JP2006299409A - High-strength/high-conductivity copper alloy having excellent workability, and copper alloy member using the same - Google Patents

Abstract

<P>PROBLEM TO BE SOLVED: To provide a new copper alloy material in which strength, bending workability, press blanking properties, stress relaxation resistance and the anisotropy thereof are simultaneously improved to high levels while maintaining its high conductivity level of ≥70%IACS. <P>SOLUTION: The copper alloy has a composition comprising, by mass, 0.1 to 0.3% Fe, 0.05 to 0.3% Ni, 0.04 to 0.2% P and 0.03 to 0.15% Sn, and in which the total content of elements other than Cu and the above elements is ≤0.1%, and the balance Cu, and has a structure where, regarding crystal grains in the cross-section parallel to the rolling direction and the sheet thickness direction, the average aspect ratio (major axis/minor axis) A is ≥10, and the ratio between the maximum value A<SB>max</SB>and the minimum value A<SB>min</SB>of the aspect ratio, A<SB>max</SB>/A<SB>min</SB>is 1.0 to 3.0. <P>COPYRIGHT: (C)2007,JPO&INPIT

Description

  The present invention is a copper alloy suitable for current-carrying members such as connector terminals for automobiles, bus bars, and terminals for electric / electronic parts, and particularly has a high level of balance between conductivity, strength, bending workability, and press punchability. It relates to a copper alloy.

  Conventionally, brass having excellent strength, press punchability, and cost has been used for narrow bus bars such as a junction box for automobiles (hereinafter referred to as “J / B”). However, as the J / B becomes smaller and more dense, the current-carrying part of the bus bar becomes thinner, and brass has various problems such as generation of Joule heat due to low conductivity (about 28% IACS). Occurred.

  In order to cope with such a problem, an alloy having a conductivity of about 45 to 70% IACS and a medium strength, such as Cu-1Ni-0.5Sn-0.05P (C19020 alloy), Cu-0.7Mg- Copper alloys such as 0.005P (C18605 alloy) and Cu-2.2Fe-0.13Zn-0.03P (C19400 alloy) have been developed and used. In addition, high-conductivity type high-strength copper alloys as disclosed in Patent Documents 1 to 4 have been proposed.

Japanese Patent Laid-Open No. 10-130755 JP-A-11-343527 JP 2000-54043 A JP 2000-239812 A

  However, in recent years, there has been a tendency for the number of circuits of electrical components to increase due to weight reduction and high performance of automobiles, and the existing copper alloys (C19020 alloy, C18605 alloy, C19400 alloy) cannot be used in terms of conductivity. ing.

In addition, for the purpose of reducing the cost, weight, and size of bus bars, the technology of eliminating relay terminals has become the mainstream. The relay terminal-less means that the relay terminal that has been used to connect the bus bar and the fuse is eliminated, and a new press-fitting female terminal function (tuning fork terminal) is provided on the bus bar side. In other words, this tuning fork terminal maintains the electrical connection by directly contacting the end face punched out by the bus bar side press with the fuse, so that the material used for the bus bar is the one after being punched out by the press. It is desired that the shape of the end face is stable and good. In this regard, the existing copper alloys and the copper alloys of Patent Documents 1 to 4 do not give sufficient consideration to press punchability (end face shape). Further, these are not always satisfactory in terms of the balance of conductivity, strength and bending workability.
Furthermore, it has been found that when used for tuning fork type J / B and terminals, it is necessary to have a stress relaxation resistance superior and anisotropy smaller than that of the conventional stress relaxation characteristics.

  In view of the current situation, the present invention is a new copper that has improved strength, bending workability, press punchability, stress relaxation resistance and anisotropy at the same time while having a high conductivity level of 70% IACS or higher. It is intended to provide alloy materials.

The purpose is mass%, Fe: 0.1-0.3%, Ni: 0.05-0.3%, P: 0.04-0.2%, Sn: 0.03-0.15. %, The total content of elements excluding Cu and the above elements: 0.1% or less, the composition consisting of the balance Cu, conductivity 70% IACS or more conductivity, tensile strength 400N / mm ² or more strength Achieved by a copper alloy having a bending workability that does not cause cracking when bending at 90 ° with a bending radius that is a half of the plate thickness, and a press punching property that provides a defect rate of 5% or less when press punching. Is done.

Here, as a typical composition, “in mass%, Fe: 0.1 to 0.3%, Ni: 0.05 to 0.3%, P: 0.04 to 0.2%, Sn: 0.00. 03 to 0.15%, the balance Cu and unavoidable impurities (however, the total of unavoidable impurities is suppressed to 0.1% or less) ".
As the tensile strength, a value obtained by conducting a tensile test based on JIS Z2241 using a JIS No. 5 tensile test piece whose longitudinal direction is parallel to the rolling direction can be adopted.
“Bending workability that does not cause cracking when bending at 90 ° with a bending radius of ½ of the plate thickness” is in accordance with JIS H3110 using a bending specimen whose longitudinal direction is perpendicular to the rolling direction. When a 90 ° bending test was performed and a cross section perpendicular to the bending axis of the bent portion was observed with an optical microscope, no cracks were observed.

The defect rate at the time of press punching is as shown in FIG. That is, FIG. 1 illustrates a cross-sectional photograph of the press punched portion. The defect rate is obtained by dividing the value obtained by dividing the size (width) of the defect corresponding to the fractured surface as indicated by A in FIG. In the punching test for obtaining this value, a value obtained by punching under the condition of a clearance of 3 to 10% (for example, 8%) can be adopted. However,
Clearance = (Gap between punch and die) / (Material thickness) x 100
It is.

Further, the copper alloy of the present invention is a hot rolled material having the above composition or a material heat-treated after cold rolling, cold rolling before finishing at a rolling rate of 50% or more, finishing at 400 to 525 ° C. × 5 to 20 h. Pre-heat treatment, finish cold rolling with a rolling rate of 30% or more, and having a metal structure obtained by finishing heat treatment at 250 to 750 ° C. × 5 sec to 10 h, conductivity of 70% IACS or more, tensile strength of 400 N / mm ² or more It can be understood as a copper alloy.
The metal structure is particularly hard before and after the pre-finish heat treatment in the process of “pre-finish cold rolling → pre-finish heat treatment → finish cold rolling → finish heat treatment” for the hot-rolled material or the material heat-treated after cold rolling. The reduction rate of the HV value is 20% or less, the area ratio of the recrystallized structure is 15% or less, and the average crystal grain size of the recrystallized structure is 20 μm or less in the metal structure after the heat treatment before finishing. Characterized as an organized tissue. The balance other than the recrystallized structure is a rolled structure.

Here, “finish cold rolling” is the final cold rolling that determines the sheet thickness of the material, and “finish heat treatment” is the final heat treatment performed after finish cold rolling. “Pre-finish cold rolling” is the last cold rolling performed before the finish cold rolling, and “pre-finish heat treatment” is a heat treatment performed between the pre-finish cold rolling and the finish cold rolling. “The decrease rate of the hardness HV value before and after the heat treatment before finishing is 20% or less” means that the hardness before the heat treatment before finishing is a (HV) and the hardness after the heat treatment before finishing is b (HV).
(Ab) / a × 100 ≦ 20
Means that

From the viewpoint of metal structure, the copper alloy of the present invention is a plate-like copper alloy manufactured through a rolling process, and the average aspect ratio A is 10 for crystal grains in a cross section parallel to the rolling direction and the plate thickness direction. As described above, the structure has a structure in which the ratio A _max / A _min of the maximum value A _max and the minimum value A _min of the aspect ratio is 1.0 to 3.0.

The aspect ratio of the crystal grains is the ratio of the major axis to the minor axis for the crystal grains appearing in the cross section. The major axis is measured on the microscope observation image as the length of the crystal grain in the rolling direction and the minor axis is the length of the longest part in the thickness direction of the crystal grain. As a measuring method, in an area excluding the surface layer portion from the surface to 1/8 depth in the sheet thickness direction (hereinafter referred to as “sheet thickness central area”), an observation area of 100 μm in the rolling direction × 30 μm in the sheet thickness direction is randomly selected. A part is selected, and the aspect ratio of each crystal grain is measured for each crystal grain excluding the crystal grains that partially protrude from the boundary of the observation area among the crystal grains existing in each observation area. The average aspect ratio A is determined by calculating the average value of the aspect ratios of all particles whose aspect ratios were measured in five observation regions. The ratio A _max / A _min between the maximum value A _max and the minimum value A _min of the aspect ratio is the aspect ratio A _{max of the} crystal grains having the largest aspect ratio among all the grains whose aspect ratios were measured in the five observation regions. It is determined by taking the ratio of the aspect ratio A _min of the crystal grains having the smallest aspect ratio.

  Furthermore, in this invention, the terminal or bus bar using the said copper alloy is provided.

According to the present invention, it has a high conductivity of 70% IACS or more and a high strength of 400 N / mm ² or more, a good bending workability and press punching property, and excellent stress relaxation resistance, and its anisotropy. A copper alloy with a small amount can be provided. Therefore, the present invention is extremely excellent as a current-carrying material for various electric / electronic parts such as automobile bus bars represented by J / B and terminals.

  According to the study by the inventors, the copper alloy that fulfills the object of the present invention is a Cu—Fe—Ni—Sn—P alloy containing an appropriate amount of metal elements (Fe, Ni) that form a P compound in a Cu matrix. Was found to be achievable. Such an aging precipitation type copper alloy is usually produced by a process of performing “cold rolling → heat treatment” once or twice or more. However, a structure state that simultaneously improves the conductivity, strength, bending workability, and press punchability cannot be obtained simply by going through the process of “cold rolling → heat treatment”. It requires some ingenuity.

The inventors have studied Cu—Fe—Ni—Sn—P based alloy materials by “hot rolling → (cold rolling → heat treatment; at least once if necessary) → cold rolling before finishing → aging”. When manufacturing by the process of pre-finish heat treatment → finish cold rolling → finish heat treatment that also serves as a treatment, it is possible to simultaneously give the above characteristics by appropriately controlling the structure state after the pre-finish heat treatment I found it. That is,
i) To suppress the decrease rate of the hardness HV value before and after the heat treatment before finishing to 20% or less,
ii) In the metal structure after heat treatment before finishing, the area ratio of the recrystallized structure is 15% or less, and the average crystal grain size of the recrystallized structure is 20 μm or less,
Was found to be extremely effective.

  The mechanism by which the above properties are balanced at a high level in copper alloys manufactured through such treatment is not yet elucidated, but it is clearly different from those manufactured under conditions that deviate from i) ii) above. Therefore, it is considered that some characteristic organization state is realized by the process i) ii) in the middle of the process.

The chemical composition of the alloy of the present invention will be described.
[Fe]
Fe forms an Fe—P-based compound with P, or forms an Ni—P and Fe—Ni—P-based compound, thereby contributing to improvement in conductivity, strength, and heat resistance. However, when the Fe content is less than 0.1% by mass, the effect is not sufficient. When the Fe content exceeds 0.3% by mass, the decrease in conductivity becomes large and the target value cannot be obtained. Therefore, the Fe content needs to be 0.1 to 0.3% by mass. 0.15-0.25 mass% is still more preferable.

[Ni]
Ni forms Fe, P and Fe—Ni—P-based compounds to contribute to the improvement of conductivity, strength and heat resistance, and also contributes to the improvement of strength by solid solution strengthening. However, if the Ni content is less than 0.05% by mass, the effect is not sufficient, and if it exceeds 0.3% by mass, the decrease in the conductivity becomes large and the target value cannot be obtained. Therefore, the Ni content needs to be 0.05 to 0.3% by mass. 0.10 to 0.20% by mass is more preferable.

[P]
P forms an Fe—P compound with Fe, or forms an Fe—Ni—P compound with Fe, Ni, and contributes to improvement in conductivity, strength, and heat resistance. However, if the P content is less than 0.04 mass%, the formation of the compound becomes insufficient, and a sufficient effect cannot be obtained. If it exceeds 0.2% by mass, not only will the decrease in conductivity increase, but problems in production such as the occurrence of casting defects and hot cracks will become apparent. Therefore, the P content needs to be 0.05 to 0.2% by mass. 0.06 to 0.12% by mass is more preferable.

[Sn]
Sn is dissolved in the Cu matrix and contributes to strength improvement. However, if the Sn content is less than 0.03% by mass, the effect is insufficient, and if it exceeds 0.15% by mass, the decrease in conductivity is large and the target characteristics cannot be obtained. For this reason, Sn content needs to be 0.03-0.15 mass%. 0.05-0.10 mass% is still more preferable.

[Other elements]
In the present invention, it is preferable to eliminate as much as possible the factors that reduce the conductivity and bending workability of the alloy. Therefore, the total content (including inevitable impurities) of elements other than Cu, Fe, Ni, Sn, and P is desirably suppressed to 0.1% by mass or less. Specifically, the contents of Zn, Ti, Al, B, As, Sb, Ag, Pb, Be, Zr, Si, Cr, Mn, and In were examined, and the total of these was reduced to 0.1% by mass or less. If not, unless the elements other than these are added, the total content of elements other than Cu, Fe, Ni, Sn, and P (including inevitable impurities) may be considered to be 0.1% by mass or less. Absent. The total content (including inevitable impurities) of elements other than Cu, Fe, Ni, Sn, and P is more preferably 0.05% by mass or less.

Next, the characteristics of the copper alloy of the present invention will be described.
〔conductivity〕
The electrical conductivity is preferably 70% IACS or more, more preferably 73% IACS or more, and even 75% IACS or more in order to cope with an increase in the amount of heat generated due to miniaturization and high density of electric / electronic parts (especially bus bars). More preferably.

〔Tensile strength〕
In order to maintain a stable contact pressure between the tuning fork terminal and the fuse due to the introduction of the tuning fork terminal accompanying the elimination of the relay terminal, the copper alloy used for the bus bar needs to have a certain strength or more. Specifically, 400 N / mm ² or more, and more preferably is desired to be at 450 N / mm ² or more.

[Bending workability]
Electrical / electronic parts such as terminals and bus bars are usually formed into final products by punching copper or copper alloy strips with a press and then bending them. Therefore, since a serious defect is produced as a product when a crack is generated by bending, the material is required to have good bending workability. Specifically, if cracking does not occur when bending 90 ° with a bending radius of 1/2 the plate thickness, it can be put to practical use. It is more preferable to have excellent bending workability that does not break at a bending radius of 0.

[Press punchability]
In order to have good press punchability, when the copper alloy is punched with a press, the above-mentioned defect rate of the fractured portion in the cross-sectional shape of the punched surface may be 5% or less, and 3% or less. Is more preferable. If the material has a defect rate exceeding 5%, for example, when used for a tuning fork terminal of a bus bar, the shape of the end surface that will be in contact with the fuse is not stable, so the electrical connection is reliable. It is not obtained and the performance of J / B etc. is adversely affected. That is, the flatness of the press punched surface is important. Further, if the material has a defect rate exceeding 5%, the amount of punching waste increases, the number of die maintenance increases, and the cost problems such as shortening the life of the die become obvious. This defect rate can be examined by punching with a general clearance of 3 to 10%, and can be particularly tested under the condition of a clearance of 8%.

[Aspect ratio of crystal grains]
In order to improve the punchability, it is extremely effective to control the average aspect ratio of crystal grains in a cross section parallel to the rolling direction and the plate thickness direction to 10 or more, preferably 15 or more. In order to reduce the anisotropy of the stress relaxation characteristics, the maximum and minimum ratio of the aspect ratio is 1.0 to 3.0, preferably 1.0 to 2.0, more preferably 1.0 to 1. .5 is extremely effective.

The copper alloy of this invention which has the above characteristics can manufacture a slab according to the melting method of a general copper alloy, and can manufacture it through the following processes.
(Hot rolling)
The slab can be extracted after being held at 800 to 950 ° C. for 1 to 10 hours, hot rolled at a rolling rate of, for example, 50 to 95%, and then rapidly cooled (for example, immersed in water). It is desirable to maintain the finishing temperature (the temperature immediately after the end of the final pass) at 500 ° C. or higher.

[Cold rolling and heat treatment in the middle]
Thereafter, it may be subjected to the following pre-finishing cold rolling, but if necessary to achieve a predetermined plate thickness, the process of “cold rolling → heat treatment” was performed once or twice or more as an intermediate step. It can be used for cold rolling before finishing. Also in this case, it is preferable to perform the cold rolling and the heat treatment in the middle with the same considerations as the cold rolling before finishing and the heat treatment before finishing, which will be described later.

[Cold rolling before finishing]
In the cold rolling before finishing, lattice defects are introduced into the copper alloy as starting points for precipitate formation. For that purpose, it is desirable to secure a rolling rate of 50% or more. If the rolling rate is smaller than that, the formation of precipitates is not sufficiently accelerated in the subsequent heat treatment before finishing, and as a result, it becomes difficult to finally obtain a desired conductivity. More preferably, the rolling rate is 60% or more. The upper limit of the rolling rate does not need to be specified in particular, and may be performed within a range that is allowable in terms of facilities, but usually good results are obtained within a range of 90% or less.

[Heat treatment before finishing]
In this step, aging precipitation is promoted, and a basic structure state for imparting the respective characteristics targeted by the present invention is formed.
As a result of intensive studies, the inventors have found that there is a strong correlation between the hardness and structure after heat treatment before finishing and the press punchability. That is, the rate of decrease in hardness before and after the heat treatment before finishing is less than 20% of the initial hardness, and the area ratio of the recrystallized structure is less than 15% of the entire metal structure in the material after the heat treatment before finishing. In addition, when the average crystal grain size in the recrystallized structure portion is 20 μm or less, excellent press punchability (breakage ratio of fracture portion) in the final product obtained by subjecting the material to finish cold rolling and finish heat treatment (5% or less) can be realized. More preferably, the rate of decrease in hardness before and after the heat treatment before finishing is 10% or less. The average crystal grain size in the recrystallized structure after the heat treatment before finishing is more preferably 10 μm. The area ratio of the recrystallized structure is more preferably 10% or less, and further preferably 7% or less, and further preferably 5% or less.

  Such a reduction rate of hardness and the state of the recrystallized structure can be controlled by the rolling rate of cold rolling before finishing, the temperature and time of heat treatment before finishing. Specifically, pre-finish heat treatment may be performed, for example, in a range of 400 to 525 ° C. × 5 to 20 h for a material that has been cold-rolled before finishing at a rolling rate of 50% or more. When the temperature is less than 400 ° C. or the time is less than 5 hours, it is difficult to achieve both the desired conductivity and the bending workability. On the other hand, when the temperature exceeds 525 ° C., the hardness is lowered, and the crystal grains of the recrystallized structure are coarsened and the area ratio of the recrystallized structure is easily increased. In this case, the press punchability is lowered as a result. Furthermore, when the heat treatment time exceeds 20 h, the crystal grains of the recrystallized structure are coarsened and the press punchability is liable to be reduced. The temperature of the heat treatment before finishing is more preferably in the range of 425 to 475 ° C., and the time is more preferably 6 to 10 hours.

[Finish cold rolling]
In finish cold rolling, in order to improve the strength by work hardening, it is preferable to secure a rolling rate of 30% or more, and more preferably 50% or more. However, an excessively high rolling rate is uneconomical. Usually, good results are obtained at a rolling rate of 80% or less.

[Finish heat treatment]
In finishing heat treatment, the main purpose is to remove strain and aim to restore ductility, that is, improve bending workability. Although it can be carried out in the range of 250 to 750 ° C. × 5 sec to 10 h, it is not preferable to employ conditions of a very high temperature and a long time because it is uneconomical. In general, good results are obtained in the range of 350 to 600 ° C. × 30 sec to 2 h.

  The copper alloy having the composition shown in Table 1 was melted using a high-frequency melting furnace and cast into a carbon mold to produce a 40 × 40 × 150 mm ingot. Casting was performed in an Ar atmosphere. Next, the slab cut out from the ingot was held at 800 to 950 ° C. for 30 minutes, and then hot-rolled at a rolling rate of 63%, immersed in water and cooled. After cooling, the surface oxide was removed, and then cold rolling before finishing was performed at a rolling rate of 66%, followed by heat treatment before finishing at 480 ° C. × 8 h. Further, finish cold rolling was performed at a rolling rate of 60%, and then finish heat treatment was performed as strain relief annealing at 400 ° C. × 1 h to obtain a specimen having a thickness of 0.64 mm. The manufacturing conditions are all appropriate conditions. Except for Comparative Example 12, the total content of Zn, Ti, Al, B, As, Sb, Ag, Pb, Be, Zr, Si, Cr, Mn, and In is suppressed to 0.1% by mass or less. Yes.

The obtained copper alloy was examined for tensile strength, electrical conductivity, bending workability, press punchability, average aspect ratio of crystal grains, maximum / minimum aspect ratio, and stress relaxation characteristics.
The tensile strength was obtained by conducting a tensile test parallel to the rolling direction based on JIS Z2241, using a JIS Z2201 No. 5 test piece.
The conductivity was measured based on JIS H0505.
The bending workability is 90 ° in which the bending radius R is ½ of the plate thickness using a test piece having a width of 10 mm and a length of 60 mm in which the longitudinal direction is perpendicular to the rolling direction in accordance with JIS H3110. Bending test was performed, and the cross section perpendicular to the bending axis of the bent part after processing was observed with a metal microscope to check for cracks, where no cracks were observed (good), cracks were observed It evaluated as x (defect).

  The press punchability test was performed in accordance with the shear test method for copper and copper alloy sheet strips of JCBA (Japan Copper and Brass Association). The clearance was set to 8% with respect to the test material, the cross-sectional shape of the punched hole was observed as shown in FIG. Note that an average value of N = 20 was used for the measurement of the defect rate.

For the copper alloy sheet after the finish heat treatment, the copper alloy sheet is cut so that a section parallel to the rolling direction and the sheet thickness direction is exposed, and then the section is polished and etched, and crystal grains are obtained by SEM (scanning electron microscope). And the aspect ratio of the crystal grains was measured. As described above, five observation regions are provided in the central region of the plate thickness as described above, and the average aspect ratio A and the ratio A _max / A _min between the maximum value A _max and the minimum value A _min of the aspect ratio are obtained by the method described above. It was.

The stress relaxation characteristics were examined as follows. A tuning fork terminal having a shape as shown in FIG. 2 was produced by press punching from the copper alloy sheet after the finish heat treatment. At that time, for each copper alloy plate material, a tuning fork terminal in which the longitudinal direction shown in FIG. 2A was parallel to the rolling direction and a tuning fork terminal in which the longitudinal direction was perpendicular to the rolling direction were required. The gap between each tuning fork terminal is subjected to a heating test at 150 ° C. × 500 h in the atmosphere with a copper alloy tab inserted, and the gap interval after removing the tab after the heating test is the original gap interval (initial interval). ), The stress relaxation rate was determined by determining how much it changed. FIG. 2B shows a state before the heating test and shows an outline of initial dimensions of the tuning fork terminal. The initial interval is 0.7 mm. FIG. 2C shows a state in which a tab is inserted for use in the heating test. The thickness of the inserted tab is 0.8 mm. FIG. 2D shows a state when the tab is removed after the heating test is completed. The stress relaxation rate R (%) is defined by the following formula.
Stress relaxation rate R (%) = (Z−X) / (Y−X) × 100
Here, X: gap interval before the heating test = 0.7 mm
Y: Insert tab thickness = 0.8 mm
Z: Gap interval after the heating test (mm)
2C and 2D, the insertion tab thickness and the gap interval Z after the heating test are exaggerated.

When the stress relaxation rate in a tuning fork terminal whose longitudinal direction is parallel to the rolling direction is R _L (%), and the stress relaxation rate in a tuning fork terminal whose longitudinal direction is perpendicular to the rolling direction is R _T (%), R R The anisotropy of stress relaxation characteristics was evaluated by calculating the ratio of _L / _RT . As J / B and terminals become smaller, the amount of heat generated from the product becomes a problem. However, if the stress relaxation characteristics are excellent, the contact pressure can be maintained with little opening of the tuning fork (between terminals). Therefore, it is possible to cope with downsizing with little temperature rise of the contact portion. If the anisotropy is small, especially when using a tuning fork in both the LD and TD directions, such as J / B, there is little difference in characteristics and temperature rise in one product, and the product is stable. Leads to sex. In consideration of these uses, in the stress relaxation property evaluation method performed here, both R _L and R _T are 25% or less, and R _L / R _T representing anisotropy is 0.75 to 1. A copper alloy sheet material in the range of .25 is determined to be acceptable as having good stress relaxation characteristics.
These results are shown in Table 2.

As can be seen from Table 2, in the copper alloy of the inventive example having an appropriate chemical composition, the average aspect ratio A is 10 or more, and the ratio A _max / A _min between the maximum value A _max and the minimum value A _min of the aspect ratio is 1. A plate material satisfying 0 to 3.0 can be manufactured, having an electrical conductivity of 70% IACS or more, a tensile strength of 400 N / mm ² or more, excellent bending workability, press punching ability, and stress relaxation resistance. Was also excellent. These are suitable as materials for electric and electronic parts represented by bus bars and terminals.

  On the other hand, Comparative Example No. 7 had too much Sn content, No. 8 had too much Fe content, and No. 9 had too much P content. In No. 9, cracks occurred during hot rolling. Since No. 10 had too little Ni content and No. 11 had too little Sn content, these were all inferior in strength (tensile strength). In particular, in No. 10, sufficient heat resistance was not obtained due to insufficient Ni amount, and the rate of decrease in hardness was increased by heat treatment before finishing, resulting in poor press punchability. No. 12 was inferior in conductivity because Zn content exceeded 0.1% by mass as an impurity element.

  A hot-rolled material having a composition corresponding to Invention Example 1 in Table 1 was produced in the same manner as in Example 1, and the hot-rolled material was cold-rolled before finishing under various conditions shown in Table 3. Pre-finish heat treatment, finish cold rolling, and finish heat treatment were performed to obtain a specimen having a thickness of 0.64 mm. However, with respect to Invention Examples 21 and 22, intermediate cold rolling and intermediate heat treatment were performed under the conditions shown in Table 3 before finish cold rolling. There was almost no decrease in hardness before and after the intermediate heat treatment in any sample, and the area ratio of the recrystallized structure after the intermediate heat treatment was 0% in any sample. In addition, No. 13 employs the same manufacturing conditions as in Example 1.

For each example, the hardness reduction rate before and after the heat treatment before finishing, the average crystal grain size in the recrystallized structure after the heat treatment before finishing, the area ratio of the recrystallized structure, the tensile strength of the obtained plate material, the electrical conductivity, the bending process Properties, press punchability, average aspect ratio, maximum / minimum aspect ratio, and stress relaxation characteristics were investigated.
The hardness before and after the heat treatment before finishing was measured by measuring the Vickers hardness in accordance with JIS Z2244, and the reduction rate with respect to the hardness before the heat treatment before finishing was determined.

The average crystal grain size in the recrystallized structure after the heat treatment before finishing is obtained by polishing and etching the surface (rolled surface) of the sample after the heat treatment before finishing and the cross section (L cross section) parallel to the rolling direction and the plate thickness direction, respectively. An optical microscope photograph was taken and measured from the structure photograph by the quadrature method defined in JIS H0501. At that time, the surface and the L cross section of the same sample were observed in 10 fields, and the average value was defined as the average crystal grain size.
Further, the area ratio of the recrystallized structure was measured by analyzing the above-described structure photograph with an image analyzer.
The bending workability, press punchability, tensile strength, electrical conductivity, average aspect ratio, aspect ratio maximum / minimum ratio, and stress relaxation characteristics were examined in the same manner as in Example 1.
The results are shown in Table 4.

As can be seen from Table 4, in the example of the invention manufactured under appropriate conditions, the average aspect ratio A is 10 or more, and the ratio A _max / A _min between the maximum value A _max and the minimum value A _min of the aspect ratio is 1.0. A plate material satisfying ~ 3.0 can be manufactured, and the strength, bending workability, press punchability, and stress relaxation characteristics are all improved to a high level in a balanced manner while having high conductivity of 70% IACS or higher. It was suitable as a material for electric / electronic parts including J / B and terminals.

  On the other hand, Comparative Example No. 23 was inferior in conductivity as a result of the rolling ratio of the cold rolling before finishing being too low. In No. 24, the temperature of the heat treatment before finishing was too low, and in No. 28, the time of the heat treatment before finishing was too short, so that both were inferior in bending workability and conductivity. In Nos. 25, 26 and 27, since the temperature of the heat treatment before finishing was too high, the hardness reduction rate before and after the heat treatment before finishing was large, and the area ratio of the recrystallized structure was increased. As a result, a crystal grain structure having a sufficiently large average aspect ratio could not be obtained, and as a result, press punchability and stress relaxation characteristics were inferior. In No. 29, since the pre-finish heat treatment time was too long, the crystal grains in the recrystallized structure after the pre-finish heat treatment became coarse. As a result, a crystal grain structure having a sufficiently large average aspect ratio could not be obtained, and as a result, press punchability and stress relaxation characteristics were inferior. In No. 30, the rolling ratio of finish cold rolling was too low, so the strength could not be improved sufficiently. Further, the ratio of the maximum value and the minimum value of the aspect ratio became a crystal grain structure exceeding 3.0, and the anisotropy of the stress relaxation rate was inferior. No. 31 had a finish heat treatment temperature too low, and No. 33 had a finish heat treatment time too short. In No. 32, the temperature of the finish heat treatment was too high, and in No. 34, the time for the finish heat treatment was too long.

The figure which showed an example of the cross-sectional photograph of a press punching part. The figure which showed typically the shape of the tuning fork terminal used for evaluation of a stress relaxation characteristic.

Claims (5)

In mass%, Fe: 0.1-0.3%, Ni: 0.05-0.3%, P: 0.04-0.2%, Sn: 0.03-0.15%, Cu and Total content of elements excluding the above elements: 0.1% or less, balance Cu composition, conductivity 70% IACS or more conductivity, tensile strength 400N / mm ² or more strength, plate thickness A copper alloy having bending workability that does not cause cracking when bending at 90 ° with a bending radius of ½, and press punching ability in which a defect rate when press punching is 5% or less. In mass%, Fe: 0.1-0.3%, Ni: 0.05-0.3%, P: 0.04-0.2%, Sn: 0.03-0.15%, Cu and Total content of elements excluding the above elements: 0.1% or less, cold rolling before finishing with a rolling rate of 50% or more for a hot-rolled material having a composition consisting of the balance Cu or a material heat-treated after cold rolling Conductivity 70% IACS having a structure obtained by applying pre-finish heat treatment at 400 to 525 ° C. for 5 to 20 hours, finish cold rolling at a rolling rate of 30% or more, and finish heat treatment at 250 to 750 ° C. for 5 seconds to 10 hours. As described above, a copper alloy having a tensile strength of 400 N / mm ² or more. In mass%, Fe: 0.1-0.3%, Ni: 0.05-0.3%, P: 0.04-0.2%, Sn: 0.03-0.15%, Cu and Total content of elements excluding the above-mentioned elements: 0.1% or less, hot-rolled material having a composition composed of the balance Cu or a material heat-treated after cold-rolling, “cold rolling before finishing → heat treatment before finishing → finishing An alloy that has undergone the processing and thermal history of “cold rolling → finish heat treatment”, and the decrease rate of the hardness HV value before and after the heat treatment before finishing is 20% or less, and the recrystallized structure in the metal structure after the heat treatment before finishing. A copper alloy having an electrical conductivity of 70% IACS or more and a tensile strength of 400 N / mm ² or more, having a structure that is processed so that the area ratio is 15% or less and the average crystal grain size of the recrystallized structure is 20 μm or less. . In mass%, Fe: 0.1-0.3%, Ni: 0.05-0.3%, P: 0.04-0.2%, Sn: 0.03-0.15%, Cu and Total content of elements excluding the above elements: 0.1% or less, balance Cu: average aspect ratio (major axis / minor axis) A for crystal grains in a cross section parallel to the rolling direction and the plate thickness direction Is a copper alloy having a structure in which the ratio A _max / A _min of the maximum value A _max and the minimum value A _min of the aspect ratio is 1.0 to 3.0.   A terminal or bus bar using the copper alloy according to claim 1.