PRODUCTION OF ALUMINIUM NITRIDE POWDER BY CARBOREDUCTIVE NITRIDATION

Abstract: Alumina powder, e.g. ≦ 5 µm diameter, and carbon powder, preferably acetylene black eg. ≦ 1 µm, are admixed, e.g. in an aqueous slurry followed by drying; the carbon is present in molar excess, preferably the C:Al₂O₃ ratio is 3-10:1. The mixture is heated in a nitrogen atmosphere at 1500-1700°C for 2-10 hours to make aluminium nitride. To remove excess C, the product is further heated in air at 600-750°C, before or after being pulverized, to a BET specific surface area ≦ 6 m² to contain not more than 50% of powder < 1 µm diameter, preferably in dry air or N. Thus a powder of a tapped density 1.0. /cm³ is obtained. There may then be added 0.01-10 wt % of a sintering aid and 0.05-2 wt % of an oleophilic dispersant, to give a powder containing 0.05-10% of the sintering aid and having an oleophilic surface. The apparatus used should be non-metallic. A product of low Fe, Si and Ti impurity content is thus obtained and which can be sintered satisfactorily to make pore-free bodies of high thermal conductivity.

Description: The present invention relates to an aluminum nitride powder with excellent moldability, which has a high tapped density; has less formation of coagulated particles, and which has a sharp particle size distribution and a process for preparation of the same. Alumina has hitherto been used as an IC packaging material or substrate material. However, with the increasing integration, speed and output power of, e.g., LSI, it has become necessary to efficiently dissipate heat generated in a chip out of the system, and materials which have higher thermal conductivity and more excellent heat dissipation than alumina are being demanded. Since aluminum nitride not only has high thermal conductivity but is excellent in electrical characteristics such as insulation resistance, dielectric strength and dielectric constant and mechanical characteristics such as strength, it is now attracting special attention as a packaging material or substrate material best adapted for heat dissipation. For preparation of aluminum nitride powder, there have hitherto been known the following two nitriding methods: (1) a direct nitriding method of nitriding a metallic aluminum powder by heating in a nitrogen-containing atmosphere, and (2) a reductive nitriding method of heating a mixture of alumina or alumina hydrate and carbon in a nitrogen-containing atmosphere. A process to produce AlN-powder starting from a mixture of carbon on alumina in a a molar ratio of about 3:1 to 9:1 is described in EP-A- 0 176737 and GB-A-2127390. Carbon and alumina are reacted in a nitrogen atmosphere and the excess of carbon is removed by heating the reaction product at a temperature comprised between 600° and 750°C Although the aluminium nitride powder obtained by the former method is a readily moldable powder having a high tapped density, it contains relatively high amounts of cation impurities such as iron and, hence, it is not always satisfactory in order to obtain a sintered body having high thermal conductivity. Accordingly, the aluminum nitride powder synthesized by the latter reductive nitriding method is most likely to be used for obtaining high thermal conductivity substrates. However, though the aluminum nitride powder obtained by the reductive nitriding method has the advantage that the amounts of oxygen and cation impurities such as iron are low, it has a low tapped density so that it is hard to be molded. In addition, the aluminum nitride powder is readily hydrolyzable and so special care is needed in its storage and handling. Moreover, since the surface of the aluminum nitride powder is usually oxidized or hydrolyzed whereby it is covered by a very thin oxide film layer, even when the aluminum nitride powder is sintered under atmospheric pressure as it is, a high thermal conductivity sintered body cannot be obtained. Therefore, the aluminum nitride powder is usually sintered after addition of a compound such as calcium carbonate, strontium carbonate, or yttrium oxide, whereby a high thermal conductivity sintered material is obtained. However, this method involves a problem that it is not easy to uniformly mix and disperse such a compound added, because the surface characteristics of the aluminum nitride powder are not always identical to those of the compound added. Furthermore, the aluminum nitride powder is so bulky that if the tapped density is low, it is difficult to not only disperse it in a solvent but also obtain a highly dense molded article therefrom. Thus, the degree of shrinkage is high during sintering, and a sintered material with good dimensional precision can hardly be obtained. Still further, if the mixing and dispersion of the aluminum nitride powder and additive powder are insufficient and the homogeniety is poor, the sintering may not uniformly proceed so that the shrinkage during the sintering is not uniform, resulting in easy formation of warpage of a sintered body or occurrence of anisotropy of the shrinkage. The present invention is intended to solve the defects which the powder obtained by the reductive nitriding method involves and relates to the production of an aluminum powder with excellent moldability, which contains small amounts of cation impurities, has a high tapped density, has less formation of coagulated particles, and which has a sharp particle size distribution, and a process for preparation of the same. According to the present invention we provide a reductive nitriding process for preparing an aluminum nitride powder, by heating a powdered mixture of alumina and carbon in a nitrogen-containing atmosphere, in which an excess of carbon is used in the reaction and the reaction product is further heated in air at a temperature of 600 to 750°C to remove the excess carbon, characterised in that the reaction product is pulverized after said further heating, and the obtained aluminum nitride powder has a tapped density of at least 1.0 gram/cubic centimeter. Preferably, the molar ratio of the carbon to alumina in the reaction mixture is from 3:1 to 10:1. The reaction product may be mixed with 0.01 to 10 wt% of a sintering aid and 0.05 to 2 wt% of a dispersing agent containing an oleophilic group in its molecule, before the further heating in air. The powder obtained preferably has a weight content of oxygen of not more than 2.0%, iron not more than 20 ppm, silicon not more than 100 ppm and titanium not more than 20 ppm. It is known that the presence of oxygen, iron, silicon and titanium contained in a raw material powder for the preparation of the aluminum nitride powder is likely to reduce the thermal conductivity of a sintered body obtained by use of this raw material powder. Such a tendency is more likely observed as the content of these impurities increases. Accordingly, in order to stably attain a high thermal conductivity of at least 180 W/mK through sintering by using yttrium oxide as a sintering aid, it is required that the foregoing impurities be not present in amounts exceeding certain limits. In accordance with a reductive nitriding method, it is easy to synthesize a high-purity powder having an oxygen content of not more than 2.0% by weight, an iron content of not more than 20 ppm, a silicon content of not more than 100 ppm and a titanium content of not more than 20 ppm. However, at present according to the conventional reductive nitriding method, only a powder having a tapped density of at most about 0.8 g/cm³ is obtainable. The present invention can provide a high-purity aluminum nitride powder having a tapped density of at least 1.0 g/cm³. If the tapped density is too low, the tightness during the molding is not satisfactory so that a highly dense molded article can hardly be obtained. Further, the degree of shrinkage during the sintering increases so that a sintered body having good dimensional precision can hardly be obtained. Still further, there is a problem that in adding the aluminum nitride powder as a highly thermal conductive filler to a high molecular weight material such as rubbers or resins, the filling properties are inferior. In particular, if the tapped density is less than 1.0 g/cm³, for example, it is impossible to contain 20 kg of such a powder in a 20-liter vessel so that a special vessel is required. The oleophilicity of the aluminum nitride powder can be imparted by introducing oleophilic groups into the surface thereof. While the method for introducing oleophilic groups into the surface of the aluminum nitride powder will be described later in detail, it can be done by subjecting the aluminum nitride powder to a wet or dry contact treatment together with from 0.01 to 10% by weight of a sintering aid and a dispersing agent containing therein an oleophilic group. When such oleophilic groups are introduced into the surface of the aluminum nitride powder, the water resistance and hydrolysis resistance of the aluminum nitride powder are markedly improved. In addition, if the tapped density of the aluminum nitride powder is at least 1.0 g/cm³, it becomes easy to obtain a highly dense molded article. As a result, the degree of shrinkage during the sintering becomes low so that a sintered body having good dimensional precision can be readily obtained. Now, the preparation processes according to the present invention are described. First of all, an aluminum nitride powder is synthesized by reacting a mixture of an alumina powder and a carbon powder in a nitrogen-containing atmosphere at from 1,500 to 1,700°C for from 2 to 10 hours in the reductive nitriding method. As the alumina powder which is used as one of the staring materials in the present invention, not only those produced by the Bayer method, which are most commonly commercially available, but also those produced by various other methods can be used. The alumina powder preferably has an average particle diameter of not more than 5 µm and more preferably not more than 3 µm. However, it is preferred to use an alumina powder having low contents of metal impurities which are hardly volatile during the reductive nitriding reaction, such as silicon and titanium. Further, it is preferred that the carbon powder which is another starting material used in the present invention is a fine powder having a purity as high as possible. More preferably, the carbon powder has a particle diameter of primary particle of not more than 1 µm and an ash content of not more than 0.3% by weight. Examples of the carbon powder which can be used include acetylene black, channel black, and furnace black. Among them is preferred acetylene black from the viewpoint of high purity. Further, if subsequent dispersion is to be readily achieved, it is advantageous to use those which have been granulated to a size of from 0.3 to 1.5 mm or those which have been compressed in a powder state, from the viewpoint of handling. As the method for mixing and dispersing the alumina powder and carbon powder, there are employable usual methods such as a ultrasonic dispersion method as well as those using various mixing apparatus such as a ball mill and a vertical granulator. It is desired that parts of such apparatus which are brought into direct contact with the starting materials are constructed from a material into which metal impurities are not incorporated. As such a material, synthetic resins such as polyethylene, nylon and polyurethane, natural or synthetic rubbers, and alumina or aluminum nitride can be suitably used. Also, those lined or coated with the foregoing materials are suitable. As the method for drying the mixture, usual industrial methods can be employed. However, if the slurry concentration during the mixing is low, resulting in likely causing, for example, separation of the alumina powder from the carbon powder during the drying, it is preferred to employ spray drying, freeze drying, or a method using a rotary evaporator. Further, if desired, in addition to the mixing and drying, granulation of the particles to a size of from about 20 µm to 3 mm can be carried out. In this case, there is an advantage from the viewpoint of easiness in handling during the subsequent operations. In order to easily complete the reductive nitriding reaction, the amount of the carbon powder which is reacted is usually at least equivalent to that of the alumina powder which is also reacted. A mixing ratio of the alumina powder and carbon powder is preferably from 3 to 10 and more preferably from 3.2 to 7 in terms of a carbon/alumina molar ratio. If the molar ratio is less than 3, unreacted alumina remains. On the other hand, if it exceeds 10, not only it is difficult to remove the carbon in the subsequent stage, but such is not preferred from the economical viewpoint. Accordingly, the reaction product obtained by the reductive nitriding reaction is usually a mixture of the aluminum nitride powder and excessive carbon powder. This mixture is fired in dry air at from 600 to 750°C to calcine and remove the excessive carbon, whereby an aluminum nitride powder is obtained. The aluminum nitride powder obtained by these steps is a powder containing small amounts of coagulated particles and having a low tapped density. In the present invention, the mixture of the aluminum nitride powder and excess carbon powder obtained by the above-described reductive nitriding reaction is pulverized and then fired in air at from 600 to 750°C to calcine and remove the excessive carbon, whereby an aluminum nitride powder having a high tapped density, which is less in formation of coagulated particles, is obtained. In the present invention, the mixture of the aluminum nitride powder and excessive carbon powder obtained by the above-described reductive nitriding reaction is fired in air at from 600 to 750°C to calcine and remove the excessive carbon and then pulverized, whereby an aluminum nitride powder having a high tapped density, which is less in formation of coagulated particles, is obtained. For achieving the pulverizing, usual mills such as a ball mill, a vibrating mill, and a jet mill can be used. However, the aluminum nitride powder is readily hydrolyzable so that its oxygen content tends to increase during the pulverizing stage. Further, if a BET specific surface area increases due to the pulverizing, or the content of fine powders having a size of less than 1 µm increases, the surface of the aluminum nitride powder is likely oxidized, resulting in an increase in oxygen content. Accordingly, the pulverizing must be carried out such that the BET specific surface area be not more than 6 m² and that the content of fine powders having a size of less than 1 µm be not more than 50% and preferably not more than 30%. Further, the pulverizing is preferably carried out in dry air or a dry nitrogen gas for a period of time as short as possible. Usually, the pulverizing is preferably carried out in dry air or a dry nitrogen gas for a period of time as short as possible by the addition of a suitable amount of a pulverizing aid such as methanol, oleic acid, lauric acid, calcium stearate, and arylalkyl sulfones for increasing the pulverizing efficiency. Moreover, since contamination by metal impurities such as iron and silicon arises depending on the materials for the pulverizing apparatus and pulverizing medium, it is preferred to use those made of aluminum nitride or alumina or those lined or coated with plastics or rubbers. In another embodiment of the present invention, the aluminum nitride powder obtained by the above-described reductive nitriding reaction is mixed with from 0.01 to 10% by weight of a sintering aid and further with from 0.05 to 2.0% by weight of a dispersing agent containing therein an oleophilic group to effect a dry contact treatment, whereby an aluminum nitride powder containing from 0.5 to 10% by weight of the sintering aid, having an oleophilic surface, and having a tapped density of at least 1.0 g/cm³ is obtained. The aluminum nitride powder used herein is one obtained by the above-described reductive nitriding reaction but preferably has an oxygen content of not more than 2.0% by weight, an iron content of not more than 80 ppm, a silicon content of not more than 150 ppm and a titanium content of not more than 30 ppm, from the standpoint of obtaining a high thermal conductivity sintered body. As the sintering aid, any of those which have been proposed can be used without specific limitations. Preferably, one or more of alkaline earth metal compounds, yttrium compounds and rare earth metal compounds can be used. Most preferably, one or more compounds selected from calcium carbonate, strontium carbonate, and yttrium oxide can be used. A suitable amount of the sintering aid used is in the range of from 0.01 to 10% by weight. If the amount is less than 0.01% by weight, there is no effect of improving the sintering properties and thermal conductivity of the sintered body. On the other hand, if the amount exceeds 10% by weight, though an effect for improving the sintering properties is obtained, a high amount of the sintering aid component remains in the sintered body so that a high thermal conductivity sintered body cannot be obtained. Further, the sintering aid preferably has an average particle diameter of not more than 3 µm. Examples of the dispersing agent containing therein an oleophilic group which can be used in the present invention include higher fatty acids containing from 10 to 18 carbon atoms, such as decanoic acid, dodecanoic acid, and oleic acid, and salts thereof (the term "salt of acid" referred to herein means a salt of ammonium, Na, K, Mg, Ca, Sr, Al, or Y); sulfuric acid ester salts of higher alcohols containing from 10 to 18 carbon atoms, such as decyl sulfate and dodecyl sulfate; alkylarylsulfonic acid ester salts in which the alkyl moiety thereof contains from 10 to 18 carbon atoms, and the aryl moiety thereof contains 6 or 12 carbon atoms, such as dodecylbenzenesulfonic acid; dialkylsulfosuccinic acid salts in which the alkyl moiety thereof contains from 4 to 12 carbon atoms, such as di-2-ethylhexylsulfosuccinate; polyoxyethylene alkylsulfuric acid ethers in which the alkyl moiety thereof contains from 10 to 18 carbon atoms, and the molar number of ethylene oxide added is from 7 to 13, such as polyoxyethylene decyl ether sulfuric acid salt; polyoxyethylene higher alcohol ethers in which the alcohol moiety thereof contains from 10 to 18 carbon atoms, and the molar number of ethylene oxide added is from 7 to 13, such as polyoxyethylene decyl ether; polyoxyethylene alkylphenol ethers in which the alkyl moiety thereof contains from 8 to 18 carbon atoms, and the molar number of ethylene oxide added is from 7 to 13, such as polyoxyethylene octylphenol ether; sorbitan higher fatty acid esters in which the higher fatty acid moiety thereof contains from 10 to 18 carbon atoms, such as sorbitan decanate and sorbitan oleate; polyoxyethylene sorbitan fatty acid esters in which the higher fatty acid moiety thereof contains from 10 to 18 carbon atoms, and the molar number of ethylene oxide added is from 7 to 13, such as polyoxyethylene sorbitan decanate and polyoxyethylene sorbitan oleate; polyoxyethylene higher fatty acid esters in which the higher fatty acid moiety thereof contains from 10 to 18 carbon atoms, and the molar number of ethylene oxide is from 7 to 13, such as polyoxyethylene decanate; glycerin higher fatty acid esters in which the higher fatty acid moiety thereof contains from 10 to 18 carbon atoms, such as dodecanoic acid glyceride, octadecanoic acid glyceride, and oleic acid glyceride; higher alkylamine acetic acid salts in which the alkyl moiety thereof contains from 10 to 18 carbon atoms, such as decylamine acetate; polyoxyethylene alkylamines in which the alkyl moiety thereof contains from 10 to 18 carbon atoms, and the molar number of ethylene oxide added is from 7 to 13, such as polyoxyethylene decylamine; phosphoric acid esters of a C₁₀-C₁₈ higher fatty acid, such as lecithin; and organoaluminum coupling agents such as acetoalkoxyaluminum diisopropylates. These compounds can be used alone or in admixture. The dispersing agent containing therein an oleophilic group can be used as it is or in the state dissolved or dispersed in a suitable solvent. Though the amount of the dispersing agent containing therein an oleophilic group varies depends on the surface area of the aluminum nitride powder used or the nature of the dispersing agent, it is suitably in the range of from 0.05 to 2.0% by weight. If the amount is less than 0.05% by weight, an effect for rendering the surface of the aluminum nitride powder oleophilic does not substantially reveal. On the other hand, if it exceeds 2.0% by weight, not only the surface of the aluminum nitride powder is tacky, but such is not economically preferred. As the method for introducing oleophilic groups, it is preferred to choose a dry contact treatment method in which the foregoing dispersing agent containing therein an oleophilic group or a solution thereof is added to the aluminum nitride powder and sintering aid, followed by mixing and pulverizing in a ball mill or the like. Though the oleophilic groups can be introduced by a wet contact treatment method in which the aluminum nitride powder and sintering aid are dispersed in a solution of the dispersing agent containing therein an oleophilic group, since this method requires a drying step, it is not always an economically suitable method. Further, according to this wet method, it is difficult to obtain a powder having a high tapped density. The dry contact treatment method can be carried out by means of an apparatus used for the usual decoagulating or pulverizing, such as a ball mill, a vibrating mill, and a jet mill. However, the aluminum nitride powder is readily hydrolyzable so that its oxygen content tends to increase during the dry contact treatment stage. Accordingly, the dry contact treatment is preferably carried out in dry air or a dry nitrogen gas for a period of time as short as possible. Moreover, since contamination by metal impurities such as iron and silicon depends on the materials of the pulverizing apparatus and pulverizing medium, it is preferred to use those made of aluminum nitride or alumina or those lined or coated with plastics or rubbers. The aluminum nitride powder obtained in the present invention is a powder which has low contents of oxygen, iron, silicon and titanium, has a low amount of coagulated particles, has a high tapped density, and which is excellent in moldability. When this powder is used, not only the degree of shrinkage during the sintering can be reduced, but also a highly dense sintered body which does not substantially contain pores and which has a high thermal conductivity can be readily obtained. Further, according to the present invention, when the aluminum nitride powder is brought into contact with a dispersing agent containing therein an oleophilic group in the presence of a dry sintering aid, an aluminum nitride powder with good dispersion between the aluminum nitride powder and the sintering aid can be obtained. The resulting aluminum nitride powder is a readily sintering aluminum nitride powder having an oleophilic surface, which is substantially freed of formation of coagulated particles, has a high tapped density, and which is excellent in hydrolysis resistance and moldability. When this powder is used, not only the degree of shrinkage during the sintering can be reduced, but also a highly dense sintered body which does not substantially contain pores and which has a high thermal conductivity can be readily obtained. Accordingly, the present invention can provide a starting material useful for production of high thermal conductivity aluminum nitride sintered bodies. The present invention is hereunder described specifically with reference to Examples and Comparative Examples. EXAMPLE 1 2600 g of ion exchange water having dissolved therein 306 g of a low-sodium content alumina powder (purity: 99.9%, an average particle diameter measured by sedigraph: 0.7 µm, content of particles having a particle diameter of not more than 1 µm: 80%), 216 g of a 100% pressed product of acetylene black having an ash content of 0.005%, 11.3 g of aluminum nitrate [Al(NO₃)₃·9H₂O], 5.2 g of polyethylene glycol, and 15.1 g of a nonionic surfactant comprising polyoxyethylene alkylphenyl ethers (Noigen® EA137, a trade name of Dai-ichi Kogyo Seiyaku Co., Ltd.) was charged in a polyethylene-made pot together with 600 pieces of nylon balls having a diameter of 15 mm and wet mixed at a revolution rate of 40 rpm for 10 hours. The thus obtained mixed slurry was dried in a dryer. 500 g of the dried slurry was weighed on a graphite-made tray and subjected to reductive nitriding reaction upon firing at 1,580°C for 7 hours while flowing a nitrogen gas at a rate of 200 cm/min in an electric furnace. Thereafter, 150 g of the reaction product was taken into a 2-liter polyethylene-made pot, and 2.5 kg of alumina-made balls having a diameter of 15 mm and 1.5 g of lauric acid were added thereto. After thoroughly purging the pot with a nitrogen gas, the mixture was subjected to dry ball mill pulverizing at a revolution rate of 60 rpm for 3 hours. The pulverized material was further fired in dry air at 700°C for 3 hours to calcine and remove excessive carbon, whereby an aluminum nitride powder was obtained. Various physical properties of this aluminum nitride powder are shown in Table 1. This powder was a high-purity fine powder which is substantially freed of the formation of coagulated particles and which has a sharp particle size distribution. The measurements of oxygen content, metal ion content, particle size distribution, and bulk density and tapped density were carried out by the impulse heat infrared absorption method (Model TC-436 of an oxygen-nitrogen simultaneous analysis apparatus manufactured by LECO Corp.), the ICP emission spectroscopic analysis method (Quantolet GQM-75 manufactured by Shimadzu Corporation), the sedigraph (Sedi Graph 5000ET manufactured by Micromeritics Corp.), and the method according to JIS H-1902, respectively. The respective measurements in the following Examples and Comparative Examples were carried out in the same manners as those described above. To this powder were added as sintering aids 1% by weight, calculated as CaO, of calcium carbonate and 3% by weight, of yttrium oxide, and the mixture was press molded under a pressure of 1,500 kg/cm² to give a molded article. The molded article was embedded in a mixed powder of aluminum nitride and boron nitride and sintered at 1,850°C for 3 hours under atmospheric pressure. The molded article had a high relative density of 58.5% and showed a low degree of shrinkage as 16% during the sintering. Further, the resulting sintered body was a pore-free sintered body and showed a high thermal conductivity of 200 W/mK. The measurement of the thermal conductivity was carried out by the laser flash method (Model TC-7000 manufactured by Shinku Riko K.K.). The measurement of the thermal conductivity in the following Examples and Comparative Examples was carried out in the same manner as that described above. EXAMPLE 2 A reaction product of an aluminum nitride powder and a carbon powder was obtained by undergoing the same reductive nitriding reaction as in Example 1, except that a usual alumina powder obtained the Bayer method (purity: 99.7%, an average particle diameter: 0.6 µm, content of particles having a particle diameter of not more than 1 µm: 80%) was used as the alumina starting material. Thereafter, this reaction product was fired in dry air at 700°C for 3 hours to calcine and remove excessive carbon, whereby an aluminum nitride powder was obtained. 150 g of this aluminum nitride powder was taken into a 2-liter polyethylene-made pot, and 2.5 kg of alumina-made balls having a diameter of 15 mm and 1.5 g of methanol were added thereto. After thoroughly purging the pot with dry air, the mixture was subjected to dry ball mill pulverizing at a revolution of 60 rpm for 3 hours. Various physical properties of this aluminum nitride powder are shown in Table 1. This powder was a high-purity fine powder which is substantially freed of the formation of coagulated particles and which has a sharp particle size distribution. The resulting powder was molded and sintered in the same manner as in Example 1, to form a molded article. The molded article had a high relative density of 59% and showed a low degree of shrinkage as 16% during the sintering. Further, the resulting sintered body showed a high thermal conductivity as 205 W/mK. COMPARATIVE EXAMPLE 1 2600 g of ion exchange water having dissolved therein 306 g of a low-sodium content alumina powder (purity: 99.9%, an average particle diameter measured by sedigraph: 0.7 µm, content of particles having a particle diameter of not more than 1 µm: 80%), 216 g of a 100% pressed product of acetylene black having an ash content of 0.005%, 11.3 g of aluminum nitrate [Al(NO₃)₃·9H₂O], 5.2 g of polyethylene glycol, and 15.1 g of a nonionic surfactant comprising polyoxyethylene alkylphenyl ethers (Noigen® EA137, a trade name of Dai-ichi Kogyo Seiyaku Co., Ltd.) was charged in a polyethylene-made pot together with 600 pieces of nylon balls having a diameter of 15 mm and wet mixed at a revolution rate of 40 rpm for 10 hours. The thus obtained mixed slurry was dried in a dryer. 500 g of the dried slurry was weighed on a graphite-made tray and subjected to reductive nitriding reaction upon firing at 1,580°C for 7 hours while flowing a nitrogen gas at a rate of 200 cm/min in an electric furnace. This reaction product was then fired in dry air at 700°C for 3 hours to calcine and remove excessive carbon, whereby an aluminum nitride powder was obtained. Various physical properties of this aluminum nitride powder are shown in Table 1. This powder was a high-purity fine powder in which coagulated particles were slightly present. The resulting powder was molded and sintered in the same manner as in Example 1, to form a molded article. The molded article had a relative density of 52% and showed a high degree of shrinkage of 20% during the sintering. Further, the resulting sintered body showed a high thermal conductivity of 195 W/mK. Example 1 Example 2 Comparative Example 1 Oxygen content (%) 1.3 1.2 1.3 Iron content (ppm) 8 9 8 Silicon content (ppm) 56 36 52 Titanium content (ppm) 13 14 13 Average diameter (µm) 1.3 1.4 1.7 Content of particles of greater than 2 µm (%) 15 14 42 Content of particles of greater than 1 µm (%) 13 14 12 Bulk density (g/cm³) 0.6 0.6 0.3 Tapped density (g/cm³) 1.2 1.5 0.6 EXAMPLE 3 The reaction product obtained by the reductive nitriding reaction in Example 1 was fired in dry air at 700°C for 3 hours to calcine and remove excessive carbon, whereby an aluminum nitride powder (a) was obtained. Various physical properties of this aluminum nitride powder are shown in Table 2. This aluminum nitride powder was a high-purity fine powder which is relatively low in formation of coagulated particles. Then, 150 g of this powder and, as sintering aids, 2 g of a calcium carbonate powder and 4.5 g of an yttrium oxide powder were taken into a 2-liter polyethylene-made pot, and 2.5 kg of alumina-made balls having a diameter of 15 mm and, as a dispersing agent containing therein an oleophilic group, 1.5 g of oleic acid were added thereto. After thoroughly purging the pot with dry air, the mixture was subjected to dry ball mill pulverizing at a revolution rate of 60 rpm for 3 hours. Various physical properties of the resulting powder are shown in Table 2. This powder was a fine powder which is substantially freed of the formation of coagulated particles and which has a sharp particle size distribution. Further, this powder was not at all compatible with water. Then, this powder was dispersed in an aqueous solution of a nonionic surfactant (Tween® 60, a product of Nakarai Chemical Co., Ltd.), and its hydrolyzability was examined. As the result, even after immersing for 90 days, the pH value did not change from the initial value of 6.1 so that it had remarkably improved hydrolysis resistance. Further, this powder was press molded at 1,500 kg/cm² to form a molded article which was then embedded in a mixed powder of aluminum nitride and boron nitride and sintered in a nitrogen atmosphere at 1,900°C for 3 hours under atmospheric pressure. The molded article had a high relative density of 58.5% and showed a low degree of shrinkage of 16% during the sintering. Further, the resulting sintered body was a pore-free sintered body and showed a high thermal conductivity of 200 W/mK. EXAMPLE 4 The reaction product obtained by the reductive nitriding reaction in Example 2 was fired in dry air at 700°C for 3 hours to calcine and remove excessive carbon, whereby an aluminum nitride powder (b) was obtained. Various physical properties of this aluminum nitride powder are shown in Table 2. This aluminum nitride powder was a high-purity fine powder which is relatively low in formation of coagulated particles. This powder was subjected to a dry contact treatment by means of a ball mill together with the sintering aids and dispersing agent containing therein an oleophilic group in the same manner as in Example 3. Various physical properties of the resulting powder are shown in Table 3. This powder was a fine powder which is substantially freed of the formation of coagulated particles and which has a sharp particle size distribution. Further, this powder was not at all compatible with water. Then, this powder was dispersed in an aqueous solution containing the same surfactant as in Example 3 to examine its hydrolyzability. As the result, even after immersing for 90 days, the pH value of the aqueous solution did not change from the initial value of 5.9 so that it had remarkably improved hydrolysis resistance. Further, the resulting powder was molded and sintered in the same manner as in Example 1. The resulting molded article had a high relative density of 59% and showed a low degree of shrinkage as 16% during the sintering. The sintered body showed a high thermal conductivity of 205 W/mK. COMPARATIVE EXAMPLE 2 2600 g of ion exchange water having dissolved therein 306 g of a low-sodium content alumina powder (purity: 99.9%, an average particle diameter measured by sedigraph: 0.8 µm, content of particles having a particle diameter of not more than 1 µm: 78%), 216 g of a 100% pressed product of acetylene black having an ash content of 0.005%, 11.3 g of aluminum nitrate [Al(NO₃)₃·9H₂O], 5.2 g of polyethylene glycol, and 15.1 g of a nonionic surfactant comprising polyoxyethylene alkylphenyl ethers (Noigen® EA137, a trade name of Dai-ichi Kogyo Seiyaku Co., Ltd.) was charged in a polyethylene-made pot together with 600 pieces of nylon balls having a diameter of 15 mm and wet mixed at a revolution rate of 40 rpm for 10 hours. The thus obtained mixed slurry was dried in a dryer. 500 g of the dried slurry was weighed on a graphite-made tray and subjected to reductive nitriding reaction upon firing at 1580°C for 7 hours while flowing a nitrogen gas at a rate of 200 cm/min in an electric furnace. This reaction product was then fired in dry air at 700°C for 3 hours to calcine and remove excess carbon, whereby an aluminum nitride powder was obtained. Various physical properties of this aluminum nitride powder are shown in Table 3. This powder was a high-purity fine powder in which coaguated particles were slightly present. Further, this powder was dispersed in an aqueous solution containing the same surfactant as in Example 3 to examine its hydrolyzability. As the result, after immersing for only one day, the pH of the aqueous solution increased from 5.8 to 10.6 so that it was likely that hydrolysis took place. The resulting powder was molded and sintered in the same manner as in Example 3. As the result, the molded article had a relative density of 52% and showed a high degree of shrinkage of 20% during the sintering. Further, the sintered body had a thermal conductivity of 75 W/mK. Physical Aluminum Properties of Powder (a) (b) Oxygen content (%) 1.0 1.1 Iron content (ppm) 8 9 Silicon content (ppm) 56 40 Titanium content (ppm) 13 13 Average diameter (µm) 1.8 1.8 Content of particles of greater than 2 µm (%) 43 46 Content of particles of smaller than 1 µm (%) 11 10 Bulk density (g/cm³) 0.3 0.3 Tapped density (g/cm³) 0.6 0.6 Example 3 Example 4 Comparative Example 2 Iron content (ppm) 9 10 8 Silicon content (ppm) 61 46 52 Titanium content (ppm) 13 14 13 CaCO₃ content (%) 1.26 1.26 - Y₂O₃ content (%) 2.85 2.85 - Average diameter (µm) 1.4 1.5 1.7 Content of particles of greater than 2 µm (%) 14 14 42 Content of particles of smaller than 1 µm (%) 13 13 12 Bulk density (g/cm³) 0.6 0.6 0.3 Tapped density (g/cm³) 1.4 1.5 0.6 EXAMPLE 5 Each of the aluminum nitride powders (a) and (b) obtained in Examples 3 and 4 was subjected to a dry contact treatment together with the sintering aid and dispersing agent containing therein an oleophilic group as shown in Table 4 in the same manner as in Example 3. All of the resulting aluminum nitride powders were incompatible with water and exhibited oleophilicity. Various properties of these aluminum nitride powders were evaluated in the same manner as in Example 3, the results of which are shown in Table 4. 100 g of each of the thus obtained aluminum nitride powders was added to 100 ml of an n-butanol solution having dissolved therein 1 g of an acrylic binder (CB-1, a product of Sanyo Chemical Co., Ltd.), followed by mixing and dispersing in a ball mill for 6 hours. After drying, the dispersion was passed through an No. 80 US Standard sieve. The powder which had passed through the sieve was press molded at 1,500 kg/cm² to form a molded article which was then embedded in a mixed powder of aluminum nitride and boron nitride and sintered in a nitrogen atmosphere at 1,850°C for 3 hours under atmospheric pressure. The characteristics of the resulting molded articles and sintered bodies are also shown in Table 4.

Claims: A reductive nitriding process for preparing an aluminum nitride powder, by heating a powdered mixture of alumina and carbon in a nitrogen-containing atmosphere, in which an excess of carbon is used in the reaction and the reaction product is further heated in air at a temperature of 600 to 750°C to remove the excess carbon, characterized in that the reaction product is pulverized after said further heating, and the obtained aluminum nitride powder has a tapped density of at least 1.0 gram/cubic centimeter. A process as claimed in Claim 1, wherein the molar ratio of the carbon to alumina in the reaction mixture is from 3:1 to 10:1. A process as claimed in either preceding claim, wherein the reaction product is mixed with 0.01 to 10 wt% of a sintering aid and 0.05 to 2 wt% of a dispersing agent containing an oleophilic group in its molecule, before the further heating in air. A process as claimed in any preceding claim, wherein the carbon powder reactant used is acetylene black. A process as claimed in any preceding claim, wherein the nitriding reaction in the nitrogen atmosphere is at a temperature of 1500 to 1700°C for a period of 2 to 10 hours. A process as claimed in any preceding claim, wherein the reaction mixture and/or the carbon is granulated prior to the reaction. A process as claimed in any preceding claim, wherein the powder obtained has a weight content of oxygen of not more than 2.0%, iron not more than 20 ppm, silicon not more than 100 ppm and titanium not more than 20 ppm. A process as claimed in Claim 7, wherein the powder has an oleophilic surface and contains 0.01-10 wt% of a sintering aid.

Inventors: MATSUDA, NORIO, MURAKAMI, HIDEAKI, MURASE, MITSUTOSHI, NAKANO, KAZUHIKO
Applicants: SUMITOMO CHEMICAL COMPANY, LIMITED
Application year: 1989
Main classification: C01B21
IPC codes: H01L21, C01B21