JPS62133050A - Manufacture of high strength and high conductivity copper-base alloy - Google Patents

Abstract

PURPOSE:To manufacture a high strength and high conductivity copper-base alloy excellent in mechanical strength and electric conductivity, by subjecting a Cu-base alloy containing specific amounts of Ti and Sn or further small amounts of other specific elements to solution heat treatment, ageing treatment, cold rolling, and heat treatment. CONSTITUTION:The Cu-base alloy in which 0.1-5.0wt% Ti and 0.1-5.0wt% Sn are added to Cu or further 0.005-2wt%, in total, of 1 or >=2 kinds among specific amounts of P, Al, Zn, Ni, Si, Pb, Be, Fe, Mn, Mg, Cr, Co, and other elements are added is refined. An ingot of this Cu-base alloy is heated to 880 deg.C and hot-rolled into a plate, and the plate is subjected to facing and then heated at 880 deg.C for 30min and water-quenched to undergo solution heat treatment. Successively, the above plate is subjected to ageing treatment at 200-700 deg.C for 10sec-10hr and to cold rolling at >=10% draft and, finally, the cold-rolled sheet is subjected to heat treatment at 200-700 deg.C for 10sec-10hr.

Description

DETAILED DESCRIPTION OF THE INVENTION ([Object 1]) The present invention relates to a method for producing a high-strength, high-conductivity copper nor-alloy having excellent mechanical strength and good electrical conductivity.

(Prior Art and Problems) High-strength copper alloys currently used for high-grade precision springs include beryllium copper alloys and titanium copper alloys. Although beryllium steel alloy has a high tensile strength of 90-140 kg/mm2 and a good electrical conductivity of 20-25% lAC3, it is very expensive because it contains about 2% beryllium, and beryllium-11 is a highly toxic substance. Second, this beryllium-copper alloy has the disadvantage that it becomes brittle at temperatures above 250° C., resulting in deterioration of the alloy. Furthermore, titanium-copper alloy has the advantage of being superior to Veriwau 11 copper alloy in terms of spring properties, heat resistance, and abrasion resistance, and has approximately the same mechanical strength and is less expensive. It has the major drawback of being extremely inferior.

For this reason, it has been proposed to further add Sn as a third element to the titanium-copper alloy in order to maintain its mechanical strength and obtain good electrical conductivity. However, even if tin-containing titanium-copper alloys are subjected to ordinary solution treatment, aging treatment, or cold working and aging treatment, the tensile strength remains at only 80 to 05 kg/mm. In order to use it as an alternative alloy, it was necessary to further improve its mechanical strength.

(Structure of the Invention) The present invention has been made in view of the above points, and it improves the mechanical strength while maintaining the good electrical conductivity of the tin-containing titanium-copper alloy, and solves the economic efficiency and toxicity problems of the beryllium-copper alloy. The object of the present invention is to provide a method for manufacturing a six-force highly conductive copper-based alloy having various conditions suitable as a material for high-grade precision springs.

The present invention has a T"i of 0.1 to 5.0 st1%, 0.1
Copper-based alloy containing ~5.0% Sn, with the remainder consisting of CIJ and unavoidable impurities, and 0.1~5.0% Sn
Contains 0% Ti, 0.1-5°Owt, % Sn, and further contains 0.005-1. kt, %P, 0.00
5-0.1wt. % Al, 0.005-1. owt
,% Zn.

0.005-0.1wt. %Ni, 0.005-1
．． 0wt. % Si.

0.005-0.5w and 1% Pb, 0.005-1
．． owt, %Be.

0.005-1. , 0wt. % Fe, 0.005-
1.0tyt, %Mn.

0.005-0.1wt. % Mg,, 0.005~
0.1wt. %Cr.

0.005-0.1wt. %Co, 0.005-1
．． '0wt. % Zr.

0.005-0.1tit, %Δs, 0.005~
0.1wt. % of A gro, 005-0.1wt.
% Cd, 0.005-0.1 wt. % In.

0,005-0,1wt,%Sb,0.0
05-1. Owl:,% of 1゛e.

0.005-0.1wt. %Ge, 0.005~0
．． 1wt. After solution treatment of a copper-based alloy containing one or more of Hf in a total amount of 0.005 to 2.0 t1% and whose row portions are made of Cu and unavoidable impurities, the material temperature is 200 to 200%. After performing aging treatment at 700°C for 10 seconds to 10 hours, followed by cold rolling of 10% or more, heat treatment is performed at a material temperature of 200 to 700°C for 10 seconds to 10 hours to improve mechanical strength and The present invention relates to a method for manufacturing a high-strength, high-conductivity steel-based alloy with improved conductivity.

(Effect) As a result, when manufactured by the method of the present invention, tensile strength and electrical conductivity could be significantly improved at the same time.

(Detailed Description of the Invention) Next, the reasons for limiting the alloy components and manufacturing method of the present invention will be explained.

Ti content is 0.1 to 5. (The reason for using ht, % is 0
．． If 1 oath is less than 0%, the expected strength cannot be obtained, and on the other hand, if 5
．． 0wt. This is because if it exceeds %, no improvement in electrical conductivity can be expected.

The Sn content is 0.1 to 5. (The reason for using ht, % is 0
．． If it is less than 1iit, 3, the expected electrical conductivity cannot be obtained, and on the other hand, if it exceeds 5.0% or 0%, the excess Sn that cannot be dissolved even after heat treatment will form intermetallic compounds with Ti and precipitate. This is because, as coarse extruded particles, they significantly reduce the strength of the alloy.

As a secondary force, the predetermined amount of P + A I + Z
n + N J + Si, Pb, Be, Fe,
Cr, Mg, Zr, Go, Zr.

Δs, Af;, Cd, Te, Sb, 'I
'e, Ge, ■ (the total amount of one or more selected from the group consisting of f is 0.005-2.0i, % fil 4!, 0.005wt, % not i+]tF is This is because the expected high strength cannot be obtained by adding the subcomponent, and if it exceeds 2.0 wt.%, the electrical conductivity decreases significantly, and furthermore, the solderability and hot workability deteriorate.

The solution-treated material is aged at a material temperature of 200 to 700°C for 10 seconds to 10 hours, and then the workability is 10.
Add more than % cold rolling. The aging temperature is set to 2 (l 0~
The reason for setting it to 700°C is that it is less than 200°C or 70°C.
The expected strength and conductivity cannot be obtained at temperatures exceeding 0°C, and the reason why the aging temperature is set to 10 seconds to 10 hours is that the effect of aging treatment is not observed at temperatures below 10 seconds.1
This is because if the time exceeds 0 hours, the strength decreases significantly due to the over-aging phenomenon. Furthermore, the reason why the degree of cold working is set to 10% or more is that if the degree of cold working is less than 10%, the strength and conductivity obtained by the heat treatment in the next step cannot be improved as expected.

When the material that has been aged and cold-rolled as described above is heat-treated again at a material temperature of 200 to 700°C for 10 seconds to 10 hours, the tensile strength of the material is significantly increased by this heat treatment. In this case, at temperatures below 200°C or above 700°C, the expected strength and electrocardiographic rate cannot be obtained. Furthermore, if the heat treatment time is less than 10 seconds, no effect of the heat treatment will be observed, and if it exceeds 10 hours, the strength will be significantly reduced due to over-aging phenomenon, so it must be avoided. Normally: Sufficient effect can be obtained in about 30 seconds to 1 hour.

(Example) Next, an example will be described.

Ingots 1 to 1 with various component compositions according to the present invention shown in Table 1 were melted and cast in a high-frequency melting R'+: furnace using electrolytic copper or oxygen-free copper as raw materials. This inkotsu 1~
was heated at 880℃ for 1 hour and then hot rolled to a thickness of 5.
It was made into a board of n++n. After facing, heat at 880'C for 30 minutes and water quench the solution-treated material at 450'C for 1.
Aging treatment was performed for 5 hours. Further, it was cold rolled into a J (f 0.5 mm' plate) and heat treated at 450° C. for 3 minutes.

As for the evaluation of the sample prepared in this way, the strength was evaluated by a tensile test, ffi gas conductivity, and electrical conductivity (%IAC5). In addition, the solderability was determined using the vertical dipping method.
They were immersed in a solder bath (Sn60%-Pb40%) at 0+5°C for 5 seconds, and the state of solder wetting was evaluated on a three-grade scale by LI visual inspection. These results and hot workability are shown in Table 1 along with comparative alloys.

In Table 1, Comparative Examples 16 and 17 were treated after solution treatment.
This is a material that has been cold rolled and then aged.

As shown in Table 1, the manufacturing method of the alloy according to the present invention has resulted in an alloy suitable as a material for high-grade precision springs, which has strength and conductivity comparable to that of 5-beryllium copper alloy, and also exhibits good workability and solderability. Become.

Margin below Table 1 ○: Good Δ: ”）T extension ×: Bad

Claims (2)

[Claims] (1) 0.1-5.0wt. % Ti, 0.1-5.0
wt. After solution treatment of a copper-based alloy containing % Sn and the balance consisting of Cu and unavoidable impurities, the material temperature was 200-7.
After performing aging treatment at 00°C for 10 seconds to 10 hours, followed by cold rolling of 10% or more, the material temperature was further increased to 2.
A method for producing a high-strength, high-conductivity copper-based alloy that is heat-treated at 00 to 700°C for 10 seconds to 10 hours to improve mechanical strength and conductivity. (2) 0.1-5.0wt. % Ti, 0.1-5.0
wt. % of Sn, and further contains 0.005 to 1.0 w
t. % P, 0.005-1.0wt. % Al, 0.
005~1.0wt. % Zn, 0.005~1.0w
t% Ni, 0.005-1.0wt. % Si, 0.
005~0.5wt. % Pb, 0.005-1.0w
t. % Be, 0.005-1.0wt. 0.00 of %
5-1.0wt. % Cr, 0.005-1.0wt.
% Co, 0.005-1.0 wt. % Zr, 0.0
05-0.1wt. % As, 0.005-1.0wt
．． % Ag, 0.005-1.0 wt. % Cd, 0.
005~1.0wt. %In, 0.005~0.1w
t. % Sb, 0.005-1.0wt. %Te, 0
．． 005~1.0wt. %Ge, 0.005-1.0
wt. % of Hf in a total amount of 0.005 to 2.0 wt. %, with the balance consisting of Cu and unavoidable impurities. After solution treatment, an aging treatment is performed at a material temperature of 200 to 700°C for 10 seconds to 10 hours, followed by cold rolling of 10% or more. After that, a heat treatment is performed at a material temperature of 200 to 700° C. for 10 seconds to 10 hours to improve mechanical strength and conductivity.