[go: up one dir, main page]

EP1009866A1 - Laiton a l'etain a grain affine - Google Patents

Laiton a l'etain a grain affine

Info

Publication number
EP1009866A1
EP1009866A1 EP98912110A EP98912110A EP1009866A1 EP 1009866 A1 EP1009866 A1 EP 1009866A1 EP 98912110 A EP98912110 A EP 98912110A EP 98912110 A EP98912110 A EP 98912110A EP 1009866 A1 EP1009866 A1 EP 1009866A1
Authority
EP
European Patent Office
Prior art keywords
alloy
iron
copper alloy
zinc
weight
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Withdrawn
Application number
EP98912110A
Other languages
German (de)
English (en)
Other versions
EP1009866A4 (fr
Inventor
Dennis R. Brauer
John F. Breedis
Ronald N. Caron
Carl Deepisch
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Olin Corp
Original Assignee
Olin Corp
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Priority claimed from US08/844,478 external-priority patent/US5853505A/en
Application filed by Olin Corp filed Critical Olin Corp
Publication of EP1009866A1 publication Critical patent/EP1009866A1/fr
Publication of EP1009866A4 publication Critical patent/EP1009866A4/fr
Withdrawn legal-status Critical Current

Links

Classifications

    • 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

Definitions

  • This invention relates to copper alloys having high strength, good formability and relatively high electrical conductivity. More particularly, grain refinement of a tin brass is obtained by a controlled addition of iron, cobalt or other element that initiates a peritectic reaction during solidification.-.
  • tin brasses are copper alloys containing from 0.35%-4% tin, up to 0.35% phosphorous, from 49% to 96% copper and the balance zinc.
  • the alloys are designated by the Copper Development Association (CDA) as copper alloys C40400 through C49080.
  • One commercial tin brass is a copper alloy designated as C42500.
  • the alloy has the composition 87%-90% of copper, 1.5%-3.0% of tin, a maximum of 0.05% of iron, a maximum of 0.35% phosphorous and the balance zinc.
  • the products formed from this alloy are electrical switch springs, terminals, connectors, fuse clips, pen clips and weather stripping.
  • the ASM Handbook specifies copper alloy C42500 as having a nominal electrical conductivity of 28% IACS (International Annealed Copper Standard where "pure” copper is assigned a conductivity value of 100% IACS at 20 °C) and a yield strength, dependent on temper, of between 45 si and 92 ksi.
  • IACS International Annealed Copper Standard where "pure” copper is assigned a conductivity value of 100% IACS at 20 °C
  • yield strength dependent on temper
  • the maximum permissible iron content, as an impurity is typically 0.05%. This is because iron is known to reduce electrical conductivity and, through the formation of stringers, deteriorate the bend properties.
  • tin brass alloy having increased strength. It is a feature of the invention that the increased strength is achieved by an addition of controlled amounts of a combination of iron and zinc. It is another feature of the invention that by processing the alloy according to a specified sequence of steps, a fine microstructure is retained in the wrought alloy.
  • the yield strength is increased without a degradation in electrical conductivity.
  • the microstructure of a refined as-cast alloy, grain size less than 100 microns, and a wrought alloy, grain size of about 5-20 microns, is fine grain.
  • the electrical conductivity is about equal to that of copper alloy C42500 with a significant increase in yield strength.
  • a copper alloy This alloy consists essentially of from 1 % to 4% by weight of tin, from 0.8% to 4.0% by weight of iron, from an amount effective to enhance iron initiated grain refinement to 20% by weight of zinc, up to 0.4% by weight of phosphorus and the remainder is copper, as well as inevitable impurities.
  • the grain refined alloy has an average as-cast grain size of less than 100 microns and an average grain size after processing of between about 5 and 20 microns.
  • Figure 1 is a flow chart illustrating one method of processing the alloy of the invention.
  • Figure 2 graphically illustrates the effect of iron content on the yield strength.
  • Figure 3 graphically illustrates the effect of iron content on the ultimate tensile strength.
  • Figure 4 graphically illustrates the effect of tin content on the yield strength.
  • Figure 5 graphically illustrates the effect of tin content on the ultimate tensile strength.
  • Figure 6 graphically illustrates the effect of zinc content on the yield strength.
  • Figure 7 graphically illustrates the effect of zinc content on the ultimate tensile strength.
  • the copper alloys of the invention are an iron modified tin brass.
  • the alloys consist essentially of from 1% to 4% of tin, from 0.8% to 4.0% of iron, from 5% to 20% of zinc, up to 0.4% of phosphorus and the remainder is copper along with inevitable impurities.
  • the grain refined alloy has an average crystalline grain size of less than 100 microns.
  • the tin content is from 1.5% to 2.5% and the iron content is from 1.6% to 2.2%. 1.6% of iron has been found to be a critical minimum to achieve as-cast grain refinement. Most preferably, the iron content is from 1.6% to 1.8%.
  • Tin increases the strength of the alloys of the invention and also increases the resistance of the alloys to stress relaxation.
  • the resistance to stress relaxation is recorded as percent stress remaining after a strip sample is preloaded to 80% of the yield strength in a — cantilever mode per ASTM (American Society for Testing and Materials) specifications.
  • the strip is heated to 125°C for the specified number of hours and retested periodically.
  • the properties were measured at up to 3000 hours at 125 °C. The higher the stress remaining, the better the utility of the specified composition for spring applications.
  • the tin content of the alloys of the invention is from about
  • the refined microstructure is characterized by an average grain size of less than 100 microns.
  • the average grain size is from 30 to 90 microns and most preferably, from 40 to 70 microns.
  • This refined microstructure facilitates mechanical deformation at elevated temperatures, such as rolling at 850 °C.
  • the iron content is less than about 1.6%, the grain refining effect is reduced and coarse crystalline grains, with an average grain size on the order of 600-2000 microns, develop.
  • the iron content exceeds 2.2%, excessive amount of stringers develop during hot working.
  • the effective iron range 1.6%-2.2%, differs from the iron range of the alloys disclosed in EP 0769563 A 1 that discloses that grain refinement was not optimized until the iron content exceeded about 2%.
  • the ability to refine the grain structure at lower iron contents in the alloys of the present invention was unexpected and believed due to a phase equilibrium shift due to the inclusion of zinc. To be effective, this phase shift interaction requires a minimum zinc content of about 5%.
  • Large stringers having a length in excess of about 200 microns, are expected to form when the iron content exceeds about 2.2%.
  • the large stringers impact both the appearance of the alloy surface as well as the properties, electrical and chemical, of the surface.
  • the large stringers can change the solderability and electro-platability of the alloy.
  • the iron content should be maintained between about 1.6% and 2.2% and preferably, between about 1.6% and 1.8%.
  • the zinc content is from that effective to enhance iron initiated grain refinement to about 20%. More preferably, the zinc content is from about 5% to about 15% and most preferably, the zinc content is from about 8% to about 12%.
  • Cobalt is a suitable substitute for either a portion, or all, of the iron as shown in Table 4.
  • the cobalt content when used as the primary grain refiner, should be in excess of about 3.0%.
  • the cobalt content is between about 3.2% and 4.4% and most preferably from between 3.2% and 3.6%. Excessive amounts of cobalt should be avoided because coarse stringers of excess properitectic cobalt particles may occur and degrade alloy properties.
  • Cobalt may be added as a partial substitute for iron. Cobalt less effectively refines the grain structure of the alloys of the invention and the substitution should satisfy the equation:
  • Fe+MCo iron ranges specified above.
  • M is between 0.45 and 0.65, and preferably from 0.5 to 0.6. Most preferably, the substitution is in the higher range, about 0.6 for lower contents of cobalt and about 0.5 for higher contents of cobalt with an approximate delineation between the lower contents and the higher contents being a 2% cobalt.
  • Suitable properitectic particle formers include iridium in an amount of from about 10% to about 20% and preferably in an amount of from about 1 1% to 15%; niobium in an amount of from about 0.01% to about 5% and preferably in an amount of from about 0.1 % to about 1 %; vanadium in an amount of from about 0.01% to about 5% and preferably in an amount of from about 0.1% to about 1%; and molybdenum in an amount of from about 0.5% to about 5% and preferably in an amount of from about 1% to about 3%.
  • peritectic reaction initiators may substitute, in whole or in part, for cobalt or iron.
  • Phosphorous is added to the alloy for conventional reasons, to prevent the formation of copper oxide or tin oxide precipitates and to promote the formation of iron phosphides. Phosphorous causes problems with the processing of the alloy, particularly with hot rolling. It is believed that the iron addition counters the detrimental impact of phosphorous. At least a minimal amount of iron must be present to counteract the impact of the phosphorous.
  • a suitable phosphorous content is any amount up to about 0.4%.
  • a preferred phosphorous content is from about 0.03% to 0.3%.
  • additions of elements that affect the properties of the alloy are less preferred.
  • additions such as nickel, magnesium, beryllium, silicon, zirconium, titanium, chromium and mixtures thereof may be included.
  • the less preferred additions are preferably present in an amount of less than about 0.4% and most preferably, in an amount of less than about
  • the sum of all less preferred alloying additions is less than about 0.5%.
  • the alloys of the invention are preferably processed according to the flow chart illustrated in Figure 1.
  • An ingot being an alloy of a composition specified herein, is cast 10 by a conventional process such direct chill casting.
  • the alloy is hot rolled 12, at a temperature of from about 650°C to about 950°C and preferably, at a temperature of between about 825 °C and 875 °C.
  • the alloy is heated 14 to maintain the desired hot roll 12 temperature.
  • the hot rolling reduction is, typically, by thickness, up to 98% and preferably, from about 80% to about 95%.
  • the hot rolling may be in a single pass or in multiple passes, provided that the temperature of the ingot is maintained at above 650 °C.
  • the alloy is, optionally, water quenched 16.
  • the bars are then mechanically milled to remove surface oxides and then cold rolled 18 to a reduction of at least 60%, by thickness, from the gauge at completion of the hot roll step 12, in either one or multiple passes.
  • the cold roll reduction 18 is from about 60%-90%.
  • the strip is then annealed 20 at a temperature between about 400 °C and about 600 °C for a time of from about 0.5 hour to about 8 hours to recrystallize the alloy.
  • this first recrystallization anneal is at a temperature between about 500°C and about 600°C for a time between 3 and 5 hours. These times are for bell annealing in an inert atmosphere such as nitrogen or in a reducing atmosphere such as a mixture of hydrogen and nitrogen.
  • the strip may also be strip annealed, such as for example, at a temperature of from about 600°C to about 950°C for from 0.5 minute to 10 -- minutes.
  • the first recrystallization anneal 20 causes additional precipitates of iron and iron phosphide to develop. These precipitates control the grain size during this and subsequent anneals, add strength to the alloy via dispersion hardening and increase electrical conductivity by drawing iron out of solution from the copper matrix.
  • the bars are then cold rolled 22 a second time to a thickness reduction of from about 30% to about 70% and preferably of from about 35% to about 45%.
  • the strip is then given a second recrystallization anneal 24, utilizing the same times and temperatures as the first recrystallization anneal.
  • the average grain size is between 3 and 20 microns.
  • the average grain size of the processed alloy is from 5 to 10 microns.
  • the alloys are then cold rolled 26 to final gauge, typically on the order of between 0.25 mm (0.010 inch) and 0.38 mm (0.015 inch). This final cold roll imparts a spring temper comparable to that of copper alloy C51000.
  • the alloys are then relief annealed 28 to optimize resistance to stress relaxation.
  • One exemplary relief anneal is a bell anneal in an inert atmosphere at a temperature of between about 200°C and about 300°C for from 1 to 4 hours.
  • a second exemplary relief anneal is a strip anneal at a temperature of from about 250°C to about 600°C for from about 0.5 minutes to about 10 minutes.
  • the copper alloy strip is formed into a desired product such as a spring or an electrical connector.
  • Copper alloys containing 10.5% zinc, 1.7% tin, 0.04% phosphorous, between 0% and 2.3% iron and the balance copper were prepared according to the process of Figure 1. Following the relief anneal 28, the yield strength and the ultimate tensile strength of sample coupons, 51 mm (2 inch) gauge length, were measured at room temperature (20 °C).
  • the 0.2% offset yield strength and the tensile strength were measured on a tension testing machine (manufactured by Tinius Olsen, Willow Grove, PA).
  • Figure 3 graphically illustrates a similar relationship between the iron content and the ultimate tensile strength.
  • Copper alloys containing 10.4% zinc, 1.8% iron, 0.04% phosphorous, between 1.8% and 4.0% tin and the balance copper were processed according to Figure 1.
  • Test coupons in the relief anneal condition 28, were evaluated for yield strength and ultimate tensile strength.
  • Figure 4 graphically illustrates that increasing the tin content leads to an increase in yield strength. While Figure 5 graphically illustrates the same effect from tin additions for the ultimate tensile strength. Since the strength increase is monatomic with the amount of tin while the conductivity decreases, the tin content should be a trade-off between desired strength and conductivity.
  • Example 3 Copper alloys containing 1.9% iron, 1.8% tin, 0.04% phosphorous, between 0% and 15% zinc and the balance copper were processed according to Figure 1.
  • Test coupons in the relief anneal condition 28, were evaluated for yield strength and ultimate tensile strength.
  • Figure 6 graphically illustrates that a zinc content of less than about 5% does not contribute to the strength of the alloy, and as discussed above, does not enhance the grain refining capability of the iron. Above 5% zinc, the alloy strength is increased, although a decrease in electrical conductivity is experienced.
  • Figure 7 graphically illustrates the same effect from zinc additions for the ultimate tensile strength of the alloy.
  • Example 4 Table 5 illustrates a series of alloys processed according to Figure 1.
  • Alloy A is an alloy of the type disclosed in EP 0769563 Al. Alloys B and C are in accordance with the present invention and alloy D is conventional copper alloy C510. All properties were measured when the alloy was in a spring temper following a 70% cold roll reduction in thickness. Table 5
  • Table 5 shows that the addition of 5% zinc did not increase the strength of the alloy and slightly reduced electrical conductivity. A 10% zinc addition had a favorable impact on the strength.
  • % Red. percent reduction in thickness at the final cold step (reference numeral 26 in Figure 5).
  • YS Yield strength in MPa and (ksi).
  • MBR t (GW) Good way bends about a 180° radius of curvature.
  • MBR/t (BW) Bad way bends about a 180° radius of curvature.
  • a further benefit of the zinc addition is the improved good way bends achieved with alloy C. Bend formability was measured by bending a 12.7 mm (0.5 inch) wide strip 180° about a mandrel having a known radius of curvature. The minimum mandrel about which the strip could be bent without cracking or "orange peeling" is the bend formability value. The "good way” bend is made in the plane of the sheet and perpendicular to the longitudinal axis (rolling direction) during thickness reduction of the strip. "Bad way” is parallel to the longitudinal axis. Bend formability is recorded as MBR/t, the minimum bend radius at which cracking or orange peeling in not apparent, divided by the thickness of the strip.
  • Table 7 shows the effectiveness of cobalt as a partial substitute for iron in the tin brass alloys of the invention.
  • the alloys of the invention may be cast by other processes as well.
  • Some of the alternative processes have higher cooling rates such as spray casting and strip casting. The higher cooling rates reduce the size of the properitectic iron particles and are believed to shift the critical maximum iron content to a higher value such as 4%.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Conductive Materials (AREA)

Abstract

L'invention concerne un alliage de laiton à l'étain dont la structure granulaire est affinée par l'addition de quantités contrôlées de zinc et de fer. D'autres éléments métalliques subissant une décomposition péritectique dans un alliage de laiton à l'étain, tel que le cobalt, l'iridium, le niobium, le vanadium et le molybdène, peuvent remplacer une partie ou la totalité du fer. Les alliages coulés par refroidissement intense et direct, qui contiennent 1 à 4 % en poids d'étain, 0,8 à 4 % de fer, du zinc en une quantité comprise entre une quantité efficace pour améliorer l'affinage des grains amorcé par le fer et 20 %, le cuivre restant et les impuretés inévitables, sont immédiatement déformés à chaud. L'addition de zinc augmente la résistance de l'alliage et son aptitude à une déformation par flexion 'correcte', c'est-à-dire perpendiculaire à l'axe longitudinal de la bande laminée.
EP98912110A 1997-04-18 1998-03-30 Laiton a l'etain a grain affine Withdrawn EP1009866A4 (fr)

Applications Claiming Priority (5)

Application Number Priority Date Filing Date Title
US08/844,478 US5853505A (en) 1997-04-18 1997-04-18 Iron modified tin brass
US844478 1997-04-18
US885930 1997-06-30
US08/885,930 US20010001400A1 (en) 1997-04-18 1997-06-30 Grain refined tin brass
PCT/US1998/006157 WO1998048068A1 (fr) 1997-04-18 1998-03-30 Laiton a l'etain a grain affine

Publications (2)

Publication Number Publication Date
EP1009866A1 true EP1009866A1 (fr) 2000-06-21
EP1009866A4 EP1009866A4 (fr) 2002-02-06

Family

ID=27126508

Family Applications (1)

Application Number Title Priority Date Filing Date
EP98912110A Withdrawn EP1009866A4 (fr) 1997-04-18 1998-03-30 Laiton a l'etain a grain affine

Country Status (8)

Country Link
US (1) US20010001400A1 (fr)
EP (1) EP1009866A4 (fr)
JP (1) JP2001522404A (fr)
KR (1) KR20010006488A (fr)
CN (1) CN1086207C (fr)
AU (1) AU6590698A (fr)
CA (1) CA2287440A1 (fr)
WO (1) WO1998048068A1 (fr)

Families Citing this family (17)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE19919196C1 (de) * 1999-04-28 2000-12-14 Henkel Kgaa Zahnbürste
KR100576141B1 (ko) * 2003-03-03 2006-05-03 삼보신도고교 가부기키가이샤 내열성 동합금재 및 그 제조방법
US20080147118A1 (en) * 2006-12-15 2008-06-19 Cichocki Frank R Tungsten alloy suture needles with surface coloration
CN102784982A (zh) * 2011-05-20 2012-11-21 昆山市瑞捷精密模具有限公司 快走丝电火花加工用钼铜合金电极线及其制备方法
CN102784981A (zh) * 2011-05-20 2012-11-21 昆山市瑞捷精密模具有限公司 慢走丝电火花线切割金属丝及其制备方法
CN102784979A (zh) * 2011-05-20 2012-11-21 昆山市瑞捷精密模具有限公司 快走丝电火花加工用金属丝及其制备方法
CN102784980A (zh) * 2011-05-20 2012-11-21 昆山市瑞捷精密模具有限公司 一种快走丝电火花线切割钼合金电极丝
CN102784978A (zh) * 2011-05-20 2012-11-21 昆山市瑞捷精密模具有限公司 慢走丝电火花线切割铜合金电极线及其制备方法
CN102806392A (zh) * 2011-05-30 2012-12-05 昆山市瑞捷精密模具有限公司 铜锌合金电火花线切割用皮芯结构丝材
CN102806394A (zh) * 2011-05-30 2012-12-05 昆山市瑞捷精密模具有限公司 钼铜合金电火花线切割用皮芯结构丝材
TWI591192B (zh) * 2011-08-13 2017-07-11 Wieland-Werke Ag Copper alloy
DE102012002450A1 (de) * 2011-08-13 2013-02-14 Wieland-Werke Ag Verwendung einer Kupferlegierung
CN103031466B (zh) * 2013-01-10 2015-04-15 宁波博威合金材料股份有限公司 一种锡黄铜合金及其制造方法
US10287653B2 (en) 2013-03-15 2019-05-14 Garrett Transportation I Inc. Brass alloys for use in turbocharger bearing applications
CN104032170A (zh) * 2014-05-12 2014-09-10 蚌埠市宏威滤清器有限公司 一种易切削黄铜合金材料及其制备方法
KR101830841B1 (ko) * 2016-11-29 2018-02-22 한국생산기술연구원 고내마모성을 갖는 싱크로나이저 링용 동합금 및 이의 제조방법
CN113106291B (zh) * 2021-03-23 2022-04-26 宁波金田铜业(集团)股份有限公司 一种综合性能优异的锡磷青铜带材及其制备方法

Family Cites Families (13)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
GB2179673A (en) * 1985-08-23 1987-03-11 London Scandinavian Metall Grain refining copper alloys
JP2555067B2 (ja) * 1987-04-24 1996-11-20 古河電気工業株式会社 高力銅基合金の製造法
JP2605833B2 (ja) * 1988-10-17 1997-04-30 三菱マテリアル株式会社 Ｃｕ系焼結合金製変速機同期リング
JPH02163331A (ja) * 1988-12-15 1990-06-22 Nippon Mining Co Ltd 酸化膜密着性に優れた高力高導電性銅合金
JPH03111529A (ja) * 1989-09-26 1991-05-13 Nippon Mining Co Ltd 高強度耐熱性ばね用銅合金
JPH03162536A (ja) * 1989-11-22 1991-07-12 Nippon Mining Co Ltd めっき耐熱剥離性を改善した高力高導電銅合金
JPH03193849A (ja) * 1989-12-22 1991-08-23 Nippon Mining Co Ltd 結晶粒が微細でかつ低強度な銅合金及びその製造方法
JPH04231443A (ja) * 1990-12-27 1992-08-20 Nikko Kyodo Co Ltd 通電材料
JPH059619A (ja) * 1991-07-08 1993-01-19 Furukawa Electric Co Ltd:The 高力銅合金の製造方法
JP2599526B2 (ja) * 1992-02-03 1997-04-09 新日本製鐵株式会社 特性異方性の小さいバネ限界値と強度に優れた銅−鉄系金属薄板およびその製造方法
JP2501275B2 (ja) * 1992-09-07 1996-05-29 株式会社東芝 導電性および強度を兼備した銅合金
JPH06299275A (ja) * 1993-04-12 1994-10-25 Mitsubishi Shindoh Co Ltd 高強度を有する電気電子機器の構造部材用Ｃｕ合金
JP3335224B2 (ja) * 1993-08-27 2002-10-15 清仁 石田 高加工性銅系形状記憶合金の製造方法

Also Published As

Publication number Publication date
CN1086207C (zh) 2002-06-12
WO1998048068A1 (fr) 1998-10-29
KR20010006488A (ko) 2001-01-26
JP2001522404A (ja) 2001-11-13
HK1026925A1 (en) 2000-12-29
US20010001400A1 (en) 2001-05-24
AU6590698A (en) 1998-11-13
EP1009866A4 (fr) 2002-02-06
CN1255167A (zh) 2000-05-31
CA2287440A1 (fr) 1998-10-29

Similar Documents

Publication Publication Date Title
US5565045A (en) Copper base alloys having improved bend formability
EP0908526B1 (fr) Alliage de cuivre et procédé pour sa production
US4605532A (en) Copper alloys having an improved combination of strength and conductivity
US6471792B1 (en) Stress relaxation resistant brass
US5370840A (en) Copper alloy having high strength and high electrical conductivity
US5985055A (en) Copper alloy and process for obtaining same
US6132528A (en) Iron modified tin brass
JP4177104B2 (ja) 曲げ加工性に優れた高強度銅合金及びその製造方法及びそれを用いた端子・コネクタ
WO1998048068A1 (fr) Laiton a l'etain a grain affine
KR20060073490A (ko) 구부림성 및 응력완화성을 갖는 구리 합금
US5853505A (en) Iron modified tin brass
US5882442A (en) Iron modified phosphor-bronze
US5508001A (en) Copper based alloy for electrical and electronic parts excellent in hot workability and blankability
US6379478B1 (en) Copper based alloy featuring precipitation hardening and solid-solution hardening
JP4664584B2 (ja) 高強度銅合金板および高強度銅合金板の製造方法
CA1119920A (fr) Alliages spinoidaux a base de cuivre
EP1021575B1 (fr) Alliage au cuivre presentant des caracteristiques de trempe structurale et de durcissement en solution solide
US5865910A (en) Copper alloy and process for obtaining same
JP2007107062A (ja) 電子材料用Ｃｕ−Ｎｉ−Ｓｉ系銅合金
JPH0559974B2 (fr)
EP1264905A2 (fr) Alliage au cuivre présentant des caractéristiques de trempe structurale et de durcissement en solution solide
US4606889A (en) Copper-titanium-beryllium alloy
CN112048637A (zh) 一种铜合金材料及其制造方法
JPH0219434A (ja) ワイヤーハーネスのターミナル用銅基合金
MXPA00002305A (en) Copper based alloy featuring precipitation hardening and solid-solution hardening

Legal Events

Date Code Title Description
PUAI Public reference made under article 153(3) epc to a published international application that has entered the european phase

Free format text: ORIGINAL CODE: 0009012

17P Request for examination filed

Effective date: 19991015

AK Designated contracting states

Kind code of ref document: A1

Designated state(s): CH DE FR GB IT LI SE

A4 Supplementary search report drawn up and despatched

Effective date: 20011221

AK Designated contracting states

Kind code of ref document: A4

Designated state(s): CH DE FR GB IT LI SE

17Q First examination report despatched

Effective date: 20030318

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: THE APPLICATION IS DEEMED TO BE WITHDRAWN

18D Application deemed to be withdrawn

Effective date: 20040205