JP4963831B2 - Semiconductive structure, conductive and / or thermally conductive structure, method for producing the structure, and use thereof - Google Patents

Description

  The present invention relates to a semiconductive structure, a conductive and / or thermally conductive structure, a method for producing the structure, and uses thereof. Specifically, a plastic structure in which carbon filler as conductive and / or thermally conductive filler is dispersed in a polymer exhibits higher conductivity and / or thermal conductivity than the conventional one even with the same blending amount. Or a structure that exhibits high electrical conductivity and / or thermal conductivity equivalent to or higher than that of conventional ones with a smaller blending amount than the conventional one, can withstand high temperature and high load, has a small friction coefficient, and is not easily worn, and the structure This invention relates to the manufacturing method of

Semiconductor parts and precision electrical equipment are often used in automobiles and aircraft. Since semiconductor components can be damaged by static electricity, measures must be taken to prevent the generation of static electricity at semiconductor manufacturing sites and devices incorporating semiconductor components. In addition, since precision electrical equipment and the like may malfunction due to external electromagnetic waves, measures for shielding electromagnetic waves may be required. Therefore, semiconductive resin molded products are used for the purpose of preventing the generation of static electricity and shielding electromagnetic waves.
As a semiconductive / conductive resin molded product, a product obtained by molding a material obtained by kneading a conductive filler in a resin or an elastomer is known.
Increasing the amount of conductive filler to be filled in resin, rubber, etc. will increase the conductivity gradually, and if it exceeds a certain critical filling amount (threshold), the conductivity will increase dramatically and the conductivity will increase dramatically. After that, the conductivity gradually increases again.

  In order to obtain a volume specific resistance value suitable for antistatic using a material in which a conductive filler is kneaded into a resin or the like, it is necessary to add the conductive filler above a threshold value. However, when the conductive filler is added to a threshold value or more, the melt fluidity of the resin is lowered and the molding process becomes difficult, and a short shot is likely to occur. Even if a large amount of conductive filler can be added and molded, the surface appearance of the molded product tends to deteriorate, and satisfactory molded products cannot be obtained due to variations in the mass of each shot. In some cases, only molded articles with inferior physical properties can be obtained.

For this reason, various studies have been made to obtain a molded article having high conductivity by blending a small amount of conductive filler. For example, it has been proposed to adjust the particle diameter, aspect ratio, specific surface area, and the like of the conductive filler, but the fluidity at the time of molding may be deteriorated, and applicable conductive fillers are limited. It has been proposed to blend a resin having a high affinity with the conductive filler and a resin having a low affinity to form a microdomain having a sea-island structure (Patent Documents 1 and 2). However, this method cannot be applied to applications where the property cannot be allowed to change due to the resin blend. Also, a method has been proposed in which the surface of the conductive filler is treated to increase the interface energy between the resin / conductive filler (Non-patent Document 1). However, the resin to which this method can be applied is limited, and the surface treatment of the conductive filler may impair the original characteristics of the conductive filler and its application is limited.
As described above, no satisfactory method has been found for obtaining a molded product having high conductivity with a small amount of conductive filler without causing deterioration in physical properties other than conductivity, fluidity during molding, and the like.

  On the other hand, in a device having a sliding portion such as a hard disk, static electricity or heat generated by friction of the sliding portion may cause the device to malfunction. In addition, fine powder generated by wear of the sliding portion may enter into precision equipment and cause malfunction. Therefore, conductive and / or thermally conductive resin molded products are used for the purpose of preventing static electricity due to static electricity and dissipating frictional heat. As a conductive and / or thermally conductive resin molded product used for a sliding member or the like, for example, a product obtained by mixing carbon fiber with a resin has been proposed (Patent Documents 3 and 4). However, as described above, it is necessary to add a large amount of filler in order to obtain conductivity / thermal conductivity. For this reason, the blended filler may be scattered as fine powder due to wear. In this way, a molded article having high conductivity / thermal conductivity is obtained with a small amount of conductive / thermal conductive filler without causing deterioration in physical properties other than conductivity / thermal conductivity, fluidity reduction during molding, and the like. No satisfactory method has been found for this.

JP-A-2-201811 JP-A-1-263156 Journal of Japan Adhesion Association 23, 103, 1987 JP-A-3-38327 Japanese Patent Laid-Open No. 4-11893

  An object of the present invention is to provide a plastic structure in which a carbon filler as a conductive and / or heat conductive filler is dispersed in a polymer. A structure that exhibits high electrical conductivity and / or thermal conductivity equivalent to or higher than that of a conventional material with a blending amount less than that of the prior art, withstands high temperature and high load, has a low coefficient of friction, and is not easily worn. It is in providing the manufacturing method of a structure, and its use.

As a result of intensive studies, the inventors of the present invention dry-mixed the polymer particles and the carbon filler so that the carbon filler is present on at least a part of the surface of the polymer particle, and between one polymer particle and another polymer particle. A mixture in which carbon fillers are present is obtained, and the mixture is pressure-molded at a pressure of 1 to 500 kgf / cm ² and at a temperature equal to or higher than the deflection temperature under load, melting point, or glass transition temperature of the polymer particles. And a B phase containing a carbon filler as a main component, the B phase surrounds each of the A phases, and a B phase is interposed between one A phase and another A phase. , A structure in which the B phase is distributed in a three-dimensional network structure or in a marble pattern is obtained. Exhibits thermal conductivity or was found to exhibit a conventional equal to or more high conductivity and / or thermal conductivity with a smaller amount than before. Furthermore, when this structure is applied to a sliding member, it can withstand high temperatures and high loads, has a low friction coefficient, is not easily worn, has good thermal conductivity, and can quickly release the generated heat. It has been found that even if the material is aluminum, the sliding performance can be maintained for a long time without damaging the aluminum. The present invention has been completed based on these findings.

Thus, according to the present invention,
[1] A mixture in which a carbon filler is present on at least a part of the surface of the polymer particle, and the carbon filler is interposed between one polymer particle and another polymer particle.
[2] By heating the mixture according to the above [1] at a temperature equal to or higher than the deflection temperature under load, melting point or glass transition temperature of the polymer particles, the polymer particles are softened, and one carbon filler and another carbon filler A structure in which a softening polymer is soaked in a gap, and includes a phase A made of only a polymer and a phase B containing a carbon filler as a main component, and the phase B forms a three-dimensional network structure.
[3] A phase comprising only a polymer and a B phase containing a carbon filler as a main component, the B phase surrounding each of the A phases, and between one A phase and another A phase A structure in which the B phase intervenes and the B phase is distributed in a marble pattern.
[4] The structure according to [2], wherein the polymer particles are particles composed of at least one polymer selected from the group consisting of a thermoplastic resin, a thermoplastic elastomer, an uncrosslinked thermosetting resin, and an uncrosslinked elastomer. body.
[5] The structure according to [2], wherein the polymer particles have an average particle diameter of 1 μm to 500 μm.

[6] carbon fillers include carbon black, structure according to the carbon fibers, and that the at least one thing selected from black lead or Ranaru group [2] or [3].
[7] The carbon filler is vapor grown carbon fiber,
The vapor grown carbon fiber has an average fiber diameter of 20 to 500 nm, an aspect ratio of 20 to 1000, a BET specific surface area of 4 to 100 m ² / g, an X-ray diffraction d ₀₀₂ of 0.345 nm or less, and a Raman scattering spectrum. the ratio of the peak height of the band 1341~1349cm ^-1 (I _d) and the band peak height _{^{1570~1578cm -1 (I g): (}} I d / I g) is 0.1 to 2 The structure according to [2] or [3].
[8] The carbon filler is vapor grown carbon fiber,
The structure according to [2] or [3], wherein the vapor grown carbon fiber is heat-treated at a temperature of 2000 to 3500 ° C. in an inert atmosphere.
[9] The structure according to [7] or [8], wherein the vapor grown carbon fiber has an average fiber diameter of 50 to 200 nm.
[10] The above-mentioned obtained by dry-mixing polymer particles and carbon filler, and then press-molding at a pressure of 1 to 500 kgf / cm ^{2 and at} a temperature higher than the deflection temperature under load, melting point or glass transition temperature of the polymer particles [ [2] or [3].

[11] The method comprising dry-mixing polymer particles and carbon filler, and then press-molding at a pressure of 1 to 500 kgf / cm ² and at a temperature equal to or higher than the deflection temperature under load, melting point or glass transition temperature of the polymer particles [2 ] Or the manufacturing method of the structure as described in [3].
[12] The method for producing a structure according to [11], wherein a holding time at the time of pressure molding is 15 minutes or more.
[13] The method for manufacturing a structure according to [11], further including cutting into a desired shape after the pressure forming.
[14] The method for producing a structure according to [11], wherein pressure molding is performed using a mold having a desired shape.
[15] The method for producing a structure according to [11], wherein the dry mixing is performed at a temperature lower than the deflection temperature under load, the melting point, or the glass transition temperature of the polymer particles.

[16] The above-mentioned [2], containing 99.5 to 90 parts by mass of a polymer and 0.5 to 10 parts by mass of a carbon filler with respect to 100 parts by mass of the structure, and having a volume resistivity of 10 ² to 10 ¹⁰ Ωcm. ] Or the semiconductive structure according to [3].
[17] The semiconductive structure according to [16], wherein the carbon filler is vapor grown carbon fiber.
[18] 80 to 50 parts by mass of the polymer and 20 to 50 parts by mass of the carbon filler with respect to 100 parts by mass of the structure, the volume resistivity is 10 ⁻⁴ to 10 ² Ωcm, and the thermal conductivity is 7 W. The conductive and / or thermally conductive structure according to [2] or [3], which is / mK or more.
[19] The above [18], wherein 20 to 50 parts by mass of carbon filler comprises 0.5 to 30 parts by mass of vapor grown carbon fiber, 0 to 20 parts by mass of graphite powder, and 0 to 30 parts by mass of graphitized carbon fiber. The electrically conductive and / or thermally conductive structure described in 1.

[20] An antistatic member comprising the semiconductive structure according to [16] or [17].
[21] The antistatic member according to [20], which is for a semiconductor, a semiconductor component, a hard disk head, or a tray for transporting a hard disk. [22] The semiconductive structure according to [16] or [17] An antistatic sliding member comprising a body.
[23] The antistatic sliding member according to [22], which is for a part used in a clean room.
[24] The antistatic sliding member according to [22], which is used for manufacturing machine parts used in a clean room.

[25] A conductive member comprising the conductive and / or thermally conductive structure according to [18] or [19].
[26] The conductive member according to [25], which is for a fuel cell separator.
[27] A heat-resistant sliding member comprising the conductive and / or thermally conductive structure according to [18] or [19].
[28] The heat-resistant sliding member according to [27], which is for parts used in a high-temperature and high-load environment.
[29] The heat-resistant sliding member according to [27], which is used for manufacturing equipment parts, OA equipment parts, or automobile parts used in a high temperature and high load environment.
Is provided.

  When a conductive filler and / or thermally conductive filler is dispersed in one kind of polymer to obtain a plastic having excellent conductive performance and / or thermal conductive performance, the conductive filler and resin are usually melt-kneaded and then injected. Often molded. In that case, since the conductive filler in the molten resin is dispersed by shearing force, the conductive and heat transfer networks are broken, or the conductive filler is broken. Especially, the aspect ratio tends to be small in the fibrous conductive filler. It is known that a large amount of filler needs to be added in order to obtain the desired conductivity or heat conductivity. In the present invention, since no shear force is applied in the softened polymer, an effective network structure can be formed, and the amount of carbon filler added to obtain the desired conductivity or heat conductivity can be dramatically reduced. It becomes possible, and its industrial utility value is extremely high.

  The (semiconductive, conductive and / or thermally conductive) structure of the present invention has the mechanical strength inherent to the polymer, and has electrical characteristics such as conductivity and antistatic properties, and thermal conductivity. Excellent thermal characteristics. In addition, since the structure of the present invention is excellent in mechanical strength, paintability, thermal stability, impact strength, and excellent in conductivity and antistatic properties, it is possible to transport electric and electronic parts, packaging parts, electric and electronic parts. It is useful in many fields such as fields, parts for office automation equipment, and automotive parts for electrostatic coating. Furthermore, since the structure of the present invention is excellent in thermal conductivity, the allowable range of temperature and load is wide, and it is suitable for a sliding member used at high temperature and high load. The structure of the present invention has a very high industrial utility value.

In the structure of the present invention, even when vapor-grown carbon fiber having a high aspect ratio is used, the destruction of the carbon fiber is suppressed and the aspect ratio is hardly lowered. By high-filling carbon fiber, it can withstand high temperatures and high loads, has a low coefficient of friction, is hard to wear, has little filler detachment, has good thermal conductivity, and can quickly release generated heat. . Furthermore, even if the counterpart material is aluminum, a sliding member that can maintain the performance for a long time without damaging the aluminum can be obtained. The present invention has an extremely high industrial utility value.
The sliding member of the present invention is excellent in mechanical properties, heat resistance, and thermal conductivity. In particular, with regard to slidability, both the coefficient of friction and the amount of wear are small, and the limit PV value is very large. Therefore, it can be used for a wide range of applications as a sliding member in automobiles, electrical / electronic fields and the like.

(Mixture of polymer particles and carbon filler)
In the mixture of the present invention, a carbon filler is present on at least a part of the surface of the polymer particle, and the carbon filler is interposed between one polymer particle and another polymer particle. FIG. 4 (1) is a diagram conceptually showing an example of the mixture of the present invention. In the figure, polymer particles indicated by white circles are floated and dispersed in the carbon filler indicated by black lines. In this mixture, the polymer particles can move freely and are not bonded to each other.

  The polymer particles used in the present invention have a particle size of usually 1 to 500 μm, preferably 5 to 200 μm. If this particle size is too large, poor dispersion tends to occur. The polymer constituting the polymer particles is not particularly limited, and can be selected from, for example, a thermoplastic resin, a thermoplastic elastomer, an uncrosslinked thermosetting resin, and an uncrosslinked elastomer.

The thermoplastic resin is not particularly limited as long as it is a thermoplastic resin used in the molding field. For example, polyethylene terephthalate (PET), polybutylene terephthalate (PBT), polytrimethylene terephthalate (PTT), polyethylene naphthalate ( PEN), polyesters such as liquid crystal polyester (LCP); polyolefins such as polyethylene (PE), polypropylene (PP), polybutene 1 (PB-1), polybutylene; styrene resins; polyoxymethylene (POM), polyamide (PA) , Polycarbonate (PC), polymethyl methacrylate (PMMA), polyvinyl chloride (PVC), polyphenylene ether (PPE), polyphenylene sulfide (PPS), polyimide (PI), polyamideimide (PAI), poly Etherimide (PEI), polysulfone (PSU), polyethersulfone, polyketone (PK), polyetherketone (PEK), polyetheretherketone (PEEK), polyetherketoneketone (PEKK), polyarylate (PAR), Polyether nitrile (PEN); Phenol (novolak type, etc.) phenoxy resin; Fluorine resin such as polytetrafluoroethylene (PTFE); Thermoplastic polyimide, polybenzimidazole, liquid crystal polymer, cycloolefin polymer, polyacetal, polyphenylene oxide, heat Examples thereof include plastic polyester and ultrahigh molecular weight polyethylene. These may be copolymers or modified products, or may be a resin in which two or more types are blended. Further, in order to further improve impact resistance, a resin obtained by adding another elastomer or a rubber component to the thermoplastic resin may be used.
Resins with very high molecular weight such as ultra-high molecular weight polyethylene, resins such as polytetrafluoroethylene that cannot be melt kneaded with a narrow range of molding conditions, and resins that do not show melt fluidity such as polybenzimidazole Even so, if the method of the present invention is used, a semiconductive, conductive and / or thermally conductive structure can be easily obtained.
Examples of the thermoplastic elastomer include thermoplastic elastomers such as polystyrene, polyolefin, polyurethane, polyester, polyamide, polybutadiene, polyisoprene, and fluorine.

The thermosetting resin is not particularly limited as long as it is a thermosetting resin used in the molding field, and examples thereof include unsaturated polyester, vinyl ester, epoxy, phenol (resole type), urea melamine, polyimide, and the like. It is done. These may be copolymers or modified products, or may be a resin in which two or more types are blended. Further, in order to further improve the impact resistance, a resin obtained by adding an elastomer or a rubber component to the thermosetting resin may be used. The polymer particles made of thermoplastic resin, thermosetting resin or elastomer are uncrosslinked / uncured in the mixture. Then, as will be described later, the thermoplastic resin, thermosetting resin or elastomer may be crosslinked / cured when the mixture is pressure-molded.
Elastomers include natural rubber, isoprene rubber, styrene butadiene rubber, butadiene rubber, chloroprene rubber, nitrile rubber, butyl rubber, ethylene propylene rubber, urethane rubber, silicone rubber, acrylic rubber, chlorosulfonated polyethylene rubber, fluoro rubber, hydrogenated hydrogen Examples include tolyl rubber, epichlorohydrin rubber and polysulfide rubber.

  Among these polymers, polyetheretherketone, polyetherketone, thermoplastic polyimide, polybenzimidazole, liquid crystal polymer, polyethersulfone, polysulfone, polyetherimide, polyamideimide, polyphenylene sulfide, cycloolefin polymer, polycarbonate, polyamide, Polyacetal, polyphenylene oxide, thermoplastic polyester, polytetrafluoroethylene, and ultrahigh molecular weight polyethylene are preferred.

  If the carbon filler used by this invention is a carbon material which can provide electroconductivity or heat conductivity, there will be no restriction | limiting in particular. For example, carbon black, carbon fiber, graphite and the like can be mentioned. Of these, carbon fibers, particularly vapor grown carbon fibers are preferred.

The vapor grown carbon fiber used in the present invention can be produced, for example, by blowing an organic compound gasified with iron serving as a catalyst in a high-temperature inert gas atmosphere (Japanese Patent Laid-Open No. 7-150419). etc).
The vapor grown carbon fiber used in the present invention preferably has an average fiber diameter of 20 to 500 nm, and more preferably 50 to 200 nm. When the average fiber diameter decreases, the surface energy increases exponentially, and the cohesion between fibers tends to increase. Simple dry blending of vapor-grown carbon fibers and polymer particles with a small average fiber diameter does not dissolve the carbon fibers and does not fully disperse, making it difficult to form an effective conductive or heat conductive network Become. Therefore, it is necessary to increase the amount of carbon fiber added, and the mechanical properties of the structure, in particular, impact properties tend to be lowered. On the other hand, when the average fiber diameter is increased, the carbon fibers are easily dispersed, but not only microscopically uniform cannot be obtained, but also the carbon fibers are likely to appear on the surface of the molded product, thereby reducing the sliding characteristics. There is.

The vapor grown carbon fiber used in the present invention preferably has an aspect ratio of 20 to 1000, more preferably 40 to 500.
When the aspect ratio is large (that is, the fiber length is long), the carbon fibers are entangled and cannot be easily loosened, and sufficient dispersion cannot be obtained. On the other hand, when the aspect ratio is small, it is not preferable because a filler of 10% by mass or more must be added to form a conductive network, and the fluidity and tensile strength of the polymer are significantly reduced.

  The degree of branching of the vapor grown carbon fiber used in the present invention is preferably 0.3 pieces / μm or less, more preferably 0.2 pieces / μm or less, and further preferably 0.1 pieces / μm or less. . If the degree of branching exceeds 0.3 / μm, the carbon fiber forms a strong aggregate, and it tends to be difficult to efficiently impart conductivity in a small amount.

The vapor grown carbon fiber used in the present invention has an average interplanar spacing d ₀₀₂ by an X-ray diffraction method of preferably 0.345 nm or less, more preferably 0.343 nm or less, and further preferably 0.340 nm or less. When the average interplanar spacing d ₀₀₂ exceeds 0.345 nm, the graphite crystal is not sufficiently developed, so that the resistivity of the carbon fiber alone tends to increase. Furthermore, when mixed with a polymer or the like, the movement of electrons between carbon fiber-polymer-carbon fiber tends to be difficult, and the amount of carbon fiber added to obtain desired conductivity tends to increase.

Vapor grown carbon fiber employed in the present invention has a BET specific surface area is preferably 4~100m ² / g, more preferably 10 to 40 m ² / g. A carbon fiber having a large BET specific surface area tends to be difficult to disperse because its surface energy increases and adhesion / cohesion force increases. Furthermore, the interfacial area between the matrix polymer and the carbon fiber increases, and the matrix polymer cannot sufficiently cover the fiber, or the probability that the carbon fiber peels from the matrix polymer tends to increase. As a result, when a composite with a polymer is produced, not only electrical conductivity but also mechanical strength may be deteriorated.

Vapor grown carbon fiber employed in the present invention, the ratio of the band peak height of the Raman scattering spectrum of 1341~1349cm ^-1 _{(I d)} and the band peak height 1570~1578cm ^-1 _{(I g)} (I _d / I _g ) is preferably 0.1 to 2, more preferably 0.1 to 1.4, still more preferably 0.15 to 1.3, and particularly preferably 0.2 to 1.2. is there.

The vapor grown carbon fiber used in the present invention can be produced by thermally decomposing a carbon source (organic compound) in the presence of an organic transition metal compound.
Examples of the carbon source (organic compound) used as the raw material for the carbon fiber include gases such as toluene, benzene, naphthalene, ethylene, acetylene, ethane, natural gas, carbon monoxide, and the like, alone or in combination of two or more. Can be used. Among these, aromatic hydrocarbons such as toluene and benzene are preferable.

An organic transition metal compound is a compound containing a transition metal serving as a catalyst. Examples of the transition metal used as the catalyst include elements in groups 4 to 10 of the periodic table. Preferable organic transition metal compounds include ferrocene and nickelocene.
Sulfur compounds such as sulfur and thiophene can be used as a co-catalyst for efficiently removing gas such as hydrogen adsorbed on the surface of the transition metal catalyst particles and enhancing the catalytic activity in a pyrolysis reaction atmosphere.

  A carbon fiber can be obtained by using a reducing gas such as hydrogen as a carrier gas, supplying the organic compound, the organic transition metal compound, and the sulfur compound to a reaction furnace heated to 800 to 1300 ° C. and performing a thermal decomposition reaction. it can.

  As the form of the raw material, a material obtained by dissolving an organic transition metal compound and a sulfur compound in an aromatic hydrocarbon (liquid raw material), or a material vaporized at 500 ° C. or lower (gas raw material) can be used. However, the liquid raw material is vaporized and decomposed on the reaction tube wall, and the concentration distribution of the raw material is locally generated in the reaction tube. As a result, the generated carbon fibers tend to aggregate. Therefore, as a form of the raw material, a gaseous raw material that hardly causes a raw material concentration distribution in the reaction tube is preferable.

  The ratio of the transition metal catalyst and the sulfur compound co-catalyst is preferably 15 to 35% by mass in the formula of transition metal / (transition metal + sulfur) × 100 [% by mass]. When the amount is 15% by mass or less, the catalytic activity increases, the number of fiber branches increases, the fibers are generated radially, and the like, and the interaction between the fibers increases to form a strong aggregate. On the other hand, when it is 35% by mass or more, hydrogen adsorbed on the catalyst cannot be sufficiently removed, and the supply of the carbon source to the catalyst is hindered, and carbon particles other than carbon fibers are likely to be generated.

  The number of branches of the carbon fiber and the degree of loosening of the aggregate are determined by the raw material concentration at the time of carbon fiber synthesis. That is, when the raw material concentration in the gas phase is high, non-uniform nuclei of the catalyst particles are generated on the surface of the produced carbon fiber, and the carbon fiber grows further from the surface of the carbon fiber to form a frost-like carbon fiber. Moreover, carbon fibers produced at a high concentration are entangled and cannot be easily loosened. Therefore, the ratio of the raw material supply amount in the reaction tube to the carrier gas flow rate is preferably 1 g / liter or less, more preferably 0.5 g / liter or less, and particularly preferably 0.2 g / liter or less.

  In order to remove organic substances such as tar adhering to the carbon fiber surface, heat treatment is preferably performed at 900 to 1300 ° C. in an inert atmosphere. In order to improve the electrical conductivity of the carbon fiber, it is preferable to further develop a crystal by performing a heat treatment at 2000 to 3500 ° C. in an inert atmosphere.

  The heat treatment furnace used to develop the crystal may be any furnace that can be maintained at a desired temperature of 2000 ° C. or higher, preferably 2300 ° C. or higher, and any ordinary apparatus such as an Atchison furnace, a resistance furnace, a high-frequency furnace, or the like. But you can. Moreover, depending on the case, the method of heating by energizing powder or a molded object directly can also be used.

  The atmosphere for the heat treatment is a non-oxidizing atmosphere, preferably an atmosphere of one or more rare gases such as argon, helium and neon. The heat treatment time is preferably as short as possible from the viewpoint of productivity. If heating is continued for a long time, the product yield deteriorates because it sinters and hardens. Therefore, after the temperature of the center part of the molded body or the like reaches the target temperature, it is sufficient to hold the temperature for 10 minutes to 1 hour.

Boron carbide (B ₄ C), boron oxide (B ₂ ) when performing graphitization treatment in which heating is performed at 2000 to 3500 ° C. in an inert atmosphere in order to further develop carbon fiber crystals and improve conductivity. Boron compounds such as O ₃ ), elemental boron, boric acid (H ₃ BO ₃ ), and borate may be mixed.

The amount of boron compound added depends on the chemical and physical properties of the boron compound used, and thus cannot be specified unconditionally. For example, when boron carbide (B ₄ C) is used, the amount of boron compound added is 0. The range is from 05 to 10% by mass, preferably from 0.1 to 5% by mass.

  By the heat treatment with the boron compound, the crystallinity of the carbon fiber is improved and the conductivity is improved. The amount of boron contained in the carbon fiber crystal or on the crystal surface is preferably 0.01 to 5% by mass. In order to improve the conductivity of the carbon fiber and the affinity with the polymer, it is more preferable to contain 0.1% by mass or more of boron. Further, the amount of boron that can be substituted for the graphene sheet is about 3% by mass, and more than that, especially 5% by mass or more of boron exists as boron carbide or boron oxide, and tends to lower the conductivity.

  In order to improve the affinity between the carbon fiber and the polymer, the carbon fiber can be oxidized to introduce a phenolic hydroxyl group, a carboxyl group, a quinone group, or a lactone group on the fiber surface. Furthermore, surface treatment may be performed with a silane-based, titanate-based, aluminum-based, or phosphate ester-based coupling agent.

  Various other polymer additives can be blended in the mixture of the present invention within a range not impairing the object and effects of the present invention. Examples of the polymer additive that can be blended include a colorant, a plasticizer, a lubricant, a heat stabilizer, a light stabilizer, an ultraviolet absorber, a filler, a foaming agent, a flame retardant, and a rust inhibitor. These various polymer additives are preferably added when the polymer particles and the carbon filler are dry-mixed.

The mixture of the present invention is obtained by dry-mixing polymer particles and carbon filler.
The mixing ratio of the polymer particles and the carbon filler is not particularly limited, but from the viewpoint of obtaining a structure excellent in antistatic properties, 99.5 to 90 parts by mass of the polymer and 0. The ratio is preferably 5 to 10 parts by mass.

  From the viewpoint of obtaining a structure excellent in electrical conductivity and / or thermal conductivity, the ratio is preferably 80 to 50 parts by mass of the polymer and 20 to 50 parts by mass of the carbon filler with respect to 100 parts by mass of the structure. Moreover, from a viewpoint of obtaining the structure which has electroconductivity and heat conductivity in this invention, 20-50 mass parts of carbon fillers, 0.5-30 mass parts of vapor-grown carbon fiber, and graphite powder 0-20 It is preferable to consist of a mass part and 0-30 mass parts of graphitized carbon fiber.

  Dry mixing is preferably performed at a temperature below the deflection temperature under load, melting point or glass transition temperature of the polymer particles. By this dry mixing, a carbon filler surrounds each of the polymer particles. A carbon filler is interposed between one polymer particle and another polymer particle, and the carbon filler is distributed in a three-dimensional network structure.

(Structure)
The structure of the present invention includes an A phase composed only of a polymer and a B phase containing a carbon filler as a main component. The B phase surrounds each of the A phases, and one A phase and another A phase. The B phase intervenes between the phases, and the B phase is distributed in a marble pattern.
Further, the structure of the present invention softens the polymer particles by heating the mixture at a temperature equal to or higher than the deflection temperature under load, melting point or glass transition temperature of the polymer particles, and one carbon filler and another carbon filler And a B phase containing a carbon filler as a main component, and the B phase forms a three-dimensional network structure. The heating temperature is based on the melting point for crystalline polymers, the glass transition temperature for amorphous polymers, and the deflection temperature under load when the melting point and glass transition temperature are unknown or absent.

FIG. 1 is a view showing an optical microscope image of an example of the structure of the present invention. In the figure, the black portion is a B phase containing a carbon filler as a main component, and the white portion is an A phase consisting only of a polymer.
When the cross section of the structure is observed as shown in FIG. 1, the B phase surrounds the A phase, and the B phase is distributed in a marble pattern. The B phase in the structure forms a three-dimensional network structure.
The average width of the B phase distributed in a marble pattern in a three-dimensional network structure or cross-sectional observation is usually 0.5 to 100 μm, and the size of the A phase is an average equivalent diameter, usually 0.1 to 1000 μm, preferably 1 to 500 μm.

The structure of the present invention can be obtained by pressure-molding the mixture at a pressure of 1 to 500 kgf / cm ^{2 and} a temperature higher than the deflection temperature under load, melting point or glass transition temperature of the polymer particles. FIG. 4B is a diagram schematically showing the structure of the structure. In the pressure molding, since the shearing force applied to the carbon filler is weak, the structure (FIG. 4 (2)) can be formed while maintaining the three-dimensional network structure of the mixture (FIG. 4 (1)). The holding time at the time of pressure molding is preferably 15 minutes or more.

  By using a mold having a desired shape in the pressure molding, a structure having a shape corresponding to the application can be easily obtained. Moreover, you may obtain the structure of a shape according to a use by cutting into a desired shape after press-molding.

The conductive structure of the present invention contains 99.5 to 90 parts by mass of a polymer and 0.5 to 10 parts by mass of a carbon filler with respect to 100 parts by mass of the structure, and has a volume resistivity of 10 ² to 10 ¹⁰ Ωcm. It is.
In addition, the conductive / thermally conductive structure of the present invention includes 80 to 50 parts by mass of a polymer and 20 to 50 parts by mass of a carbon filler with respect to 100 parts by mass of the structure, and has a volume resistivity of 10 ⁻⁴ to 10. ² Ωcm and the thermal conductivity is 7 W / mK or more.

  The structure of the present invention can be made into a semiconductive structure or a conductive / thermally conductive structure depending on the amount of carbon filler added. The semiconductive structure is suitable as an antistatic member or an antistatic sliding member. The antistatic member of the present invention is particularly suitable for tray applications for transporting semiconductors, semiconductor components, hard disk heads, and hard disks. Further, the antistatic sliding member of the present invention is suitable for parts used in a clean room and for manufacturing machine parts used in a clean room. The conductive and / or thermally conductive structure of the present invention is used as a conductive member and a heat-resistant sliding member, and the conductive member is suitable for a fuel cell separator. It is suitable for parts used in the above, manufacturing equipment parts used in high temperature and high load environments, OA equipment parts or automobile parts.

EXAMPLES The present invention will be described in detail below with reference to examples, but the present invention is not limited to these ranges.
Example 1
Macroscopically, 99.5 parts by mass of polyether ether ketone (PEEK) particles and 0.5 parts by mass of vapor grown carbon fiber (VGCF-S) were dry-mixed at room temperature for 10 minutes with a Henschel mixer (capacity 10 liters). A homogeneous mixture was obtained. In this mixture, as shown in FIG. 4 (1), the carbon filler surrounds each of the polymer particles, and the carbon filler is interposed between one polymer particle and another polymer particle.
This mixture was filled in a mold and subjected to pressure molding at a temperature of 360 ° C. and a pressure of 200 kgf / cm ² for 30 minutes to obtain a structure (200 × 200 × 60 mm thickness). This structure was cut into a shape necessary for various evaluation tests to obtain a test piece. The evaluation results are shown in Table 1. In this structure, the PEEK phase (white portion) and the carbon filler phase (black portion) were distributed in a marble pattern as shown in FIG. The average width of the B phase was about 10 μm, and the average equivalent diameter of the A phase was about 30 μm.

Examples 2-5
A structure was obtained in the same manner as in Example 1 except that the formulation shown in Table 1 was used. The evaluation results are shown in Table 1. In the cross section of these structures, the PEEK phase (white portion) and the carbon filler phase (black portion) were distributed in a marble pattern as shown in FIG.
Examples 6-8
A structure was obtained in the same manner as in Example 1 except that the temperature at the time of pressure molding was changed to 310 ° C. instead of the formulation shown in Table 1. The evaluation results are shown in Table 1. In these structures, the PPS phase (white portion) and the carbon filler phase (black portion) were distributed in the same marble pattern as in Example 1.
Examples 9-10
A structure was obtained in the same manner as in Example 1 except that the temperature at the time of pressure molding was changed to 500 ° C. instead of the formulation shown in Table 1. The evaluation results are shown in Table 1. In these structures, the PBI phase (white portion) and the carbon filler phase (black portion) were distributed in the same marble pattern as in Example 1.

Comparative Example 1
93 parts by mass of polyetheretherketone (PEEK) particles and 7 parts by mass of vapor grown carbon fiber (VGCF-S) were kneaded at 360 ° C. using the same direction twin screw extruder, and then injection molded at 380 ° C. A body (100 × 100 × 3 mm thick, film gate) was obtained. The molded body was cut into a shape necessary for various evaluation tests to obtain a test piece. The evaluation results are shown in Table 2. In the transmission electron microscope image of this molded product, as shown in FIG. 3, the carbon filler was uniformly dispersed in the polymer matrix.
Comparative Examples 2-3
A structure was obtained in the same manner as in Comparative Example 1 except that the formulation shown in Table 2 was used. The evaluation results are shown in Table 2. In this molded body, the carbon filler was uniformly dispersed in the polymer matrix.
Comparative Examples 4-5
A molded body was obtained in the same manner as in Comparative Example 1 except that it was mixed at 310 ° C. and injection molded at 320 ° C. instead of the formulation shown in Table 2. The evaluation results are shown in Table 2. In this molded body, the carbon filler was uniformly dispersed in the polymer matrix. As shown in the transmission electron microscope image of this molded product, the carbon filler was uniformly dispersed in the polymer matrix.

Examples 11-15
A structure was obtained in the same manner as in Example 1 except that the formulation shown in Table 3 was used. The evaluation results are shown in Table 3. In these structures, a PEEK phase (white portion) and a carbon filler phase (black portion) were distributed in a marble pattern.
Examples 16-18
A structure was obtained in the same manner as in Example 1 except that the temperature at the time of pressure molding was changed to 310 ° C. instead of the formulation shown in Table 3. The evaluation results are shown in Table 3. In these structures, a PPS phase (white portion) and a carbon filler phase (black portion) were distributed in a marble pattern.
Examples 19-21
A structure was obtained in the same manner as in Example 1 except that the temperature at the time of pressure molding was changed to 220 ° C. instead of the formulation shown in Table 3. The evaluation results are shown in Table 3. In these structures, a PP phase (white portion) and a carbon filler phase (black portion) were distributed in a marble pattern.

Comparative Example 6
70 parts by mass of polyether ether ketone (PEEK) particles and 30 parts by mass of vapor grown carbon fiber (VGCF-S) are kneaded at 360 ° C. using the same direction twin screw extruder, and then injection molded at 380 ° C. to form. A body (100 × 100 × 3 mm thick, film gate) was obtained. The molded body was cut into a shape necessary for various evaluation tests to obtain a test piece. The evaluation results are shown in Table 4. As shown in FIG. 2, in this molded body, the carbon filler was uniformly dispersed in the polymer matrix.
Comparative Examples 7-8
A structure was obtained in the same manner as in Comparative Example 6, except that the formulation shown in Table 4 was used. The evaluation results are shown in Table 4. In this molded body, the carbon filler was uniformly dispersed in the polymer matrix.

The carbon fillers used in the examples and comparative examples are as follows.
[Vapor grown carbon fiber]
A) VGCF (registered trademark): Showa Denko's vapor grown carbon fiber (average fiber diameter: 150 nm, average fiber length: 10 μm, specific surface area: 13 m ² / g, aspect ratio: 67, I ₀ = 0.2) used.
B) VGCF-S: Showa Denko vapor phase carbon fiber (average fiber diameter: 100 nm, average fiber length: 11 μm, specific surface area: 20 m ² / g, aspect ratio: 110, I ₀ = 0.2) was used. .
〔Carbon fiber〕
Graphitized carbon fiber Grade name: XN-100 (chopped fiber) manufactured by Nippon Graphite Fiber Co., Ltd. [ graphite]
Grade name: UFG-30 Showa Denko

The polymer particles used in the examples and comparative examples are as follows.
1) PEEK
Grade name: 450P Victrex MC, Inc. Average particle size 20 μm, melting point 343 ° C.
2) PPS
Grade name: LD-10 Dainippon Ink Co., Ltd. average particle size 20 μm, melting point 280 ° C.
3) PBI
100MESH POLYMER PBI PERFORMANCE PRODUCTS, INC. Average particle size 20 μm, deflection temperature under load 435 ° C. (ASTM D-648, load 1.82 MPa)
4) PP
Grade name: PM801A (homo) Sun Allomer's average particle size 20 μm, melting point 160 ° C.

Measurement method of physical properties of evaluation 1) Volume resistivity Based on JIS K7194, it was measured by a four-probe method.
2) Measured by notched Izod impact test ASTM D256.
3) Thermal conductivity A rapid thermal conductivity meter manufactured by Kyoto Electronics Industry Co., Ltd. was used and measured by a hot wire method.

It is a figure which shows the optical microscope image of an example of the structure (dry mixing and pressure molding) of this invention. It is a figure which shows the SEM image of the molded article which melt-kneaded and compression-molded the polymer and the carbon filler. It is a figure which shows the TEM image of the molded article which melt-kneaded and injection-molded the polymer and the carbon filler. (A) is the figure which showed the mixture of this invention typically, (B) is the figure which showed the structure of this invention typically.

Explanation of symbols

A: polymer phase; B: carbon filler phase;

Claims (24)

The polymer particles and the carbon filler are dry mixed to obtain a mixture in which the carbon filler is present on at least a part of the surface of the polymer particles and the carbon filler is interposed between one polymer particle and the other polymer particle,
By pressing the mixture at a pressure of 1 to 500 kgf / cm ^{2 and at} a temperature higher than the deflection temperature, melting point or glass transition temperature of the polymer particles, the polymer particles are softened, and one carbon filler and another carbon Soaking the softening polymer in the gap with the filler,
And a B phase mainly containing A-phase and the carbon filler consisting of only the polymer and the carbon filler B phase forms a three-dimensional network structure is intended to include carbon fibers, the manufacturing method of the structure. 2. The method for producing a structure according to claim 1 , wherein the polymer particles are particles composed of at least one polymer selected from the group consisting of a thermoplastic resin, a thermoplastic elastomer, an uncrosslinked thermosetting resin, and an uncrosslinked elastomer. . The method for producing a structure according to claim 1 or 2 , wherein the polymer particles have an average particle diameter of 1 µm to 500 µm. Method for manufacturing a structure according to any one of claims 1 to 3 carbon filler is one that further comprises at least one selected from carbon black and graphite or Ranaru group. The carbon fiber is a vapor grown carbon fiber,
The vapor grown carbon fiber has an average fiber diameter of 20 to 500 nm, an aspect ratio of 20 to 1000, a BET specific surface area of 4 to 100 m ² / g, an X-ray diffraction d ₀₀₂ of 0.345 nm or less, and a Raman scattering spectrum. the ratio of the peak height of the band 1341~1349cm ^-1 (I _d) and the band peak height _{^{1570~1578cm -1 (I g): (}} I d / I g) is 0.1 to 2 The manufacturing method of the structure as described in any one of Claims 1-4 . The carbon fiber is a vapor grown carbon fiber,
The method for producing a structure according to any one of claims 1 to 4 , wherein the vapor grown carbon fiber is heat-treated at a temperature of 2000 to 3500 ° C in an inert atmosphere. The method for producing a structure according to claim 5 or 6 , wherein the vapor grown carbon fiber has an average fiber diameter of 50 to 200 nm. The method for producing a structure according to any one of claims 1 to 7 , wherein a holding time during pressure molding is 15 minutes or more. The method for manufacturing a structure according to any one of claims 1 to 8, further comprising cutting into a desired shape after the pressure forming. The method for manufacturing a structure according to any one of claims 1 to 9, wherein pressure molding is performed using a mold having a desired shape. The manufacturing method of the structure as described in any one of Claims 1-10 which performs dry mixing at the temperature below load deflection temperature of polymer particle, melting | fusing point, or glass transition temperature. The volume resistivity is determined by the method according to any one of claims 1 to 11, using 99.5 to 90 parts by mass of polymer particles and 0.5 to 10 parts by mass of carbon filler with respect to 100 parts by mass of the structure. The manufacturing method of a semiconductive structure including the process of manufacturing the structure which is ¹⁰ < ² > -10 < ¹⁰ > (omega | ohm) cm. The volume resistivity is 10 ⁻⁴ to 10 ⁻⁴ by the method according to claim 1, using 80 to 50 parts by mass of polymer particles and 20 to 50 parts by mass of carbon filler with respect to 100 parts by mass of the structure. method for producing a conductive and / or thermally conductive structure including a step of 10 且 one thermal conductivity ² [Omega] cm to produce a structure is 7W / mK or more. The conductive material according to claim 13 , wherein 20 to 50 parts by mass of carbon filler comprises 0.5 to 30 parts by mass of vapor grown carbon fiber, 0 to 20 parts by mass of graphite powder, and 0 to 30 parts by mass of graphitized carbon fiber. For manufacturing a conductive and / or thermally conductive structure. Method for producing an antistatic member comprising a step of producing a semiconducting structure by the production method according to claim 12. Semiconductor including the steps of producing a semi-conductive structure by the production method according to claim 12, a semiconductor component, a hard disk head, or a manufacturing method of the antistatic member tray for conveying the hard disk. Method for producing antistatic sliding member comprising a step of producing a semiconducting structure by the production method according to claim 12. The manufacturing method of the antistatic sliding member for components used in the clean room including the process of manufacturing a semiconductive structure with the manufacturing method of Claim 12 . The manufacturing method of the antistatic sliding member for manufacturing machine parts used in the clean room including the process of manufacturing a semiconductive structure by the manufacturing method of Claim 12 . Method for producing a conductive member including a step of producing a conductive and / or thermally conductive materials by the production method according to claim 13 or 14. Method for producing a conductive member for a separator of a fuel cell comprising a step of producing a conductive and / or thermally conductive materials by the production method according to claim 13 or 14. Method for producing a heat-resistant sliding member comprising a step of producing a conductive and / or thermally conductive materials by the production method according to claim 13 or 14. Method for producing a heat-resistant sliding member for components used in high temperature and high load environments, including the step of producing a conductive and / or thermally conductive materials by the production method according to claim 13 or 14. A heat-resistant slide for manufacturing equipment parts, OA equipment parts, or automobile parts used in a high-temperature and high-load environment including a step of manufacturing a conductive and / or thermally conductive structure by the manufacturing method according to claim 13 or 14. Manufacturing method of moving member.

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