U.S. patent application number 14/535239 was filed with the patent office on 2015-03-05 for carbon material and method for producing same.
This patent application is currently assigned to INCUBATION ALLIANCE, INC.. The applicant listed for this patent is INCUBATION ALLIANCE, INC.. Invention is credited to Kazuo MURAMATSU, Masahiro Toyoda.
Application Number | 20150064464 14/535239 |
Document ID | / |
Family ID | 43222700 |
Filed Date | 2015-03-05 |
United States Patent
Application |
20150064464 |
Kind Code |
A1 |
MURAMATSU; Kazuo ; et
al. |
March 5, 2015 |
CARBON MATERIAL AND METHOD FOR PRODUCING SAME
Abstract
(Problem) In conventional method for producing artificial
graphite, in order to obtain a product having excellent
crystallinity, it was necessary to mold a filler and a binder and
then repeat impregnation, carbonization and graphitization, and
since carbonization and graphitization proceeded by a solid phase
reaction, a period of time of as long as 2 to 3 months was required
for the production and cost was high and further, a large size
structure in the shape of column and cylinder could not be
produced. In addition, nanocarbon materials such as carbon
nanotube, carbon nanofiber and carbon nanohorn could not be
produced. (Means to solve) A properly pre-baked filler is sealed in
a graphite vessel and is subsequently subjected to hot isostatic
pressing (HIP) treatment, thereby allowing gases such as
hydrocarbon and hydrogen to be generated from the filler and
precipitating vapor-phase-grown graphite around and inside the
filler using the generated gases as a source material, and thereby,
an integrated structure of carbide of the filler and the
vapor-phase-grown graphite is produced. In addition, nanocarbon
materials are produced selectively and efficiently by adding a
catalyst or adjusting the HIP treating temperature.
Inventors: |
MURAMATSU; Kazuo; (Kobe-shi,
JP) ; Toyoda; Masahiro; (Oita-shi, JP) |
|
Applicant: |
Name |
City |
State |
Country |
Type |
INCUBATION ALLIANCE, INC. |
Kobe-shi |
|
JP |
|
|
Assignee: |
INCUBATION ALLIANCE, INC.
Kobe-shi
JP
|
Family ID: |
43222700 |
Appl. No.: |
14/535239 |
Filed: |
November 6, 2014 |
Related U.S. Patent Documents
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Application
Number |
Filing Date |
Patent Number |
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13321944 |
Nov 22, 2011 |
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PCT/JP2010/058834 |
May 25, 2010 |
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14535239 |
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Current U.S.
Class: |
428/367 |
Current CPC
Class: |
B82Y 30/00 20130101;
Y10T 428/298 20150115; C04B 35/6455 20130101; C04B 2235/728
20130101; C04B 2235/3215 20130101; H01G 11/34 20130101; H01M 4/8673
20130101; H01M 4/587 20130101; C01B 2202/36 20130101; C04B 2235/528
20130101; Y10T 428/2918 20150115; B29K 2105/251 20130101; C04B
35/532 20130101; C01B 32/18 20170801; C04B 35/6325 20130101; H01M
4/583 20130101; C01B 32/205 20170801; F16L 59/028 20130101; C04B
2235/422 20130101; C01B 32/158 20170801; C04B 2235/405 20130101;
H01G 11/84 20130101; H01M 4/625 20130101; C01B 32/156 20170801;
C04B 2235/3208 20130101; H01M 4/62 20130101; Y02E 60/50 20130101;
C04B 35/52 20130101; C04B 35/522 20130101; C04B 2235/77 20130101;
C04B 2235/526 20130101; Y02E 60/13 20130101; B29B 13/021 20130101;
C04B 2235/40 20130101; C04B 2235/725 20130101; Y02E 60/10 20130101;
C01B 32/154 20170801; C04B 2235/48 20130101; Y10T 83/0591 20150401;
B82Y 40/00 20130101; H01G 11/36 20130101; Y10T 428/2982 20150115;
C04B 2235/72 20130101; H01G 11/32 20130101; C01B 32/16 20170801;
H01M 10/0525 20130101; H01B 1/04 20130101; H01M 4/366 20130101;
Y10T 428/24999 20150401; C01B 32/184 20170801; C04B 2235/425
20130101; C04B 2235/428 20130101; C04B 2235/5248 20130101; C04B
2235/5436 20130101; C01B 32/159 20170801 |
Class at
Publication: |
428/367 |
International
Class: |
C01B 31/02 20060101
C01B031/02; H01G 11/36 20060101 H01G011/36; H01M 4/86 20060101
H01M004/86; H01B 1/04 20060101 H01B001/04; H01M 4/587 20060101
H01M004/587; H01M 4/62 20060101 H01M004/62 |
Foreign Application Data
Date |
Code |
Application Number |
May 26, 2009 |
JP |
2009-126492 |
Mar 31, 2010 |
JP |
2010-084371 |
Claims
1-29. (canceled)
30. A carbon nanotube having a tube thickness of 10 nm to 30 nm, an
outer diameter of 100 nm to 300 nm and a ratio of a tube thickness
to the outer diameter of less than 20%.
31. (canceled)
Description
TECHNICAL FIELD
[0001] The present invention relates to a novel structure and
production method of an artificial graphite material which is used
on electrode materials and diffusion layer for lithium ion battery,
lithium ion capacitor, fuel cell, primary battery, second battery,
steel making, refining and electrolysis, crucible for crystal
growth of crystalline silicon and silicon carbide, insulating
material and reactor for nuclear electric power generation.
[0002] The present invention relates to a method for producing
nanocarbon materials such as a carbon nanotube, carbon nanohorn,
graphene and fullerene which are practically used for hydrogen
storing material for fuel cell-powered vehicle, catalyst-carrying
substrate, electrodes for field emission display (FED) assuring low
power consumption, high luminance and low dependency on view angle
and having self-luminescence in the fields of information home
appliances, probe of tunneling microscope, an additive used for a
conductive sheet and high thermal conductivity sheet as a measure
for dust-proofing in semi-conductor manufacturing process by making
use of high thermal conductivity and high electric conductivity
thereof, a light-weight high strength composite material for robot,
and pharmaceutical medicals.
BACKGROUND ART
[0003] Graphite materials are chemically stable and are excellent
in electric and thermal conductivity and mechanical strength at
high temperature, and therefore, are widely used for electrodes for
steel making, electrodes for arc melting and reducing of high
purity silica and electrodes for aluminum refining. Graphite has a
crystal structure formed by stacking of carbon hexagonal planes
generated by growth of carbon hexagonal rings by sp2 hybridized
orbital of carbon atoms, and is classified into a hexagonal system
and rhombohederal system depending on the form of lamination. The
both systems show good electric and thermal conductivity since a
carrier concentration and carrier mobility of free electron and
holes in the carbon hexagonal planes are high.
[0004] On the other hand, since the carbon hexagonal planes are
weakly bonded to each other by so-called Van der Waals force, slip
occurs relatively easily between the planes, and as a result,
graphite has lower strength and hardness as compared with those of
metallic materials and has self-lubricating property.
[0005] Since natural graphite produced naturally is a
polycrystalline material, breakdown occurs at an interface of
crystal grains and natural graphite is produced in a flaky form,
not in a massive form having sufficient hardness and strength.
Therefore, generally natural graphite is classified by its particle
size and is used as an aggregate (a filler).
[0006] On the other hand, in order to use graphite in various
applications mentioned above by making use of excellent
characteristics thereof, it is necessary to produce a graphite
structure having practicable strength and hardness. Since it is
difficult to obtain such a structure from natural graphite alone,
various so-called artificial graphite materials have been developed
and put into practical use.
[0007] (General Method for Producing Artificial Graphite
Materials)
[0008] Artificial graphite materials are produced by mixing a
filler as an aggregate and a binder and subjecting the mixture to
molding, baking for carbonization and graphitization treatment. It
is essential that both of the filler and the binder remain as
carbon after the baking for carbonization so as to give high
carbonization yield, and a suitable filler and binder are selected
depending on applications.
[0009] A pre-baked petroleum coke, a pre-baked pitch coke, a
natural graphite, a pre-baked anthracite, a carbon black and the
like are used as a filler. These fillers are kneaded with coal tar
pitch, coal tar, a polymer resin material, or the like and molded
into a desired form by extruding, casting, pressing or the like
method.
[0010] A molded material is baked for carbonization at a
temperature of 1000.degree. C. or more in an inert atmosphere and
then baked at a high temperature of 2500.degree. C. or more for
developing a graphite crystal structure and graphitizing. During
the baking for carbonization, the starting material are subject to
decomposition, and moisture, carbon dioxide, hydrogen, and
hydrocarbon gases are generated from component elements other than
carbon such as hydrogen and nitrogen, and therefore, the baking is
controlled to be a low temperature elevating rate, and generally a
very long period of time of 10 to 20 days for heating up and 5 to
10 days for cooling, totally 15 to 30 days is necessary for
production.
[0011] Graphitization process is carried out by electric heating
with a large-sized oven such as an Acheson electrical resistance
oven. Also in the graphitization process, a period of time of 2 to
7 days for electric heating and 14 days for cooling, totally 16 to
21 days is necessary. Totally about two months is required for
production including preparation of a staring material, molding,
baking for carbonization and graphitization. (Non-patent Document
1)
[0012] In general artificial graphite, a filler added in a molding
step is easily formed evenly in a certain direction and
crystallinity is enhanced as carbonization and graphitization
proceed. Therefore, anisotropy tends to be increased and as a
result, a bulk density and a mechanical strength tend to be
decreased.
[0013] Both of the filler and binder to be used are hydrocarbon
substances to be carbonized after heat treatment and are roughly
classified into easily graphitizable materials to be easily
graphitized due to a chemical structure thereof and hardly
graphitizable materials hardly graphitized due to crosslinking of a
benzene ring in a structure thereof.
[0014] (Method for Producing High Density Isotropic Graphite
Material)
[0015] Examples of means for achieving high density are to use a
filler capable of being easily graphitized such as mesocarbon
microbeads comprising extracted matter of mesophase, gilsonite coke
or carbon beads, and then to adjust particle size distribution
thereof, to enhance compatibility thereof with a binder pitch, or
to repeat impregnation treatment thereof. Also, in order to impart
isotropic property, application of isotropic pressure with cold
isostatic pressing equipment at the molding stage is effective and
is a general method. In order to further increase a density, a
process for impregnating the material with a binder pitch again
after the graphitization and repeating the graphitization treatment
has been carried out, but in this process, a total period of time
required for production is as extremely long as 2 to 3 months.
[0016] In the case of use for electrode materials and nuclear power
application, purity of a graphite material is critical, and it is
necessary to carry out a treatment for securing high purity with
halogen gas such as chlorine gas at a temperature of as high as
around 2000.degree. C. By the treatment for securing high purity, a
concentration of impurities is decreased from about several
hundreds ppm to about several ppm.
[0017] A starting material to be used for producing general
artificial graphite and high density isotropic graphite is in a
liquid or solid form. In molding, carbonizing and graphitizing
processes, a liquid phase-solid phase reaction or a solid phase
reaction proceeds predominantly. These hydrocarbon based materials
expand its benzene ring network due to dissipation of elements such
as hydrogen, oxygen and nitrogen therefrom, and approximates a
graphite crystal structure by growth and stacking of carbon
hexagonal planes. Particularly in the graphitization process, which
is a solid phase reaction, an extremely long reaction time at a
temperature of as high as 2500.degree. C. or more is required.
[0018] In the case of artificial graphite and high density
isotropic graphite, the graphitization proceeds in a liquid phase
or a solid phase, and therefore even if heat treatment is carried
out for a long period of time at a temperature of as high as
3000.degree. C. or more, complete crystallization (graphitization)
is difficult, a density of the graphite does not reach a
theoretical density of 2.54 g/cm.sup.3, and there is a limit in a
crystal size thereof.
[0019] (Heat Treatment of Polymer Resin Material)
[0020] In the case of a carbon fiber produced using a resin such as
polyacrylonitrile (PAN), coal or petroleum pitch as a starting
material, such starting material of a polymer material are draw
into a fiber and then carbonized and graphitized in the following
heat treatment. In addition, a highly oriented graphite film having
high crystallinity can be produced by depositing or applying boron,
rare earth element or a compound thereof to a polyimide film or a
carbonized polyimide film, laminating a plurality of films and then
carrying out baking while applying pressure to the film surface in
the vertical direction thereof at a temperature of 2000.degree. C.
or more in an inert atmosphere. However, an upper limit of the film
thickness is several millimeters. (Patent Document 3)
[0021] (Method for Precipitating Highly Oriented Graphite in Glassy
Carbon)
[0022] In JP 2633638 B (Patent Document 6), it is disclosed that a
graphite in the form of like bean jam of Monaka of a Japanese-style
confection is precipitated in a glassy carbon by means of molding a
thermosetting resin into a thick plate by hot press or the like,
forming the resin into a glassy carbon by carbonization treatment
and subsequently subjecting the glassy carbon to hot iso static
pressing treatment. In this method, it is necessary to control
thickness of the glassy carbon to about 6 mm in order to enable
baking and also necessary to break a shell of the glassy carbon
after generation of graphite in order to take out a graphite
precipitate.
[0023] (Method for Producing Graphite Material by Vapor Phase
Growth)
[0024] There is a method for producing carbon and a graphite
material through vapor phase growth by using hydrocarbon and
hydrogen gas as starting materials and a reactor such as CVD
(Chemical Vapor Deposition) equipment and bringing the starting
materials into contact with a metal catalyst at high temperature.
Examples of carbon materials to be produced by vapor phase growth
are a vapor-phase-grown carbon fiber, a carbon nanotube, a carbon
nanohorn, fullerene and the like.
[0025] In the case of a vapor-phase-grown carbon fiber, by
suspending an oxide of transition metal having a size of several
hundreds angstrom in a solvent such as an alcohol and spraying the
solvent onto a substrate and drying it, the substrate carrying a
catalyst is produced. This substrate is put in a reactor and a
hydrocarbon gas is flowed thereinto at a temperature of
1000.degree. C., thus growing a carbon fiber from the surface of
the transition metal on the substrate by vapor phase reaction.
Alternatively there is a case of letting a mixture of a gas of
organic transition metal compound and a hydrocarbon gas flow into a
reactor of about 1000.degree. C. (Patent Document 1)
[0026] A graphitized fiber is obtained by subsequently
heat-treating the carbon fiber obtained by vapor phase growth at
high temperature of 2000.degree. C. or more in an oven for
graphitization treatment. (Patent Document 2) In order to produce a
graphitized fiber directly by vapor phase growth, a reaction
temperature of around 2000.degree. C. is required. However, in such
a temperature range, a transition metal as a catalyst is liquefied
and vaporized, and a function of the catalyst is not exhibited.
Therefore, generally graphitization is carried out separately after
carbonization at low temperature.
[0027] (Carbon Nanotube)
[0028] A carbon nanotube is a very minute substance having an outer
diameter of the order of nanometer and comprising cylindrical shape
carbon hexagonal plane having a thickness of several atomic layers,
which was found in 1991. (Non-patent Document 1) It is known that
this carbon nanotube exists in a deposit generated on a negative
electrode due to arc discharge of a carbon material such as a
graphite, and this carbon nanotube is produced by using a carbon
material such as a graphite as a positive electrode and a heat
resistant conductive material as a negative electrode and carrying
out arc discharge while adjusting a gap between the positive
electrode and the negative electrode in response to growth of a
deposit on a negative electrode. (Patent Document 4)
[0029] A carbon nanotube is generated by arc discharge. However, a
large-sized reactor is required and yield obtained is extremely
low, and therefore, a mass production method has been studied.
Generally in arc discharge of carbon to be used for production of a
nanotube, plasma in a state where carbon molecular species such as
C, C2 and C3 being contained is generated in a reactor fully filled
with an inert gas, and, in the next stage, these carbon molecular
species are solidified into soot, fullerene, a nanotube or a high
density solid. Therefore, yield of nanotube is increased by
optimizing a partial pressure of gases in a chamber and a plasma
temperature. (Patent Document 5)
[0030] A tube composed of carbon hexagonal planes (graphene sheet)
is CNT, and a carbon nanotube comprising a single layer graphene
sheet is called a mono-layer CNT or SWCNT (Single-walled Carbon
Nanotube) having an outer diameter of about 0.5 nm to about 10 nm,
and a carbon nanotube comprising multi-layer graphene sheets is
called a multi-layer CNT or MWCNT (Multi-walled Carbon Nanotube)
having an outer diameter of 10 nm to 100 nm. Thus carbon nanotubes
are classified in such a manner. Currently most of commercially
available carbon nanotubes are multi-layer CNT, which are a mixture
with carbon fibers and graphite fibers that do not form a tube.
[0031] Methods for producing a carbon nanotube are explained
systematically as follows.
1) Arc Discharging Method
[0032] High voltage is applied between carbon electrodes in vacuo
or under reduced pressure to cause arc discharging and deposit
carbon vaporized at locally super high temperature (4050.degree.
C.) on the negative electrode.
2) Laser Vaporization Method
[0033] Laser is emitted to a mixture of carbon and a catalyst in
vacuuo or under reduced pressure to vaporize carbon at a locally
super high temperature (4050.degree. C.), and grow the vaporized
carbon into CNT on the catalyst.
3) Chemical Vapor Phase Growth Method
[0034] CNT is precipitated on a catalyst by passing a
carbon-containing gas (hydrocarbon) and a metal catalyst through a
reaction tube heated to 1000-2000.degree. C.
4) Other Methods Such as SiC Surface Decomposition Method and
Polymer Blend Spinning Method
[0035] Fullerene is a spherical molecule comprising 60 carbon
atoms, and one having a structure similar to a soccer ball is
called C60, one having more than 60 carbon atoms in a cage is
called a high-order fullerene, and one containing metal in a cage
is called a metal-incorporated fullerene. Fullerene is extracted
from a vaporized carbon obtained by applying a high voltage between
carbon electrodes in vacuo or under reduced pressure to cause arc
discharging and vaporizing at locally super high temperature
(4050.degree. C.) by the arc discharging method in the same manner
as in CNT. In addition, at an initial stage of the arc discharging,
fullerene is generated by combusting a gas mixture of a
carbon-containing gas (hydrocarbon), oxygen and argon under reduced
pressure by a combustion method.
[0036] Also, nanocarbon materials such as graphene composed of one
carbon hexagonal plane and a carbon nanohorn obtained by forming
graphene into a tube of a circular cone shape are reported.
However, any of them are produced by the same method as in
fullerene, and in many cases, carbon materials other than CNT are
produced secondarily and a selective production method has not been
established.
PRIOR ART DOCUMENTS
Patent Documents
[0037] Patent Document 1: JP 62-49363 B [0038] Patent Document 2:
JP 2664819 B [0039] Patent Document 3: JP 3065896 B [0040] Patent
Document 4: JP 2526408 B [0041] Patent Document 5: JP 2541434 B
[0042] Patent Document 6: JP 2633638 B
Non-Patent Document
[0042] [0043] Non-Patent Document 1: Nature 354, 56-58, 1991
DISCLOSURE OF INVENTION
Problem to be Solved by the Invention
[0044] In the case of producing a graphite material having good
crystallinity (degree of graphitization) and being in the form of
mass, block, cylinder, polygonal rod or sheet, a material once
carbonized need to be graphitized at high temperature of about
3000.degree. C. for a long period of time in a solid phase
reaction. Therefore, productivity is remarkably low and cost is
high. In order to allow the graphitization to proceed in a solid
phase, it has been difficult to obtain complete crystallinity of
graphite in an industrially applicable processing time for
graphitization. In addition, in order to obtain a high density
graphite material, it is necessary to control an orientation of
carbon hexagonal planes at the carbonization stage so that the
graphitization should proceed even in a solid phase reaction.
Further there is a problem that steps for preparing a starting
material, molding and carbonizing are complicated and troublesome,
productivity is very low and metal impurities remain in the
graphite material.
[0045] Also, in electrodes of secondary batteries such as lithium
ion batteries and hybrid capacitors and electrodes and diffuser
panels of fuel cells, a porous graphite panel or sheet having a
high open pore ratio is required. However, when a porous article is
made of an artificial graphite material, strength of the material
cannot be maintained, and therefore, it is necessary to pulverize
the material into a powdery and/or particulate form, to form it
into slurry and then to coat the slurry on a metal plate or the
like.
[0046] In the method for producing vapor-phase-grown carbon fibers
using hydrocarbon gas as a starting material, the fibers can be
produced by a relatively easy process. However, it is necessary to
provide a vapor phase reaction chamber (reactor) and graphitizing
treatment is required separately, and therefore, there is a problem
that equipment cost increases greatly in a mass production. In
addition, an obtained material is in the form of fiber having a
diameter of 1 mm or less, and therefore, in order to obtain a
graphite material with a desired shape having a sufficient
strength, it is necessary to combine with a binder by impregnation
or to mold together with a resin or to conduct carbonization and
graphitization again. Further, since a metal catalyst is an
essential material for generation of fibers, it is necessary to
remove the added catalytic metal in order to achieve a highly
purity.
[0047] Also, in the case of nanocarbon materials such as a carbon
nanotube, fullerene and carbon nanohorn, yield is extremely low,
and in order to use them as a structural component, it is necessary
to combine with a polymer material as an additive and then conduct
carbonization and graphitization again or coating of slurry and
drying.
[0048] In the method for producing a highly oriented graphite by
treating a polyimide resin at high pressure (application of direct
pressure on a material in a vertical direction thereto) at high
temperature, there are problems that there is a limit in a
thickness of a producible product, anisotropy is large and strength
is very low.
[0049] In the method for precipitating highly oriented graphite
inside a thick glassy carbon material by hot isostatic pressing
treatment, it is difficult to bake a dense glassy carbon into a
thickness of 10 mm or more, and further, since it is necessary to
take out precipitated graphite by breaking a shell of a glassy
carbon, there is a problem that a large in size or porous graphite
cannot be obtained.
[0050] As mentioned above, in the methods for carbonization and
graphitization in a solid phase using a liquid or solid starting
material in the conventional methods for producing graphite
materials, there is a problem that (1) in order to develop carbon
hexagonal planes (graphite crystal structure), a very long period
of time of about two months is required at a maximum ultimate
temperature of about 3000.degree. C., (2) a complete graphite
crystal structure cannot be obtained, (3) even if a complete
graphite crystal structure is obtained, anisotropy is high and
strength is low (being strong in a plane direction but low in a
thickness direction), (4) it is difficult to produce a porous
article having a large open pore ratio, (5) in order to obtain a
high strength, it is necessary to enhance both of isotropy and
density and carry out repeated adjustment of a composition and
structure of a filler and a binder, impregnation, molding,
carbonization and graphitization, and (6) purity enhancing
treatment is separately required for removing impurities.
[0051] In the method for allowing carbonization and graphitization
to proceed in a gaseous phase (including radical in plasma) by
using a gaseous or solid starting material or for producing a
material mainly comprising a graphite crystal structure such as a
carbon nanotube, graphene, fullerene, a carbon nanofiber and a
carbon nanohorn, there is a problem that (1) quite a large-scaled
reactor is required compared to an amount of obtained material, and
therefore, production efficiency is very low and a mass production
is difficult, (2) there is a limit in size to nano scale to at most
millimeter scale, and it is difficult to directly produce a
material of a large size in a form such as a mass, block, cylinder,
polygonal rod or plate, and (3) in many cases, a metal catalyst is
required, and in order to increase purity, such metal need to be
removed.
[0052] In an arc discharge method and a laser vaporization method,
super high temperature up to a sublimation point (4050.degree. C.)
at which carbon is vaporized is necessary and an extremely large
energy is required. In addition, in an arc discharge method and a
laser vaporization method, CNT, fullerene, carbon nanohorn and
graphene and the like which are generated unintentionally are
screened, and therefore, although SWCNT is relatively easily
generated, yield and productivity are still very low, i.e.,
production efficiency of several grams per day.
[0053] In a CVD method for CNT for enhancing productivity, a
substrate for carrying a catalyst is necessary and a generation
reaction occurs on a two-dimensional substrate plane. Therefore, in
order to enhance productivity, a large area is required, and a
generation rate is 0.2 to 0.3 g/hrcm.sup.2 and productivity is
still low. A fluid bed method as a method for reacting CNT on a
three-dimensional space has been developed by National Institute of
Advanced Industrial Science and Technology and Nikkiso Co., Ltd.
However, hydrocarbon gas (liquid) as a starting material and a
catalyst come into contact with each other fluidly and
nonuniformly, and therefore, carbide can be obtained but a
probability of generation of SWCNT and MWCNT is low and especially
yield of SWCNT is low.
[0054] Currently, productivity of a multilayer CNT is 1 kg to 10
kg/day and a price thereof is 30,000 to 100,000 yen/kg,
productivity of a single layer CNT is 10 to 100 g/day and a price
thereof is 300,000 to 1,000,000 yen/kg, and a price of fullerene is
500,000 yen/kg. Thus, prices are very high. Mass production method
has not been established with respect to graphene and carbon
nanohorn. Such being the case, there is a problem that irrespective
of excellent characteristics, application development thereof has
not proceeded.
Means to Solve the Problem
[0055] As mentioned above, with respect to carbon and graphite
materials, there are many problems to be solved and in many cases,
production cannot be carried out in an industrial scale while such
materials of various structures can be produced and they have
excellent characteristics. As a result of intensive study made with
respect to development of efficient method for producing carbon and
graphite materials, however, an epoch-making material and
production method thereof were found out.
[0056] Namely, the first aspect of the present invention relates to
direct generation of vapor-phase-grown carbon and vapor-phase-grown
graphite having developed carbon hexagonal planes by means of a
vapor phase reaction using, as a source material, gases such as
hydrogen and hydrocarbon generated from a pre-baked filler without
using a binder, wherein a hydrocarbon-based starting material in
the form of powder, particle, fiber or mesophase sphere which has
been used as a filler so far is pre-baked, properly charged in a
graphite crucible or the like and heat-treated at about
2000.degree. C. under isotropic gas pressure. FIG. 1 is a
diagrammatic view of the present invention.
[0057] The second aspect of the present invention relates to:
[1] a method for producing a vapor-phase-grown nanocarbon material,
which comprises preparing a filler pre-baked to an extent of
containing remaining hydrogen and then allowed to carry a catalyst
thereon, charging the filler in a closed vessel made of a heat
resistant material, and subjecting the filler together with the
vessel to hot isostatic pressing treatment using a compressed gas
atmosphere. [2] the production method of the above [1], wherein the
filler is a powdery and/or particulate material, [3] the production
method of the above [1] or [2], wherein the nanocarbon material is
a carbon nanotube, or a graphene-laminated carbon nanofiber, a
cup-stacked type carbon nanofiber, a screw type carbon nanofiber or
a carbon nanohorn-stacked carbon nanofiber, [4] the production
method of any of the above [1] to [3], wherein the catalyst is one
or two or more selected from the group consisting of (1) tungsten,
rhenium, osmium, tantalum, molybdenum, niobium, iridium, ruthenium,
hafnium, technetium, rhodium, vanadium, chromium, zirconium,
platinum, thorium, lutetium, titanium, palladium, protactinium,
thulium, scandium, iron, yttrium, erbium, cobalt, holmium, nickel,
dysprosium, terbium, curium, gadolinium, beryllium, manganese,
americium, promethium, uranium, copper, samarium, gold, actinium,
neodymium, berkelium, silver, germanium, praseodymium, lanthanum,
californium, calcium, europium, ytterbium, cerium, strontium,
barium, radium, aluminum, magnesium, plutonium, neptunium,
antimony, zinc, lead, cadmium, thallium, bismuth, polonium, tin,
lithium, indium, sodium, potassium, rubidium, gallium, cesium,
silicon and tellurium, (2) sulfide, boride, oxide, chloride,
hydroxide, nitride and organometallic compound of any one of the
above (1), and (3) a mixture of any of the above (1) and (2) and
sulfur and/or sulfide (including an organosulfur compound) and a
mixture of any of the above (1) and (2) and boron and/or boride
(including an organoboron compound), [5] the production method of
any of the above [1] to [4], wherein the filler is one or two or
more selected from the group consisting of starch, cellulose,
protein, collagen, alginic acid, dammar, kovar, rosin,
gutta-percha, natural rubber, cellulose resin, cellulose acetate,
cellulose nitrate, cellulose acetate butyrate, casein plastic,
soybean protein plastic, phenol resin, urea resin, melamine resin,
benzoguanamine resin, epoxy resin, diallyl phthalate resin,
unsaturated polyester resin, a bisphenol A type epoxy resin,
Novolac type epoxy resin, polyfunctional epoxy rein, alicyclic
epoxy resin, alkyd resin, urethane resin, vinyl chloride resin,
polyethylene, polypropylene, polystyrene, polyisoprene, butadiene,
nylon, vinylon, acrylic fiber, rayon, polyvinyl acetate, ABS resin,
AS resin, acrylic resin, polyacetal, polyimide, polycarbonate,
modified polyphenylene ether (PPE), polyethylene terephthalate,
polybutylene terephthalate, polyalylate, polysulfone, polyphenylene
sulfide, polyether ether ketone, fluorine-containing resin,
polyamide imide, benzene, naphthalene, anthracene, petroleum pitch,
coal pitch, petroleum coke, coal coke, carbon black, activated
carbon, waste plastic, waste wood, waste plants and garbage, [6]
the production method of any of the above [1] to [5], wherein the
filler pre-baked to an extent of containing remaining hydrogen is
poured into an ionic solution or a complex solution of transition
metal to allow the filler to carry transition metal on the surface
thereof, [7] the production method of the above [6], wherein the
ionic solution of transition metal is one prepared by dissolving a
transition metal chloride and/or an transition metal alkoxide in
water, an alcohol or a mixture of water and alcohol, [8] the
production method of the above [6], wherein the complex solution of
transition metal is one prepared by dissolving a transition metal
acetylacetonate in water, an alcohol or a mixture of water and
alcohol, [9] the production method of any of the above [1] to [8],
wherein the filler pre-baked to an extent of containing remaining
hydrogen is one or two or more selected from the group consisting
of petroleum coke, coal coke and carbon black having hydrogen
corresponding to the remaining hydrogen beforehand. [10] the
production method of any of the above [1] to [9], wherein the
closed vessel made of a heat resistant material is a screw-capped
graphite crucible, [11] a carbon nanotube having an outer diameter
of 1 nm to 500 nm and a ratio of a tube thickness to the outer
diameter of less than 20%, [12] a carbon nanotube having laminated
carbon hexagonal planes around the tube so as to provide a
polygonal cross-section in which the tube is a center.
Effect of the Invention
[0058] In the first aspect of the present invention, as mentioned
above, the method for producing an artificial graphite material by
a simple process as compared with conventional method was invented.
By this method, a period of time for production which has been two
to three months can be shortened to about one week, productivity is
greatly enhanced to enable decrease in cost. In applications to
fuel cells and capacitors, in which cost of carbon materials is
high, it is expected diffusion is promoted due to decrease in
cost.
[0059] In the first aspect of the present invention, in order to
produce graphite by vapor phase growth, it is possible to design
and produce porous and high density graphite materials having ideal
crystal structure and crystal size. In addition, it is possible to
provide electrode materials having an ideal structure for batteries
such as lithium ion batteries and hybrid capacitors utilizing a
reaction for generating a graphite intercalation compound because a
thin material, in which edge portions of carbon hexagonal planes
face toward a plane direction of the material (conventionally in
the case of a thin material, carbon hexagonal planes gather on the
surface of the material), can be produced. Further, it is possible
to produce and provide an ideal material for applications to a
diffuser panel for fuel cell where graphite materials having good
gas permeability because of proper open pores, high electric
conductivity due to high graphite crystallinity, high purity and
high strength are required.
[0060] Also, since it is possible to make on a massive scale at a
low price a carbon fiber-reinforced carbon material, a carbon
fiber-reinforced graphite material, a graphite sheet, a carbon
nanotube, a carbon nanofiber, fullerene, a carbon nanohorn, and a
composite material thereof, application of these materials is
expected to be promoted and enlarged. While carbon nanomaterials,
thin films and fibers have been produced by various vapor phase
reactions, obtained materials were nano structures and thin films,
and in order to form them into optional shapes, separate steps were
required. FIG. 4 compares the conventional method for vapor phase
growth and the present invention with respect to production
processes and obtained shapes.
[0061] In the second aspect of the present invention, nanocarbon
materials can be produced by a CVD reaction using a general large
size HIP equipment and a vessel made of a heat resistant material
such as graphite as a reaction vessel, and therefore, productivity
is enhanced significantly and materials of low price can be
provided. Specifically it becomes possible to charge a starting
material of 10 ton/batch in large-scaled HIP equipment being
currently available on the market, and production of 5 ton/batch
per day at yield of 50% can be obtained.
[0062] In addition, it is possible to allow a filler to carry a
catalyst for generating a nanocarbon material directly thereon or
to carry a nano size catalyst ionized in a solution thereon, and
therefore, a nanocarbon material such as CNT of a desired shape
having a controlled diameter can be produced with high
selectivity.
BRIEF DESCRIPTION OF DRAWINGS
[0063] (FIG. 1) A diagrammatic view explaining a theory of the
present invention.
[0064] (FIG. 2) A chart showing that the number of steps of the
present invention is very small by comparing a conventional
production process of artificial graphite with one example of the
production process of the present invention.
[0065] (FIG. 3) A graph showing a comparison of a period of time
required for production between conventional artificial graphite
and one example of the present invention.
[0066] (FIG. 4) A chart showing comparison between the production
method of conventional vapor-phase-grown graphite and carbon
hexagonal plane derivative and the production method of the present
invention as well as shapes obtained therefrom.
[0067] (FIG. 5) A photograph showing an appearance of one example
of a pre-baked filler in the form of fine powder.
[0068] (FIG. 6) A photograph showing appearances of a graphite
crucible to be used at hot isostatic pressing treatment and an
obtained vapor-phase-grown graphite structure.
[0069] (FIG. 7) A photograph showing a cross-section of a
vapor-phase-grown graphite structure. Herein the portions A
indicate graphite vapor-phase-grown between the starting particles
(a porous layer is being formed), the portions B indicate graphite
vapor-phase-grown in the starting particles, and the portion C
indicates a carbonaceous material on an outer surface of the
starting particle (shell) (here, the carbonaceous material includes
carbide, glassy carbon and hardly-graphitizable carbon, and the
like, but does not include graphite substantially). The total
length of a scale is 10 .mu.m.
[0070] (FIG. 8) An electron microscope photograph of the pre-baked
filler of Example 1 (phenol resin powder heat-treated at
750.degree. C.). The total length of a scale is 10 .mu.m.
[0071] (FIG. 9) A photograph showing an appearance of the
vapor-phase-grown graphite structure obtained in Example 1.
[0072] (FIG. 10) An electron microscope photograph of the broken
surface of the vapor-phase-grown graphite structure obtained in
Example 1. The total length of a scale is 50 .mu.m.
[0073] (FIG. 11) An electron microscope photograph of the
vapor-phase-grown graphite structure obtained in Example 1, showing
graphite and carbon hexagonal plane derivative generated between
the particles. The total length of a scale is 10 .mu.m.
[0074] (FIG. 12) An electron microscope photograph of the
vapor-phase-grown graphite structure obtained in Example 1. The
total length of a scale is 10 .mu.m.
[0075] (FIG. 13) A laser Raman spectrum of vapor-phase-grown
graphite portion generated between the starting particles in the
vapor-phase-grown graphite structure obtained in Example 1. This
indicates that crystallinity is very high.
[0076] (FIG. 14) A laser Raman spectrum of the outer surface
portion (shell) of the starting particles of the vapor-phase-grown
graphite structure obtained in Example 1. This indicates that the
peak at 1360 kayser is very high and this portion has a structure
being similar to that of glassy carbon or hardly-graphitizable
carbon.
[0077] (FIG. 15) An electron microscope photograph of the surface
of the vapor-phase-grown graphite structure obtained in Example 1,
in which the surface was traced with a bamboo spatula. This
indicates that the structure easily slides in a plane direction due
to being a graphite structure and is deformed and that the
structure is a material having high crystallinity. The total length
of a scale is 50 .mu.m.
[0078] (FIG. 16) An electron microscope photograph of the
vapor-phase-grown graphite generated around the filler and obtained
in Example 1. The total length of a scale is 10.0 .mu.m.
[0079] (FIG. 17) A high magnification (25000.times.) electron
microscope photograph of the portion (indicated by numeral 1)
enclosed with a rectangular in FIG. 16. A number of carbon tubes of
nano size were observed. The total length of a scale is 2.00
.mu.m.
[0080] (FIG. 18) An electron microscope photograph of the
vapor-phase-grown graphite generated around the filler and obtained
in Example 1. The total length of a scale is 10.0 .mu.m.
[0081] (FIG. 19) A high magnification (25000.times.) electron
microscope photograph of the portion (indicated by numeral 2)
enclosed with a rectangular in FIG. 18. A number of pencil-like
vapor-phase-grown graphites of micron size having a polygonal
cross-section and grown in the form of long and narrow rod were
observed. The total length of a scale is 2.00 .mu.m.
[0082] (FIG. 20) An electron microscope photograph of the
vapor-phase-grown graphite generated inside the filler and obtained
in Example 1. The total length of a scale is 10.0 .mu.m.
[0083] (FIG. 21) A high magnification (25000.times.) electron
microscope photograph of the portion (indicated by numeral 4)
enclosed with a rectangular in FIG. 20. The total length of a scale
is 2.00 .mu.m.
[0084] (FIG. 22) A high magnification (100000.times.) electron
microscope photograph of the portion (indicated by numeral 4-1)
enclosed with a rectangular in FIG. 21. This portion has a
structure comprising about 10 nm spheroids and several tens
nanometer cavities. The total length of a scale is 500 nm. A higher
magnification (300000.times.) electron microscope photograph of
this photograph is shown in FIG. 80, and a further higher
magnification (800000.times.) electron microscope photograph
thereof is shown in FIG. 81.
[0085] (FIG. 23) A scanning electron microscope (SEM) photograph of
the broken surface of the vapor-phase-grown graphite generated in
Example 10. This indicates that the vapor-phase-grown graphite A is
in a state etched with hydrogen as compared with Example 1 shown in
FIG. 11.
[0086] (FIG. 24) A SEM photograph of the product generated in
Example 10. This indicates that the carbon hexagonal planes grown
in the form of like pencil around CNT are in a state etched with
hydrogen (being similar to CNT generated in Example 13).
[0087] (FIG. 25) A SEM photograph of the product generated in
Example 10. This indicates that the various products are in a state
etched with hydrogen (being similar to ones generated in Example
13).
[0088] (FIG. 26) Vapor-phase-grown graphites in the form of fiber
generated in Example 10 and existing on top of a sample.
[0089] (FIG. 27) An enlarged view of FIG. 26 indicating that a
number of vapor-phase-grown graphites are connected to each other
to be formed into a fiber.
[0090] (FIG. 28) A view showing a state that graphite fibers
generated in Example 10 are growing from the vapor-phase-grown
graphites in a spherical form.
[0091] (FIG. 29) A SEM photograph of the graphite fibers generated
in Example 10 and existing in a sample. The graphite fibers are the
same as those in FIGS. 26 and 27, but are etched with hydrogen.
[0092] (FIG. 30) A still image taken by CCD camera of rod-like
continuous graphite generated by deposition on an inside wall of a
graphite crucible in Example 10.
[0093] (FIG. 31) A SEM photograph of rod-like continuous graphites
generated by deposition on an inside wall of a graphite crucible in
Example 10, and there is a white spherical portion at the tip of
the rod-like graphite.
[0094] (FIG. 32) A SEM photograph showing generation of a number of
rod-like continuous graphites shown in FIG. 31.
[0095] (FIG. 33) A fluorescent X-ray diagram of elements existing
at a tip of the rod-like graphites shown in FIGS. 31 and 32. Si, S,
Ba, Ca and Fe are detected.
[0096] (FIG. 34) A SEM photograph of the vapor-phase-grown
graphites generated in Example 11.
[0097] (FIG. 35) A SEM photograph of a fibrous product in the form
of connection of triangular pyramid and generated in Example
11.
[0098] (FIG. 36) An enlarged view of FIG. 35.
[0099] (FIG. 37) A SEM photograph of the vapor-phase-grown
graphites generated in Example 12.
[0100] (FIG. 38) A SEM photograph of the vapor-phase-grown graphite
fibers generated in Example 12.
[0101] (FIG. 39) An enlarged view of FIG. 38.
[0102] (FIG. 40) A diagrammatic cross-sectional view showing a
structure of a graphite crucible in the embodiment of the present
invention.
[0103] (FIG. 41) A SEM photograph of the CNT having high linearity
generated in Example 13.
[0104] (FIG. 42) A transmission electron microscope (TEM)
photograph of the CNT generated in Example 13, which indicates that
the CNT is of a hollow structure and has high linearity.
[0105] (FIG. 43) A SEM photograph of the tip portion of the CNT
generated in Example 13, which indicates that the CNT has a
multi-layer structure.
[0106] (FIG. 44) A SEM photograph of a carbon material having a
novel structure generated in Example 13, in which carbon hexagonal
planes are laminated around the CNT and grown in the form of like
pencil. The carbon material is a hollow one having a polygonal
cross-section, and a tip portion thereof is in the form of
polygonal pyramid.
[0107] (FIG. 45) An enlarged view of FIG. 44, which indicates a
structure having multi-layers laminated around CNT.
[0108] (FIG. 46) A transmission electron microscope (TEM)
photograph of a carbon material having a novel structure generated
in Example 13, in which carbon hexagonal planes are laminated
around the CNT and grown in the form of like pencil. It can be
confirmed that the carbon material has a hollow.
[0109] (FIG. 47) A SEM photograph of the CNT generated in Example
14, which indicates that the CNT being excellent in linearity and
having an outer diameter of about 10 nm to about 50 nm is slightly
generated.
[0110] (FIG. 48) A SEM photograph showing that the hose-like CNT of
Example 16 is generated around the pre-baked starting material.
[0111] (FIG. 49) A SEM photograph of the tip portion (opening) of
the hose-like CNT of FIG. 48, which indicates a feature such that
the thickness of the CNT is quite thin compared to the diameter
thereof and the CNT is long.
[0112] (FIG. 50) A SEM photograph of the tip portion (opening) of
the CNT having an elliptical cross-section generated in Example
16.
[0113] (FIG. 51) A SEM photograph of the carbon nanohorn-stacked
CNF generated in Example 17. A number of fibrous products grown in
the form of connection of triangular pyramid are observed.
[0114] (FIG. 52) A SEM photograph of a graphene-laminated CNF
generated in Example 17, which indicates that a number of graphene
sheets are laminated to be grown in the form of fiber.
[0115] (FIG. 53) A SEM photograph of a cup-stacked type CNF and a
screw type CNF generated in Example 17.
[0116] (FIG. 54) A SEM photograph of radially grown CNT and a
graphene-laminated CNF generated in Example 18.
[0117] (FIG. 55) A SEM photograph of higher magnification of the
graphene-laminated CNF shown in FIG. 54.
[0118] (FIG. 56) A SEM photograph of the CNT generated in Example
19.
[0119] (FIG. 57) A higher magnification SEM photograph of FIG.
56.
[0120] (FIG. 58) A higher magnification SEM photograph of the CNT
generated in Example 19.
[0121] (FIG. 59) A TEM photograph of the CNT generated in Example
19.
[0122] (FIG. 60) A fluorescent X-ray map of Co of generated CNT
portion, and white points indicate presence of Co.
[0123] (FIG. 61) A fluorescent X-ray peak of the end portion of CNT
generated in Example 19, in which Co is detected.
[0124] (FIG. 62) A TEM photograph of the CNT generated in Example
19, which indicates that the thickness of the tube is about 24 nm
and the inner diameter thereof is about 145 nm.
[0125] (FIG. 63) A TEM photograph showing that graphene layers are
laminated in the thickness direction of the CNT of FIG. 62 (lattice
fringe image).
[0126] (FIG. 64) A TEM photograph of the CNT obtained in Example
23, which indicates that the thickness of the tube is about 14 nm
and the inner diameter thereof is about 14 nm.
[0127] (FIG. 65) A SEM photograph of the sample obtained in Example
22.
[0128] (FIG. 66) A SEM photograph of the CNT obtained in Example
23.
[0129] (FIG. 67) A higher magnification SEM photograph of FIG.
66.
[0130] (FIG. 68) A TEM photograph of the CNT obtained in Example
23.
[0131] (FIG. 69) A TEM photograph of the CNT obtained in Example
23. It can be considered that the circle inside the CNT is
fullerene, which indicates that the CNT is a fullerene-incorporated
CNT.
[0132] (FIG. 70) A SEM photograph of a large amount of CNT
generated in Example 25.
[0133] (FIG. 71) A SEM photograph of a cup-stacked type CNF and a
screw type CNF generated in Example 25.
[0134] (FIG. 72) An enlarged photograph of FIG. 71.
[0135] (FIG. 73) An X-ray diffraction pattern of a sample after the
treatment in Example 25. A strong peak around 26.5.degree. showing
a graphite structure is observed.
[0136] (FIG. 74) A SEM photograph of a surface of a sample after
the treatment in Example 26.
[0137] (FIG. 75) An enlarged photograph of a cluster portion of
FIG. 74.
[0138] (FIG. 76) A SEM photograph of the CNT obtained in Example
16.
[0139] (FIG. 77) A fluorescent X-ray peak of the CNT portion of
FIG. 76.
[0140] (FIG. 78) A cross-sectional view of a structure of a
graphite crucible relating to one embodiment of the present
invention, in which all of the top, bottom and side of the
pre-baked starting material 3 are covered with spacers and a
sleeve.
[0141] (FIG. 79) A laser Raman spectrum of a graphite portion
vapor-phase-grown in the starting particle in the vapor-phase-grown
graphite structure obtained in Example 1. It is indicated that
graphite crystallinity is very high.
[0142] (FIG. 80) An electron microscope photograph of high
magnification (300000.times.) of FIG. 22. The total length of a
scale is 100 nm.
[0143] (FIG. 81) An electron microscope photograph of high
magnification (800000.times.) of FIG. 80. The total length of a
scale is 50.0 nm.
EMBODIMENT FOR CARRYING OUT THE INVENTION
[0144] Since carbon generated in a vapor phase plays a role of a
binder, an obtained material is connected uniformly even to minute
portions of carbonated and graphitized filler, thereby making it
possible to obtain carbon materials and graphite materials of
various shapes such as a mass, a block, a cylinder, a polygonal rod
and a plate.
[0145] In heat treatment under isotropic gas pressure, a
temperature can be elevated at a rate of several hundreds degrees
per hour, and therefore, a material can be taken out within 24
hours including a cooling time. Accordingly, the production period
can be shortened to a great extent while two to three months have
been required for the production so far. FIG. 2 shows a comparison
between the production process of conventional artificial graphite
with the production process of the present invention. FIG. 3 shows
a comparison of a period of time required for production of the
conventional artificial graphite with a period of time required for
production of the present invention. While in conventional methods,
carbonization and graphitization proceed in a liquid or solid
phase, vapor-phase-grown graphite is generated in a vapor phase in
the present invention, and therefore, graphite material can be
produced in a remarkably small number of production steps within a
significantly short period of time.
[0146] A material having a desired anisotropy, open pore ratio,
degree of growth of graphite crystal structure, mechanical strength
and physical properties is produced by adjusting a shape and size
of a starting material to be used, or adjusting a particle size
distribution in the case of particles, and properly controlling
pre-baking conditions, isotropic pressure and heating
conditions.
[0147] Vapor-phase-grown carbon and composite materials of graphite
and various carbon materials, for example, carbon fiber-reinforced
carbon materials (CC composite) and graphite/carbon composite
materials are produced by subjecting a pre-baked filler to mixing
or laminating with various carbon materials such as a carbon fiber,
a natural graphite, an artificial graphite, a graphite fiber, an
expanded graphite, a glassy carbon or an amorphous carbon as an
additive, charging the filler in a graphite crucible in the same
manner as mentioned above and conducting heat treatment under
isotropic gas pressure. The above-mentioned various carbon
materials can be used alone or in combination of two or more
thereof.
[0148] For the heat treatment under isotropic gas pressure, hot
isotropic pressing equipment (HIP equipment) can be used suitably.
In the case of producing large size graphite materials such as
electrodes for steel making and graphite for nuclear reactor,
desired large size graphite materials are produced using a large
size equipment having an inner diameter of 800 mm and a height of
2100 mm or an inner diameter of 800 mm and a height of 3700 mm by
charging the pre-baked starting material in a graphite crucible and
conducting about 24-hour treatment.
[0149] In the case of producing electrode materials for primary
batteries and secondary batteries such as lithium ion batteries,
capacitors and fuel cells, a porous graphite block adjusted to a
proper open pore ratio and pore size distribution by the
above-mentioned method is cut into a sheet of 50 to 1000 .mu.m by
electric discharge machining, or water jetting, or with a
multi-wire saw, thereby enabling a slurry preparation step and a
coating step to be eliminated.
[0150] In the case where a graphite material to be used for a
slurry preparation step and a coating step is needed similarly to a
conventional method, a starting material, pre-baking conditions, a
method for charging into a crucible and hot isostatic pressing
treatment conditions are properly adjusted to decrease a degree of
connection of vapor-phase-grown graphite to the pre-baked filler,
and the obtained treated product is crushed or pulverized to be
used for the above-mentioned steps.
[0151] In order to produce a carbon nanotube, a carbon nanofiber,
fullerene, a carbon nanohorn or the like as a simple substance or a
composite material with a pre-baked filler, vapor-phase-grown
carbon and graphite, a pre-baked filler are mixed with a metal
component, silicon or the like by various methods, and pre-baking
conditions, a method for charging into a crucible and hot isostatic
pressing treatment conditions are properly adjusted.
[0152] In the case of producing a high purity material, polymer
resin materials such as PAN, a phenol resin, a furan resin and a
polyimide resin are used as a starting material. This is because
residues obtained by refining of petroleum and coal such as pitches
and cokes contain a lot of impurities such as metals.
[0153] When producing graphite sheets to be used on packings of
automobile engine and insulating materials for high temperature
applications, high density graphite materials (including materials
in a sheet-like form) in which carbon hexagonal planes are
laminated in the plane direction can be produced by applying force
(compressing) on a vapor-phase-grown graphite structure by rolling
or cold press in a thickness direction of the structure.
[0154] Hydrocarbons and polymer materials in the form of particle,
powder or short fiber which can be carbonized at high yield after
the heat treatment are used as a starting material. Specific
examples thereof which can be suitably used are petroleum pitch,
coal pitch, asphalt, PVC pitch, tetrabenzophenazine pitch,
naphthalene pitch, anthracene pitch, petroleum mesophase pitch,
polyacrylonitrile, rayon, phenol resin, furan resin, cellulose
resin and the like.
[0155] The starting material is heat-treated in inert gas
atmosphere for pre-baking. Conditions such as a pre-baking
temperature and a temperature elevating rate are properly set
depending on a shape, density, strength and porosity of a targeted
material. If the pre-baking conditions are insufficient, a large
amount of gases such as moisture is generated in the following hot
isostatic pressing treatment, and thereby, connection of the
materials by vapor phase growth becomes insufficient. If the
pre-baking temperature is too high and carbonization of the
material proceeds excessively, generation of hydrogen and
hydrocarbon which are starting materials for production of
vapor-phase-grown graphite becomes insufficient, and a material
having sufficient strength cannot be obtained. FIG. 5 shows a
photograph of an appearance of one example of the starting material
in the form of fine powder after the pre-baking.
[0156] The starting powdery and/or particulate material after the
pre-baking is charged in a graphite crucible which are previously
processed to a desired shape of material to be produced. The
graphite crucible is one configured to have a screw type cap on the
top thereof, and after charging of the starting material, the
crucible is sealed by tightening the screw type cap. High density
isotropic graphite materials and artificial graphite materials can
be used as a material of the graphite crucible, and thereby,
purity, bulk density, closed-pore-ratio and pore size distribution
are suitably adjusted.
[0157] The function of the graphite crucible for precipitating
vapor-phase-grown graphite at the hot isostatic pressing treatment
is to generate vapor-phase-grown graphite while maintaining the
shape of the crucible, holding the inside of the crucible at an
isotropic gas pressure being equal to the outside pressure by
permeating a medium gas such as argon through the wall of the
crucible with a proper pore size and keeping hydrogen and
hydrocarbon generated from the starting material inside the
crucible without scattering outside the crucible. When the crucible
material and structure are too air-tight, the crucible is broken
due to a difference in pressure between the inside and the outside
of the crucible, and the starting material scatters inside the
equipment. In the case where the crucible material and structure
have too high permeability, hydrogen and hydrocarbon generated from
the starting material are scattered inside the pressure vessel of
the hot isostatic pressing equipment, and vapor-phase-grown
graphite cannot be generated.
[0158] The graphite crucible charged with the starting material is
set inside the hot isostatic pressing equipment, and isostatic
pressing and heating treatment is carried out using inert gas such
as argon gas. In this case, it is necessary to increase the inside
pressure to a given value until the temperature rise to a
pre-baking temperature of the starting material and apply enough
pressure in a temperature range higher than the pre-baking
temperature. In the temperature range higher than the pre-baking
temperature, hydrogen and hydrocarbon gas to be used as starting
materials for vapor-phase-grown graphite are generated, and
therefore, if the inside pressure is not sufficient, these gases
scatter outside the crucible and sufficient vapor phase growth does
not arise. FIG. 6 is a photograph showing appearances of a
screw-capped sealable graphite crucible and an obtained
vapor-phase-grown graphite structure.
[0159] A temperature elevating rate in the temperature range higher
than the pre-baking temperature is also important. When the
temperature elevating rate is too low, amounts of hydrogen and
hydrocarbon generated per hour is small, and hydrogen and
hydrocarbon do not reach the concentrations necessary for
generation of vapor-phase-grown graphite, resulting in scattering
of an increased proportion thereof outside the crucible.
[0160] When a phenol resin, a furan resin or the like is used as a
starting material, vapor-phase-grown graphite is precipitated at a
pre-baking temperature within the range from 350.degree. C. to
1100.degree. C., and a structure sufficiently exhibiting a function
of vapor-phase-grown graphite as a binder can be obtained at a
pre-baking temperature within the range from 500.degree. C. to
900.degree. C. at 0.5% by weight of remaining hydrogen amount in
the starting material. When a starting material in the spherical
and/or elliptical form is used, vapor-phase-grown graphite A having
a fine structure is generated around the starting material particle
in the spherical and/or elliptical form, and vapor-phase-grown
graphite B is generated also inside the particle in the spherical
and/or elliptical form to give a structure combined with the outer
surface (shell) C of the particle in the spherical and/or
elliptical form. FIG. 7 is an electron microscope photograph of a
vapor-phase-grown graphite structure and shows the bodies A, B and
C. Here, the spherical form represents a solid body having a form
like a sphere and the elliptical form represents a solid body
having a form like an ellipse, and the both include solid bodies
having a nearly spherical or elliptical shape and in addition,
solid bodies having a shape somewhat deviated from a spherical or
elliptical shape as far as they can form the three-layer structure
comprising the above bodies A, B and C according to the present
invention. Also, "the starting material in the spherical and/or
elliptical form" means any of one comprising a starting material in
the spherical form alone, one comprising a starting material in the
elliptical form alone, or a mixture of a starting material in the
spherical form and a starting material in the elliptical form.
[0161] A powder, particle, piece, long fiber or short fiber of the
pre-baked starting material is charged in a graphite crucible and
vapor-phase-grown graphite is grown using the crucible as a
reaction vessel. Inner dimensions (shape) of the crucible is set in
consideration of a shrinkage of the starting material depending on
a shape, density, porosity, pore size distribution of a material to
be produced and conditions for preparing the starting material to
be used. The crucible is configured to have a top screw cap or top
and bottom screw caps in order to seal the crucible after charging
of the starting material, thereby preventing scattering of the
starting material in the following heating and pressing steps and
controlling an equilibrium between hydrogen and hydrocarbon to be
used as a starting material for vapor phase growth and a compressed
medium gas by open pores in the crucible material.
[0162] FIG. 40 is a cross-sectional view of the structure of the
top screw-capped graphite crucible. The inner wall 2a at the top of
the crucible body 2 and the outer circumference 1a of the crucible
cap are threaded by specified tap processing, and thereby the
crucible can be sealed by turning the cap to the thread after
charging of the pre-baked starting material 3. In addition, the
pre-baked starting material 3 can be subjected to HIP treatment by
covering the whole (or a part) of the top and/or bottom thereof
with spacers made of a carbon material for the purposes of
preventing scattering of gas for vapor phase growth reaction and
increasing the gas concentration, thereby enhancing a reaction
efficient. Further, the pre-baked starting material 3 can be
subjected to HIP treatment by covering the whole (or a part) of the
side thereof with a sleeve made of a carbon material for the same
purposes as mentioned above. FIG. 78 shows the pre-baked starting
material being in a state of the top and bottom thereof being
covered with the spacers 4 and the side thereof being covered with
the sleeve 5. When the top of the pre-baked starting material is
covered with the spacer, the spacer functions as a weight, and
helps uniform shrinkage of the carbon material that proceeds as
graphite is generated, and is useful to avoid cracking and crazing
of the generated carbon material. Examples of the carbon material
for the spacer and the sleeve are graphite, glassy carbon,
diamond-like carbon, amorphous carbon and the like, and one of them
can be used alone or two or more thereof can be used together.
Among these, a spacer or sleeve made of graphite is preferred. In
the present invention, the spacer is one covering the pre-baked
starting material mainly at the top or bottom thereof and the
sleeve is one covering the pre-baked starting material mainly at
the side thereof. However, there is a case where discrimination of
the both does not make sense, depending on the shape of the
vessel.
[0163] With respect to the material of the crucible, it is
preferable to use artificial graphite or isotropic graphite
material having a bulk density of 1.6 to 1.9, an open pore ratio of
less than 20%, a pore size of less than 3 .mu.m and a thermal
conductivity of not less than 50 W/(mK).
[0164] In the hot isostatic pressing treatment, heating is carried
out at a temperature elevating rate of 20.degree. C. or more per
hour, desirably 100.degree. C. or more per hour. The maximum
ultimate temperature during the heating is set to be 1000.degree.
C. or more, desirably 1400.degree. C. or more. In a temperature
range not less than the pre-baking temperature of the starting
material, the pressure during the pressing is set to be 10 MPa or
more, desirably 50 MPa or more. Upper limits of the maximum
ultimate temperature and the maximum ultimate pressure are not
limited particularly, and when using the hot isostatic pressing
equipment, usually these upper limits are determined accordingly
depending on performance of the equipment. These upper limits are
obvious for a person skilled in the art, and the upper limit of the
maximum ultimate temperature is usually about 3000.degree. C. The
upper limit of the maximum ultimate pressure is usually about 200
MPa, and especially in the case of high performance equipment, it
is about 300 MPa.
[0165] In the above-mentioned first aspect of the present
invention, the pre-baking temperature varies with various
conditions such as kind of a filler to be used and the maximum
ultimate temperature at the hot isostatic pressing treatment, and
usually is preferably within a range from about 350.degree. C. to
about 1100.degree. C., more preferably within a range from about
500.degree. C. to about 900.degree. C. The amount of remaining
hydrogen can fluctuate depending on the size of the filler to be
used, and usually is preferably within a range from about 0.05% by
weight to about 10% by weight, more preferably within a range from
about 0.5% by weight to about 5% by weight.
[0166] In the first aspect of the present invention, since
vapor-phase-grown graphite having high graphite crystallinity is
mainly generated, the carbon material obtained by sufficiently
conducting the reaction mainly comprises vapor-phase-grown graphite
having high graphite crystallinity as component element. Therefore,
such carbon material can substantially be called a graphite
material. In such a carbon material, in the case of generating the
above-mentioned porous carbon material comprising the bodies A, B
and C, the maximum ultimate temperature at the hot isostatic
pressing treatment is adjusted to be within a range preferably from
about 1000.degree. C. to about 3000.degree. C., more preferably
from about 1400.degree. C. to about 2500.degree. C. In this case, a
bulk density of the generated carbon material is within a range
preferably from 0.4 to 1.5, more preferably from 0.6 to 1.2. An
open pore ratio thereof is within a range preferably from 20% to
80%, more preferably from 30% to 70%.
[0167] The explanation on the second aspect of the present
invention mentioned infra can be applied to the explanation on the
first aspect of the present invention as far as there is no
inconsistency between the both explanations. For example, in
addition to a graphite crucible, a closable vessel made of a heat
resistant material can be used as a closable vessel to be used for
charging the filler therein as explained in the second aspect of
the present invention. Also, the fillers explained in the second
aspect of the present invention can be used similarly. The purports
such that the filler is preferably powdery and/or particulate
material and "the filler pre-baked to an extent of containing
remaining hydrogen" includes a filler which has not been pre-baked
and previously contains hydrogen in such a proper amount as to be
reserved by the pre-baked filler are also applied to the first
aspect of the present invention as explained in the second aspect
of the present invention.
[0168] Next, the second aspect of the present invention, namely,
the production method of the present invention for selectively and
efficiently generating nanocarbon materials is explained below.
According to the present invention, nanocarbon materials can be
produced selectively by using, as a starting material, the filler
which is a solid organic material having high carbon density and
causing CVD reaction highly efficiently without sublimation of
carbon. For example, a filler is carbonized under proper pre-baking
conditions to prepare a pre-baked filler in a state of hydrogen
remaining therein and then the pre-baked filler is allowed to carry
a catalyst thereon or a filler previously allowed to carry a
catalyst thereon is pre-baked. Then, the pre-baked filler is
charged in a closed vessel made of a heat-resistant material and
used as a reaction vessel, and is subjected to heating and pressing
treatment with hot isostatic pressing equipment (HIP) by using a
compressed atmosphere such as argon.
[0169] In the present invention, the catalyst is carried directly
on the filler as a solid starting material. Therefore, for example,
by dissolving a catalyst such as metallic chloride or
organometallic compound in a solvent for ionization and bringing
the ionized catalyst into contact with the filler, it is possible
to allow the filler to carry a catalyst having an extremely fine
size and shape. Also, it is thought that the presence of such a
catalyst allows selective and efficient generation of the
nanocarbon materials by carrying out HIP treatment at relatively
low temperature while avoiding high temperature range where
graphite (laminated graphene layers) is easily precipitated by CVD
reaction.
[0170] It can be considered that scattering of hydrocarbon,
hydrogen and carbon monoxide (CO) generated from the pre-baked
starting material by the heat treatment is regulated with a highly
compressed medium such as argon gas, resulting in formation of a
concentration distribution thereof around the pre-baked starting
material. It is considered that when the heating temperature
exceeds the pre-baking temperature and becomes sufficiently high,
these gases are thermally excited and the CVD reaction proceeds in
a three-dimensional area in the reaction vessel, thus generating
nanocarbon materials such as vapor-phase-grown CNT, CNF,
fullerenes, graphenes and carbon nanohorns on the catalyst carried
on the filler and functioning as a reaction starting point. Various
nanocarbon materials can be generated selectively by regulating
factors such as kind of the filler as a starting material, a
temperature for pre-baking the filler, an amount of remaining
hydrogen contained in the pre-baked filler, kind, amount and size
of a catalyst to be carried on the filler, a maximum ultimate
temperature, a maximum ultimate pressure, a heating and pressing
speed and a heating and pressing pattern at the HIP treatment and a
material of a graphite vessel and a sealing method thereof.
[0171] Examples of the heat resistant materials constituting the
reaction vessel are graphite and in addition, ceramics such as
alumina, magnesia and zirconia, and metals such as iron, nickel,
zirconium and platinum. Among these, graphite is preferred. With
respect to the graphite vessel, the same one as explained above can
be used. Namely, the graphite vessel functions as a reaction vessel
for causing the CVD reaction with hydrogen, carbon monoxide and
hydrocarbon gases generated from the pre-baked starting material
during the HIP treatment. Since it is necessary to cause a chemical
reaction without scattering the generated reaction gas outside the
vessel while keeping isotropic high pressure by a gas pressure, the
material of the vessel and the sealing structure thereof are
properly selected. If the material is too dense, a difference in
pressure between the inside and the outside of the vessel arises,
which results in an explosive breakdown of the vessel. On the other
hand, if the material is too porous, the reaction gas generated
inside the vessel is easily scattered outside the vessel and
efficiency of the chemical reaction is lowered to a large
extent.
[0172] The material and structure of the vessel are properly
selected in consideration of necessity of taking a HIP-treated
product out of the vessel, sealing the vessel as easily as possible
in view of facilitating charging of the starting material before
the HIP treatment, and maintaining strength of the vessel at high
temperature so as to be capable of withstanding the inside pressure
caused by generation of the reaction gas from the pre-baked
starting material, and also in consideration of exposure to high
temperature during the HIP treatment.
[0173] The graphite vessel is made using artificial graphite
materials specifically prepared by extrusion molding, CIP molding,
squeeze molding, vibration molding or rammer molding, hard carbon
materials including glassy carbon and prepared mainly by molding a
thermosetting resin, carbon fiber-reinforced carbon materials or
composite materials thereof. The porosity of the graphite material
is important for efficiently causing the chemical reaction in the
crucible, and therefore, a material of which open pore ratio has
been controlled is used. In the case of a material having an open
pore ratio of 20% or more, the reaction gases are excessively
diffused outside the vessel, and therefore, a concentration of the
gases necessary for generating the graphite cannot be kept. Example
of a suitable graphite vessel is a graphite crucible.
[0174] A screw-capped graphite crucible can be used so that
charging of the pre-baked starting material in the vessel and
discharging of the product after the HIP treatment can be carried
out efficiently. (FIG. 40)
[0175] The filler to be used in the present invention is a solid
organic material having a relatively high density. In such a
filler, as the increase in a molecular weight proceeds by heating,
oxygen, nitrogen and hydrogen atoms in the filler structure become
instable and are discharged, and thereby, carbonization proceeds.
In the present invention, the (pre-baked) filler of which
carbonization is stopped in a state of carbon, hydrogen and oxygen
remaining in the filler is used as a pre-baked starting
material.
[0176] Examples of usable filler are natural organic polymers such
as starch, cellulose, protein, collagen, alginic acid, dammar,
kovar, rosin, gutta-percha and natural rubber; semisynthetic
polymers such as cellulose resin, cellulose acetate, cellulose
nitrate, cellulose acetate butyrate, casein plastic and soybean
protein plastic; and synthetic polymers such as thermosetting reins
such as phenol resin, urea resin, melamine resin, benzoguanamine
resin, epoxy resin, diallyl phthalate resin, unsaturated polyester
resin, bisphenol A type epoxy resin, Novolac type epoxy resin,
polyfunctional epoxy resin, alicyclic epoxy resin, alkyd resin and
urethane resin, thermoplastic resins such as vinyl chloride resin,
polyethylene, polypropylene and polystyrene, synthetic rubbers such
as polyisoprene and butadiene, synthetic fibers such as nylon,
vinylon, acrylic fiber and rayon, and other materials such as
polyvinyl acetate, ABS resin, AS resin, acrylic resin, polyacetal,
polyimide, polycarbonate, modified polyphenylene ether (PPE),
polyethylene terephthalate, polybutylene terephthalate,
polyalylate, polysulfone, polyphenylene sulfide, polyether ether
ketone, fluorine-containing resin, polyamide imide, benzene,
naphthalene and anthracene.
[0177] It is a matter of course that petroleum pitch, coal pitch,
petroleum coke, coal coke, carbon black and active carbon which are
generated when fossil fuels such as petroleum and coal, for
example, being refinined can be used as a starting material. In
addition, toward the establishment of resources-recycling society,
introduction of carbonization system has been advanced from the
viewpoint of effective utilization of carbon in wastes, and waste
plastics which are mixtures of the above-mentioned various resins,
waste wood, waste plants and food wastes such as garbage can also
be used as a starting material. Among these, thermosetting resins
such as phenol resin are preferred from the viewpoint of a large
amount of remaining carbon after heat treatment, waste plastics and
waste carbides are preferred from the viewpoint of production cost
and from environment point of view by an effect of reducing CO2,
and carbon black is preferred from the viewpoint of production of
carbon materials of fine size.
[0178] The filler to be used in the present invention is preferably
a powdery and/or particulate material. In the powdery and/or
particulate material of the present invention, a size and shape of
the component units thereof are not limited, and the powdery and/or
particulate material incorporates a powder comprising relatively
fine component units or particles comprising relatively coarse
component units of aggregate. The shape of these component units
includes various ones such as particle, small piece, long fiber and
short fiber.
[0179] The fillers to be used in the present invention can include
those which contain beforehand hydrogen corresponding to the
remaining hydrogen in an amount being proper for the use in the
present invention even without pre-baking. When the filler contains
beforehand a proper amount of hydrogen, pre-baking is not required,
and the filler can be used as it is as "the filler pre-baked to an
extent of containing remaining hydrogen" in the present invention.
Namely, in the present invention, "the filler pre-baked to an
extent of containing remaining hydrogen" includes one not subjected
to pre-baking and reserving a proper amount of hydrogen which
should be reserved in a filler after pre-baking. Examples of such a
filler are petroleum coke, coal coke, carbon black and the
like.
[0180] In the present invention, the fillers can be used alone or
can be used in a mixture of two or more thereof.
[0181] The catalyst to be used in the present invention is one of
factors for controlling kind, amount, shape, size (diameter, number
of laminated graphene layers, length and the like) and the like of
the nanocarbon materials to be generated. Examples of usable
catalysts are (1) metals such as tungsten, rhenium, osmium,
tantalum, molybdenum, niobium, iridium, ruthenium, hafnium,
technetium, rhodium, vanadium, chromium, zirconium, platinum,
thorium, lutetium, titanium, palladium, protactinium, thulium,
scandium, iron, yttrium, erbium, cobalt, holmium, nickel,
dysprosium, terbium, curium, gadolinium, beryllium, manganese,
americium, promethium, uranium, copper, samarium, gold, actinium,
neodymium, berkelium, silver, germanium, praseodymium, lanthanum,
californium, calcium, europium, ytterbium, cerium, strontium,
barium, radium, aluminum, magnesium, plutonium, neptunium,
antimony, zinc, lead, cadmium, thallium, bismuth, polonium, tin,
lithium, indium, sodium, potassium, rubidium, gallium, and cesium,
and in addition, elements such as silicon and tellurium, (2)
sulfide, boride, oxide, chloride, hydroxide, nitride and
organometallic compound of any one of the (1) above, and (3) a
mixture of any of the (1) and (2) above and sulfur and/or sulfide
(including an organosulfur compound) and a mixture of any of the
(1) and (2) above and boron and/or boride (including an organoboron
compound). Among these, preferred are tungsten, tantalum,
molybdenum, niobium, iridium, vanadium, chromium, zirconium,
titanium, iron, cobalt, nickel, manganese, copper, samarium,
neodymium, silver, praseodymium, lanthanum, calcium, strontium,
barium, aluminum, magnesium, zinc, lead, cadmium, bismuth, tin,
lithium, indium, sodium, potassium, rubidium, gallium, cesium and
silicon, (2) oxide, chloride, hydroxide, nitride and organometallic
compound of any one of the (1) above, and (3) a mixture of any of
the (1) and (2) above and sulfur and/or sulfide (including an
organosulfur compound) and a mixture of any of the (1) and (2)
above and boron and/or boride (including an organoboron compound).
These can be used alone or can be used in a mixture of two or more
thereof.
[0182] In the present invention, an extremely small amount of the
catalyst suffices, and usually when the amount is not less than
1000 ppm, preferably not less than 2000 ppm, the present invention
can be executed suitably. A further preferred amount of the
catalyst is not less than 10000 ppm, more preferably not less than
100000 ppm.
[0183] Since the catalysts become a starting point of the CVD
reaction for generating nanocarbon materials, it is desirable to
allow the catalysts to be carried on the pre-baked starting
material in a state of being dispersed as uniformly as possible. In
addition, the finer the size of the catalysts is, the finer
nanocarbon materials can be generated.
[0184] Example of a method for allowing the catalysts to be carried
on the pre-baked starting material is to mix the pre-baked starting
material with the catalysts prepared in a fine form.
[0185] In addition, there is exemplified a method for pouring a
filler before pre-baked or a filler after pre-baked (pre-baked
filler) in catalysts in a fused form or in a solution and then
dispersing the filler therein substantially uniformly and carrying
out a drying step or the like. For example, in the case of using
the filler before pre-baked, a water or alcohol solution of a
chloride of cobalt, nickel, iron or the like is prepared, and the
filler is dissolved in this solution, followed by polymerization,
drying, heat treatment and pulverization steps, thus enabling the
catalysts to be finely carried on the filler nearly uniformly. The
filler carrying the catalysts can be subjected to pre-baking.
[0186] In the case of using the pre-baked starting material, metal,
for example, vanadium, chromium, titanium, iron, cobalt, nickel,
manganese, copper, calcium, aluminum or magnesium is allowed to be
carried directly on the material by a spattering, spraying,
electroplating or electroless plating method or catalysts are
allowed to be carried on the pre-baked starting material by
preparing a solution by dissolving a chloride or organometallic
compound of the metal mentioned above in a solvent such as alcohol
and then pouring the pre-baked starting material in the solution,
followed by stirring, adsorption, precipitation, filtration, drying
and heat treatment steps.
Further, the catalysts can also be allowed to be carried on the
pre-baked starting material by mixing a transition metal hydroxide
with the pre-baked starting material. The transition metal
hydroxide can be obtained by dissolving a transition metal alkoxide
or a transition metal complex in alcohol to synthesize an alcohol
solution of metal complex, hydrolyzing the solution and then
filtering off the obtained precipitated product. When synthesizing
a transition metal hydroxide through hydrolysis by using a
transition metal alkoxide or a transition metal complex as a
starting material, further fine particles can be obtained. It can
be considered that fine particles of a transition metal hydroxide
are reduced during the HIP treatment to form a metal, and when the
transition metal hydroxide as a starting material is in the form of
finer particles, the metal generated by the reduction also become
finer particles, thereby enabling the generated CNT to be
controlled to have a smaller size. A method for allowing a
transition metal to be carried on a surface of the pre-baked
starting material by pouring the pre-baked starting material in an
ionic solution of a transition metal or a solution of a transition
metal complex is also an effective method. An ionic solution of a
transition metal can be prepared by dissolving a chloride of a
transition metal and/or a transition metal alkoxide in water,
alcohol or a mixture of water and alcohol, and a solution of a
transition metal complex can be prepared by dissolving a transition
metal complex such as a transition metal acetylacetonate in water,
alcohol or a mixture of water and alcohol. In this case, a
transition metal is adsorbed in the pre-baked filler as a single
metal ion or a metal complex ion, and by drying this filler, the
transition metal can be carried as a catalyst on the filler. The
catalyst thus allowed to be carried on the filler can function as a
fine starting point for the reaction.
[0187] The filler carrying the catalyst is pre-baked at a specified
temperature elevating rate in a nitrogen gas stream or in an inert
atmosphere. For the pre-baking, an electric heating or gas heating
type externally heating batch oven, continuous multi-tubular oven,
internal heating rotary kiln, rocking oven or the like is used.
[0188] In the present invention, the kind and amount of gases for
causing a reaction for vapor phase growth during the HIP treatment
can be controlled by the pre-baking temperature or the amount of
remaining hydrogen in the pre-baked starting material. Namely, in a
fixed amount of a certain filler, the kind, concentration and total
amount of gases (hydrogen, hydrocarbon, carbon monoxide, steam and
the like) to be generated during the HIP treatment naturally become
constant as far as the pre-baking temperature is constant. Also,
each amount of the generated hydrogen, hydrocarbon, carbon
monoxide, steam and the like has a correlation with the amount of
remaining hydrogen. Accordingly, the degree of pre-baking can be
properly adjusted by using the pre-baking temperature or the amount
of remaining hydrogen as an index.
[0189] The pre-baking temperature can vary depending on various
conditions such as the kind of the filler to be used and the
maximum ultimate temperature at the HIP treatment, and usually is
preferably not less than 400.degree. C., desirably within a range
from about 500.degree. C. to about 1000.degree. C.
[0190] The preferred range of the amount of remaining hydrogen
varies depending on the size of the filler to be used, and is
usually within a range from about 500 ppm to about 60000 ppm,
preferably from about 2500 ppm to about 40000 ppm.
[0191] In the case of selectively generating CNT, it is preferable
that the pre-baking temperature is within a range from about
500.degree. C. to about 700.degree. C. and the amount of remaining
hydrogen is within a range from about 20000 ppm to about 40000 ppm.
In the case of using the filler having a size of about 1 .mu.m or
less (for example, carbon black having a size of about 1 .mu.m or
less), the range from about 500 ppm to about 20000 ppm is
preferred.
[0192] In the present invention, by subjecting the pre-baked
starting material to HIP treatment, gases such as hydrogen,
hydrocarbon and carbon monoxide are generated and the CVD reaction
proceeds inside the reaction vessel. These gases can be generated
at the temperature range from about 400.degree. C. to about
1500.degree. C. depending on kind of the starting material by
controlling the pre-baking temperature and the HIP treating
conditions. Accordingly, it is possible to generate at a time
various kinds of nanocarbon materials in the temperature range for
generating these gases by mixing a plurality of metal catalysts
having different melting points.
[0193] In the present invention, the catalyst and the maximum
ultimate temperature at the HIP treatment are important factors. In
the case of selectively generating graphite, it is possible to
obtain vapor-phase-grown graphite having a bulky form, a flower
shape or the like by carrying out the HIP treatment in a relatively
high temperature range where graphite grows, without using a
catalyst. However, since graphite is generated by stacking of
graphenes which are carbon hexagonal planes, it can be considered
that when a catalyst is present within the temperature range for
generating graphite, various carbon nanofibers such as a
graphene-stacked type where graphenes are stacked in parallel with
each other, a carbon nanohorn-stacked type where carbon nanohorn
are stacked, a cup-stacked type where component units of a cup
shape are stacked, and a screw type where a carbon nanofiber is
grown and warped like a screw, are generated. When a catalyst is
present at a temperature of a relatively low HIP treating
temperature range where graphite cannot be generated selectively,
various carbon nanotubes and cup-stacked CNF can be obtained.
[0194] As mentioned above, by allowing the catalyst to be carried
on the pre-baked filler, various nanocarbon materials such as
carbon nanofibers and carbon nanotubes can be generated selectively
by using the HIP treating temperature as a control factor.
[0195] The maximum ultimate temperature range at the HIP treatment
for selectively generating the respective nanocarbon materials can
vary depending on various conditions such as the kind and amount of
the catalyst and the maximum ultimate pressure at the HIP
treatment, and is, for example, from about 850.degree. C. to about
1300.degree. C. in the case of carbon nanotubes and from about
850.degree. C. to about 1800.degree. C. in the case of carbon
nanofibers.
[0196] The maximum ultimate pressure at the HIP treatment is, for
example, within a range from 1 MPa to 200 MPa, preferably within a
range from 10 MPa to 200 MPa.
[0197] The explanations on the first aspect of the present
invention can be applied to the second aspect of the present
invention unless they are inconsistent with the explanations on the
second aspect of the present invention.
[0198] Herein, the nanocarbon materials are carbon materials having
a structure with a size of about 0.5 nm to about 5000 nm
(preferably about 3000 nm) or comprising component units with a
size of about 0.5 nm to about 5000 nm (preferably about 3000 nm),
and include any of carbon nanotubes (CNT), carbon nanofibers (CNF),
fullerenes, graphenes and carbon nanohorns (CNH). CNT is, for
example, one having an outer diameter within a range from about 0.5
nm to about 5000 nm (preferably about 3000 nm), preferably within a
range from about 1 nm to about 1000 nm, further preferably within a
range from about 1 nm to about 500 nm, still further preferably
within a range from about 10 nm to about 300 nm. CNT includes one
having a small ratio of a thickness to the outer diameter, for
example, preferably a ratio of less than 20%. CNF is, for example,
one having a diameter within a range from about 0.5 nm to about
5000 nm, preferably within a range from about 100 nm to about 3000
nm, further preferably within a range from about 200 nm to about
2000 nm. CNF includes a graphene-laminated CNF where graphene
sheets are linearly laminated, a screw type CNF where graphene
sheets are spirally laminated, a cup-stacked type CNF where
component units having a cup shape are laminated, and a carbon
nanohorn-stacked CNF where CNH are laminated. The thickness of
graphene sheets and CNH as component units constituting these CNF
is about 0.5 nm or more and less than about 10 nm. The nanocarbon
material is also called carbon type nanomaterial.
[0199] Herein, the amount of hydrogen is one measured in accordance
with general rules on a method for determining an amount of
hydrogen of a metallic material (JIS Z 2614: 1990. The analysis
method is in accordance with an inert gas heating method for
"steel". Specifically a sample is heated up to 2000.degree. C. in
an argon gas atmosphere, and an integrated quantity of hydrogen is
measured by gas chromatography). The amount of hydrogen is
represented by % by weight or parts per million (ppm) by a
weight.
[0200] The open pore ratio (apparent porosity) is a volumetric
ratio of cavities (open) which are present in the volume of a
material calculated from its outer dimensions and into which
cavities liquid and gas can invade. Generally materials having a
high open pore ratio have continuous pores and gas permeability.
Herein, an open pore ratio is obtained from the following
equation.
Open pore ratio (%)=((Apparent specific gravity)-Bulk specific
gravity)/Apparent specific gravity).times.100
Apparent specific gravity: A value measured with a densimeter
AccuPyc 1330-PCW available from Shimadzu Corporation by a helium
gas-substituted picnometer method, using a sample which has not
been pulverized Bulk specific gravity: A value obtained by dividing
a sample weight by a volume calculated from the outer dimensions of
the sample
[0201] The true density is a density of a target object measured
with the object being pulverized into a fine powder in order to
minimize an influence of cavities contained therein, and in
Examples of the present invention, the true density is measured
using a powder sample having passed a 74 .mu.m filter.
[0202] The bulk density is a synonym of a bulk specific gravity,
and the apparent density is a synonym of an apparent specific
gravity.
[0203] The present invention is then explained by means of
Examples, but is not limited to the following Examples.
Example 1
[0204] Phenol formaldehyde resin powder having an average particle
size of 20 .mu.m was pre-baked at 750.degree. C. in an inert gas
atmosphere. The amount of hydrogen contained in the starting
material after the pre-baking was 0.8% by weight. The pre-baked
starting material powder was charged in a graphite crucible and a
screw type top cover was closed to seal the crucible. FIG. 8 is an
electron microscope photograph of the starting material after the
pre-baking, and at this stage, the starting material exhibits forms
of thermosetting resin and hard carbon (hardly graphitizable
carbon).
[0205] As a material for the graphite crucible, isotropic graphite
having a bulk density of 1.85, an open pore ratio of 8%, a porosity
of 2 .mu.m, a heat conductivity of 140 W/(mK) and inner dimensions
of .phi.50.times.100 mm was used. After the sealing, the graphite
crucible was charged in hot isostatic pressing equipment, and then
the inside temperature and pressure were increased to reach
700.degree. C. and 70 MPa, respectively in one hour using argon
gas, followed by heating and pressing up to a maximum ultimate
temperature of 2000.degree. C. and a maximum ultimate pressure of
200 MPa, respectively at a temperature elevating rate of
500.degree. C. per hour, holding the temperature and pressure for
one hour and then decreasing the temperature to room temperature
and lowering the pressure. A required period of time between
charging to and discharging from the graphite crucible was 22
hours. The top cover of the graphite crucible was opened and the
material inside the crucible was discharged, and thus, a molded
article of .phi.46.times.90 mm was obtained. While the starting
material before the pre-baking was a fine powder when charged in
the crucible, the material changed its form to one structure having
sufficient strength due to generation of vapor-phase-grown graphite
as shown in FIG. 9. The bulk density of the obtained
vapor-phase-grown graphite structure was 1.1, and the open pore
ratio and total ash content thereof were 43% and 0.005% by weight,
respectively.
[0206] In FE-SEM photograph showing the broken surface of the
obtained structure, it was confirmed that the vapor-phase-grown
graphite A having a fine structure was generated around the
spherical starting material particles and that the
vapor-phase-grown graphite B was generated inside the spherical
particle to form a structure being integrated with the outer
surface (being in the form of shell) of the spherical particle.
FIG. 10 is an electron microscope photograph showing the surface of
the obtained structure.
[0207] FIGS. 11 and 12 are electron microscope photographs of high
magnification showing the portion of the vapor-phase-grown graphite
A, in which vapor-phase-grown graphite of various nano-structures
such as a flat nano-structure similar to graphene, a special fiber
structure having a length of several tens micrometers formed by
lamination of flat layers, and structures in the form, like needle
and pencil, similar to carbon nanotubes were observed.
[0208] As shown in an electron microscope photograph of FIG. 19, a
lot of vapor-phase-grown graphites of novel structures (for
example, a structure having a tip in the form of polygonal cone and
a structure having a cavity at a center of cross-section) having a
polygonal cross-section such as octagonal or decagonal
cross-section of a micron size and grown in a longitudinal
direction were generated.
[0209] As shown in electron microscope photographs of FIGS. 20, 21,
22, 80 and 81, the vapor-phase-grown graphite generated inside the
filler has a novel structure, in which graphite spheres of about 10
nm and highly ordered fullerene structures are overlapped with each
other and there are cavities of several tens of nanometers. More
specifically, the diameter of the graphite spheres is from about 1
nm to about 50 nm, and the diameter of the cavities is from about 1
nm to about 50 nm.
[0210] (FIG. 13) Laser Raman spectra of vapor-phase-grown graphites
A and B are shown in FIGS. 13 and 79, respectively. In FIG. 13, R
value represented by I1360/I1580 (I.sub.D/I.sub.G), which is a peak
intensity ratio of a peak around 1580 cm.sup.-1 that reflects
lamination structure to a peak around 1360 cm.sup.-1 that reflects
turbostratic structure, according to spectrum of carbon hexagonal
planes by laser Raman spectroscopy, is 0.085, and in FIG. 79, R
value is 0.084, and the both R values are extremely low, which
indicates that the graphite structure is one having high
crystallinity of graphite. Raman spectrum of the outer surface
(shell) C of the spherical phenol resin which is a thermosetting
resin and a hardly graphitizable resin is shown in FIG. 14, and R
value is 1.200 which is close to a value of high hardness glassy
carbon.
[0211] A bamboo spatula was lightly pressed and slid on the surface
of the obtained vapor-phase-grown graphite structure, resulting in
occurrence of a mark in graphite color. An electron microscope
photograph of the mark in graphite color is shown in FIG. 5, which
indicates that by pressing the vapor-phase-grown graphite with the
spatula, the carbon hexagonal planes changed its forms while
sliding in parallel with the plane surface.
Example 2
[0212] Phenol formaldehyde resin powder having an average particle
size of 20 .mu.m was pre-baked at 750.degree. C. in an inert gas
atmosphere. The pre-baked starting material powder was charged in a
graphite crucible and a screw type top cover was closed to seal the
crucible. As a material for the graphite crucible, isotropic
graphite having a bulk density of 1.85, an open pore ratio of 8%, a
porosity of 2 .mu.m, a heat conductivity of 140 W/(mK) and inner
dimensions of .phi.50.times.100 mm was used. After the sealing, the
graphite crucible was heated up to 700.degree. C. in one hour in
argon gas stream, followed by heating up to a maximum ultimate
temperature of 2000.degree. C. at a temperature elevating rate of
500.degree. C. per hour, holding that temperature for one hour and
then decreasing the temperature to room temperature. A required
period of time between charging to and discharging from the
graphite crucible was 22 hours. The top cover of the graphite
crucible was opened and the material inside the crucible was
discharged. While the pre-baked starting material was a fine powder
when charged in the crucible, the material remained in a state of
fine powder, and the vapor-phase-grown graphite structure could not
be obtained.
Example 3
[0213] Phenol formaldehyde resin powder having an average particle
size of 20 .mu.m was subjected to baking for carbonization at
1200.degree. C. in an inert gas atmosphere. The amount of hydrogen
contained in the starting material after the baking was 0.05% by
weight. The baked starting material powder was charged in a
graphite crucible and a screw type top cover was closed to seal the
crucible. After the sealing, the graphite crucible was charged in
hot isostatic pressing equipment, and then the inside temperature
and pressure were increased to reach 700.degree. C. and 70 MPa,
respectively in one hour using argon gas, followed by heating and
pressing up to a maximum ultimate temperature of 2100.degree. C.
and a maximum ultimate pressure of 200 MPa, respectively at a
temperature elevating rate of 500.degree. C. per hour, holding the
temperature and pressure for one hour and then decreasing the
temperature to room temperature and lowering the pressure. The top
cover of the graphite crucible was opened and the material inside
the crucible was discharged. While the starting material was a fine
powder when charged in the crucible, the material remained in a
state of fine powder, and the vapor-phase-grown graphite structure
could not be obtained.
Example 4
[0214] Phenol formaldehyde resin powder having an average particle
size of 20 .mu.m was pre-baked at 750.degree. C. in an inert gas
atmosphere. The pre-baked starting material powder was charged in a
graphite crucible, and the graphite crucible was charged in hot
isostatic pressing equipment without closing a top cover, and then
the inside temperature and pressure were increased to reach
700.degree. C. and 70 MPa, respectively in one hour using argon
gas, followed by heating and pressing up to a maximum ultimate
temperature of 2100.degree. C. and a maximum ultimate pressure of
200 MPa, respectively at a temperature elevating rate of
500.degree. C. per hour, holding the temperature and pressure for
one hour and then decreasing the temperature to room temperature
and lowering the pressure. While the starting material before the
pre-baking was a fine powder when charged in the crucible,
vapor-phase-grown graphite was slightly generated around the
pre-baked starting material and a structure having sufficient
strength could not be obtained.
Example 5
[0215] Phenol formaldehyde resin powder having an average particle
size of 20 .mu.m was pre-baked at 750.degree. C. in an inert gas
atmosphere. The pre-baked starting material powder was charged in a
graphite crucible and a screw type top cover was closed to seal the
crucible. As a material for the graphite crucible, isotropic
graphite having a bulk density of 1.85, an open pore ratio of 8%, a
porosity of 2 .mu.m, a heat conductivity of 140 W/(mK) and inner
dimensions of .phi.50.times.100 mm was used. A spacer having the
same material quality as that of the .phi.50.times.100 mm crucible
was used as a weight on the top of the starting material powder.
After the sealing, the graphite crucible was charged in hot
isostatic pressing equipment, and then the inside temperature and
pressure were increased to reach 700.degree. C. and 70 MPa,
respectively in one hour using argon gas, followed by heating and
pressing up to a maximum ultimate temperature of 2100.degree. C.
and a maximum ultimate pressure of 200 MPa, respectively at a
temperature elevating rate of 500.degree. C. per hour, holding the
temperature and pressure for one hour and then decreasing the
temperature to room temperature and lowering the pressure. The top
cover of the graphite crucible was opened and the material inside
the crucible was discharged, and thus, a molded article of
.phi.46.times.50 mm was obtained. While the starting material
before the pre-baking was a fine powder when charged in the
crucible, the material changed to one structure having sufficient
strength. The bulk density of the obtained vapor-phase-grown
graphite structure was 1.4, and the open pore ratio and total ash
content thereof were 33% and 0.005% by weight, respectively.
Example 6
[0216] Phenol formaldehyde resin powder having an average particle
size of 20 .mu.m was pre-baked at 750.degree. C. in an inert gas
atmosphere. A starting material prepared by adding 10% by weight of
3 mm long carbon fibers to the pre-baked powder was charged in a
graphite crucible and a screw type top cover was closed to seal the
crucible. After the sealing, the graphite crucible was charged in
hot isostatic pressing equipment, and then the inside temperature
and pressure were increased to reach 700.degree. C. and 70 MPa,
respectively in one hour using argon gas, followed by heating and
pressing up to a maximum ultimate temperature of 2100.degree. C.
and a maximum ultimate pressure of 200 MPa, respectively at a
temperature elevating rate of 500.degree. C. per hour, holding the
temperature and pressure for one hour and then decreasing the
temperature to room temperature and lowering the pressure. The top
cover of the graphite crucible was opened and the material inside
the crucible was discharged, and thus, an integrated composite
material of .phi.46.times.70 mm comprising carbon fibers,
vapor-phase-grown graphite and carbide of the starting material
powder was obtained.
Example 7
[0217] Phenol formaldehyde resin powder having an average particle
size of 20 .mu.m was pre-baked at 750.degree. C. in an inert gas
atmosphere. A starting material prepared by adding 10% by weight of
natural graphite powder having a particle size of 30 .mu.m and 10%
by weight of artificial graphite powder having a particle size of
20 .mu.m to the pre-baked powder was charged in a graphite crucible
and a screw type top cover was closed to seal the crucible. After
the sealing, the graphite crucible was charged in hot isostatic
pressing equipment, and then the inside temperature and pressure
were increased to reach 700.degree. C. and 70 MPa, respectively in
one hour using argon gas, followed by heating and pressing up to a
maximum ultimate temperature of 2100.degree. C. and a maximum
ultimate pressure of 200 MPa, respectively at a temperature
elevating rate of 500.degree. C. per hour, holding the temperature
and pressure for one hour and then decreasing the temperature to
room temperature and lowering the pressure. The top cover of the
graphite crucible was opened and the material inside the crucible
was discharged, and thus, an integrated composite material of
.phi.46.times.60 mm comprising carbon fibers, vapor-phase-grown
graphite and carbide of the starting material powder was
obtained.
Example 8
[0218] Phenol formaldehyde resin powder having an average particle
size of 20 .mu.m was pre-baked at 750.degree. C. in an inert gas
atmosphere. The pre-baked starting material powder was charged in a
graphite crucible and a screw type top cover was closed to seal the
crucible. After the sealing, the graphite crucible was charged in
hot isostatic pressing equipment, and then the inside temperature
and pressure were increased to reach 700.degree. C. and 70 MPa,
respectively in one hour using nitrogen gas, followed by heating
and pressing up to a maximum ultimate temperature of 2000.degree.
C. and a maximum ultimate pressure of 200 MPa, respectively at a
temperature elevating rate of 500.degree. C. per hour, holding the
temperature and pressure for one hour and then decreasing the
temperature to room temperature and lowering the pressure. The top
cover of the graphite crucible was opened and the material inside
the crucible was discharged, and thus, a molded article of
.phi.46.times.90 mm was obtained. The starting material changed to
one structure having sufficient strength. The bulk density of the
obtained vapor-phase-grown graphite structure was 1.0, and the open
pore ratio and total ash content thereof were 50% and 0.005% by
weight, respectively. The obtained structure showed a fluorescent
X-ray peak indicating residual of nitrogen used as a pressing
medium.
Example 9
[0219] The vapor-phase-grown graphite structure obtained in Example
1 was charged in a metal die and subjected to cold pressing at a
load of 200 kgf to obtain a cubic molded article of 20 mm.times.20
mm.times.20 mm. The bulk density of the obtained molded article was
2.0.
Example 10
[0220] Phenol formaldehyde resin powder having an average particle
size of 20 .mu.m was pre-baked at a maximum ultimate temperature of
900.degree. C. in an inert gas atmosphere. The amount of hydrogen
remaining in the starting material after the pre-baking was
measured in accordance with general rules on a method for
determining an amount of hydrogen of a metallic material (JIS Z
2614: 1990), and the measured amount was 5000 ppm. Each of the
starting materials pre-baked at each temperature was charged in a
screw type graphite crucible made of a material having a bulk
density of 1.80 and an open pore ratio of 10%, and a screw type top
cover was turned to tighten the screw and seal the crucible. After
the sealing, the graphite crucible was charged in hot isostatic
pressing equipment, and then the inside temperature and pressure
were increased to reach 700.degree. C. and 70 MPa, respectively in
one hour using argon gas, followed by heating and pressing up to a
maximum ultimate temperature of 2500.degree. C. and a maximum
ultimate pressure of 190 MPa, respectively at a temperature
elevating rate of 500.degree. C. per hour, holding the temperature
and pressure for one hour and then decreasing the temperature to
room temperature and lowering the pressure. A required period of
time between charging to and discharging from the graphite crucible
was 8 to 12 hours. The bulk density of the treated sample was 1.15
g/cm.sup.3, its apparent density was 1.68 g/cm.sup.3, and its true
density was 1.73 g/cm.sup.3. Measurement of the density was carried
out by a helium gas-substituted picnometer method with a densimeter
AccuPyc 1330-PCW available from Shimadzu Corporation, and the true
density was measured with the sample being pulverized into fine
powder. The inside of the treated sample contained a lot of remains
which seem to have resulted from etching by excited hydrogen of
various vapor-phase-grown graphites as generated in Example 1.
Particularly on the top of the sample were observed graphite fibers
grown in the form of fiber from the vapor-phase-grown graphite, and
on the inner wall of the used graphite crucible were observed
rod-like continuous graphite grown on the peripheries of elements
other than carbon. (FIG. 23 to FIG. 32) A fluorescent X-ray peak
indicating presence of elements such as Si, Ca, Fe and Ba was
obtained from the tip of the rod-like continuous graphite. (FIG.
33)
Example 11
[0221] Phenol formaldehyde resin powder having an average particle
size of 20 .mu.m was pre-baked at a maximum ultimate temperature of
900.degree. C. in an inert gas atmosphere. The amount of hydrogen
remaining in the starting material after the pre-baking was
measured in accordance with general rules on a method for
determining an amount of hydrogen of a metallic material (JIS Z
2614: 1990), and the measured amount was 5000 ppm. A mixture of 2
parts by weight of the pre-baked starting material and 1 part by
weight of artificial graphite powder having an average particle
size of 5 .mu.m was charged in a screw type graphite crucible made
of a material having a bulk density of 1.80 and an open pore ratio
of 10%, and a screw type top cover was turned to tighten the screw
and seal the crucible. After the sealing, the graphite crucible was
charged in hot isostatic pressing equipment, and then the inside
temperature and pressure were increased to reach 700.degree. C. and
70 MPa, respectively in one hour using argon gas, followed by
heating and pressing up to a maximum ultimate temperature of
1800.degree. C. and a maximum ultimate pressure of 190 MPa,
respectively at a temperature elevating rate of 500.degree. C. per
hour, holding the temperature and pressure for one hour and then
decreasing the temperature to room temperature and lowering the
pressure. The bulk density of the treated sample was 0.4
g/cm.sup.3, its apparent density was 2.11 g/cm.sup.3, and its true
density was 2.16 g/cm.sup.3. Measurement of the density was carried
out by a helium gas-substituted picnometer method with a densimeter
AccuPyc 1330-PCW available from Shimadzu Corporation, and the true
density was measured with the sample being pulverized into fine
powder. Vapor-phase-grown graphite fibers having a diameter of
several micrometers and a length of from several tens micrometers
to several millimeters had been generated on the treated sample. In
these vapor-phase-grown graphite fibers, a fiber formed by
connection of a linear one and triangular pyramid one which seems
to be carbon nanohorn was observed. (FIG. 34 to FIG. 36)
Example 12
[0222] Phenol formaldehyde resin powder having an average particle
size of 20 .mu.m was pre-baked at a maximum ultimate temperature of
900.degree. C. in an inert gas atmosphere. The amount of hydrogen
remaining in the starting material after the pre-baking was
measured in accordance with general rules on a method for
determining an amount of hydrogen of a metallic material (JIS Z
2614: 1990), and the measured amount was 5000 ppm. A mixture of 2
parts by weight of the pre-baked starting material and 1 part by
weight of mesophase spherical graphite powder having an average
particle size of 25 .mu.m was charged in a screw type graphite
crucible made of a material having a bulk density of 1.80 and an
open pore ratio of 10%, and a screw type top cover was turned to
tighten the screw and seal the crucible. After the sealing, the
graphite crucible was charged in hot isostatic pressing equipment,
and then the inside temperature and pressure were increased to
reach 700.degree. C. and 70 MPa, respectively in one hour using
argon gas, followed by heating and pressing up to a maximum
ultimate temperature of 1800.degree. C. and a maximum ultimate
pressure of 190 MPa, respectively at a temperature elevating rate
of 500.degree. C. per hour, holding the temperature and pressure
for one hour and then decreasing the temperature to room
temperature and lowering the pressure. The bulk density of the
treated sample was 1.12 g/cm.sup.3, its apparent density was 2.01
g/cm.sup.3, and its true density was 2.06 g/cm.sup.3. Measurement
of the density was carried out by a helium gas-substituted
picnometer method with a densimeter AccuPyc 1330-PCW available from
Shimadzu Corporation, and the true density was measured with the
sample being pulverized into fine powder. Vapor-phase-grown
graphite fibers having a diameter of several micrometers and a
length of from several tens micrometers to several millimeters had
been generated in the treated sample. In these vapor-phase-grown
graphite fibers, a fiber formed by connection of a linear one and
triangular pyramid one which seems to be carbon nanohorn was
observed. (FIG. 37 to FIG. 39)
Example 13
[0223] Spherical phenol resin was pre-baked at a maximum ultimate
temperature of 900.degree. C. in a nitrogen gas stream. The amount
of hydrogen remaining in the starting material after the pre-baking
was measured in accordance with general rules on a method for
determining an amount of hydrogen of a metallic material (JIS Z
2614: 1990), and the measured amount was 3500 ppm. The pre-baked
starting material was poured into a platinum crucible and was
subjected to ashing in an electric oven. The sample formed into
ashes was added to an alkali mixture solvent to be dissolved,
followed by extraction with hydrochloric acid and then elemental
analysis with an inductively coupled plasma spectrometry (ICPS)
analyzer ICPS-8000 (available from Shimadzu Corporation). As a
result of the analysis, the amounts of Fe, Si and Zn contained in
the pre-baked starting material were 500 ppm, 200 ppm and 120 ppm,
respectively. This pre-baked starting material was charged in a
screw type (FIG. 40) graphite crucible, and a screw type top cover
was turned to tighten the screw and seal the crucible. The graphite
crucible was charged in hot isostatic pressing equipment, and then
the inside temperature was increased to 2000.degree. C. at a
temperature elevating rate of 1000.degree. C. per hour while
carrying out isostatic pressing at 190 MPa using argon gas. CNT
having an outer diameter of about 10 nm to about 50 nm and being
excellent in linearity was generated slightly on the treated
product. (FIGS. 41 and 42)
[0224] The generated products were CNT being in a process of
forming into MWCNT, in which a second layer and a third layer of
carbon hexagonal planes were stacked on the surface of the single
CNT (FIG. 43), vapor-phase-grown graphites formed by stacking of
carbon hexagonal planes flatly (FIG. 41), and carbon materials
having a novel pencil-like structure formed by stacking of carbon
hexagonal planes around CNT so that the cross-section was in a
polygonal shape and the tube became a center of the material (FIGS.
44, 45 and 46). It can be considered that these were generated in
the HIP treatment in such a manner that growth of CNT occurred in a
lengthwise direction in a low temperature range, growth of carbon
such as graphene occurred on the surface of the CNT in a diameter
direction as the temperature became higher, and at a temperature of
1500.degree. C. or more, growth in a diameter direction was
accelerated.
[0225] In the pencil-like carbon material, its portion
corresponding to a lead had an outer diameter of from about 0.5
.mu.m to about 2 .mu.m and a length of from about 2 .mu.m to about
20 .mu.m, its center was a hollow of CNT, and its cross-sectional
structure was polygonal. The pencil-like carbon material was one
having extremely high crystallinity, in which carbon hexagonal
planes were oriented in an axial direction of the tube in the same
manner as in CNT.
Example 14
[0226] Spherical phenol resin was pre-baked at a maximum ultimate
temperature of 900.degree. C. in a nitrogen gas stream. The amount
of hydrogen remaining in the starting material after the pre-baking
was measured in accordance with general rules on a method for
determining an amount of hydrogen of a metallic material (JIS Z
2614: 1990), and the measured amount was 3000 ppm. The amounts of
Fe, Si and Zn contained in the pre-baked starting material were
measured by the same method as in Example 13, and the amounts of
Fe, Si and Zn were 500 ppm, 200 ppm and 150 ppm, respectively. This
pre-baked starting material was charged in a screw type (FIG. 40)
graphite crucible, and a screw type top cover was turned to tighten
the screw and seal the crucible. The sealed graphite crucible
containing the pre-baked starting material was charged in HIP
equipment, and then the inside temperature was increased to
1500.degree. C. at a temperature elevating rate of 500.degree. C.
per hour while carrying out isostatic pressing at 190 MPa using
argon gas. CNT having an outer diameter of about 10 nm to about 50
nm and being excellent in linearity was generated slightly on the
treated product.
[0227] On the surface of the slightly generated single CNT were
stacked a second layer and a third layer of carbon hexagonal
planes, and this CNT was one being in a process of forming into
MWCNT, and a pencil-like carbon material as observed in Example 13
was not observed. In addition, a lot of flaky stacked graphite was
generated. (FIG. 47)
Example 15
[0228] Spherical phenol resin was pre-baked at a maximum ultimate
temperature of 900.degree. C. in a nitrogen gas stream. The amounts
of Fe, Si and Zn contained in the pre-baked starting material were
measured by the same method as in Example 13, and the amounts of
Fe, Si and Zn were 500 ppm, 200 ppm and 120 ppm, respectively. This
pre-baked starting material was charged in a screw type (FIG. 40)
graphite crucible, and a screw type top cover was turned to tighten
the screw and seal the crucible. The sealed graphite crucible
containing the pre-baked starting material was charged in HIP
equipment, and then the inside temperature was increased to
1200.degree. C. at a temperature elevating rate of 500.degree. C.
per hour while carrying out isostatic pressing at 190 MPa using
argon gas. A large diameter hose-like CNT having a thickness of
from about 10 nm to about 20 nm, an outer diameter of from about
100 nm to about 200 nm and a length of from about 10 .mu.m to about
20 .mu.m was generated slightly on the treated product.
Example 16
[0229] Spherical phenol resin was pre-baked at a maximum ultimate
temperature of 900.degree. C. in a nitrogen gas stream. One part by
weight of metallic silicon powder was mixed to four parts by weight
of the pre-baked starting material, and after pulverizing and
mixing the mixture in an agate mortar, the powder of the starting
material was charged in a screw type graphite crucible, and a screw
type top cover was turned to tighten the screw and seal the
crucible. The sealed graphite crucible containing the pre-baked
starting material was charged in HIP equipment, and then the inside
temperature was increased to 1200.degree. C. at a temperature
elevating rate of 500.degree. C. per hour while carrying out
isostatic pressing at 190 MPa using argon gas. A lot of large
diameter hose-like CNT having a thickness of from about 10 nm to
about 20 nm, an outer diameter of from about 100 nm to about 200 nm
and a length of from about 10 .mu.m to about 20 .mu.m were
generated on the treated product. The cross-section of the
hose-like CNT was circular, elliptical or polygonal, and was
featured by being thin and long for its diameter as compared with
conventional reported CNT. A ratio of the thickness to the outer
diameter was less than 5%. (FIGS. 48, 49 and 50)
Example 17
[0230] Spherical phenol resin was pre-baked at a maximum ultimate
temperature of 600.degree. C. in a nitrogen gas stream. The amount
of hydrogen remaining in the starting material after the pre-baking
was measured in accordance with general rules on a method for
determining an amount of hydrogen of a metallic material (JIS Z
2614: 1990), and the measured amount was 24000 ppm. To 1 mol of
cobalt acetylacetonate (Special Grade available from NACALAI
TESQUE, INC., hereinafter referred to as Co(AcAc)2) was mixed 10
liter of methoxyethanol (available from NACALAI TESQUE, INC.,
purity: 99%). In this case, since Co(AcAc)2 was solidified soon,
the mixture was sufficiently pulverized and stirred with a glass
rod or a stirrer. Thereafter, a specific amount, totally 100 ml of
distilled water was dividedly added dropwise to the mixture with a
syringe or a micropipet. The precipitate generated at the same time
as the addition was allowed to stand overnight, and the solution
containing the precipitate was subjected to filtration under
reduced pressure with an aspirator equipped with a diaphragm pump
to recover the precipitate only. The obtained precipitate was
air-dried in a draft for 24 hours. The cobalt precipitate and the
pre-baked material were dry-mixed to give a starting material to be
subjected to HIP treatment with a cobalt concentration of 5000 ppm
assuming that the total cobalt used initially had been precipitated
in the generated precipitate (cobalt precipitate). The mixture was
charged in a screw type graphite crucible, and a screw type top
cover was turned to tighten the screw and seal the crucible. The
sealed graphite crucible containing the starting material was
charged in HIP equipment, and then the inside temperature was
increased to 1450.degree. C. at a temperature elevating rate of
500.degree. C. per hour while carrying out isostatic pressing at
190 MPa using argon gas.
[0231] A lot of fibrous carbon was generated on the surfaces of the
treated sample. There were four kinds of products generated, that
is, carbon nanohorn-stacked carbon nanofibers (CNF) in the form of
bamboo having a diameter of from about 200 nm to about 1000 nm and
a length of from about 10 .mu.m to about several millimeters (FIG.
51), graphene-laminated CNF having a diameter of from about 200 nm
to about 1000 nm and a length of from about 10 .mu.m to about
several millimeters (FIG. 52), and cup-stacked type and screw type
CNF having a diameter of from about 500 nm to about 2000 nm and a
length of about several millimeters (FIG. 53). In any of the
products, many long fibers were generated on the surface portion of
the sample, and short fibers were generated around the spherical
phenol resin.
Example 18
[0232] Spherical phenol resin was pre-baked at a maximum ultimate
temperature of 600.degree. C. in a nitrogen gas stream. Cobalt
chloride hexahydrate was dissolved in ethanol to prepare a 0.6
mol/liter solution. Then, 120 g of the pre-baked phenol resin was
poured into 500 ml of this solution, followed by sufficiently
stirring with a stirrer. The residue after filtration of ethanol
was put in a ceramic vessel and heated at 400.degree. C. in the
atmosphere in an electric oven for five hours to prepare a
pre-baked starting material carrying a catalyst thereon. The
concentration of cobalt measured by fluorescent X-ray analysis
(SEM-EDX) was 3000 ppm. The pre-baked starting material carrying
the catalyst thereon was charged in a screw type graphite crucible,
and a screw type top cover was turned to tighten the screw and seal
the crucible. The sealed graphite crucible containing the starting
material was charged in HIP equipment, and then the inside
temperature was increased to 1400.degree. C. at a temperature
elevating rate of 300.degree. C. per hour while carrying out
isostatic pressing at 190 MPa using argon gas.
[0233] A lot of graphene-stacked CNF having a diameter of from
about 0.5 microns to about several microns were generated on the
treated sample. Also, CNT having a thin tip and an outer diameter
of about 100 nm was generated slightly around the spherical phenol
resin. (FIG. 54) The thickness of one layer of the graphene-stacked
CNF was about several nanometers. (FIG. 55)
Example 19
[0234] Spherical phenol resin was pre-baked at a maximum ultimate
temperature of 600.degree. C. in a nitrogen gas stream. Cobalt
precipitate was prepared by treating in the same manner as in
Example 17. The cobalt precipitate and the pre-baked starting
material were dry-mixed to give a starting material to be subjected
to HIP treatment with a cobalt concentration of 5000 ppm assuming
that the total cobalt used initially had been precipitated in the
cobalt precipitate. The mixture was charged in a screw type
graphite crucible, and a screw type top cover was turned to tighten
the screw and seal the crucible. The sealed graphite crucible
containing the starting material was charged in HIP equipment, and
then the inside temperature was increased to 1200.degree. C. at a
temperature elevating rate of 500.degree. C. per hour while
carrying out isostatic pressing at 190 MPa using argon gas.
[0235] A lot of CNT with a nearly circular cross-section having an
outer diameter of from about 100 nm to about 300 nm, a thickness of
from about 10 nm to about 30 nm and a length of from about 10 .mu.m
to about 10 mm were generated on the treated product. The CNT was
featured by having a thin thickness for its diameter as compared
with conventional reported CNT, and a ratio of the thickness to the
outer diameter was less than 20%. (FIGS. 56, 57, 58 and 59)
[0236] FIG. 60 shows a fluorescent X-ray map of generated CNT
portion, and it was confirmed that cobalt used as a catalyst was
present in a size of from about 100 nm to about 200 nm (in the form
of dots) and functioned as a starting point for generating CNT.
FIG. 61 shows a fluorescent X-ray peak of the tip portion of the
CNT.
[0237] FIG. 62 shows a TEM photograph of the obtained CNT, which
indicates the measured thickness of the tube wall and the measured
inner diameter thereof. The outer diameter was 193.5 nm, and the
thickness was from 24.3 to 24.4 nm, and the ratio of the thickness
to the outer diameter was about 13%. A lattice fringe image of a
TEM photograph showing that graphene layers are stacked in the
thickness direction of this CNT is shown in FIG. 63. The photograph
indicates an image comprising about 70 layers of laminated
graphene, and this CNT was confirmed to be a multi-layer CNT having
extremely good crystallinity.
[0238] Graphene layer is very good in electron conductivity, and
has a possibility for catalytic activity, selective reaction of
pharmaceuticals or the like utilizing the graphene surface, and
therefore, effective utilization thereof is expected. Further, in
the CNT as a one-dimensional space, a behavior being different from
conventional physical and chemical reactions is anticipated, and
therefore, interest is taken in its effective utilization. In the
case of general CNT, even if an outer diameter is increased for
easy utilization of the inside, it only leads to increase in the
number of graphene layers stacked and the inner diameter does not
change. For example, the CNT obtained in Example 23 has the same
sizes as that of conventional CNT. FIG. 64 shows a TEM photograph
of this CNT, and the outer diameter and the thickness determined
from the lattice fringe image were 42.9 nm and 14.3 to 14.4 nm,
respectively and the ratio of the thickness to the outer diameter
was about 33%. On the other hand, the inside space of the thin CNT
obtained in Examples 16, 19 and 21 is very wide and is suitably
used since gases and liquids are easily passed therethrough.
Example 20
[0239] Spherical phenol resin was pre-baked at a maximum ultimate
temperature of 600.degree. C. in a nitrogen gas stream. Iron
precipitate was obtained by treating in the same manner as in the
preparation of the cobalt precipitate in Example 17, using 1 mol of
iron acetylacetonate (Special Grade available from NACALAI TESQUE,
INC., hereinafter referred to as Fe(AcAc)2) and 10 liter of
methoxyethanol (available from NACALAI TESQUE, INC., purity: 99%).
The iron precipitate and the pre-baked starting material were
dry-mixed to give a starting material to be subjected to HIP
treatment with a iron concentration of 5000 ppm assuming that the
total iron used initially had been precipitated in the generated
iron precipitate. The mixture was charged in a screw type graphite
crucible, and a screw type top cover was turned to tighten the
screw and seal the crucible. The sealed graphite crucible
containing the starting material was charged in HIP equipment, and
then the inside temperature was increased to 1200.degree. C. at a
temperature elevating rate of 500.degree. C. per hour while
carrying out isostatic pressing at 190 MPa using argon gas.
[0240] A lot of carbon nanotubes having an outer diameter of about
100 nm, a length of from about 10 .mu.m to about 10 mm and a
thickness of from about 10 nm to about 20 nm were generated on the
treated products.
Example 21
[0241] Spherical phenol resin was pre-baked at a maximum ultimate
temperature of 600.degree. C. in a nitrogen gas stream. Nickel
precipitate was obtained by treating in the same manner as in the
preparation of the cobalt precipitate in Example 17, using 1 mol of
nickel acetylacetonate (Special Grade available from NACALAI
TESQUE, INC., hereinafter referred to as Ni(AcAc)2) and 10 liter of
methoxyethanol (available from NACALAI TESQUE, INC., purity: 99%).
The nickel precipitate and the pre-baked starting material were
dry-mixed to give a starting material to be subjected to HIP
treatment with a nickel concentration of 5000 ppm assuming that the
total nickel used initially had been precipitated in the generated
nickel precipitate. The mixture was charged in a screw type
graphite crucible, and a screw type top cover was turned to tighten
the screw and seal the crucible. The sealed graphite crucible
containing the starting material was charged in HIP equipment, and
then the inside temperature was increased to 1200.degree. C. at a
temperature elevating rate of 500.degree. C. per hour while
carrying out isostatic pressing at 190 MPa using argon gas.
[0242] A lot of carbon nanotubes having an outer diameter of about
100 nm and a length of from about 10 .mu.m to about 10 mm were
generated on the treated products.
Example 22
[0243] Spherical phenol resin was pre-baked at a maximum ultimate
temperature of 600.degree. C. in a nitrogen gas stream. Cobalt
precipitate was obtained by treating in the same manner as in
Example 17. The cobalt precipitate and the pre-baked starting
material were dry-mixed to give a starting material to be subjected
to HIP treatment with a cobalt concentration of 5000 ppm assuming
that the total cobalt used initially had been precipitated in the
generated cobalt precipitate. The mixture was charged in a screw
type graphite crucible, and a screw type top cover was turned to
tighten the screw and seal the crucible. The sealed graphite
crucible containing the starting material was charged in HIP
equipment, and then the inside temperature was increased to
800.degree. C. at a temperature elevating rate of 500.degree. C.
per hour while carrying out isostatic pressing at 190 MPa using
argon gas. An electron microscope photograph of the treated sample
is shown in FIG. 65, in which most of spherical phenol resins were
carbonized as they were, and vapor-phase-grown graphite was not
generated and several CNT were generated slightly around the
spheres.
Example 23
[0244] Spherical phenol resin was pre-baked at a maximum ultimate
temperature of 600.degree. C. in a nitrogen gas stream. Cobalt
precipitate was obtained by treating in the same manner as in
Example 17. The cobalt precipitate and the pre-baked starting
material were dry-mixed to give a starting material to be subjected
to HIP treatment with a cobalt concentration of 5000 ppm assuming
that the total cobalt used initially had been precipitated in the
generated cobalt precipitate. The mixture was charged in a screw
type graphite crucible, and a screw type top cover was turned to
tighten the screw and seal the crucible. The sealed graphite
crucible containing the starting material was charged in HIP
equipment, and then the inside temperature was increased to
1000.degree. C. at a temperature elevating rate of 500.degree. C.
per hour while carrying out isostatic pressing at 190 MPa using
argon gas.
[0245] A lot of CNT having an outer diameter of from about 10 nm to
about 30 nm were generated selectively in the treated sample, and
vapor-phase-grown graphite was not generated. FIGS. 66 and 67 show
electron microscope photographs of the generated CNT. FIG. 68 shows
the result of TEM observation of the obtained CNT. The lattice
fringe image showing that graphenes are stacked in the form of tube
was obtained. In addition, as shown in FIG. 69, a
fullerene-incorporated CNT, in which fullerene was inside the CNT,
was present.
Example 24
[0246] Bottles for beverage made of polyethylene terephthalate
resin (PET) were pulverized and pre-baked at a maximum ultimate
temperature of 600.degree. C. in a nitrogen gas stream. The amount
of hydrogen remaining in the starting material after the pre-baking
was measured in accordance with general rules on a method for
determining an amount of hydrogen of a metallic material (JIS Z
2614: 1990), and the measured amount was 32000 ppm. Cobalt
precipitate was obtained by treating in the same manner as in
Example 17. The cobalt precipitate and the pre-baked starting
material were dry-mixed to give a starting material to be subjected
to HIP treatment with a cobalt concentration of 5000 ppm assuming
that the total cobalt used initially had been precipitated in the
generated cobalt precipitate. The mixture was charged in a screw
type graphite crucible, and a screw type top cover was turned to
tighten the screw and seal the crucible. The sealed graphite
crucible containing the starting material was charged in HIP
equipment, and then the inside temperature was increased to
1000.degree. C. at a temperature elevating rate of 500.degree. C.
per hour while carrying out isostatic pressing at 190 MPa using
argon gas.
[0247] A lot of CNT having an outer diameter of from about 10 nm to
about 30 nm were generated selectively in the treated sample, and
vapor-phase-grown graphite was not generated.
Example 25
[0248] To 100 ml of methoxyethanol was added 4.95 g of cobalt
acetylacetonate (Co(AcAc)2), followed by stirring with a glass rod
or a stirrer to be completely dissolved. Then, to this solution was
added 10 g of pre-baked starting material measured previously
(pre-baked at 600.degree. C.) little by little, and after the total
amount had been added, stirring was carried out for another 30
minutes. The mixture after the stirring was allowed to stand
overnight, and then was subjected to filtration under reduced
pressure with an aspirator equipped with a diaphragm pump to
recover the solid content. The obtained solid content was air-dried
in a draft for 24 hours. This operation was repeated ten times, and
thereby, a cobalt-carrying starting material to be subjected to HIP
treatment and having a cobalt concentration of 5000 ppm was
prepared. The starting material carrying the catalyst thereon was
charged in a screw type graphite crucible, and a screw type top
cover was turned to tighten the screw and seal the crucible. The
sealed graphite crucible containing the starting material was
charged in HIP equipment, and then the inside temperature was
increased to 1000.degree. C. at a temperature elevating rate of
500.degree. C. per hour while carrying out isostatic pressing at 90
MPa using argon gas.
[0249] A lot of CNT having an outer diameter of several tens
nanometers and a length of from about several micrometers to about
several tens micrometers were generated on the surface of the
treated products. (FIG. 70)
[0250] On the other hand, a screw type CNF was selectively
generated inside the product, and a composite material of a
slightly generated CNT and a cup-stacked type and screw type CNF
was obtained. (FIGS. 71 and 72)
[0251] FIG. 73 shows an X-ray diffraction pattern of the sample,
and strong diffraction peak indicating 002, 004, 101 and 110 of
graphite were observed.
Example 26
[0252] The starting material carrying cobalt thereon, which was
prepared in the same manner as in Example 25, was charged in a
screw type graphite crucible, and a screw type top cover was turned
to tighten the screw and seal the crucible. The sealed graphite
crucible containing the starting material was charged in HIP
equipment, and then the inside temperature was increased to
900.degree. C. at a temperature elevating rate of 500.degree. C.
per hour while carrying out isostatic pressing at 190 MPa using
argon gas.
[0253] A lot of curled CNT in a state of being collected in the
form of cluster were generated in the treated sample. FIG. 74 is a
SEM photograph showing the surface of the sample, and white cloudy
ones are clusters. FIG. 75 is a SEM photograph showing enlarged
view of the clusters. A lot of curled CNT were generated, and
cup-stacked type and screw type carbon nanofibers are partially
contained. Yield of the curled CNT to the charged starting material
was 60%.
Study on Examples 13 to 26
[0254] Table 1 shows the main treating conditions and the state of
products in Examples 13 to 26. It is considered that when the
maximum ultimate temperature at the HIP treatment is high, graphite
is precipitated significantly by vapor phase growth, and therefore,
in order to selectively generate CNT, a proper maximum ultimate
temperature is within a range from about 850.degree. C. to
1300.degree. C. Further, with respect to the shape of CNT, when the
HIP treating temperature is 1000.degree. C., CNT having a diameter
of 10 nm level (about 10 nm or more and less than about 100 nm) are
mainly obtained, and when the HIP treating temperature is
1200.degree. C., CNT having a diameter of 100 nm level (about 100
nm or more and less than about 1000 nm) are mainly obtained.
[0255] In the case of the HIP treating temperature being
1000.degree. C., when the pressure was 190 MPa, CNT were
selectively generated, while when the pressure is 90 MPa, a lot of
CNT were generated on the surface portion of the treated sample and
in the whole sample, a lot of cup-stacked type and screw type CNF
were generated. These cup-stacked type and screw type CNF showed a
peak of graphite in X-ray diffraction, and therefore are considered
to have a graphite structure.
[0256] With respect to the pre-baking temperature, CNT have been
obtained efficiently in the case of pre-baking at 600.degree. C.
and containing remaining hydrogen in a large amount as compared
with the case of pre-baking at 900.degree. C. In addition, when the
pre-baking temperature was 600.degree. C., CNT were generated
efficiently irrespective of the kind of resins.
[0257] According to the fluorescent X-ray analysis of the generated
CNT and CNF, a peak being characteristic to argon was detected.
This indicates that argon used as a pressing medium at the HIP
treatment had been occluded in the material, and thus, it was
confirmed that the material has a characteristic of occluding
hydrogen. FIG. 76 shows an electron microscope photograph of the
CNT obtained in Example 16 and FIG. 77 shows the result of
fluorescent X-ray analysis of the CNT portion. In addition to the
carbon peak, the peaks of the catalyst Si and the occluded Ar were
confirmed.
TABLE-US-00001 TABLE 1 Metal HIP treating HIP treating Pre-baking
temp. component pressure temp. Example Starting filler .degree. C.
ppm MPa .degree. C. 13 Spherical phenol resin 900 Fe: 500 190 2000
Si: 200 Zn: 120 14 Spherical phenol resin 900 Fe: 500 190 1500 Si:
200 Zn: 150 15 Spherical phenol resin 900 Fe: 500 190 1200 Si: 200
Zn: 120 16 Spherical phenol resin 900 Si: 200000 190 1200 17
Spherical phenol resin 600 Co: 5000 190 1450 18 Spherical phenol
resin 600 Co: 3000 190 1400 Products Example CNT Graphite Others 13
generated slightly A large number of graphites Products having a
polygonal were generated around cross-section were generated
spherical phenol resin 14 generated slightly A large number of
graphites were generated around spherical phenol resin 15 generated
slightly generated slightly 16 CNT having a large diameter
generated slightly (100 nm) was generated 17 generated slightly CNF
of carbon nanohorn- stacked type, graphene- stacked type,
cup-stacked type and screw type were generated 18 generated
slightly CNF of graphene-stacked type and carbon nanohorn-stacked
type were generated Metal HIP treating HIP treating Pre-baking
temp. component pressure temp. Example Starting filler .degree. C.
ppm MPa .degree. C. 19 Spherical phenol resin 600 Co: 5000 190 1200
20 Spherical phenol resin 600 Fe: 5000 190 1200 21 Spherical phenol
resin 600 Ni: 5000 190 1200 22 Spherical phenol resin 600 Co: 5000
190 800 23 Spherical phenol resin 600 Co: 5000 190 1000 24 PET
resin 600 Co: 5000 190 1000 25 Spherical phenol resin 600 Co: 50000
90 1000 26 Spherical phenol resin 600 Co: 50000 190 900 Products
Example CNT Graphite Others 19 A lot of CNT having large generated
slightly diameter (100 nm) were generated 20 A lot of CNT having
large generated slightly diameter (100 nm) were generated 21 A lot
of CNT having large generated slightly diameter (100 nm) were
generated 22 generated slightly not generated 23 A lot of CNT (10
nm) not generated Fullerene-incorporated CNT were generated were
present 24 A lot of CNT (10 nm) not generated were generated 25 A
lot of CNT (10 nm) A lot of cup-stacked type and were generated
screw type CNF were on the surface generated in the sample 26 A lot
of curled CNT Cup-stacked type and screw (10 nm) were generated
type CNF were generated
INDUSTRIAL APPLICABILITY
[0258] The carbon materials can be suitably used for applications
relating to industrial fields making use of characteristics of
graphite materials such as 1) applications making use of friction
property, electrical property and mechanical property of graphite
such as bearing, sealing, graphite sheet, packing, blade, contact
strip for pantograph, mold, crucible and die, 2) electrical
applications such as electrode for steel making use, electrode for
refining of aluminum and brushing material, 3) electronics-related
applications such as heater, jig and vessel for furnaces for
growing silicon, silicon carbide and compound semiconductor, 4)
applications requiring graphite crystallinity, porosity and proper
pore size distribution such as diffuser panel and electrode for
fuel cell, electrode material for lithium ion battery and electrode
material for capacitor, and 5) nuclear energy-related applications
such as core materials for nuclear reactor and first wall material
for fusion reactor.
[0259] In particular, for a diffuser panel for fuel cell, an
electrode for capacitor, a negative electrode material for lithium
ion battery and the like in the fields of accumulator batteries, it
is demanded to prepare graphite materials having excellent graphite
crystallinity, high electric conductivity and a large porosity, in
which control of pore size distribution is easy and edge portions
of carbon hexagonal planes, where an intercalation reaction arises,
face toward the surface of the material. In the present invention,
the materials satisfying these requirements ideally can be
produced.
[0260] The materials can be suitably used for applications in
various industrial fields such as electronic devices, medical care
and living goods by making use of characteristics of carbon
hexagonal plane derivatives such as carbon nanofiber, carbon
nanotube, graphene and carbon nanohorn.
EXPLANATIONS OF SYMBOLS
[0261] 1 Crucible cover portion [0262] 1a Periphery of crucible
cover portion [0263] 2 Crucible body [0264] 2a Inner wall of top
portion of crucible body [0265] 3 Pre-baked starting material
[0266] 4 Spacer [0267] 5 Sleeve
* * * * *