WO2002083961A1 - Procede de preparation d'un materiau platine renforcee - Google Patents
Procede de preparation d'un materiau platine renforcee Download PDFInfo
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- WO2002083961A1 WO2002083961A1 PCT/JP2002/003663 JP0203663W WO02083961A1 WO 2002083961 A1 WO2002083961 A1 WO 2002083961A1 JP 0203663 W JP0203663 W JP 0203663W WO 02083961 A1 WO02083961 A1 WO 02083961A1
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C32/00—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ
- C22C32/001—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with only oxides
- C22C32/0015—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with only oxides with only single oxides as main non-metallic constituents
- C22C32/0021—Matrix based on noble metals, Cu or alloys thereof
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F1/00—Metallic powder; Treatment of metallic powder, e.g. to facilitate working or to improve properties
- B22F1/12—Metallic powder containing non-metallic particles
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F1/00—Metallic powder; Treatment of metallic powder, e.g. to facilitate working or to improve properties
- B22F1/14—Treatment of metallic powder
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F1/00—Metallic powder; Treatment of metallic powder, e.g. to facilitate working or to improve properties
- B22F1/14—Treatment of metallic powder
- B22F1/145—Chemical treatment, e.g. passivation or decarburisation
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- C—CHEMISTRY; METALLURGY
- C03—GLASS; MINERAL OR SLAG WOOL
- C03B—MANUFACTURE, SHAPING, OR SUPPLEMENTARY PROCESSES
- C03B5/00—Melting in furnaces; Furnaces so far as specially adapted for glass manufacture
- C03B5/16—Special features of the melting process; Auxiliary means specially adapted for glass-melting furnaces
- C03B5/167—Means for preventing damage to equipment, e.g. by molten glass, hot gases, batches
- C03B5/1672—Use of materials therefor
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- C—CHEMISTRY; METALLURGY
- C03—GLASS; MINERAL OR SLAG WOOL
- C03B—MANUFACTURE, SHAPING, OR SUPPLEMENTARY PROCESSES
- C03B5/00—Melting in furnaces; Furnaces so far as specially adapted for glass manufacture
- C03B5/16—Special features of the melting process; Auxiliary means specially adapted for glass-melting furnaces
- C03B5/167—Means for preventing damage to equipment, e.g. by molten glass, hot gases, batches
- C03B5/1672—Use of materials therefor
- C03B5/1675—Platinum group metals
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C5/00—Alloys based on noble metals
- C22C5/04—Alloys based on a platinum group metal
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F9/00—Making metallic powder or suspensions thereof
- B22F9/02—Making metallic powder or suspensions thereof using physical processes
- B22F9/04—Making metallic powder or suspensions thereof using physical processes starting from solid material, e.g. by crushing, grinding or milling
- B22F2009/041—Making metallic powder or suspensions thereof using physical processes starting from solid material, e.g. by crushing, grinding or milling by mechanical alloying, e.g. blending, milling
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F9/00—Making metallic powder or suspensions thereof
- B22F9/02—Making metallic powder or suspensions thereof using physical processes
- B22F9/06—Making metallic powder or suspensions thereof using physical processes starting from liquid material
- B22F9/08—Making metallic powder or suspensions thereof using physical processes starting from liquid material by casting, e.g. through sieves or in water, by atomising or spraying
- B22F9/082—Making metallic powder or suspensions thereof using physical processes starting from liquid material by casting, e.g. through sieves or in water, by atomising or spraying atomising using a fluid
- B22F2009/0848—Melting process before atomisation
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F2998/00—Supplementary information concerning processes or compositions relating to powder metallurgy
- B22F2998/10—Processes characterised by the sequence of their steps
Definitions
- the present invention relates to a method for producing a reinforced platinum material which is a structural material used when melting and handling glass materials or ceramic materials such as optical glass and optical fibers, and more particularly to a platinum alloy powder obtained by melt spraying.
- the present invention relates to a technology for manufacturing a reinforced platinum material using the method. Landscape technology
- reinforced platinum materials with excellent high-temperature strength properties have been used as structural materials for handling glass materials and ceramic materials in the molten state.
- Reinforced platinum materials used for melting at high temperatures, such as glass materials are required to have high so-called creep strength.
- the durability time until creep rupture occurs is an important issue to make a material with a longer duration.
- This reinforced platinum material is required to have a high temperature creep strength, for example, a high creep strength at 140 ° C. Therefore, control of the material structure in the production of reinforced platinum materials is extremely important.
- a method of finely and uniformly dispersing a metal oxide such as zirconium oxide in a platinum base material of a reinforced platinum material in order to improve the high-temperature creep strength.
- Various manufacturing methods have been proposed to obtain reinforced platinum materials with dispersed oxides.
- Japanese Patent Application Laid-Open No. Hei 8-134451 discloses a method for producing a reinforced platinum material in which a metal oxide is finely dispersed in a platinum base material. It is disclosed that a platinum alloy composed of platinum is melted and sprayed, and then the obtained platinum alloy powder is subjected to wet pulverization.
- the manufacturing time can be shortened, compression molding in the manufacturing process, It is possible to obtain a reinforced platinum material that does not swell in heat treatment, hot forging, annealing, cold rolling, etc., and has stable creep strength.
- the reinforced platinum material produced by this method is subjected to a heat treatment at a high temperature such as 140 ° C., fine swelling may occur on the surface of the material.
- the reason that the strengthened platinum material obtained by the method of Japanese Patent Application Laid-Open No. 8-134345 / 11 generates fine swelling on the material surface by high-temperature heat treatment is that the melt-sprayed platinum alloy powder is wet-milled. It is presumed that the gas adsorbed on the fine powder surface during the treatment was released during the high-temperature heat treatment. Therefore, in order to prevent fine swelling during high-temperature heat treatment, it is conceivable to perform the subsequent manufacturing process at a high temperature so that the adsorption gas of the platinum alloy fine powder can be reduced as much as possible.
- Japanese Patent Application Laid-Open No. 2000-168600 discloses that a platinum alloy containing 0.05 to 2 wt% of zirconium, samarium, or the like is powdered by an atomizing method, and that A method is disclosed in which oxidation and sintering are performed at a high temperature of 750 ° C. for 1 to 100 hours, followed by plastic working. According to this publication, when the platinum alloy powder is oxidized and sintered at a high temperature of 140 ° C. or higher, metal oxide particles such as zirconium oxide dispersed in the reinforced platinum alloy material are about 1 to It is shown that the particles are dispersed with a relatively large diameter of 10 im.
- a reinforced platinum material that can be easily deformed can be realized, but it can only maintain a certain level of creep characteristics at a high temperature of 100 ° C. or higher, and is more effective than the case of fine metal oxide particles. Creep properties at high temperatures tend to decrease.
- the gas adsorbed on the platinum alloy fine powder that has been subjected to the wet pulverization processing is removed, so that the subsequent manufacturing processing step is simply performed at a high temperature. If this is done, it is expected that coarsening of the metal oxide will occur and the high-temperature creep properties will deteriorate. Disclosure of the invention
- the present invention has been made in view of the above circumstances, and in the case of producing a reinforced platinum material using a melt-sprayed platinum alloy powder, the material can be heat-treated at 140 ° C. or more. No swelling on the surface, zirconium oxide Provided is a method for producing a reinforced platinum material in which metal oxides such as are dispersed finely and which have extremely excellent high-temperature cleave characteristics.
- the present inventor studied various heat treatment conditions in each processing step when producing a reinforced platinum material using a melt-sprayed platinum alloy powder, and obtained by wet pulverization.
- the platinum alloy fine powder is degassed in a vacuum atmosphere at 1200 to 140 ° C, the surface of the reinforced platinum material swells in a high-temperature atmosphere of 140 ° C or higher.
- the present inventors have also found that metal oxide particles dispersed in the material can be obtained without coarsening, and have arrived at the present invention.
- the present invention provides a reinforced platinum material in which a platinum alloy powder obtained by melt spraying is oxidized, and the platinum alloy powder is subjected to wet pulverization using an organic solvent, followed by sintering and forging.
- the fine powder of wet-processed platinum alloy is placed in a heat-resistant container and heated in a vacuum atmosphere at 120 to 140 to carry out degassing.
- the degassing treatment of the present invention When the degassing treatment of the present invention is performed, the organic solvent and other adsorbed gas adsorbed on the platinum alloy fine powder in the wet pulverization treatment are almost completely separated from the fine powder surface, and the high-temperature heat treatment is carried out. The occurrence of swelling on the material surface is eliminated. Even after degassing at such a high temperature, the reinforced platinum material produced through the subsequent sintering and forging processes is in a state in which metal oxide particles such as zirconium oxide are finely dispersed. Therefore, the high temperature creep characteristics are extremely excellent.
- the degassing treatment in the present invention is carried out by charging the wet-milled platinum alloy fine powder into a heat-resistant container. At this time, the platinum alloy fine powder charged into the heat-resistant container is subjected to tapping or compression. However, it is preferable not to compact the fine powder in the container. This is because if the platinum alloy fine powder in the heat-resistant container is brought into a compacted state, the contact between the fine powder particles becomes dense and the adsorbed gas cannot be sufficiently released from the surface of the fine powder. In the degassing treatment of the present invention, if the temperature is lower than 1200 ° C., the adsorbed organic solvent or other adsorbed gas tends to not sufficiently desorb from the surface of the fine powder, and exceeds 140 ° C.
- the pressure is preferably reduced to 1 Pa or less as a vacuum atmosphere. If the pressure exceeds IPa, removal of adsorbed gas and the like tends to be insufficient.
- the vacuum atmosphere should be able to remove the organic solvent and other adsorbed gas adsorbed on the platinum alloy fine powder, so reduce the pressure to lkPa to 10 kPa while introducing an inert gas such as argon gas. What you can do.
- the degassed platinum alloy fine powder is heated to 140 to 170 ° C. in an inert gas atmosphere to perform a sintering process. Is preferably performed. Since the degassing process of the present invention is performed at a high temperature of 1200 to 140 Ot, sintering of the platinum alloy fine powder in the heat-resistant container proceeds to some extent. Therefore, when the platinum alloy fine powder is taken out of the heat-resistant container after the degassing process, a sintered body having a shape conforming to the inner shape of the heat-resistant container is formed.
- the present inventor has studied the coarsening of particles in this enhanced platinum material, and found that the platinum alloy fine powder after the wet pulverization processing was continuously subjected to degassing and sintering. It was found that a reinforced platinum material with excellent high-temperature creep properties in a fine particle state could be stably manufactured.
- the wet-milled platinum alloy The powder is put into a heat-resistant container, placed in a degassing furnace, heated to a predetermined degassing temperature, degassed, cooled, and once taken out of the degassing furnace. Then, it is a common practice to separately put it into a sintering furnace and heat it to a predetermined sintering temperature again to perform sintering. However, if degassing and sintering are performed continuously on the wet-milled platinum alloy fine powder, that is, if the processing furnace is changed between degassing and sintering, etc.
- a heat-resistant container charged with platinum alloy fine powder is placed in a vacuum inert gas sintering furnace (for example, vacuum argon sintering furnace), degassed in a reduced-pressure atmosphere, and The sintering process is performed in the same furnace as it is without taking it out.
- a vacuum inert gas sintering furnace for example, vacuum argon sintering furnace
- the sintering process is performed in the same furnace as it is without taking it out.
- the degassing process is performed at 1200 to 140 ° C. as described above, and the sintering process is performed at 140 to 140; It is preferable to perform the treatment at 0 ° C., and therefore, it is desirable to perform the treatment at 120 ° C. to 170 ° C. as the temperature range when both processes are continuously performed.
- the temperature of the oxidation process before the wet pulverization process be as low as possible.
- the oxidation treatment of the platinum alloy powder is generally performed in a temperature range of 100 to 130 ° C, but in order to suppress the coarsening of the particles, 900 to 110 ° C is required.
- the oxidation treatment is preferably performed in the temperature range of C. This is because, when the platinum alloy powder is oxidized within this temperature range, the tendency to manufacture a reinforced platinum alloy in a fine particle state stably increases.
- heptane or alcohol as the organic solvent in the wet pulverization treatment in the method for producing a strengthened platinum material according to the present invention.
- Heptane or alcohol enhances the effect of treating the melt-sprayed platinum alloy powder into fine powder, and is easily separated from the surface of the platinum alloy fine powder by the degassing treatment of the present invention.
- the platinum alloy used when producing the reinforced platinum material of the present invention is preferably a platinum alloy containing at least one of a group I Va element, a lanthanum-based rare earth element, rhodium, iridium and gold. This is because these elements become metal oxides capable of improving high-temperature creep properties and are dispersed in the reinforced platinum material.
- those containing zirconium, samarium, europium, or rhodium can be used as a reinforced platinum material having excellent high-temperature cleave properties.
- FIG. 1 is a SEM observation photograph of the zirconium oxide particles in Example 1.
- FIG. 2 is an SEM observation photograph of the zirconium oxide particles in Comparative Example 2.
- FIG. 3 is a SEM observation photograph of the zirconium oxide particles in Example 2.
- FIG. 4 is a SEM observation photograph of the zirconium oxide particles in Comparative Example 3.
- FIG. 5 is a SEM observation photograph of the zirconium oxide particles in Comparative Example 4.
- Example 1 First, 14 kg of a platinum-zirconium alloy ingot containing 0.3 wt% of zirconium was produced by vacuum melting. Then, this platinum alloy ingot was subjected to groove roll rolling to be drawn to a wire diameter of 1.6 mm. Next, the drawn wire was melted by arc discharge using an arc spray gun, and the molten platinum-zirconium alloy was sprayed toward the surface of distilled water lm away from the muzzle of the arc spray gun by compressed air, 12 kg of spherical powder with a particle size of 10 to 200 m was prepared. The spherical powder was placed in an aluminum tray with an open top, and oxidized in an air atmosphere at 1250 ° C for 24 hours. 12 kg of this oxidized spherical powder was divided into three equal parts (4 kg).
- the attritor pot is formed of a container made of zirconia, and a lid and a crushing blade provided in the container are formed of SUS304. Also, this container has reduced A pressure mechanism and an organic solvent charging valve are provided.
- the pressure inside the pot was reduced to 0.4 Pa by a pressure reducing mechanism, and 30 cc of heptane was added from an organic solvent input valve while introducing argon gas into the pot, and finally the inside of the pot was filled. 1.
- the valve was closed with the argon gas at la tm.
- the attritor pot was mounted on an upright pole plate, and the milling blade was rotated at a rotation speed of 200 rpm to perform a wet-type fine grinding treatment for about 15 hours.
- the wet-pulverized fine powder was placed in a stainless steel pad container without a lid and dried at 120 ° (2 hours to remove heptane.
- the remaining oxidized spherical powder (8 kg) was subjected to wet pulverization and drying in the same manner, and the fine powder obtained in this manner was scale-like in various forms having a thickness of about 0.3 to 1 Aim.
- the surface area of each part was very large.4 kg of this fine powder was used in Examples, and the remaining 8 kg was used in Comparative Examples.
- the degassed fine powder sintered body is placed as it is in a vacuum argon sintering furnace, and is heated in a 0.4 Pa argon atmosphere at a temperature rising rate of 5 ° C / min from room temperature to 1300 ° C / min.
- a heating rate of 1300 ° C to 10 ° C / min was performed for 3 hours while maintaining the temperature at 1600 ° C.
- the fineness of the sintered compact after the sintering process was 35%.
- This sintered fine powder sintered body is subjected to high-temperature forging at 1250 ° C, and the forged ingot is subjected to an annealing treatment at 1250 ° C for 30 minutes in the air.
- Comparative Example 1 In Comparative Example 1, first, 4 kg of the scaly powder after the above-mentioned wet pulverization treatment and drying treatment was put into a steel die, compressed under a pressure of 65 OMpa, and formed into a compact (5 mm in length). 68 mm wide x 6 Omm high). Then, the formed body was heat-treated in the atmosphere at 1250 for 1 hour, then put again in a steel die, and subjected to a compression treatment at a pressure of 85 OMPa. The compactness of the compact after the compression treatment was 95%.
- Comparative Example 2 In Comparative Example 2, first, 4 kg of the platinum alloy fine powder after the above-mentioned wet pulverization treatment and drying treatment was converted into a cylindrical almi-lupo (porous aluminum lupo) having an inner diameter of 8 OmmX and a depth of 15 Omm.
- the sintering process was performed in an air atmosphere in an air atmosphere from room temperature to 1600 ° C at a heating rate of 10 ° C / min, and a sintering treatment was performed at 160 ° C for 3 hours. After that, the sintered body was cooled and taken out from the aluminum crucible. The obtained sintered body had a denseness of 40%.
- This sintered body was also subjected to high-temperature forging at 1250 ° C in the same manner as in the above-described embodiment, and the forged ingot was subjected to annealing at 1250 ° C for 30 minutes in an air atmosphere.
- the ingot was cold-rolled to produce a lmm thick reinforced platinum material.
- the high-temperature creep characteristic of 1400 can realize a very excellent creep durability even when a load of 20 MPa and 15 MPa is applied, The material itself does not swell at all even in a heat treatment in a temperature atmosphere.
- Comparative Example 1 at a load of 15 MPa, the same high-temperature creep characteristics as those of the example were exhibited, but it was 20 MPa.
- the creep durability time is inferior to that of the examples, and the material swells by heat treatment in an atmosphere at a temperature of 1400 ° C or higher.
- Example 2 In Example 2, unlike Example 1, a case is described in which a degassing process and a sintering process are continuously performed to produce a reinforced platinum material. First, 14 kg of platinum-rhodium containing 10 wt% zirconium alloy ingot (Rh—Zr platinum alloy ingot) containing 2 wt% of zirconium was produced by vacuum melting.
- this Rh-Zr platinum alloy ingot was subjected to groove roll rolling to draw a wire having a wire diameter of 1.6 mm.
- the drawn wire is melted by arc discharge using an arc spray gun, and the molten metal is sprayed with compressed air toward the surface of distilled water lm away from the muzzle of the arc spray gun, and the particle size is 10 to 200 m.
- 12 kg of spherical powder was prepared.
- 8 kg of the spherical powder was put into an alumina tray having an open top, and oxidized at 1100 ° C for 24 hours in an air atmosphere to obtain an oxidized spherical powder.
- Example 2 Of the 8 kg of the spherical powder that had been subjected to the oxidation treatment (1 100 ° C), half of the 4 kg was used in Example 2 and the remaining 4 kg was used in Comparative Example 3. The remaining 4 kg of the spherical powder was placed in an alumina tray with an open top and oxidized at 1250 ° C for 24 hours in an air atmosphere. And Subsequently, 4 kg each of the oxidized spherical powder used in Example 2, Comparative Example 3, and Comparative Example 4 and 7 kg of a zirconia pole having a sphere diameter of 5 mm were wet-milled into an Atrai-Yu Pond. Wet pulverizers were separately charged and wet pulverized.
- This attrition pot is the same as that described in Example 1 above.
- the pressure inside the pot is reduced to 0.4 Pa by a pressure reducing mechanism, and 30 cc of heptane is dissolved in an organic solvent while introducing argon gas into the pot.
- the valve was closed with the addition of the injection valve and the final pressure inside the pot of 1.1 atm argon. Then, attach the Attra Itapot to the upright pole plate, and rotate the milling blades at a rotation speed of 200 rpm. It was rotated and subjected to wet pulverization for about 15 hours.
- the wet-pulverized fine powder was placed in a stainless steel pad container without a lid, and dried at 120 ° C. for 2 hours to remove heptane.
- Example 2 Each of the oxidized spherical powders (4 kg) of Example 2, Comparative Example 3, and Comparative Example 4 was subjected to wet pulverization and drying as described above.
- Each of the fine powders thus obtained was in the form of scales of various shapes with a thickness of about 0.3 to 1 m, and the surface area of each was very large.
- Example 2 4 kg of this wet-milled fine powder (1100 ° C oxidation treatment) was filled in a carbon container without a lid (same shape as in Example 1), and was baked under vacuum argon. Place in a kiln, heat from room temperature to 1400 ° C at a rate of 5 ° C Zmin in an argon atmosphere of 0.4 kPa, hold at 1400 ° C for 3 hours, degas and sinter The treatment was performed continuously. After the degassing and sintering treatment and cooling, the platinum alloy fine powder was taken out of the carbon container, and the fine powder was a sintered body in the inner shape of the carbon container. The compactness of the body was 39%.
- Example 2 the degassed and sintered fine powder sintered body is subjected to high-temperature forging at 1300 in the air, and the forged ingot is subjected to annealing at 1300 ° C. for 30 minutes in the air. After that, the ingot was cold-rolled to produce a 1 mm thick reinforced platinum material (Example 2).
- Comparative Example 3 In Comparative Example 3 (4 kg of spherical powder oxidized at 1100 ° C.), 4 kg of the scaly powder after the wet pulverization and drying described above was placed in the same carbon container as in Example 2 above. Filled and placed in a vacuum roasting furnace.
- the sample was heated from normal temperature to 1300 ° C at a heating rate of 5 ⁇ / ⁇ in, kept at 1300 ° C for 3 hours, degassed, and cooled.
- the compactness of the sintered compact after the degassing was 34%.
- the powdered sintered compact after degassing is put into a vacuum argon sintering furnace as it is, and in a 0.4 kPa argon atmosphere, from normal temperature to 1300 at a heating rate of 5 ° CZmin. Heating, and from 1300 ° C to 1600 ° C at a heating rate of 1 O ⁇ Zmin, Sintering was performed for 3 hours while maintaining the temperature at 60 Ot.
- the fineness of the sintered compact after this sintering process was 40%.
- Comparative Example 4 In Comparative Example 4 (4 kg of spherical powder oxidized at 1250 ° C), 4 kg of the flaky fine powder after the wet pulverization treatment and the drying treatment described above was replaced with the same carbon as in Example 2 above.
- the container was filled into a container and made into a vacuum roasting furnace. In a vacuum atmosphere of 0.4 Pa, the temperature was raised from room temperature to 1300 ° C.
- the powdered sintered body after degassing is put into a vacuum argon sintering furnace as it is, and is heated at a temperature rising rate of 5 ° C / min from room temperature in an argon atmosphere of 0.4 kPa. It was heated to 300, and further heated from 1600 ° C to 1600 ° C at a rate of 1300 ° C to 10 ° C Zmin, and sintered at 1600 for 3 hours.
- the fineness of the sintered compact after the sintering process was 40%.
- the sintered fine powder after the sintering is also subjected to high-temperature forging at 1300 ° C, and the forged ingot is subjected to an annealing treatment at 1300 ° C for 30 minutes in an air atmosphere, and then the ingot is cooled.
- a 1 mm thick reinforced platinum material (Comparative Example 4) was manufactured.
- Tables 5 to 7 show the results of high-temperature creep property evaluation of Example 2, Comparative Example 3 and Comparative Example 4.
- the high-temperature creep test method is the same as in Example 1 above, and Tables 5 to 7 show the results of the creep test under a predetermined load in a 1400 ° C temperature atmosphere. [Table 5]
- FIG. 3 shows FE-SEM photographs of Example 2
- FIG. 4 shows Comparative Example 3
- FIG. 5 shows Comparative Example 4.
- the zirconia oxide particles of Example 2 had a size of about 50 to 200 nm in diameter, and Comparative Example 1 was found to be at the same level. On the other hand, dispersed particles having a diameter of about 0.1 to 1 m in Comparative Example 3 and a diameter of about 0.5 to 5 m in Comparative Example 4 were confirmed.
- Example 2 The reinforced platinum materials of Example 2 and Comparative Examples 3 and 4 were compared and investigated. The results were summarized as follows: oxidation of platinum alloy powder was performed at 1100 ° C, and degassing and sintering were performed using vacuum argon. It has been found that continuous operation in a sintering furnace results in oxides of fine particles.
- the high-temperature creep characteristic at 1400 ° C can realize a very good creep life time even when a stress of 20 MPa or 15 MPa is applied, and is 1200 to 1600. The material itself did not swell at all even in the heat treatment in a temperature atmosphere of ° C.
- metal oxides such as zirconium oxide are finely dispersed, and have excellent high-temperature creep characteristics, and swelling occurs on the material surface even at a high-temperature heat treatment such as 1400 ° C. This makes it possible to obtain a reinforced platinum material that does not need to be used.
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Description
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Priority Applications (6)
Application Number | Priority Date | Filing Date | Title |
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KR10-2002-7016562A KR100506633B1 (ko) | 2001-04-13 | 2002-04-12 | 강화 백금재료의 제조방법 |
CA002410805A CA2410805C (en) | 2001-04-13 | 2002-04-12 | Method for preparing reinforced platinum material |
EP02717123A EP1380660B1 (en) | 2001-04-13 | 2002-04-12 | Method for preparing reinforced platinum material |
DE60212363T DE60212363T2 (de) | 2001-04-13 | 2002-04-12 | Verfahren zur herstellung von verstärktem platinmaterial |
US10/276,322 US7217388B2 (en) | 2001-04-13 | 2002-04-12 | Method for preparing reinforced platinum material |
JP2002581700A JP4094959B2 (ja) | 2001-04-13 | 2002-04-12 | 強化白金材料の製造方法 |
Applications Claiming Priority (2)
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JP2001115161 | 2001-04-13 | ||
JP2001-115161 | 2001-04-13 |
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WO2002083961A1 true WO2002083961A1 (fr) | 2002-10-24 |
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PCT/JP2002/003663 WO2002083961A1 (fr) | 2001-04-13 | 2002-04-12 | Procede de preparation d'un materiau platine renforcee |
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US (1) | US7217388B2 (ja) |
EP (1) | EP1380660B1 (ja) |
JP (1) | JP4094959B2 (ja) |
KR (1) | KR100506633B1 (ja) |
CA (1) | CA2410805C (ja) |
DE (1) | DE60212363T2 (ja) |
WO (1) | WO2002083961A1 (ja) |
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WO2005052200A1 (ja) * | 2003-11-28 | 2005-06-09 | Tanaka Kikinzoku Kogyo K.K. | 強化白金材料の製造方法 |
JP2012087385A (ja) * | 2010-10-21 | 2012-05-10 | Tanaka Kikinzoku Kogyo Kk | 酸化物分散強化型白金合金の製造方法 |
Families Citing this family (4)
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CN101215652B (zh) * | 2008-01-04 | 2010-06-23 | 无锡英特派金属制品有限公司 | 氧化锆弥散强化钯金合金生产方法 |
JP5308499B2 (ja) * | 2011-11-11 | 2013-10-09 | 田中貴金属工業株式会社 | 白金系熱電対 |
WO2015111563A1 (ja) * | 2014-01-24 | 2015-07-30 | 株式会社フルヤ金属 | 金又は白金ターゲット及びそれらの製造方法 |
JP2022086046A (ja) * | 2020-11-30 | 2022-06-09 | 田中貴金属工業株式会社 | 強化白金合金及び強化白金合金の製造方法、並びにガラス製造装置 |
Citations (5)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US3511640A (en) * | 1968-03-27 | 1970-05-12 | Du Pont | Degassing platinum powders |
JPH04236701A (ja) * | 1991-01-17 | 1992-08-25 | Mitsubishi Heavy Ind Ltd | 金属粉末の脱ガス方法 |
JPH06336631A (ja) * | 1993-05-28 | 1994-12-06 | Tanaka Kikinzoku Kogyo Kk | 酸化物分散強化白金又は白金合金及びその製造方法 |
JPH08134511A (ja) * | 1994-11-11 | 1996-05-28 | Tanaka Kikinzoku Kogyo Kk | 強化白金材料の製造方法 |
US5623725A (en) * | 1994-05-19 | 1997-04-22 | Schott Glaswerke | Process for producing very pure platinum materials, semi-finished parts and foils dispersion-reinforced with Y203 |
Family Cites Families (15)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US2636819A (en) * | 1951-01-31 | 1953-04-28 | Baker & Co Inc | Grain stabilizing metals and alloys |
GB981792A (en) * | 1962-05-07 | 1965-01-27 | Mond Nickel Co Ltd | Improvements relating to precious metals and alloys thereof |
CH540984A (de) * | 1968-01-20 | 1973-10-15 | Degussa | Verfahren zur Herstellung eines dispersionsgehärteten Werkstoffs |
GB1280815A (en) | 1968-07-12 | 1972-07-05 | Johnson Matthey Co Ltd | Improvements in and relating to the dispersion strengthening of metals |
FR1587716A (ja) * | 1968-08-30 | 1970-03-27 | ||
US3578443A (en) * | 1969-01-21 | 1971-05-11 | Massachusetts Inst Technology | Method of producing oxide-dispersion-strengthened alloys |
US3709667A (en) * | 1971-01-19 | 1973-01-09 | Johnson Matthey Co Ltd | Dispersion strengthening of platinum group metals and alloys |
US4292079A (en) * | 1978-10-16 | 1981-09-29 | The International Nickel Co., Inc. | High strength aluminum alloy and process |
US4409038A (en) * | 1980-07-31 | 1983-10-11 | Novamet Inc. | Method of producing Al-Li alloys with improved properties and product |
US4600556A (en) * | 1983-08-08 | 1986-07-15 | Inco Alloys International, Inc. | Dispersion strengthened mechanically alloyed Al-Mg-Li |
US4707184A (en) * | 1985-05-31 | 1987-11-17 | Scm Metal Products, Inc. | Porous metal parts and method for making the same |
US4705560A (en) * | 1986-10-14 | 1987-11-10 | Gte Products Corporation | Process for producing metallic powders |
JP3359583B2 (ja) | 1998-12-01 | 2002-12-24 | 田中貴金属工業株式会社 | 強化白金材料及びその製造方法 |
JP3778338B2 (ja) * | 2000-06-28 | 2006-05-24 | 田中貴金属工業株式会社 | 酸化物分散強化型白金材料の製造方法 |
JP3776296B2 (ja) * | 2000-06-28 | 2006-05-17 | 田中貴金属工業株式会社 | 酸化物分散強化型の白金材料及びその製造方法 |
-
2002
- 2002-04-12 DE DE60212363T patent/DE60212363T2/de not_active Expired - Lifetime
- 2002-04-12 CA CA002410805A patent/CA2410805C/en not_active Expired - Fee Related
- 2002-04-12 WO PCT/JP2002/003663 patent/WO2002083961A1/ja active IP Right Grant
- 2002-04-12 JP JP2002581700A patent/JP4094959B2/ja not_active Expired - Fee Related
- 2002-04-12 EP EP02717123A patent/EP1380660B1/en not_active Expired - Lifetime
- 2002-04-12 KR KR10-2002-7016562A patent/KR100506633B1/ko active IP Right Grant
- 2002-04-12 US US10/276,322 patent/US7217388B2/en not_active Expired - Lifetime
Patent Citations (5)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US3511640A (en) * | 1968-03-27 | 1970-05-12 | Du Pont | Degassing platinum powders |
JPH04236701A (ja) * | 1991-01-17 | 1992-08-25 | Mitsubishi Heavy Ind Ltd | 金属粉末の脱ガス方法 |
JPH06336631A (ja) * | 1993-05-28 | 1994-12-06 | Tanaka Kikinzoku Kogyo Kk | 酸化物分散強化白金又は白金合金及びその製造方法 |
US5623725A (en) * | 1994-05-19 | 1997-04-22 | Schott Glaswerke | Process for producing very pure platinum materials, semi-finished parts and foils dispersion-reinforced with Y203 |
JPH08134511A (ja) * | 1994-11-11 | 1996-05-28 | Tanaka Kikinzoku Kogyo Kk | 強化白金材料の製造方法 |
Non-Patent Citations (1)
Title |
---|
See also references of EP1380660A4 * |
Cited By (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
WO2005052200A1 (ja) * | 2003-11-28 | 2005-06-09 | Tanaka Kikinzoku Kogyo K.K. | 強化白金材料の製造方法 |
JP2012087385A (ja) * | 2010-10-21 | 2012-05-10 | Tanaka Kikinzoku Kogyo Kk | 酸化物分散強化型白金合金の製造方法 |
Also Published As
Publication number | Publication date |
---|---|
EP1380660B1 (en) | 2006-06-14 |
KR20030023634A (ko) | 2003-03-19 |
JPWO2002083961A1 (ja) | 2004-08-05 |
US20030124015A1 (en) | 2003-07-03 |
DE60212363T2 (de) | 2007-05-16 |
DE60212363D1 (de) | 2006-07-27 |
EP1380660A4 (en) | 2005-07-20 |
CA2410805C (en) | 2008-01-22 |
CA2410805A1 (en) | 2002-10-24 |
US7217388B2 (en) | 2007-05-15 |
EP1380660A1 (en) | 2004-01-14 |
JP4094959B2 (ja) | 2008-06-04 |
KR100506633B1 (ko) | 2005-08-10 |
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