JP2804966B2 - High strength copper alloy for conductive - Google Patents

Description

DETAILED DESCRIPTION OF THE INVENTION

[0001]

BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a conductive copper alloy having excellent wire drawing properties, and more particularly to a copper alloy having excellent mechanical properties such as tensile strength and repetitive bending strength. The present invention relates to a conductive copper alloy suitable for an electric wire conductor for an automobile provided with the above.

[0002]

2. Description of the Related Art Various in-vehicle devices mounted on an automobile are:
2. Description of the Related Art In recent years, in order to control driving of an automobile or to facilitate operation of an in-vehicle device itself, there is a tendency to be electronic or electric. With this trend, the number of wiring circuits between the power supply and the in-vehicle device or between the in-vehicle devices has increased remarkably, and the total weight and the occupied space inside the vehicle of the automobile have increased. As a result, the weight and the required space of the entire vehicle are increased, fuel economy is increased, which is not only economically disadvantageous but also against social demands for energy saving. For this reason, it is possible to realize a conductor for an automobile electric wire having excellent mechanical properties such as tensile strength and repeated bending strength, and also having high conductivity and elongation, thereby reducing the weight of the automobile electric wire and the space occupied by the conductor. There is a demand for narrowing of the size.

Conventionally, annealed copper wire has been mainly used as a conductor for electric wires for automobiles. However, since annealed copper wire has inferior mechanical properties, it travels in a place where an ultrafine wire for a minute current circuit may actually be used. It was necessary to use a conductor larger than the required electrical diameter in order to secure mechanical strength against vibrations and shocks inside, and it was difficult to reduce the weight. For this reason,
Hard copper wire was studied as a material to replace the soft copper wire, but the hard copper wire has a remarkably low elongation, and the terminal crimping portion is a mechanical weak point due to external force, resulting in poor reliability. Therefore, a wire having excellent properties in place of annealed copper wire, that is, a wire having excellent mechanical properties such as tensile strength and repetitive bending strength, capable of reducing the conductor diameter, and having good conductivity and elongation. Required. As such a wire material, Cu
-Mg alloy or Cu-Fe-P-Mn-Si alloy as disclosed in JP-A-1-212732. This latter alloy is composed of Fe, P, Mn, S
It is obtained by depositing the intermetallic compound of i in a copper matrix, has relatively good conductivity, and is excellent in wire drawing properties, tensile strength, and repeated bending properties.

[0004]

However, the above-mentioned Cu-Mg alloy improves the tensile strength by dissolving Mg in Cu, but is insufficient, and has a low flexural strength. Further, Mg is highly susceptible to oxidation and elimination during melting and casting, and tends to have unstable characteristics because the added components are apt to fluctuate. In addition, since there is a difficulty in castability, casting cracks are likely to occur during continuous casting, and there is a possibility that disconnection frequently occurs during subsequent wire drawing. Cu-M with Sn added to it
g-Sn alloy has also been proposed, but enough of those tensile strength is somewhat improved not name. Further, the above-mentioned Cu-Fe-P
-Mn-Si alloy has good characteristics because it precipitates Fe, P, Mn, and Si finely to improve tensile strength, elongation, and electrical conductivity. For,
In addition to the usual electric wire manufacturing process, a solution treatment and an age hardening treatment in which the temperature of the heat treatment is accurately controlled are required. For this reason, the number of equipments and the number of steps are increased, and the production cost is increased. In addition, P in the alloy acts as a deoxidizing agent and reacts with oxygen during a continuous casting process for converting the alloy into a wire, causing a variation in the P content of the cast product, resulting in uneven characteristics of the product wire. There was also a problem that would occur.

[0005] The present invention provides a high-strength copper for conductive use which is a solid solution strengthened copper alloy which does not require a complicated heat treatment step, is excellent in wire drawing workability, and is excellent in strength, elongation, conductivity and bending resistance. The purpose is to provide alloys.

[0006]

In order to achieve the above-mentioned object, the present invention relates to a method for producing Mg in an amount of 0.1 to 0.5 wt% and Ni in an amount of 0.1 to 0.5 wt%.
0.5 wt%, Sn: 0.1 to 0.5 wt%, Li: 0.02 to 0.2
wt.%, with the balance substantially consisting of Cu.

Further, the present invention relates to a method for preparing Mg from 0.1 to 0.5 wt%,
0.15 to 0.75 wt% of Sn, 0.05 to 0.35 wt% of In
May be contained, the balance being Cu, and the content ratio of Mg: Sn being in the range of 1: 1.2 to 1.8, thereby realizing a high-strength copper alloy for conductive use having excellent wire drawing properties. doing.

[Action]

[0008] The alloy of the present invention according to claim 1 comprises Mg, Sn
Is dissolved in a Cu matrix to improve tensile strength and elongation after annealing, and by adding Ni, castability is improved. Further, the addition of Li stabilizes the Mg content. In the present invention, the reason why the content of Mg is defined as 0.1 to 0.5 wt% will be described.
When Mg is added to Cu, cast cavities are likely to occur during casting, and castability deteriorates. In particular, casting cracks are apt to occur during continuous casting, and even fine cracks become defective portions during cold rolling and wire drawing in the subsequent steps, and disconnection frequently occurs. Therefore, Cu
-Magnesium alloy is drawn after its surface is chamfered, but breakage may occur frequently. However, the solid solution of Mg has a large effect of improving the tensile strength, although the decrease in the conductivity is small.
When the content of Mg is less than 0.1 wt%, the effect of improving the tensile strength is small, and when the content of Mg is more than 0.5 wt%, the effect of improving the tensile strength is saturated, the electric conductivity is greatly reduced, and the castability is poor. Become. Therefore, the content was set to 0.1 to 0.5 wt%.

The reason for limiting the Ni content to 0.1 to 0.5 wt% will be described. When Ni is added to a Cu-Mg alloy, not only the castability deteriorated by Mg is remarkably improved, but also the tensile strength and elongation after annealing are improved. However, when the Ni content is less than 0.1 wt%, the castability reduced by the addition of Mg cannot be completely improved, and when the Ni content is 0.5 wt% or more, the castability is improved but the conductivity is greatly reduced, which is not practical. Tensile strength and elongation after annealing are saturated. Also, since Ni lowers the electrical conductivity, it is desirable that the amount of addition is not so large, and the ratio of Mg: Ni is 0.8 to 0.8.
1.0 is good. When the ratio of Mg: Ni is 0.8 or less, Mg
However, if the amount of Ni is too large, the castability is improved, but the electrical conductivity is lowered, which is not practical.

The reason for limiting the Sn content to 0.1 to 0.5 wt% will be described. Sn has a very large effect of improving elongation after annealing, has significantly improved bending resistance, has a large effect of improving tensile strength, and has a larger effect of improving castability than Ni. However, less than 0.1 wt% has little effect,
Above t%, the effect of improvement is saturated and the decrease in conductivity is increased, which is not practical.

The reason for limiting the Li content to 0.02 to 0.2 wt% will be described. Li contributes to the improvement of the tensile strength,
There is little decrease in conductivity. However, the main purpose of Li addition is M
g content stabilization. Normally, when Mg is dissolved in Cu, it is largely lost due to oxidation. Therefore, the copper alloy containing Mg is protected from oxidation by changing the atmosphere in the furnace to an inert gas or protecting the surface of the molten metal with a flux for preventing oxidation. However, when casting is performed for a long time, Mg reacts with oxygen in the molten copper and in the atmosphere to be oxidized and disappear. By adding Li, oxygen in the molten copper and in the atmosphere reacts preferentially and prevents oxidation of Mg. Li remaining in the molten copper contributes to improvement in tensile strength. If the addition of Li is 0.02% by weight or less, the above effect cannot be obtained. If the addition is 0.2% by weight or more, Li is expensive, so that the cost is increased and the conductivity is lowered.

Further, the alloy according to the present invention according to claim 2 is characterized in that:
By dissolving g, Sn, and In in a Cu matrix, the comparatively high conductivity is maintained, the tensile strength is enhanced, and the elongation after annealing is improved.
In the present invention, the reason why Mg is contained is that the content of Mg enhances the tensile strength as described above, and also the reason that the Mg content is limited to the range of 0.1 to 0.5 wt%,
As described above, when the content is 0.5 wt% or more, the effect of increasing the tensile strength is saturated, and moreover, defects such as cavities are likely to occur during ingot casting, and castability is deteriorated. On the other hand, when the content is less than 0.1 wt%, the effect of increasing the tensile strength is low.

In the present invention, the reason why Sn is contained is that, as described above, the continuous castability is greatly improved, the tensile strength is enhanced, and the elongation after annealing is improved. Is greatly improved. Also, the reason why the Sn content is limited to the range of 0.15 to 0.75 wt% is that when the Sn content is 0.75 wt% or more, the conductivity is higher than that of the effect of enhancing the tensile strength, elongation after annealing and improving the repetitive bending characteristics. On the other hand, if it is 0.15 wt% or less, the effect of improving the continuous castability is small, and the effect of increasing the tensile strength and the effect of improving the elongation after annealing and the repetitive bending characteristics are also low. Because.

In the present invention, the reason for including In is that the inclusion of In enhances the tensile strength without sacrificing conductivity. In content 0.05 ~ 0.35wt
The reason for limiting to the range of% is that In is an expensive element, so that the content should be as small as possible.
If the content is more than 0.35% by weight, the effect of enhancing the tensile strength is saturated, and the cost is greatly increased.
This is because the effect of increasing the tensile strength is small below.

In the present invention, the reason why the content ratio of Mg and Sn is limited to the range of 1: 1.2 to 1.8 is that Mg and Sn are contained.
If the content ratio is 1: 1.2 or less, the deterioration of castability due to the inclusion of Mg cannot be compensated for by the improvement of castability due to the inclusion of Sn.
This is because casting cracks are likely to occur, and as a result, disconnection is likely to occur. Cast cracks appear as defects in the wire drawing process after rolling, and as a result, disconnection frequently occurs. Also,
If the content ratio of Mg and Sn is 1: 1.8 or more, the effect of improving the castability by Sn is saturated.

[0016]

The first embodiment of the present invention will be described below. Table 1 shows the copper alloy of the present invention and Comparative Example No. 1 to 1
From the alloy as No. 2, a sample wire was obtained as follows. First, copper (Cu) is melted under a graphite particle coating in a melting furnace maintained in an inert gas atmosphere, and then Mg, Ni, Sn and Li are added in required amounts in the form of pure metals, respectively, to obtain a uniform composition. A molten metal was obtained. This was subjected to continuous casting, as shown in Table 1.
A 20 mmφ cast rod having the composition shown in Table 1 was produced. This was cold-rolled, drawn to 1 mmφ, electrically annealed by an electric resistance annealing machine, and the tensile strength, elongation, electrical conductivity, and repeated bending strength were measured. In addition, the comparative example No. Reference numeral 13 denotes a hard copper wire, which is pure copper.

[0017]

[Table 1]

In addition, in Comparative Example No. 1
The Cu-Fe-P-Mn-Si alloy of No. 4 was prepared by melting copper under a graphite particle coating in a melting furnace maintained in an inert gas atmosphere.
Fe, P, Mn, and Si were added in the form of a mother alloy to obtain a uniform molten metal. This was continuously cast into a 20
A mmφ cast rod was prepared. This was cold-rolled and drawn to obtain a 3.2 mmφ wire. This wire was heated in an inert gas atmosphere furnace at 900 ° C. for 1 hour and then water-cooled to perform a solution treatment. Thereafter, the wire was drawn to 1.0 mmφ and subjected to age hardening treatment in an inert gas atmosphere furnace at 470 ° C. for 6 hours, and the tensile strength, elongation, electric conductivity, and repeated bending strength were measured. In addition,
In Table 1, the conductivity is% IACS, the tensile strength is Kg / mm ² ,
The elongation is indicated by%, and the repeated bending strength is indicated by the number of times.

Next, in order to evaluate the castability of the alloy according to the present invention, a thin wire up to 0.08 mmφ was drawn. Cold rolled 20mmφ cast rod made by continuous casting, 9.5mmφ
Created a rough drawing line. This is 2.6mm with a large continuous wire drawing machine.
Wire was drawn to φ. Subsequently, the wire was drawn from 2.6 mmφ to 0.6 mmφ using a small wire drawing machine. Furthermore, the wire was drawn from 0.6mmφ to 0.08mmφ with a fine wire machine, and the number of disconnections was investigated.
This is shown in Table 1 above. The wire drawing quantity is 50k wire weight.
g was taken out.

In the bending test, as shown in FIG. 1, a sample 2 is interposed between a jig 1 and a tensile load W of 2 kg is applied to the other end of the jig 1, and (a) → (b) → (c) → 90 ° left and right with (d)
Bending once, repeat until break,
The number of times was defined as bending strength.

As shown in Table 1, the alloy No. 1
-No. 9 and Comparative Alloy No. 9 In comparison with No. 14, it can be seen that the conductivity is slightly lower, but has the same or higher characteristics in tensile strength, elongation and flexural strength. In addition, comparative alloy No. No. 14 has undergone a complicated heat treatment step such as a solution treatment and an age hardening treatment as described in the section of the problem to be solved.

Comparative Alloy No. 1 and No. 2 is normal C
It is a u-Mg alloy. Compared with the alloy of the present invention, the conductivity is the same, but the tensile strength, elongation and flexural strength are significantly inferior. Comparative alloy No. Reference numeral 3 denotes a Cu—Ni alloy, which is inferior in conductivity, tensile strength, elongation, and flexural strength. Comparative alloy N
o. 4 and No. 5 is a Cu-Sn alloy. Conductivity is the same, but tensile strength, elongation and flexural strength are inferior. Comparative alloy No. In No. 6, Mg, Ni, Sn and Li are lower than the lower limit of the alloy of the present invention. Excellent conductivity, but poor in tensile strength, elongation, and flexural strength. Comparative alloy No. 7 is Cu-Mg
-Sn alloy. Conductivity is the same, but tensile strength, elongation and flexural strength are inferior. Comparative alloy No. 8 is Cu-Mg
-Ni alloy. Conductivity is the same, but tensile strength, elongation and flexural strength are inferior.

Comparative Alloy No. 9, No. 10, No. 1
1 is a Cu-Mg-Ni-Sn alloy. No. No. 9 has significantly lower conductivity because the content of Ni and Sn is equal to or more than the upper limit of the alloy of the present invention. No. 10 and No. No. 11 has the same composition. No. 11 is the composition immediately after the start of casting. 1
0 is the composition 2 hours after the start of casting. Despite the inert gas atmosphere and under the graphite particle coating, the amount of Mg is about 3
It has decreased by 0%. For this reason, the tensile strength and elongation are slightly reduced. On the other hand, the alloy No. of the present invention. No. 8 is a composition immediately after casting. 9 is the composition at the end of casting after 6 hours. Since Li protects the oxidation and disappearance of Mg, there is almost no decrease in Mg, and there is no change in characteristics. The alloy No. of the present invention. No. 5 is a comparative alloy No. 11 to Li
Is a composition to which is added. The properties in tensile strength, elongation and flexural strength are improved.

Comparative alloy no. 12 is Mg, Ni, S
n and Li are compositions that are equal to or more than the upper limit of the alloy of the present invention. The conductivity is extremely deteriorated and is not practical. Comparative alloy No. 1
No. 4 has good properties as described above, but the manufacturing process of casting → rolling → drawing → solution treatment → drawing → age hardening treatment is complicated, and accurate temperature control is required, and the manufacturing cost is high. Is very high.

Further, in order to evaluate the castability of the alloy of the present invention, the drawing characteristics were examined. Comparative alloy No. 1,
No. No. 2 is a Cu-Mg alloy, and the drawing properties were very poor, and drawing from 0.6 mmφ to 0.08 mmφ was impossible due to frequent breakage. Comparative alloy No. 7 is a Cu-Mg-Sn alloy, but because it does not contain Ni, very many disconnections occurred. No. 12 is the same component as that of the alloy of the present invention, but since the content is more than the upper limit of the alloy of the present invention, wire breakage frequently occurred in the fine wire machine. This is because, especially since the Mg content is as high as 0.9%, the wire drawing characteristics cannot be improved even if the Ni content is increased. The wire drawing characteristics of the other comparative alloys were good.

Next, a second embodiment of the present invention will be described. The alloys of the present invention shown in Table 2 1 to 9 and Comparative Example N
o. From the alloys Nos. 1 to 8, sample wires were obtained as follows. First, copper is melted under a graphite particle coating in a melting furnace maintained in an inert gas atmosphere, and then Mg, Sn and In are added in required amounts in the form of pure metals, respectively, to obtain a molten metal having a uniform composition. Was. This was continuously cast, and Table 2
A 20 mmφ cast rod having the composition shown in Table 1 was formed. Next, the obtained cast rod was cold-rolled, then drawn to 1 mmφ, and further electrically annealed by an electric resistance annealing machine to measure tensile strength, elongation, electrical conductivity, and repeated bending strength. In addition, in Comparative Example No. Cu-Fe-P-Mn-Si alloy No. 9 was prepared by dissolving copper under a graphite particle coating in a melting furnace maintained in an inert gas atmosphere, and then adding Fe, P, Mn, and Si in the form of a master alloy. Then a uniform molten metal was obtained. This was subjected to continuous casting to produce a 20 mmφ cast rod having the composition shown in Table 1. this,
Cold rolling and drawing were performed to obtain a 3.2 mmφ wire. This wire was heated in an inert gas atmosphere furnace at 900 ° C. for 1 hour and then water-cooled to perform a solution treatment. Thereafter, the wire was drawn to 1.0 mmφ and subjected to age hardening treatment in an inert gas atmosphere furnace at 470 ° C. for 6 hours, and the tensile strength, elongation, electric conductivity, and repeated bending strength were measured. The tensile strength, elongation, electrical conductivity and repetitive bending strength of this sample wire were measured according to a conventional test method, and the results are shown in Table 2. In Table 2, conductivity is%
In IACS, the tensile strength is expressed in Kg / mm ² , the elongation is expressed in%, and the repeated bending strength is expressed in number.

[0027]

[Table 2]

In the bending test, as in the case of the first embodiment, FIG.
The jig 1 shown in FIG.

Further, in order to evaluate the castability of the alloy of the present invention, the alloy No. of the present invention shown in Table 2 was evaluated. A wire drawing test of a sample wire rod made of an alloy having a composition of 1 to 9 was performed by drawing to a wire diameter of 0.08 mmφ. For this purpose, first, a 20 mmφ cast rod produced by continuous casting from the alloy of the present invention was cold-rolled to 9.5 mmφ.
A rough drawing of φ was obtained. This is drawn to 2.6mmφ using a large continuous wire drawing machine, and then from 2.6mmφ to 0.6mm using a small wire drawing machine.
Draw wire to φ, then use a fine wire machine to increase the diameter from 0.6mmφ to 0.08mm
The wire was drawn to φ. The number of breaks in the wire drawing process using a large wire drawing machine, a small wire drawing machine, and a fine wire drawing machine was counted, and the wire drawing characteristics were evaluated based on the number of times of wire breaking. In addition, the number of times of wire breakage in each wire drawing process is the number of times of wire breakage per 50 kg of wire material weight.

In the same manner as the sample wire of the alloy of the present invention, the conductivity, tensile strength, elongation,
The flexural strength and drawing characteristics were measured repeatedly, and the results are shown in Table 2. In the same manner as the sample wire of the alloy of the present invention, the electrical conductivity, tensile strength, elongation, repeated bending strength, and wire drawing characteristics of the obtained sample wire of the conventional alloy were measured, and the results are shown in Table 2. Further, as a reference example, a wire made of only hard copper was similarly manufactured, tested, and the results were displayed.

Hereinafter, the electrical conductivity, tensile strength, elongation, and repeated bending strength of the sample wire rods will be described.
9. Comparative alloy Nos. 1 to 9 will be compared and examined. The alloy of the present invention has a conventional Cu-Fe-P-Mn-Si conductivity.
Although it shows a value slightly lower than that of the alloy, it is a decrease that is not problematic in practical use, while the tensile strength, elongation and cyclic bending strength are lower than those of the Cu-Fe-P-Mn-Si alloy. It shows equal or better values.

The comparative alloys No. 1, No. 2 and No. 4
An alloy to which n was not added. The sample wire produced therefrom has substantially the same conductivity as the alloy of the present invention, but has a significantly reduced tensile strength. Comparative alloy No. 3 has a Sn content equal to or less than the lower limit of the Sn content defined in the present invention.
The elongation and the flexural strength are considerably lower than those of the alloy of the present invention. On the other hand, Comparative Alloy No. 5 is an alloy to which Sn was not added at all. The sample wire produced from this has significantly reduced elongation and repeated bending strength.

Comparative alloy No. 6 has a tensile strength, since Mg, Sn and In are not more than the lower limits of the contents specified in the present invention.
The elongation and the flexural strength are significantly reduced. On the other hand, in Comparative Alloy No. 7, since the Mg content is equal to or more than the upper limit of the content specified in the present invention, the conductivity is significantly lower than that of the alloy of the present invention. In Comparative Alloy No. 8, since the Sn content was equal to or more than the upper limit of the content specified in the present invention, the conductivity was significantly lower than that of the alloy of the present invention.

Next, in order to evaluate the castability of the alloy of the present invention, the drawing characteristics of the sample wire are examined. Invention alloy N
o. In Nos. 1 to 9, no disconnection occurred during wire drawing. This indicates that the alloy of the present invention has extremely good drawing properties. On the other hand, the comparative alloy is inferior to the alloy of the present invention in wire drawing characteristics as described below. First,
In Comparative Alloy Nos. 1 to 3, since the ratio of Mg: Sn was equal to or less than the lower limit of the range of the ratio specified in the present invention, disconnection occurred more frequently during drawing than in the alloy of the present invention. Since Comparative Alloy No. 5 is an alloy to which Sn was not added, wire breakage frequently occurred during wire drawing, and in particular, wire drawing from a wire diameter of 0.6 mmφ to 0.08 mmφ was broken immediately because it was broken immediately. It was impossible. Comparative alloy No. 7
Is that the addition amounts of Sn and In and the addition ratio of Mg: Sn are within the ranges specified in the present invention, but since the Mg content is equal to or more than the upper limit of the content specified in the present invention, the drawing property is It was lower than the invention alloy.

On the other hand, Comparative Alloy No. 4 had good wire drawing characteristics because the contents of Mg and Sn and the content ratio of Mg: Sn were within the ranges specified by the present invention. Comparative alloy No.
In No. 6, although the contents of Mg, Sn, and In were not more than the lower limits specified by the present invention, the content ratio of Mg: Sn was within the range specified by the present invention, so that the drawing properties were good. In Comparative Alloy No. 8, the Sn content and the Mg: Sn content ratio were equal to or higher than the upper limits specified in the present invention, but the drawing properties were good. Comparative alloy No. Cu-Fe-PM shown in 9
Both the n-Si alloy and the hard copper wire of the reference example have good wire drawing characteristics.

As described above, the alloy of the present invention is made of the conventional Cu
Although it can be manufactured by a much simpler manufacturing process than that of the -Fe-P-Mn-Si alloy, it has been confirmed that the alloy has the same characteristics. In other words, the alloy of the present invention is a copper alloy having relatively high conductivity and elongation, and excellent in mechanical properties such as tensile strength and repetitive bending strength and wire drawing properties. Fe-P
-It was confirmed that the copper alloy can be produced more economically than the Mn-Si alloy.

[0037]

As described above, the alloy according to the present invention has slightly lower conductivity than hard copper, but has the same tensile strength as hard copper, and has significantly improved elongation and flexibility. . In addition, the drawability is significantly improved as compared with conventional Cu-Mg alloys and Cu-Mg-Sn alloys, and the conductivity, tensile strength, elongation,
Excellent flexibility. Age hardening type Cu-Fe-PM
Although the conductivity is slightly lower than that of the n-Si alloy, it has the same or better characteristics in tensile strength, elongation and flexibility, and its manufacturing process is not as complicated as that of the age hardening type and is the same as pure copper. Low cost. As described above, first, the alloy according to the present invention firstly causes the conductivity to be reduced to a degree that is not harmful to practical use as compared with hard copper, but the tensile strength is equal to or higher than that of hard copper. In addition, elongation and flexibility are greatly increased as compared with hard copper.

[Brief description of the drawings]

FIGS. 1 (a), (b), (c) and (d) are explanatory views for explaining a bending test method of a wire rod.

[Explanation of symbols]

 1 jig for test 2 test material

──────────────────────────────────────────────────続 き Continued on the front page (72) Inventor Yasuhito Taki 2771 Ooka, Numazu-shi, Shizuoka Yazaki Electric Wire & Cable Co., Ltd. In-house (56) References JP-A-63-243239 (JP, A) JP-A-4-28838 (JP, A) Japanese Patent Publication No. 50-4179 (JP, B1) (58) Field surveyed (Int. Cl. ⁶ , DB name) C22C 9/00-9/10

Claims (2)

(57) [Claims] 1. Mg content of 0.1 to 0.5 wt% and Ni content of 0.1 to 0.5 wt%.
0.5 wt%, Sn: 0.1 to 0.5 wt%, Li: 0.02 to 0.2
A high-strength copper alloy for conductive use having excellent wire drawing characteristics, containing wt% and the balance substantially consisting of Cu. 2. Mg: 0.1 to 0.5 wt%, Sn: 0.15 to
0.75% by weight, 0.05 to 0.35% by weight of In, the balance substantially consisting of Cu, and the content ratio of Mg: Sn in the range of 1: 1.2 to 1.8. High-strength copper alloy for electrical conductivity with excellent wire drawing characteristics.