EP1508625B1 - Kupferlegierung, die exzellente Korrosionsbeständigkeit und Entzinkungsbeständigkeit aufweist, und eine Methode zu deren Herstellung - Google Patents

Kupferlegierung, die exzellente Korrosionsbeständigkeit und Entzinkungsbeständigkeit aufweist, und eine Methode zu deren Herstellung Download PDF

Info

Publication number
EP1508625B1
EP1508625B1 EP03018581A EP03018581A EP1508625B1 EP 1508625 B1 EP1508625 B1 EP 1508625B1 EP 03018581 A EP03018581 A EP 03018581A EP 03018581 A EP03018581 A EP 03018581A EP 1508625 B1 EP1508625 B1 EP 1508625B1
Authority
EP
European Patent Office
Prior art keywords
zinc
resistance
copper
copper alloy
content
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.)
Expired - Lifetime
Application number
EP03018581A
Other languages
English (en)
French (fr)
Other versions
EP1508625A1 (de
Inventor
Yoshinori Yamagishi
Shu-Xin Dong
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.)
Dowa Holdings Co Ltd
Original Assignee
Dowa Holdings Co Ltd
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
Application filed by Dowa Holdings Co Ltd filed Critical Dowa Holdings Co Ltd
Priority to AT03018581T priority Critical patent/ATE353981T1/de
Priority to EP03018581A priority patent/EP1508625B1/de
Priority to DE60311803T priority patent/DE60311803T2/de
Publication of EP1508625A1 publication Critical patent/EP1508625A1/de
Application granted granted Critical
Publication of EP1508625B1 publication Critical patent/EP1508625B1/de
Anticipated expiration legal-status Critical
Expired - Lifetime 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
    • 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 generally relates to a copper alloy and a method for producing the same. More specifically, the invention relates to a copper alloy having an excellent corrosion cracking resistance and an excellent dezincing resistance, in addition to characteristics of conventional brasses having an excellent machinability or cutting workability and an excellent recyclability, and a method for producing the same.
  • Japanese Patent Laid-Open No. 10-183275 discloses that tin (Sn) is added to a copper-zinc alloy to be extruded to control the concentration of Sn in a gamma phase through various heat treatments to improve the dezincing resistance of the alloy.
  • Japanese Patent Laid-Open No. 6-108184 proposes that Sn is added to a copper-zinc alloy to be extruded to form a single alpha phase to enhance the dezincing corrosion resistance of the alloy. That is, the above described alloys are characterized in that a larger amount of Sn than that in conventional brasses is added.
  • Japanese Patent Laid-Open No. 2001-294956 proposes that very small amounts of phosphorus (P) and tin (Sn) are added to a copper-zinc alloy to be extruded and reduced to be heat-treated to form a structure wherein a beta phase is separated by an alpha phase, to improve the dezincing resistance of the alloy.
  • EP 1 008 664 A1 discloses a copper-based alloy comprising 58 to 63 % of copper, 0.5 to 4.0 % of lead, 0.05 to 0.25 % of phosphorus, 0.5 to 3.0 % of tin and 0.05 to 0.3 % of nickel, with the balance being zinc and unavoidable impurities.
  • the method for adding the very small amounts of Sn and P to carry out heat treatments can be inexpensively carried out to improve the dezincing resistance due to the small amount of additives.
  • this method can not improve the stress corrosion cracking resistance of the alloy.
  • the inventors have diligently studied and found that it is possible to provide a copper alloy having an excellent corrosion cracking resistance and an excellent dezincing resistance while maintaining excellent characteristics of conventional brasses, by adding appropriate amounts of tin (Sn), silicon (Si), phosphorus (P), and at least one of bismuth (Bi) and lead (Pb), and optionally at least one of nickel (Ni) and iron (Fe) to a conventional brass material and by carrying out a heat treatment on appropriate conditions to control the structure of the alloy.
  • tin tin
  • Si silicon
  • P phosphorus
  • Pb bismuth
  • Pb bismuth
  • Fe nickel
  • the inventors have made the present invention.
  • a copper alloy comprises 58 to 66 wt% of copper, 0.3 to 0.5 wt% of tin, 0.01 to 0.5 wt% of silicon 0.02 to 0.15 wt% of phosphorus at least one of 0.3 to 3.0 wt% of bismuth and 0.3 to 3.5 wt% of lead, and optionally at least one of 0.02 to 3.0 wt% of nickel and 0.02 to 0.6 wt% of iron, with the balance being zinc and unavoidable impurities, wherein a proportion of an alpha phase is 80 vol% or more.
  • the total amount of phosphorus, nickel and iron may be in the range of from 0.02 to 3.0 wt%.
  • a method for producing a copper alloy comprising the steps of: preparing raw materials of a copper alloy comprising 58 to 66 wt% of copper, 0.3 to 0.5 wt% of tin, 0.01 to 0.5 wt% of silicon, 0.02 to 0.15 wt% of phosphorus at least one of 0.3 to 3.0 wt% of bismuth and 0.3 to 3.5 wt% of lead, and optionally at least one of 0.02 to 3.0 wt% of nickel and 0.02 to 0.6 wt% of iron, with the balance being zinc and unavoidable impurities; casting the raw materials to form an ingot; hot working the ingot; cold or hot working the hot worked ingot; annealing the cold or hot worked ingot at a temperature of 300 to 600 °C for two minutes to five hours; and cooling the annealed ingot at a cooling rate of 0.2 to 10 °C/sec.
  • the total amount of phosphorus, nickel and iron may be in the range of from 0.02 to 3.0 wt%.
  • a copper alloy having an excellent corrosion cracking resistance and an excellent dezincing resistance consists of 58 to 66 wt% of copper (Cu), 0.3 to 0.5 wt% of Sn, 0.01 to 0.5 wt% of Si, 0.02 to 0.15 wt% of P, at least one of 0.3 to 3.0 wt% of Bi and 0.3 to 3.5 wt% of Pb, and optionally at least one of 0.02 to 3.0 wt% of Ni and 0.02 to 0.6 wt% of FE, with the balance being zinc (Zn) and unavoidable impurities, wherein the proportion of an alpha phase is 80 vol% or more.
  • the amount of Cu is less than 58 wt%, a beta phase increases, so that it is not possible to improve the dezincing resistance of the alloy even if a heat treatment is subsequently carried out.
  • the amount of Cu exceeds 66 wt%, a beta phase does not sufficiently deposit even in a high temperature range, so that the hot workability of the alloy deteriorates. Therefore, the amount of Cu is preferably in the range of from 58 to 66 wt%, more preferably in the range of from 60 to 62 wt%.
  • Tin (Sn) has the function of improving the dezincing resistance of an alpha phase and a beta phase. If the amount of Sn is less than 0.3 wt%, it is not possible to obtain a satisfied dezincing resistance. If the amount of Sn exceeds 0.5 wt%, a hard, friable gamma phase is easy to deposit, so that the extension of mechanical characteristics deteriorates. Therefore, the amount of Sn is in the range of from 0.3 to 0.5 wt%.
  • Silicon (Si) remarkably has the functions of improving the dezincing resistance of a beta phase and of improving the stress corrosion cracking resistance of the whole alloy if a predetermined proportion of Si is solid-dissolved in beta and alpha phases. If the amount of Si is less than 0.01 wt%, these functions can not be obtained. Since the zinc equivalent of Si is a high value of 10, if the amount of Si to be added exceeds 0.5 wt%, the proportion of a beta phase increases, and the extension of mechanical characteristics deteriorates. Therefore, the amount of Si is preferably in the range of 0.01 to 0.5 wt%, more preferably in the range of 0.1 to 0.2 wt%.
  • a third element such as Sn, Si or Ni
  • a third element such as Sn, Si or Ni
  • it is often solid-dissolved in alpha and beta phases without forming a specific phase.
  • the amount of Zn increases or decreases is produced in the copper-zinc alloy, so that the alloy has properties corresponding thereto.
  • Guillet has proposed a method for expressing this relationship by using the zinc equivalent of an additional element.
  • the proportion of an alpha phase is 80 vol% or more, advantageous effects will be described below.
  • the beta phase is inferior to the alpha phase with respect to both of stress corrosion cracking resistance and dezincing resistance.
  • the zinc equivalents of Sn and Si are 2 and 10, respectively, and the solid solutions of Sn and Si are preferentially formed in a beta phase. If the amount of these elements to be added increases, the proportion of the beta phase increases, and the hardness of the whole material increases to decrease the elongation thereof.
  • the proportion of the alpha phase is set to be 80 vol% or more, the residual beta phase can be reinforced by adding a very small amount of elements without damaging the elongation of the whole material, and the stress corrosion cracking resistance of the alpha phase can be improved by the solid solution of Si. Therefore, the proportion of the alpha phase is preferably 80 vol% or more, and more preferably 90 vol% or more.
  • a copper alloy having an excellent stress corrosion cracking resistance and dezincing resistance contains at least one of 0.3 to 3.5 wt% of Pb and 0.3 to 3.0 wt% of Bi.
  • Pb and Bi serve to improve the machinability or cutting workability of brasses, respectively. If the amount of Pb is 0.3 wt% or more, it is possible to obtain a good free-cutting workability. However, if the amount of Pb exceeds 3.5 wt%, the mechanical properties of brasses deteriorate to tend to cause embrittlement. Therefore, the amount of Pb is preferably in the range of from 0.3 to 3.5 wt%. In addition, since the material cost of Pb is low, the amount of Pb is more preferably in the range of 2.5 to 3.5 wt%.
  • the amount of Bi is in the range of from 0.3 to 3.0 wt%, preferably in the range of from 1.4 to 2.5 wt%, it is possible to obtain a good free-cutting workability. Since Pb is harmful to the human body although Bi is more expensive than Pb, Bi can be substituted for Pb.
  • a copper alloy having an excellent stress corrosion cracking resistance and dezincing resistance preferably contains at least one of 0.02 to 0.15 wt% of P, 0.02 to 3.0 wt% of Ni, and 0.02 to 0.6 wt% of Fe, the total amount of these elements being in the range of from 0.02 to 3.0 wt%.
  • Nickel (Ni) has the function of decreasing the size of crystal grains, and also has the function of increasing the proportion of the alpha phase since the zinc equivalent of Ni is negative. If the amount of Ni is less than 0.02 wt%, it is not sufficiently obtain these functions. On the other hand, if the amount of Ni exceeds 3.0 wt%, there are problems on mechanical characteristics and adding costs. Therefore, the amount of Ni is preferably in the range of 0.02 to 3.0 wt%, and more preferably in the range of 0.1 to 0.4 wt%.
  • Phosphorus (P) has the function of improving the dezincing resistance of the alpha phase without damaging mechanical characteristics. However, if the amount of P is less than 0.02 wt%, it is not possible to obtain such a function, and if the amount of P exceeds 0.15 wt%, intergranular segregation is caused to deteriorate the ductility and stress corrosion cracking resistance of the alloy. Therefore, the amount of P to be added is in the range of from 0.02 to 0.15 wt%.
  • Iron has the functions of inhibiting the size of the alpha phase from being increased and of stabilizing mechanical characteristics. Since most of scrap materials include Fe, costs increase if the amount of Fe is less than 0.02 wt%, and the elongation of the alloy deteriorates if the amount of Fe exceeds 0.6 wt%. Therefore, the amount of Fe to be added is preferably in the range of from 0.02 to 0.6 wt%.
  • the total amount of Ni, Fe and P is preferably in the range of from 0.02 to 3.0 wt%, and more preferably in the range of from 0.05 to 0.5 wt%.
  • the mixture is cast to form an ingot, it is extruded in a temperature range of from 600 to 850 °C.
  • a temperature range of from 600 to 850 °C By the mixing, it is possible to obtain an alpha-plus-beta phase structure having a good hot workability in a high temperature region.
  • the bar After the hot forging or cold reduction of a bar thus obtained is carried out, the bar is heat-treated at a temperature of 300 to 600 °C for two minutes to five hours, and then cooled at a cooling rate of 0.2 to 10 °C/sec to control the structure.
  • the beta phase portion after extruding is changed to an alpha or gamma phase except for a part of the beta phase portion.
  • the concentration of additives in the residual beta phase increases, and the solid solution of Si is formed in the alpha phase, so that the stress corrosion cracking resistance and dezincing resistance of the bar are improved.
  • the heat treatment temperature is lower than 300 °C, phase transformation is not sufficiently carried out.
  • the heat treatment temperature is higher than 600 °C, the beta phase is stable, so that no alpha-plus-gamma phase is deposited. Therefore, the heat treatment temperature is preferably in the range of from 300 to 600 °C.
  • the cooling rate is higher than 10 °C/sec, there is the possibility that distortion may be caused by cooling.
  • the cooling rate is lower than 0.2 °C /sec, there are some cases where the size of crystal grains increases to have an influence on dezincing resistance. Therefore, the cooling temperature is preferably in the range of from 0.2 to 10 °C/sec.
  • Raw materials of components in each of Examples 1 through 19 shown in Table 1 were mixed to be melted in an induction furnace to be semi-continuously cast to form a bar having a diameter of 80 mm. Then, the bar was hot-extruded so as to have a diameter of 30 mm, and cold-drawn so as to have a diameter of 29.5 mm. Thereafter, in each example, the bar was heat-treated on heat treatment conditions shown in Table 2, and the cooling rate was in the range of from 0.2 to 10 °C/sec.
  • the proportion of the alpha phase was obtained by the point calculating method on a microphotograph of a cross section (see "Handbook of Metals” (edited by Japan Society for Metals, the revised fifth edition, Maruzen), p 289). Furthermore, 23 x 30 points were measured at intervals of 10 ⁇ m in a lattice.
  • the dezincing resistance was evaluated on the basis of ISO 6509 by observing the depth of dezincing resistance after the sample was dipped in a solution containing 12.7 g/L of CuCl 2 ⁇ 2H 2 O at a temperature of 75 ⁇ 3 °C for 24 hours. The sample was tested so that the direction of extruding was coincident with the direction of dezincing corrosion. After the region of 10 mm x 10 mm was measured, the dezincing resistance was evaluated as "good” when the maximum dezincing depth was 100 ⁇ m or less, and the dezincing resistance was evaluated as "not bad” when the maximum dezincing depth exceeds 100 ⁇ m.
  • each of the samples before cold drawing was cut into pieces having a thickness of 1.5 mm to be hot-rolled so as to have a thickness of about 0.5 mm, and the surface thereof was cold-rolled by about 0.03 mm. Thereafter, a heat treatment was carried out, so that a sample having a thickness of 0. 5 mm, a width of 10 mm and a length of 140 mm was prepared. Then, a stress being 50 % of the proof stress was applied to each of the samples by the two-point load method based on JIS H8711, and each of the samples was held in a desiccator including 14 % NH 3 . In this state, the time required to cause corrosion cracking was measured. The stress corrosion cracking resistance was evaluated by "bad" when cracks were produced within 5 hours, "not bad” when cracks are produced in 5 to 15 hours, and "good” when no cracks are produced after 15 hours or more.
  • Table 2 shows the proportions of the alpha phase and the results of dezincing tests and stress corrosion cracking tests in Examples 1 through 19. As can be seen from this table, in all examples, the proportions of the alpha phase were 80 vol% or more, and the stress corrosion cracking resistance and dezincing resistance were good. Table 2 Ex.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Conductive Materials (AREA)
  • Preventing Corrosion Or Incrustation Of Metals (AREA)

Claims (4)

  1. Kupferlegierung enthaltend 58 bis 66 Gew.-% Kupfer, 0,3 bis 0,5 Gew.-% Zinn, 0,01 bis 0,5 Gew.-% Silizium, 0,02 bis 0,15 Gew.-% Phosphor, wenigstens eines von 0,3 bis 3,0 Gew.-% Bismut und 0,3 bis 3,5 Gew.-% Blei, sowie optional wenigstens eines von 0,02 bis 3 Gew.-% Nickel und 0,02 bis 0,6 Gew.-% Eisen, wobei der Rest Zink und unvermeidbare Verunreinigungen sind, und, wobei der Anteil einer Alpha-Phase 80 Vol.-% oder mehr beträgt.
  2. Kupferlegierung nach Anspruch 1, wobei der scheinbare Gehalt B' von Zink in der Kupferlegierung in einem Bereich zwischen 34 und 39 Gew.-% liegt, wobei der scheinbare Gehalt B' von Zink durch die nachfolgende Gleichung ausgedrückt wird: Bʹ = B + t 1 ⁢ q 1 + t 2 ⁢ q 2 + t 3 ⁢ q 3 + t 4 ⁢ q 4 / A + B + t 1 ⁢ q 1 + t 2 ⁢ q 2 + t 3 ⁢ q 3 + t 4 ⁢ q 4 × 100
    Figure imgb0003
     worin A den Gehalt (Gew.-%) an Kupfer bezeichnet und B den Gehalt (Gew.-%) an Zink bezeichnet, t1, t2, t3 und t4 Zinkäquivalente von Zinn, Silizium, Nickel bzw. Eisen bedeuten (t1 = 2,0, t2 = 10,0, t3 = -1,3, t4 = 0,9) sowie q1, q2, q3 und q4 die Mengen (Gew.-%) an Zinn, Silizium, Nickel bzw. Eisen bedeuten.
  3. Verfahren zum Herstellen einer Kupferlegierung, wobei das Verfahren die nachfolgenden Schritte umfasst:
    Herstellen von Rohmaterialien einer Kupferlegierung enthaltend 58 bis 66 Gew.-% Kupfer, 0,3 bis 0,5 Gew.-% Zinn, 0,01 bis 0,5 Gew.-% Silizium, 0,02 bis 0,15 Gew.-% Phosphor, wenigstens eines von 0,3 bis 3,0 Gew.-% Bismut und 0,3 bis 3,5 Gew.-% Blei, sowie optional wenigstens eines von 0,02 bis 3,0 Gew.-% Nickel und 0,02 bis 0,6 Gew.-% Eisen, wobei der Rest Zink und unvermeidliche Verunreinigungen sind,
    Gießen der Rohmaterialien, um einen Gussblock zu formen, Warmbearbeiten des Gussblocks,
    Kalt- oder Warmbearbeiten des warmbearbeiteten Gussblocks, Glühen des kalt- oder warmbearbeiteten Gussblocks bei einer Temperatur zwischen 300 und 600°C für zwei Minuten bis fünf Stunden und
    Abkühlen des geglühten Gussblocks mit einer Abkühlrate von 0,2 bis 10 °C/Sek.
  4. Verfahren zum Herstellen einer Kupferlegierung nach Anspruch 3, wobei der scheinbare Gehalt B' von Zink in der Kupferlegierung in einem Bereich zwischen 34 und 39 Gew.-% liegt, wobei der scheinbare Gehalt B' von Zink durch die nachfolgende Gleichung ausgedrückt wird: Bʹ = B + t 1 ⁢ q 1 + t 2 ⁢ q 2 + t 3 ⁢ q 3 + t 4 ⁢ q 4 / A + B + t 1 ⁢ q 1 + t 2 ⁢ q 2 + t 3 ⁢ q 3 + t 4 ⁢ q 4 × 100
    Figure imgb0004
     worin A den Gehalt (Gew.-%) an Kupfer bezeichnet und B den Gehalt (Gew.-%) an Zink bezeichnet, t1, t2, t3 und t4 Zinkäquivalente von Zinn, Silizium, Nickel bzw. Eisen bedeuten (t1 = 2,0, t2 = 10,0, t3 = -1,3, t4 = 0,9) sowie q1, q2, q3 und q4 die Mengen (Gew.-%) an Zinn, Silizium, Nickel bzw. Eisen bedeuten.
EP03018581A 2003-08-18 2003-08-18 Kupferlegierung, die exzellente Korrosionsbeständigkeit und Entzinkungsbeständigkeit aufweist, und eine Methode zu deren Herstellung Expired - Lifetime EP1508625B1 (de)

Priority Applications (3)

Application Number Priority Date Filing Date Title
AT03018581T ATE353981T1 (de) 2003-08-18 2003-08-18 Kupferlegierung, die exzellente korrosionsbeständigkeit und entzinkungsbeständigkeit aufweist, und eine methode zu deren herstellung
EP03018581A EP1508625B1 (de) 2003-08-18 2003-08-18 Kupferlegierung, die exzellente Korrosionsbeständigkeit und Entzinkungsbeständigkeit aufweist, und eine Methode zu deren Herstellung
DE60311803T DE60311803T2 (de) 2003-08-18 2003-08-18 Kupferlegierung, die exzellente Korrosionsbeständigkeit und Entzinkungsbeständigkeit aufweist, und eine Methode zu deren Herstellung

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
EP03018581A EP1508625B1 (de) 2003-08-18 2003-08-18 Kupferlegierung, die exzellente Korrosionsbeständigkeit und Entzinkungsbeständigkeit aufweist, und eine Methode zu deren Herstellung

Publications (2)

Publication Number Publication Date
EP1508625A1 EP1508625A1 (de) 2005-02-23
EP1508625B1 true EP1508625B1 (de) 2007-02-14

Family

ID=34042861

Family Applications (1)

Application Number Title Priority Date Filing Date
EP03018581A Expired - Lifetime EP1508625B1 (de) 2003-08-18 2003-08-18 Kupferlegierung, die exzellente Korrosionsbeständigkeit und Entzinkungsbeständigkeit aufweist, und eine Methode zu deren Herstellung

Country Status (3)

Country Link
EP (1) EP1508625B1 (de)
AT (1) ATE353981T1 (de)
DE (1) DE60311803T2 (de)

Families Citing this family (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
KR101133704B1 (ko) 2006-12-28 2012-04-06 가부시키가이샤 기츠 내응력부식균열성이 우수한 무연 황동합금
US9601767B2 (en) 2010-11-17 2017-03-21 Luvata Appleton Llc Alkaline collector anode
WO2013115363A1 (ja) * 2012-02-01 2013-08-08 Toto株式会社 耐食性に優れた黄銅
CN102851532A (zh) * 2012-09-10 2013-01-02 顾建 一种用于阀门的铜合金材料
CN102864327A (zh) * 2012-09-10 2013-01-09 任静儿 用于阀门的铜合金材料
CN102851531A (zh) * 2012-09-10 2013-01-02 虞雪君 一种铜锌合金
CN109930026B (zh) * 2017-12-18 2020-12-18 有研工程技术研究院有限公司 一种高强度高导电、耐应力松弛铜合金引线框架材料及其制备方法

Family Cites Families (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US4294629A (en) * 1979-10-02 1981-10-13 Trefimetaux Drawn rods made of lead brass and a process for the thermal treatment thereof
JPS58185738A (ja) * 1982-04-20 1983-10-29 Yamamoto Sangyo Kk 黄銅合金
US5445687A (en) * 1991-11-14 1995-08-29 Toyo Valve Co., Ltd. Hot working material of corrosion resistant copper-based alloy
JP3104828B2 (ja) * 1993-09-24 2000-10-30 株式会社日立製作所 エレベーターのデータ伝送方式
US5507885A (en) * 1994-01-17 1996-04-16 Kitz Corporation Copper-based alloy
EP1008664B1 (de) * 1997-04-08 2004-12-08 Kitz Corporation Kupferbasislegierung mit hervorragender korrosions- und spannungsrisskorrosionsbeständigkeit und verfahren zu eren herstellung
JP3761741B2 (ja) * 1999-05-07 2006-03-29 株式会社キッツ 黄銅とこの黄銅製品
JP2001294956A (ja) * 2000-04-11 2001-10-26 Sumitomo Light Metal Ind Ltd 耐脱亜鉛腐食性に優れた快削黄銅およびその製造方法

Also Published As

Publication number Publication date
ATE353981T1 (de) 2007-03-15
DE60311803T2 (de) 2007-10-31
DE60311803D1 (de) 2007-03-29
EP1508625A1 (de) 2005-02-23

Similar Documents

Publication Publication Date Title
EP2784167B1 (de) Cu-Ti-basierte Kupferlegierungsfolie, Herstellungsverfahren dafür, und elektrischen Strom führendes Bauteil
EP1441040B1 (de) Kupfer-Legierung und Verfahren zu deren Herstellung
US5565045A (en) Copper base alloys having improved bend formability
EP2743360B1 (de) Messing mit hervorragender korrosionsbeständigkeit
EP2194149B1 (de) Kupferlegierungsplatte und Verfahren zu deren Herstellung
EP0175183B1 (de) Kupferlegierungen mit Festigkeits- und Leitfähigkeitseigenschaften
EP1698708B1 (de) Verfahren zur Herstellung einer nichtmagnetischen Legierung mit hoher Härte
US5370840A (en) Copper alloy having high strength and high electrical conductivity
EP2957646B1 (de) Hochfestes cu-ni-co-si-basiertes kupferlegierungsblech, verfahren zur herstellung davon und stromführende komponente
EP2653574B1 (de) Kupferlegierung und herstellungsverfahren für die kupferlegierung
EP3158095B1 (de) Kupfer-nickel-silizium-legierungen
EP3085799B1 (de) Kupferlegierung und verfahren zur herstellung davon
EP2607508B1 (de) Kupfer-kobalt-silicium-legierung für ein elektrodenmaterial
US20050039827A1 (en) Copper alloy having excellent corrosion cracking resistance and dezincing resistance, and method for producing same
US20010009168A1 (en) Copper Alloy
EP3578678A1 (de) Maraging-stahl und verfahren zur herstellung davon
EP1508625B1 (de) Kupferlegierung, die exzellente Korrosionsbeständigkeit und Entzinkungsbeständigkeit aufweist, und eine Methode zu deren Herstellung
JP3824944B2 (ja) 耐応力腐食割れ性および耐脱亜鉛性に優れた銅合金およびその製造方法
EP0385257A1 (de) Verfahren zur Herstellung gehärteter Bleche aus Aluminiumlegierungen mit hoher Festigkeit und sehr guter Korrosionsbeständigkeit
CA1119920A (en) Copper based spinodal alloys
EP3085798A1 (de) Kupferlegierung
CN100415911C (zh) 优异抗腐裂性和抗脱锌性能的铜合金及其制造方法
JPH07258804A (ja) 電子機器用銅合金の製造方法
JP3410125B2 (ja) 高強度銅基合金の製造方法
JPH06145930A (ja) 析出型銅合金の製造法

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

AK Designated contracting states

Kind code of ref document: A1

Designated state(s): AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HU IE IT LI LU MC NL PT RO SE SI SK TR

AX Request for extension of the european patent

Extension state: AL LT LV MK

17P Request for examination filed

Effective date: 20050425

AKX Designation fees paid

Designated state(s): AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HU IE IT LI LU MC NL PT RO SE SI SK TR

GRAP Despatch of communication of intention to grant a patent

Free format text: ORIGINAL CODE: EPIDOSNIGR1

GRAS Grant fee paid

Free format text: ORIGINAL CODE: EPIDOSNIGR3

RAP1 Party data changed (applicant data changed or rights of an application transferred)

Owner name: DOWA HOLDINGS CO., LTD.

GRAA (expected) grant

Free format text: ORIGINAL CODE: 0009210

AK Designated contracting states

Kind code of ref document: B1

Designated state(s): AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HU IE IT LI LU MC NL PT RO SE SI SK TR

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: LI

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20070214

Ref country code: FI

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20070214

Ref country code: AT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20070214

Ref country code: BE

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20070214

Ref country code: SI

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20070214

Ref country code: CH

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20070214

Ref country code: DK

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20070214

Ref country code: NL

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20070214

REG Reference to a national code

Ref country code: GB

Ref legal event code: FG4D

REG Reference to a national code

Ref country code: CH

Ref legal event code: EP

REF Corresponds to:

Ref document number: 60311803

Country of ref document: DE

Date of ref document: 20070329

Kind code of ref document: P

REG Reference to a national code

Ref country code: IE

Ref legal event code: FG4D

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: SE

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20070514

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: BG

Free format text: LAPSE BECAUSE OF EXPIRATION OF PROTECTION

Effective date: 20070515

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: ES

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20070525

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: PT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20070716

NLV1 Nl: lapsed or annulled due to failure to fulfill the requirements of art. 29p and 29m of the patents act
ET Fr: translation filed
REG Reference to a national code

Ref country code: CH

Ref legal event code: PL

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: SK

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20070214

PLBE No opposition filed within time limit

Free format text: ORIGINAL CODE: 0009261

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

Free format text: STATUS: NO OPPOSITION FILED WITHIN TIME LIMIT

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: RO

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20070214

Ref country code: CZ

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20070214

26N No opposition filed

Effective date: 20071115

GBPC Gb: european patent ceased through non-payment of renewal fee

Effective date: 20070818

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: GR

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20070515

Ref country code: MC

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20070831

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: IE

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20070820

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: GB

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20070818

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: EE

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20070214

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: CY

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20070214

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: LU

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20070818

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: TR

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20070214

Ref country code: HU

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20070815

REG Reference to a national code

Ref country code: FR

Ref legal event code: PLFP

Year of fee payment: 14

REG Reference to a national code

Ref country code: FR

Ref legal event code: PLFP

Year of fee payment: 15

REG Reference to a national code

Ref country code: FR

Ref legal event code: PLFP

Year of fee payment: 16

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: FR

Payment date: 20200715

Year of fee payment: 18

Ref country code: DE

Payment date: 20200804

Year of fee payment: 18

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: IT

Payment date: 20200713

Year of fee payment: 18

REG Reference to a national code

Ref country code: DE

Ref legal event code: R119

Ref document number: 60311803

Country of ref document: DE

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: IT

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20210818

Ref country code: FR

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20210831

Ref country code: DE

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20220301