gas, and moreover, the carbonaceous material is obtained
by single treatment of continuously supplying the raw material
gas.
[0045] The CVI (CVD) is performed in a CVI (CVD) furnace at a
degree of vacuum of 1 kPa to 30 kPa and a temperature of about
1,200.degree. C. to 1,900.degree. C., using a hydrocarbon gas as a
raw material and hydrogen as a carrier gas.
[0046] Further, in order to form an SiC layer having a sufficient
thickness in a subsequent SiC layer forming step, the treatment may
be continued after the carbonaceous material has been filled in
interstices between the fibers of the aggregate to allow a thick
carbonaceous material layer composed of only the pyrolytic carbon
to grow on a surface of the fiber-reinforced carbonaceous
substrate. When the CVI (CVD) treatment is stopped at the stage
where the carbonaceous material has been filled in interstices
between the fibers of the aggregate, only a carbonaceous layer
having a thickness of at most about 100 .mu.m composed of only the
pyrolytic carbon is formed on the surface of the fiber-reinforced
carbonaceous substrate. However, the carbonaceous material layer
composed of only the pyrolytic carbon and necessary for obtaining
the SiC layer having a sufficient thickness can be obtained by
continuing the treatment more.
[0047] If the carbonaceous material layer composed of only the
pyrolytic carbon and necessary for obtaining the SIC layer having a
sufficient thickness is not formed in the carbonaceous material
forming step, a tubular body in which silicon atoms are diffused in
an inside of the carbonaceous material of the fiber-reinforced
carbonaceous substrate, as shown in FIG. 3, can be obtained.
(3) SiC Layer Forming Step
[0048] As for an intermediate product produced as described above,
a surface of the pyrolytic carbon is subjected to the following
chemical vapor reaction (CVR) in an SiO.sub.2 gas, using a reaction
furnace of atmospheric pressure and under a temperature of
1,200.degree. C. to 2,300.degree. C., thereby being able to obtain
a CVR-SiC layer composed of reaction-converted SiC.
2C+SiO.fwdarw.SiC+CO.uparw.
[0049] The SiC layer may be formed not only on an outer surface of
the fiber-reinforced carbonaceous substrate but also on an inner
surface thereof
[0050] If the SiC layers are formed on both surfaces, the tubular
aggregate is placed in a CVD furnace as it is, and the pyrolytic
carbon is subjected to the CVI (CVD) treatment, followed by SiC
conversion treatment in a reaction furnace, thereby
reaction-converting the outer surface and the inner surface to
perform SiC conversion. Further, the SiC layers can also be formed
on both surfaces by inserting an inner core die into the tubular
aggregate, subjecting the pyrolytic carbon to the CVI (CVD)
treatment in the CVD furnace to obtain the fiber-reinforced
carbonaceous substrate, then, drawing the inner core die out, and
reaction-converting the outer surface and the inner surface in a
reaction furnace to perform SiC conversion.
[0051] As described above, according to the exemplary embodiment,
the tubular body having the CVR-SiC layer on the outer surface can
be obtained by three steps of (1) the aggregate forming step, (2)
the carbonaceous material forming step and (3) the SiC layer
forming step. Therefore, the process can be largely simplified
compared to the related-art technique, for example, that described
in JP-A-2008-501977.
[0052] Furthermore, in order to increase airtightness of the
CVR-SiC layer, a CVD-SiC layer may be deposited thereon. It is
obtained by using methyltrichlorosilane (MTS: CH.sub.3Cl.sub.3Si)
as a raw material gas, and performing deposition in a CVD furnace
at a degree of vacuum of 5 kPa to 30 kPa and a temperature of about
1,000.degree. C. to 1,400.degree. C.
EXAMPLES
[0053] A more specific configuration of the tubular body according
to an exemplary embodiment and a production methods thereof will be
described with reference to the following examples. The present
invention is not limited to the production method described in the
examples.
(1) Aggregate Forming Step
[0054] First, a rod-like inner core die for forming a triaxial
weave braid is prepared. As the inner core die, an inner core die
made of graphite is used so as not to react in a CVD step.
[0055] The size (diameter) of the inner core die is approximately
equal to the size of a nuclear fuel (diameter: 8 to 11 mm)
[0056] Ribbon-like strands are each formed by bundling a plurality
of SiC fibers, and the strands are woven along an outer periphery
of a forming die by a three-dimensional braiding method to form a
braid. A commercially available automatic loom (for example,
TWM-32C, TRI-AX, manufactured by Howa Machinery, Ltd.) is utilized
for weaving the strands.
[0057] As the SiC fibers used herein, it is advantageous to use
high-purity SiC fibers.
(2) Carbonaceous Material Forming Step
[0058] The aggregate obtained in the above-described step is placed
in a CVD furnace of pyrolytic carbon, and the pyrolytic carbon is
deposited in interstices between the SiC fibers. At that time,
using propane as a raw material and hydrogen as a carrier gas, the
pyrolytic carbon is deposited in the interstices between the SiC
fibers under conditions of about 1,700.degree. C. for about 1 hour,
thereby obtaining a fiber-reinforced carbonaceous substrate having
a thickness of 1 mm and containing a carbonaceous material in an
amount of 20% by mass.
(3) SiC Layer Forming Step
[0059] A surface of the fiber-reinforced carbonaceous substrate
obtained in the above-described step is converted to SiC by
reaction with an SiO gas in a reaction furnace. The SiO gas is
generated from a source mounted in the furnace, in which an SiC
powder and an SiO.sub.2 powder are mixed, and the conversion can be
suitably performed at a reaction temperature of 1,900.degree. C.,
atmospheric pressure and a reaction time of 1 hour in an argon
atmosphere. A CVR-SiC layer has a thickness of 10 .mu.m.
(4) CVD-SiC Deposition Step
[0060] The tubular body according to the exemplary embodiment can
be produced by the above-described steps (1) to (3). However, in
order to more increase airtightness, a CVD-SiC layer is further
deposited on the reaction-converted SiC surface. The
above-described intermediate product is placed in a CVD furnace,
and film formation is performed at 1,350.degree. C. using a
methyltrichlorosilane gas. CVD-SiC layer has a thickness of 20
.mu.m.
[0061] The tubular body according to the exemplary embodiment can
be obtained by the above-described method. An example using this
tubular body as a cladding tube 1 for a nuclear fuel 2 is shown in
FIG. 1.
[0062] While the present invention has been shown and described
with reference to certain exemplary embodiments thereof, it will be
understood by those skilled in the art that various changes in form
and details may be made therein without departing from the spirit
and scope of the invention as defined by the appended claims.
* * * * *