JPH11293431A - Method for producing ultrafine copper alloy wire - Google Patents

Abstract

[PROBLEMS] To provide a method for producing a copper alloy ultrafine wire having a wire diameter of 50 µm or less, which is excellent in drawability, strength, fatigue resistance and the like. SOLUTION: A copper alloy soft material (Cu-1.0-4.5 wt% Ag alloy, Cu-0.2-
1.5wt% Cr alloy, Cu-0.1 ~ 0.3wt% Zr alloy, Cu-0.2 ~ 1.5wt% Cr-0.1 ~ 0.3wt
% Zr alloy or Cu-0.3 to 4.0 wt% Ti alloy), which is subjected to cold working and, if necessary, intermediate annealing, and is a method for producing a copper alloy ultrafine wire having a wire diameter of 50 μm or less, The cold working rate from the copper alloy soft material is set to 99.999% or less, the cold working rate until the next intermediate annealing after the intermediate annealing other than the final intermediate annealing is set to 99.999% or less, and after the final intermediate annealing. To a cold working ratio of 80 to 99%.

Description

DETAILED DESCRIPTION OF THE INVENTION

[0001]

BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a method for producing an ultrafine copper alloy wire having a wire diameter of 50 .mu.m or less, which is excellent in drawability, strength, fatigue resistance and the like, and particularly suitable for winding.

[0002]

2. Description of the Related Art Ultrafine copper alloy wires used for windings and the like are required to have drawability, strength, fatigue resistance and the like. In particular, drawability is important because it greatly affects cost.
For such ultrafine copper alloy wires, conventionally, tough pitch copper, Sn-containing copper alloy, copper alloy containing 0.2% or less of Ag, and the like have been used. With the recent miniaturization of portable devices, ultrafine wires for windings are required to be reduced to 50 μm or less, and further from 30 μm to 20 μm, and strength and fatigue resistance are more important than before. It is becoming.

[0003]

However, when the diameter of the conventional ultrafine copper alloy wire is 50 μm or less, the wire becomes liable to be broken, causing a problem in productivity. Therefore, the present inventors have searched for various copper alloys having excellent cold workability, and for copper alloys containing 1% or more of Ag and Cu-Cr alloys, by selecting the processing conditions, a thin wire having a diameter of 20 μm or less is selected. The present inventors have found that the present invention can be realized, and have further advanced the research to complete the present invention. An object of the present invention is to provide a method for producing a copper alloy ultrafine wire having a wire diameter of 50 μm or less, which is excellent in drawability, strength, fatigue resistance and the like.

[0004]

According to the first aspect of the present invention,
Cold working of copper alloy soft material containing foreign phase such as crystallized material,
A method for producing a copper alloy ultrafine wire having a wire diameter of 50 μm or less, where intermediate annealing is performed as needed, wherein the cold working rate from the copper alloy soft material is set to 99.999% or less and the intermediate annealing is performed. , The cold working rate between the intermediate annealings is 9
This is a method for producing a copper alloy ultrafine wire, wherein the ultra-fine copper alloy wire is not more than 9.999% and the cold working ratio after the final intermediate annealing is 80 to 99%.

According to a second aspect of the present invention, the soft copper alloy material containing a heterogeneous phase such as a crystallized substance is Cu-1.0 to 4.5 wt% Ag.
Alloy, Cu-0.2 to 1.5 wt% Cr alloy, Cu-0.
1-0.3wt% Zr alloy, Cu-0.2-1.5wt% C
r-0.1 to 0.3 wt% Zr alloy or Cu-0.3
2. The alloy according to claim 1, wherein the alloy is Ti-4.0 wt%.
It is a manufacturing method of the copper alloy ultrafine wire of description.

According to a third aspect of the present invention, the intermediate annealing is performed for 300 hours.
The method for producing a copper alloy ultrafine wire according to claim 1 or 2, wherein the method is performed by holding at -550 ° C for 1 second to 30 minutes.

[0007]

BEST MODE FOR CARRYING OUT THE INVENTION The present invention is to provide a copper alloy soft material containing a heterogeneous phase such as a crystallized product by subjecting it to cold working at a predetermined working rate while performing intermediate annealing as necessary. It is a method of processing into an extra fine line. The hetero phase such as the crystallized substance also includes a precipitate. As the copper alloy soft material, C
u-1.0-4.5 wt% Ag alloy, Cu-0.2-1.
5wt% Cr alloy, Cu-0.1 ~ 0.3wt% Zr alloy,
Cu-0.2 ~ 1.5wt% Cr-0.1 ~ 0.3wt% Z
Examples include small diameter ingots such as r alloys or Cu-0.3 to 4.0 wt% Ti alloys, hot rolled materials (rough drawn wires), hot extruded materials, and annealed materials. The copper alloy soft material is cold-processed by rolling, groove roll rolling, drawing, wire drawing, or the like, and is processed into an ultrafine wire having a desired shape.

[0008] Each of the copper alloys has a different phase (eg, Ag particles, Cr particles, Zr.Cu compound particles,
Ti / Cu compound particles, etc.) are finely dispersed in the form of short fibers by cold working, and these dispersions finely and uniformly distribute dislocation cells formed in a copper alloy matrix during cold working. To improve the cold workability of each of the copper alloys. The reason for defining the alloy element amount of each of the copper alloys is that, below the lower limit, the dislocation cells are not finely and uniformly distributed because the amount of the crystallized substance is small, and the crystallized substance is significantly coarsened when the amount exceeds the upper limit. This is to cause disconnection.

As described above, the crystallized substance makes the dislocation cells fine and uniform, but on the other hand, as the cold working proceeds, the dislocation cells become extremely fine, where the dislocations are pinned and disconnection occurs. It will be easier.

Therefore, in the present invention, when the cold working rate from the copper alloy soft material exceeds 99.999%, intermediate annealing is performed to prevent disconnection. By the intermediate annealing, dislocations are thermally activated and dislocation cells are coarsened to improve cold workability. When the intermediate annealing is performed a plurality of times, the cold working rate during the intermediate annealing is set to 99.999% or less, similarly to the cold working rate from the copper alloy soft material. However, the cold working ratio after the final intermediate annealing is specified to be 80 to 99%. The reason is that if it is less than 80%, the strength required for the copper alloy ultrafine wire cannot be obtained, and if it exceeds 99%, the dislocation cell becomes finer and it becomes easy to break during coiling or the like. Note that Cu
The strength of the -Cr alloy, Cu-Zr alloy, and Cu-Ti alloy can be further improved by performing aging treatment after cold working.

As described above, when a cold-worked wire rod in which dislocation cells are finely formed is subjected to intermediate annealing, dislocations are thermally activated and dislocation cells are coarsened to improve cold workability.
When the annealing temperature is lower than 300 ° C., the effect of the intermediate annealing is not sufficiently obtained. When the temperature exceeds 550 ° C., the strength is significantly reduced by the annealing, and thereafter, sufficient strength cannot be obtained even by cold working. On the other hand, if the annealing time is less than 1 second, the time required for the dislocations to move thermally is insufficient. If the annealing time is more than 30 minutes, the effect of the intermediate annealing is saturated and energy costs are disadvantageous. Therefore, the intermediate annealing is performed at 300 to 550 ° C. for 1 second to 3 seconds.
It is desirable to apply for 0 minutes.

[0012]

The present invention will be described below in detail with reference to examples. (Example 1) Various copper alloys having a composition within the specified range of the present invention were cast into a rod-shaped ingot having a diameter of 10.8 mm by a horizontal continuous casting machine, the ingot was peeled to a diameter of 10 mm, and the cast after peeling was cast. The lump was drawn into a wire having a diameter of 0.10 mm or 0.05 mm. Next, 30 to 300 ° -550 ° C.
Annealing during running was performed under the condition of holding for 2 seconds, and then drawing was performed again to produce a copper alloy ultrafine wire having a diameter of 20 μm (0.02 mm).

(Example 2) Various copper alloys having the composition specified in the present invention were cast into a rod-shaped ingot having a diameter of 10.8 mm by a horizontal continuous casting machine, and the ingot was peeled to a diameter of 10 mm. The ingot after drawing is 0.10 mm diameter or 0.0
The wire had a diameter of 5 mm. Next, each wire was subjected to running annealing under the condition of holding at 580 ° C. or 280 ° C. for 30 seconds, and then was drawn again to produce a copper alloy ultrafine wire having a diameter of 20 μm.

(Comparative Example 1) Various copper alloys having the composition specified in the present invention were cast into a rod-shaped ingot having a diameter of 10.8 mm by a horizontal continuous casting machine, and the ingot was peeled to a diameter of 10 mm. After the ingot is drawn to 0.30mm diameter or 0.0
A wire having a diameter of 3 mm was used. Next, each wire was subjected to running annealing under the condition of maintaining the wire at 400 ° C. for 30 seconds, and thereafter was drawn again to produce a copper alloy ultrafine wire having a diameter of 20 μm.

(Comparative Example 2) Various copper alloys having the composition specified in the present invention were cast into a rod-shaped ingot having a diameter of 10.8 mm by a horizontal continuous casting machine, and the ingot was peeled to a diameter of 10 mm. The subsequent ingot was subjected to wire drawing to produce a copper alloy ultrafine wire having a diameter of 20 μm. No annealing was performed during the run.

Comparative Example 3 A copper alloy having a composition outside the specified range of the present invention was cast into a rod-shaped ingot having a diameter of 10.8 mm by a horizontal continuous casting machine, and the ingot was peeled to a diameter of 10 mm. 0.10mm diameter or 0.05mm by drawing ingot
It was a wire rod of a diameter. Next, each wire was subjected to running annealing at a temperature of 400 ° C. for 30 seconds, and then drawn again to produce a copper alloy ultrafine wire having a diameter of 20 μm.

With respect to each of the copper alloy ultrafine wires obtained in Examples 1 and 2 and Comparative Examples 1 to 3, the tensile strength, fatigue rupture characteristics,
The drawability was investigated. Fatigue rupture characteristics were expressed as the number of times until rupture when bending was repeated 90 degrees while applying a stress of 200 N / mm ² . One round trip was counted as one time. Drawability is 30
It was expressed as a value obtained by dividing the amount of elongation by the number of breaks when the wire was continuously drawn from μm to 20 μm. The analysis values of the alloy composition are shown in Table 1, and the results of the investigation are shown in Tables 2 to 5, respectively. Tables 2 to 5 also show drawing conditions and annealing conditions.

[0018]

[Table 1]

[0019]

[Table 2] (Note) # 10mm diameter-(99.99%)-> 0.1mm diameter-(96%)-> 0.02mm diameter 10mm diameter-(99.9975%)-> 0.05mm diameter-(84%)-> 0.02mm diameter Sample No.1 ~ 12 is Example 1.

[0020]

[Table 3] (Note) # 10mm diameter-(99.99%) → 0.1mm diameter (96%) → 0.02mm diameter 10mm diameter-(99.9975%) → 0.05mm diameter (84%) → 0.02mm diameter Sample Nos. 13 to 20 Example 1 and Sample Nos. 21 to 24 are Example 2.

[0021]

[Table 4] (Note) # 10mm diameter-(99.91%)-> 0.3mm diameter-(99.56%)-> 0.02mm diameter 10mm diameter-(99.9991%)-> 0.03mm diameter-(55.56%)-> 0.02mm diameter

[0022]

[Table 5] (Note) # 10mm diameter− (99.9996%) −−−−−−−− →→ 0.02mm diameter (no intermediate annealing) 10mm diameter −− (99.99%) → 0.1mm diameter (96%) → 0.02mm diameter 10mm diameter − (99.9975%) → 0.05mm diameter (84%) → 0.02mm diameter

As is clear from Tables 2 to 5, Sample Nos. 1 to 24 of the present invention all have a drawability of 3.0 kg or more per disconnection, and have strength and fatigue resistance characteristics. (Tensile strength 800 N / mm ² or more, fatigue fracture frequency 10 ⁷ times or more). On the other hand, Nos. 25 to 36 of Comparative Example 1 and Nos. 37 to 42 of Comparative Example 2 had the cold working ratios outside the range of the present invention. In any case, the drawability was low, and these were not suitable for practical use. In addition, those having a cold working ratio of more than 99% after the final intermediate annealing (No. 25, 27, 29, 31, 33, 35) have poor stiffness and poor coilability (not shown). Those with a working ratio of less than 80% (Nos. 26, 28, 30, 32, 34, 36) were inferior in tensile strength and fatigue fracture characteristics. No.4 out of alloy elements with insufficient amount
5 to 50 were inferior in at least one of tensile strength and fatigue rupture characteristics.

[0024]

As described above, the copper alloy used in the present invention is excellent in cold workability because the crystallized substances and the like contained in the copper alloy finely and uniformly distribute the dislocation cells. Since the copper alloy is cold-worked under predetermined conditions while annealing as needed, an ultrafine wire of 50 μm or less can be favorably manufactured. Furthermore, the ultrafine wire obtained by the present invention is excellent in strength and fatigue resistance. Therefore, the present invention has a remarkable effect when applied to the manufacture of windings and the like.

Continued on the front page (51) Int.Cl. ⁶ Identification symbol FI C22F 1/00 630 C22F 1/00 630A 630G 630K 685 685Z 686 686 686Z 691 691C 691B 694 694A

Claims (3)

[Claims] 1. A copper alloy soft material containing a heterogeneous phase such as a crystallized material is cold-worked and subjected to intermediate annealing if necessary.
A method for producing a copper alloy ultrafine wire having a thickness of not more than μm, wherein the cold working rate from the copper alloy soft material is not more than 99.999% and the intermediate annealing is performed. A method for producing a copper alloy ultrafine wire, characterized in that the working ratio is 99.999% or less, and the cold working ratio after the final intermediate annealing is 80 to 99%. 2. A copper alloy soft material containing a heterogeneous phase such as a crystallized substance is a Cu-1.0-4.5 wt% Ag alloy, a Cu-0.2-
1.5wt% Cr alloy, Cu-0.1 ~ 0.3wt% Zr alloy, Cu-0.2 ~ 1.5wt% Cr-0.1 ~ 0.3wt
2. The method for producing a copper alloy ultrafine wire according to claim 1, wherein the alloy is a% Zr alloy or a Cu-0.3 to 4.0 wt% Ti alloy. 3. 3. The intermediate annealing is performed at 300 to 550 ° C. for 1 second to 3 hours.
3. The method according to claim 1, wherein the treatment is carried out for 0 minute.
The method for producing a copper alloy ultrafine wire according to the above.