EP2653574A1 - Kupferlegierung und herstellungsverfahren für die kupferlegierung - Google Patents

Kupferlegierung und herstellungsverfahren für die kupferlegierung Download PDF

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Publication number
EP2653574A1
EP2653574A1 EP11848127.4A EP11848127A EP2653574A1 EP 2653574 A1 EP2653574 A1 EP 2653574A1 EP 11848127 A EP11848127 A EP 11848127A EP 2653574 A1 EP2653574 A1 EP 2653574A1
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Prior art keywords
mass
copper alloy
electrical conductivity
high strength
phase
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EP11848127.4A
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English (en)
French (fr)
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EP2653574A4 (de
EP2653574B1 (de
Inventor
Kiyohito Ishida
Ryosuke Kainuma
Ikuo Ohnuma
Toshihiro Omori
Takashi Miyamoto
Hiroki Sato
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Nippon Seisen Co Ltd
Tohoku Techno Arch Co Ltd
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Nippon Seisen Co Ltd
Tohoku Techno Arch Co Ltd
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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
    • C22C9/02—Alloys based on copper with tin as the next major constituent
    • 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
    • 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
    • C22C9/01—Alloys based on copper with aluminium as the next major constituent
    • 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
    • C22C—ALLOYS
    • C22C9/00—Alloys based on copper
    • C22C9/05—Alloys based on copper with manganese as the next major constituent
    • 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
    • C22C9/06—Alloys based on copper with nickel or cobalt 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
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01B—CABLES; CONDUCTORS; INSULATORS; SELECTION OF MATERIALS FOR THEIR CONDUCTIVE, INSULATING OR DIELECTRIC PROPERTIES
    • H01B1/00—Conductors or conductive bodies characterised by the conductive materials; Selection of materials as conductors
    • H01B1/02—Conductors or conductive bodies characterised by the conductive materials; Selection of materials as conductors mainly consisting of metals or alloys
    • H01B1/026—Alloys based on copper

Definitions

  • the present invention relates to a copper alloy having the high strength and high electrical conductivity which is applied to a lead frame, a connector, a terminal material and the like for electric and electronic instruments and a process for producing a copper alloy, which produces this copper alloy.
  • An aging hardening-type copper alloy is a copper alloy which, by aging-treating a supersaturated solid solution which has been solution-treated, contributes to improvement in strength property such as a proof stress or a spring limit value by uniform precipitation of fine particles, and improvement in electrical conductivity by decrease in a solid solution element amount.
  • an aging hardening-type copper alloy such as a Cu-Ni-Si alloy (Colson) and beryllium copper is used.
  • Patent Literature 1 discloses a copper alloy material containing 1.0 to 5.0 mass% of Ni, 0.2 to 1.0 mass% of Si, 1.0 to 5.0 mass% of Zn, 0.1 to 0.5 mass% of Sn, and 0.003 to 0.3 mass% of P, with the remainder consisting of Cu and incidental impurities, which is obtained by a first cold rolling step of cold rolling to a thickness which is 1.3 to 1.7-fold of an objective final plate thickness, a first heat-treating step of heating a material after the first cold rolling to 700 to 900°C and, thereafter, cooling the material to 300°C or lower at a temperature lowering rate of 25°C or more per minute, a second cold rolling step of cold-rolling a material after the first heat treatment to a final plate thickness, a second heat-treating step of heating
  • Patent Literature 2 describes a copper alloy for electronic materials containing Ni: 1.0 to 4.5 mass%, Si: 0.50 to 1.2 mass%, and Cr: 0.0030 to 0.3 mass% (provided that a weight ratio of Ni and Si is 3 ⁇ Ni/Si ⁇ 5.5), with the remainder being composed of Cu and incidental impurities, in which a Cr-Si compound having a size of 0.1 ⁇ m or more and 5 ⁇ m or less, which is dispersed in a material is such that an atomic concentration ratio of Cr relative to Si in the dispersed particle is 1 to 5, and a dispersion density thereof is 1 ⁇ 10 6 /mm 2 or less.
  • this alloy improves the strength of a Ni-Si intermetallic compound, and there is a limit regarding the high strength and high electrical conductivity.
  • Patent Literature 7 describes a copper alloy for electric and electronic instruments containing 1 to 3 mass% of Ni and 0.2 to 1.4 mass% of Ti, in which a ratio (Ni/Ti) of a mass percentage of the Ni and the Ti is 2.2 to 4.7, containing 0.02 to 0.3 mass % of one or both of Mg and Zr, and 0.1 to 5 mass% of Zn, with the remainder consisting of Cu and incidental impurities, in which the copper alloy contains at least one of an intermetallic compound consisting of Ni, Ti and Mg, an intermetallic compound consisting of Ni, Ti and Zr, or an intermetallic compound consisting of Ni, Ti, Mg, and Zr, a distribution density of the intermetallic compounds is 1 ⁇ 10 9 to 1 ⁇ 10 13 /mm 2 , the tensile strength is 650 MPa or more, electrical conductivity is 55 IACS% or more, and a stress relaxation ratio when held at 150°C for 1000 hours is 20% or less.
  • the present inventors studied in order to obtain a high strength copper alloy and, as a result, found out that it is effective to finely precipitate a ⁇ ' phase of the L1 2 structure with Ni 3 Al in a parent phase of the FCC structure, in a Cu-Ni-Al alloy. Further, it was found out that the copper alloy is further highly strengthened by adding Si.
  • the copper alloy of the present invention is a copper alloy of the FCC structure containing Ni: 3.0 to 29.5 mass%, Al : 0.5 to 7.0 mass%, and Si: 0.1 to 1.5 mass%, with the remainder consisting of Cu and incidental impurities, in which a ⁇ ' phase of the L1 2 structure is precipitated at an average particle diameter of 100 nm or less with Ni 3 Al including Si, in a parent phase of the copper alloy.
  • the copper alloy of the present invention is further characterized in that the copper alloy contains Ni: 3.0 to 14.0 mass%, Al: 0.5 to 4. mass%, and Si: 0.1 to 1.5 mass%, and electrical conductivity is 8.5 IACS% or more.
  • the copper alloy of the present invention is further characterized in that the copper alloy contains, as an addition element, a total amount of 0.01 to 5.0 mass% of one or two or more elements selected from the group consisting of Co, Ti, Sn, Cr, Fe, Zr, Mg and Zn. Further, the copper alloy of the present invention is further characterized in that the copper alloy contains, as an addition element, a total amount of 0.001 to 0.5 mass% of one or two or more elements selected from the group consisting of C, P and B.
  • the process for producing a high strength copper alloy of the present invention is characterized in that raw materials are integrated, melted and mixed, and hot-worked and cold-worked and, thereafter, the mixture is heat-treated in a range of 700 to 1020°C for 0.1 to 10 hours and, thereafter, this is aging-treated in a range of 400 to 650°C and 0.1 to 48 hours. Further, the process for producing a high strength copper alloy of the present invention is further characterized in that, before or after the aging treatment, cold working at a working rate of 10 to 95% is performed.
  • High electrical conductivity was studied by the copper alloy of the present invention which is the means to solve the problems and, as a result, it was found out that both of the strength and electrical conductivity are satisfied in a region A and a region B.
  • a high strength copper alloy having, particularly, high electrical conductivity and excellent workability can be obtained and, in the region B, particularly, a high strength copper alloy having the high strength can be obtained.
  • high electrical conductivity was studied by the process for producing a copper alloy of the present invention and, as a result, in the region A and the region B, a copper alloy satisfying both of the strength and electrical conductivity can be produced.
  • Fig. 1 is a photograph of a transmission electron microscope in which an upper side shows a crystal structure L1 2 of a precipitate according to electron beam diffraction, and a lower shows the state of a precipitate.
  • the copper alloy of the present invention is a copper alloy of the FCC structure containing Ni: 3.0 to 29.5 mass%, Al: 0.5 to 7.0 mass%, and Si: 0.1 to 1.5 mass%, with the remainder consisting of Cu and incidental impurities, in which a ⁇ ' phase of the L1 2 structure is precipitated at an average particle diameter of 100 nm or less with Ni 3 Al including Si, in a parent phase of the copper alloy.
  • the L1 2 structure can be confirmed, for example, by an arrangement structure of an electron beam diffraction image.
  • Fig. 1 is a photograph of a transmission electron microscope in which an upper side shows a crystal structure L1 2 of a precipitate by electron beam diffraction, and a lower side shows the state of a precipitate.
  • the present photograph is a composition of Ni: 12.3 mass%-Al: 1.0 mass%-Si: 0.3 mass%-Cu, and the composition has been subjected to solution treatment: 900°C 10 minutes-cold working 30%-aging treatment 500°C 6 hours.
  • electron beam diffraction is directed to a regular phase having a diffraction plane 110.
  • the ⁇ ' phase is an intermetallic compound, and has a regularized FCC structure in which an atom positioning at a corner is Al and Si, and an atom positioning at a face center is Ni.
  • the ⁇ ' phase of the L1 2 structure is finely precipitated.
  • the copper alloy of the present invention is a copper alloy while it has the FCC structure.
  • the FCC structure is a structure in which metal elements are laminated most closely, and is suitable as a parent phase alloy of the high strength and high electrical conductivity. Therefore, copper having the FCC structure is excellent in workability, and an objective shape can be easily made.
  • Ni and Al precipitate an intermetallic compound of Ni 3 Al to form a y' phase in Cu of a parent phase.
  • Al and Si together with Ni form a Ni 3 (Al, Si) intermetallic compound
  • Al and Si together are required at an amount adapted for this system, and form not a system of Ni 3 Al or Ni 3 Si alone, but one Ni 3 (Al, Si) intermetallic compound while it resides in mixture at a corner of the FCC structure in the L1 2 type.
  • the y' phase having the L1 2 structure in the copper alloy of the present invention is an intermetallic compound, and has a regularized FCC structure in which an atom positioning at a corner is Al and Si, and an atom positioning at a face center is Ni.
  • these copper of a parent phase having the FCC structure and ⁇ ' phase having the L1 2 structure are both of the FCC structure, they are good in integrity, contribute to improvement in the strength and, at the same time, a solute element concentration of a parent phase is decreased by precipitating the ⁇ ' phase, and they also contribute to improvement in electrical conductivity.
  • the ⁇ ' phase of the L1 2 structure belongs to the GCP (Geometrically close packing) phase, has ductility due to a closed packed structure thereof, and further, is high in integrity, a ⁇ + ⁇ ' structure is formed, in which a ⁇ ' phase being a fine structure is precipitated, thereby, a copper alloy having high workability with toughness can be obtained.
  • This ⁇ ' phase is precipitated finely and spherically in a ⁇ phase containing mainly copper being parent phase. Since the ⁇ ' phase is spherical, a highly workable copper alloy with toughness can be obtained without stress concentration at an interface between the ⁇ ' phase and the ⁇ phase. Further, by controlling an average particle diameter of the ⁇ ' phase small, it is possible to improve the strength more. By reducing an average particle diameter of the ⁇ ' phase, a pinning site of moving rearrangement is increased in the number, and the high tensile strength can be obtained. Further, the ⁇ ' phase is an intermetallic compound, its own hardness is high, and the tensile strength is also high. Therefore, by preventing rearrangement from moving in the ⁇ ' phase, it can contribute to a hardness and the tensile strength of a copper alloy.
  • electrical conductivity is lowered as a concentration of a solute element which forms a solid solution in copper, but since a solute element concentration in a parent phase is decreased as compared with the solutionized state of a ⁇ monophase by heat-treating an alloy at a low temperature to precipitate a ⁇ ' phase, precipitation of the ⁇ ' phase also contributes to improvement in electrical conductivity.
  • electrical conductivity of the ⁇ ' phase is lower than electrical conductivity of pure Cu, movement of electrons is reduced by a portion corresponding to a volumetric ratio occupied by this ⁇ ' phase, but high electrical conductivity can be maintained by adopting an area fraction of a suitable amount of the ⁇ ' phase.
  • the copper alloy greatly contributes to mechanical property such as a hardness, the tensile strength and the like without considerably deteriorating ductility such as cold workability and the like, and as a second phase having the effect of improving electrical conductivity, the ⁇ ' phase is suitable.
  • an area fraction of the ⁇ ' phase is 5 to 40%. This area fraction can be obtained by comparing an area of each metal structure of a certain cross section of a copper alloy.
  • an area fraction and a volume fraction if areas of sections when two three dimensional-objects are cut with a plane parallel with a certain plane are equal in accordance with Cavalier principle, volumes of two three dimensional-objects are equal.
  • an average particle diameter of this ⁇ ' phase is 100 nm or less. A smaller average particle diameter is preferable, but it is difficult to control a practical precipitation size finer than 1 nm due to coarsening by heat treatment, and when the size is 1 nm or more and 100 nm or less, the sufficient strength can be obtained.
  • An average particle diameter of the ⁇ ' phase is obtained by measuring diameters of a plurality of ⁇ ' phases by image analysis from structural observation with an electron microscope, and averaging them.
  • an intermetallic compound such as Ni 2 (Al, Si), NiAl, Ni 5 Si 2 and the like other than the ⁇ ' phase of an intermetallic compound of Ni 3 Al is precipitated by added Ni, Al and Si, in some cases.
  • Ni 2 (Al, Si) is smaller in a precipitation amount as compared with that of Ni 3 (Al, Si), and influences little on a mechanical nature and an electric nature of a copper alloy.
  • An intermetallic compound of a ⁇ phase represented by NiAl is precipitated.
  • This ⁇ phase is of the B2 structure of the BCC regular structure, but a compositional range at which precipitation occurs, is narrow, and if precipitated, an amount thereof is smaller as compared with that of Ni 3 (Al, Si), and the ⁇ phase influences little on a mechanical nature and an electric nature of a copper alloy. Further, an intermetallic compound of Ni 5 Si 2 is precipitated in some cases. This Ni 5 Si 2 is also smaller in a precipitation amount as compared with that of Ni 3 (Al, Si), and influences little on a mechanical nature and an electric nature of a copper alloy.
  • Si has the effect of reducing a concentration of a solute element in a matrix, and has the effect of increasing a volume fraction of the ⁇ ' phase and, at the same time, enhancing electrical conductivity.
  • the copper alloy of the present invention has a compositional range containing Ni: 3.0 to 14.0 mass%, Al: 0.5 to 4.0 mass%, and Si: 0.1 to 1.5 mass%, and has electrical conductivity of 8.5 IACS% or more.
  • electrical conductivity can be made to be 8.5 IACS% or more.
  • electrical conductivity 8.5 IACS% or more the copper alloy as a copper alloy having high electrical conductivity is applied to a lead frame, a connector, a terminal material and the like of electronic instruments and the like.
  • cold workability is defined as a reduction ratio of a maximum thickness at which rolling is possible with no cracking without performing annealing in the case of rolling implemented at a temperature of 20°C, and is defined as a maximum area reduction ratio at which wire drawing is possible with no cracking without performing annealing in the case of wire drawing.
  • Ni 3 (Al, Si) intermetallic compound of the ⁇ ' phase has lower workability than that of pure Cu, a working ratio cannot be increased by a portion corresponding to a ratio of a volume occupied by this Ni 3 (Al, Si) intermetallic compound. Therefore, by adopting a compositional range containing Ni: 3.0 to 14.0 mass%, Al: 0.5 to 4.0 mass%, and Si: 0.1 to 1.5 mass%, a precipitation amount of the ⁇ ' phrase can be controlled to adjust cold workability at 10 to 95% while electrical conductivity is maintained high. When cold workability is less than 10%, there is a problem that a material having an objective shape cannot be made.
  • cold workability is preferably in a range of 10 to 95%, further preferably 20 to 90%.
  • the copper alloy as a copper alloy having the high strength is applied to a lead frame, a connector, a terminal material and the like of electronic instruments and the like.
  • the copper alloy of the present invention can afford high electrical conductivity and high cold workability by residing in a range of this region A and adopting 5 to 20% of a volume fraction at which the ⁇ ' phase is precipitated.
  • the copper alloy as a contact material can reduce abrasion even when the material is contacted and sliding-rubbed frequently. Therefore, the copper alloy can be applied to a lead frame, a connector, a terminal material and the like of electronic instruments and the like, as a copper alloy having high electrical conductivity and high cold workability.
  • Ni: 9.5 to 29.5mass%, Al: 1.5 to 7.0 mass%, and Si: 0.1 to 1.5 mass% are contained, and a Vickers hardness is in a range of 220 to 450 Hv.
  • a Vickers hardness can be enhanced.
  • an average particle diameter of the ⁇ ' phase is preferably 100 nm or less like the above.
  • a smaller average particle diameter is preferable, but it is difficult to perform practical precipitation completely uniformly, and the sufficient strength can be obtained at an average particle diameter of 1 nm or more and 100 nm or less, and 30 nm or less is more preferable.
  • electrical conductivity in this compositional range electrical conductivity of approximately 7 to 15 IACS% can be obtained, abrasion is little, and durability is good, the copper alloy can stand use for a long term, even when applied to a lead frame, a connector, a terminal material and the like of electronic instruments and the like, by possession of a high Vickers hardness together.
  • the copper alloy of the present invention can further have the high strength represented by a Vickers hardness by residing in a range of this region B and adjusting a volume fraction at which the ⁇ ' phase is precipitated, at 25 to 40%.
  • the ⁇ ' phase is an intermetallic compound, and the strength is very high.
  • the copper alloy can be also provided with a high Vickers hardness, while high electrical conductivity is obtained.
  • the copper alloy can be widely applied to a lead frame, a connector, a terminal material and the like of electronic instruments and the like.
  • a total amount of 0.01 to 5.0 mass% of one or two or more elements selected from the group consisting of Co, Ti, Sn, Cr, Fe, Zr, Mg and Zn can be contained as an addition element. Since Co, Ti, Cr and Zr stabilize the ⁇ ' phase and promote precipitation thereof, they contribute to improvement in the strength, and since they also have the effect of decreasing a concentration of a solute element in Cu, they also contribute to improvement in electrical conductivity. Since Sn, Mg and Zn have the effect of improving stress relaxation resistance property and, at the same time, dissolve in Cu, they contribute to improvement in the strength.
  • Fe has the effect of miniaturization of a crystal grain by dispersion of a fine grain of Fe in Cu, and contributes to improvement in the strength and improvement in heat resistance.
  • An addition amount of an addition element is so that selected one or two more addition elements are contained at a total amount of 0.01 to 5.0 mass%. When a total amount of selected one or two or more addition elements is less than 0.01 mass%, there is a problem that this does not contribute to improvement in electrical conductivity and improvement in the strength, for a copper alloy.
  • the copper alloy of the present invention can further contain a total amount of 0.001 to 0.5 mass% of one or two or more elements selected from the group consisting of C, P and B as an addition element.
  • C is thought to have the effect on miniaturization of a crystal grain, and contributes to improvement in the strength. Further, C reduces solid solubility of a solute element in Cu, and contributes to improvement in electrical conductivity.
  • P is used as a deoxidant, has the effect of decreasing a concentration of impurities of Cu, and contributes to improvement in electrical conductivity.
  • B has the effect of suppressing growth of a crystal grain and, therefore, has the effect of miniaturizing a crystal grain to improve the strength. B can improve heat resistance.
  • An addition amount is such that selected one or two or more addition elements are contained at a total amount of 0.001 to 0.5 mass% .
  • a total amount of addition elements is less than 0.001 mass%, there is a problem that addition elements do not contribute to improvement in electrical conductivity and improvement in the strength, for a copper alloy.
  • a total amount of addition elements exceeds 0. 5 mass%, there is a problem that addition elements contribute to improvement in electrical conductivity and improvement in the strength, but it becomes impossible to control electric property such as electrical conductivity and the like and mechanical property such as a Vickers hardness and the like in a suitable range.
  • raw materials are integrated, melted, mixed and cast and, thereafter, the cast product is formed into a shape such as a plate material, a wire material, a tube material and the like by hot working such as hot forging and, if necessary, cold working such as cold rolling, cold wire drawing and the like.
  • the formed material is heat-treated in a range of 700 to 1020°C and 0.1 to 10 hours and, thereafter, aging-treated in a range of 400 to 650°C and 0.1 to 48 hours.
  • the process for producing a copper alloy of the present invention has (a) a step of integrating, melting and mixing Ni: 3.0 to 29.5 mass%, Al: 0.5 to 7.0 mass%, Si: 0.1 to 1.5 mass% and Cu to form a copper alloy material as an ingot, (b) a step of performing solution treatment of heat-treating the copper alloy material at a temperature in a range of 700°C to 1020°C for a time in a range of 0.1 to 10 hours, after the material is formed by hot working and, if necessary, cold working, and (c) a step of performing aging treatment of heating the copper alloy material after solution treatment at a temperature in a range of 400°C to 650°C for a time in a range of 0.1 to 48 hours.
  • a total amount of 0.01 to 5.0 mass% of one or two or more elements selected from the group consisting of Co, Ti, Sn, Cr, Fe, Zr, Mg and Zn can be also further added as an addition element.
  • a total amount of 0.001 to 0.5 mass% of one or two or more elements selected from the group consisting of C, P and B can be also added.
  • a deoxidant such as calcium boride and the like
  • a bubbling treatment may be performed using an argon gas or a nitrogen gas
  • melting may be performed in vacuum in a vacuum container.
  • a method of melting is not particularly limited, but a raw material may be heated at a temperature of a melting point of a copper alloy raw material or higher using the known apparatus such as a high frequency melting furnace and the like.
  • a copper alloy material is heat-treated at a temperature in a range of 700°C to 1020°C for a time in a range of 0.1 to 10 hours.
  • a method of heating is not particularly limited, but heating may be performed according to the known method.
  • Ni, Al, Si and the like are dispersed homogeneously, thereby, the ⁇ ' phase having a fine average particle diameter of 100 nm or less can be precipitated by aging treatment described later.
  • a copper alloy material is aging-treated at 400 to 650°C, for a time in a range of 0.1 to 48 hours. The ⁇ ' phase cannot be precipitated at lower than 400°C and/or for shorter than 0.1 hour.
  • the process for producing a high strength copper alloy of the present invention is further characterized in that, before or after the aging treatment, cold working of 10 to 95% is performed.
  • a step of subjecting the copper alloy material to cold working of 10 to 95% before or after the aging treatment is provided.
  • a lattice defect such as a crystal grain boundary, rearrangement, a lamination defect and the like is formed to miniaturize and working-cure a crystal grain and, at the same time, thereafter, disperse and precipitate a number of ⁇ ' phases of Ni 3 (Al, Si), thereby, an average particle diameter of the ⁇ ' phase can be made to be 100 nm or less and, at the same time, a temperature of aging treatment can be lowered, and a time of aging treatment can be shortened.
  • a method of cold working is not particularly limited, but the method may be performed by the known method such as rolling with a roller and the like.
  • low temperature aging may be performed in a range of 100 to 400°C.
  • a method of low temperature aging is not particularly limited, but the method can be performed according to the known method.
  • a copper alloy obtained by such the production process can precipitate a sufficient amount of a fine ⁇ ' phase while suppressing coarsening of a ⁇ ' phase of the L1 2 structure precipitating in a copper alloy, electric property such as electrical conductivity and the like, and mechanical property such as cold workability, a Vickers hardness and the like can be easily controlled.
  • copper alloy materials of compositions of Examples 1 to 57 were integrally placed into a high frequency induction melting furnace, fused, melted and mixed. This was formulated into a cast ingot (as-cast).
  • Heat treatment condition is representative production condition, and is hot rolling (900°C, rolling reduction 90%)-solutionizing (900°C, 10 minutes)-cold rolling (20°C, rolling reduction 30%)-aging precipitation treatment (500°C, 18 hours). Electrical conductivity, workability, a Vickers hardness at each composition thereupon are shown.
  • Copper alloy materials of compositions of Examples 58 to 70 were integrally placed into a high frequency induction melting furnace, fused, melted and mixed. This was formulated into a cast ingot (as-cast).
  • Heat treatment condition is representative production condition, and is hot rolling (900°C, rolling reduction 90%)-solutionizing (900°C, 10 minutes)-cold rolling (20°C, rolling reduction 30%)-aging precipitation treatment (500°C, 18 hours). Electrical conductivity and a Vickers hardness at each composition thereupon are shown.
  • compositions of Examples 71 to 76 are shown in the following Table 7.
  • Heat treatment condition is representative production condition, and is hot rolling (900°C, rolling reduction 90%)-solutionizing (900°C, 10 minutes)-cold rolling (20°C, rolling reduction 30%)-aging precipitation treatment (500°C, 18 hours). Electrical conductivity and a Vickers hardness at each composition thereupon are shown. As seen from Table 8, under production condition of the production process of the present invention, under all heat treatment working conditions essentially including aging treatment other than heat treatment working conditions 1, 5, 12 and 13, electrical conductivity was 8.5 IACS% or more. Further, under all heat treatment working conditions essentially including aging treatment other than treatment working conditions 1, 5, 6, 7, 8, 12 and 13, a Vickers hardness was 220 Hv or more.
  • compositions of Examples 77 to 82 are shown in the following Table 9.
  • Heat treatment condition is representative production condition, and is hot rolling (900°C, rolling reduction 90%)-solutionizing (900°C, 10 minutes)-cold rolling (20°C, rolling reduction 30%)-aging precipitation treatment (500°C, 18 hours). Electrical conductivity and a Vickers hardness at each composition thereupon are shown. As seen from Table 10, under production condition of the production process of the present invention, under all heat treatment working conditions essentially including aging treatment other than heat treatment working conditions 1, 5, 12 and 13, electrical conductivity was 8.5 IACS% or more, and a Vickers hardness was 220 Hv or more.
  • Heat treatment condition is representative production condition, and is hot rolling (900°C, rolling reduction 90%)-solutionizing (900°C, 10 minutes)-cold rolling (20°C, rolling reduction 30%)-aging precipitation treatment (500°C, 18 hours). Electrical conductivity and a Vickers hardness at each composition thereupon are shown. As seen from Table 12, under production condition of the production process of the present invention, under all heat treatment working conditions essentially including aging treatment other than heat treatment working conditions 1, 5, 12 and 13, electrical conductivity was 8.5 IACS% or more, and a Vickers hardness was 220 Hv or more.
  • compositions of Examples 89 to 94 are shown in the following Table 13.
  • Heat treatment condition is representative production condition, and is hot rolling (900°C, rolling reduction 90%)-solutionizing (900°C, 10 minutes)-cold rolling (20°C, rolling reduction 30%) -aging precipitation treatment (500°C, 18 hours). Electrical conductivity and a Vickers hardness at each composition thereupon are shown. As seen from Table 14, under production condition of the production process of the present invention, under all heat treatment working conditions essentially including aging treatment other than heat treatment working conditions 1, 5, 12 and 13, electrical conductivity was 8.5 IACS% or more, and a Vickers hardness was 220 Hv or more.
  • compositions of Examples 95 to 100 are shown in the following Table 15.
  • Heat treatment condition is representative production condition, and is hot rolling (900°C, rolling reduction ratio 90%)-solutionizing (900°C, 10 minutes)-cold rolling (20°C, rolling reduction 30%)-aging precipitation treatment (500°C, 18 hours). Electrical conductivity and a Vickers hardness at each composition thereupon are shown. As seen from Table 16, under production condition of the production process of the present invention, under all heat treatment working conditions essentially including aging treatment other than heat treatment working conditions 1, 5, 12 and 13, electrical conductivity was 8.5 IACS% or more, and a Vickers hardness was 220 Hv or more.
  • compositions of Examples 101 to 106 are shown in the following Table 17.
  • Heat treatment condition is representative production condition, and is hot rolling (900°C, rolling reduction 90%)-solutionizing (900°C, 10 minutes)-cold rolling (20°C, rolling reduction 30%)-aging precipitation treatment (500°C, 18 hours). Electrical conductivity and a Vickers hardness at each composition thereupon are shown. As seen from Table 18, under production condition of the production process of the present invention, under all heat treatment working conditions essentially including aging treatment other than heat treatment working conditions 1, 5, 12 and 13, electrical conductivity was 8.5 IACS% or more, and a Vickers hardness was 220 Hv or more.
  • compositions of Examples 107 to 112 are shown in the following Table 19.
  • Heat treatment condition is representative production condition, and is hot rolling (900°C, rolling reduction 90%)-solutionizing (900°C, 10 minutes)-cold rolling (20°C, rolling reduction 30%)-aging precipitation treatment (500°C, 18 hours). Electrical conductivity and a Vickers hardness at each composition thereupon are shown. As seen from Table 20, under production condition of the production process of the present invention, under all heat treatment working conditions essentially including aging treatment other than heat treatment working conditions 1, 5, 12 and 13, electrical conductivity was 8.5 IACS% or more, and a Vickers hardness was 220 Hv or more.
  • Heat treatment condition is representative production condition, and is hot rolling (900°C, rolling reduction 90%)-solutionizing (900°C, 10 minutes)-cold rolling (20°C, rolling reduction 30%)-aging precipitation treatment (500°C, 18 hours). Electrical conductivity and a Vickers hardness at each composition thereupon are shown. As seen from Table 22, under production condition of the production process of the present invention, under all heat treatment working conditions essentially including aging treatment other than heat treatment working conditions 1, 5, 12 and 13, electrical conductivity was 8.5 IACS% or more, and a Vickers hardness was 220 Hv or more.
  • Heat treatment condition is representative production condition, and is hot rolling (900°C, rolling reduction 90%)-solutionizing (900°C, 10 minutes)-cold rolling (20°C, rolling reduction 30%)-aging precipitation treatment (500°C, 18 hours). Electrical conductivity and a Vickers hardness at each composition thereupon are shown. As seen from Table 24, under production condition of the production process of the present invention, under all heat treatment working conditions essentially including aging treatment other than heat treatment working conditions 1, 5, 12 and 13, electrical conductivity was 8.5 IACS% or more, and a Vickers hardness was 220 Hv or more.
  • Heat treatment condition is representative productive condition, and is hot rolling (900°C, rolling reduction 90%)-solutionizing (900°C, 10 minutes)-cold rolling (20°C, rolling reduction 30%)-aging precipitation treatment (500°C, 18 hours). Electrical conductivity and a Vickers hardness at each composition thereupon are shown. As seen from Table 26, under production condition of the production process of the present invention, under all heat treatment working conditions essentially including aging treatment other than heat treatment working conditions 1, 5, 12 and 13, electrical conductivity was 8.5 IACS% or more, and a Vickers hardness was 220 Hv or more.
  • the copper alloy of the present invention is a copper alloy having a predetermined composition, which is obtained by a predetermined production process, and since the copper alloy can precipitate a sufficient amount of a fine ⁇ ' phase while coarsening of a ⁇ ' phase of the LI 2 structure which is precipitated in a copper alloy is suppressed, it was seen that it can easily control electric property such as electrical conductivity and the like, and mechanical property such as cold workability, a Vickers hardness and the like. [table 1-1] Alloy No.
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Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP3859022A4 (de) * 2018-09-27 2022-07-27 Dowa Metaltech Co., Ltd Kupferlegierungsblech auf der basis von cu-ni-al, verfahren zu seiner herstellung und leitendes federelement

Families Citing this family (18)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US9476474B2 (en) * 2010-12-13 2016-10-25 Nippon Seisen Co., Ltd. Copper alloy wire and copper alloy spring
CN106103756B (zh) * 2014-03-25 2018-10-23 古河电气工业株式会社 铜合金板材、连接器和铜合金板材的制造方法
CN104532055A (zh) * 2014-11-21 2015-04-22 华南理工大学 一种高镍含量的变形铝白铜合金材料及其制备方法
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EP3085799B1 (de) * 2015-04-22 2018-01-17 NGK Insulators, Ltd. Kupferlegierung und verfahren zur herstellung davon
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DE102016006824A1 (de) 2016-06-03 2017-12-07 Wieland-Werke Ag Kupferlegierung und deren Verwendungen
WO2018100919A1 (ja) * 2016-12-02 2018-06-07 古河電気工業株式会社 銅合金線材及び銅合金線材の製造方法
EP3577247B1 (de) * 2017-02-04 2022-09-14 Materion Corporation Verfahren zur herstellung von kupfer-nickel-zinn-legierungen
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CN110551917B (zh) * 2019-09-29 2021-07-09 广东和润新材料股份有限公司 一种高导电耐腐蚀铜带及其制备方法
CN115094266B (zh) * 2022-07-05 2023-06-27 中南大学 一种高强导电弹性铜合金及其制备方法

Citations (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
GB2051127A (en) * 1979-04-30 1981-01-14 Delta Enfield Metals Precipitation hardening copper alloys
JPH02179839A (ja) * 1988-12-29 1990-07-12 Kobe Steel Ltd 耐衝撃特性及び熱間加工性に優れた高強度銅合金
JPH03126829A (ja) * 1989-10-06 1991-05-30 Sumitomo Metal Mining Co Ltd 工具用非発火性銅合金
JPH03173730A (ja) * 1989-12-01 1991-07-29 Sumitomo Metal Mining Co Ltd 工具用非発火性銅合金
JPH0499140A (ja) * 1990-08-03 1992-03-31 Hitachi Ltd プラスチック成形用金型材料
DE4226692A1 (de) * 1991-08-13 1993-03-04 Mitsubishi Materials Corp Ausscheidungshaertbare legierungen auf kupferbasis mit hoher festigkeit bei erhoehten temperaturen
JPH07268512A (ja) * 1994-03-30 1995-10-17 Mitsubishi Materials Corp 熱伝導度、高温硬さおよび耐酸化性に優れた耐熱銅合金およびこの耐熱銅合金からなる焼成型
JP2010007174A (ja) * 2008-05-29 2010-01-14 Nippon Mining & Metals Co Ltd 電子材料用Ｃｕ−Ｎｉ−Ｓｉ系合金板又は条

Family Cites Families (17)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US2851353A (en) * 1953-07-15 1958-09-09 Ibm Copper-base alloys
US4378332A (en) * 1981-06-15 1983-03-29 Ford Motor Company Aluminum hardened copper alloy
US4692192A (en) * 1984-10-30 1987-09-08 Ngk Insulators, Ltd. Electroconductive spring material
JPH0238653B2 (ja) * 1986-01-27 1990-08-31 Kobe Steel Ltd Purasuchitsukukanagatayodogokinoyobisonoseizohoho
JPS63210247A (ja) * 1987-02-27 1988-08-31 Sumitomo Metal Mining Co Ltd 高強度銅合金
JPS63266033A (ja) * 1987-04-23 1988-11-02 Mitsubishi Electric Corp 銅合金
JP3383615B2 (ja) * 1999-08-05 2003-03-04 日鉱金属株式会社 電子材料用銅合金及びその製造方法
JP3465108B2 (ja) 2000-05-25 2003-11-10 株式会社神戸製鋼所 電気・電子部品用銅合金
JP4728704B2 (ja) 2005-06-01 2011-07-20 古河電気工業株式会社 電気電子機器用銅合金
WO2006093140A1 (ja) * 2005-02-28 2006-09-08 The Furukawa Electric Co., Ltd. 銅合金
JP4501818B2 (ja) 2005-09-02 2010-07-14 日立電線株式会社 銅合金材およびその製造方法
JP4408275B2 (ja) * 2005-09-29 2010-02-03 日鉱金属株式会社 強度と曲げ加工性に優れたＣｕ−Ｎｉ−Ｓｉ系合金
JP2007126739A (ja) 2005-11-07 2007-05-24 Nikko Kinzoku Kk 電子材料用銅合金
JP2008266787A (ja) 2007-03-28 2008-11-06 Furukawa Electric Co Ltd:The 銅合金材およびその製造方法
JP4440313B2 (ja) 2008-03-31 2010-03-24 日鉱金属株式会社 電子材料用Ｃｕ−Ｎｉ−Ｓｉ−Ｃｏ−Ｃｒ系合金
JP5261122B2 (ja) 2008-10-03 2013-08-14 Ｄｏｗａメタルテック株式会社 銅合金板材およびその製造方法
US9476474B2 (en) * 2010-12-13 2016-10-25 Nippon Seisen Co., Ltd. Copper alloy wire and copper alloy spring

Patent Citations (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
GB2051127A (en) * 1979-04-30 1981-01-14 Delta Enfield Metals Precipitation hardening copper alloys
JPH02179839A (ja) * 1988-12-29 1990-07-12 Kobe Steel Ltd 耐衝撃特性及び熱間加工性に優れた高強度銅合金
JPH03126829A (ja) * 1989-10-06 1991-05-30 Sumitomo Metal Mining Co Ltd 工具用非発火性銅合金
JPH03173730A (ja) * 1989-12-01 1991-07-29 Sumitomo Metal Mining Co Ltd 工具用非発火性銅合金
JPH0499140A (ja) * 1990-08-03 1992-03-31 Hitachi Ltd プラスチック成形用金型材料
DE4226692A1 (de) * 1991-08-13 1993-03-04 Mitsubishi Materials Corp Ausscheidungshaertbare legierungen auf kupferbasis mit hoher festigkeit bei erhoehten temperaturen
JPH07268512A (ja) * 1994-03-30 1995-10-17 Mitsubishi Materials Corp 熱伝導度、高温硬さおよび耐酸化性に優れた耐熱銅合金およびこの耐熱銅合金からなる焼成型
JP2010007174A (ja) * 2008-05-29 2010-01-14 Nippon Mining & Metals Co Ltd 電子材料用Ｃｕ−Ｎｉ−Ｓｉ系合金板又は条

Non-Patent Citations (4)

* Cited by examiner, † Cited by third party
Title
"Mechanical Properties of Intermetallic Compounds Formed Between Tin (Solder) and Copper or Nickel - Hardness as a function of temperature for Cu6Sn5, Cu3Sn, and Ni3Sn4", , 23 July 2014 (2014-07-23), pages 1-2, XP002727695, Retrieved from the Internet: URL:http://www.msed.nist.gov/mechanical_properties/solder_mechanicalprop.html [retrieved on 2014-07-23] *
GRYZIECKI JANUSZ ET AL: "The role of microadditions in the kinetic change of precipitation during the aging process of nickel-aluminium bronze", ARCHIVES OF METALLURGY,, vol. 48, no. 3, 31 December 2003 (2003-12-31), pages 245-259, XP009179304, *
See also references of WO2012081573A1 *
ZHU ZHI-YUAN ET AL: "Solid solution and aging of Cu-Ni-Al-Si alloy", JINSHU RECHULI - HEAT TREATMENT OF METALS, ZHONGGUO JIXIE GONGCHENG XUEHUI, RECHULI XUEHUI, BEIJING, CN, vol. 32, no. 4, 31 December 2007 (2007-12-31), pages 83-85, XP009179303, ISSN: 0254-6051 *

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP3859022A4 (de) * 2018-09-27 2022-07-27 Dowa Metaltech Co., Ltd Kupferlegierungsblech auf der basis von cu-ni-al, verfahren zu seiner herstellung und leitendes federelement

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KR101576715B1 (ko) 2015-12-10
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