CN115961227B - High-strength high-plastic conductive copper alloy material and preparation method thereof - Google Patents
High-strength high-plastic conductive copper alloy material and preparation method thereof Download PDFInfo
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- 239000000956 alloy Substances 0.000 title claims abstract description 163
- 229910000881 Cu alloy Inorganic materials 0.000 title claims abstract description 34
- 238000002360 preparation method Methods 0.000 title claims abstract description 16
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 144
- 238000001556 precipitation Methods 0.000 claims abstract description 38
- 230000032683 aging Effects 0.000 claims abstract description 31
- 229910052759 nickel Inorganic materials 0.000 claims abstract description 6
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 claims description 56
- 238000000034 method Methods 0.000 claims description 54
- 238000005096 rolling process Methods 0.000 claims description 48
- 238000010438 heat treatment Methods 0.000 claims description 47
- 238000005097 cold rolling Methods 0.000 claims description 43
- 238000011282 treatment Methods 0.000 claims description 32
- 239000007788 liquid Substances 0.000 claims description 28
- 229910052757 nitrogen Inorganic materials 0.000 claims description 28
- 230000001360 synchronised effect Effects 0.000 claims description 25
- 238000005266 casting Methods 0.000 claims description 18
- 238000010791 quenching Methods 0.000 claims description 18
- 230000000171 quenching effect Effects 0.000 claims description 18
- 229910000831 Steel Inorganic materials 0.000 claims description 12
- 239000010959 steel Substances 0.000 claims description 12
- 238000001816 cooling Methods 0.000 claims description 11
- 239000002994 raw material Substances 0.000 claims description 11
- 239000002244 precipitate Substances 0.000 claims description 10
- 238000005098 hot rolling Methods 0.000 claims description 9
- 239000010949 copper Substances 0.000 claims description 8
- 238000003723 Smelting Methods 0.000 claims description 7
- 238000003756 stirring Methods 0.000 claims description 7
- 230000009467 reduction Effects 0.000 claims description 6
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims description 5
- 238000002844 melting Methods 0.000 claims description 3
- 230000008018 melting Effects 0.000 claims description 3
- 229910052804 chromium Inorganic materials 0.000 claims description 2
- 238000010309 melting process Methods 0.000 claims description 2
- 239000000126 substance Substances 0.000 claims description 2
- 229910052726 zirconium Inorganic materials 0.000 claims description 2
- 238000009826 distribution Methods 0.000 abstract description 18
- 229910017876 Cu—Ni—Si Inorganic materials 0.000 abstract description 11
- 229910019819 Cr—Si Inorganic materials 0.000 abstract description 5
- 229910018098 Ni-Si Inorganic materials 0.000 abstract description 5
- 229910018529 Ni—Si Inorganic materials 0.000 abstract description 5
- 230000001105 regulatory effect Effects 0.000 abstract description 4
- 230000035755 proliferation Effects 0.000 abstract description 2
- 230000008569 process Effects 0.000 description 39
- 239000000243 solution Substances 0.000 description 21
- 230000033228 biological regulation Effects 0.000 description 14
- 239000000463 material Substances 0.000 description 14
- 238000013461 design Methods 0.000 description 10
- 239000011159 matrix material Substances 0.000 description 9
- 230000015572 biosynthetic process Effects 0.000 description 7
- 230000001276 controlling effect Effects 0.000 description 7
- 230000000694 effects Effects 0.000 description 6
- 239000006104 solid solution Substances 0.000 description 6
- 229910052802 copper Inorganic materials 0.000 description 5
- 239000013078 crystal Substances 0.000 description 5
- 238000000265 homogenisation Methods 0.000 description 5
- 230000002195 synergetic effect Effects 0.000 description 5
- 238000005516 engineering process Methods 0.000 description 4
- 230000006698 induction Effects 0.000 description 4
- 238000011160 research Methods 0.000 description 4
- 238000005728 strengthening Methods 0.000 description 4
- 230000009286 beneficial effect Effects 0.000 description 3
- 238000012545 processing Methods 0.000 description 3
- 229910008458 Si—Cr Inorganic materials 0.000 description 2
- 239000011362 coarse particle Substances 0.000 description 2
- 230000002079 cooperative effect Effects 0.000 description 2
- 230000000875 corresponding effect Effects 0.000 description 2
- 230000001351 cycling effect Effects 0.000 description 2
- 238000011161 development Methods 0.000 description 2
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- 238000004519 manufacturing process Methods 0.000 description 2
- 230000001737 promoting effect Effects 0.000 description 2
- 230000000930 thermomechanical effect Effects 0.000 description 2
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 1
- 229910017824 Cu—Fe—P Inorganic materials 0.000 description 1
- 238000005219 brazing Methods 0.000 description 1
- 238000012512 characterization method Methods 0.000 description 1
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Classifications
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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02E—REDUCTION OF GREENHOUSE GAS [GHG] EMISSIONS, RELATED TO ENERGY GENERATION, TRANSMISSION OR DISTRIBUTION
- Y02E60/00—Enabling technologies; Technologies with a potential or indirect contribution to GHG emissions mitigation
- Y02E60/10—Energy storage using batteries
Abstract
The invention belongs to the technical field of copper alloy, and particularly relates to a high-strength high-plastic conductive copper alloy material and a preparation method thereof. Not only can effectively promote the rapid proliferation of dislocation, but also can further promote the rapid precipitation of fine precipitated phases. Meanwhile, the rapid precipitation of the precipitated phase at a lower aging temperature can be effectively promoted, so that the coarsening of the precipitated phase can be effectively avoided, and the morphology and distribution of various precipitated phases can be reasonably regulated and controlled. The invention changes the Ni, si content and Ni/Si ratio of Cu-Ni-Si alloy, and finally obviously improves the strength and conductivity of the alloy based on the dual-phase collaborative precipitation of Ni-Si and Cr-Si.
Description
Technical Field
The invention belongs to the technical field of copper alloy, and particularly relates to a high-strength high-plastic conductive copper alloy material and a preparation method thereof.
Background
With the rapid development of electronic information technology in recent years, particularly, the semiconductor industry with integrated circuits as a core is further developed as a pillar industry of modern information technology, so that the requirements on material varieties and performances are also increased and severe. The integrated circuit mainly comprises a chip and a lead frame, wherein the lead frame material plays a role in transmitting signals, protecting internal components and radiating outwards, and is a key component of the integrated circuit. At present, more than 80% of the lead frame materials of the integrated circuits are formed by high-precision copper alloy erosion. As integrated circuits move toward larger scale and more functionality, higher performance requirements are also placed on lead frame materials. The original performance index (tensile strength > 600MPa and conductivity > 50%) of the lead frame material can not meet the use requirement, and needs to be further improved. In addition, in addition to further improvement in strength and conductivity properties, there are also higher demands for heat conductive properties, moldability, stress relaxation resistance, and the like.
At present, copper-based lead frame materials used at home and abroad are various, but are mainly represented by Cu-Fe-P alloy and Cu-Ni-Si alloy. The Cu-Ni-Si alloy is used as a typical aging strengthening alloy, and can obtain higher strength, electric conductivity and heat conductivity through aging precipitation of a nano-scale delta-Ni 2 Si phase, so that the Cu-Ni-Si alloy is a key raw material for manufacturing a lead frame terminal of a large-scale integrated circuit. In order to meet the higher performance requirements of the next-generation copper alloy lead frame materials, researchers generally adopt methods such as microalloying and optimizing deformation heat treatment processes to promote alloy precipitation phases and regulate and control the sizes, shapes, structures and distribution of the precipitation phases, and further, the comprehensive performances such as strength, conductivity and the like of Cu-Ni-Si series alloys are expected to be remarkably improved.
Studies have shown that the precipitation of Ni 2 Si precipitate phase can be promoted by adding a proper amount of Zn, so that not only can the precipitation strengthening effect be increased, but also the brazing interface performance can be effectively improved. And the addition of trace P element can effectively inhibit coarsening of a precipitated phase, and the precipitation of Ni 3 P phase can also improve the strength and the conductivity of the alloy. In addition, researches show that the addition of a proper amount of Co can form a (Ni, co) 2 Si composite precipitate phase through the synergistic effect of Ni and Si, so that amplitude modulation decomposition in the aging process can be effectively inhibited, the aging precipitation of a second phase can be obviously accelerated, and finally the strength of the Cu-Ni-Si alloy is greatly improved. On the basis of component design and microalloying regulation, a great deal of research has been carried out on improving the comprehensive performance of the alloy through the thermomechanical treatment, and finally, the strength of the alloy can be greatly improved through the synergistic effect of deformation strengthening and precipitation strengthening. However, most of the research on the thermomechanical treatment process is focused on optimizing ageing process parameters to date, or the tensile strength of the alloy is further improved by cold rolling deformation of the ageing alloy, but the prepared hard alloy has lower plasticity and other problems. As a whole, there has been little attention paid to cold rolling deformation processes (including deformation amount, deformation temperature, deformation mode, and the like) of cu—ni—si based alloys. For example, cold rolling deformation of different degrees often causes significant differences in dislocation density and dislocation distribution in the alloy matrix, thereby directly affecting nucleation and growth rate of alloy precipitation phases. In addition, the mutual collocation mode and sequence of different cold rolling deformation and aging processes have obvious influence on precipitation behavior, and finally the structure and performance of the alloy are obviously influenced, but the aspects lack systematic research.
Disclosure of Invention
Aiming at the problems existing in the prior art, the invention provides a high-strength high-plasticity conductive copper alloy material and a preparation method thereof, and the high-strength high-plasticity conductive copper alloy material is prepared by improving the processing technology of the copper alloy material, and specifically comprises the following contents:
the preparation method of the high-strength high-plastic conductive copper alloy material comprises the following steps:
(1) Vacuum smelting to prepare copper alloy cast ingot;
(2) Homogenizing heat treatment at 930-980 deg.c for 2-6 hr;
(3) Hot rolling deformation, wherein the initial rolling temperature is 750-820 ℃, and the deformation is 70-80%;
(4) Repeatedly circulating ultra-low temperature deep cold rolling, wherein the deformation temperature is between-80 ℃ and-190 ℃, and the deformation amount is 45-60%;
(5) Carrying out solution quenching treatment, wherein the solution temperature is 950-980 ℃, the solution time is 1-3h, and the quenching mode is water quenching;
(6) Pre-ageing at 430-480 deg.c for 1-3 hr;
(7) Repeatedly cycling ultra-low temperature deep cold rolling deformation, wherein the deformation temperature is between-80 ℃ and-190 ℃, and the deformation amount is between 70 and 80 percent;
(8) Artificially aging at 400-550deg.C for 3-12 hr;
(9) Repeatedly cycling ultra-low temperature deep cold rolling deformation, wherein the deformation temperature is between 80 ℃ below zero and 190 ℃ below zero, and the deformation amount is between 40 and 65 percent;
(10) The low-temperature heat treatment regulates the cooperative precipitation behavior of the precipitate phase, the aging temperature is 330-380 ℃ and the time is 10-20h.
Preferably, the copper alloy cast ingot comprises the following chemical components in percentage by mass: 3.0 to 4.5 weight percent of Ni, 0.65 to 0.92 weight percent of Si, 0.005 to 0.15 weight percent of Cr, less than or equal to 0.05 weight percent of B, less than or equal to 0.05 weight percent of Zr, and the balance of Cu. Specifically, the Ni content may be 3.0wt%, 3.25wt%, 3.5wt%, 3.75wt%, 4.0wt%, 4.25wt%, or 4.5wt%, etc.; si content may be 0.65wt%, 0.70wt%, 0.75wt%, 0.80wt%, 0.85wt%, 0.90wt%, 0.92wt%, etc.; cr content may be 0.005wt％、0.008wt％、0.010wt％、0.012wt％、0.014wt％、0.05wt％、0.075wt％、0.09wt％、0.1wt％、0.12wt％、0.14wt％、0.15wt％ or the like; the content of B may be specifically 0, 0.0001wt%, 0.001wt%, 0.01wt%, 0.025wt%, 0.05wt%, etc.; the Zr content may be specifically 0, 0.0001wt%, 0.001wt%, 0.01wt%, 0.025wt%, 0.05wt% and the like.
Preferably, the vacuum melting process in step (1) comprises: adding alloy raw materials according to the proportion, heating and melting the alloy raw materials after the vacuum degree is less than 0.1Pa, preserving heat for 3-7min at 1200-1300 ℃ after the alloy raw materials are completely melted, stirring the solution for 30-90s, starting casting when the solution temperature is stable at 1230-1260 ℃, and controlling the casting speed. Specifically, the temperature can be 1200 ℃, 1220 ℃, 1250 ℃, 1270 ℃, 1290 ℃, 1300 ℃ and the like, and the temperature can be 3min, 4min, 5min, 6min, 7min and the like; the stirring time may be 30s, 40s, 50s, 70s, 90s, etc.
Preferably, the homogenizing heat treatment in the step (2) comprises the following steps: the temperature is 930-970 ℃, the time is 2-5h, the heating rate is more than 100 ℃/min, and the cooling rate is more than 120 ℃/min. Specifically, the temperature may be 930, 940, 950, 960, 965, 970 ℃, etc., the time may be 2 hours, 3 hours, 4 hours, 4.5 hours, 5 hours, etc., the heating rate may be 101 ℃/min, 105 ℃/min, 110 ℃/min, 120 ℃/min, 150 ℃/min, 200 ℃/min, etc., and the cooling rate may be 121 ℃/min, 125 ℃/min, 130 ℃/min, 140 ℃/min, 150 ℃/min, 200 ℃/min, etc.
Preferably, in the step (3), the hot rolling deformation start rolling temperature is 750-810 ℃, the finish rolling temperature is higher than 500 ℃, the total deformation is 72-80%, the pass reduction is 5-15%, and the deformation mode is unidirectional rolling. Specifically, the initial rolling temperature may be 750 ℃, 760 ℃, 770 ℃, 780 ℃, 790 ℃, 800 ℃, 810 ℃, and the like, the final rolling temperature may be 520 ℃, 550 ℃, 580 ℃, 600 ℃, 610 ℃, and the like, the total deformation may be 72%, 73%, 75%, 78%, 79%, 80%, and the like, and the pass reduction may be 5%, 7%, 9%, 11%, 13%, 15%, and the like.
Preferably, the multi-cycle ultra-low temperature deep cold rolling process in the step (4) is as follows: firstly, placing the material in a liquid nitrogen tank for more than 20min (such as 30min, 35min, 40min, 50min, 60min and the like), and then performing ultralow-temperature deformation, wherein the deformation temperature is between-100 ℃ and-190 ℃ (such as-100 ℃, -110 ℃, -120 ℃, -150 ℃, -180 ℃, -190 ℃ and the like), and the deformation amount is between 5 and 15% (such as 5%, 7%, 9%, 11%, 13%, 15% and the like), and the deformation mode is as follows: synchronous rolling, wherein the pass deformation is 3-10% (e.g. 3%, 5%, 7%, 9%, 10%, etc.); then placing the ultra-low temperature rolled plate into a liquid nitrogen tank to be cooled for 2-10min (such as 2min, 4min, 6min, 8min, 10min and the like), deforming at the ultra-low temperature at the deformation temperature of-100 ℃ to-190 ℃ (such as-100 ℃, -110 ℃, -120 ℃, -150 ℃, -180 ℃, -190 ℃ and the like), wherein the deformation amount is 5% -15% (such as 5%, 7%, 9%, 11%, 13%, 15% and the like), and the deformation mode is as follows: synchronous rolling, pass deformation: 3% -10% (e.g., 3%, 5%, 7%, 9%, 10%, etc.); the above-mentioned ultra-low temperature deformation cycle is repeated for more than 5 times, so that the total deformation of the alloy sheet material can reach 45% -55% (for example 45%, 47%, 49%, 51%, 53%, 55% etc.).
Preferably, the solution hardening treatment in step (5) is performed at a temperature of 950-980 ℃ (e.g., 950 ℃, 955 ℃, 960 ℃, 970 ℃, 975 ℃, 980 ℃, etc.) for a time of 1-3 hours (e.g., 1h, 1.5h, 2h, 2.5h, 3h, etc.), at a heating rate of greater than 20 ℃/sec (e.g., 21 ℃/sec, 25 ℃/sec, 30 ℃/sec, 40 ℃/sec, 80 ℃/sec, 100 ℃/sec, etc.), and at a hardening rate of greater than 120 ℃/sec (e.g., 121 ℃/sec, 130 ℃/sec, 140 ℃/sec, 180 ℃/sec, 200 ℃/sec, etc.).
Preferably, the multi-cycle ultra-low temperature deep cold rolling deformation process in the step (7) is as follows: firstly, placing the material in a liquid nitrogen tank for more than 20min (such as 30min, 35min, 40min, 50min, 60min and the like), and then performing ultralow-temperature deformation, wherein the deformation temperature is between-100 ℃ and-190 ℃ (such as-100 ℃, -110 ℃, -120 ℃, -150 ℃, -180 ℃, -190 ℃ and the like), and the deformation amount is between 5 and 15% (such as 5%, 7%, 9%, 11%, 13%, 15% and the like), and the deformation mode is as follows: synchronous rolling, wherein the pass deformation is 3-10% (e.g. 3%, 5%, 7%, 9%, 10%, etc.); then placing the ultra-low temperature rolled plate into a liquid nitrogen tank to be cooled for 2-10min (such as 2min, 4min, 6min, 8min, 10min and the like), deforming at the ultra-low temperature at the deformation temperature of-100 ℃ to-190 ℃ (such as-100 ℃, -110 ℃, -120 ℃, -150 ℃, -180 ℃, -190 ℃ and the like), wherein the deformation amount is 5% -15% (such as 5%, 7%, 9%, 11%, 13%, 15% and the like), and the deformation mode is as follows: synchronous rolling, pass deformation: 3% -10% (e.g., 3%, 5%, 7%, 9%, 10%, etc.); the above ultra-low temperature deformation cycle is repeated for more than 6 times, so that the total deformation of the alloy sheet material reaches 70-80% (such as 70%, 72%, 75%, 78%, 80%, etc.).
Preferably, the process of the multi-cycle ultra-low temperature deep cold rolling deformation in the step (9) is as follows: firstly, placing the material in a liquid nitrogen tank for more than 20min (such as 30min, 35min, 40min, 50min, 60min and the like), and then performing ultralow-temperature deformation, wherein the deformation temperature is between-100 ℃ and-190 ℃ (such as-100 ℃, -110 ℃, -120 ℃, -150 ℃, -180 ℃, -190 ℃ and the like), and the deformation amount is between 5 and 15% (such as 5%, 7%, 9%, 11%, 13%, 15% and the like), and the deformation mode is as follows: synchronous rolling, wherein the pass deformation is 3-10% (e.g. 3%, 5%, 7%, 9%, 10%, etc.); then placing the ultra-low temperature rolled plate into a liquid nitrogen tank to be cooled for 2-10min (such as 2min, 4min, 6min, 8min, 10min and the like), deforming at the ultra-low temperature at the deformation temperature of-100 ℃ to-190 ℃ (such as-100 ℃, -110 ℃, -120 ℃, -150 ℃, -180 ℃, -190 ℃ and the like), wherein the deformation amount is 5% -15% (such as 5%, 7%, 9%, 11%, 13%, 15% and the like), and the deformation mode is as follows: synchronous rolling, pass deformation: 3% -10% (e.g., 3%, 5%, 7%, 9%, 10%, etc.); the above-mentioned ultra-low temperature deformation cycle is repeated for more than 5 times, so that the total deformation of the alloy sheet material can reach 45% -65% (for example, 45%, 47%, 49%, 51%, 53%, 55%, 60%, 65%, etc.).
The high-strength high-plasticity conductive copper alloy material prepared by the method disclosed by the invention.
The invention has the beneficial effects that:
(1) The preparation method of the copper alloy material disclosed by the invention adopts repeated circulating ultralow-temperature deformation, not only can effectively promote dislocation to rapidly proliferate to form a large number of tiny dislocation cells or sub-crystal tissues, but also can interact with tiny precipitates to uniformly disperse and distribute in an alloy matrix, and further promote rapid precipitation of tiny precipitate phases. Meanwhile, the strain energy storage of the alloy matrix can be obviously increased after ultralow-temperature deformation, and the rapid precipitation of the precipitated phase at a lower aging temperature can be effectively promoted, so that the coarsening of the precipitated phase can be effectively avoided, and the morphology and distribution of various precipitated phases can be reasonably regulated and controlled.
(2) In order to ensure that the copper alloy material can have excellent plastic deformation capability while obviously improving alloy strength and conductivity, the method disclosed by the invention further provides a novel process based on the cooperative regulation and control of ultra-low temperature deep cold rolling deformation and multistage variable temperature heat treatment, and the novel process can be used for separating out multi-scale and multi-type precipitated phases in an alloy matrix at first, so that tissue evolution can be influenced by cooperative action in a hot working process, and dislocation cell distribution characteristics can be influenced by cooperative action in the ultra-low temperature deep cold rolling process. The reason is that the pinning effect of coarse and fine particles on dislocation is different in the deformation process, and is more different in the deep cold rolling deformation process, which inevitably leads to different dislocation cell forms and sizes formed by the pinned dislocation, and the dislocation annihilation degree is also greatly different. The reasonable regulation and control can necessarily form multi-size multi-type dislocation cells or sub-crystal tissues, namely, the dislocation quantity density distributed in the dislocation cells or sub-crystal tissues has certain difference, and the dislocation quantity density has a high concentration area (hard micro-area) and a low concentration area (soft micro-area). The formation of the structural characteristics can necessarily increase the coordinated deformation capability among alloy tissues, and finally, the novel Cu-Ni-Si-Cr alloy which is developed based on the component design and the novel hot working process regulation and control of special tissues can necessarily have high strength and high conductivity and also have high plasticity.
(3) Besides improving the preparation process of the copper alloy, the invention optimally designs the components of the copper alloy material, changes the Ni content, the Si content and the Ni/Si ratio of the Cu-Ni-Si alloy, optimizes the precipitation behavior of the alloy, can effectively promote the rapid precipitation of Ni-Si precipitation phases by adding a proper amount of solute element Cr, and can further act with Si element to precipitate Cr-Si precipitation phases, and finally obviously improves the strength and the conductivity of the alloy based on the dual-phase collaborative precipitation of Ni-Si and Cr-Si.
Drawings
FIG. 1 is a process flow diagram of a method for preparing a copper alloy according to the present disclosure;
FIG. 2 is a graph showing the distribution of the aged hardness of the 1# and 3# alloys in example 1 at 400 ℃ C./8 h after the heat treatment;
FIG. 3 is a graph showing the distribution of the aged hardness of the 1# and 3# alloys of example 1 at 450 ℃ C./8 h after heat treatment;
FIG. 4 is a graph showing the distribution of the aged hardness of the 1# and 3# alloys of example 1 at 500 ℃/4 hours after the heat treatment;
FIG. 5 is a graph showing the hardness distribution of the 1# and 3# alloys of example 2 after heat treatment at 400 ℃ C./8h+50% deep cold rolling deformation;
FIG. 6 is a graph showing the hardness distribution of the 1# and 3# alloys of example 2 after heat treatment at 450 ℃ C./8h+50% deep cold rolling deformation;
FIG. 7 is a graph showing the hardness distribution of the 1# and 3# alloys of example 2 after 500 ℃ C./4h+50% deep cold rolling deformation;
FIG. 8 shows a TEM microstructure of example 3 after 500 ℃/4h+50% deep cold rolling deformation+350 ℃/16 aging after heat treatment of the 3# alloy.
Detailed Description
The invention will be described in detail below with reference to the drawings and the detailed description. The embodiments shown below do not limit the inventive content described in the claims in any way. The whole contents of the constitution shown in the following examples are not limited to the solution of the invention described in the claims.
The invention is further supplemented and described below in connection with the specific embodiments and the accompanying figures 1-6.
The preparation method of the alloy comprises the following steps: alloy preparation, alloy ingot casting preparation by vacuum smelting, homogenization heat treatment, hot rolling deformation, multiple-cycle ultra-low temperature deep cold rolling, solution treatment, water quenching treatment, pre-aging treatment, multiple-cycle ultra-low temperature deep cold rolling deformation, artificial aging, multiple-cycle ultra-low temperature deep cold rolling deformation, low temperature heat treatment regulation and control of precipitation phase collaborative precipitation behavior, dislocation cell or sub-crystal structure morphology and distribution can be controlled, morphology, structure and distribution characteristics of multiple-scale and multiple-type precipitation phases can be effectively regulated, and finally the developed copper alloy has high strength, high plasticity and high conductivity (shown in figure 1).
The raw materials respectively adopt 99.9wt percent of electrolytic high-purity Cu, ni, si, cu-10wt percent Cr intermediate alloy and the like. Firstly preparing alloy, placing the alloy in an intermediate frequency induction smelting furnace, heating the alloy after the vacuum degree is less than 0.1Pa, directly heating the alloy with high power to ensure that the solution is completely melted and the temperature is 1200-1300 ℃, preserving the heat for 3-7min, then stirring the solution with high power for 30-90 s, then starting casting when the temperature of the solution is stable at about 1250 ℃, and controlling the casting speed to avoid shrinkage cavity generation as much as possible; then carrying out homogenization treatment (the temperature is 930-980 ℃ and the time is 2-6 h) on the alloy cast ingot, and carrying out hot working multi-process cooperative regulation and control, wherein the specific treatment process is as follows: hot rolling deformation (initial rolling temperature 750-820 ℃, deformation 70-80%), multiple cycle ultra-low temperature deep cold rolling (deformation temperature: 80 ℃ to 190 ℃, deformation 45-60%), solution treatment (temperature: 950-980 ℃, time: 1-3 h), water quenching treatment (quenching mode: water quenching), pre-aging treatment (temperature: 430-480 ℃, time: 1-3 h), multiple cycle ultra-low temperature deep cold rolling deformation (deformation temperature: 80 ℃ to 190 ℃, deformation 70-80%), artificial aging (aging temperature: 400-550 ℃, time: 3-12 h), multiple cycle ultra-low temperature deep cold rolling deformation (deformation temperature: 80 ℃ to 190 ℃, deformation 40-65%), low temperature heat treatment controlling precipitate phase collaborative precipitation behavior (aging temperature: 330-380 ℃, time, 10-20 h). And finally, measuring microhardness, conductivity and tensile property of the alloy in different states and characterizing the microstructure of the alloy in typical states. Specific examples are as follows:
TABLE 1 implementation of the inventive alloy chemistry
| Alloy numbering | Ni(wt％) | Si(wt％) | Cr(wt％) | B(wt％) | Zr(wt％) | Cu(wt％) |
| 1# | 3.2 | 0.7 | ≤0.005 | ≤0.05 | ≤0.05 | Bal. |
| 2# | 3.2 | 0.7 | 0.05 | ≤0.05 | ≤0.05 | Bal. |
| 3# | 3.2 | 0.7 | 0.1 | ≤0.05 | ≤0.05 | Bal. |
| 4# | 4.0 | 0.8 | 0.12 | ≤0.05 | ≤0.05 | Bal. |
| 5# | 4.2 | 0.9 | 0.15 | ≤0.05 | ≤0.05 | Bal. |
Example 1
According to the component design value of the alloy 1# -5#, firstly, casting the alloy 1# and the alloy 3#, wherein the raw materials respectively adopt 99.9 weight percent of electrolytic high-purity Cu, ni, si, cu-10 weight percent Cr intermediate alloy and the like during casting. Firstly preparing alloy, placing the alloy in an intermediate frequency induction smelting furnace, heating the alloy after the vacuum degree is less than 0.1Pa, directly heating the alloy with high power to ensure that the solution is completely melted and the temperature is 1200-1300 ℃, preserving the heat for 3-7min, then stirring the solution with high power for 30-90 s, then starting casting when the temperature of the solution is stable at about 1250 ℃, and controlling the casting speed to avoid shrinkage cavity generation as much as possible; then carrying out homogenization treatment (the temperature is 930-970 ℃, the time is 2-5h, the heating rate is more than 100 ℃/min, the cooling rate is more than 120 ℃/min) on the alloy cast ingot, and carrying out hot working multi-process cooperative regulation and control, wherein the specific treatment process is as follows: firstly, hot rolling deformation is carried out on the steel plate, the initial rolling temperature is 750-810 ℃, the final rolling temperature is higher than 500 ℃, the total deformation is 72-80%, and the pass reduction is as follows: 5% -15%, the deformation mode: unidirectional rolling; then carrying out multiple-cycle ultralow-temperature deep cold rolling, wherein the low-temperature deformation cycle times are more than 5 times, firstly placing the steel plate in a liquid nitrogen tank for more than 20min, and then carrying out ultralow-temperature deformation, wherein the deformation temperature is as follows: -100-190 ℃, deformation: 5% -15%, the deformation mode: synchronous rolling, wherein the pass deformation is 3-10%; then the ultra-low temperature rolled plate is put into a liquid nitrogen tank to be cooled for 2-10min, and the deformation temperature is as follows: -100-190 ℃, deformation: 5% -15%, the deformation mode: synchronous rolling, pass deformation: 3-10%, repeating the above process to finally enable the total deformation of the alloy plate to reach 45-55%; then carrying out solid solution treatment, quenching and pre-ageing treatment, wherein the solid solution treatment temperature is as follows: 950-980 ℃, time: 1-3h, heating rate: greater than 20 ℃/sec; quenching rate is greater than 120 ℃/s, pre-ageing treatment temperature: 430-475 ℃ and the time is as follows: 1-2.5h; then, carrying out multiple times of circulation ultralow temperature deep cold rolling deformation, wherein the times of ultralow temperature deformation circulation is more than 6 times, firstly placing the steel wire rope in a liquid nitrogen tank for more than 20 minutes, and then carrying out ultralow temperature deformation, wherein the deformation temperature is as follows: -100-190 ℃, deformation: 5% -15%, the deformation mode: synchronously rolling, wherein the pass deformation is 3-10%, and then placing the ultra-low temperature rolled plate into a liquid nitrogen tank for cooling for 2-10min, wherein the deformation temperature is as follows: -100-190 ℃, deformation: 5% -15%, the deformation mode: synchronous rolling, pass deformation: 3-10%, repeating the above process to finally ensure that the total deformation of the alloy plate reaches 70-80%; and then carrying out different artificial aging heat treatments on the deep cold-rolled sheet, namely 400 ℃/8h,450 ℃/8h and 500 ℃/4h. Finally, typical aged alloys were subjected to microhardness, electrical conductivity and tensile properties characterization as shown in tables 2 and 3, and in figures 2,3 and 4.
Example 2
According to the component design value of the alloy 1# -5#, firstly, casting the alloy 1# and the alloy 3#, wherein the raw materials respectively adopt 99.9 weight percent of electrolytic high-purity Cu, ni, si, cu-10 weight percent Cr intermediate alloy and the like during casting. Firstly preparing alloy, placing the alloy in an intermediate frequency induction smelting furnace, heating the alloy after the vacuum degree is less than 0.1Pa, directly heating the alloy with high power to ensure that the solution is completely melted and the temperature is 1200-1300 ℃, preserving the heat for 3-7min, then stirring the solution with high power for 30-90 s, then starting casting when the temperature of the solution is stable at about 1250 ℃, and controlling the casting speed to avoid shrinkage cavity generation as much as possible; then carrying out homogenization treatment (the temperature is 930-970 ℃, the time is 2-5h, the heating rate is more than 100 ℃/min, the cooling rate is more than 120 ℃/min) on the alloy cast ingot, and carrying out hot working multi-process cooperative regulation and control, wherein the specific treatment process is as follows: firstly, hot rolling deformation is carried out on the steel plate, the initial rolling temperature is 750-810 ℃, the final rolling temperature is higher than 500 ℃, the total deformation is 72-80%, and the pass reduction is as follows: 5% -15%, the deformation mode: unidirectional rolling; then carrying out multiple-cycle ultralow-temperature deep cold rolling, wherein the low-temperature deformation cycle times are more than 5 times, firstly placing the steel plate in a liquid nitrogen tank for more than 20min, and then carrying out ultralow-temperature deformation, wherein the deformation temperature is as follows: -100-190 ℃, deformation: 5% -15%, the deformation mode: synchronous rolling, wherein the pass deformation is 3-10%; then the ultra-low temperature rolled plate is put into a liquid nitrogen tank to be cooled for 2-10min, and the deformation temperature is as follows: -100-190 ℃, deformation: 5% -15%, the deformation mode: synchronous rolling, pass deformation: 3-10%, repeating the above process to finally enable the total deformation of the alloy plate to reach 45-55%; then carrying out solid solution treatment, quenching and pre-ageing treatment, wherein the solid solution treatment temperature is as follows: 950-980 ℃, time: 1-3h, heating rate: greater than 20 ℃/sec; quenching rate is greater than 120 ℃/s, pre-ageing treatment temperature: 430-475 ℃ and the time is as follows: 1-2.5h; then, carrying out multiple times of circulation ultralow temperature deep cold rolling deformation, wherein the times of ultralow temperature deformation circulation is more than 6 times, firstly placing the steel wire rope in a liquid nitrogen tank for more than 20 minutes, and then carrying out ultralow temperature deformation, wherein the deformation temperature is as follows: -100-190 ℃, deformation: 5% -15%, the deformation mode: synchronously rolling, wherein the pass deformation is 3-10%, and then placing the ultra-low temperature rolled plate into a liquid nitrogen tank for cooling for 2-10min, wherein the deformation temperature is as follows: -100-190 ℃, deformation: 5% -15%, the deformation mode: synchronous rolling, pass deformation: 3-10%, repeating the above process to finally ensure that the total deformation of the alloy plate reaches 70-80%; then carrying out different artificial aging heat treatments on the deep cold-rolled sheet, namely 400 ℃/8h,450 ℃/8h and 500 ℃/4h; and then carrying out multiple-cycle ultralow-temperature deep cold rolling deformation on the heat-treated plate, wherein the multiple-cycle ultralow-temperature deformation cycle times are more than 6 times, firstly placing the plate in a liquid nitrogen tank for more than 20min, and then carrying out ultralow-temperature deformation at the deformation temperature: -100-190 ℃, deformation: 5% -15%, the deformation mode: synchronous rolling, wherein the pass deformation is 3-10%; then placing the ultra-low temperature rolled plate into a liquid nitrogen tank for cooling for 2-10min, wherein the deformation temperature is as follows: -100-190 ℃, deformation: 5% -15%, the deformation mode: synchronous rolling, pass deformation: 3-10%; repeating the above process to finally lead the total deformation of the alloy plate to reach 45-65%. Finally, microhardness, electrical conductivity and tensile properties were measured on typical ultra-low temperature deep cold rolled wrought alloys, as shown in tables 2 and 3, and in figures 5,6 and 7.
Example 3
According to the component design value of the alloy 1# -5#, firstly the alloy 3# is melted and cast, and the raw materials respectively adopt 99.9 weight percent of electrolytic high-purity Cu, ni, si, cu-10 weight percent Cr intermediate alloy and the like during the melting and casting. Firstly preparing alloy, placing the alloy in an intermediate frequency induction smelting furnace, heating the alloy after the vacuum degree is less than 0.1Pa, directly heating the alloy with high power to ensure that the solution is completely melted and the temperature is 1200-1300 ℃, preserving the heat for 3-7min, then stirring the solution with high power for 30-90 s, then starting casting when the temperature of the solution is stable at about 1250 ℃, and controlling the casting speed to avoid shrinkage cavity generation as much as possible; then carrying out homogenization treatment (the temperature is 930-970 ℃, the time is 2-5h, the heating rate is more than 100 ℃/min, the cooling rate is more than 120 ℃/min) on the alloy cast ingot, and carrying out hot working multi-process cooperative regulation and control, wherein the specific treatment process is as follows: firstly, hot rolling deformation is carried out on the steel plate, the initial rolling temperature is 750-810 ℃, the final rolling temperature is higher than 500 ℃, the total deformation is 72-80%, and the pass reduction is as follows: 5% -15%, the deformation mode: unidirectional rolling; then carrying out multiple-cycle ultralow-temperature deep cold rolling, wherein the low-temperature deformation cycle times are more than 5 times, firstly placing the steel plate in a liquid nitrogen tank for more than 20min, and then carrying out ultralow-temperature deformation, wherein the deformation temperature is as follows: -100-190 ℃, deformation: 5% -15%, the deformation mode: synchronous rolling, wherein the pass deformation is 3-10%; then the ultra-low temperature rolled plate is put into a liquid nitrogen tank to be cooled for 2-10min, and the deformation temperature is as follows: -100-190 ℃, deformation: 5% -15%, the deformation mode: synchronous rolling, pass deformation: 3-10%, repeating the above process to finally enable the total deformation of the alloy plate to reach 45-55%; then carrying out solid solution treatment, quenching and pre-ageing treatment, wherein the solid solution treatment temperature is as follows: 950-980 ℃, time: 1-3h, heating rate: greater than 20 ℃/sec; quenching rate is greater than 120 ℃/s, pre-ageing treatment temperature: 430-475 ℃ and the time is as follows: 1-2.5h; then, carrying out multiple times of circulation ultralow temperature deep cold rolling deformation, wherein the times of ultralow temperature deformation circulation is more than 6 times, firstly placing the steel wire rope in a liquid nitrogen tank for more than 20 minutes, and then carrying out ultralow temperature deformation, wherein the deformation temperature is as follows: -100-190 ℃, deformation: 5% -15%, the deformation mode: synchronously rolling, wherein the pass deformation is 3-10%, and then placing the ultra-low temperature rolled plate into a liquid nitrogen tank for cooling for 2-10min, wherein the deformation temperature is as follows: -100-190 ℃, deformation: 5% -15%, the deformation mode: synchronous rolling, pass deformation: 3-10%, repeating the above process to finally ensure that the total deformation of the alloy plate reaches 70-80%; then carrying out different artificial aging heat treatments on the deep cold-rolled sheet, namely 400 ℃/8h,450 ℃/8h and 500 ℃/4h; and then carrying out multiple-cycle ultralow-temperature deep cold rolling deformation on the heat-treated plate, wherein the multiple-cycle ultralow-temperature deformation cycle times are more than 6 times, firstly placing the plate in a liquid nitrogen tank for more than 20min, and then carrying out ultralow-temperature deformation at the deformation temperature: -100-190 ℃, deformation: 5% -15%, the deformation mode: synchronous rolling, wherein the pass deformation is 3-10%; then placing the ultra-low temperature rolled plate into a liquid nitrogen tank for cooling for 2-10min, wherein the deformation temperature is as follows: -100-190 ℃, deformation: 5% -15%, the deformation mode: synchronous rolling, pass deformation: 3-10%; repeating the above process to finally ensure that the total deformation of the alloy plate reaches 45-65%; then, the ultra-low temperature deep cold-rolled alloy sheet is subjected to low temperature heat treatment to regulate and control precipitation phase to cooperatively separate out, and the temperature is: 350 ℃, and 16 hours. Finally, tensile properties and electrical conductivity measurements were made on typical aged alloys, as shown in table 2.
TABLE 2 conductivity of the alloys of the invention in different states
TABLE 3 tensile Properties of the alloys of the invention in different states
Aiming at the problems of poor strength, conductivity and other performances of the traditional Cu-Ni-Si alloy and the like, the invention provides the method for effectively regulating and controlling the distribution characteristics of the alloy structure based on the biphase collaborative precipitation and the novel hot working process, thereby greatly improving the comprehensive performance of the alloy. Specifically, the invention not only optimizes the precipitation behavior of the alloy by changing the Ni, si content and Ni/Si ratio of the Cu-Ni-Si series alloy, but also expects to be capable of effectively promoting the precipitation of Ni-Si precipitation phase by adding a trace amount of solute element Cr, and simultaneously can further act with Si to precipitate Cr-Si phase, and finally obviously improves the strength and the conductivity of the alloy based on the dual-phase collaborative precipitation of Ni-Si and Cr-Si. In addition, on the basis of component design, the invention further fully utilizes ultralow temperature deformation to effectively promote dislocation rapid proliferation and form a large number of fine dislocation cells or sub-crystal tissues. In the formation process of the dislocation cells, a large number of dislocation lines can also interact with the fine precipitates so as to be uniformly dispersed and distributed on the alloy matrix, and the rapid precipitation of the fine precipitates and the uniform dispersion and distribution degree can be effectively promoted in the aging process so as to improve the comprehensive performance of the alloy. Meanwhile, due to the introduction of ultralow-temperature deformation, the strain energy storage in an alloy matrix can be obviously increased, and the method has an obvious promotion effect on rapid precipitation of a precipitation phase. The rapid promotion effect on the precipitated phase can effectively avoid coarsening of the precipitated phase, further effectively promote the promotion of alloy strength and conductivity, and reasonably regulate and control the morphology and distribution of the precipitated phase to improve the coordination deformation capability among alloy tissues. Finally, in order to remarkably improve the strength and the conductivity of the alloy, the invention also hopes that the alloy in a high-strength state still has excellent plastic deformation capacity, and further provides a new idea of cooperative regulation and control based on ultralow-temperature deep cold rolling and multistage variable-temperature heat treatment. Specifically, through multistage variable temperature heat treatment and reasonable matching with the ultralow temperature deep cold rolling deformation process, a multi-scale multi-type precipitated phase can be separated out from the alloy matrix, and the multi-scale multi-type precipitated phase can be used for affecting tissue evolution under the synergistic effect in the hot working process and affecting dislocation and dislocation cell distribution characteristics under the synergistic effect in the ultralow temperature deep cold rolling process. The reason is that coarse and fine particles have different pinning effects on dislocation, different pinning dislocation capacities of dispersed particles with different dimensions are necessarily caused in the deep cold rolling deformation process, and the formed dislocation cells have different forms and sizes. The dislocation cell or the subgrain structure with multiple sizes and types can be formed by reasonable regulation, namely, the dislocation quantity density distributed in the dislocation cell or the subgrain structure has certain difference, and a high concentration area (hard micro-area) and a low concentration area (soft micro-area) are formed. The formation of the structural characteristics can necessarily increase the coordinated deformation capability among alloy tissues, and finally, the novel Cu-Ni-Si-Cr alloy which is developed based on the component design and the novel hot working process regulation and control of special tissues can necessarily have high strength and high conductivity and also have high plasticity.
According to the design concept, the alloy prepared by using the embodiment 1 has quite different performances, and as can be seen from fig. 2,3 and 4, a solute element Cr is further introduced on the basis of the original Cu-Ni-Si alloy, so that not only can the hardness of the aged state of the alloy be remarkably improved, but also the hardness in the alloy matrix has the hardness gradient distribution characteristic due to the formation of multi-size multi-type dislocation cells and sub-crystalline structures. The appearance of the structure characteristic is also very beneficial to greatly improving the plasticity of the alloy while effectively improving the strength of the alloy. The promotion of plasticity by this structure is evident from the corresponding tensile properties of alloy # 3 (as shown in table 3), which corresponds to a tensile strength of up to 803MPa, but which still maintains a relatively high level of elongation of 5.5%. In addition, the addition of the solute element Cr is also very beneficial in promoting the formation and maintenance of the hardness gradient profile, and this profile can be maintained after increasing the aging temperature (as shown in FIGS. 3 and 4). The main point is that the addition of the element can effectively promote the high temperature softening resistance of the alloy, namely, the high hardness micro-area cannot be coarsened or recrystallized at high temperature. Furthermore, it can be seen from Table 2 that the effect on the conductivity of the alloy is not significant indeed after addition of the solute element Cr, and that a rapid increase in conductivity of the alloy can be obtained with an increase in the heat treatment temperature. If the developed alloy is further subjected to further ultra-low temperature deep cold rolling deformation on the basis of example 1, both the hardness and strength of the alloy can be further changed. However, as can be seen from fig. 5,6 and 7, the hardness of the alloy is not increased after the alloy is deformed by ultra-low temperature deep cold rolling, and the hardness is reduced by a part of the process. This is mainly due to the formation of a multiscale precipitate phase, which has different pinning ability to dislocations, and dislocation annihilation occurs after some micro-regions have grown dislocation lines to some extent. From the conductivity and tensile properties shown in tables 2 and 3, it can be seen that further ultra-low temperature deep cold rolling deformation does not significantly affect the conductivity of the alloy, with only a slight decrease, but some conditions also result in an increase in conductivity, which is due to dislocation annihilation. As can be seen from the tensile property test of the 3# alloy, the strength after deep cold rolling is obviously improved, and the elongation can be maintained at a certain level, so that the elongation is improved compared with that of the corresponding strength alloy prepared by the traditional process (as shown in Table 3). In addition, if the 3# alloy prepared in example 2 is further subjected to low temperature heat treatment to regulate multiphase synergistic precipitation, it is obvious from fig. 8 that not only the multiscale precipitated phase is distributed in the matrix, but also dislocation cells or sub-crystalline structures with different sizes and dislocation densities are distributed, and the strength, conductivity and plasticity of the alloy are significantly improved due to the formation of these special structure features (as shown in tables 2 and 3). Therefore, on the basis of component design and optimization, the alloy can be formed into the expected special structure characteristics by further carrying out cooperative regulation and control on the multistage variable temperature heat treatment and the ultralow temperature deep cold rolling process, so that the comprehensive performance of the developed alloy is obviously improved.
In conclusion, the invention optimizes the components of the traditional Cu-Ni-Si alloy, adds the proper solute element Cr, and realizes remarkable improvement on the microstructure of the alloy through the cooperative regulation and control of multiple processes, so that the strength and the conductivity of the alloy are improved due to the rapid precipitation of a precipitation phase, and the high-strength alloy also has high plastic property due to the appearance of special structure characteristics. The high-strength high-plasticity conductive copper alloy material and the preparation method thereof can well meet the urgent requirements of manufacturing typical components in a plurality of high-new technical fields such as electronic industry, aerospace, instruments and meters, household appliances and the like on high-strength high-conductivity high-plasticity copper alloy. Therefore, the preparation method of the invention is not only very suitable for being applied to a plurality of high and new technical fields, especially the fields with special requirements on high-strength and high-conductivity novel copper alloy, but also can well solve the problems frequently occurring in the application process of lead frame materials, such as poor processability and the like. In addition, the preparation technology has a certain guiding significance for further development, processing and application of high-strength high-conductivity copper alloy and other similar metal materials in other fields, and is worthy of copper alloy processing enterprises to pay attention to the alloy and the preparation process thereof, so that the alloy can be popularized and applied as soon as possible.
The previous description of the disclosed embodiments is provided to enable any person skilled in the art to make or use the present invention. Various modifications to these embodiments will be readily apparent to those skilled in the art, and the generic principles defined herein may be applied to other embodiments without departing from the spirit or scope of the invention. Thus, the present invention is not intended to be limited to the embodiments shown herein but is to be accorded the widest scope consistent with the principles and novel features disclosed herein.
Claims (6)
1. The preparation method of the high-strength high-plastic conductive copper alloy material is characterized by comprising the following steps of:
(1) Vacuum smelting to prepare a copper alloy cast ingot, wherein the copper alloy cast ingot comprises the following chemical components in percentage by mass: 3.0 to 4.5 weight percent of Ni, 0.65 to 0.92 weight percent of Si, 0.005 to 0.15 weight percent of Cr, less than or equal to 0.05 weight percent of B, less than or equal to 0.05 weight percent of Zr, and the balance of Cu;
(2) Homogenizing heat treatment at 930-980 deg.c for 2-6 hr;
(3) Hot rolling deformation, wherein the initial rolling temperature is 750-820 ℃, and the deformation is 70-80%;
(4) Multiple circulation ultra-low temperature deep cold rolling: firstly, placing the steel wire rope in a liquid nitrogen tank for more than 20min, then performing ultralow-temperature deformation, wherein the deformation temperature is between-100 ℃ and-190 ℃, the deformation amount is 5% -15%, and the deformation mode is as follows: synchronous rolling, wherein the pass deformation is 3-10%; then placing the ultralow temperature rolled plate into a liquid nitrogen tank to be cooled for 2-10min, deforming at ultralow temperature, wherein the deformation temperature is-100 ℃ to-190 ℃, the deformation amount is 5% -15%, and the deformation mode is as follows: synchronous rolling, pass deformation: 3% -10%; repeating the ultralow temperature deformation cycle times more than 5 times to ensure that the total deformation of the alloy plate reaches 45% -55%;
(5) Carrying out solution quenching treatment, wherein the solution temperature is 950-980 ℃, the solution time is 1-3h, and the quenching mode is water quenching;
(6) Pre-ageing at 430-480 deg.c for 1-3 hr;
(7) Multiple circulation ultra-low temperature deep cold rolling deformation: firstly, placing the steel wire rope in a liquid nitrogen tank for more than 20min, then performing ultralow-temperature deformation, wherein the deformation temperature is between-100 ℃ and-190 ℃, the deformation amount is 5% -15%, and the deformation mode is as follows: synchronous rolling, wherein the pass deformation is 3% -10%; then placing the ultralow temperature rolled plate into a liquid nitrogen tank to be cooled for 2-10min, and then carrying out ultralow temperature deformation, wherein the deformation temperature is-100 ℃ to-190 ℃, the deformation amount is 5% -15%, and the deformation mode is as follows: synchronous rolling, wherein the pass deformation is 3% -10%; repeating the ultralow temperature deformation cycle times more than 6 times to ensure that the total deformation of the alloy plate reaches 70% -80%;
(8) Artificially aging at 400-550deg.C for 3-12 hr;
(9) Multiple circulation ultra-low temperature deep cold rolling deformation: firstly, placing the steel wire rope in a liquid nitrogen tank for more than 20min, then performing ultralow-temperature deformation, wherein the deformation temperature is between-100 ℃ and-190 ℃, the deformation amount is 5% -15%, and the deformation mode is as follows: synchronous rolling, wherein the pass deformation is 3% -10%; then the ultra-low temperature rolled plate is placed into a liquid nitrogen tank to be cooled for 2-10min, and then ultra-low temperature deformation is carried out, wherein the deformation temperature is-100 ℃ to-190 ℃, the deformation amount is 5% -15%, and the deformation mode is as follows: synchronous rolling, wherein the pass deformation is 3% -10%; repeating the ultralow temperature deformation cycle times more than 6 times to ensure that the total deformation of the alloy plate reaches 45% -65%;
(10) The low-temperature heat treatment regulates the cooperative precipitation behavior of the precipitate phase, the aging temperature is 330-380 ℃ and the time is 10-20h.
2. The method for preparing the high-strength high-plastic conductive copper alloy material according to claim 1, wherein the vacuum melting process in the step (1) is as follows: adding alloy raw materials according to the proportion, heating and melting the alloy raw materials after the vacuum degree is less than 0.1Pa, preserving heat for 3-7min at 1200-1300 ℃ after the alloy raw materials are completely melted, stirring the solution for 30-90s, starting casting when the solution temperature is stable at 1230-1260 ℃, and controlling the casting speed.
3. The method for preparing a high-strength high-plastic conductive copper alloy material according to claim 1, wherein the homogenizing heat treatment in the step (2) comprises the following steps: the temperature is 930-970 ℃, the time is 2-5h, the heating rate is more than 100 ℃/min, and the cooling rate is more than 120 ℃/min.
4. The method for preparing the high-strength high-plastic conductive copper alloy material according to claim 1, wherein the hot rolling deformation start rolling temperature in the step (3) is 750-810 ℃, the finish rolling temperature is higher than 500 ℃, the total deformation is 72-80%, and the pass reduction is as follows: 5-15%, and the deformation mode is unidirectional rolling.
5. The method for preparing the high-strength high-plastic conductive copper alloy material according to claim 1, wherein the temperature of the solution quenching treatment in the step (5) is 950-980 ℃, the time is 1-3h, the heating rate is more than 20 ℃/s, and the quenching rate is more than 120 ℃/s.
6. A high strength, high plasticity conductive copper alloy material prepared by the method of any one of claims 1-5.
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