WO2005052200A1 - 強化白金材料の製造方法 - Google Patents
強化白金材料の製造方法 Download PDFInfo
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- WO2005052200A1 WO2005052200A1 PCT/JP2004/017567 JP2004017567W WO2005052200A1 WO 2005052200 A1 WO2005052200 A1 WO 2005052200A1 JP 2004017567 W JP2004017567 W JP 2004017567W WO 2005052200 A1 WO2005052200 A1 WO 2005052200A1
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- Prior art keywords
- platinum
- producing
- treatment
- reinforced
- sintered body
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Classifications
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/04—Making non-ferrous alloys by powder metallurgy
- C22C1/05—Mixtures of metal powder with non-metallic powder
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/10—Alloys containing non-metals
- C22C1/1078—Alloys containing non-metals by internal oxidation of material in solid state
-
- 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
- B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
- B22F3/24—After-treatment of workpieces or articles
-
- 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
- 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
- B22F2998/00—Supplementary information concerning processes or compositions relating to powder metallurgy
- B22F2998/10—Processes characterised by the sequence of their steps
-
- 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
- B22F2999/00—Aspects linked to processes or compositions used in powder metallurgy
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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02E—REDUCTION OF GREENHOUSE GAS [GHG] EMISSIONS, RELATED TO ENERGY GENERATION, TRANSMISSION OR DISTRIBUTION
- Y02E60/00—Enabling technologies; Technologies with a potential or indirect contribution to GHG emissions mitigation
- Y02E60/30—Hydrogen technology
- Y02E60/50—Fuel cells
Definitions
- the present invention relates to a method for producing a reinforced platinum material, and more particularly to a technique for producing a reinforced platinum material using a platinum alloy powder obtained by melt spraying.
- a method for producing a reinforced platinum material having high-temperature strength characteristics for example, in order to improve high-temperature creep strength at 1400 ° C, zirconium oxide or the like is contained in a platinum base material of the reinforced platinum material.
- a method for finely and uniformly dispersing the metal oxidized product is known.
- Various production methods have been proposed for obtaining a reinforced platinum material in which such a metal oxide is dispersed in a platinum base material.
- the present inventors have proposed a method for producing a reinforced platinum material using a melt-sprayed platinum alloy powder. According to this manufacturing method, even when a heat treatment at 1400 ° C. or more is performed, no swelling occurs on the material surface, and a metal oxide such as zirconium oxide is finely dispersed. This makes it possible to produce a reinforced platinum material. (See Patent Document 1).
- Patent Document 1 International Publication No. 02Z083961 pamphlet
- the manufacturing method proposed by the present inventors is to oxidize a platinum alloy powder obtained by melt spraying, wet-pulverize the platinum alloy powder with an organic solvent, and perform sintering and forging. Platinum alloy fine powder that has been wet-milled is placed in a heat-resistant container and heated to 1200-1400 ° C in a vacuum atmosphere to degas. To do.
- the manufacturing method proposed by the present inventors has the following points to be improved.
- the manufacturing process is described in order.
- a platinum alloy powder that has been melt-sprayed is put into an alumina tray and subjected to an oxidation treatment at a temperature of 1200 ° C. or more in an atmospheric atmosphere for 24 hours.
- the powder in the tray undergoes sintering and becomes a massive sintered body.
- the sintered body formed into a lump by the oxidation treatment is pulverized and powdered again using a mortar or the like. Further, in order to equalize the re-ground powder particles, they were sieved with a sieve having a predetermined opening.
- the manufacturing method proposed by the present inventor since the above-described oxidation treatment is performed, the manufacturing time is prolonged due to the increase in the number of steps, and platinum is adhered to the alumina tray to form a platinum base metal. , And the production yield could not be improved.
- the platinum alloy fine powder subjected to wet pulverization is put into a heat-resistant container (made of carbon) and degassed at 1300 ° C in a vacuum atmosphere.
- a heat-resistant container made of carbon
- degassed at 1300 ° C in a vacuum atmosphere.
- complicated maintenance such as cutting off the platinum metal with a knife or a spatula is required.
- the platinum alloy sheet material obtained by rolling after the forging process is liable to generate voids and splashes (a phenomenon in which a small amount of molten metal is splashed and scattered when welding a reinforced platinum material).
- the ingot has a compactness of about 35% after sintering in an argon atmosphere at 1600 ° C.
- 65% of the total ingot to be forged is air, and when forged with an air hammer in the atmosphere, most of the air is pushed out of the ingot, but only a small portion of the air
- the gas components remaining inside the ingot are trapped between the sintered platinum particles, causing voids and splashes during welding.
- the present invention has been made in view of the above circumstances, and has improved the method of manufacturing a reinforced platinum material using a platinum alloy powder by melt spraying, proposed by the present inventor, and has achieved simpler operations. Further, it is an object of the present invention to provide a method for producing a reinforced platinum material that does not cause various problems at the time of forging processing, that is, does not generate voids and spatters at the time of welding and can secure the strength of a welded portion.
- Patent Document 1 In order to solve the above-mentioned problems, the present inventors have studied a method for producing a conventionally proposed reinforced platinum material (see Patent Document 1). From the manufacturing method according to Patent Document 1, about 10 g of a reinforced platinum material sample for analysis was sampled, and oxygen analysis was performed to investigate the degree of oxidation of the added zirconium. However, melt spray Platinum alloy powder 50%, followed by oxidation in a heat-resistant container (alumina tray) 60%, and degassing at 1300 ° C after fine grinding by an attritor, almost 60% It was an acid dandelion rate.
- the present invention provides a platinum alloy powder obtained by melt spraying, which is subjected to wet pulverization processing by adding an organic solvent, heating the platinum alloy fine powder, performing degassing processing, sintering processing, and forging processing.
- a sintered body formed by a sintering treatment is subjected to an oxidation treatment, and the sintered body is subjected to a compression molding treatment.
- the sintered body having a low density is subjected to the oxidation treatment, the zirconium oxidation can be progressed all the way to the center of the sintered body.
- the oxidized sintered compact By subjecting the oxidized sintered compact to compression molding, it becomes possible to convert the low-density sintered compact into a molded article having a predetermined shape, and to easily and quickly perform the subsequent forging process.
- the sintered body in a sparse state (extremely porous state) having a denseness of about 35% is subjected to the acid treatment, so that the acid progresses to the center of the sintered body in a short time.
- the denseness of the sintered body be 25% to 50%. If the fineness is less than 25%, the powder easily collapses and becomes difficult to handle when carrying, and if it exceeds 50%, the central part of the sintered body cannot be sufficiently oxidized.
- the oxidation treatment temperature in the method for producing a strengthened platinum material of the present invention is preferably from 1000 ° C. to 1400 ° C. When the temperature is lower than 1000 ° C., the oxidation treatment of zirconium does not proceed sufficiently, and the time for the oxidation treatment must be lengthened. If the temperature exceeds 1400 ° C, oxidized zirconia aggregates and coarsens, and a reinforced platinum material having high creep strength cannot be obtained immediately.
- the compression molding process in the present invention is preferably performed by hot pressing (hot press molding).
- hot press molding compression molding can be performed from above and below while reducing the pressure in a vacuum, so that degassing can be performed simultaneously with the press treatment, and a high-density compact can be obtained.
- the hot pressing temperature at that time is desirably 20 ° C to 1200 ° C. When the temperature exceeds 1200 ° C, when hot pressing is performed in a vacuum atmosphere, a reduction reaction easily occurs, and oxide dispersion components (for example, zirconium oxide) contained in the platinum alloy are reduced and decomposed. Oxygen turns into a gas to form bubbles, which cause material swelling and voids during welding.
- the reason for expanding the hot press temperature to 20 ° C, the so-called normal temperature, as the lower limit temperature is that, due to the research of the present inventor, even when press forming at normal temperature in a vacuum atmosphere, air This is because it has been found that a low-density sintered body with almost no confinement phenomenon can be made into a high-density compact, and the forging process can be performed easily and quickly.
- the hot press pressure is preferably 14MPa-40MPa. At a pressure of less than 14MPa, the compact density of the compact does not increase very much, it collapses during forging and heat is easily radiated immediately, trapping air during forging and expanding when welding the formed plate. Or voids. Also, if the pressure exceeds 40 MPa, there is a possibility that the carbon mold and the punch rod of the hot press may be damaged due to their strength.
- the heat-resistant container used in the degassing process of the present invention is used in a hot press in which it is preferable to provide a carbon sheet in the container and to put the platinum alloy fine powder after the wet pulverization process into the carbon sheet.
- the press die it is desirable to provide a carbon sheet and arrange the sintered body in the press die.
- the thickness of the carbon sheet is preferably from 0.03 to 0.5 mm.
- the thickness is less than 0.03 mm, it is not practical because the sheet does not have enough stiffness and the shape maintenance function is poor, and it is easily broken. On the other hand, if the thickness exceeds 0.5 mm, on the contrary, the flexibility of the sheet is poor and the sheet itself is easily broken, which is not practical.
- the platinum alloy is a Pt (platinum) -Zr (zirconium) alloy, a Pt (platinum) Rh (rhodium) Zr (zirconium) alloy, a Pt (platinum) -Au (gold) Zr (zirconium)
- Pt (platinum) -Zr alloy a Pt (platinum) -Zr (zirconium) alloy
- Pt (platinum) Rh (rhodium) Zr (zirconium) alloy a Pt (platinum) -Au (gold) Zr (zirconium)
- Zr in the platinum alloy becomes a metal oxide which can improve high-temperature creep properties and is dispersed in the reinforced platinum material.
- the composition of 0.05-0.4 wt% Zr and the balance Pt is preferred.
- a composition of 0.05—0.4 wt% Zr, 5-20 wt% Au, and the balance Pt is desirable. With such a composition, a reinforced platinum material having excellent high-temperature creep properties can be obtained.
- the wet pulverizing treatment, the sintering treatment, and the forging treatment be performed as follows.
- the wet fine powder reprocessing it is preferable to use heptane or alcohol as the organic solvent. Heptane or alcohol enhances the effect of processing the melt-sprayed platinum alloy powder into fine powder, and is easily separated from the surface of the platinum alloy fine powder.
- the wet pulverization it is desirable to dry the platinum alloy fine powder.
- the organic solvent attached to the powder is removed.
- the sintering process is preferably performed at a temperature of 1400 ° C to 1700 ° C.
- the sintering of the platinum alloy powder does not proceed sufficiently, and the material strength tends to decrease. If the temperature exceeds 1700 ° C, the platinum particles in the strengthened platinum material become coarse and This is because the metal oxide becomes coarse and the desired material strength cannot be achieved.
- This sintering process is desirably performed in an inert gas atmosphere such as argon gas.
- the forging process is preferably performed at a temperature of 1100 ° C. to 1400 ° C. in an air atmosphere. If the temperature is lower than 1100 ° C, cracks tend to occur easily. If the temperature exceeds 1400 ° C, zirconium oxide tends to become coarse.
- FIG. 1 is an X-ray observation photograph of a welded part when the reinforced platinum alloy material of the example is used.
- FIG. 2 is an X-ray observation photograph of a weld when a reinforced platinum alloy material of a comparative example is used.
- FIG. 3 is a cross-sectional structure observation photograph of a strengthened platinum alloy material of an example.
- FIG. 4 is a cross-sectional structure observation photograph of a reinforced platinum alloy material subjected to an oxidation treatment after hot pressing.
- spherical powder which is half of 24 kg, was divided into three equal parts without performing oxidation treatment. , Respectively, were subjected to wet pulverization and drying.
- Wet pulverization was carried out by feeding 4 kg of spherical powder and 7 kg of zirconia balls having a diameter of 5 mm into an attritor, which is a wet pulverizer.
- the atlite pot is a container made of zirconia, and the lid and the crushing blades provided in the container are made of SUS304.
- this container is provided with a pressure reducing mechanism and an organic solvent injection valve.
- the fine powder of platinum alloy in the carbon container was a lump having the shape of the interior of the lump, and the carbon sheet was fixed except for the upper surface of the lump. Then, this lump was put into an electric furnace and subjected to high-temperature fuel treatment at 1200 ° C for 30 minutes in an air atmosphere. By this high-temperature heat treatment, the carbon sheet adhered to the surface was removed by oxidizing and burning.
- the lump of the platinum alloy fine powder from which the carbon sheet had been removed was a so-called sintered body having an inner shape of a carbon container, and the denseness of the sintered body was 30%.
- the density is determined by measuring the mass and dimensions of the sintered body and calculating the density of the sintered body from the mass and volume. The value obtained by dividing the density of the sintered body by the platinum density (21.37 ⁇ 10 3 kg / m 3 ) is shown as a percentage.
- the degassed sintered body is placed as it is in a vacuum argon sintering furnace, and is heated to 1300 ° C at a temperature rising rate of 5 ° C from normal temperature to 5 ° C in a 0.4 Pa argon gas atmosphere. It was heated to 1600 ° C at a heating rate of 1300 ° C to 10 ° C Zmin, and then sintered at 1600 ° C for 3 hours. After this sintering process, the dimensions of the sintered body were 118 mm long ⁇ 118 mm wide ⁇ 115 mm high, and its compactness was 35%. Then, the sintered body was put into an atmospheric furnace at 1300 ° C, and kept at 1300 ° C for 1 hour to perform an oxidation treatment. Thereafter, the sintered body was allowed to stand at room temperature in the air and air-cooled.
- the hot press machine is a vacuum heating hot press of resistance heating type, made of carbon material (ISO-63), and has a die holder with inner dimensions of 120mm x 120mm x 200mm in depth, and 120mm x 120mm. It is equipped with a carbon mold for hot pressing consisting of a punch rod with a height of 160 mm.
- a carbon sheet (PF-20 made by Toyo Carbon Co., Ltd.) was previously inserted between the carbon mold for hot pressing and the sintered body.
- the molded body Since the carbon sheet was adhered to the surface of the molded body taken out, the molded body was put into an electric furnace and subjected to a high-temperature heat treatment at 1200 ° C for 30 minutes in an air atmosphere to obtain a carbon sheet. Oxidized and burned. The compact density of the molded body from which the carbon sheet was removed was 78%.
- the compact thus obtained was subjected to a high-temperature forging treatment at 1300 ° C.
- the ingot density after forging was 100%.
- the forging process there was no collapse of the sintered body without any collapse of the sintered body, and the forging starting force was 1 hour and 40 minutes from the completion of the forging to the end of the heat treatment.
- the forged ingot was annealed at 1300 ° C for 30 minutes in the atmosphere.
- the in The got was cold-rolled to produce a 1 mm thick reinforced platinum material.
- This comparative example is based on the method of manufacturing a reinforced platinum material conventionally proposed by the present inventors.
- the remaining 12 kg of the spherical powder obtained by the melt spraying in the above example was used.
- 12 kg of this spherical powder was divided into two equal parts, placed in an alumina tray open at the top, and oxidized in an air atmosphere at 1250 ° C for 24 hours.
- the degassed sintered body is placed as it is in a vacuum argon sintering furnace, and is heated from room temperature to 1300 ° C at a temperature rising rate of 5 ° C / min in a 0.4 Pa argon atmosphere. It was heated to 1600 ° C at a heating rate of 1300 ° C to 10 ° C Zmin, and sintered at 1600 ° C for 3 hours. After this sintering treatment, the dimensions of the sintered body were 118 mm long ⁇ 118 mm wide ⁇ 115 mm high, and the compactness of the sintered body was 35%.
- the sintered body subjected to the sintering treatment was subjected to a high-temperature forging treatment at 1300 ° C.
- the surface of the sintered body collapsed like lava and was hit carefully and immediately, due to the low density of the sintered body in the early stage.However, the metal equivalent to about 250 g collapsed and collapsed after forging. Although bullion was recovered, 5g of bullion was lost.
- the forging starting force required a process time of as much as 5 hours until the completion of annealing after forging.
- the ingot density after forging was 100%.
- the forged ingot was annealed at 1300 ° C for 30 minutes in an air atmosphere. Thereafter, the ingot was cold-rolled to produce a 1 mm thick reinforced platinum material.
- Ratio 3 198> 500 Compare 4 208> 500
- FIGS. 1 and 2 show negative photographs of X-ray observations of the welds in Examples and Comparative Examples.
- the Example had a creep rupture strength of 50 hours at 5 MPa, while the Comparative Example exhibited a significantly shorter rupture time. From the above, it was found that the reinforced platinum material of the example was clearly superior in the characteristics at the time of welding, as compared with the comparative example.
- FIG. 3 shows a photograph of the ingot cross-sectional structure after the high-temperature forging treatment of the above-described example.
- FIG. 4 shows the ingot cross-sectional structure obtained by manufacturing a reinforced platinum material when the oxidation treatment was performed after hot pressing in the manufacturing procedure in the above example (each processing step). Are the same as in the Example).
- the surface layer of the obtained reinforced platinum material was mainly oxidized (the oxidation rate of the zirconium after the oxidation treatment was:
- the microstructure on the surface layer was elongated crystal grains with a large aspect ratio. It was observed that the inner side had a spherical crystal structure as compared with the surface layer. Judging from the strength of this tissue condition, it was expected that strong creep strength could not be expected.
- FIG. 3 in the reinforced platinum material obtained by the procedure of the example, the microstructures in the surface layer and the inner side were almost the same, and it was determined that high creep strength could be realized.
Abstract
Description
Claims
Priority Applications (5)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
CA2512096A CA2512096C (en) | 2003-11-28 | 2004-11-26 | Method for producing reinforced platinum material |
US10/543,596 US20060153727A1 (en) | 2003-11-28 | 2004-11-26 | Method for producing reinforced platinum material |
DE602004023305T DE602004023305D1 (de) | 2003-11-28 | 2004-11-26 | Verfahren zur herstellung von verstärktem platinmaterial |
EP04819434A EP1657316B1 (en) | 2003-11-28 | 2004-11-26 | Method for producing reinforced platinum material |
AT04819434T ATE443778T1 (de) | 2003-11-28 | 2004-11-26 | Verfahren zur herstellung von verstärktem platinmaterial |
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
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JP2003-400540 | 2003-11-28 | ||
JP2003400540A JP4136914B2 (ja) | 2003-11-28 | 2003-11-28 | 強化白金材料の製造方法 |
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WO2005052200A1 true WO2005052200A1 (ja) | 2005-06-09 |
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PCT/JP2004/017567 WO2005052200A1 (ja) | 2003-11-28 | 2004-11-26 | 強化白金材料の製造方法 |
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US (1) | US20060153727A1 (ja) |
EP (1) | EP1657316B1 (ja) |
JP (1) | JP4136914B2 (ja) |
KR (1) | KR100698394B1 (ja) |
CN (1) | CN100363517C (ja) |
AT (1) | ATE443778T1 (ja) |
CA (1) | CA2512096C (ja) |
DE (1) | DE602004023305D1 (ja) |
ES (1) | ES2333726T3 (ja) |
WO (1) | WO2005052200A1 (ja) |
Families Citing this family (17)
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JP4702003B2 (ja) | 2005-11-16 | 2011-06-15 | セイコーエプソン株式会社 | 液晶装置およびプロジェクタ |
KR100969991B1 (ko) * | 2007-05-03 | 2010-07-15 | 희성금속 주식회사 | 용사법을 이용한 백금과 강화백금 복합재료의 제조방법 |
JP4965696B2 (ja) * | 2010-10-21 | 2012-07-04 | 田中貴金属工業株式会社 | 酸化物分散強化型白金合金の製造方法 |
KR101279553B1 (ko) * | 2011-03-10 | 2013-06-28 | 희성금속 주식회사 | 플라즈마를 이용한 산화물 분산강화형 백금재료의 제조방법 |
KR20120103908A (ko) * | 2011-03-11 | 2012-09-20 | 희성금속 주식회사 | 산화물 분산강화형 백금 재료 제조용 백금 분말 제조 방법 |
KR101279555B1 (ko) * | 2011-03-24 | 2013-06-28 | 희성금속 주식회사 | 교차압연법을 이용한 산화물 분산강화형 백금재료의 제조방법 |
KR101321945B1 (ko) * | 2012-03-27 | 2013-10-28 | 희성금속 주식회사 | 건식법을 이용한 산화물 분산강화형 백금-금 합금 분말의 제조방법 |
KR20140074032A (ko) * | 2012-12-07 | 2014-06-17 | 희성금속 주식회사 | 산화물 분산 강화형 백금합금 판재 제조방법 |
US9157002B2 (en) * | 2013-07-12 | 2015-10-13 | Xerox Corporation | Phase change ink pigment dispersion process |
KR20150028037A (ko) * | 2013-09-05 | 2015-03-13 | 희성금속 주식회사 | 백금-로듐-산화물계 합금의 제조방법 |
CN105814218B (zh) * | 2013-09-06 | 2017-07-07 | “以V.N.古利朵娃命名的克拉斯诺亚尔斯克有色金属厂”股份公司 | 制备铂基或铂铑合金基复合材料的方法 |
KR101560455B1 (ko) * | 2013-10-29 | 2015-10-14 | 희성금속 주식회사 | 방전 플라즈마 소결을 이용한 LCD Glass 제조용 산화물 분산 강화형 백금로듐 합금의 제조 방법 |
DE102013225187B4 (de) * | 2013-12-06 | 2018-07-19 | Heraeus Deutschland GmbH & Co. KG | Verfahren zur Bearbeitung einer dispersionsgehärteten Platinzusammensetzung |
JP5769854B1 (ja) * | 2014-09-08 | 2015-08-26 | 石福金属興業株式会社 | 白金族金属又は白金族基合金の製造方法 |
CN105256167B (zh) * | 2015-10-09 | 2017-05-17 | 内江至诚铂业科技有限公司 | 一种铂铑合金漏板底板材料制备方法 |
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 |
CN113073224A (zh) * | 2021-03-19 | 2021-07-06 | 泓武科技材料(苏州)有限公司 | 铂族金属弥散强化材料的制备方法 |
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WO2002083961A1 (fr) * | 2001-04-13 | 2002-10-24 | Tanaka Kikinzoku Kogyo K.K. | Procede de preparation d'un materiau platine renforcee |
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US3709667A (en) * | 1971-01-19 | 1973-01-09 | Johnson Matthey Co Ltd | Dispersion strengthening of platinum group metals and alloys |
JPH08134511A (ja) * | 1994-11-11 | 1996-05-28 | Tanaka Kikinzoku Kogyo Kk | 強化白金材料の製造方法 |
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2003
- 2003-11-28 JP JP2003400540A patent/JP4136914B2/ja not_active Expired - Fee Related
-
2004
- 2004-11-26 CA CA2512096A patent/CA2512096C/en active Active
- 2004-11-26 US US10/543,596 patent/US20060153727A1/en not_active Abandoned
- 2004-11-26 CN CNB2004800032967A patent/CN100363517C/zh not_active Expired - Fee Related
- 2004-11-26 ES ES04819434T patent/ES2333726T3/es active Active
- 2004-11-26 DE DE602004023305T patent/DE602004023305D1/de active Active
- 2004-11-26 WO PCT/JP2004/017567 patent/WO2005052200A1/ja active IP Right Grant
- 2004-11-26 EP EP04819434A patent/EP1657316B1/en not_active Not-in-force
- 2004-11-26 KR KR1020057015476A patent/KR100698394B1/ko active IP Right Grant
- 2004-11-26 AT AT04819434T patent/ATE443778T1/de not_active IP Right Cessation
Patent Citations (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
WO2002083961A1 (fr) * | 2001-04-13 | 2002-10-24 | Tanaka Kikinzoku Kogyo K.K. | Procede de preparation d'un materiau platine renforcee |
Also Published As
Publication number | Publication date |
---|---|
CA2512096C (en) | 2012-09-11 |
JP4136914B2 (ja) | 2008-08-20 |
EP1657316B1 (en) | 2009-09-23 |
ATE443778T1 (de) | 2009-10-15 |
CA2512096A1 (en) | 2005-06-09 |
EP1657316A1 (en) | 2006-05-17 |
CN1745185A (zh) | 2006-03-08 |
KR20060011939A (ko) | 2006-02-06 |
CN100363517C (zh) | 2008-01-23 |
ES2333726T3 (es) | 2010-02-26 |
KR100698394B1 (ko) | 2007-03-23 |
DE602004023305D1 (de) | 2009-11-05 |
US20060153727A1 (en) | 2006-07-13 |
EP1657316A4 (en) | 2008-07-23 |
JP2005163069A (ja) | 2005-06-23 |
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