JP2002154875A - Method for manufacturing supporting member for high temperature heating metal formed body - Google Patents

Abstract

PROBLEM TO BE SOLVED: To efficiently manufacture a homogeneous supporting member made of a non-graphite carbon material (e.g. a base board for a metal powder compacted body for powder metallurgy) suitable to support a high temperature heating metal formed body to be heated at a temperature as high as >=800 deg.C. SOLUTION: A fine carbon material which is hardly graphitized is coated with a thermosetting resin, then press formed and calcined to obtain a non- graphite carbon material having 0.9 to 1.5 g/ml apparent density and <0.5% ash content.

Description

DETAILED DESCRIPTION OF THE INVENTION

[0001]

BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a method for manufacturing a support member made of a non-graphitic carbon material used for supporting a metal molded body heated at a high temperature.

[0002] Jigs for metal shell rings in glass sealing for electronic parts (for example, JP-A-5-319929)
Alternatively, when sintering the metal powder molded body in a reducing or non-oxidizing atmosphere in powder metallurgy, an underlay plate (setter) for supporting the metal powder molded body (for example, see JP-A-8-1)
For example, a support member made of a carbon-based material having excellent lightness and thermal conductivity is used. The carbon-based support members of these high-temperature heated metal moldings include:
In addition to thermal shock resistance to withstand heating and cooling cycles to temperatures of 800 ° C. or higher, it is important not to cause carburizing phenomenon (transfer phenomenon by diffusion and infiltration of carbon into solid metal) into a high-temperature heated metal molded body. Required as a property. Such a requirement is that an iron (Fe) based metal (Fe alone or Fe and nickel (Ni), cobalt (Co), aluminum (Al), silicon (Si)
, Etc.) or alloys with other elements, etc.). Carbon (C) is important F
Although it is an alloying element with e, unexpected carburization causes a local deviation from the target composition in the metal product and should be avoided, and severe carburization occurs at the contact point between the metal product and the support member. It leads to seizure (that is, both wastes).

[0003] For example, when sintering a Fe-based metal powder molded body in a reducing atmosphere, carburization using a carbon underlay proceeds by the following mechanism.

[0004] That is, Fe constituting the Fe-based metal powder compact is partially an oxide, and is reduced by the reaction of the following formula (1) with hydrogen which gives a reducing atmosphere during sintering: Fe ₂ O ₃ + 3H ₂ → 2Fe + 3H ₂ O (1) The water vapor generated here reacts with C of the carbon underlay to produce a water gas by the reaction of the following formula (2): C + H ₂ O → CO + H _2.・ (2) This water gas is mixed with nitrogen in the atmosphere, and carbon-containing F
It has a composition similar to that of a weakly carburizing carrier gas used for gas carburizing for the production of an e-based alloy, and activated carbon (C) is generated on the surface of the Fe-based metal powder molded body and diffuses and permeates into the product. This reaction is represented by the following formulas (3) and (4). Here, the reaction to the right is a carburization reaction, and the reaction to the left is a decarburization reaction: 2CO⇔ [C] + CO ₂ (3) CO + H ₂ ⇔ [C] + H ₂ O (4) Further, the generated carbon dioxide reacts with C in the carbon underlay plate to generate carbon monoxide according to the following equation (5). The generated steam further progresses the equation (2) at C in the carbon underlay plate, so that the reaction proceeds continuously at the interface between the carbon underlay plate and the sintered metal body, and the activated carbon [C] in the product becomes Diffusion infiltration continues: CO ₂ + C → 2CO (5) As described above, when the gas carburizing action in the product continues, Fe ₃ C increases on the surface of the product, and the product quality is significantly reduced. Further, when Ni, Co, Al, or Si, which is a graphitization promoting element having a lower affinity for carbon than Fe, is contained, Fe ₃ C is destabilized to cause the precipitation of graphite, resulting in heat. The product may crack due to the difference in expansion rate.

[0005] Further, when the reactions of formulas (2) to (5) continue, the sintered metal body may be baked with the carbon underlay plate.

Some proposals have been made to prevent the carburizing phenomenon.

[0007] For example, Ti, Nb, V, Ta, W, Mo, Cr, M
The carburizing phenomenon can be prevented by forming a film of a carbide of these elements on the surface of the carbon underlay plate.
However, in order to form a metal carbide film as described above, not only an expensive treatment method such as a plasma spraying method is required, but also the thermal expansion coefficient between the formed film and the base carbon underlay plate. Due to the difference, the repetition of the heating-cooling cycle to a high temperature causes the peeling of the film.

[0008] In addition, several methods have been proposed for forming a ceramic layer on the surface of a carbon underlay plate to prevent carburization. For example, a method of forming a chromium oxide film by baking after applying chromic acid (JP-A-2-212385), a method of heat-pressing a sheet made mainly of ceramic powder (JP-A-8-198685), A method of plasma spraying yttrium oxide (Y ₂ O ₃ ) (Japanese Patent Laid-Open No. 2000-509102) and the like. However, none of these films can withstand repeated heating-cooling cycles to a high temperature due to the difference in the coefficient of thermal expansion from the base carbon plate, and only shows a limited life.

On the other hand, the main (2) in the above carburizing phenomenon
It is known that the reaction of the formula is promoted when the carbon material constituting the carbon underlay plate is graphite, and is suppressed in the chemically stable amorphous carbon material as compared with the graphite material. . Accordingly, it has been proposed to use a plate-like molded product of glassy carbon (amorphous carbon), which is a carbonized material using a thermosetting resin as a starting material (for example, produced by the method disclosed in JP-A-10-67559). It has also been proven effective in preventing carburization. However, this glassy carbon plate is obtained by injecting a thermosetting resin liquid between resin films, heating and curing the removed film, and further sandwiching it between graphite plates.
It is obtained by progressing carbonization very gradually in order to moderate the heat shrinkage accompanying carbonization. Therefore, it is inevitably expensive, and is susceptible to impact, may be damaged by thermal shock, and has limitations in size and shape even in the manufacturing process.

[0010]

SUMMARY OF THE INVENTION In view of the above-mentioned problems of the conventional materials, the present invention provides a homogeneous non-graphitic carbon which is suitably used for supporting a metal molded body heated to a high temperature of 800 ° C. or more. A main object is to provide an efficient method of manufacturing a support member made of a material.

[0011]

According to the study of the present inventors, in order to achieve the above-mentioned object, a molded article of a fine non-graphitizable carbon material coated with a thermosetting resin is fired. It has been found preferable to form a carbon material. More specifically, the method for producing a high-temperature heated metal molded body support member according to the present invention comprises the steps of coating a finely non-graphitizable carbon material with a thermosetting resin, press-molding the resultant, and firing the molded body. A non-graphitic carbon material having a density of 0.9 to 1.5 g / ml and an ash content of less than 0.5%.

In the present invention, the thermosetting resin which coats the finely graphitizable carbon material assists the pressure molding of the finely graphitizable carbon material, and itself becomes amorphous (non-graphitic) by firing.
It has the effect of providing a support member made of a non-graphitic carbon material that is carbonized into carbon and integrated with the finely non-graphitizable carbon material as a whole and is uniform as a whole.

[0013]

BEST MODE FOR CARRYING OUT THE INVENTION The fine graphitizable carbon material used in the present invention is a fibrous or granular (including spherical) fine material of a non-graphitizable carbon material. Average fiber diameter is 7-30 μm, number average fiber length is 0.09
It is preferably about 0.5 mm. The average particle size (mass average diameter) of the granular (including spherical) fine particles is 150 μm.
m to 2 mm are preferable, and especially 0.3 to 1 mm is preferable. The non-graphitizable property of a carbon material is determined by the fact that large carbon crystallite growth does not occur during carbonization at the graphitization temperature. Here, the carbon crystallite after carbonization at 2800 ° C. for 10 hours is used. A carbon material having a thickness (Lc002) of 300 ° or less, particularly 100 ° or less, is preferably used.

In the present invention, petroleum pitch is used as a precursor,
It is preferable to use the finely divided product which is made infusible in an oxidizing atmosphere. Infusibilization not only prevents melting of the non-graphitizable carbon material during carbonization, but also ensures the non-graphitizable nature of the finely graphitizable carbon material and improves the adhesion of the coated thermosetting resin. It is also preferable to impart preferable porosity to the finely non-graphitizable carbon material for improvement.

[0015] The finely non-graphitizable carbon material preferably has an oxygen content of 5 to 30% by mass as a result of the infusibilization treatment of the precursor. If the oxygen content is less than 5%, foaming of the pressure-molded body occurs during firing, and the desired shape may not be obtained. In addition, the degree of crystallinity increases during high-temperature firing, making it difficult to obtain the desired non-graphitic carbon material. On the other hand, if the oxygen content exceeds 30% by mass, the amount of water generated at the time of firing increases, and there is a problem that a reaction between carbon and water gas occurs to accelerate oxidative consumption. For similar reasons,
It is preferable that the fixed carbon content at 800 ° C. is 70% by mass or more. In particular, a carbon material having an oxygen content in the range of 5 to 10% by mass gives a good non-graphitic carbon material (support member) which exhibits good self-sintering property when fired, and has a dense structure and markedly improved strength. It is preferred.

In the present invention, as the finely non-graphitizable carbon material that is particularly preferably used, for example, a porous pitch-based carbon material obtained as follows can be mentioned. That is, a 2- to 3-ring aromatic compound having a boiling point of 200 ° C. or higher or a mixture thereof is added as an additive to petroleum pitch, heated and melt-mixed, and then molded to obtain a pitch molded body. Next, the additive is extracted and removed from the pitch formed body with a solvent having a low solubility in the pitch and a high solubility in the additive, and the obtained porous pitch is oxidized to obtain an infusible material. Micronization is performed at any stage after or before infusibilization to obtain a finely non-graphitizable carbon material.

The above-mentioned aromatic additive is selected from one or a mixture of two or more of, for example, naphthalene, methylnaphthalene, phenylnaphthalene, benzylnaphthalene, methylanthracene, phenanthrene and biphenyl. The amount added to the pitch is preferably in the range of 30 to 70 parts by weight per 100 parts by weight of the pitch.

The mixing of the pitch and the additive is performed in a heated and molten state in order to achieve uniform mixing. The mixture of the pitch and the additive is preferably formed into particles having a particle size of 1 mm or less so that the additive can be easily extracted from the mixture. The molding may be performed in a molten state, or by a method such as pulverizing the mixture after cooling.

Solvents for extracting and removing additives from the mixture of pitch and additives include aliphatic hydrocarbons such as butane, pentane, hexane and heptane; mixtures mainly composed of aliphatic hydrocarbons such as naphtha and kerosene; And aliphatic alcohols such as ethanol, propanol and butanol.

By extracting the additive from the mixture of pitch and additive with such a solvent, the additive can be removed from the molded body while maintaining the shape of the molded body. At this time, it is presumed that holes for the additive are formed in the molded article, and a pitch molded article having uniform porosity is obtained.

Next, the thus obtained porous formed compact is oxidized (infusible). The oxidation is preferably performed at a temperature from normal temperature to 400 ° C. As oxidizing agents,
O ₂ , O ₃ , SO ₃ , NO ₂ , a mixed gas obtained by diluting them with air, nitrogen, or the like, or an oxidizing gas such as air, or an oxidizing liquid such as sulfuric acid, nitric acid, or hydrogen peroxide can be used. it can.

It is convenient to oxidize the porous pitch at 120 ° C. to 300 ° C. using an oxygen-containing gas such as air or a mixture of air and another gas such as a combustion gas as an oxidizing agent. Yes, it is economically advantageous.

The porous pitch-based carbon material obtained as described above is characterized by having open pores. For example, open pores having a diameter of 3 to 100 nm determined by a mercury intrusion method have a diameter of 0.02. Those exhibiting a specific volume of 0.1 ml / g are preferably used.

In the present invention, the above-mentioned fine infusibilized carbon material, its carbonized material (for example, calcined at a temperature of 900 to 1500 ° C. in a non-oxidizing atmosphere), or a mixture thereof is used as the fine graphite powder. It can be suitably used as a carbonizable material. In particular, fine infusibilized carbon material alone,
Alternatively, a mixture thereof with a carbonized material having the main component is preferably used.

Next, the finely graphitizable carbon material obtained as described above is coated with a thermosetting resin to obtain a compression molding raw material. The coating with a thermosetting resin imparts the binding property at room temperature, which lacks the fine graphitizable carbon material, and imparts compression moldability to a predetermined shape. It is carbonized by filling gaps between them, and is used to give a non-graphitic carbon material integral with the carbonized fine non-graphitizable carbon material. In this case, the thermosetting resin is added in an amount of 10 to 60 parts by mass of the fine non-graphitizable carbon material.
It is preferable to coat at a ratio of 40 parts by mass (the total amount with the carbon material is 100 parts by mass). 10 thermosetting resins
If the amount is less than 40 parts by mass, it is difficult to obtain the predetermined effect sufficiently. If the amount is more than 40 parts by mass, the volatile matter generated at the time of firing increases, and the molded body foams. It becomes difficult to obtain a carbon material. Thermosetting resin is
During firing, it is more preferably used than thermoplastic resin because it has a high carbonization rate to non-graphitic carbon and easily forms a good C / C composite with a carbonized fine non-graphitizable carbon material. The carbonized material of the finely non-graphitizable carbon material and the carbonized material of the thermosetting resin give similar non-graphitic structures. Gives a graphitic carbon material. The thermosetting resin is preferably at least partially liquid, and examples thereof include a phenol resin, a furan resin, an unsaturated polyester resin, and a polyimide resin (precursor). Among them, a phenol resin is preferable, and it is particularly preferable to use a form in which a resol type liquid phenol resin is first coated on the surface of a finely non-graphitizable carbon material, and then a novolak type solid phenol resin is adhered. The liquid phenol resin and the solid phenol resin are in a weight ratio of 1:
It is preferable to use a ratio of 0.5 to 1: 3.

Next, the finely graphitizable carbon material coated with the thermosetting resin is compression molded to obtain a molded body. In the method for producing a non-graphitic carbon material supporting member of the present invention, the coated finely non-graphitizable carbon material used as a raw material is almost granular as a whole, and can be given any shape in compression molding. Is the feature. This is disclosed in
It is understood that this is an important advantage over the method for producing a glassy carbon material according to the method described in JP-A-0-67559. Therefore,
In compression molding, not only a flat molded body can be obtained by a flat mold, but also a concavo-convex shape or a mountain shape can be imparted by integral molding by using a previously engraved mold. For example, when the support member of the present invention is used as an underlaying plate of a metal powder molded body for powder metallurgy, unevenness is preferable because the metal powder molded body does not contact each other when the metal powder molded body is small,
The mountain shape is preferable for reducing the contact area between the metal powder molded body and the carbon underlay plate. If the metal powder molded body is sintered while being in contact, a problem arises in that the contact portions are united when melting. In addition, by reducing the contact area, the carbonization reaction area between the carbon underlay plate and the metal is reduced, so that the life of the underlay plate for metal sintering can be improved.

The compression molding is generally carried out by filling a mold with a coated raw material made of a finely non-graphitizable carbon material and applying a pressure such that a surface pressure applied to the mold is 5 to 100 MPa in a projected sectional area. . When the surface pressure is less than 5 MPa, the strength of the molded body after molding is low, so that the molded body is likely to be damaged when transferred into a firing furnace. On the other hand, if it exceeds 100 MPa, the apparent density of the molded body increases, which causes a problem that firing cracks occur during firing. It is necessary to select a material for the molding die according to the surface pressure at the time of molding. If the molding surface pressure is less than 50 MPa, a carbon mold can be used.
When the pressure is 0 MPa or more, it is preferable to use a metal mold.

In the case of hot molding using a heat source for molding, when heat is applied, the thermosetting resin plasticizes and acts as a binder while filling the voids of the non-graphitizable carbon. By further applying heat, it cures and becomes a molded body. In particular, when the surface of non-graphitizable carbon is coated with a thermosetting resin,
The object is to prevent the destruction of non-graphitizable carbon due to molding pressure and to fill only the voids while maintaining the shape of non-graphitizable carbon. Therefore, plasticization of the thermosetting resin can be promoted as compared with cold molding without applying heat, for example, 60 to
Hot forming at 170 ° C. is effective for the present invention.

Next, the compression molded body is fired in an inert or non-oxidizing atmosphere to obtain a fired body. The finely non-graphitizable carbon material and the thermosetting resin carbonize by releasing hydrogen, methane, carbon dioxide, carbon monoxide, water, and the like during the carbonization process. The firing temperature in this case is from 1000 ° C. to 2
The temperature is preferably 000 ° C, more preferably from 1200 ° C to 1500 ° C. 15 for non-graphitizable carbon materials
This is because even if the temperature exceeds 00 ° C., no significant structural change is received until 3000 ° C. 2000 ° C if necessary
The ash content is reduced to, for example, 200 p
It is also preferable to reduce it to pm or less. This demineralization process
This is effective when the purity of raw materials is low. In particular, when the contained impurities remain at a low sintering temperature, the product quality deteriorates due to the reaction with the contained impurities when the metal powder molded body is sintered. However, by performing the demineralization (purification) treatment, such a reaction can be suppressed, and in addition, there is an effect that deterioration due to catalysis of impurities contained in the metal sintering base plate can be prevented.

[0030]

The present invention will be described more specifically with reference to the following examples and comparative examples. The physical property values described in the present specification including the following examples are based on the values obtained by the following methods.

(1) Oxygen content After grinding the sample carbon material to about 0.1 mm,
About 2 mg of a powder sample obtained by drying at 2 ° C. for 1 hour is measured using “MT-5” manufactured by Yanaco. (2) Fixed carbon content The fixed carbon content at 800 ° C. is measured according to the method for determining the fixed carbon content described in JIS K2425 “Testing method for creosote oil, processed tar, tar pitch”. (3) Ash content The ash content is measured according to the method for determining the ash content of tar pitch described in JIS K2425 “Testing method for creosote oil, processed tar, tar pitch”. (4) Average particle size The mass average particle size described in JIS K1474 “Test method for activated carbon” is measured. (5) Open pore specific volume An open pore specific volume (ml) having a pore diameter in a range of 3 to 100 nm.
/ G) is measured by a mercury intrusion method.

Example 1 Spherical infusible petroleum-based pitch particles having an average particle diameter of 0.62 mm ("KH-1B" manufactured by Kureha Chemical Industry Co., Ltd .; oxygen content = 7) as a fine non-graphitizable carbon material 0.1%, fixed carbon content = 72.1%, open pore specific volume = about 0.05 ml / g) 80 parts by mass of the surface was coated with a resol type liquid phenolic resin (Gunei Chemical Industry Co., Ltd. “Regitop” PL-4804 ") after wetting with 8 parts by mass, a novolak-type solid phenolic resin (" P-4 "manufactured by Gunei Chemical Industry Co., Ltd.)
G-2411 ”; average particle size = 20 to 80 μm) to obtain a raw material. The raw materials are filled in a flat mold heated to 170 ° C., and the temperature is raised from an initial temperature of 60 ° C. to an internal temperature of 1 ° C.
5MPa per projected sectional area at 50 ° C or more for 10 minutes
To obtain a flat compression molded body having a thickness of about 7 mm. Next, the molded body is placed flat in a graphite crucible,
Placed in a firing furnace together with the crucible, and after vacuum replacement, fired at 1500 ° C. for 1 hour in a nitrogen stream to obtain a size of 420 mm
An underlaying plate for metal sintering of × 250 mm × 6 mm was obtained. The underlay plate had an apparent density of 1.42 g / ml and an ash content of 0.04% by mass.

On the metal sintering base plate, 10
Diameter 20mm x thickness 5m, compression molded at 0MPa pressure
m and a metal powder compact 1 composed of a mixed powder of 99% by mass of iron + 1% by mass of graphite and a powdered mixture of 97% by mass of iron + 1% by mass of graphite + 2% by mass of nickel The body 2 is placed and held for 1 hour in an ammonia reforming gas (H ₂ : 30% by volume, N ₂ : 70% by volume) at 1120 ° C., and sintered, the sintered body and the carbon underlay plate Was visually observed to determine the presence or absence of carburization (skin appearance or discoloration on the surface of the sintered body). The results were evaluated according to the following criteria. A: Carburizing is not recognized. B: Carburization is observed in at least one of the sintered body and the carbon underlay plate. C: Remarkable carburization was observed in the sintered body, and seizure with the carbon underlay plate was caused.

Then, for the carbon underlaying plate sample having no problem in the sintering test at 1120 ° C., the sample was prepared in an ammonia reforming gas (H ₂ : 60% by volume, N ₂ : 40% by volume) at 1150 ° C. and 1180 ° C. A 1 hour similar sintering test was performed to determine the presence or absence of carburization.

As a result, it was confirmed that the carbon underlaying plate did not show carburization after any of the sintering tests and was a satisfactory underlaying plate for metal sintering. An outline of the test and the results are summarized in Table 1 below together with the following Examples and Comparative Examples.

Example 2 90 parts by mass of spherical infusibilized petroleum-based pitch particles ("KH-1B" manufactured by Kureha Chemical Industry Co., Ltd.) were mixed with a resole type liquid phenol resin ("Registration" manufactured by Gunei Chemical Industry Co., Ltd.). Using a raw material treated in the same manner as in Example 1 with 4 parts by mass of Top PL-4804 ") and 6 parts by mass of a novolak type solid phenol resin (" PG-2411 "manufactured by Gunei Chemical Industry Co., Ltd.), In the same manner as in Example 1, a carbon underlay plate was obtained, and the metal powder molded body 1 and the metal powder molded body 2 were sintered to determine the state of carburization.

Example 3 60 parts by mass of spherical infusibilized petroleum-based pitch particles ("KH-1B" manufactured by Kureha Chemical Industry Co., Ltd.) were mixed with a resole type liquid phenol resin ("Regiseki" manufactured by Gunei Chemical Industry Co., Ltd.). Using raw materials treated in the same manner as in Example 1 with 16 parts by mass of Top PL-4804) and 24 parts by mass of a novolak type solid phenol resin (“PG-2411” manufactured by Gunei Chemical Industry Co., Ltd.), In the same manner as in Example 1, a carbon underlay plate was obtained, and the metal powder molded body 1 and the metal powder molded body 2 were sintered, and the carburizing state was determined.

(Comparative Example 1) As in Example 1, a graphite sheet having a size of 420 mm x 250 mm x 6 mm cut out from a commercially available graphite extruded material ("PS-G12" manufactured by SSC Corporation) was used as an underlaying plate. Then, the metal powder molded body 1 and the metal powder molded body 2 were sintered, and the carburizing state was determined.

Comparative Example 2 99.2 parts by mass of spherical infusibilized petroleum-based pitch particles (“KH-1B” manufactured by Kureha Chemical Industry Co., Ltd.) were added to a 20.5% water-soluble acrylic resin aqueous solution (Chuo Rika Kogyo Co., Ltd.) (Two-fold dilution of 41% aqueous solution of acrylic resin)
A molded body obtained by compression-molding the raw material coated with 0.8 parts by mass under a pressure of 10 MPa is baked under the same conditions as in Example 1 to obtain an underlay plate, and is used in the same manner as in Example 1 Then, the metal powder molded body 1 and the metal powder molded body 2 are sintered,
The carburization status was determined.

Comparative Example 3 Granulated infusible petroleum-based pitch particles having an average particle size of 9 μm (“KH-1” manufactured by Kureha Chemical Industry Co., Ltd.)
P "= pulverized product of" KH-1B ") 80 parts by mass, and a granular novolak phenol resin having an average particle size of 20 to 80 [mu] m as a thermosetting resin (" Cashew No. 05 "manufactured by Cashew Resin Industry Co., Ltd.) ) 20 parts by weight at normal temperature and normal pressure,
Except for using raw materials obtained by mixing with a Henschel mixer, an underlaying plate was obtained in the same manner as in Example 1, and the metal powder molded bodies 1 and 2 were sintered to determine the state of carburization. As a result, the 1180 ° C.
Carburization was observed in the sintering of the steel. This is considered to be because the granular novolak-type solid phenol resin was insufficient at 20% by mass to fill the voids of the finely non-graphitizable carbon material.

(Reference Example) 94.5 parts by mass of spherical infusibilized petroleum-based pitch particles ("KH-1B" manufactured by Kureha Chemical Industry Co., Ltd.) were mixed with a resol type liquid phenol resin ("Gunei Chemical Industry Co., Ltd."). Example 1 using 1.8 parts by mass of REGISTOP PL-4804 ") and 2.7 parts by mass of a novolak type solid phenol resin (" PG-2411 "manufactured by Gunei Chemical Industry Co., Ltd.)
Using the raw materials treated in the same manner as in Example 1, a carbon underlay plate was obtained in the same manner as in Example 1, and the metal powder molded bodies 1 and 2 were sintered to determine the state of carburization. The metal powder molded body 1 was not carburized to 1150 ° C., but the metal molded body 2 was carburized at 1150 ° C. This is because the amount of the thermosetting resin is small, so that only the surface layer of the non-graphitizable carbon can be coated and molded. However, it is considered that oxidative consumption accelerated due to the presence of many voids inside. .

The summary of the above example is summarized in Table 1 below.

[0043]

[Table 1]

[0044]

According to the present invention, it is possible to efficiently produce a homogeneous non-graphitic carbon material for supporting a high-temperature-heated metal molded body, which hardly causes carburization.

 ──────────────────────────────────────────────────続 き Continued on the front page (72) Inventor Tamio Haga 16 Nishimachi Ochiai, Iwaki City, Fukushima Prefecture Kureha Chemical Industry Co., Ltd. F term (reference) 4G032 AA09 AA13 AA14 AA52 BA01 GA06 GA12

Claims (11)

[Claims] 1. A finely non-graphitizable carbon material is coated with a thermosetting resin and then molded under pressure, and the molded body is baked to obtain an apparent density of 0.9 to 1.5 g / ml and an ash content of 0.5
% Of a non-graphitic carbon material having a content of less than 10% by weight. 2. The method according to claim 1, wherein the non-graphitizable fine carbon material is an infusibilized petroleum pitch compact, a carbonized product thereof, or a mixture thereof. 3. The process according to claim 1, wherein the fine graphitizable carbon material is particles of a non-graphitizable carbon material having an oxygen content of 5 to 30% by mass. 4. The process according to claim 1, wherein the fine graphitizable carbon material is particles of a graphitizable carbon material having an oxygen content of 5 to 10% by mass. 5. The method according to claim 3, wherein the non-graphitizable carbon material particles have an average particle size of 0.3 to 1 mm. 6. The finely graphitizable carbon material is a carbon material having a fixed carbon content at 800 ° C. of 70% by mass or more.
5. The production method according to any one of items 1 to 5, 7. After coating 60 to 90 parts by mass of the fine graphitizable carbon material with 10 to 40 parts by mass of a thermosetting resin (100 parts by mass in total with the fine graphitizable carbon material), The production method according to any one of claims 1 to 6, wherein pressure molding is performed. 8. The production method according to claim 1, wherein surface irregularities are imparted to the molded body during pressure molding. 9. A non-graphitic carbon material having a ash content of 200 ppm or less by performing a deashing treatment in a firing process.
Manufacturing method. 10. The method according to claim 1, wherein the thermosetting resin is a liquid thermosetting resin. 11. The production method according to claim 10, wherein after the finely non-graphitizable carbon material is coated with a liquid thermosetting resin, a solid thermosetting resin is further adhered and then pressure molded.