WO2011125264A1 - Wrought copper alloy, copper alloy part, and process for producing wrought copper alloy - Google Patents

Abstract

Provided is a wrought copper alloy which has excellent cuttability and extensibility and is optimal for applications where high strength and/or high electrical conductivity is necessary while alleviating environmental burdens. The wrought copper alloy contains 1.5-7.0 mass% Ni, 0.3-2.3 mass% Si, and 0.02-1.0 mass% S and optionally further contains at least one element selected from a group consisting of Sn, Mn, Co, Zr, Ti, Fe, Cr, Al, P, and Zn in a total amount of 0.05-2.0 mass%, with the remainder comprising Cu and incidental impurities. The wrought copper alloy contains a sulfide dispersed therein which contributes to an improvement in cuttability, the sulfide having an average diameter of 0.1-10 µm and an areal proportion of 0.1-10%. The wrought copper alloy has a tensile strength of 500 MPa or more and an electrical conductivity of 25% IACS or more.

Description

Copper alloy wrought material, copper alloy parts, and method for producing copper alloy wrought material

The present invention relates to metal parts used in electronic equipment, precision machines, automobiles, etc., particularly copper alloy parts produced by cutting, and further relates to a copper alloy wrought material suitable for the copper alloy parts and a method for producing the same. is there.

There are cutting methods such as turning and drilling as methods for producing metal parts. Cutting is an effective processing method particularly for manufacturing parts having complicated shapes and parts requiring high dimensional accuracy. When cutting, machinability is often a problem. The machinability includes items such as cutting waste treatment, tool life, cutting resistance, and cutting surface roughness, and the material has been improved to improve them.

Copper alloys are used in many metal parts for reasons such as high strength, excellent conductivity and thermal conductivity, excellent corrosion resistance, and excellent color tone. Many cutting processes are also carried out. For example, there are water taps, valves, gears, ornaments, etc., brass (Cu-Zn), bronze (Cu-Sn), aluminum bronze (Cu-Al) In order to improve machinability, a white alloy (Cu—Zn—Ni series) is used. These are all applications that do not require high strength or high conductivity.

For applications that require high strength or high conductivity, such as pin materials for coaxial connectors, for example, free-cutting phosphor bronze (see Patent Document 1) in which lead is added to phosphor bronze or beryllium copper, free-cutting beryllium copper ( Patent Document 2) is used. These are cut by a precision machine tool such as an NC lathe and used for highly reliable parts such as electronic devices.

Thus, in order to improve the machinability of the copper alloy, lead is generally added. This is because lead does not dissolve in the copper alloy, so it is finely dispersed in the material, and the cutting waste is easily divided at that portion during cutting. However, the use of lead is being restricted because it is believed to affect the human body and the environment, and there is an increasing demand for materials that have improved machinability without containing lead. As an alternative material for a copper alloy containing lead, a copper alloy in which bismuth is added to brass or bronze (see Patent Documents 3 and 4) is known. In brass, the zinc concentration is increased to form a β-phase or γ-phase that is a copper-zinc compound, or silicon is added to form a κ-phase that is a copper-silicon compound, and these compounds are cut. It is also known that machinability is improved by acting as a starting point for scrap separation (Patent Documents 5 and 6). Furthermore, there is a method in which sulfur is added to bronze to form a sulfide to act as a starting point for cutting waste fragmentation (Patent Document 7). A method related to a zirconium-based and copper-titanium-based aging precipitation type alloy is known (Patent Document 8).

Japanese Patent Laid-Open No. 50-066423 JP 52-117244 A JP 2001-059123 A JP 2000-336442 A JP 2000-319737 A JP 2004-183056 A JP 2006-152373 A JP 2001-240923 A JP 2008-75172 A JP-A-6-212374 Japanese Unexamined Patent Publication No. 7-90520

However, the technique described in each patent document has the following problems.
In the techniques described in Patent Documents 1 and 2, as described above, lead is used as an additive element for improving the machinability, and there is a concern about the burden on the environment. In particular, in the technique described in Patent Document 2, there is no substitute for lead as an additive element for improving the machinability of free-cutting beryllium copper, and beryllium itself is listed as one of the elements affecting the environment. In addition, there is a growing demand for a beryllium copper substitute as well as a lead-added copper alloy substitute.

Also, in the techniques described in Patent Documents 3 and 4, machinability is improved when bismuth is added, but cracking is likely to occur during machining, and hot working is particularly difficult. That is, it is necessary to improve the hot workability. The compounds formed by the alloys described in Patent Documents 5 and 6 are unique to the brass system, and are practically difficult to apply to other alloy systems. Patent Document 7 is a technique related to a casting, and is suitable for direct cutting of a casting, but there is no disclosure as a technique for obtaining a stretched material (plastically processed material) such as a bar or a plate. The material obtained by the technique described in Patent Document 8 is generally low in strength, and is insufficient for applications that require high strength, such as a pin material of a coaxial connector, and other techniques need to be applied.

The ones disclosed in Patent Documents 1 to 8 above are not Corson alloys (Cu—Ni—Si based copper alloys) and are not helpful in the first place. Japanese Patent Laid-Open No. 2008-75172 (the above-mentioned Patent Document 9) discloses Cu— for an electronic material that does not contain other alloy elements as much as possible and has improved conductivity, strength, bendability and stress relaxation characteristics. It is disclosed to provide a Ni-Si based alloy. However, there is no disclosure regarding compatibility between extensibility and machinability, and there is no mention of adjusting the sulfur concentration. JP-A-6-212374 (Patent Document 10) and JP-A-7-90520 (Patent Document 11) disclose a Corson alloy in consideration of the extensibility. Is regulated to 20 ppm (0.002%) or less.

The present invention has been made in view of such problems, and is an excellent copper alloy wrought material that is excellent in machinability and stretchability, and is suitable for applications that require high strength or high conductivity while reducing environmental burden. It is a problem to provide. Furthermore, this invention makes it a subject to provide the manufacturing method of the copper alloy component obtained by cutting the said copper alloy wrought material, and the said wrought material.

As a result of intensive studies, the inventors of the present invention have developed extensibility (hot and cold workability) by controlling the size (average diameter) and area ratio of sulfides in an aging precipitation type copper alloy having a specific composition. Further, the present inventors have found that a copper alloy wrought material having excellent machinability and excellent strength and conductivity can be obtained. In addition, the present inventors have found a composition and a casting method for obtaining the above sulfide, and further found a composition, a structure, and a casting method that are excellent in hot workability and cold workability.
Further, as a result of intensive studies, the inventors of the present invention have formed sulfides in the matrix in an aging precipitation type copper alloy having a specific composition, and 40% or more of the sulfides have a matrix crystal having a cross section parallel to the extending direction. Dispersibility (hot / cold workability) and coating by dispersing sulfides having a cross-sectional aspect ratio of 1: 1 to 1: 100 in the grain in the matrix. It has been found that a copper alloy wrought material having excellent machinability and further excellent strength and conductivity can be obtained. In addition, the present inventors have found a composition and a production method for obtaining the above sulfide, and further found a composition, a structure, and a production method that are excellent in hot workability and cold workability.
The present invention has been made based on these findings.

That is, the present invention provides the following solutions.
(1) A copper alloy containing 1.5 to 7.0 mass% of Ni, 0.3 to 2.3 mass% of Si, 0.02 to 1.0 mass% of S, and the balance of Cu and inevitable impurities A stretched material in which sulfides are dispersed, the size (average diameter) of the sulfides is 0.1 to 10 μm, the area ratio of the sulfides is 0.1 to 10%, and A copper alloy wrought material having a tensile strength of 500 MPa or more and an electrical conductivity of 25% IACS or more.
(2) Further, it contains 0.05 to 2.0 mass% in total of at least one selected from the group consisting of Sn, Mn, Co, Zr, Ti, Fe, Cr, Al, P and Zn. The copper alloy wrought material according to (1).
(3) The sulfide is at least one selected from the group consisting of Cu—S, Mn—S, Zr—S, Ti—S, Fe—S, Al—S, Cr—S, and Zn—S. The copper alloy wrought material according to (1) or (2).
(4) A copper alloy part formed by cutting the copper alloy wrought material according to any one of (1) to (3).
(5) The copper alloy part according to (4), which is used for an electronic device part, a structural part, or an element part.
(6) A method for producing a wrought copper alloy material according to any one of (1) to (3), wherein a cooling rate during casting is 0.1 to 50 ° C./second. A method for producing a copper alloy wrought material.
(7) A copper alloy containing 1.5 to 7.0 mass% of Ni, 0.3 to 2.3 mass% of Si, 0.02 to 1.0 mass% of S, and the balance of Cu and inevitable impurities A stretched material having an area ratio of sulfide of 40% or more in the cross section parallel to the extending direction in the crystal of the matrix, and having an aspect ratio of 1: 1 to 1: 100 in the cross section parallel to the extending direction. A copper alloy wrought material in which sulfide is dispersed in a matrix, tensile strength is 500 MPa or more, and conductivity is 25% IACS or more.
(8) Further, it contains 0.05 to 2.0 mass% in total of at least one selected from the group consisting of Sn, Mn, Co, Zr, Ti, Fe, Cr, Al, P and Zn. The copper alloy wrought material according to (7).
(9) The sulfide is selected from any of sulfides of Cu—S, Mn—S, Zr—S, Ti—S, Fe—S, Al—S, Cr—S and Zn—S. The copper alloy wrought material according to (7) or (8), which is more than one type.
(10) A copper alloy part formed by cutting the copper alloy wrought material according to any one of (7) to (9).
(11) The copper alloy part according to (10), which is used for applications that require strength, electrical conductivity, thermal conductivity, and wear resistance, such as electronic equipment parts, structural parts, and element parts.
(12) A method for producing a copper alloy wrought material according to any one of (7) to (9), wherein Ni is 1.5 to 7.0 mass% and Si is 0.3 to 2. 3% by mass, containing 0.02 to 1.0% by mass of S, and the rest of the copper alloy composition consisting of Cu and inevitable impurities is subjected to one of the steps (a) and (b), More than 40% of the total area of sulfide dispersed in a matrix with a cross-section parallel to the extension direction after being reduced in area by 0% to 95% is present in the crystal of the matrix and has a cross-section parallel to the extension direction. A method for producing a copper alloy wrought material, comprising aging a sulfide having an aspect ratio of 1: 1 to 1: 100 dispersed in a matrix.
(A) Rapid cooling after hot working.
(B) After hot working, cold working and heat treatment at a temperature of 600 ° C. to 1000 ° C. are repeated at least once, and solution treatment is performed before the final cold working.
(13) Further, it contains 0.05 to 2.0 mass% in total of at least one selected from the group consisting of Sn, Mn, Co, Zr, Ti, Fe, Cr, Al, P and Zn. The method for producing a copper alloy wrought material according to (12).
Here, the fact that the area ratio of the sulfide having a cross section parallel to the extension direction is 40% or more in the crystal of the matrix means that the sulfide dispersed in the matrix is 40% or more in the crystal grain boundary. Further, the aspect ratio of the sulfide having a cross section parallel to the extending direction is dispersed in the range of 1: 1 to 1: 100 means that the aspect ratio of all the sulfides dispersed in the matrix is 1: 1 to 1: 100. Say that it is in the range. Here, the matrix refers to an individual region or a set thereof surrounded by a grain boundary in an alloy structure, and is typically surrounded by a grain boundary and is in the form of islands adjacent to each other in any form. To do.

The copper alloy wrought material of the present invention has excellent strength and electrical conductivity, and further has excellent machinability and extensibility without using environmentally hazardous substances such as lead and beryllium. For example, in order to prevent a decrease in the insertion / removal force required for the connector pin material, a decrease in the insertion / removal force can be suppressed by having a tensile strength as high as that of beryllium copper. In the present invention, the tensile strength is 500 MPa or more, and it is equivalent to beryllium copper. In addition, parts such as electronic devices that do not require tensile strength or conductivity are more excellent in conductivity than beryllium copper because they have a conductivity of 25% IACS or more. Moreover, the copper alloy wrought material of the present invention is suitable as a material for parts such as electronic equipment manufactured by cutting. The copper alloy part of the present invention can be manufactured with high precision by cutting, and has sufficient characteristics required for parts such as electronic equipment.

The above and other features and advantages of the present invention will become more apparent from the following description and accompanying drawings.

It is the figure which showed typically the side surface (a) and cross section (b) which looked at the copper alloy rod in parallel with the extending direction. A cross-sectional structure of a copper alloy rod viewed with an electron microscope (SEM) in parallel with the extending direction is schematically shown, and is an overall image of crystal grain boundaries and sulfides. FIG. 2 schematically shows a cross-sectional structure of a copper alloy bar viewed with an electron microscope (SEM) in parallel with the direction of extension, and is a view showing FIG. 2 excluding sulfides on grain boundaries. is there. It is a figure explaining the aspect-ratio of the sulfide which expanded and showed a part of FIG. FIG. 5 is a side view schematically showing one shape of a connector pin produced in Examples 1-3 and 2-3. FIG. 6 is a side view schematically showing another shape of the connector pin produced in Examples 1-3 and 2-3.

The preferred embodiment of the copper alloy wrought material of the present invention will be described in detail by dividing it into the first embodiment and the second embodiment. However, the description of the second embodiment may be omitted with respect to the points in common with the first embodiment. Both of these embodiments have the same or corresponding special technical features and form a single inventive concept. In this specification, “copper alloy” refers to a material that does not include the concept of shape, and “copper alloy material”, “copper alloy stretched material”, and the like refer to materials that include the concept of shape.

[First Embodiment]
<Ni, Si>
Nickel (Ni) and silicon (Si) in a preferred embodiment of the copper alloy wrought material of the present embodiment are formed by depositing Ni—Si precipitates in the metal cloth (matrix) by controlling the content ratio of Ni and Si. Ni ₂ Si) is formed for precipitation strengthening and added to improve the strength and conductivity of the copper alloy wrought material. This Ni—Si precipitate (Ni ₂ Si: precipitate for strengthening precipitation) does not contribute much to the improvement of machinability.

In a preferred embodiment of the copper alloy wrought material of the present embodiment, sulfide that contributes to improvement of machinability is formed in the matrix by adding sulfur (S). The sulfide acts as a starting point for cutting waste when cutting is performed, so that the cutting waste is easily finely divided and machinability is improved. In addition, by controlling the cooling rate at the time of casting, the size (average diameter) and area ratio of sulfides are controlled to improve cutting waste separation, and further, hot and cold workability is not impaired, Extending processes such as extrusion, rolling, and drawing are possible.

The copper alloy in the present embodiment is hot or cold worked in a state where nickel (Ni) and silicon (Si) are in a solid solution or a Ni—Si precipitate is formed. However, in general, the stretch workability is poor, and cracking, breakage, etc. are likely to occur during processing. When sulfides are formed in this copper alloy, the stretch workability is further deteriorated and the processing becomes difficult. Since the size (average diameter) and area ratio of sulfides affect the stretchability, in this embodiment, the size (average diameter) and area ratio of sulfides are defined. As a result, in the Cu—Ni—Si system, it is possible to simultaneously improve the stretchability and the machinability that are difficult to achieve at the same time.

The content of Ni is 1.5 to 7.0 mass% (mass%), and preferably 1.7 to 6.5 mass%. If the amount of Ni is too small, the amount of precipitation hardening due to Ni—Si precipitates is small and the strength is insufficient. If the amount of Ni is too large, not only does the amount of Ni-Si precipitates contributing to strength improvement increase, but also a large amount of Ni-Si precipitates are formed during melt casting, resulting in hot workability and cold work. This is not preferable because it deteriorates the property (ie, extensibility).

As for the Si content, in the formation of Ni—Si precipitates (Ni ₂ Si), an amount of about 1/5 to 1/3 of the Ni content is required when calculated by mass%. Therefore, in the present embodiment, the Si content is 0.3 to 2.3% by mass, and preferably 0.34 to 2.2% by mass.

<S>
In the copper alloy wrought material of this embodiment, it is necessary that the sulfide size (average diameter) is 0.1 to 10 μm and the sulfide area ratio is 0.1 to 10%. For this purpose, the S content is 0.02 to 1.0 mass%, preferably 0.03 to 0.8 mass%. If the amount is too small, the area ratio of the sulfide is small, and sufficient cutting waste separation property cannot be obtained. When there is too much content of S, hot workability and cold workability (namely, extensibility) will deteriorate.
Conventionally, it is known that the amount of S is regulated to a very small amount in a Corson alloy (Patent Documents 10 and 11). In the present embodiment, the sulfide has a predetermined aspect ratio in the extending direction by increasing the amount of the other additive elements in a specific range, preferably by performing the processing under specific conditions. A copper alloy wrought material that achieves both machinability and extensibility.

Furthermore, the copper alloy wrought material of this embodiment includes tin (Sn), manganese (Mn), cobalt (Co), zirconium (Zr), titanium (Ti), iron (Fe), chromium (Cr), aluminum You may contain 1 type, or 2 or more types of (Al), phosphorus (P), and zinc (Zn). These elements improve the strength of the Cu—Ni—Si alloy by forming solid solutions or precipitates, or improve the machinability by forming sulfides. In the case of inclusion, 0.05 to 2.0 mass% in total of one or more selected from Sn, Mn, Co, Zr, Ti, Fe, Cr, Al, P, Zn is contained. Is preferred. When the content is less than 0.05 mass%, the effects of improving the strength and improving the machinability are not different from the case of not containing these elements. Moreover, when there is more content than 2.0 mass%, since not only the effect of intensity | strength and a machinability improvement is saturated, but electrical conductivity falls, it is not a policy. Sulfide components include Cu-S, Mn-S, Zr-S, Ti-S, Fe-S, Al-S, Cr-S, and Zn-S, and Cu-S sulfides are particularly effective. It is. There are also sulfides of unavoidable impurities and S.

<Rules related to sulfides>
Examples of the sulfide component include Cu—S, Mn—S, Zr—S, Ti—S, Fe—S, Al—S, Cr—S, and Zn—S. The sulfide is preferably at least one selected from the group consisting of Cu—S, Mn—S, Zr—S, Ti—S, Fe—S, Al—S, Cr—S, and Zn—S. In particular, Cu-S is effective. There are also sulfides of unavoidable impurities and S. Here, “Cu—S” means a generic name of sulfides composed of Cu and S such as Cu ₂ S and CuS, and the same applies to “Mn—S” and the like.

Next, the specifications and characteristics of the size (average diameter) and area ratio of sulfides, which are compounds that contribute to the improvement of machinability, will be described. Sulfide has the effect | action which cuts up the cutting waste generated at the time of cutting finely, and, thereby, machinability improves. However, if the sulfide size (average diameter) is smaller than 0.1 μm, a great effect cannot be obtained. Further, even if there is a sulfide having a size (average diameter) of 0.1 μm or more, the cutting waste is not finely divided if the total area ratio is small. Specifically, if the sulfide having a size (average diameter) of 0.1 μm or more is not distributed with a density of 0.1 to 10% in terms of area ratio, the cutting waste is not sufficiently divided. Since sulfides are soft, they may be elongated in the longitudinal direction depending on the degree of hot working or cold working, but the size (average diameter) and area ratio of sulfides are perpendicular to the longitudinal direction of the wrought material. What is necessary is just to satisfy the above in a simple cross section (transverse cross section). The size of the sulfide (average diameter) is a value obtained by observing the cross section with an electron microscope, converting 100 or more sulfide particles into a circle, and averaging the diameters. The area ratio of sulfides is the number of sulfides seen in one field of view observed with an electron microscope. Each sulfide is converted into a circle to obtain its diameter, averaged, and the area is obtained from the average diameter. Multiply the number of sulfides to obtain the total area per field of sulfide and divide by the total area of one field of view.

On the other hand, sulfide deteriorates hot and cold workability of the material. Sulfides are easily formed at the grain boundaries and reduce the grain boundary strength. Therefore, if the sulfide size (average diameter) is too large or the area ratio is too large, hot working or cold working is applied. Occasionally, cracking occurs, making it unusable as a wrought material. Therefore, the size (average diameter) of the sulfide needs to be 10 μm or less and the area ratio of the sulfide needs to be 10% or less.

The size (average diameter) of this sulfide varies depending on the cooling rate during casting. When the cooling rate is slow, the sulfide becomes large, and conversely when it is fast, it becomes small. A preferable cooling rate is 0.1 to 50 ° C./second, more preferably 0.3 to 40 ° C./second.

<Mechanical properties and manufacturing conditions>
Next, the mechanical properties of the copper alloy wrought material in the preferred embodiment of the first embodiment will be described.
The copper alloy wrought material in this embodiment is intended to replace lead-containing phosphor bronze and beryllium copper, that is, a copper alloy containing environmentally hazardous substances, and is equivalent to the wrought material of these alloys. Requires strength. Therefore, the strength and conductivity that do not cause a problem in practical use are required to be a tensile strength of 500 MPa or more and an electrical conductivity of 25% IACS or more by IACS (International Annealed Copper Standard). The copper alloy in this embodiment is an aging precipitation type, and the strength and conductivity are improved by forming Ni ₂ Si as described above. For this purpose, Ni is 1.5 to 7.0 mass%, Si It is necessary to contain 0.3 to 2.3 mass%. The temperature during the solution treatment in the production process is preferably in the range of 750 to 1000 ° C., and the temperature during the aging treatment is preferably in the range of 350 to 600 ° C.

In this embodiment, the method for producing a copper alloy wrought material is not particularly limited except that the size of the sulfide (average diameter) is controlled within the above range of the cooling rate during casting. For example, the area of the cross section of the ingot (cake or billet) may be larger than the area of the cross section of the wrought material. Since the copper alloy wrought material of the present embodiment is a wrought material of an aging precipitation type copper alloy, an aging heat treatment step is indispensable at least after the melt casting step of the copper alloy raw material, a hot working step, an annealing step. The solution treatment step is performed as necessary except for the step for obtaining the copper alloy wrought material. For example, regarding the hot working process, the copper alloy wrought material of this embodiment can be manufactured by any of manufacturing methods such as hot extrusion of billets, hot forging of ingots, or continuous casting. Moreover, there is no restriction | limiting in particular in the shape of a product, It is preferable to set it as the shape which is easy to obtain the copper alloy component which is a last form by the cutting process which is a post process. That is, it can be manufactured as a copper alloy wrought material having a predetermined shape such as a wire, a bar, a strip, a plate, or a tube depending on the use of the copper alloy component. For example, when the copper alloy part in the final form is a screw or a rivet, the shape of the copper alloy wrought material is preferably a round bar shape.

Copper alloy parts include male connector and male pins for coaxial connectors that currently use lead-containing phosphor bronze and beryllium copper, as well as probe barrels and plunger materials used in IC sockets and battery terminal connectors, and audio cable components. Strength, electrical conduction, such as electronic parts such as connector terminals, structural parts such as antenna hinges, fasteners, bearings, guide rails, resistance welders, watches, and parts such as gears, bearings, and eject pins of molds Parts that require heat resistance, heat conductivity, and wear resistance, and are manufactured in a complicated shape mainly by cutting. The “copper alloy part” in the present embodiment may include a copper alloy part manufactured by cutting.

[Second Embodiment]
<Ni, Si>
Also in the copper alloy wrought material of this embodiment, the content ratio of Ni and Si is controlled. The gist is the same as in the first embodiment.

In a preferred embodiment of the copper alloy wrought material of the present embodiment, sulfide that contributes to improvement of machinability is formed in the matrix by adding sulfur (S). The sulfide acts as a starting point for cutting waste when cutting is performed, so that the cutting waste is easily finely divided and the machinability is improved, which is common to the first embodiment. Sulfide is formed at the time of casting, but when it is formed, it is present in a large amount at the grain boundary and deteriorates hot workability and cold workability (that is, stretchability). Therefore, the sulfide formed in the ingot (cake or billet) is present in the matrix crystal with an area ratio of sulfide of 40% or more in the cross-section parallel to the extension direction by extension processing and heat treatment. By dispersing a sulfide having an aspect ratio of 1: 1 to 1: 100, preferably an aspect ratio of 1: 1 to 1:50, as viewed from the extending direction of a cross section parallel to the extending direction, in a matrix, By improving the cutting property of cutting waste and not impairing the workability in hot and cold conditions, it becomes possible to perform extension processing such as extrusion, rolling and drawing. The copper alloy of the present embodiment is hot or cold worked in a state where nickel (Ni) and silicon (Si) are in solid solution or Ni—Si precipitates are formed. In general, the stretchability is poor, and cracking, breakage, etc. are likely to occur during processing. When sulfides are formed in this copper alloy, the stretch workability is further deteriorated and the processing becomes difficult. The position at which sulfide is present has a great influence on the stretch workability, and the presence of a large amount of sulfide in the crystal improves the stretchability. In this embodiment, the area ratio existing in the crystal grains of sulfide is defined.

The content of Ni is 1.5 to 7.0 mass% (mass%), and preferably 1.7 to 6.5 mass%. If the amount of Ni is too small, the amount of precipitation hardening due to Ni—Si precipitates is small and the strength is insufficient. If the amount of Ni is too large, not only does the amount of Ni-Si precipitates contributing to strength improvement increase, but also a large amount of Ni-Si precipitates are formed during melt casting, resulting in hot workability and cold work. This is not preferable because it deteriorates the property (ie, extensibility).

As for the Si content, in the formation of Ni—Si precipitates (Ni ₂ Si), an amount of about 1/5 to 1/3 of the Ni content is required when calculated by mass%. Therefore, in the present embodiment, the Si content is 0.3 to 2.3% by mass, and preferably 0.34 to 2.2% by mass.

<S>
In the copper alloy wrought material of this embodiment, 40% or more of the area ratio of the formed sulfide exists in the crystal of the cross-sectional matrix parallel to the extending direction, and the sulfide having a cross section parallel to the extending direction. The aspect ratio must be the above ratio. In order to achieve this, the S content is 0.02 to 1.0 mass%, preferably 0.03 to 0.8 mass%. If the amount is too small, sufficient cutting waste separation property cannot be obtained. When there is too much content of S, hot workability and cold workability (namely, extensibility) will deteriorate. Preferably, 50% or more of the area ratio of the formed and dispersed sulfide is present in the matrix crystals. Also in this embodiment, it is the same as that of 1st Embodiment by the point which contains S by the said positive addition amount exceeding the conventional general regulation amount.

<Other additive elements>
The copper alloy wrought material of this embodiment includes tin (Sn), manganese (Mn), cobalt (Co), zirconium (Zr), titanium (Ti), iron (Fe), chromium (Cr), aluminum (Al ), Phosphorus (P), or zinc (Zn) may be contained. The action and the range of the preferred content are the same as in the first embodiment.

<Rules related to sulfides>
Next, the ratio of the sulfide present in the matrix in the cross section parallel to the extending direction of the sulfide, which is a compound contributing to the improvement of machinability, the definition of the aspect ratio of the sulfide, and the characteristics will be described. Sulfide has the effect | action which cuts up the cutting waste generated at the time of cutting finely, and, thereby, machinability improves. However, the position where sulfide is present greatly affects the stretchability (hot workability, cold workability). The ratio existing in the crystal grains of the sulfide matrix is to observe the cross section parallel to the stretching direction with an electron microscope, count the number of all sulfides observed in one field of view, Calculate the diameter in terms of a circle, average, calculate the area from the average diameter and multiply by the number of sulfides to determine the total area of all sulfides seen in one field of view, then within the crystal grains and the crystal grains Count the number of sulfides only across the boundary, calculate the diameter of each sulfide by converting it to a circle, average it, find the area from the average diameter, multiply by the number of sulfides, and This is a value obtained by obtaining the total area of sulfides straddling the crystal grain boundary and dividing by the total area of all sulfides seen in one field of view. This ratio should be 40% or more of the sulfide straddling the crystal grain and the crystal grain boundary. If it is 40% or less, the extensibility deteriorates. At this time, the area ratio of the sulfide is in the range of 0.1% to 20%, preferably 0.1 to 10%. The area ratio of sulfide is a value obtained by dividing the total area of sulfide seen in one field of view by the total area of one field of view.

Since sulfide is soft, it is elongated in the longitudinal direction according to the degree of hot working or cold working, and is divided and dispersed in the matrix. The aspect ratio of the dispersed sulfide, the cross section was observed with an electron microscope, if the vertical length t ₁ and 1 in the wrought direction, sulfides was stretched parallel to the wrought direction length and the ratio of _{t 2 (t 2 / t 1} ). If it exceeds 1: 100, there is a possibility that the prescribed S content is not satisfied, and the cutting waste is not finely divided during the cutting process. Even when the sulfide is not linear in the extending direction, the above definition remains unchanged, and as shown in FIG. 4, the length t ₂ of the extending direction of the portion occupying the region and the direction orthogonal thereto determine the length _{t 1,} to evaluate.

Measurement Example of Sulfide FIG. 1A is a front view of a copper alloy rod 10 viewed in parallel with the extending direction R, FIG. 1B is a cross-sectional view, and FIG. is there.
FIG. 2 is a schematic diagram of an electron microscope observation of a cross section parallel to the extension direction, showing a crystal grain boundary 21 and a sulfide state observed in one field of view, in which 21 is a crystal grain boundary, and 22 is a crystal A sulfide at the grain boundary, 23 indicates an intracrystalline grain sulfide. Here, the total area of all sulfides observed in one field of view is obtained.
Next, FIG. 3 schematically shows a cross-sectional structure of a copper alloy rod viewed with an electron microscope (SEM) in parallel to the extending direction. The grain boundaries and the sulfides at the grain boundaries in FIG. It is a sulfide in the crystal grains excluding. The total area of the sulfides in the crystal grains shown in the figure is obtained, and the ratio of the sulfides in one field of view to the sulfides in the crystal grains is obtained. In this case, the area ratio of the sulfide in the crystal grains is 61%.
As shown in FIG. 4, the aspect ratio of the sulfide is that the length t _{1 in the} direction perpendicular to the extension direction of the sulfide is 1, and the length t of the sulfide stretched in parallel to the extension direction with respect to this. The ratio of ₂ (13 in the lower example in the figure).

<Mechanical properties and manufacturing conditions>
Next, the mechanical properties of the copper alloy wrought material in a preferred embodiment of this embodiment will be described. The copper alloy in this embodiment is intended to replace lead-containing phosphor bronze and beryllium copper, that is, to replace copper alloys containing environmentally hazardous substances. This is the same as in the first embodiment. Therefore, a preferable range of practically required characteristics (tensile strength, conductivity) and the like are the same as those in the first embodiment.

In the method for producing a copper alloy wrought material according to the present embodiment, a large amount of sulfide existing at the grain boundary at the time of casting is 40% in terms of the area ratio of the sulfide having a cross section parallel to the extending direction by the drawing process and heat treatment. As described above, the main feature is to disperse the aspect ratio of the sulfide having a cross section parallel to the extending direction within the range of 1: 1 to 1: 100.
The following examples are given as preferred examples of the stretching and heat treatment.
(A) Rapid cooling after hot working, surface reduction of 0% to 95% (more preferably 30 to 90%) is applied, and final aging treatment is performed.
(B) After hot working, cold working and heat treatment at a temperature of 600 ° C. to 1000 ° C. are repeated one or more times. After the solution treatment before the final cold working, 0% to 95% (more preferably 30% (~ 90%) and a final aging treatment.
Here, when the cold working and the heat treatment at a temperature of 600 ° C. to 1000 ° C. are performed once, the cold working is a final cold working, and the heat treatment at a temperature of 600 ° C. to 1000 ° C. is a solution treatment.
Further, the surface reduction processing is cold processing, and 0% surface reduction processing means that the surface reduction processing is not performed. The temperature at the final aging treatment is preferably 350 to 600 ° C., more preferably 400 to 550 ° C.
The purpose of the heat treatment at a temperature of 600 ° C. to 1000 ° C. is to improve the workability of the wrought material. The temperature range is preferably 800 ° C. to 1000 ° C., more preferably 900 ° C. to 1000 ° C. The heat treatment time is preferably 1 to 3 hours. Further, the cooling conditions are virtually arbitrary, and may be slow cooling or rapid cooling. A cooling rate in the range of 0.1 to 1000 ° C./second is sufficient.
From the viewpoint of the step immediately before the surface-reduction processing, the aspect ratio of the sulfide in a cross section parallel to the extending direction is brought close to 1: 1, and the shape and dispersion state of the sulfide by the surface-reduction processing are appropriately controlled. Hot working or solution treatment is preferred. In this case, the temperature of the hot working or solution treatment is preferably 750 ° C. to 1000 ° C., more preferably 850 ° C. to 1000 ° C., and further preferably 900 ° C. to 1000 ° C.
In addition, the effect equivalent to a solution treatment can be acquired by performing rapid cooling (quenching in water etc.) immediately after hot processing (hot rolling, hot wire drawing, hot extrusion, etc.).
Since the copper alloy wrought material of the present embodiment is a wrought material of an aging precipitation type copper alloy, it is a premise that the aging treatment step is preferably adopted at least after the melting and casting step of the copper alloy raw material. The processing step, the annealing step, the solution treatment step, and the heat treatment step at a temperature of 600 ° C. to 1000 ° C. are performed as necessary in addition to the step for obtaining the copper alloy wrought material. For example, with regard to the hot working process, the copper alloy wrought material of this embodiment can be produced by any of the usual production methods such as billet hot extrusion, ingot hot forging, or continuous casting. It is.
In addition, as the shape of the product and the copper alloy part, the same ones as those in the first embodiment are preferable.

Hereinafter, the present invention will be described in more detail based on examples, but the present invention is not limited thereto.

Example 1
Example 1-1
A copper alloy having the composition shown in Table 1-1 was melted in a high-frequency melting furnace, and each billet was cast at a cooling rate of 0.5 to 5 ° C./second. The diameter of the billet was 200 mm. The billet was hot extruded at a temperature of 950 ° C. and immediately quenched in water to obtain a round bar having a diameter of 20 mm. Next, the round bar was drawn out cold to produce a round bar having a diameter of 10 mm, and further subjected to aging heat treatment at a temperature of 450 ° C. for 2 hours.

[1] Tensile strength, [2] Electrical conductivity, and [3] Machinability of each of the copper alloy wrought materials (round bars) obtained in this manner were examined by the following methods. The measurement method for each evaluation item is as follows.
[1] Tensile strength Three were measured according to JIS Z 2241 and the average value (MPa) was shown.
[2] Conductivity Using a four-terminal method, two samples were measured for each sample in a thermostatic chamber controlled at 20 ° C. (± 1 ° C.), and the average value (% IACS) was shown.
[3] Machinability Using a general-purpose lathe, cut the outer diameter of a round bar with a stepped cut to produce a rivet with a diameter of 9.6 mm for the large diameter part and a diameter of 8 mm for the small diameter part. The morphology was observed. The cutting waste was divided into 5 mm or less, and the cutting waste was divided, but the length was 5 mm or more and 10 mm or less, and the cutting waste was spirally connected. It is good and good that there is no practical problem. The cutting conditions were a rotation speed of 1010 rpm, a feed rate of 0.1 mm per rotation, and a cutting allowance of 0.2 mm. The tool was made of cemented carbide and no cutting oil was used.

In addition, the size (average diameter) and area ratio of the sulfides were observed in three cross sections using a scanning electron microscope (SEM) for each of three arbitrary cross-sections of a 10 mm diameter round bar sample. Determined by doing. The size (average diameter) of the sulfide was obtained by converting 100 or more sulfides per field of view into a circle and averaging the diameters. The area ratio of sulfides is obtained by counting the number of sulfides seen in one field of view and calculating the total area per field of sulfide by multiplying the area obtained from the average diameter assuming that the sulfide is a circle. It was calculated by dividing by the area. Moreover, the component of sulfide was investigated using the energy dispersive X-ray fluorescence spectrometer (EDX) attached to SEM.

Table 1-1 shows the results. Inventive Examples 1-1 to 1-25 have components within the scope of the present invention, and all satisfy a tensile strength of 500 MPa or more and a conductivity of 25% IACS or more. In addition, the sulfide size (average diameter) is 0.1 to 10 μm and the area ratio of sulfide is 0.1 to 10%, there is no cracking during material processing, and machinability is also satisfied. ing.

Comparative Examples 1-1 to 1-9 are examples whose components are outside the scope of the present invention. In Comparative Examples 1-1 and 1-3, the Ni concentration and the Si concentration are low, and the tensile strength is inferior. In Comparative Example 1-2, the Ni concentration and the Si concentration are high, and the conductivity is inferior. In Comparative Example 1-4, the Ni concentration and the Si concentration were high, and cracks occurred during cold working. In Comparative Example 1-5, the S concentration was low, the area ratio of sulfide was small, and the machinability was poor. In Comparative Examples 1-6 and 1-7, the S concentration was high and the area ratio of sulfide increased, and cracks occurred during hot working. In Comparative Examples 1-8 and 1-9, the total amount of Sn, Mn, Co, Zr, Ti, Fe, Cr, Al, P, and Zn exceeded 2.0 mass%, and the conductivity was inferior.
Conventional examples 1-1 and 1-2 are free-cutting phosphor bronze and free-cutting beryllium copper. The copper alloy wrought material of the example of the present invention does not contain an environmentally hazardous substance like the materials of the conventional examples 1-1 and 1-2, and obtains characteristics equal to or higher than those of the conventional examples 1-1 and 1-2. be able to.

Example 1-2
Using the alloy components of Invention Example 1-6 and Invention Example 1-16 in Table 1-1, using a small experimental mold (25 mm × 25 mm × 300 mm) and changing the mold preheating temperature, etc. Small ingots with different cooling rates were produced. The obtained ingot was hot-rolled at a temperature of 950 ° C. and directly quenched in water to obtain a round bar having a diameter of 20 mm. Next, the round bar was drawn out cold to produce a round bar having a diameter of 10 mm, and further subjected to aging heat treatment at a temperature of 450 ° C. for 2 hours. [1] Tensile strength, [2] conductivity, and [3] machinability of each copper alloy wrought material (round bar) sample thus obtained were the same as in Example 1-1. The sulfide size (average diameter) and area ratio were similarly determined by the above method. The results are shown in Table 1-2.

Inventive Examples 1-26 to 1-29 in Table 1-2 are the same alloy components as Inventive Example 1-6, Inventive Examples 1-30 to 1-33 are the same alloy components as Inventive Example 1-16, This is an example in which the cooling rate is changed within the range of the present invention. When the cooling rate is increased, the size (average diameter) of the sulfide tends to decrease, but both are within the scope of the present invention, and excellent machinability is obtained. Comparative Examples 1-10 and 1-11 in Table 1-2 are the same alloy components as Invention Example 1-6, Comparative Examples 1-12 and 1-13 are the same alloy components as Invention Example 1-16, and cooling rate Is an example outside the scope of the present invention. When the cooling rate was slow (Comparative Examples 1-10 and 1-12), the size (average diameter) of the sulfide increased, and cracking occurred during cold or hot working. When the cooling rate is high (Comparative Examples 1-11 and 1-13), the size (average diameter) of the sulfide is less than 0.1 μm, and the machinability is poor.

(Example 1-3)
Using the alloy components of Invention Example 1-6 and Invention Example 1-16 of Table 1-1, round bars of φ2 mm and φ7 mm were prepared from the round bars of diameter 10 mm obtained by the method of Example 1-1. did. With respect to these round bars, 1000 connector pins as shown in FIGS. 5 and 6 were produced using an NC lathe. As a result, parts could be processed without entanglement of the cutting scraps into the processed parts and dimensional changes due to tool wear. The cutting conditions are as follows: outer diameter processing is 3000 rpm, feed rate is 0.02 mm per revolution, and drilling is 2500 rpm, feed rate is 0.03 mm per revolution, and cutting oil is used. did. In FIG. 5, 50 indicates a connector pin, and 51 indicates a slit. In FIG. 6, 60 is a connector pin according to another embodiment, 61 is a slit, and 62 is a tapered portion.
About the connector pin of the shape of FIG. 5, the insertion / extraction property required as a characteristic of a pin material was evaluated. The evaluation method is to insert a φ0.92 mm pin gauge into the processed pin and measure the insertion / extraction force (initial value T0), and after repeating the same pin repeatedly 500 times, measure the insertion / extraction force again ( T1), the ratio T1 / T0 with respect to the initial value was obtained. The larger T1 / T0 is, the smaller the drop in insertion / extraction force is, and it can be said that the performance as a connector pin is good. Evaluation was performed on five pins, and an average value was obtained. For comparison, the materials of Conventional Examples 1-1 and 1-2 in Table 1-1 were also evaluated. The results are shown in Table 1-3.
From Table 1-3, it can be seen that the present invention example is an excellent connector pin, showing the same insertability as the free-cutting beryllium copper of Conventional Example 1-2. The insertability of the free-cutting phosphor bronze of Conventional Example 1-1 was inferior to that of the present invention example, and there was a concern about poor contact during long-term use.

(Example 2)
Example 2-1
A sample was obtained using a copper alloy having the composition shown in Table 2-1 in the same manner as in Example 1-1. The measuring method and conditions for each characteristic are the same as in Example 1-1.

The area ratio in which the sulfide having a cross section parallel to the extension direction exists in the crystal of the matrix is a scanning electron microscope (for a cross section parallel to the extension direction at any three points of a sample of a round bar having a diameter of 10 mm ( It was calculated | required by performing structure | tissue observation about 3 visual fields each using SEM. Count the number of all sulfides observed in one field of view, calculate the diameter of each sulfide by circular conversion, determine the average, determine the area from the average diameter, and multiply by the number of sulfides in one field of view. After determining the total area of all the sulfides that can be seen, count the number of sulfides only within the crystal grains and across the crystal grain boundaries, calculate the diameter by converting each sulfide into a circle, and average Find the area from the average diameter and multiply by the number of sulfides to obtain the total area of sulfides across the crystal grains and grain boundaries, and divide by the total area of all sulfides seen in one field of view. I asked for it. Moreover, the component of sulfide was investigated using the energy dispersive X-ray fluorescence spectrometer (EDX) attached to SEM. Although not shown in the table, each of the wrought materials of the examples of the present invention has an aspect ratio in the range of 1: 1 to 1: 100 in a cross section parallel to the stretch direction, and The area ratio of sulfide in the cross section was 0.1 to 10%.

Table 2-1 shows the results. Inventive Examples 2-1 to 2-25 have components within the scope of the present invention, and all satisfy a tensile strength of 500 MPa or more and a conductivity of 25% IACS or more. Further, 40% or more of the sulfide having a cross section parallel to the extending direction is present in the crystal of the matrix, there is no cracking during material processing, and machinability is also satisfied.

Comparative Examples 2-1 to 2-9 are examples in which the alloy composition is outside the scope of the present invention. In Comparative Examples 2-1 and 2-3, since the Ni concentration and the Si concentration were too low, only those having insufficient tensile strength were obtained. In Comparative Example 2-2, the Ni concentration and the Si concentration are too high, and the conductivity is inferior. In Comparative Example 2-4, the Ni concentration and the Si concentration were too high, and cracking occurred during cold working. In Comparative Example 2-5, 40% or more of the sulfide having a low S concentration and parallel to the extension direction was present in the matrix crystal, but the machinability was poor. In Comparative Examples 2-6 and 2-7, 40% or more of the sulfide having a high S concentration and a cross section parallel to the extending direction was not present in the matrix crystal, and cracking occurred during hot working. In Comparative Examples 2-8 and 2-9, the total amount of Sn, Mn, Co, Zr, Ti, Fe, Cr, Al, P, and Zn exceeded 2.0 mass%, and the conductivity was inferior.
Conventional examples 2-1 and 2-2 are free-cutting phosphor bronze and free-cutting beryllium copper. The copper alloy wrought material of the example of the present invention does not contain an environmentally hazardous substance like the materials of the conventional examples 2-1 and 2-2, and obtains characteristics equal to or higher than those of the conventional examples 2-1 and 2-2. be able to.

(Example 2-2)
Inventive Examples 2-1, 2-6, 2-16 and Comparative Example 2-5 in Table 2-1 were melted in a high frequency melting furnace and each billet having a diameter of 300 mm was cooled at a cooling rate of 1 ° C. / Sec. The billet was hot extruded at a temperature of 950 ° C. and immediately quenched in water to obtain a round bar having a diameter of 30 mm. Thereafter, it was processed to a diameter of 20 mm by cold drawing, and a solution treatment was performed at a temperature of 950 ° C. to obtain a round bar having a diameter of 20 mm.
This round bar is surface-reduced, diameter 20mm (area reduction 0%), diameter 16mm (area reduction 36.0%), diameter 10mm (area reduction 75.0%), diameter 4.5mm (area reduction) Round bars with 94.9% processing and 3.5 mm diameter (96.9% surface-reducing processing) were produced. Furthermore, 20 mm in diameter was subjected to aging treatment at 500 ° C. for 2 hours, 16 mm in diameter at 480 ° C. for 2 hours, 10 mm in diameter at 450 ° C. for 2 hours, and 4.5 mm and 3.6 mm in diameter at 430 ° C. for 2 hours. For each sample of the copper alloy wrought material (round bar) thus obtained, [1] tensile strength and [2] conductivity were examined by the same method as in Example 1, and [3] covered The machinability was examined by the following method.
[3] Machinability Using a general-purpose lathe, materials of each diameter were externally machined to produce a round bar having a diameter of 3 mm, and stepped cutting of the round bar with an outer diameter was performed. Observe the shape of the generated cutting waste. Good if the cutting waste is divided to a length of 5 mm or less. Good if the cutting waste is divided but the length is 5 mm or more and 10 mm or less. The cutting waste is spiral. Those that led to were considered bad. It is good and good that there is no practical problem. The cutting conditions were a rotation speed of 1010 rpm, a feed rate of 0.1 mm per rotation, and a cutting allowance of 0.2 mm. The tool was made of cemented carbide and no cutting oil was used.

The area ratio in which the sulfide having a cross section parallel to the extension direction exists in the crystal of the matrix is the extension at any three locations of the round bar samples having diameters of 20, 16, 10, 4.5, and 3.5 mm. About the cross section parallel to the direction, the structure | tissue observation was performed about 3 visual fields each using the scanning electron microscope (SEM), and it calculated | required by the said method. The aspect ratio of the sulfide was determined from the ratio of the lengths of the sulfides stretched parallel to the extension direction, with the direction perpendicular to the extension direction of the sulfide observed with the electron microscope described above being 1.

Inventive Examples 2-26 to 2-37 in Table 2-2 are the same alloy components as Inventive Examples 2-1, 2-6, and 2-16, and are subjected to surface reduction within the scope of the present invention. is there. All satisfy tensile strength of 500 MPa or more and conductivity of 25% IACS or more. Further, 40% or more of the sulfide having a cross section parallel to the extending direction exists in the matrix crystal, and the aspect ratio of the sulfide having a cross section parallel to the extending direction is dispersed in a range of 1: 1 to 1: 100. Therefore, there are no cracks during material processing, and the machinability is satisfactory.
Comparative Examples 2-10 to 2-12 have alloy compositions within the scope of the present invention, but the area reduction ratio is outside the scope of the present invention, and cracks occurred during cold working. Comparative Examples 2-13 to 2-16 are the same alloy components as Comparative Example 2-5. Comparative Examples 2-13 to 2-15 are surface-reducing processes within the scope of the present invention. However, since the S concentration is low, 40% or more of the sulfide having a cross section parallel to the extending direction is present in the matrix crystal. However, machinability was inferior. In Comparative Example 2-16, 40% or more of the sulfide having a cross-section parallel to the extension direction was present in the matrix crystal in the area reduction processing outside the scope of the present invention, and no cracks occurred. The aspect ratio of the sulfide having a parallel cross section was dispersed exceeding 1: 100 and the machinability was poor.

(Example 2-3)
With the alloy compositions of Invention Example 2-6 and Invention Example 2-16 in Table 2-1, connector insertion / removability was evaluated in the same manner as in Example 1-3. From the results shown in Table 2-3, it can be seen that the present invention example is an excellent connector pin, showing the same insertability as the free-cutting beryllium copper of Conventional Example 2-2. The insertability of the free-cutting phosphor bronze of Conventional Example 2-1 is inferior to that of the present invention.

While this invention has been described in conjunction with its embodiments, we do not intend to limit our invention in any detail of the description unless otherwise specified and are contrary to the spirit and scope of the invention as set forth in the appended claims. I think it should be interpreted widely.
This application is priority based on Japanese Patent Application No. 2010-280946 filed in Japan on December 16, 2010, and based on Japanese Patent Application No. 2010-210201 filed in Japan on September 17, 2010 , Priority based on Japanese Patent Application 2010-143420 filed in Japan on June 24, 2010, and priority based on Japanese Patent Application 2010-88228 filed in Japan on April 7, 2010 All of which are hereby incorporated by reference as if fully set forth herein.

DESCRIPTION OF SYMBOLS 10 Copper alloy rod 10 'Copper alloy rod 10a cut | disconnected in extension direction Cross section R parallel to extension direction Extension direction 21 Grain boundary 22 Sulfide in a crystal grain boundary 23 Intragranular sulfide 24 Exhibit of sulfide Length in the direction perpendicular to the extending direction 25 Length in the direction parallel to the extending direction of sulfide 50, 60 Connector pins 51, 61 Slit 62 Tapered portion

Claims (13)

A copper alloy wrought material containing 1.5 to 7.0 mass% of Ni, 0.3 to 2.3 mass% of Si, 0.02 to 1.0 mass% of S, and the balance of Cu and inevitable impurities. The sulfide is dispersed, the average diameter of the sulfide is 0.1 to 10 μm, the area ratio of the sulfide is 0.1 to 10%, and the tensile strength is 500 MPa or more. A copper alloy wrought material having a conductivity of 25% IACS or higher. Containing 1.5 to 7.0 mass% of Ni, 0.3 to 2.3 mass% of Si, 0.02 to 1.0 mass% of S, and Sn, Mn, Co, Zr, Ti, Fe, Cr A copper alloy wrought material containing 0.05 to 2.0 mass% of the total amount of at least one selected from the group consisting of Al, P and Zn, with the balance being Cu and inevitable impurities, The sulfide has an average diameter of 0.1 to 10 μm, the area ratio of the sulfide is 0.1 to 10%, the tensile strength is 500 MPa or more, and the conductivity is 25%. Copper alloy wrought material characterized by being IACS or higher. The sulfide is at least one selected from the group consisting of Cu-S, Mn-S, Zr-S, Ti-S, Fe-S, Al-S, Cr-S, and Zn-S. The copper alloy wrought material according to claim 1 or claim 2. A copper alloy part formed by cutting the copper alloy wrought material according to any one of claims 1 to 3. The copper alloy part according to claim 4, which is used for an electronic device part, a structural part, or an element part. A method for producing a copper alloy wrought material according to any one of claims 1 to 3, wherein a cooling rate during casting is 0.1 to 50 ° C / second. A method of manufacturing stretched material. A copper alloy wrought material containing 1.5 to 7.0 mass% of Ni, 0.3 to 2.3 mass% of Si, 0.02 to 1.0 mass% of S, and the balance of Cu and inevitable impurities. There is a sulfide having an area ratio of 40% or more of the sulfide in the cross section parallel to the extending direction in the matrix crystal, and having an aspect ratio of 1: 1 to 1: 100 in the cross section parallel to the extending direction. A copper alloy wrought material dispersed in a matrix, having a tensile strength of 500 MPa or more, and an electrical conductivity of 25% IACS or more. Furthermore, 0.05 to 2.0 mass% in total of at least one selected from the group consisting of Sn, Mn, Co, Zr, Ti, Fe, Cr, Al, P and Zn is contained. The copper alloy wrought material according to 7. The sulfide is one or more selected from any of sulfides of Cu—S, Mn—S, Zr—S, Ti—S, Fe—S, Al—S, Cr—S and Zn—S. The copper alloy wrought material according to claim 7 or 8. A copper alloy part formed by cutting the copper alloy wrought material according to any one of claims 7 to 9. The copper alloy part according to claim 10, which is used for applications requiring strength, electrical conductivity, thermal conductivity, and wear resistance, such as electronic equipment parts, structural parts, and element parts. A method for producing a copper alloy wrought material according to any one of claims 7 to 9, wherein Ni is 1.5 to 7.0 mass%, Si is 0.3 to 2.3 mass%, and S is used. In processing a copper alloy composition containing 0.02 to 1.0 mass% and the balance being Cu and inevitable impurities, one of the following steps (a) and (b) is performed, and then 0% More than 40% of the total area of sulfide dispersed in a matrix with a cross-section parallel to the extension direction after surface reduction of ~ 95% exists in the matrix crystal, and the aspect ratio of the cross-section parallel to the extension direction is A method of producing a copper alloy wrought material, characterized by subjecting a sulfide dispersed in a matrix of 1: 1 to 1: 100 to an aging treatment.
(A) Rapid cooling after hot working.
(B) After hot working, cold working and heat treatment at a temperature of 600 ° C. to 1000 ° C. are repeated at least once, and solution treatment is performed before the final cold working. Furthermore, 0.05 to 2.0 mass% in total of at least one selected from the group consisting of Sn, Mn, Co, Zr, Ti, Fe, Cr, Al, P and Zn is contained. 12. A method for producing a copper alloy wrought material according to item 12.

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