JP2020097793A - Copper alloy sheet material, manufacturing method therefor, contraction processed article, member for electric and electronic component, electromagnetic wave-shielding material and heat release member - Google Patents

Abstract

To provide a copper alloy sheet material capable of stably providing excellent contraction processability without deteriorating basic characteristics of the copper alloy sheet material, a manufacturing method therefor, a contraction processed article, a member for electric and electronic component, an electromagnetic wave-shielding material, and a heat release member.SOLUTION: Regarding 3 kinds of test pieces having a prescribed composition, conductivity of 38% IACS or more, and cut in a rolling parallel direction, a direction of 45° to a rolling direction, and a rolling vertical direction respectively, an arithmetic mean value Aave. calculated by assigning a value obtained from a nominal stress-nominal train curve obtained by conducting a tensile test, and a value of Cube direction area percentage obtained by an electron back scattering diffraction (EBSD) method into a first formula to obtain values of each direction of parameters Ax (x:0°, 45°, 90°), A, A, and A, and assigning obtained values of each direction A, A, and Ainto a specified second formula is in a range of 4.0 to 13.0 GPa %.SELECTED DRAWING: Figure 1

Description

The present invention relates to a copper alloy plate material, a method for manufacturing the same, a drawn product, a member for electric/electronic parts, an electromagnetic wave shielding material, and a heat dissipation part.

Copper alloy plate material, for example, connectors for electric/electronic parts, lead frames, relays, switches, sockets, shield cases, shield cans, liquid crystal reinforcing plates, liquid crystal chassis, organic EL display reinforcing plates, and in-vehicle connectors Copper alloy plate materials used for shield cases, shield cans and the like are usually subjected to press working such as punching, bending, drawing, and overhanging.

In the case of using a conventional copper alloy plate material, mechanical and electrical characteristics had to be sacrificed in order to realize a difficult-to-machine shape that should not have been realized. The "difficult-to-machine shape" here means, for example, the shape formed when processed with a jig such as a punch whose radius of curvature of corners and edges is smaller than usual when manufacturing drawn products. To do. When manufacturing a drawn product having such a difficult-to-form shape, it cannot be said that the original mechanical and electrical characteristics of the copper alloy sheet are fully utilized. Further, when the mechanical and electrical characteristics of the copper alloy plate material are emphasized, it is necessary to give up processing to a target difficult-to-machine shape, and it is not possible to satisfy the demand for miniaturization of electronic devices. This is because, as a result, the radius of curvature of the jig (punch) has to be increased to some extent, and as a result, the mounting space of the drawn product forming the electronic component naturally increases. Furthermore, by optimizing the shape of the drawn product, there is room for improving heat dissipation at the expense of the drawability, but the problem is that it is currently difficult to draw the optimum shape. There is.

In particular, with the high performance of electric and electronic parts and automotive in-vehicle parts in recent years, the pressed products, which are one of the parts that compose them, have not only mechanical and electrical characteristics and heat dissipation In order to enable deformation into a shape, it has been strongly required to have excellent workability even under severe processing conditions. However, in the present process, the level of drawability required by the customer has not been achieved in the process of processing into a target difficult-to-machine shape.

For example, Patent Document 1 contains one or two kinds of Ni and Co in an amount of 0.8 to 4.0 mass%, contains 0.2 to 1.0 mass% of Si, and one or two kinds of Ni and Co. The mass ratio of Si is 3.0 to 7.0, the balance is Cu and unavoidable impurities, the tensile strength in the rolling parallel direction is 570 MPa or more, the proof stress is 500 MPa or more, the elongation is 5% or more, and the direction perpendicular to the rolling direction. Tensile strength is 550MPa or more, proof stress is 480MPa or more, elongation is 5% or more, conductivity is more than 35%IACS, and ratio R/t between bending radius R and plate thickness t is 0.5, and bending line is rolled. The bending limit width when performing 90 degree bending in the vertical direction is 70 mm or more, the bending processing limit width when performing contact bending in which the bending line is in the vertical direction is 20 mm or more, and Rankford value is 0.9. The above is the strength as a structural member, in particular, the strength that can withstand deformation and drop impact, the bending process that can withstand processing into complex shapes, the processability such as overhanging and drawing, and the high heat dissipation capability against heat from semiconductor elements, etc. There is described a copper alloy plate for a heat dissipation component.

Moreover, in patent document 2, 0.5-3.0 mass% Co, 0.1-2.0 mass% Ni, and 0.1-1.5 mass% Si are contained, and it is a mass ratio. (Ni+Co)/Si is 3 to 5, the balance consists of copper and unavoidable impurities, 0.2% proof stress in the rolling parallel direction is 630 MPa or more, the conductivity is 50% IACS or more, and the average crystal grain in the rolling parallel cross section. The diameter is 10 to 20 μm, and the integrated X-ray diffraction intensity I{200} from the {200} crystal plane on the surface and the X-ray diffraction integrated intensity I{220} from the {220} crystal plane, and {311} crystal X-ray diffraction integrated intensity I{311} from the plane satisfies the relationship of (I{220}+I{311})/I{200}≧5.0, which is 0.2% suitable for use in electronic materials. A copper alloy for electronic materials is described which has a proof stress and an electrical conductivity and can improve the dimensional stability when pressed into a connector shape or the like.

Further, in Patent Document 3, 1.0 to 3.0 mass% of Ni is contained, Si is contained at a concentration of 1/6 to 1/4 with respect to the mass% concentration of Ni, and the balance is Cu and unavoidable. The average deviation Ra of the surface is 0.02 to 0.2 μm, and the standard deviation of the absolute values of the peaks and valleys when the surface roughness average line is taken as a reference is 0.1 μm or less, the average value of the aspect ratio of the crystal grains in the alloy structure (minor axis of crystal grains/major axis of crystal grains) is 0.4 to 0.6, and with a backscattered electron diffraction image system All the GOS crystals when the orientations of all the pixels within the measurement area range are measured by the EBSD method using a scanning electron microscope and the boundaries where the orientation difference between adjacent pixels is 5° or more are regarded as grain boundaries. The average value in the grain is 1.2 to 1.5°, and the ratio (Lσ/L) of the total special grain boundary length Lσ of the special grain boundary to the total grain boundary length L of the crystal grain boundary is 60 to 70%. Cu-Ni having a spring limit value of 450 to 600 N/mm ² , good solder heat resistance peelability at 150° C. for 1000 hours, little change in fatigue resistance, and excellent deep drawability. -Si-based copper alloy (Corson alloy) plate is described.

The above-mentioned Patent Documents 1 to 3 are inventions relating to a copper alloy sheet containing at least one of Ni and Co and Si, and have good drawability, but copper alloys Among the steps constituting the method for manufacturing a plate material, particularly in the series of steps from the finish cold rolling step to the temper annealing step, control is not performed to suppress the generation of crystal grains that deteriorate the drawability. If the processing conditions are particularly severe when performing a deep drawing test, especially if the drawing is performed with a punch having a small radius of curvature R at the corner portion (for example, the radius of curvature R is 0.9 mm or less), a satisfactory level of drawing is obtained. There is a problem that workability cannot be stably obtained.

JP, 2017-89003, A Japanese Unexamined Patent Application Publication No. 2018-62705 International Publication No. 2012/160684

An object of the present invention is to provide a copper alloy sheet material capable of stably obtaining excellent drawability even under severe drawing conditions without impairing the basic characteristics (especially heat dissipation) of the conventional copper alloy sheet material. And a manufacturing method thereof, a drawn product, a member for electric/electronic parts, an electromagnetic wave shielding material, and a heat dissipation part.

但し、Ｓ_ｃ：Cube方位面積率（％）、σ_ｎは公称応力（ＧＰａ）、ε_ｎは公称歪（％）、そして、ＥＬは破断伸び（％）を表す。

（２）前記算術平均値Ａave.および前記パラメータＡｘの値を下記（３）式に代入して算出されるパラメータＢｘ（ｘ：０°、４５°、９０°）の前記各方向の値Ｂ_０°、Ｂ_４５°およびＢ_９０°が、いずれも１０％以下となる、上記（１）に記載の銅合金板材。

（３）エリクセン試験におけるエリクセン値（Er）の板厚（ｔ）に対する比（Er/t比）と、圧延平行方向に引っ張ったときの破断伸びＥＬ（％）とは、下記（４）式の不等式の関係を満たす、上記（１）または（２）に記載の銅合金板材。

（４）前記組成は、さらに、Ｓｎ、Ｍｇ、Ｍｎ、Ｃｒ、Ｚｒ、Ｔｉ、ＦｅおよびＺｎからなる群から選ばれる少なくとも１種の成分を、合計で０．２〜１．２質量％以下含有する上記（１）〜（３）のいずれか１項に記載の銅合金板材。
（５）上記（１）〜（４）のいずれか１項に記載の銅合金板材を絞り加工して得られた絞り加工品。
（６）上記（１）〜（４）のいずれか１項に記載の銅合金板材または上記（５）に記載の絞り加工品を用いて作製された電気・電子部品用部材。
（７）上記（１）〜（４）のいずれか１項に記載の銅合金板材または上記（５）に記載の絞り加工品を用いて作製された電磁波シールド材。
（８）上記（１）〜（４）のいずれか１項に記載の銅合金板材または請求項５に記載の絞り加工品を用いて作製された放熱部品。
（９）上記（１）〜（４）のいずれか１項に記載の銅合金板材の製造方法であって、銅合金素材に、鋳造[工程１]、均質化処理[工程２]、熱間圧延[工程３]、面削[工程４]、冷間圧延[工程５]、溶体化熱処理[工程６]、中間熱処理[工程７]、仕上げ冷間圧延[工程８]、矯正［工程９］、および調質焼鈍[工程１０]を順次施し、前記仕上げ冷間圧延[工程８]における圧延時の材料の最大温度Ｔ_Ｒを、７５℃以上１００℃以下に制御し、前記矯正［工程９］における材料の伸び率δを、０．１〜１．０％とし、そして、前記調質焼鈍［工程１０］の材料温度Ｔ_Ａ（℃）を、前記伸び率δとの関係で下記（５）式に示す不等式の関係を満たすように制御することを特徴とする銅合金板材の製造方法。
５５×δ＋４５０≧Ｔ_Ａ≧５５×δ＋３５０ ・・・（５） In order to achieve the above object, the gist of the present invention is as follows.
(1) It has a composition containing 1.0 to 5.0 mass% of Ni and Co in total, and 0.1 to 1.5 mass% of Si, with the balance being Cu and inevitable impurities. , A conductivity of 38% IACS or more, and obtained by performing a tensile test on three kinds of test pieces cut out in the rolling parallel direction, the direction of 45° to the rolling direction, and the vertical direction of the rolling. The value obtained from the nominal stress-nominal strain curve and the value of the Cube azimuth area ratio obtained by the electron backscatter diffraction (EBSD) method were substituted into the following formula (1) to obtain the parameter Ax(x:0° , 45°, 90°) in each direction, A _0° , A _45° and A _90° are obtained, and the obtained values in each direction A _0° , A _45° and A _90° are given in (2) below. A copper alloy sheet material, wherein an arithmetic mean value Aave. calculated by substituting in a formula is in a range of 4.0 to 13.0 GPa·%.

However, S _c : Cube azimuth area ratio (%), σ _n is a nominal stress (GPa), ε _n is a nominal strain (%), and EL is a breaking elongation (%).

(2) The value B _{0 of} each direction of the parameter Bx (x: 0°, 45°, 90°) calculated by substituting the values of the arithmetic mean value Aave. and the parameter Ax into the following equation (3). _° , B _45° and B _90° are all 10% or less, the copper alloy sheet material according to the above (1).

(3) The ratio (Er/t ratio) of the Erichsen value (Er) to the plate thickness (t) in the Erichsen test and the breaking elongation EL (%) when pulled in the rolling parallel direction are expressed by the following formula (4). The copper alloy sheet material according to (1) or (2), which satisfies the inequality relationship.

(4) The composition further contains at least one component selected from the group consisting of Sn, Mg, Mn, Cr, Zr, Ti, Fe and Zn in a total amount of 0.2 to 1.2% by mass or less. The copper alloy sheet material according to any one of (1) to (3) above.
(5) A drawn product obtained by drawing the copper alloy sheet material according to any one of (1) to (4).
(6) A member for electric/electronic parts produced by using the copper alloy sheet according to any one of (1) to (4) or the drawn product according to (5).
(7) An electromagnetic wave shield material produced using the copper alloy sheet material according to any one of (1) to (4) or the drawn product according to (5).
(8) A heat dissipation component manufactured using the copper alloy sheet material according to any one of (1) to (4) or the drawn product according to claim 5.
(9) The method for producing a copper alloy sheet according to any one of (1) to (4) above, wherein the copper alloy material is cast [step 1], homogenized [step 2], and hot. Rolling [step 3], chamfering [step 4], cold rolling [step 5], solution heat treatment [step 6], intermediate heat treatment [step 7], finish cold rolling [step 8], straightening [step 9] sequentially subjected and temper annealing [step 10], the maximum temperature T _R of the rolling time of the material in the finish cold rolling [step 8], and controls the 75 ° C. or higher 100 ° C. or less, the correction [step 9] The elongation rate δ of the material in 0.1 is set to 0.1 to 1.0%, and the material temperature T _A (° C.) of the temper annealing [step 10] is expressed by the following (5) in relation to the elongation rate δ. A method for manufacturing a copper alloy sheet material, which is controlled so as to satisfy the relationship of the inequality shown in the equation.
55×δ+450≧T _A ≧55×δ+350 (5)

The copper alloy sheet of the present invention contains 1.0 to 5.0 mass% of Ni and Co in total, and 0.1 to 1.5 mass% of Si, with the balance being Cu and unavoidable impurities. Tensile tests were carried out on three types of test pieces having a certain composition, an electric conductivity of 38% IACS or more, and cut in the rolling parallel direction, the direction of 45° to the rolling direction, and the vertical direction of the rolling. The value obtained from the nominal stress-nominal strain curve obtained by performing and the value of the Cube azimuth area ratio obtained by the electron backscatter diffraction (EBSD) method are substituted into the above equation (1) to obtain the parameter Ax. (X: 0°, 45°, 90°) values A _0° , A _45° and A _90° in each direction are obtained, and the obtained values A _0° , A _45° and A _90° in each direction are obtained. , The arithmetic mean value Aave. calculated by substituting in the above equation (2) is in the range of 4.0 to 13.0 GPa·%, and thus the basic characteristics (especially heat dissipation) of the conventional copper alloy sheet are Even if the drawing conditions are severe, it is possible to stably obtain excellent drawing workability without loss.

The method for producing a copper alloy sheet according to the present invention is performed on a copper alloy material by casting [step 1], homogenizing treatment [step 2], hot rolling [step 3], chamfering [step 4], cold rolling [step. 5], solution heat treatment [step 6], intermediate heat treatment [step 7], finish cold rolling [step 8], straightening [step 9], and temper annealing [step 10], and the finish cold rolling. the maximum temperature _{T R} of the rolling time of the material in [step 8], is controlled to 75 ° C. or higher 100 ° C. or less, the correction of elongation of the material δ in [step 9], and 0.1% to 1.0%, Then, by controlling the material temperature T _A (° C.) of the temper annealing [step 10] so as to satisfy the relationship of the inequality shown in the expression (5) in relation to the elongation rate δ, the above-mentioned copper is obtained. An alloy plate material can be manufactured.

FIG. 1 is a diagram showing, as an example, a nominal stress-nominal strain curve obtained by performing a tensile test on a test piece cut in a rolling parallel direction from a copper alloy sheet material according to an embodiment of the present invention. .. Fig. 2 shows the fracture ratio when the ratio (Er/t ratio) of the Erichsen value (Er) to the plate thickness (t) obtained by conducting the Erichsen test for various copper alloy sheet materials was pulled in the rolling parallel direction. It is a figure when it plots in relation with elongation EL (%). FIG. 3 conceptually shows a state in which the center portion of the test plate W is pushed in by a punch having a cylindrical tip and a small radius of curvature R at the corner in order to evaluate the drawability with a deep drawing tester. FIG. FIG. 4 is a diagram conceptually showing a state in which the central portion of the test plate W is pushed in by a punch having a hemispherical tip in order to obtain the Erichsen value by the Erichsen tester.

Hereinafter, preferred embodiments of the copper alloy sheet material of the present invention will be described in detail.
The copper alloy sheet according to the present invention contains 1.0 to 5.0 mass% of Ni and Co in total, and 0.1 to 1.5 mass% of Si, and the balance of Cu and unavoidable impurities. Tensile tests were carried out on three types of test pieces having a certain composition, an electric conductivity of 38% IACS or more, and cut in the rolling parallel direction, the direction of 45° to the rolling direction, and the vertical direction of the rolling. The value obtained from the nominal stress-nominal strain curve obtained by performing and the value of the Cube orientation area ratio obtained by the electron backscatter diffraction (EBSD) method were substituted into the following formula (1) to obtain the parameter Ax. (X: 0°, 45°, 90°) values A _0° , A _45° and A _90° in each direction are obtained, and the obtained values A _0° , A _45° and A _90° in each direction are obtained. The arithmetic mean value Aave. calculated by substituting in the following equation (2) is in the range of 4.0 to 13.0 GPa·%.

但し、Ｓ_ｃ：Cube方位面積率（％）、σ_ｎは公称応力（ＧＰａ）、ε_ｎは公称歪（％）、そして、ＥＬは破断伸び（％）を表す。

However, S _c : Cube azimuth area ratio (%), σ _n is a nominal stress (GPa), ε _n is a nominal strain (%), and EL is a breaking elongation (%).

(I) Composition of Copper Alloy Sheet Material First, the reason for limiting the composition of the copper alloy sheet material of the present invention will be described.
The copper alloy sheet material of the present invention contains one or more of Ni and Co in a total amount of 1.0 to 5.0 mass% and Si in an amount of 0.1 to 1.5 mass%.

<1.0 to 5.0% by mass in total of at least one of Ni and Co>
Ni (nickel) and Co (cobalt) are elements necessary for increasing the strength of the copper alloy sheet material, and it is necessary to contain 1.0 to 5.0 mass% of one or more of Ni and Co in total. Is. If the total content of one or more of Ni and Co is less than 1.0% by mass, the material strength decreases, and the strength required for an electronic component such as a shield case which is a drawn product manufactured by drawing is obtained. I can't. Further, when the total content of one or more of Ni and Co is more than 5.0% by mass, Ni and Co cannot be completely dissolved in the solution heat treatment [step 6] to be described later and a metal structure is formed as a second phase. It will remain in the (matrix) and will not contribute to the strength improvement that should occur in the subsequent intermediate heat treatment [Step 7] to be performed later, but it will also increase the cost of the ingot. is there. Therefore, the total content of at least one of Ni and Co is set to the range of 1.0 to 5.0 mass %.

<Si: 0.1 to 1.5 mass%>
Si (silicon) is an element necessary for forming a compound with Ni or Co and increasing the strength of the copper alloy sheet, and it is necessary to contain Si in an amount of 0.1 to 1.5 mass %. This is because if the Si content is less than 0.1% by mass, the amount of the compound formed with Ni or Co will decrease, and the material strength will decrease. Further, if the Si content is more than 1.5% by mass, the thermal conductivity of the copper alloy plate material is lowered and the heat dissipation is deteriorated. Therefore, the Si content is set to the range of 0.1 to 1.5 mass %.

The copper alloy sheet of the present invention contains one or more components of Ni and Co and Si as essential basic components, and further contains Sn, Mg, Mn, Cr, Zr, as an optional additional component. At least one component selected from the group consisting of Ti, Fe, and Zn can be contained in a total amount of 0.2 to 1.2% by mass or less. All of these components are components having the effect of improving the material strength, and in order to exert such effects, the total content of these components is preferably 0.2% by mass or more. If the total content of these components exceeds 1.2% by mass, the conductivity tends to decrease, so the total content of the above components is in the range of 0.2 to 1.2% by mass. It is preferable that the content be 0.5% by mass to 1.0% by mass.

<Sn: 0.1 to 0.45 mass%>
Sn (tin) is an element having a high effect of solid-solution strengthening a copper alloy, and it is preferable to add 0.1 mass% or more, but if the addition amount is larger than 0.45 mass %, the conductivity decreases. Tend to let. Therefore, the amount of Si added is preferably in the range of 0.1 to 0.45 mass %.

<Mg: 0.1 to 0.25 mass%>
Mg (magnesium) is an element having a high effect of solid-solution strengthening a copper alloy, and it is preferable to add 0.1 mass% or more, but if the addition amount exceeds 0.25 mass%, the conductivity decreases. Tend to let. Therefore, the amount of Mg added is preferably in the range of 0.1 to 0.25% by mass.

<Mn: 0.1 to 0.2 mass%>
Mn (manganese) is an element having an effect of solid solution strengthening a copper alloy and an effect of improving hot workability, and is preferably added in an amount of 0.1% by mass or more, but more than 0.2% by mass. A larger amount tends to lower the conductivity. Therefore, the amount of Mn added is preferably in the range of 0.1 to 0.2% by mass.

<Cr: 0.1 to 0.25 mass%>
Cr (chromium) has the effect of strengthening the material by forming a second phase compound containing chromium and silicon and suppressing coarsening of the crystal grain size in the solution heat treatment step by the compound. It is desirable to add 1 mass% or more, but if the addition amount is more than 0.25 mass %, coarse crystallized substances are formed during casting, and this tends to become a starting point of fracture during press working. Therefore, the Cr addition amount is preferably in the range of 0.1 to 0.25 mass %.

<Zr: 0.05 to 0.15 mass%>
Zr (zirconium) is an element that has a solid solution in the material and has an effect of suppressing the growth of recrystallized grains in the solution heat treatment by increasing the recrystallization temperature of the material, and is added in an amount of 0.05 mass% or more. However, if the addition amount is more than 0.15% by mass, coarse crystallized substances are generated during casting and are likely to be a starting point of fracture during press working. Therefore, the Zr addition amount is preferably in the range of 0.05 to 0.15 mass %.

<Ti: 0.02 to 0.1 mass%>
Ti (titanium) is an element having a solid solution in the material and having an effect of suppressing the growth of recrystallized grains in the solution heat treatment by increasing the recrystallization temperature of the material, and addition of 0.02 mass% or more However, if the addition amount is more than 0.1% by mass, the conductivity tends to decrease. Therefore, the Ti addition amount is preferably in the range of 0.02 to 0.1% by mass.

<Fe: 0.05 to 0.1 mass%>
Fe (iron) is an element having a high effect of solid-solution strengthening a copper alloy, and it is desirable to add 0.05 mass% or more, but if the addition amount is larger than 0.1 mass%, the conductivity decreases. Tend. Therefore, the amount of Fe added is preferably in the range of 0.05 to 0.1 mass %.

<Zn: 0.2 to 0.6 mass%>
Zn (zinc) is an element that has an effect of improving bending workability and improving adhesion and migration characteristics of Sn plating and solder plating. In order to exert such an effect, the Zn content is preferably 0.2% by mass or more. However, if the Zn content exceeds 0.6 mass %, sufficient heat dissipation may not be obtained due to a decrease in conductivity. Therefore, the amount of Zn added is preferably in the range of 0.2 to 0.6 mass %.

<Remainder: Cu and unavoidable impurities>
The balance other than the above-mentioned components is Cu (copper) and inevitable impurities. The unavoidable impurities referred to here mean impurities at a content level that can be unavoidably included in the manufacturing process. Since the unavoidable impurities may be a factor that decreases the conductivity depending on the content, it is preferable to suppress the content of the unavoidable impurities to some extent in consideration of the decrease in the conductivity. Examples of components that can be cited as the inevitable impurities include Bi, Se, As, Ag, and the like. The upper limit of the content of these components may be 0.03 mass% for each of the above components, and 0.10 mass% for the total amount of the above components.

(II) Electric Conductivity The copper alloy plate material of the present invention needs to have an electric conductivity of 38% IACS or more. The thermal conductivity can be calculated from the conductivity according to the Wiedemann-Franz law, and if the temperature is constant, it is proportional to the conductivity regardless of the type of metal. Are known. Therefore, the copper alloy sheet material of the present invention can have high thermal conductivity by setting the electrical conductivity to 38% IACS or more, and as a result, can have excellent thermal conductivity. The conductivity can be calculated by measuring the specific resistance by the four-terminal method in a constant temperature bath kept at 20° C. (±0.5° C.) with the distance between terminals being 100 mm, for example.

(III) Arithmetic mean value Aave. is in the range of 4.0 to 13.0 GPa·% In the copper alloy sheet of the present invention, arithmetic mean value Aave. is in the range of 4.0 to 13.0 GPa·%. It is necessary to be. The arithmetic average value Aave. is the rolling parallel direction, the direction of 45° with respect to the rolling direction (may be simply referred to as “45° direction”), and the vertical direction of rolling (may be simply referred to as “90° direction”). For each of the three types of test pieces cut out in each direction, the value obtained from the nominal stress-nominal strain curve obtained by performing the tensile test and the Cube orientation area obtained by the electron backscattering diffraction (EBSD) method By substituting the value of the ratio into the following equation (1), the values A _0° , A _45° and A _90° of the parameter Ax (x: 0°, 45°, 90°) in each direction were obtained and obtained. It is calculated by substituting the values A _0° , A _45° and A _90° in each direction into the following formula (2).

但し、Ｓ_ｃ：Cube方位面積率（％）、σ_ｎは公称応力（ＧＰａ）、ε_ｎは公称歪（％）、そして、ＥＬは破断伸び（％）を表す。

However, S _c : Cube azimuth area ratio (%), σ _n is a nominal stress (GPa), ε _n is a nominal strain (%), and EL is a breaking elongation (%).

The present inventors have obtained the knowledge that the parameter Aave. correlates well with the drawing workability with the material through experiments until reaching the present invention. It has been conventionally known that, among crystallographic orientations in copper and copper alloys, particularly the Cube orientation is integrated, which reduces the drawability of the material. However, quantitative evaluation of drawability using the integration degree of Cube orientation and drawability and quantitative integration of Cube orientation has not been performed. In the first place, precipitation-strengthened copper alloys, for example, Cu-Ni-Si-based and Cu-Co-Si-based alloys such as the component system of the present invention, copper and copper alloys conventionally used for drawing, such as pure copper and brass, Compared to pure metal such as nickel silver and solid solution strengthening type, influence of manufacturing process other than material components, such as control process such as size, existing density and existence ratio of second phase compound, on mechanical properties of material Is very large, and moreover, multiple material properties influence each other, so they change at the same time, for example, the abundance ratio of the second phase compound and the material strength change at the same time. The fact that the influence on the drawability cannot be extracted made it difficult to improve the drawability of the precipitation strengthened alloy and to evaluate the drawability.

Therefore, the present inventors have found that the drawability can be evaluated well by the precipitation strengthening type alloy by the formula (2), and further that the formula (2) and the drawability have a correlation, and the drawability is better than the conventional one. The inventors have invented a precipitation-strengthened alloy with improved properties.

In the equation (1), the degree of integration of the Cube orientation, which adversely affects the drawability, is expressed so as to have a negative correlation with the parameter Ax, and the larger the integral value of the nominal stress-nominal strain curve, the greater the drawability. It has a positive correlation, so it is expressed as a positive correlation. FIG. 1 is a diagram showing, as an example, a nominal stress-nominal strain curve obtained by performing a tensile test on a test piece cut in a rolling parallel direction from a copper alloy sheet material according to an embodiment of the present invention. ..

Furthermore, the arithmetic mean value Aave. calculated by substituting the three-direction parameters A _0° , A _45°, and A _90° obtained from the equation (1) into the equation (2) has a good correlation with the drawing workability. I found that. By obtaining this correlation, it becomes possible to evaluate the drawability by the formula (2).

Here, when the arithmetic average value Aave. is less than 4.0 GPa·%, a satisfactory level of drawability cannot be obtained under particularly severe deep drawing conditions, and when it is larger than 13.0 GPa·%. Then, the elongation of the material becomes large, and it becomes impossible to obtain sufficient strength which is a contradictory characteristic. Therefore, in the present invention, the arithmetic mean value Aave. is set in the range of 4.0 to 13.0 GPa·%.

The integral values obtained from the nominal stress-nominal strain curves used to calculate the parameter Ax are three types of JIS cut out in the rolling parallel direction, 45° direction and 90° direction, respectively.
9 pieces (n=9) of the test pieces of No. 13B of Z2241 were prepared and measured according to JIS Z2241, and when the case where the breaking elongation was the largest was the first, the breaking elongation was the fifth largest. The nominal stress-nominal strain curve when measured using the test piece was determined, and the integral value shown in the equation (1) is a trapezoid from the plot of the nominal stress-nominal strain curve obtained above. It can be calculated from the area obtained by approximation. The nominal stress may be measured, for example, every time the nominal strain is 0.001% or more and 0.300% or less.

The Cube azimuth area ratio (%) used to calculate the parameter Ax is continuously measured using an EBSD detector attached to a high resolution scanning analysis electron microscope (JEOL Ltd., trade name: JSM-7001FA). It can be calculated from the crystal orientation data measured by using analysis software (manufactured by TSL, trade name: OIM-Analysis). Here, “EBSD” is an abbreviation for Electron BackScatter Diffraction, which is a crystal orientation analysis technique that utilizes backscattered electron Kikuchi line diffraction that occurs when a sample is irradiated with an electron beam in a scanning electron microscope (SEM). Yes, and "OIM-Analysis" is an analysis software for data measured by EBSD.

Therefore, the values A _0° , A _45°, and A _90° in each direction of the parameter Ax are obtained by substituting the integral value calculated by the above-described method and the Cube azimuth area ratio (%) into the above formula (1). The values A _0° , A _45° and A _90° of the parameter Ax in each direction can be calculated, and the arithmetic mean value Aave. is obtained by using the calculated A _0° , A _45° and A _90° in equation (2). It can be calculated by substituting into

The drawability is measured by a deep drawing tester (for example, a thin plate forming tester manufactured by Erichsen Co., Ltd.) 10 after the edge of the test plate W is clamped between the die 12 and the wrinkle holding member 16 as shown in FIG. Then, the center portion of the test plate W was pushed by the punch 14 to form a cylindrical cup. The minimum punch corner radius R at which a cylindrical cup can be formed without cracking and the difference between the maximum valley depth and the maximum peak height of the undulation of the edge of the cylindrical cup were evaluated. In addition, the value of the punch moving distance (depth of the depression) until the occurrence of penetration cracking in the overhanging test (Erichsen test), that is, the Erichsen value Er was measured, and the thickness of the test plate W in addition to this Erichsen value Er (Mm), elongation at break (%) when pulled in the rolling direction, and the results were taken into consideration for comprehensive evaluation.

(IV) The values B _0° , B _45° and B ₉₀ in each direction of the parameter Bx (x: 0°, 45°, 90°) are all 10% or less, and the copper alloy sheet material of the present invention is The value of the parameter Bx (x: 0°, 45°, 90°) in each direction calculated by substituting the values of the arithmetic average value Aave. % Or less is preferable.

By controlling the values B _0° , B _45° and B _90° of the parameter Bx defined in the above formula (3) in each direction to be 10% or less, the undulation of the edge after drawing Can be stably reduced, the shape can be made uniform, and the drawability can be further improved. If the values B _0° , B _45° , and B _90° in any direction of the parameter Bx are larger than 10%, the yield in the production of drawn products tends to decrease, so the value of the parameter Bx in each direction B _0° , B _45° and B _90° are all preferably 10% or less.

The parameter Bx can be calculated by substituting the calculated parameter Ax and the arithmetic mean value Aave. into the equation (3) as described above.

(V) The ratio of the Erichsen value (Er) to the plate thickness (t) (Er/t ratio) and the breaking elongation EL (%) when stretched in the rolling parallel direction are expressed by the following inequality (4). The copper alloy sheet of the present invention has a ratio (Er/t ratio) of the Erichsen value (Er) to the sheet thickness (t) in the Erichsen test, and an elongation at break EL (%) when pulled in the rolling parallel direction. Preferably satisfies the inequality relation of the following equation (4).

The inventors further calculated that the ratio (Er/t ratio) of the Erichsen value (Er) to the plate thickness (t) obtained by the Erichsen test and the breaking elongation EL (%) when pulled in the rolling parallel direction were The effect on drawability was examined. Fig. 2 shows the ratio of the Erichsen value (Er) to the plate thickness (t) (Er/t ratio) on the vertical axis, and the elongation at break EL (%) when pulled in the rolling parallel direction on the horizontal axis. It is plotted about the Example and the comparative example shown. From the results shown in FIG. 2, it can be seen that all the examples are in the upper region and all the comparative examples are in the lower region with the linear function: Er/t=1.5EL as the boundary. Therefore, in the present invention, it is possible to determine whether the copper alloy plate material has excellent drawability by satisfying the above expression (4).

As shown in FIG. 4, the Erichsen value (Er value) is obtained by tightening the edge of the test plate W between the die 12 and the wrinkle holding member 16 by the Erichsen tester, and then measuring the central part of the test plate W by The value of the moving distance of the punch (the depth of the depression) until the penetration crack was generated by pushing in with the punch 14A having a hemispherical tip was taken as the measured value.

(VI) Method of Manufacturing Copper Alloy Sheet Material According to One Embodiment of the Present Invention The copper alloy sheet material described above can be realized by controlling the alloy composition and the manufacturing process in combination. Hereinafter, a suitable method for manufacturing the copper alloy sheet of the present invention will be described.

Such a copper alloy sheet according to one embodiment of the present invention is obtained by casting [step 1], homogenizing [step 2], and hot rolling on a copper alloy material having the same composition as the above-mentioned copper alloy sheet material. [Step 3], chamfering [Step 4], cold rolling [Step 5], solution heat treatment [Step 6], intermediate heat treatment [Step 7], finish cold rolling [Step 8], straightening [Step 9], It is manufactured by sequentially performing and temper annealing [step 10]. More specifically, by optimizing a series of steps from the finish cold rolling step to the temper annealing step, more specifically, the maximum temperature _{T R} of the rolling time of the material during rolling [step 8], and controls the 75 ° C. or higher 100 ° C. or less, correct the elongation of the material δ in [step 9], and 0.1% to 1.0% Then, by controlling the material temperature T _A (° C.) of the temper annealing [step 10] so as to satisfy the relationship of the inequality shown in the following expression (5) in relation to the elongation rate δ, the heat dissipation property is particularly improved. It is possible to manufacture a copper alloy sheet material having excellent drawability even under severe drawing conditions without impairing the above.

55×δ+450≧T _A ≧55×δ+350 (5)

(I) Casting process [Process 1]
In the casting step, the alloy components shown in Table 1 are melted in a high-frequency melting furnace in the atmosphere, and the alloy components are cast to produce an ingot of a predetermined shape (for example, thickness 30 mm, width 100 mm, length 150 mm).

(Ii) Homogenization treatment process [Process 2]
In the homogenization treatment step, the mixture was heated to a predetermined temperature (for example, 1000° C.) in an inert gas atmosphere for 1 hour and subjected to a homogenization heat treatment [step 2].

(Iii) Hot rolling process [Process 3]
The hot rolling process was performed immediately after the homogenizing heat treatment, and immediately after cooling to a predetermined plate thickness (for example, 10 mm).

(Iv) Chamfering process [Process 4]
In the chamfering step, the surface of the hot-rolled sheet was chamfered to a predetermined thickness (for example, about 1 mm to 2 mm) to remove the oxide layer.

(V) Cold rolling process [Process 5]
In the cold rolling process, cold rolling was performed to 1 to 0.25 mm.

(Vi) Solution heat treatment step [Step 6]
In the solution heat treatment step, the temperature is raised at a predetermined heating rate (for example, 900°C to 990°C over 5 seconds to 10 seconds), held for 1 second to 1 hour, and then set to 250°C/s to 500°C/s. Cooled at rate.

(Vii) Intermediate heat treatment step [Step 7]
In the intermediate heat treatment step, heat treatment was performed at a predetermined temperature (for example, 300° C. to 600° C.) for 10 seconds to 10 hours.

(Viii) Finishing cold rolling process [Process 8]
Finish cold rolling step, the processing of the plate thickness of the object, the improvement of material strength, comprising the steps of performing the main purpose of controlling the crystal orientation, the maximum temperature T _R of 75 ° C. or higher 100 ° C. rolling time of the material It is necessary to control the following. By maximum temperature T _R of the rolling when the material is above 75 ° C., crystal rotation is promoted by rolling, the area ratio of the negative impact Cube orientation grains drawability is likely to decrease. However, the maximum temperature T _R of the rolling time of the material becomes higher temperature than is 100 ° C., the rolling viscous processed into lubricating oil used is that decreased, it burns like rolling defects by a surface roughness of the plate material locally in If it becomes higher, it becomes a starting point of breakage and the possibility of deterioration of drawability becomes higher. Therefore, the maximum temperature _{T R} of the rolling time of the material shall be 75 ° C. or higher 100 ° C. or less.

(Ix) Straightening process [Process 9]
The straightening step is a step performed for the purpose of removing/uniformizing the residual stress of the material, and the elongation rate δ of the material at the time of straightening by the tension leveler is set in the range of 0.1 to 1.0%. is necessary. When the elongation δ is less than 0.1%, the effect of removing and uniformizing residual stress is small, and the shape uniformity after drawing is deteriorated. On the other hand, if the elongation δ is more than 1.0%, the processing strain due to the repeated bending of the tension leveler becomes large, and the corner radius of the punch tip, which does not cause cracks during drawing, cannot be made small, and the severe drawing is difficult. The drawability is reduced under the processing conditions. Therefore, the elongation rate δ of the material in the straightening step is set to the range of 0.1 to 1.0%.

(X) Tempering annealing process [Process 10]
The temper annealing step is a step for recovering the elongation of the material and further for reducing the anisotropy of mechanical properties including the elongation, and the material temperature T _A (° C.) of the temper annealing [step 10] ) Must be controlled so as to satisfy the relationship of the inequality shown in the equation (5) in relation to the elongation rate δ(%) of the material in the straightening step.

55×δ+450≧T _A ≧55×δ+350 (5)

By controlling the material temperature T _A in the temper annealing step according to the equation (5), the drawability is improved. By recovering the dislocations introduced in the series of steps up to the straightening step by the temper annealing step, the arithmetic mean value Aave. and the Erichsen value Er, which are the parameters of the material, become large. If the material temperature T _A in the temper annealing step is below the lower limit value in the equation (5), recovery of dislocations by rolling (that is, removal of processing strain) becomes insufficient. Further, when the material temperature T _A in the temper annealing step exceeds the upper limit value in the formula (5), the amount of precipitation of Ni or Co and Si compounds increases, and the material strength accordingly decreases. For this reason, the material temperature T _A (° C.) in the temper annealing [step 10] is set so as to satisfy the relationship of the inequality shown in the expression (5) in relation to the elongation rate δ(%) of the material in the straightening step. ..

(VII) Uses of Copper Alloy Plate Material The copper alloy material of the present invention is particularly suitable for use in drawing to produce drawn products, for example, members for electric/electronic parts, electromagnetic wave shielding materials and It can be used as a heat dissipation component. For example, connectors for electric/electronic parts, lead frames, relays, switches, sockets, shield cases, shield cans, liquid crystal reinforcing plates, liquid crystal chassis, organic EL display reinforcing plates, automotive in-vehicle connectors, shield cases, A shield can or the like can be manufactured.

Although the embodiments of the present invention have been described above, the present invention is not limited to the above embodiments, and includes various aspects within the concept of the present invention and the scope of the claims, and various modifications within the scope of the present invention. Can be modified to

Next, in order to further clarify the effects of the present invention, examples of the present invention and comparative examples will be described, but the present invention is not limited to these examples.

(Examples 1 to 15 and Comparative Examples 1 to 11)
A copper alloy material having the composition shown in Table 1 was melted in a high frequency melting furnace in the atmosphere and cast to obtain an ingot having a thickness of 30 mm, a width of 100 mm and a length of 150 mm. Next, immediately after the homogenizing heat treatment of heating and holding at 1000° C. for 1 hour in an inert gas atmosphere, hot rolling was performed to obtain a hot-rolled sheet having a thickness of 10 mm and then immediately cooled. Next, chamfering and cold rolling were sequentially performed to give a plate thickness of 0.25 to 1.0 mm. Then, the solution heat treatment is performed at 800 to 990° C. for 1 minute, immediately after cooling, the intermediate heat treatment is performed at 300° C. to 600° C. for 1 hour. Then, after applying 60% finish cold rolling 0.1% at maximum temperature T _R of the materials shown in Table 3, were corrected with elongation δ shown in Table 3, then, the material temperature T _A shown in Table 3 Was heat-annealed to obtain a copper alloy sheet having a plate thickness of 0.25 to 0.3 mm. In Comparative Example 11, since the maximum temperature T _R of the material during finish cold rolling was high, since the failure of the sheet surface caused by seizure can not calculate various parameters, could not even performance evaluation.

[Various measurement and evaluation methods]
Using the copper alloy sheet materials according to the above Examples and Comparative Examples, the following characteristic evaluations were performed. The evaluation conditions for each characteristic are as follows.

[1] Method for measuring composition of copper alloy plate material The alloy composition was measured by fluorescent X-ray analysis.

[2] Conductivity measurement method The conductivity was calculated by measuring the specific resistance by the four-terminal method in a constant temperature bath kept at 20° C. (±0.5° C.) with the distance between terminals being 100 mm, for example. ..

[3] Method of calculating integral value in equation (1) The integral value in equation (1) is three types of JIS Z2241 No. 13B, which are cut out in the rolling parallel direction, 45° direction and 90° direction. 9 test pieces (n=9) were prepared and measured according to JIS Z2241, and the test piece having the fifth largest breaking elongation was defined as the case where the largest breaking elongation was the first. It is to be obtained using the nominal stress-nominal strain curve when measured using the above, and the integral value shown in the equation (1) is obtained by the trapezoidal approximation from the plot of the nominal stress-nominal strain curve obtained above. Calculated from the area. The nominal stress was measured every 0.01% of the nominal strain.

[4] Calculation method of Cube azimuth area ratio The Cube azimuth area ratio is continuously measured using an EBSD detector attached to a high-resolution scanning analysis electron microscope (JEOL Ltd., trade name: JSM-7001FA). It was calculated from the obtained crystal orientation data using analysis software (manufactured by TSL, trade name: OIM-Analysis).

[5] Calculation Method of Parameter Bx The parameter Bx is a parameter Ax obtained by substituting the integral value calculated in [3] above and the Cube orientation area ratio calculated in [4] above into the equation (1). The values A _0° , A _45° and A _{90° in the direction} and the arithmetic mean value Aave. obtained by substituting these values A _0° , A _45° and A _90° into the equation (2) It can be calculated by substituting in (3).

[6] Method for measuring Erichsen value Er The Erichsen value Er is measured by an Erichsen tester after tightening the edge portion of the test plate W between the die 12 and the wrinkle holding member 16 as shown in FIG. The central portion of W was pushed in by the punch 14A, the value of the moving distance of the punch (the depth of the recess) until the occurrence of through cracks was measured, and it was taken as the measured value.

[7] Evaluation of heat dissipation Heat dissipation was evaluated by the conductivity measured in the above [2]. The evaluation criteria for heat dissipation are shown below. In this example, "1" and "2" in the heat dissipation evaluation criteria shown below are considered to be acceptable levels. Table 2 shows the evaluation results of heat dissipation.

<Heat dissipation evaluation criteria>
1 (excellent): When conductivity is 50% IACS or more 2 (Good): When conductivity is 30% IACS or more and less than 50% IACS 3 (Improper): When conductivity is less than 30% IACS

[8] Evaluation of drawing workability As for drawing workability, as shown in FIG. After tightening between the members 16, the central portion of the test plate W is pushed by the punch 14 having a columnar tip and a small radius of curvature R at the corners to form a cylindrical cup without cracking. It was comprehensively evaluated from the minimum value of the radius of curvature R of the corner portion at the tip of the punch and the maximum value of the difference between the maximum peak height and the maximum valley depth of the undulation of the cup edge after molding. The evaluation criteria of drawability are shown below. Table 2 shows the evaluation results of the drawability. In the above test, the clearance between the punch and the die was 2.3 mm, R-303P was used as the lubricating oil applied to the surface of the test plate W, and the ratio of the punch diameter to the blank diameter (punch diameter/blank diameter) was used. ) Was performed under the test conditions of 0.64.

(A) Evaluation criteria for the minimum value of the radius of curvature R at the corner of the punch tip ◎ (excellent): When the minimum value of the radius of curvature R is 0.5 mm or less ○ (Good): The minimum value of the radius of curvature R is 0 In the case of more than 0.5 mm and less than 1.0 mm x (Not possible): When the minimum value of the radius of curvature R is 1.0 mm or more

(B) Evaluation criteria for the maximum difference between the maximum peak height and the maximum valley depth of the undulation of the cup edge ◎ (excellent): When the maximum value of the difference is 0.5 mm or less ○ (Good): The maximum value of the difference Is more than 0.5 mm and less than 1.0 mm x (not possible): When the maximum value of the difference is 1.0 mm or more

<Evaluation of drawability>
1 (excellent): When both of the evaluations (a) and (b) are “⊚” 2 (Good): Both of the evaluations (a) and (b) are “◯” or more Case 3 (No): When at least one of the evaluations (a) and (b) is “x”.

From the results of Tables 1 to 4, the copper alloy sheet materials of Examples 1 to 15 all have an alloy composition within the appropriate range of the present invention, a conductivity of 38% IACS or more, and an arithmetic average value Aave. Since it is in the range of 0.0 to 13.0 GPa·%, it can be seen that both the heat dissipation property and the drawability are at or above the passing level. In particular, Examples 3, 6, 8 and 12 were particularly excellent in electrical conductivity because the alloy composition and manufacturing conditions were appropriate. In Examples 1, 7, and 12, the conditions from casting to temper annealing were appropriate, and the parameters A and B showed good values, so the minimum value of the radius of curvature of the corner portion of the punch tip where cracks did not occur. And the maximum value of the difference between the ridges and valleys of the undulation of the cup edge became smaller, the drawability was particularly excellent.

On the other hand, Comparative Examples 1, 2, 4, 5, and 8 all had a small amount of Ni+Co or Si, and the arithmetic average value Aave. was out of the appropriate range of the present invention, and thus the drawability was poor. In Comparative Example 6, the straightening was not performed by the tension leveler and the elongation was 0%, so that the anisotropy was high, and thus Bx was out of the range. In Comparative Examples 8 and 10, the rolling temperature in finish cold rolling was low and many Cube orientations remained, so the arithmetic average value Aave. In Comparative Example 5, the parameter B _90° was out of the range, and the maximum height difference after drawing was large. In each of Comparative Examples 3, 7, and 9, the component content was larger than the appropriate range of the present invention, and thus the conductivity was particularly low. Particularly, in Comparative Example 7, the elongation in straightening was larger than the specified value, and the Erichsen value/plate thickness value was also outside the specified value, so the drawability was also poor. In Comparative Example 11, the material temperature during finish rolling became high, seizure of the material and the rolling roll occurred, and defects such as large unevenness occurred on the surface of the material. Therefore, the characteristic evaluation was not performed, but the drawability was remarkably reduced. Was obvious.

10 Erichsen Testing Machine 12 Die 14, 14A Punch (Punch)
16 Wrinkle holding member W Test plate material R Punch corner radius of curvature

Claims (9)

1.0 to 5.0 mass% in total of one or more kinds of Ni and Co, and 0.1 to 1.5 mass% of Si, with the balance being Cu and inevitable impurities,
Conductivity is 38% IACS or more,
A value obtained from a nominal stress-nominal strain curve obtained by performing a tensile test on three types of test pieces cut out in the rolling parallel direction, the direction of 45° with respect to the rolling direction, and each direction of the rolling vertical direction. And the value of the Cube azimuth area ratio obtained by the electron backscattering diffraction (EBSD) method is substituted into the following equation (1) to obtain the values of the parameters Ax (x: 0°, 45°, 90°) in each direction. value a _{0 °,} determine the _{a 45 °} and _{a 90 °,} obtained each direction values a _{0 °,} the _{a 45 °} and _{a 90 °,} the arithmetic mean value calculated by substituting the following equation (2) Aave. is in the range of 4.0 to 13.0 GPa·%, a copper alloy sheet material.

However, S _c : Cube azimuth area ratio (%), σ _n is a nominal stress (GPa), ε _n is a nominal strain (%), and EL is a breaking elongation (%).

The values B _0° and B _{0 of} each direction of the parameter Bx (x: 0°, 45°, 90°) calculated by substituting the values of the arithmetic average value Aave. and the parameter Ax into the following equation (3). The copper alloy sheet material according to claim 1, wherein both _45° and B _90° are 10% or less.

The ratio (Er/t ratio) of the Erichsen value (Er) to the plate thickness (t) in the Erichsen test and the breaking elongation EL (%) when stretched in the rolling parallel direction are expressed by the following inequality relation (4). The copper alloy sheet material according to claim 1, which satisfies the above condition.

The composition further contains at least one component selected from the group consisting of Sn, Mg, Mn, Cr, Zr, Ti, Fe and Zn in a total amount of 0.2 to 1.2% by mass or less. The copper alloy plate material according to any one of 1 to 3. A drawn product obtained by drawing the copper alloy sheet according to any one of claims 1 to 4. A member for electric/electronic parts produced by using the copper alloy sheet according to any one of claims 1 to 4 or the drawn product according to claim 5. An electromagnetic wave shielding material produced by using the copper alloy sheet according to any one of claims 1 to 4 or the drawn product according to claim 5. A heat dissipation component produced using the copper alloy sheet according to any one of claims 1 to 4 or the drawn product according to claim 5. It is a manufacturing method of the copper alloy plate material according to any one of claims 1 to 4,
Casting [step 1], homogenizing treatment [step 2], hot rolling [step 3], chamfering [step 4], cold rolling [step 5], solution heat treatment [step 6] on copper alloy material, Intermediate heat treatment [step 7], finish cold rolling [step 8], straightening [step 9], and temper annealing [step 10] are sequentially performed,
Wherein the maximum temperature T _R of the rolling time of the material in the finish cold rolling [step 8], and controls the 75 ° C. or higher 100 ° C. or less,
The elongation rate δ of the material in the straightening [step 9] is set to 0.1 to 1.0%, and
_A material temperature T _A (° C.) in the temper annealing [step 10] is controlled so as to satisfy the inequality shown in the following equation (5) in relation to the elongation δ. Manufacturing method.
55×δ+450≧T _A ≧55×δ+350 (5)

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