CN103273271A - Production process of high-strength high-conductivity copper-chromium-zirconium alloy long wire - Google Patents
Production process of high-strength high-conductivity copper-chromium-zirconium alloy long wire Download PDFInfo
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Abstract
The invention relates to the field of high-strength high-conductivity copper-chromium-zirconium alloy, in particular to a production process of a high-strength high-conductivity copper-chromium-zirconium alloy long wire. The process includes the steps of subjecting copper-chromium-zirconium alloy rods (wires) to flash butt welding, subjecting welds and matrix grains to continuous extrusion and refining, and performing cold deforming and ageing. The process has the advantages that mechanical properties of copper-chromium-zirconium alloy matrix and welds are improved, mechanical properties and electrical properties of the welds are close to those of the matrix, the problem that the performance of the copper-chromium-zirconium alloy decreases after welding is solved, and the copper-chromium-zirconium alloy long wire with fine performance is produced. The production process is applicable to high-strength high-conductivity copper-chromium-zirconium alloy, and the diameter of the copper-chromium-zirconium alloy rods (wires) for connection ranges from 10mm to 40mm.
Description
Technical field
The present invention relates to high-strength highly-conductive Cu-Cr-Zr alloy field, specifically a kind of preparation technology of high-strength highly-conductive Cu-Cr-Zr alloy long lead.
Background technology
Cu-Cr-Zr alloy is a kind of precipitation strength type copper alloy, owing to have high intensity and favorable conductive, heat conductivility and antioxygenic property, and anti-softening temperature height, advantage such as wearability is good and be widely used in electronics and mechanical field, and be expected to as novel electric railway contact wire material.Along with different field to the further developing of Cu-Cr-Zr alloy demand, the welding research work of Cu-Cr-Zr alloy seems particularly important and urgent.Especially the applied environment that length is had higher requirements for contact wire and electric winding displacement etc. because Cu-Cr-Zr alloy needs vacuum metling, is difficult to utilize up-drawing method etc. to carry out the production of continuous rod (line) material, satisfy length requirement and then must adopt welding procedure.Yet, since the Cu-Cr-Zr alloy thermal conductivity factor greatly and shortcoming such as easy oxidation cause alloy welding poor performance, the Cu-Cr-Zr alloy performance significantly reduces after common welding procedure is handled.
Summary of the invention
The preparation technology who the purpose of this invention is to provide a kind of high-strength highly-conductive Cu-Cr-Zr alloy long lead overcomes the shortcoming of this alloy mechanical properties decrease after welding, makes it satisfy the requirement of service condition.
To achieve these goals, technical scheme of the present invention is:
A kind of preparation technology of high-strength highly-conductive Cu-Cr-Zr alloy long lead, concrete steps are as follows:
(1) adopt flash-butt welding that Cu-Cr-Zr alloy bar or wire rod are carried out soldering;
(2) solution treatment 0.5-2h between 940-980 ℃, shrend is to room temperature;
(3) alloy bar material or wire rod carry out continuously extruded processing, and extrusion ratio is 0.6-1.2, and water-cooled is to room temperature;
(4) after continuously extruded, alloy bar material or wire rod are that the cold drawing of 60-80% is handled through working modulus;
(5) alloy bar material or wire rod are at 400-500 ℃ of Ageing Treatment 1-3h.
The preparation technology of described high-strength highly-conductive Cu-Cr-Zr alloy long lead, the Cu-Cr-Zr alloy ingot casting utilizes hot extrusion to prepare CuCrZr alloy bar material or wire rod, and extrusion temperature 800-900 ℃, temperature retention time 1-3h.
The preparation technology of described high-strength highly-conductive Cu-Cr-Zr alloy long lead, the technological parameter of flash-butt welding is: flash time 1-3s; Flashing speed 10-15mm/s; Upsetting force: 150-200MPa; Upset allowance 10-15mm.
The preparation technology of described high-strength highly-conductive Cu-Cr-Zr alloy long lead, the chemical composition of Cu-Cr-Zr alloy are 0＜Cr≤0.60%; 0＜Zr≤0.20%; The Cu surplus.
The preparation technology of described high-strength highly-conductive Cu-Cr-Zr alloy long lead, being used for the Cu-Cr-Zr alloy bar of connection or the diameter range of wire rod is 10-40mm.
The preparation technology of described high-strength highly-conductive Cu-Cr-Zr alloy long lead, after the continuously extruded processing, the remarkable refinement of Cu-Cr-Zr alloy matrix and weld grain, grain size range is 0.5-5 μ m.
The preparation technology of described high-strength highly-conductive Cu-Cr-Zr alloy long lead, after cold drawing distortion and Ageing Treatment, weld properties and matrix approach, electric conductivity does not obviously reduce, the yield strength scope is 460-500MPa, the tensile strength scope is 500-530MPa, conductance 70-80%IACS.
The preparation technology of described high-strength highly-conductive Cu-Cr-Zr alloy long lead, in continuously extruded process, squeegee roller rotating speed control at 4-8rpm, 400-450 ℃ of mould initial temperature, the temperature of Cu-Cr-Zr alloy at the mould outlet place is 450-600 ℃.
The invention has the advantages that:
1, the present invention make Cu-Cr-Zr alloy weld properties and matrix approach, and conductance does not significantly reduce by adopting continuously extruded and cold deformation Ageing Treatment.
2, the present invention handles by, cold deformation continuously extruded to carrying out after the Cu-Cr-Zr alloy welding and timeliness, obtains alloy bar (line) material that Weld Performance and matrix approach, and can solve the problem of this high-strength highly-conductive Cu-Cr-Zr alloy welding back performance reduction.
3, the present invention carries out continuously extruded processing behind Cu-Cr-Zr alloy flash of light electric resistance welding, after the continuously extruded processing, the remarkable refinement of Cu-Cr-Zr alloy matrix and weld grain has been alleviated the stress that the segregation of micron precipitated phase causes behind the electric resistance welding and has been concentrated, thereby improves the mechanical property of Cu-Cr-Zr alloy weld seam.
4, Cu-Cr-Zr alloy of the present invention carries out the cold deformation Ageing Treatment after continuously extruded, make that undecomposed chromium and zirconium atom are further separated out in the continuously extruded process, improve mechanics and the electric property of alloy by precipitation strength, after cold deformation and Ageing Treatment, weld properties and matrix approach, electric conductivity does not obviously reduce, thereby satisfies the requirement of its service condition.
5, the condition that the present invention was suitable for is the high-strength highly-conductive Cu-Cr-Zr alloy, and the diameter range that is used for Cu-Cr-Zr alloy rod (line) material of connection is 10-40mm, and the length of prepared Cu-Cr-Zr alloy long lead can be unrestricted.
Description of drawings
Fig. 1 high-strength highly-conductive Cu-Cr-Zr alloy of the present invention connects process chart.
Fig. 2 (a)-(d) is weld seam microstructure picture after the Cu-Cr-Zr alloy flash-butt welding.Wherein, Fig. 2 (a) weld seam macrostructure; Fig. 2 (b) weld seam center microstructure; Fig. 2 (c) transition region microstructure; Fig. 2 (d) matrix microstructure.
Fig. 3 (a)-(b) distributes for EPMA result shows transition region Cr element.Wherein, Fig. 3 (a) is the transition region metallographic structure; Fig. 3 (b) distributes with the Cr element of Fig. 3 (a) correspondence position.
Fig. 4 (a)-(d) is respectively the continuously extruded back of Cu-Cr-Zr alloy weld seam microstructure picture.Wherein, Fig. 4 (a) weld seam macrostructure; Fig. 4 (b) weld seam center microstructure; Fig. 4 (c) transition region microstructure; Fig. 4 (d) matrix microstructure.
The specific embodiment
Embodiment 1
Adopt raw material such as fine copper, copper chromium intermediate alloy and pure zirconium to carry out vacuum metling, alloy composition sees Table 1.
The chemical composition of table 1 alloy (wt.%)
| Alloy | Cr | Zr | Cu |
| Cu-0.36Cr-0.12Zr | 0.36 | 0.15 | Surplus |
Concrete production technology such as Fig. 1, the practical operation step is as follows:
(1) ingot casting utilizes hot extrusion to prepare CuCrZr alloy bar (line) material, and extrusion temperature 800-900 ℃, in the temperature retention time 1-3h(present embodiment, 850 ℃ of extrusion temperatures, time 2h);
(2) adopt flash-butt welding that alloy bar (line) material is welded, the technological parameter of flash-butt welding is: flash time 1-3s; Flashing speed 10-15mm/s; Upsetting force: 150-200MPa; In the upset allowance 10-15mm(present embodiment, flash time 2s; Flashing speed 12mm/s; Upsetting force: 180MPa; Upset allowance 12mm);
(3) between 940-980 ℃ in the solution treatment 0.5-2h(present embodiment, 960 ℃ of solid solution temperatures, time 1h), shrend is to room temperature;
(4) alloy bar (line) material carries out continuously extruded processing, and extrusion ratio is in the 0.6-1.2(present embodiment, and extrusion ratio is 1), water-cooled is to room temperature;
Undertaken in the continuously extruded process by continuous extrusion apparatus, squeegee roller rotating speed control at 4rpm, 420 ℃ of mould initial temperatures, the temperature of Cu-Cr-Zr alloy at the mould outlet place is about 500 ℃.
(5) after continuously extruded, alloy bar (line) material is 75% through working modulus for the 60-80%(present embodiment) cold drawing handle; Wherein, working modulus=(the cold drawing starting section is long-pending-cold drawing after sectional area)/the cold drawing starting section is long-pending;
(6) alloy bar (line) material is in 400-500 ℃ of Ageing Treatment 1-3h(present embodiment, 450 ℃ of aging temperatures, time 2h), obtain the Cu-Cr-Zr alloy lead.
Fig. 2 (a)-(d) is commissure microscopic structure after the Cu-Cr-Zr alloy flash-butt welding, and wherein (a) is weld seam macrostructure, (b), (c) and (d) respectively corresponding weld seam center, transition region and matrix.As can be seen from the figure, the weld seam center is equiaxed grain structure, and about crystallite dimension 50 μ m, this is to be caused recrystallization and formed by flash-butt welding.Transition region is the mixed grain structure that CRYSTALLITE SIZES is mixed, and finds gathering partially of the micron precipitated phase that caused by burning at regional area.Matrix grain is of a size of about 200 μ m, and can observe flourishing annealing contraction crystalline substance.Fig. 3 (a)-(b) is the electron probe result that transition region Cr element distributes, and the Cr element is in the obvious enrichment in crystal boundary place as can be seen, and this tissue has very adverse influence to the Weld Performance of Cu-Cr-Zr alloy.
Cu-Cr-Zr alloy after the flash-butt welding is through solution treatment, passes through continuously extrudedly again, and the gained alloy structure is shown in Fig. 4 (a)-(d).Wherein (a) is weld seam macrostructure, (b), (c) and (d) respectively corresponding weld seam center, transition region and matrix.Dotted line shows weld profile among Fig. 4 (a), and continuously extruded back weld seam encircles along continuously extruded direction as can be seen.Fig. 4 (b) and Fig. 4 (d) show that originally thick crystal grain is through continuously extruded being refined to about 0.5-5 μ m.Fig. 4 (c) is the transition region of continuously extruded back weld seam, still can see the micron order precipitated phase from figure, and the recrystal grain that these precipitated phases are of a size of about 10 μ m surrounds.Though Ju precipitated phase can cause that in the cold deformation process stress is concentrated partially, but because the inner dislocation density of recrystal grain is lower, the stress that meeting alleviation precipitated phase causes in deformation process is concentrated, and then reduces the adverse effect that welding process causes alloy property.
Carry out cold deformation and timeliness after Cu-Cr-Zr alloy is continuously extruded and handle, table 2 provides this state alloy mechanical property and electrical performance testing result.As can be seen, handle through cold deformation and timeliness, the surrender of Cu-Cr-Zr alloy weld seam and tensile strength and matrix are close, and conductance does not significantly reduce.
Adopt this invention technology that the high-strength highly-conductive Cu-Cr-Zr alloy is connected, can satisfy the requirement of its service condition so that gold alloy solder stitches mechanical property, electric conductivity is close with matrix.
Table 2 Cu-Cr-Zr alloy weld seam and matrix mechanics and electric property contrast
| ? | Yield strength/MPa | Tensile strength/MPa | Conductance/IACS% |
| Weld seam | 478.2 | 512.8 | 72.8 |
| Matrix | 490.2 | 517.6 | 77.6 |
Embodiment 2
Adopt raw material such as fine copper, copper chromium intermediate alloy and pure zirconium to carry out vacuum metling, alloy composition sees Table 3.
The chemical composition of table 3 alloy (wt.%)
| Alloy | Cr | Zr | Cu |
| Cu-0.16Cr-0.12Zr | 0.16 | 0.12 | Surplus |
Concrete steps are as follows:
(1) ingot casting utilizes hot extrusion to prepare CuCrZr alloy bar (line) material, 840 ℃ of extrusion temperatures, temperature retention time 3h;
(2) adopt flash-butt welding that alloy bar (line) material is welded, the technological parameter of flash-butt welding is: flash time 3s; Flashing speed 10mm/s; Upsetting force: 150MPa; Upset allowance 10mm;
(3) at 950 ℃ of solution treatment 2h, shrend is to room temperature;
(4) alloy bar (line) material carries out continuously extruded processing, and extrusion ratio is 0.64, and water-cooled is to room temperature;
Undertaken in the continuously extruded process by continuous extrusion apparatus, squeegee roller rotating speed control at 6rpm, 450 ℃ of mould initial temperatures, the temperature of Cu-Cr-Zr alloy at the mould outlet place is about 550 ℃.
(5) after continuously extruded, alloy bar (line) material is that 65% cold drawing is handled through working modulus;
(6) alloy bar (line) material obtains the Cu-Cr-Zr alloy lead at 475 ℃ of Ageing Treatment 1h.
Commissure microscopic structure after the Cu-Cr-Zr alloy flash-butt welding, weld seam center are equiaxed grain structure, and about crystallite dimension 50 μ m, this is to be caused recrystallization and formed by flash-butt welding.Transition region is the mixed grain structure that CRYSTALLITE SIZES is mixed, and finds gathering partially of the micron precipitated phase that caused by burning at regional area.Matrix grain is of a size of about 200 μ m, and can observe flourishing annealing contraction crystalline substance.
Cu-Cr-Zr alloy after the flash-butt welding is through solution treatment, passes through continuously extrudedly again, and the gained alloy structure has the micron order precipitated phase, and the recrystal grain that these precipitated phases are of a size of about 10 μ m surrounds.Though Ju precipitated phase can cause that in the cold deformation process stress is concentrated partially, but because the inner dislocation density of recrystal grain is lower, the stress that meeting alleviation precipitated phase causes in deformation process is concentrated, and then reduces the adverse effect that welding process causes alloy property.
Carry out cold deformation and timeliness after Cu-Cr-Zr alloy is continuously extruded and handle, table 4 provides this state alloy mechanical property and electrical performance testing result.As can be seen, handle through cold deformation and timeliness, the surrender of Cu-Cr-Zr alloy weld seam and tensile strength and matrix are close, and conductance does not significantly reduce.
Adopt this invention technology that the high-strength highly-conductive Cu-Cr-Zr alloy is connected, can satisfy the requirement of its service condition so that gold alloy solder stitches mechanical property, electric conductivity is close with matrix.
Table 4 Cu-Cr-Zr alloy weld seam and matrix mechanics and electric property contrast
| ? | Yield strength/MPa | Tensile strength/MPa | Conductance/IACS% |
| Weld seam | 472 | 509 | 73.6 |
| Matrix | 481 | 518 | 76.8 |
Embodiment result shows, the present invention improves Cu-Cr-Zr alloy rod (line) material welding procedure, by carrying out continuously extruded processing refinement weld seam and matrix grain behind the electric resistance welding that Cu-Cr-Zr alloy rod (line) material is glistened, carry out cold deformation and Ageing Treatment afterwards, this technology can improve the mechanical property of Cu-Cr-Zr alloy matrix and weld seam simultaneously, and make weld properties and electric property near matrix, solve the problem that alloy welding back performance reduces.
Claims (8)
1. the preparation technology of a high-strength highly-conductive Cu-Cr-Zr alloy long lead is characterized in that concrete steps are as follows:
(1) adopt flash-butt welding that Cu-Cr-Zr alloy bar or wire rod are carried out soldering;
(2) solution treatment 0.5-2h between 940-980 ℃, shrend is to room temperature;
(3) alloy bar material or wire rod carry out continuously extruded processing, and extrusion ratio is 0.6-1.2, and water-cooled is to room temperature;
(4) after continuously extruded, alloy bar material or wire rod are that the cold drawing of 60-80% is handled through working modulus;
(5) alloy bar material or wire rod are at 400-500 ℃ of Ageing Treatment 1-3h.
2. according to the preparation technology of the described high-strength highly-conductive Cu-Cr-Zr alloy of claim 1 long lead, it is characterized in that the Cu-Cr-Zr alloy ingot casting utilizes hot extrusion to prepare CuCrZr alloy bar material or wire rod, extrusion temperature 800-900 ℃, temperature retention time 1-3h.
3. according to the preparation technology of the described high-strength highly-conductive Cu-Cr-Zr alloy of claim 1 long lead, it is characterized in that the technological parameter of flash-butt welding is: flash time 1-3s; Flashing speed 10-15mm/s; Upsetting force: 150-200MPa; Upset allowance 10-15mm.
4. according to the preparation technology of the described high-strength highly-conductive Cu-Cr-Zr alloy of claim 1 long lead, it is characterized in that the chemical composition of Cu-Cr-Zr alloy is 0＜Cr≤0.60%; 0＜Zr≤0.20%; The Cu surplus.
5. according to the preparation technology of the described high-strength highly-conductive Cu-Cr-Zr alloy of claim 1 long lead, it is characterized in that being used for the Cu-Cr-Zr alloy bar of connection or the diameter range of wire rod is 10-40mm.
6. according to the preparation technology of the described high-strength highly-conductive Cu-Cr-Zr alloy of claim 1 long lead, it is characterized in that, after the continuously extruded processing, the remarkable refinement of Cu-Cr-Zr alloy matrix and weld grain, grain size range is 0.5-5 μ m.
7. according to the preparation technology of the described high-strength highly-conductive Cu-Cr-Zr alloy of claim 1 long lead, it is characterized in that, after cold drawing distortion and Ageing Treatment, weld properties and matrix approach, electric conductivity does not obviously reduce, the yield strength scope is 460-500MPa, and the tensile strength scope is 500-530MPa, conductance 70-80%IACS.
8. according to the preparation technology of the described high-strength highly-conductive Cu-Cr-Zr alloy of claim 1 long lead, it is characterized in that, in continuously extruded process, squeegee roller rotating speed control at 4-8rpm, 400-450 ℃ of mould initial temperature, the temperature of Cu-Cr-Zr alloy at the mould outlet place is 450-600 ℃.
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| CN105714133A (en) * | 2016-03-08 | 2016-06-29 | 广州有色金属研究院 | Preparation method for Cu-Cr-Zr-Mg alloy bar |
| CN106826114A (en) * | 2017-01-18 | 2017-06-13 | 抚顺特殊钢股份有限公司 | A kind of manufacturing process of GH3625 alloys cold-drawn material |
| CN111763846A (en) * | 2020-06-16 | 2020-10-13 | 陕西斯瑞新材料股份有限公司 | Method for manufacturing Cu-Cr-Zr alloy stranded wire for electrified railway |
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| CN106826114B (en) * | 2017-01-18 | 2020-12-04 | 抚顺特殊钢股份有限公司 | Manufacturing process of GH3625 alloy cold-drawn material |
| CN111763846A (en) * | 2020-06-16 | 2020-10-13 | 陕西斯瑞新材料股份有限公司 | Method for manufacturing Cu-Cr-Zr alloy stranded wire for electrified railway |
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