EP1967596B1 - Matériau de feuille d'alliage de cuivre à base de Cu-Ni-Si et son procédé de fabrication - Google Patents

Matériau de feuille d'alliage de cuivre à base de Cu-Ni-Si et son procédé de fabrication Download PDF

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EP1967596B1
EP1967596B1 EP20080002634 EP08002634A EP1967596B1 EP 1967596 B1 EP1967596 B1 EP 1967596B1 EP 20080002634 EP20080002634 EP 20080002634 EP 08002634 A EP08002634 A EP 08002634A EP 1967596 B1 EP1967596 B1 EP 1967596B1
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plane
copper alloy
rolling
crystal
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EP1967596A1 (fr
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Weilin Gao
Hisashi Suda
Hiroto Narieda
Akira Sugawara
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Dowa Metaltech Co Ltd
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Dowa Metaltech 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
    • C22C1/00—Making non-ferrous alloys
    • C22C1/06—Making non-ferrous alloys with the use of special agents for refining or deoxidising
    • 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

Definitions

  • This invention relates to a Cu-Ni-Si-based copper alloy sheet material suitable for use in electrical and electronic parts such as connectors, lead frames, relays, switches and the like, particularly to a copper alloy sheet material that exhibits excellent bending workability and stress relaxation resistance property while maintaining high strength and high conductivity, and a method of manufacturing the same.
  • the connectors, lead frames, relays, switches and other current-carrying components of electrical and electronic parts require good conductivity for minimizing generation of joule heat due to passage of current and also require high strength capable of enduring stress imparted during assembly and/or operation of the electrical or electronic parts. Because electrical and electronic parts are generally formed by bending, the current-carrying components must also have excellent bending workability. Moreover, in order to ensure contact reliability between the electrical and electronic parts, they require endurance against the tendency for contact pressure to decline over time (stress relaxation), namely, they need to be excellent in stress relaxation resistance property.
  • Stress relaxation resistance property is of particular importance when the part is exposed to a high-temperature environment as in the case of an automobile connector.
  • Stress relaxation refers to the phenomenon of, for instance, a spring member constituting an element of an electrical or electronic part experiencing a decline in contact pressure with passage of time in a relatively high-temperature environment of, say, 100 to 200 °C, even though it might maintain a constant contact pressure at normal temperatures. It is thus one kind of creep phenomenon. To put it in another way, it is the phenomenon of stress imparted to a metal material being relaxed by plastic deformation owing to dislocation movement caused by self-diffusion of atoms constituting the matrix and/or diffusion of solute atoms.
  • Cu-Ni-Si-based alloy (known as Corson alloy) has attracted attention in recent years for its excellent balance between strength and conductivity. Copper alloy of this type can be markedly improved in strength while still retaining relatively high conductivity (of 30% to 45% IACS).
  • Cu-Ni-Si-based alloy is known to be an alloy system that is difficult to make excellent in both strength and bending workability or both bending workability and stress relaxation resistance property.
  • DE 4 115 998 A1 discloses a method of manufacturing a copper alloy having a high strength and good bending characteristics. The alloys have a composition of 1 - 3.5 % Ni,0.1 - 0.8 % Si with the balance being Cu and inevitable impurities.
  • Strength can be increased by such commonplace methods as adding a greater amount of solute elements like Ni and Si and increasing the rolling reduction ratio following aging treatment.
  • the former method reduces conductivity and causes bending workability to decline with increasing amount of Ni-Si type precipitates.
  • the latter method increases work-hardening, thereby degrading bending workability (particularly bending workability perpendicular to the rolling direction, i.e., bending workability with respect to a bending axis lying parallel to the rolling direction).
  • a high strength level and a high conductivity level may be achieved, it may become impossible to form the electrical or electronic part.
  • a method commonly used to avoid a decrease in bending workability is to omit (or minimize) post-aging finish cold rolling and make up for the strength loss this causes by adding large amounts of solute elements such as Ni and Si.
  • this method increases the tendency of work-hardening for the material, so that when the notch-and-bend method is adopted, the notching markedly increases hardness in the vicinity of the notch. A problem therefore arises of the bending workability being radically degraded at the time of bending the material along the notch.
  • Crystal grain boundary area per unit volume increases with decreasing crystal grain diameter.
  • Crystal grain refinement therefore promotes stress relaxation, which is a type of creep phenomenon.
  • the diffusion velocity of the atom along grain boundaries is extremely high than that within the grains, so that the loss of stress relaxation resistance property caused by crystal grain refinement becomes a major problem.
  • crystal grain refinement and control of crystal orientation are effective for improving the bending workability of copper alloy sheet material.
  • control of the crystal orientation (texture) of Cu-Ni-Si-based copper alloy in the case where ordinary manufacturing processes are utilized, the X-ray diffraction pattern from the sheet surface (rolled surface) is generally dominated by diffraction peaks from the four crystal planes ⁇ 111 ⁇ , ⁇ 200 ⁇ , ⁇ 220 ⁇ and ⁇ 311 ⁇ , and the X-ray diffraction intensities from other crystal planes are very weak compared with those from these four planes.
  • the diffraction intensities from the ⁇ 200 ⁇ plane and the ⁇ 311 ⁇ plane are usually large after solution heat treatment (recrystallization).
  • the ensuing cold rolling lowers the diffraction intensities from these planes, and the X-ray diffraction intensity from the ⁇ 220 ⁇ plane increases relatively.
  • the X-ray diffraction intensity from the ⁇ 111 ⁇ plane is usually not much changed by the cold rolling.
  • Patent Document 1 defines the ratio of the sum of the X-ray diffraction intensities from the ⁇ 200 ⁇ plane and the ⁇ 311 ⁇ plane to the X-ray diffraction intensity from the ⁇ 220 ⁇ plane as: I 200 + I 311 / I 220 > 0.5.
  • This relational expression suggests that bending workability improves when the reduction ratio in the cold rolling conducted after solution heat treatment is lowered. This kind of texture regulation usually lowers strength. And, in fact, tensile strength of the copper alloy provided by Patent Document 1 is only on the order of 560 to 670 MPa.
  • Patent Documents 2 and 3 point out that the fact that bending workability is anisotropic makes it difficult to improve bending workability simultaneously both for the case where the bending axis lies perpendicular to the rolling direction (G.W.) and for the case where it lies parallel to the rolling direction (B.W.). It therefore separately defines means for improving G.W. bending workability and means for improving B.W. bending workability.
  • the former means is to make the ratio of the sum of the X-ray diffraction intensities from the ⁇ 111 ⁇ plane and the ⁇ 311 ⁇ plane to the X-ray diffraction intensity from the ⁇ 220 ⁇ plane, i.e., (I ⁇ 111 ⁇ + I ⁇ 311 ⁇ ) / I ⁇ 220 ⁇ , not greater than 2.0 and the latter means is to make the ratio not less than 2.0.
  • Patent Document 4 defines the X-ray diffraction intensities from the ⁇ 311 ⁇ plane, ⁇ 220 ⁇ plane and ⁇ 200 ⁇ plane as a function of crystal grain diameter A, as follows: I 311 x A / I 311 + I 220 + I 200 ⁇ 1.5.
  • Patent Document 5 defines the percentage of cube orientation [ ⁇ 001 ⁇ ⁇ 100>] as 50% or greater and the average crystal grain diameter as 10 ⁇ m or less. These techniques require crystal grain refinement. The stress relaxation resistance property generally decreases in such cases.
  • an object of the present invention is to provide a Cu-Ni-Si-based copper alloy that retains high strength while simultaneously achieving the demanding bending workability required in the notch-and-bend method and the stress relaxation resistance property needed to ensure reliability in the harsh use environments of, for example, vehicle-mounted connectors.
  • the inventors discovered that there exists a crystal orientation with an orientation relationship such that deformation easily occurs in a direction normal to a surface of a rolled sheet (ND direction) and also occurs easily in two mutually perpendicular directions within the sheet surface.
  • the inventors determined an alloy composition range and manufacturing conditions enabling establishment of a texture composed mainly of crystal grains having this unique orientation relationship. The present invention was accomplished based on this knowledge.
  • the present invention provides a copper alloy sheet as given in claims 1 to 3.
  • I ⁇ 420 ⁇ is the X-ray diffraction intensity from the ⁇ 420 ⁇ crystal plane in the sheet plane of the copper alloy sheet material and I 0 ⁇ 420 ⁇ is the x-ray diffraction intensity from the ⁇ 420 ⁇ crystal plane of standard pure copper powder and, similarly, I ⁇ 220 ⁇ is the X-ray diffraction intensity from the ⁇ 220 ⁇ crystal plane in the sheet plane of the copper alloy sheet material and I 0 ⁇ 220 ⁇ is the x-ray diffraction intensity from the ⁇ 220 ⁇ crystal plane of standard pure copper powder.
  • I ⁇ 420 ⁇ and I 0 ⁇ 420 ⁇ are measured under the same measurement conditions and so are I ⁇ 220 ⁇ and I 0 ⁇ 220 ⁇ .
  • the balance being Cu is meant that inclusion of elements other than those set out above is permissible within impurity ranges that do not impair the effects of the present invention. Thus, cases in which the balance is Cu and unavoidable impurities are included.
  • a copper alloy sheet material of the foregoing description having an average crystal grain diameter of 10 ⁇ m - 60 ⁇ m is particularly preferable.
  • the grain diameter is determined by the cutting method of JIS H 0501, specifically by polishing and then etching the sheet surface (rolled surface) and observing the surface with a microscope.
  • a method of manufacturing this copper alloy sheet is provided in claims 4 to 8.
  • hot rolling at 950 °C - 400 °C is meant that rolling passes of the hot rolling are conducted in the range of 950 °C - 400 °C.
  • a reduction ratio of 0% means that the rolling is not conducted. In other words, one or both of the intermediate cold rolling and the finish cold rolling can be omitted.
  • the heating time from 100 °C to 700 °C is preferably 20 sec or less and the solution heat treatment is preferably conducted by setting the holding time in the range of 700 °C - 850 °C and the ultimate temperature so that the average crystal grain diameter after solution heat treatment becomes 10 ⁇ m - 60 ⁇ m.
  • 150 °C - 550 °C low-temperature annealing is preferably conducted after the finish cold rolling.
  • the present invention provides a Cu-Ni-Si-based copper alloy sheet material having the basic properties required by connectors, lead frames, relays, switches and other such electrical and electronic parts, namely, a Cu-Ni-Si-based copper alloy sheet material of high strength having a tensile strength of 700 MPa or greater, excellent bending workability and stress relaxation resistance property, and excellent bending workability after notching.
  • Conventional Cu-Ni-Si-based copper alloy manufacturing methods have not been capable of consistently achieving marked improvement of bending workability and stress relaxation resistance property while maintaining a high strength level, namely, a tensile strength of 700 MPa or greater.
  • This invention provides a solution in response to the trend toward smaller and thinner electrical and electronic parts, which is expected to accelerate even further in the future.
  • the X-ray diffraction pattern from the Cu-Ni-Si-based copper alloy sheet surface generally includes diffraction peaks from the four crystal planes ⁇ 111 ⁇ , ⁇ 200 ⁇ , ⁇ 220 ⁇ and ⁇ 311 ⁇ , and the X-ray diffraction intensities from other crystal planes are very weak compared with those from these four planes.
  • the diffraction intensity from the ⁇ 420 ⁇ plane is so weak as to be negligible.
  • the Schmid factor is an index of ease of plastic deformation (slip) when an external force acts on a crystal in a certain direction.
  • the Schmid factor is represented by cos ⁇ ⁇ cos ⁇ and the value thereof falls in the range of 0.5 or less.
  • a larger Schmid factor (one closer to 0.5) means a larger shear stress in the slip direction. From this it follows that when a force is applied to a crystal in a certain direction, the ease of crystal deformation increases with increasing magnitude of the Schmid factor (increasing proximity to 0.5).
  • the crystal structure of the Cu-Ni-Si-based copper alloy is face centered cubic (fcc).
  • the slip plane is ⁇ 111 ⁇ and the slip direction is ⁇ 110>, and it is known that in the actual crystal, deformation more readily occurs and work-hardening decreases in proportion as the Schmid factor is larger.
  • FIG. 1 is a standard inverse pole figure showing the Schmid factor distribution of face centered cubic crystal.
  • the Schmid factor in the ⁇ 120> direction is 0.490, which is close to 0.5. In other words, when an external force is applied in the ⁇ 120> direction, the face centered cubic crystal deforms very easily.
  • the Schmid factors in the other directions are: ⁇ 100> direction, 0.408; ⁇ 113> direction 0.445; ⁇ 110> direction, 0.408; ⁇ 112> direction, 0.408; and ⁇ 111> direction, 0.272.
  • a texture's main orientation component is the ⁇ 420 ⁇ plane
  • the proportion of crystals whose ⁇ 420 ⁇ plane (and ⁇ 210 ⁇ plane) lie substantially parallel to the sheet surface (rolled surface) is high.
  • the direction normal to the sheet surface (ND) is the ⁇ 120> direction and its Schmid factor is near 0.5, so that it readily deforms in the ND and work-hardening is low.
  • the rolled texture of the Cu-Ni-Si-based alloy ordinarily has the ⁇ 220 ⁇ plane as its main orientation component.
  • the proportion of crystals whose ⁇ 220 ⁇ plane (and ⁇ 110 ⁇ plane) lie substantially parallel to the sheet surface (rolled surface) is high.
  • the ND is the ⁇ 110> direction and its Schmid factor is on the order of 0.4, so that work-hardening upon deformation in the ND is large compared with that in the case of a crystal whose main orientation plane is the ⁇ 210 ⁇ plane.
  • the recrystallized texture of the Cu-Ni-Si-based alloy ordinarily has the ⁇ 311 ⁇ plane as its main orientation component.
  • the ND In a crystal whose main orientation plane is the ⁇ 311 ⁇ plane, the ND is the ⁇ 113> direction and its Schmid factor is on the order of 0.45, so that work-hardening upon deformation in the ND is large compared with that in the case of a crystal whose main orientation plane is the ⁇ 210 ⁇ plane.
  • the degree of work-hardening at the time of deformation in the direction normal to the sheet surface (ND) is very important. This is because notching is indeed deformation in the ND, and the degree of work-hardening at the portion reduced in thickness by the notching strongly governs the bending workability during subsequent bending along the notch (see FIG. 7 discussed later).
  • a texture such as one satisfying Expression (1) that has the ⁇ 420 ⁇ plane as its main orientation component
  • work-hardening caused by notching becomes small in comparison with that in the case of the rolled texture or recrystallized texture of the Cu-Ni-Si-based alloy. This is considered to be the reason for the marked improvement in bending workability in the notch-and-bend method.
  • the ⁇ 120> direction and ⁇ 210> direction are present as other directions in the sheet plane, i.e., in the ⁇ 210 ⁇ plane, in the crystal whose main orientation plane is the ⁇ 210 ⁇ plane, and these directions are mutually perpendicular.
  • the rolling direction (LD) is the ⁇ 100> direction
  • the direction perpendicular to the rolling direction (TD) is the ⁇ 120> direction.
  • the LD is the [001] direction
  • the TD is the [-2, 1, 0] direction.
  • the Schmid factors of such a crystal are LD: 0.408 and TD: 0.490.
  • LD is the ⁇ 112> direction and TD is the ⁇ 111> direction
  • the Schmid factors are LD: 0.408 and TD: 0.272.
  • LD is the ⁇ 112> direction and TD is the ⁇ 110> direction
  • the Schmid factors are LD: 0.408 and TD: 0.408.
  • I ⁇ 420 ⁇ is the X-ray diffraction intensity from the ⁇ 420 ⁇ crystal plane in the sheet plane of the copper alloy sheet material
  • I 0 ⁇ 420 ⁇ is the X-ray diffraction intensity from the ⁇ 420 ⁇ crystal plane of standard pure copper powder.
  • the crystal orientation of the ⁇ 210 ⁇ plane is judged from the ⁇ 420 ⁇ plane reflection.
  • Still more preferable is to satisfy the following Expression (1)'.
  • the texture whose main orientation component is the ⁇ 420 ⁇ plane is formed as a recrystallized texture by the solution heat treatment explained later.
  • the cold rolling consists of the intermediate cold rolling and finish cold rolling explained later but increasing the reduction ratio of the cold rolling inhibits development of a rolled texture whose main orientation component is the ⁇ 220 ⁇ plane.
  • the ⁇ 420 ⁇ orientation density decreases as the ⁇ 220 ⁇ orientation density increases, it suffices to regulate the reduction ratio to maintain the relationship of Expression (1) or preferably Expression (1)'.
  • Expression (2) it is preferable to satisfy Expression (2) below because excessive development of the texture whose main orientation component is the ⁇ 220 ⁇ plane may cause a decline in workability.
  • I ⁇ 220 ⁇ is the X-ray diffraction intensity from the ⁇ 220 ⁇ crystal plane in the sheet plane of the copper alloy sheet material
  • I 0 ⁇ 220 ⁇ is the X-ray diffraction intensity from the ⁇ 220 ⁇ crystal plane of standard pure copper powder.
  • a smaller average crystal grain diameter is advantageous for improving bending workability but apt to degrade stress relaxation resistance property when too small.
  • a final average crystal grain diameter of 10 ⁇ m or greater, preferably exceeding 10 ⁇ m is suitable because it facilitates realization of a stress relaxation resistance property of a level satisfactory even for vehicle-mounted connector applications.
  • an excessively large average crystal grain diameter is apt to cause surface roughening at bends and may degrade bending workability, so it is preferably made to fall in the range of not greater than 60 ⁇ m. Regulation to within the range of 15 to 40 ⁇ m is desirable.
  • the final average crystal grain diameter is substantially determined by the crystal grain diameter at the stage following solution heat treatment. The average crystal grain diameter can therefore be controlled by controlling the solution heat treatment conditions explained later.
  • the present invention utilizes a Cu-Ni-Si-based copper alloy.
  • Cu-Ni-Si-based copper alloy as termed in this specification also includes copper alloys obtained by adding Sn, Zn and other alloying elements to a basic three-element Cu-Ni-Si composition, as given in the claims.
  • Ni and Si form precipitates and contribute to strength enhancement and improvement of electrical conductivity and thermal conductivity. These effects are hard to effectively elicit at a content of Ni of less than 0.7 mass% or a content of Si of less than 0.2 mass percent.
  • an excessive Ni content or an excessive Si content is apt to cause formation of coarse precipitates that tend to degrade bending workability and stress relaxation resistance property.
  • development of a recrystallization texture whose main orientation component is the ⁇ 420 ⁇ plane becomes hard to achieve in the solution heat treatment, which makes it difficult to realize a final sheet material excellent in bending workability.
  • the Ni content therefore needs to be made not greater than 4.2 mass%, preferably not greater than 3.5 mass%, still more preferably not greater than 3.0 mass%.
  • the Si content must be made not greater than 1.0 mass%, preferably not greater than 0.7 mass%.
  • the most preferable content range of Ni is 1.2 mass% - 2.5 mass% and the most preferable content range of Si is 0.3 mass% - 0.6 mass%.
  • Ni-Si-based precipitates formed by Ni and Si are thought to be intermetallic compounds consisting chiefly of Ni 2 Si.
  • the Ni and Si in the alloy may not all be converted to precipitates by the aging treatment but to some extent may be present in the Cu matrix in solid solution.
  • the Ni and Si present in solid solution enhance strength somewhat but have a smaller effect than when in the precipitated state. They also degrade conductivity.
  • the Ni to Si content ratio is therefore preferably brought as close as possible to that in the Ni 2 Si precipitate. In this invention, therefore, the Ni and Si contents expressed in mass% are adjusted to establish an Ni to Si ratio of between 3.0 and 6.0, preferably between 3.5 and 5.0.
  • the Ni to Si ratio is preferably adjusted to within the range of 3.0 to 4.0.
  • Sn has a solid solution strengthening effect and an effect of improving stress relaxation resistance property.
  • a content of 0.1 mass% or greater is preferable.
  • the Sn content is preferably adjusted to the range of 0.1 mass% -1.2 mass%, more preferably 0.2 mass% - 0.7 mass%.
  • Zn improves solderability and strength, and also has an effect of improving ease of casting. Moreover, when Zn is included, there is the merit of being able to use inexpensive brass scrap. However, a Zn content exceeding 2.0 mass% is apt to degrade conductivity and stress corrosion cracking resistance. Therefore, when Zn is included, its content is made 2.0 mass% or less. A Zn content of 0.1 mass% or greater is preferably established so that the foregoing effects can be thoroughly obtained, and adjustment of the content to within the range of 0.3 mass% - 1.0 mass% is particularly preferable.
  • Mg has an effect of improving stress relaxation resistance property and a desulfurization effect. For thorough manifestation of these effects, it is preferable to establish an Mg content of 0.01 % or greater. However, Mg is an easily oxidized element and markedly degrades ease of casting when present at a content of greater than 1.0 mass%. Therefore, when Mg is included, its content must be made 1.0 mass% or less.
  • the Mg content is preferably 0.01 mass% - 1.0 mass%, more preferably 0.1 mass% - 0.5 mass%.
  • Co is an element that can form a precipitate with Si and can also precipitate as a simple substance. So when Co is included, it reacts with Si present in solid solution in the Cu matrix to form a precipitate and the excess Co precipitates as a simple substance. As a result, an effect of simultaneously improving strength and conductivity can be obtained. For thorough manifestation of these effects, a Co content of 0.1 mass% is preferably established. However, Co is an expensive element that increases cost when added in excess. When Co is included, therefore, its content is made 2.0 mass% or less. The Co content is preferably 0.1 mass% to 2.0 mass% and is more preferably adjusted to within the range of 0.5 mass% - 1.5 mass%.
  • Fe has an effect of suppression in forming the ⁇ 220 ⁇ orientation due to promotion in forming the ⁇ 200 ⁇ , ⁇ 420 ⁇ and the likes recrystallization orientations after solution heat treatment. Specifically, when appropriate amounts of Fe are contained, it is apt to occur the decrease of the ⁇ 220 ⁇ orientation density and the increase of the ⁇ 420 ⁇ orientation density, which contributes to enhance bending workability. In order to obtain the effects sufficiently, a Fe content of 0.01 mass% or greater is preferably established. However, an excessive Fe content is apt to cause an excessive formation of the ⁇ 200 ⁇ orientation, thereby to cause decrease of ⁇ 420 ⁇ orientation density. Therefore, the Fe content should be 1.0 mass% or less when Fe is contained. Thus, the Fe content is desired to be within the range of 0.01 mass%- 1.0 mass%, more preferably within the range of 0.1 mass%- 0.5 mass%.
  • Cr, B, P, Zr, Ti, Mn and V Other elements that can be incorporated as required include Cr, B, P, Zr, Ti, Mn and V.
  • Cr, B, P, Zr, Ti, Mn and V act to heighten alloy strength and reduce stress relaxation.
  • Cr, Zr, Ti, Mn and V readily form high melting point compounds with S, Pb and other elements present as unavoidable impurities.
  • B, P, Zr and Ti have an effect of refining the grain size of the cast structure and can contribute to hot workability improvement.
  • the total content of these elements is preferably in the range of 3 mass% or less, more preferably in the range of 2 mass% or less, still more preferably in the range of 1 mass% or less, and most preferably in the range of 0.5 mass% or less.
  • the copper alloy sheet material used as a starting material should preferably have a tensile strength of 700 MPa or greater, preferably 750 MPa or greater.
  • the rolling direction is called the LD (longitudinal direction)
  • the direction perpendicular to the rolling direction and thickness direction of the sheet is called the TD (transverse direction)
  • the bending workability expressed as the ratio of minimum bending radius R to thickness t in a 90° W bend test should preferably be 1.0 or less, preferably 0.5 or less, in both the LD and TD.
  • the LD post-notching bending workability expressed as R/t should preferably be 0.
  • the post-notching bending workability is determined by the method explained in the Examples set out below.
  • the "LD bending workability” is the bending workability evaluated for a bending workability test piece cut so that its longer direction corresponds to the LD, with bending performed around an axis lying in the TD.
  • the "TD bending workability” is the bending workability evaluated for a bending workability test piece cut so that its longer direction corresponds to the TD, with bending performed around an axis lying in the LD.
  • the TD value of the stress relaxation resistance property is especially important in vehicle-mounted connectors and similar applications. Stress relaxation property is therefore preferably evaluated as stress relaxation rate using a test piece whose longer direction corresponds to the TD.
  • the stress relaxation rate measured for a test piece held at 150 °C for 1000 hours with the maximum load stress on the sheet surface at 80% of 0.2% yield strength is preferably 5% or less, more preferably 3% or less.
  • the foregoing copper alloy sheet material according to the invention can, for example, be manufactured by the production processes set out below. Melting/Casting ⁇ Hot rolling ⁇ Cold rolling ⁇ Solution heat treatment ⁇ Intermediate cold rolling ⁇ Aging treatment ⁇ Finish cold rolling ⁇ Low-temperature annealing. It is, however, necessary to introduce refinements into some of the processes as explained in the following. Although not included in the production processes enumerated above, hot rolling can be followed by optional facing, and heat treatment can be followed by optional pickling, polishing and degreasing. The processes will now be explained individually.
  • Melting/casting can be done in accordance with the ordinary copper alloy casting method.
  • the slab can be produced by continuous casting, semi-continuous casting or the like.
  • Cu-Ni-Si-based copper alloy hot rolling is usually conducted by the method of rolling in a high-temperature range of 700 °C or greater or 750 °C or greater followed by quenching upon completion of the rolling.
  • a copper alloy sheet material having the unique texture of the present invention is difficult, if not impossible, to manufacture under these commonly accepted hot rolling conditions. More specifically, the inventors conducted an investigation in which the inventors varied the conditions in the processes following the hot rolling under such conditions over broad ranges but were unable to find conditions that enabled manufacture of a copper alloy sheet material having the ⁇ 420 ⁇ plane as its main orientation direction with good reproducibility.
  • the inventors therefore carried out a further thorough study through which the inventors discovered the hot rolling conditions of the present invention, namely, the conditions of conducting a first pass in a temperature range of 950 °C - 700 °C and conducting rolling in a temperature range of less than 700 °C to 400 °C at a reduction ratio of 40% or greater.
  • rolling at a high temperature exceeding 950 °C is undesirable because it is liable to cause cracking at portions where the alloying components have segregated and other portions where the melting point has dropped.
  • a large rolling load is required to achieve a reduction of 60% in a single pass and it is acceptable to bring the total reduction up to 60% or greater by dividing the rolling into multiple passes.
  • the formation of some precipitates in this way and the combination of the cold rolling and the solution heat treatment in the ensuing processes facilitates formation of a recrystallization texture whose main orientation component is the ⁇ 420 ⁇ plane.
  • a number of rolling passes can be conducted in the less than 700 °C to 400 °C temperature range. It is more effective to conduct the final pass in the hot rolling at a temperature of 600 °C or less.
  • the total reduction in the hot rolling should be made about 80% to 95%.
  • no intermediate annealing is inserted into the cold rolling passes after the hot rolling and before the solution heat treatment. If intermediate annealing should be conducted after the hot rolling and before the solution heat treatment, the recrystallization texture whose main orientation component is the ⁇ 420 ⁇ plane formed by the solution heat treatment would be extremely weak.
  • the solution heat treatment is preferably conducted at a furnace temperature of 700 °C - 850 °C.
  • the temperature is too low, the recrystallization is incomplete and entry of the solute elements into solid solution is insufficient.
  • the temperature is too high, the crystal grains become coarse. In either case, it becomes difficult to finally obtain a high-strength material excellent in bending workability.
  • rapidly increasing the temperature to 700 °C was found to be highly effective for increasing the ⁇ 420 ⁇ orientation density.
  • the heating time from 100 °C to 700 °C is preferably made 20 sec or less, more preferably 15 sec or less.
  • the heat treatment is preferably carried out with the holding time and ultimate attaining temperature in the range of 700 °C to 850 °C set so that the average grain diameter of the recrystallization grains (twin boundaries not considered crystal boundaries) becomes 10 ⁇ m - 60 ⁇ m, more preferably 15 ⁇ m - 40 ⁇ m.
  • the recrystallization grains are too fine, the recrystallization texture whose main orientation component is the ⁇ 420 ⁇ plane becomes weak. Excessively fine recrystallization grains are also disadvantageous from the viewpoint of improving stress relaxation resistance property.
  • the recrystallization grains are too coarse, surface roughness tends to occur at bends.
  • the recrystallization grain diameter varies depending on the cold rolling reduction ratio before the solution heat treatment and chemical composition.
  • the holding time and ultimate attaining temperature can be set within the range of 700 °C to 850 °C based on the results of experiments conducted for the alloy concerned to determine the relationship between the solution heat treatment heating pattern and the average crystal grain diameter.
  • suitable conditions can be set within the heating conditions of a temperature of 700 °C to 850 °C and a holding time of 10 sec to 10 min.
  • cold rolling can be conducted at a reduction ratio of 50% or less.
  • the cold rolling at this stage has an effect of promoting precipitation in the ensuing aging treatment process, thereby making it possible to shorten the aging time for bringing out the required properties (conductivity, hardness).
  • this cold rolling develops texture whose main orientation component is the ⁇ 220 ⁇ plane, crystal grains whose ⁇ 420 ⁇ plane lies parallel to the sheet surface remain sufficiently at a cold rolling reduction rate in the range of 50% or less.
  • the cold rolling at this stage must be conducted at a reduction ratio of 50% or less and is preferably conducted at a reduction ratio between 0 and 35%. When the reduction ratio is too high, precipitation in the following aging treatment becomes uneven and overaging is apt to occur.
  • the aging treatment is conducted under conditions favorable for improving the conductivity and strength of the alloy, and is carried out without increasing the temperature very much.
  • the aging treatment temperature is too high, crystal orientation dominated by the ⁇ 420 ⁇ orientation developed by the solution heat treatment is weakened, with the result that a sufficient bending workability improvement effect may not be obtained.
  • the aging treatment is preferably conducted so that the sheet temperature becomes 400 °C - 500 °C, more preferably 420 °C - 480 °C. Good results can be obtained at an aging treatment time of around 1h to 10h.
  • This cold rolling is for further improving the strength level.
  • rolled texture whose main orientation component is the ⁇ 220 ⁇ plane develops with increase in the cold rolling reduction rate.
  • the reduction ratio is too high, the relative dominance of rolled texture with ⁇ 220 ⁇ orientation becomes excessive and realization of a crystal orientation whose strength and bending workability are both at high levels becomes impossible.
  • An exhaustive study carried out by the inventors revealed that the finish cold rolling should preferably be carried out in a reduction ratio range not exceeding 50%. A reduction ratio in this range makes it possible to maintain a crystal orientation that satisfies Expression (1). As with the foregoing intermediate cold rolling, this finish cold rolling is not absolutely necessary.
  • the final sheet thickness is defined as about 0.05 mm - 1.0 mm, preferably 0.08 mm - 0.5 mm.
  • Low-temperature annealing can be implemented after the finish cold rolling for the purpose of enhancing bending workability through reduction of sheet residual stress and enhancing stress relaxation resistance property through reduction of voids and dislocation at the slip plane.
  • the heating temperature is preferably set to make the sheet temperature 150 °C - 550 °C. Annealing under this temperature condition enables improvement of bending workability and stress relaxation resistance property with substantially no strength decrease. It also has a conductivity enhancing effect. When the heating temperature is too high, the sheet softens in a short time to make property variance likely to occur in both the batch and continuous systems. When the heating temperature is too low, the property improvement effect cannot be fully obtained.
  • the holding time at the temperature should preferably be 5 sec or greater, with good results usually being obtained within 1 h. When the finish cold rolling is not conducted, the low-temperature annealing should be omitted.
  • Molten copper alloys produced to have the compositions shown in Table 1 were cast using a vertical continuous casting machine.
  • samples of 50-mm thickness were cut from the obtained slabs (thickness: 180 mm).
  • the samples were heated to 950 °C and then extracted, whereafter hot rolling was begun.
  • the pass schedule at this time was, except in some Comparative Examples, established to conduct rolling at a reduction ratio of 60% or greater in the 950 °C - 700 °C temperature range and also conduct rolling in the temperature range of less than 700 °C.
  • the final pass temperature of the hot rolling was between 600 °C and 400 °C.
  • the total hot rolling reduction ratio starting from the slab was about 90%.
  • the oxidized surface layer was removed by machine polishing (facing).
  • cold rolling was carried out at one of various reduction ratios, whereafter each sample was subjected to solution heat treatment. Temperature change during solution heat treatment was monitored with a thermocouple attached to the sample surface and the heating time between 100 °C and 700 °C in the heating process was determined.
  • the average grain diameter (twin boundaries not considered crystal boundaries) of the recrystallization grains after the solution heat treatment was made to fall between 10 ⁇ m and 60 ⁇ m by, with consideration to the alloy composition, adjusting the ultimate attaining temperature to within the range of 700 °C - 850 °C and adjusting the holding time in the range of 700 °C - 850 °C to within the range of 10 sec - 10 min.
  • the sheet following solution heat treatment was subjected to intermediate cold rolling at one of various reduction ratios, followed by aging treatment.
  • the aging treatment temperature was made a sheet temperature of 450 °C, and the aging time was adjusted with consideration to the alloy composition so that hardness peaked with 450 °C aging.
  • test specimens were examined by the methods set out below for crystal grain texture, X-ray diffraction intensity, conductivity, tensile strength, stress relaxation rate, ordinary bending workability, and post-notching bending workability. Some test specimens were further examined for crystal orientation by the electron backscatter diffraction pattern (EBSP) method.
  • EBSP electron backscatter diffraction pattern
  • a polish-finished sample prepared by polishing the surface (rolled surface) of the test specimen with # 1500 waterproof sandpaper was measured at the polish-finished surface for reflection surface x-ray diffraction integral intensity of the ⁇ 420 ⁇ plane and ⁇ 220 ⁇ plane using an x-ray diffractometer (XRD) under conditions of Mo-K ⁇ radiation, tube voltage of 20 kV, and tube current of 2 mA.
  • XRD x-ray diffractometer
  • the measured values were used to calculate the X-ray diffraction intensity ratio I ⁇ 420 ⁇ / I 0 ⁇ 420 ⁇ in Expression (1) and the X-ray diffraction intensity ratio I ⁇ 220 ⁇ / I 0 ⁇ 220 ⁇ in Expression (2).
  • a bending test piece (width: 10 mm) was taken from each test specimen so that its longer direction corresponded to the TD and was fastened to have an arch-like bend such that the magnitude of the surface stress of the middle portion in the longer direction of the test piece became 80% of the 0.2% yield strength.
  • LD bending test pieces and TD bending test pieces (each 10 mm in width) were taken from each test specimen so that their longer directions corresponded to the LD and the TD, respectively, and were subjected to 90° W bend testing in compliance with JIS H 3110.
  • the surfaces and cross-sections at the bends of the test pieces after testing were observed with an optical microscope at a magnification of 100x to determine the smallest bending radii R at which cracking did not occur and these values were divided by the thickness t of the test specimen to determine the R/t values for the LD and the TD.
  • a test specimen whose R/t values for both the LD and TD were 0.5 or less was judged acceptable.
  • a narrow rectangular test piece (width: 10 mm) taken from each test specimen so that its longer direction corresponded to the LD was formed with a notch extending across its full width by using a notch forming jig of the cross-sectional shape shown in FIG. 4 (width of flat face at tip of protrusion: 0.1 mm, side face angles: 45°) and applying a load of 10 kN as shown in FIG 5 .
  • the notch direction i.e., the direction parallel to the groove
  • the depth of the notch of the bending-test-piece-with-notch prepared in this manner was measured and the notch depth ⁇ , illustrated schematically in FIG. 6 , was found to be about 1/4 to 1/6 the thickness t .
  • a notch bending test was carried out on each bending-test-piece-with-notch by subjecting it to a notch 90° W bend test in compliance with JIS H 3110.
  • a jig was used in which the R of the center protrusion tip of the lower die was 0 mm, and the 90° W bend test was conducted with the bending-test-piece-with-notch placed with its notched surface facing downward and set so that the center protrusion tip aligned with the notch.
  • the surface and cross-section at the bend of the test piece after testing were observed with an optical microscope at a magnification of 100x to check for cracking.
  • a rating of G (good) was assigned when no cracking was found and a rating of P (poor) was assigned when cracking was observed. Breakage at the bend was indicated by R (rupture).
  • EBSP refers to the Electron Back-Scatter Diffraction Pattern method. An electron beam is projected onto individual grains of the specimen and the orientation of the individual crystals is determined from the electron diffraction pattern. The final finishing of the specimen surface was done by vibration polishing (a polishing method that does not introduce strain). The crystal orientations determined by EBSP were used to calculate the percentage of surface area accounted for by crystals having the ⁇ 120 ⁇ plane in parallel with the sheet surface (rolled surface).
  • Crystals whose direction perpendicular to the sheet surface (ND) was within 10° of the ⁇ 120> direction were deemed to be "crystals having the ⁇ 120 ⁇ plane in parallel with the sheet surface" and the percentage of the surface area accounted for by these crystals was called the " ⁇ 120 ⁇ orientation ratio by EBSP.”
  • the ratio is preferably 20% or greater, more preferably 25% or greater.
  • the specimens of Comparative Examples No. 21 to No. 25 were manufactured from the same alloys as those of Invention Examples No. 1 to No. 4 by conventional processes (including, for example, some in which the hot rolling final pass temperature was made 650 °C or greater or 700 °C or greater, and some in which an intermediate annealing step was interposed at a point after hot rolling and before solution heat treatment).
  • the X-ray diffraction intensity of the ⁇ 420 ⁇ crystal plane was weak, and tradeoffs were seen between strength and bending workability or between bending workability and stress relaxation resistance property.
  • the specimens were particularly inferior in post-notching bending workability.
  • Comparative Example No. 34 was a commercially available product (C7025) considered to have excellent bending workability and stress relaxation resistance property.
  • a comparison with Invention Example No. 5 of substantially the same composition shows it to be inferior in both bending workability and stress relaxation resistance property.
  • FIGs. 2 and 3 are inverse pole figures showing the orientation distribution in the sheet plane direction measured by the EBSP method in an Invention Example (No. 1) and a Comparative Example (No. 21), respectively.
  • the dotted lines in the figures indicate the range of crystal orientation within 10° of the ⁇ 120 ⁇ crystal plane.
  • the ⁇ 120 ⁇ crystal plane concentration is clearly higher in the Invention Example ( FIG. 2 ) than in the Comparative Example ( FIG. 3 ).
  • the crystal orientation in the sheet surface direction is distributed in a direction whose Schmid factor is very high (see FIG. 1 ). This is considered to be the reason for the marked improvement in bending workability (particularly post-notching bending workability).
  • FIG. 7 is a photograph of a cross-section taken in Comparative Example No. 22 showing Vickers hardness distribution in the cross-section after notching. Work-hardening is present in the portion of the sheet thinned by notching.
  • FIG. 8 is a cross-sectional photograph showing the specimen after bending. The state of the cracking that occurred can be seen.

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Claims (8)

  1. Matériau de feuille d'alliage de cuivre comprenant, en pourcent en masse, Ni : 0,7% - 4,2%, Si : 0,2% - 1,0%, et optionnellement un ou plusieurs des éléments Sn : 1,2% ou moins, Zn : 2,0% ou moins, Mg : 1,0% ou moins, Co : 2,0% ou moins, et Fe : 1,0% ou moins, et comprenant en outre optionnellement un total de 3% ou moins d'un ou plusieurs des éléments Cr, B, P, Zr, Ti, Mn et V, le reste étant constitué de Cu, et ayant une orientation de cristal vérifiant l'expression (1) : I 420 / I 0 420 > 1 , 0
    Figure imgb0015
    où I{420} est l'intensité de diffraction de rayons X à partir du plan de cristal {420} dans le plan de la feuille du matériau de feuille d'alliage de cuivre et I0 {420} est l'intensité de diffraction de rayons X à partir du plan de cristal {420} d'une poudre de cuivre pur standard.
  2. Matériau de feuille d'alliage de cuivre selon la revendication 1, ayant en outre une orientation de cristal vérifiant l'expression (2) : I 220 / I 0 220 ≤ 3 , 0
    Figure imgb0016
    où I{220} est l'intensité de diffraction de rayons X à partir du plan de cristal {220} dans le plan de la feuille du matériau de feuille d'alliage de cuivre et I0{220} est l'intensité de diffraction de rayons X à partir du plan de cristal {220} d'une poudre de cuivre pur standard.
  3. Matériau de feuille d'alliage de cuivre selon la revendication 1 ou 2 ayant un diamètre moyen de grain de cristal de 10 µm - 60 µm.
  4. Procédé de fabrication d'une feuille d'alliage de cuivre selon l'une quelconque des revendications 1 à 3 comprenant :
    effectuer successivement les étapes d'un roulage à chaud à 950°C - 400°C, un roulage à froid avec un rapport de réduction de 85% ou plus, un traitement à chaud en solution à 700°C - 850°C, un roulage à froid intermédiaire avec un rapport de réduction de 0% - 50%, un vieillissement à 400°C - 500°C, et un roulage à froid de finition avec un rapport de réduction de 0% - 50%,
    et, dans l'étape de roulage à chaud dudit procédé, une première passe est effectuée dans une plage de température de 950°C - 700°C et un roulage est effectué dans une plage de température inférieure à 700°C à 400°C avec un rapport de réduction de 40% ou plus.
  5. Procédé de fabrication d'une feuille d'alliage de cuivre selon la revendication 4, dans lequel, dans l'étape de roulage à chaud, le roulage est effectué dans une plage de température de 950°C - 700°C avec un rapport de réduction de 60% ou plus, et le roulage est effectué dans une plage de température inférieure à 700°C à 400°C avec un rapport de réduction de 40% ou plus.
  6. Procédé de fabrication d'une feuille d'alliage de cuivre selon la revendication 4 ou 5, dans lequel la durée de chauffage de 100°C à 700°C dans l'étape de traitement à chaud en solution est de 20 secondes ou moins.
  7. Procédé de fabrication d'une feuille d'alliage de cuivre selon l'une quelconque des revendications 4 à 6, dans lequel, dans l'étape de traitement à chaud en solution, le traitement à chaud est effectué avec le temps de maintien et une température finale dans la plage de 700°C à 850°C, réglée de façon à ce que le diamètre de grain moyen des grains de recristallisation après le traitement à chaud en solution devienne compris entre 10 µm et 60 µm.
  8. Procédé de fabrication d'une feuille d'alliage de cuivre selon l'une quelconque des revendications 4 à 7, dans lequel lorsque le roulage à froid de finition est effectué, un recuit à basse température de 150°C - 550°C est effectué après le roulage à froid de finition.
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EP2508633A4 (fr) * 2009-12-02 2014-07-23 Furukawa Electric Co Ltd Feuille d'alliage de cuivre et son procédé de fabrication
JP4885332B2 (ja) * 2009-12-02 2012-02-29 古河電気工業株式会社 銅合金板材およびその製造方法

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US5463247A (en) * 1992-06-11 1995-10-31 Mitsubishi Shindoh Co., Ltd. Lead frame material formed of copper alloy for resin sealed type semiconductor devices
JP3739214B2 (ja) * 1998-03-26 2006-01-25 株式会社神戸製鋼所 電子部品用銅合金板
JP3520034B2 (ja) * 2000-07-25 2004-04-19 古河電気工業株式会社 電子電気機器部品用銅合金材
JP3520046B2 (ja) * 2000-12-15 2004-04-19 古河電気工業株式会社 高強度銅合金
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