EP2423339A1 - Alliage de cuivre à résistance élevée - Google Patents

Alliage de cuivre à résistance élevée Download PDF

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Publication number
EP2423339A1
EP2423339A1 EP10767017A EP10767017A EP2423339A1 EP 2423339 A1 EP2423339 A1 EP 2423339A1 EP 10767017 A EP10767017 A EP 10767017A EP 10767017 A EP10767017 A EP 10767017A EP 2423339 A1 EP2423339 A1 EP 2423339A1
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EP
European Patent Office
Prior art keywords
copper alloy
strength copper
strength
iron
mass
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EP10767017A
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German (de)
English (en)
Inventor
Katsuyoshi Kondoh
Yoshiharu Kosaka
Akimichi Kojima
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San-Etsu Metals Co Ltd
San Etsu Metals Co Ltd
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San-Etsu Metals Co Ltd
San Etsu Metals Co Ltd
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Publication of EP2423339A1 publication Critical patent/EP2423339A1/fr
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C9/00—Alloys based on copper
    • C22C9/04—Alloys based on copper with zinc as the next major constituent
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/08—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of copper or alloys based thereon

Definitions

  • the present invention relates to high-strength copper alloys having excellent mechanical characteristics, and more particularly to high-strength copper alloys produced by a casting method. More preferably, the present invention is intended to provide high-strength copper alloys having strength characteristics improved by performing hot plastic working on cast copper alloys.
  • Copper alloys are widely used in automotive parts, parts of home electric appliances, electric, electronic, or optical parts, piping members (faucet fittings, valves), etc.
  • piping members for reduction in size, weight, and thickness of products and members has been greatly desired, and the copper alloys having higher specific gravity than iron need to be increased in strength in order to meet such a demand.
  • Patent Literature 1 discloses that a brass alloy having tensile strength characteristics as high as about 600 to 800 MPa is obtained by hot extrusion of a cast copper alloy.
  • Silicon (Si) as an added element has an advantage in that it forms ⁇ -phase forming a matrix, and thus improves a cutting property of a copper alloy.
  • Si is hard, adding Si causes problems such as higher cutting resistance and a shorter tool life as compared to brass alloys as described in JIS H 3250-C3604, C3771, etc.
  • Patent Literature 2 Japanese Patent No. 3,917,304 (free-cutting copper alloy, Patent Literature 2) and Japanese Patent No. 3,734,372 (lead-free free-cutting copper alloy, Patent Literature 3).
  • a small amount of zirconium and phosphorus be added to obtain granular crystal rather than dendrite crystal formed by a normal casting method, and the granular crystal be refined to 10 ⁇ m, thereby implementing high strength and high ductility.
  • a matrix is significantly harder than conventional brass alloys, thereby causing problems such as a degraded cutting property and a shorter tool life.
  • Patent Literature 4 Japanese Patent No. 4,190,570 (lead-free free-cutting copper alloy extruded material, Patent Literature 4), the inventors succeeded in improving the cutting property of a brass powder alloy extruded material and also obtaining high tensile strength thereof by producing brass alloy powder and adding graphite particles to the brass alloy powder instead of lead by using a powder metallurgy process.
  • a manufacturing method of a copper alloy disclosed in Patent Literature 4 copper alloy powder having fine crystal grains is produced by using a rapid solidification method, and this powder is formed and solidified by hot extrusion, whereby a copper alloy base material having a fine structure can be obtained.
  • a copper alloy extruded material having high strength and high ductility is obtained.
  • the copper alloy powder need be first formed and solidified in order to prepare a billet body for extrusion. It is therefore difficult to apply this manufacturing method to a conventional process of extruding a cast billet, and a press forming machine, a compacting apparatus, etc. is required to solidify the copper alloy powder.
  • the present invention proposes a copper-zinc alloy containing a proper amount of iron and chromium.
  • the high-strength copper alloy according to the present invention is widely applicable to automotive parts, parts of home electric appliances, electric, electronic, or optical parts, piping members, etc.
  • a high-strength copper alloy according to the present invention contains 20 to 45% of zinc, 0.3 to 1.5% of iron, 0.3 to 1.5% of chromium, and a balance of copper, based on mass.
  • a content ratio (Fe/Cr) of the iron to the chromium is 0.5 to 2 based on mass.
  • the high-strength copper alloy further contains at least one kind of element selected from the group consisting of 0.05 to 4% of lead, 0.02 to 3.5% of bismuth, 0.02 to 0.4% of tellurium, 0.02 to 0.4% of selenium, and 0.02 to 0.15% of antimony, based on mass.
  • the high-strength copper alloy may further contain 0.2 to 3% of tin, based on mass.
  • the high-strength copper alloy may further contain 0.2 to 3.5% of aluminum and 0.3 to 3.5% of calcium, based on mass.
  • the high-strength copper alloy may further contain at least one kind of element selected from a lanthanoid group consisting of lanthanum, cerium, neodymium, gadolinium, dysprosium, ytterbium, and samarium, and a total content of the at least one kind of element may be 0.5 to 5%, based on mass.
  • the high-strength copper alloy may further contain at least one kind of element selected from the group consisting of 0.5 to 3% of manganese, 0.2 to 1% of silicon, 1.5 to 4% of nickel, 0.1 to 1.2% of titanium, 0.1 to 1.5% of cobalt, and 0.5 to 2.5% of zirconium, based on mass.
  • the high-strength copper alloy includes iron-chromium compound particles at grain boundaries.
  • the iron-chromium compound particles are particles precipitated at the grain boundaries during solidification in a casting method, and preferably have a particle size of 10 to 50 ⁇ m.
  • the copper alloy is a copper alloy subjected to hot plastic working after being produced by a casting method.
  • the hot plastic working is, e.g., a working method selected from the group consisting of extrusion, forging, rolling, drawing, and pulling.
  • iron and chromium are essential elements to be added.
  • the iron content is 0.3 to 1.5%
  • the chromium content is 0.3 to 1.5%, based on mass. Since chromium has low solid solubility in copper, a copper-chromium mother alloy is prepared, and is added to molten pure copper melted in a crucible, thereby adjusting the chromium content. Next, a predetermined weight of iron is added. Then, other element or elements are added as required, and lastly, zinc is added. The mixture is stirred and poured into a casting mold. Zinc tends to evaporate as compared to other elements due to its high vapor pressure. Thus, zinc is lastly added to the molten copper alloy.
  • the molten copper alloy is cooled and solidified in the casting mold.
  • chromium slightly solid-solved in copper is crystallized at copper grain boundaries, and then iron is crystallized near the crystallized chromium.
  • chromium-iron compound particles having a size (particle size) of about 10 to 50 ⁇ m are present at the grain boundaries, and strength of the brass alloy is increased due to dispersion strengthening by the compound particles at the grain boundaries.
  • Japanese Patent No. 4,190,570 (lead-free free-cutting copper alloy extruded material) as well, the inventors describe the effect of improving strength of the brass alloy by adding iron and chromium.
  • the invention described in this patent is based on a powder metallurgy process by a rapid solidification method as a basic manufacturing method, chromium and iron, supersaturatedly solid-solved in copper alloy powder, are precipitated during an extrusion process, and are precipitated at grain boundaries or inside crystal grains as an iron-chromium compound as small as several hundreds of nanometers to several microns.
  • Such submicron fine iron-chromium compound particles that are precipitated based on the powder metallurgy process are completely different in a grain size and a production mechanism from the iron-chromium particles (compound particles) crystallized at the grain boundaries during solidification by a casting method as proposed in the present invention.
  • the brass alloy contain 0.3 to 1.5% of iron and 0.3 to 1.5% of chromium, based on mass.
  • the effect of improving the strength of the brass alloy as described above is not sufficient if the iron content and the chromium content are less than 0.3%.
  • ductility of the brass alloy is reduced if the iron content and the chromium content are more than 1.5%.
  • Corrosion resistance of the brass alloy is reduced if the iron content is more than 2%.
  • the content ratio (Fe/Cr) of iron to chromium be 0.5 to 2, based on mass.
  • the proportion of the chromium-iron compound at the grain boundaries described above increases in the case where the content ratio of iron to chromium is in this range. In other words, if the content ratio of iron to chromium is less than 0.5 or more than 2, iron or chromium is independently crystallized at the grain boundaries, whereby the effect of improving the strength is reduced.
  • the brass alloy contains at least one kind of element selected from the group consisting of 0.05 to 4% of lead, 0.02 to 3.5% of bismuth, 0.02 to 0.4% of tellurium, 0.02 to 0.4% of selenium, and 0.02 to 0.15% of antimony, based on mass. If the content of each element is less than the lower limit of the above range, a sufficient cutting property cannot be obtained, and a brass alloy base material has a rough surface after a cutting process, and the tool life is reduced. On the other hand, if the content of each element is more than the upper limit of the above range, mechanical characteristics such as strength and ductility are degraded because the element serves as an origin of fracture. Note that in view of the recent environmental problems, since the use of lead is restricted, it is more preferable to select bismuth as an element for improving the cutting property.
  • Tin is effective not only in forming ⁇ -phase in the matrix, but also in increasing the strength of the alloy by forming a compound with copper.
  • a preferred tin content is 0.2 to 3% based on mass. The effect described above is not sufficient if the tin content is less than 0.2%.
  • adding more than 3% of tin reduces the ductility of the brass alloy. Adding more than 2% (the content) of tin improves dezincing resistance of ⁇ -phase.
  • Aluminum forms an intermetallic compound with copper, and its spherical particles are dispersed in the matrix, thereby improving mechanical characteristics such as strength and hardness, and high-temperature oxidation resistance of the copper alloy.
  • a preferred aluminum content is 0.2 to 3.5% based on mass. The above effect of aluminum is not sufficient if the aluminum content is less than 0.2%. On the other hand, adding more than 3.5% of aluminum coarsens the compound with copper, resulting in reduced ductility of the brass alloy.
  • aluminum together with calcium described below, forms an intermetallic compound Al 2 Ca, thereby contributing to improvement in strength and hardness.
  • a preferred calcium content is 0.3 to 3.5% based on mass. The above effect is not sufficient if the calcium content is less than 0.3%. On the other hand, adding more than 3.5% of calcium coarsens the intermetallic compound Al 2 Ca, resulting in reduced ductility of the brass alloy.
  • a lanthanoid group (lanthanum, cerium, neodymium, gadolinium, dysprosium, ytterbium, and samarium) is effective as each element of the lanthanoid group is precipitated at grain boundaries as a compound with copper or is independently crystallized at the grain boundaries, and thus strengthens the matrix. It is desirable that the total content of the lanthanoid element group be 0.5 to 5% based on mass. The effect of the lanthanoid element group is not sufficient if the total content thereof is less than 0.5%. Adding more than 5% of the lanthanoid element group reduces the ductility, and also excessively hardens the copper alloy, thereby reducing extrusion workability.
  • the strength and hardness of the copper alloy can be improved by adding at least one kind of element selected from the group consisting of 0.5 to 3% of manganese, 0.2 to 1% of silicon, 1.5 to 4% of nickel, 0.1 to 1.2% of titanium, 0.1 to 1.5% of cobalt, and 0.5 to 2.5% of zirconium as a transition metal element group, based on mass.
  • element selected from the group consisting of 0.5 to 3% of manganese, 0.2 to 1% of silicon, 1.5 to 4% of nickel, 0.1 to 1.2% of titanium, 0.1 to 1.5% of cobalt, and 0.5 to 2.5% of zirconium as a transition metal element group, based on mass.
  • the above effect of improving the characteristics is not sufficient if the content of each element is less than the lower limit of the above range.
  • the ductility of the copper alloy is reduced if the content of each element exceeds the upper limit of the above range.
  • a molten copper alloy having the above composition is produced, and an ingot material is produced by a method in which the molten copper alloy is poured into a casting mold, or a continuous casting method. Moreover, hot plastic working, such as an extrusion, forging, rolling, drawing, or pulling, is performed on the ingot material as necessary.
  • the heating temperature that allows the ingot to be sufficiently plastic-deformed is in the range of 600 to 850°C. In particular, the heating temperature is desirably 750°C or less in order to suppress evaporation of zinc during heating.
  • Sample Nos. 1 to 5 as examples of the present invention contain a predetermined amount of iron and chromium
  • tensile strength (TS) of the extruded material is higher than Sample No. 19 as a comparative example by about 130 to 210 MPa. This is because iron-chromium compound particles made of iron and chromium are dispersed at grain boundaries, and thus the strength of the copper alloy is significantly increased. It is also recognized that the tensile strength is increased as the amount of iron and chromium is increased.
  • Sample Nos. 6 to 8 as examples of the present invention are copper alloys containing bismuth (Bi), and Sample Nos. 9 to 11 as examples of the present invention are copper alloys containing lead (Pb).
  • Bismuth and lead are the elements that are added to improve the cutting property of the copper alloy.
  • the tensile strength of the copper alloys of Sample Nos. 9 to 11 is slightly lower than Sample No. 2 as an example of the present invention containing neither bismuth nor lead, but is higher than Sample No. 17 or 18 as a comparative example by about 160 to 190 MPa.
  • adding bismuth or lead to the brass alloy containing iron and chromium can improve the cutting property while maintaining high tensile strength.
  • Sample Nos. 14 to 16 as examples of the present invention contain aluminum (A1) and calcium (Ca).
  • A1 aluminum
  • Ca calcium
  • the tensile strength is significantly increased by dispersion of an intermetallic compound Al 2 Ca in the matrix of the copper alloy.
  • Example 1 cast copper alloy ingots containing elements shown in Tables 3 and 4 were prepared. Each ingot was subjected to a hot extrusion process immediately after heating and keeping the ingot at 700°C. The extrusion process was performed at an extrusion ratio of 37. Tensile test pieces were obtained from each copper alloy extruded material, and a tensile test was conducted at room temperature at a strain rate of 5 ⁇ 10 -4 /s. The result is shown in Tables 3 and 4. Sample Nos. 20 to 24 and 28 to 33 are examples of the present invention, and Sample Nos. 25 to 27, 34, and 35 are comparative examples.
  • Each of Sample Nos. 21, 22, 23, and 24 as examples of the present invention contains a lanthanoid element.
  • the tensile strength of these samples reaches 640 to 680 MPa, which is higher than Sample No. 20 as an example of the present invention containing no lanthanoid element.
  • Each of Sample Nos. 29 and 30 as examples of the present invention is also a brass alloy containing a lanthanoid element. It can be verified that the tensile strength of these samples is significantly higher than Sample No. 28 as an example of the present invention containing no lanthanoid element.
  • Sample No. 31 as an example of the present invention is a brass alloy containing a proper amount of silicon (Si)
  • Sample No. 32 as an example of the present invention is a brass alloy containing a proper amount of nickel (Ni)
  • Sample No. 33 as an example of the present invention is a brass alloy containing a proper amount of titanium (Ti). It can be verified that the tensile strength of these samples is higher than Sample No. 28 as an example of the present invention containing none of these elements.
  • Sample Nos. 25 to 27, 34, and 35 as comparative examples contain iron and chromium, the content ratio of iron to chromium is not in the range of 0.5 to 2, based on mass. Thus, it is recognized that the tensile strength of these samples is higher than Sample No. 19 as a comparative example containing neither iron nor chromium. However, the tensile strength of these elements is lower than the brass alloys as examples of the present invention whose content ratio of iron to chromium is in the range of 0.5 to 2 (Sample Nos. 1 to 5 as examples of the present invention in Table 1, Sample No. 20 as an example of the present invention in Table 3, and Sample No. 28 as an example of the present invention in Table 4).
  • Fig. 1 shows a stress-strain diagram in this tensile test. It can be seen from the figure that Sample Nos. 3 and 5 as examples of the present invention have higher tensile strength and higher endurance strength (yield strength) than Sample No. 19 as a comparative example.
  • Fig. 2 shows the result of structure observation of Sample No. 3 as an example of the present invention by an optical microscope. It can be seen from the figure that Fe-Cr compound particles having a particle size of about 20 to 50 ⁇ m are uniformly dispersed in the brass alloy matrix.
  • Fig. 3 shows the result of scanning electron microscopy-energy dispersive spectroscopy (SEM-EDS) analysis of the brass alloy extruded material of Sample No. 12 as an example of the present invention described in Example 1. It can be seen from the figure that main components of the compound that is dispersed are iron (Fe) and chromium (Cr).
  • Sample No. 5 as an example of the present invention containing none of the elements that improve the cutting property such as bismuth and lead, a hole having a depth of 5 mm was not able to be formed under the above conditions even if the drilling was performed for three minutes.
  • Sample Nos. 6 to 8 as examples of the present invention are brass alloys containing bismuth. In Sample Nos. 6 to 8, a hole was able to be formed, and the processing time decreases as the amount of bismuth is increased.
  • Sample Nos. 9 to 11 as examples of the present invention are alloys containing lead, and the cutting time decreases as the lead content is increased. Thus, it was verified that adding bismuth or lead can significantly improve the cutting property while maintaining high tensile strength.
  • Cast copper alloy ingots containing elements shown in Table 8 were prepared. Each ingot was subjected to a hot extrusion process immediately after heating and keeping the ingot at 650°C. The extrusion process was performed at an extrusion ratio of 37. Tensile test pieces were obtained from each copper alloy extruded material, and a tensile test was conducted at room temperature at a strain rate of 5 ⁇ 10 -4 /s. Regarding evaluation of the cutting property, mean processing time was calculated by a method similar to that of Example 7 described above. The result is shown in Table 8. All of Sample Nos. 40 to 56 are examples of the present invention.
  • copper alloys having high tensile strength, high elongation (ductility), and a high cutting property can be obtained by adding to brass a proper amount of element that improves the strength and a proper amount of element that improves the cutting property.
  • Molten copper alloys containing elements shown in Table 9 were prepared, and powders having a powder particle size of 150 ⁇ m or less (a mean particle size of 112 to 138 ⁇ m) were produced by a water atomizing method. Each powder was heated and pressed (with a pressure of 40 MPa) in a vacuum atmosphere at 750°C by a discharge plasma sintering apparatus to produce a dense sintered compact. Each sintered compact was subjected to a hot extrusion process immediately after heating and keeping (for 15 minutes) the sintered compact at 650°C in a nitrogen gas atmosphere. The extrusion process was performed at an extrusion ratio of 37.
  • copper alloys having high tensile strength, high elongation (ductility), and a high cutting property can be obtained by adding to brass a proper amount of element that improves the strength and a proper amount of element that improves the cutting property.
  • a grain refining effect is additionally provided, and thus the tensile strength of the extruded material is further increased as compared to the case of producing the extrusion ingot by the casting method.
  • the present invention can be advantageously used as a high-strength copper alloy having excellent mechanical characteristics.
  • Table 1 Sample No. 1 2 3 4 5 6 7 8 9 10 11 Zn 39.8 40.2 40.4 39.9 40.0 40.1 39.8 40.0 39.8 40.1 39.9 Fe 0.42 0.63 0.98 1.23 1.41 0.68 0.73 0.70 1.05 1.09 1.06 Cr 0.38 0.58 1.02 1.17 1.38 0.73 0.90 0.97 0.98 1.12 1.19

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EP10767017A 2009-04-24 2010-04-16 Alliage de cuivre à résistance élevée Withdrawn EP2423339A1 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
JP2009106162 2009-04-24
PCT/JP2010/056854 WO2010122960A1 (fr) 2009-04-24 2010-04-16 Alliage de cuivre à résistance élevée

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US (1) US20120027638A1 (fr)
EP (1) EP2423339A1 (fr)
JP (1) JP5326114B2 (fr)
CN (1) CN102361995B (fr)
WO (1) WO2010122960A1 (fr)

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US8580191B2 (en) 2009-12-09 2013-11-12 Xiamen Lota International Co., Ltd. Brass alloys having superior stress corrosion resistance and manufacturing method thereof

Families Citing this family (21)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
KR101340487B1 (ko) * 2011-09-30 2013-12-12 주식회사 풍산 쾌삭성 무연 구리합금 및 이의 제조방법
WO2013099242A1 (fr) * 2011-12-28 2013-07-04 Yazaki Corporation Matériau conducteur ultrafin, conducteur ultrafin, procédé pour la préparation de conducteur ultrafin, et fil électrique ultrafin
CN102865426A (zh) * 2012-09-18 2013-01-09 浙江波士特机械有限公司 用于快速接头上的卡套及其制造方法
CN104942472B (zh) * 2013-01-16 2017-05-03 苏州金仓合金新材料有限公司 一种用于焊接的环保锡锌锰铜合金新材料及其制备方法
CN103834845B (zh) * 2014-03-10 2015-11-11 安徽厚林神雕金属艺术品有限公司 一种艺术品的精密铸造用铜合金的制备方法以及用于精密铸造的方法
CN104513913B (zh) * 2014-11-13 2016-08-24 无锡信大气象传感网科技有限公司 传感器用高强度铜合金材料
US20170050173A1 (en) * 2015-08-19 2017-02-23 The Decaf Company, Llc Programmable mip catch and release technology
CN105296797A (zh) * 2015-11-03 2016-02-03 任静儿 一种抗拉伸铜合金材料
CN105441710A (zh) * 2015-12-25 2016-03-30 苏州露宇电子科技有限公司 核磁共振设备
CN105821241A (zh) * 2016-05-19 2016-08-03 济南大学 一种Nd增强的黄铜合金及其制备工艺
DE202016102696U1 (de) * 2016-05-20 2017-08-29 Otto Fuchs - Kommanditgesellschaft - Sondermessinglegierung sowie Sondermessinglegierungsprodukt
EP3491958B1 (fr) * 2016-07-26 2021-02-17 YKK Corporation Élément de fixation en alliage de cuivre et fermeture à glissière
CN106191512A (zh) * 2016-08-30 2016-12-07 芜湖楚江合金铜材有限公司 一种稀土抗压紧耐磨的铜合金线材及其制备方法
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EP3665313B1 (fr) 2018-10-29 2020-12-09 Otto Fuchs - Kommanditgesellschaft - Alliage de laiton spécial ainsi que produit d'alliage de laiton spécial
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CN115404378B (zh) * 2022-09-30 2023-03-24 宁波金田铜业(集团)股份有限公司 一种耐磨铜合金方棒的制备方法

Family Cites Families (14)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS6036638A (ja) * 1983-08-06 1985-02-25 Ikuo Okamoto 銅合金
JPS6086233A (ja) * 1983-10-14 1985-05-15 Nippon Mining Co Ltd 高力導電銅合金
JP2745696B2 (ja) * 1989-07-03 1998-04-28 三菱マテリアル株式会社 高温で耐摩耗性にすぐれた銅基焼結合金
JP2745699B2 (ja) * 1989-07-14 1998-04-28 三菱マテリアル株式会社 高温で耐摩耗性にすぐれた銅基焼結合金
JPH05230567A (ja) * 1992-02-25 1993-09-07 Mitsubishi Materials Corp 耐熱銅合金
US5370840A (en) * 1992-11-04 1994-12-06 Olin Corporation Copper alloy having high strength and high electrical conductivity
JP3335002B2 (ja) * 1994-05-12 2002-10-15 中越合金鋳工株式会社 熱間加工性に優れた無鉛快削黄銅合金
JP3956322B2 (ja) * 1996-05-30 2007-08-08 中越合金鋳工株式会社 ワンウェイクラッチ用エンドベアリング及びその他の摺動部品
JP3917304B2 (ja) 1998-10-09 2007-05-23 三宝伸銅工業株式会社 快削性銅合金
JP3734372B2 (ja) 1998-10-12 2006-01-11 三宝伸銅工業株式会社 無鉛快削性銅合金
JP4296344B2 (ja) * 2003-03-24 2009-07-15 Ｄｏｗａメタルテック株式会社 銅合金材
JP4190570B2 (ja) 2005-07-28 2008-12-03 サンエツ金属株式会社 無鉛快削性銅合金押出材
JP2008001964A (ja) * 2006-06-26 2008-01-10 Chuetsu Metal Works Co Ltd バルブプレートの製造方法
JP5036623B2 (ja) * 2008-05-15 2012-09-26 Ｄｏｗａメタルテック株式会社 コネクタ用銅合金およびその製造法

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
See references of WO2010122960A1 *

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US8580191B2 (en) 2009-12-09 2013-11-12 Xiamen Lota International Co., Ltd. Brass alloys having superior stress corrosion resistance and manufacturing method thereof

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WO2010122960A1 (fr) 2010-10-28
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CN102361995A (zh) 2012-02-22
CN102361995B (zh) 2014-09-03
US20120027638A1 (en) 2012-02-02

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