CN113832367A - Method for preparing CuCrZr alloy by two-stage aging process - Google Patents
Method for preparing CuCrZr alloy by two-stage aging process Download PDFInfo
- Publication number
- CN113832367A CN113832367A CN202111201564.8A CN202111201564A CN113832367A CN 113832367 A CN113832367 A CN 113832367A CN 202111201564 A CN202111201564 A CN 202111201564A CN 113832367 A CN113832367 A CN 113832367A
- Authority
- CN
- China
- Prior art keywords
- alloy
- stage aging
- cucrzr
- treatment
- temperature
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Granted
Links
- 239000000956 alloy Substances 0.000 title claims abstract description 142
- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 142
- 230000032683 aging Effects 0.000 title claims abstract description 90
- 238000000034 method Methods 0.000 title claims abstract description 27
- 238000005097 cold rolling Methods 0.000 claims abstract description 20
- 239000006104 solid solution Substances 0.000 claims abstract description 16
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 claims abstract description 15
- 229910052802 copper Inorganic materials 0.000 claims abstract description 15
- 239000010949 copper Substances 0.000 claims abstract description 15
- 238000001816 cooling Methods 0.000 claims abstract description 7
- 238000010791 quenching Methods 0.000 claims description 30
- 230000000171 quenching effect Effects 0.000 claims description 30
- 238000004321 preservation Methods 0.000 claims description 4
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims description 4
- 238000003723 Smelting Methods 0.000 claims description 3
- 150000003839 salts Chemical class 0.000 claims description 2
- 238000010438 heat treatment Methods 0.000 abstract description 21
- 238000012360 testing method Methods 0.000 abstract description 20
- 238000002360 preparation method Methods 0.000 abstract description 4
- 238000003672 processing method Methods 0.000 abstract 1
- 230000000052 comparative effect Effects 0.000 description 22
- 238000001514 detection method Methods 0.000 description 11
- 230000006698 induction Effects 0.000 description 10
- 238000005516 engineering process Methods 0.000 description 9
- 239000000203 mixture Substances 0.000 description 9
- 238000005096 rolling process Methods 0.000 description 9
- 239000000243 solution Substances 0.000 description 9
- 230000000930 thermomechanical effect Effects 0.000 description 9
- 230000006911 nucleation Effects 0.000 description 4
- 238000010899 nucleation Methods 0.000 description 4
- 239000000463 material Substances 0.000 description 3
- 239000011159 matrix material Substances 0.000 description 3
- 239000007787 solid Substances 0.000 description 3
- 230000009286 beneficial effect Effects 0.000 description 2
- HMUNWXXNJPVALC-UHFFFAOYSA-N 1-[4-[2-(2,3-dihydro-1H-inden-2-ylamino)pyrimidin-5-yl]piperazin-1-yl]-2-(2,4,6,7-tetrahydrotriazolo[4,5-c]pyridin-5-yl)ethanone Chemical compound C1C(CC2=CC=CC=C12)NC1=NC=C(C=N1)N1CCN(CC1)C(CN1CC2=C(CC1)NN=N2)=O HMUNWXXNJPVALC-UHFFFAOYSA-N 0.000 description 1
- SXAMGRAIZSSWIH-UHFFFAOYSA-N 2-[3-[2-(2,3-dihydro-1H-inden-2-ylamino)pyrimidin-5-yl]-1,2,4-oxadiazol-5-yl]-1-(2,4,6,7-tetrahydrotriazolo[4,5-c]pyridin-5-yl)ethanone Chemical compound C1C(CC2=CC=CC=C12)NC1=NC=C(C=N1)C1=NOC(=N1)CC(=O)N1CC2=C(CC1)NN=N2 SXAMGRAIZSSWIH-UHFFFAOYSA-N 0.000 description 1
- WZFUQSJFWNHZHM-UHFFFAOYSA-N 2-[4-[2-(2,3-dihydro-1H-inden-2-ylamino)pyrimidin-5-yl]piperazin-1-yl]-1-(2,4,6,7-tetrahydrotriazolo[4,5-c]pyridin-5-yl)ethanone Chemical compound C1C(CC2=CC=CC=C12)NC1=NC=C(C=N1)N1CCN(CC1)CC(=O)N1CC2=C(CC1)NN=N2 WZFUQSJFWNHZHM-UHFFFAOYSA-N 0.000 description 1
- ZRPAUEVGEGEPFQ-UHFFFAOYSA-N 2-[4-[2-(2,3-dihydro-1H-inden-2-ylamino)pyrimidin-5-yl]pyrazol-1-yl]-1-(2,4,6,7-tetrahydrotriazolo[4,5-c]pyridin-5-yl)ethanone Chemical compound C1C(CC2=CC=CC=C12)NC1=NC=C(C=N1)C=1C=NN(C=1)CC(=O)N1CC2=C(CC1)NN=N2 ZRPAUEVGEGEPFQ-UHFFFAOYSA-N 0.000 description 1
- YJLUBHOZZTYQIP-UHFFFAOYSA-N 2-[5-[2-(2,3-dihydro-1H-inden-2-ylamino)pyrimidin-5-yl]-1,3,4-oxadiazol-2-yl]-1-(2,4,6,7-tetrahydrotriazolo[4,5-c]pyridin-5-yl)ethanone Chemical compound C1C(CC2=CC=CC=C12)NC1=NC=C(C=N1)C1=NN=C(O1)CC(=O)N1CC2=C(CC1)NN=N2 YJLUBHOZZTYQIP-UHFFFAOYSA-N 0.000 description 1
- CONKBQPVFMXDOV-QHCPKHFHSA-N 6-[(5S)-5-[[4-[2-(2,3-dihydro-1H-inden-2-ylamino)pyrimidin-5-yl]piperazin-1-yl]methyl]-2-oxo-1,3-oxazolidin-3-yl]-3H-1,3-benzoxazol-2-one Chemical compound C1C(CC2=CC=CC=C12)NC1=NC=C(C=N1)N1CCN(CC1)C[C@H]1CN(C(O1)=O)C1=CC2=C(NC(O2)=O)C=C1 CONKBQPVFMXDOV-QHCPKHFHSA-N 0.000 description 1
- 239000004020 conductor Substances 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 238000009792 diffusion process Methods 0.000 description 1
- 238000009826 distribution Methods 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- 238000011156 evaluation Methods 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 238000011084 recovery Methods 0.000 description 1
- 230000001105 regulatory effect Effects 0.000 description 1
- 238000005728 strengthening Methods 0.000 description 1
- 238000009864 tensile test Methods 0.000 description 1
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C9/00—Alloys based on copper
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B3/00—Rolling materials of special alloys so far as the composition of the alloy requires or permits special rolling methods or sequences ; Rolling of aluminium, copper, zinc or other non-ferrous metals
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/02—Making non-ferrous alloys by melting
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/002—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working by rapid cooling or quenching; cooling agents used therefor
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/08—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of copper or alloys based thereon
-
- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01B—CABLES; CONDUCTORS; INSULATORS; SELECTION OF MATERIALS FOR THEIR CONDUCTIVE, INSULATING OR DIELECTRIC PROPERTIES
- H01B1/00—Conductors or conductive bodies characterised by the conductive materials; Selection of materials as conductors
- H01B1/02—Conductors or conductive bodies characterised by the conductive materials; Selection of materials as conductors mainly consisting of metals or alloys
- H01B1/026—Alloys based on copper
-
- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01B—CABLES; CONDUCTORS; INSULATORS; SELECTION OF MATERIALS FOR THEIR CONDUCTIVE, INSULATING OR DIELECTRIC PROPERTIES
- H01B13/00—Apparatus or processes specially adapted for manufacturing conductors or cables
- H01B13/0016—Apparatus or processes specially adapted for manufacturing conductors or cables for heat treatment
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B3/00—Rolling materials of special alloys so far as the composition of the alloy requires or permits special rolling methods or sequences ; Rolling of aluminium, copper, zinc or other non-ferrous metals
- B21B2003/005—Copper or its alloys
Abstract
The invention discloses a method for preparing a CuCrZr alloy by a two-stage aging process, and belongs to the technical field of alloy preparation. The method comprises the following steps: according to the mass percentage, 0.3 to 0.9 percent of Cr, 0.1 to 0.3 percent of Zr and the balance of copper are smelted into CuCrZr bulk alloy; carrying out thermal deformation and solid solution treatment on the block alloy in sequence to obtain a solid solution alloy; cooling and then carrying out cold rolling to obtain a cold-rolled alloy; and performing primary aging treatment and secondary aging treatment on the alloy after cold rolling, and controlling the temperature of the primary aging treatment to be 100-200 ℃ to prepare the CuCrZr alloy. Compared with the single-stage aging heat treatment CuCrZr alloy, the CuCrZr alloy has the advantages that the processing method is simple, the strength is improved, the elongation of the alloy is improved, the potential is higher in engineering application, a tensile curve measured by an electronic universal testing machine is analyzed, and the alloy product of strength and elongation is obviously improved after two-stage aging; and the conductivity is stably improved.
Description
The technical field is as follows:
the invention belongs to the technical field of alloy preparation, and particularly relates to a method for preparing a CuCrZr alloy by a two-stage aging process.
Background art:
the CuCrZr alloy has great advantages in the field of high-strength and high-conductivity materials, and the reason is that Cr and Zr elements are fully precipitated due to extremely low solid solubility in a copper matrix in a room temperature environment. The precipitated phase can improve the strength of the alloy, reduce the content of solid solution elements in the alloy and improve the conductivity of the alloy. The alloy is widely applied to the industrial fields of electric power, electronics, machinery and the like, and can be used as an integrated circuit lead frame, a high-power asynchronous traction motor rotor, an electrified railway contact wire, a high-pulse magnetic field conductor material and the like. In 2020, Guangdong Huaxing heat exchange equipment Co., Ltd discloses a CuCrZr alloy and a preparation method thereof (CN109385555B), and the alloy has good comprehensive performance.
The CuCrZr alloy has the advantages of high strength and high conductivity because of the extremely low solid solubility of alloy elements, but because of the limitation of the solid solubility, the strength of the alloy cannot be obviously improved by adding excessive Cr and Zr elements, so the Cr content in the common CuCrZr alloy is less than 1 percent by mass ratio. When the alloy performance is changed by regulating the content of alloy elements, the alloy strength is improved along with the increase of the content of Cr and Zr elements, but the elongation is reduced along with the increase of the content of Zr elements; when the content of the alloy elements is reduced, the plasticity of the alloy is improved, but the strength is too low to be applied in practical environment. In addition, it is difficult to balance the plasticity and the strength even if the amount of deformation is changed, and an increase in one is accompanied by a decrease in the other. In practical applications (such as contact wires), the tensile strength of the alloy is continuously improved with the updating of products. However, the material strengthening effect is evaluated, and the single pursuit of ultimate tensile strength or elongation as much as possible does not meet the practical application standard. The performance of the alloy in the stretching process is difficult to be comprehensively evaluated by taking single tensile strength or elongation as a standard, and at the moment, the evaluation by taking the product of strength and elongation as a standard is particularly important. The CuCrZr alloy prepared by the prior art has most of the product of strength and elongation distributed between 3000 and 5000MPa and is difficult to be further improved.
The invention content is as follows:
the invention aims to overcome the defects in the prior art and provides a method for preparing a CuCrZr alloy by a two-stage aging process.
In order to achieve the purpose, the invention adopts the following technical scheme:
a method for preparing a CuCrZr alloy by a two-stage aging process comprises the following steps:
(1) smelting a CuCrZr bulk alloy according to the mass ratio, wherein the CuCrZr bulk alloy comprises the following components in percentage by mass: 0.3 to 0.9 percent of Cr, 0.1 to 0.3 percent of Zr and the balance of copper;
(2) sequentially carrying out thermal deformation and solid solution treatment on the CuCrZr bulk alloy to obtain a solid solution alloy;
(3) after cooling the solid solution alloy, cold rolling to obtain a cold-rolled alloy;
(4) and performing two-stage aging treatment on the alloy after cold rolling to obtain the CuCrZr alloy, wherein the two-stage aging treatment comprises first-stage aging treatment and second-stage aging treatment, the temperature of the first-stage aging treatment is 100-200 ℃, and the temperature of the second-stage aging treatment is 385-475 ℃.
In the step (1), the smelting operation is carried out in a vacuum induction furnace.
In the step (1), preferably, the CuCrZr bulk alloy comprises the following components in percentage by mass: 0.7% of Cr, 0.19% of ZrC and the balance of copper.
In the step (2), the thermal deformation temperature is 700-900 ℃, and the heat preservation time is 1-2h, so as to obtain a thermal deformation alloy;
in the step (2), the solid solution treatment is carried out in a muffle furnace, the solid solution temperature is 950-;
in the step (3), the cooling mode of the solid solution alloy is water quenching cooling, and the scalping treatment is carried out before cold rolling to remove an oxide layer.
In the step (3), the cold rolling single-pass pressure is 10-35%, and the total pressure is 90-97%.
In the step (4), the primary aging is carried out in a salt bath furnace, and the secondary aging is carried out in a muffle furnace.
In the step (4), the alloy after the first-stage aging is quenched and cooled by water, and then the second-stage aging is carried out.
In the step (4), the primary aging time is 4-6h, and the secondary aging time is 1-2.5 h.
In the step (4), preferably, the temperature of the primary aging treatment is 120-180 ℃.
In the step (4), the temperature of the primary aging treatment is preferably 150 ℃.
In the step (4), preferably, the temperature of the secondary aging treatment is 400-450 ℃.
In the step (4), the temperature of the secondary aging treatment is preferably 425 ℃.
In the step (4), the CuCrZr alloy has a strength-ductility product of 6534-8760MPa, a tensile strength of 542-603MPa, an elongation of 11-15%, a hardness of 162-199HV0.2 and an electrical conductivity of 77-81% IACS.
In the step (4), the strength-plasticity product of the CuCrZr alloy is preferably 6996-8760 MPa%.
In the step (4), the alloy hardness is measured by using a semi-automatic Vickers hardness tester, the tensile strength is measured by using a universal electronic tester to perform a tensile test and analyze a tensile curve, and the conductivity is measured by using a direct current resistance tester.
In the primary aging process of the alloy after cold rolling, a large number of GP zones are uniformly distributed in a matrix in a specific low-temperature environment, conditions are created for the non-uniform nucleation of a second phase, and the free energy of nucleation and growth of the alloy in a high-temperature environment is reduced. The application of the specific two-stage aging avoids the uneven precipitation of the second phase along the grain boundary, is beneficial to the uniform and dense distribution of the second phase, and improves the product of strength and elongation of the alloy.
The invention has the beneficial effects that:
compared with the single-stage aging heat treatment CuCrZr alloy, the CuCrZr alloy has the advantages that the strength is improved, the elongation of the alloy is improved, the CuCrZr alloy has greater potential in engineering application, a tensile curve measured by an electronic universal testing machine is analyzed, and the alloy product of strength and elongation is obviously improved after two-stage aging; the conductivity is measured by using a direct current resistance tester, and the conductivity of the alloy is stably improved after two-stage aging.
The specific implementation mode is as follows:
the present invention will be described in further detail with reference to examples.
Example 1
The alloy adopted by the invention is prepared by a vacuum induction furnace and then is subjected to thermal deformation to obtain a block alloy with the thickness of 30mm, and the composition and the ratio (mass%) are as follows: 0.5 percent of Cr0.13 percent of Zr0.13 percent, and the balance of copper;
(1) solution treatment, keeping the temperature at 960 ℃ for 1h, and quenching;
(2) the processing technology comprises the following steps: cold rolling, namely rolling the block alloy with the thickness of 30mm to 1mm, wherein the reduction is 96%;
(3) first-stage aging heat treatment: keeping the temperature at 150 ℃ for 5h, and quenching;
(4) and (3) secondary aging heat treatment: keeping the temperature at 425 ℃ for 2h, and quenching;
the results of the comprehensive property tests of the test alloy and the comparative alloy after the above-mentioned thermomechanical treatment process are shown in Table 1.
Comparative examples 1 to 1
The difference from example 1 is that the first stage aging process is omitted, and the alloy product is obtained, and the performance indexes are shown in table 1 after detection.
Example 2
The alloy adopted by the invention is prepared by a vacuum induction furnace and then is subjected to thermal deformation to obtain a block alloy with the thickness of 30mm, and the composition and the ratio (mass%) are as follows: 0.5 percent of Cr0.13 percent of Zr0.13 percent, and the balance of copper;
(1) solution treatment, keeping the temperature at 960 ℃ for 1h, and quenching;
(2) the processing technology comprises the following steps: cold rolling, namely rolling the block alloy with the thickness of 30mm to 1mm, wherein the reduction is 96%;
(3) first-stage aging heat treatment: keeping the temperature at 120 ℃ for 5.5h, and quenching;
(4) and (3) secondary aging heat treatment: keeping the temperature at 400 ℃ for 2.5h, and quenching;
the results of the comprehensive property tests of the test alloy and the comparative alloy after the above-mentioned thermomechanical treatment process are shown in Table 1.
Comparative example 2-1
The difference from example 2 is that the first stage aging process is omitted, and the alloy product is obtained, and the performance indexes are shown in table 1 after detection.
Example 3
The alloy adopted by the invention is prepared by a vacuum induction furnace and then is subjected to thermal deformation to obtain a block alloy with the thickness of 30mm, and the composition and the ratio (mass%) are as follows: 0.7 percent of Cr0.19 percent, 0.19 percent of Zr0 percent and the balance of copper;
(1) solution treatment, keeping the temperature at 960 ℃ for 1h, and quenching;
(2) the processing technology comprises the following steps: cold rolling, namely rolling the block alloy with the thickness of 30mm to 1mm, wherein the reduction is 96%;
(3) first-stage aging heat treatment: keeping the temperature at 100 ℃ for 6h, and quenching;
(4) and (3) secondary aging heat treatment: keeping the temperature at 385 ℃ for 3h, and quenching;
the results of the comprehensive property tests of the test alloy and the comparative alloy after the above-mentioned thermomechanical treatment process are shown in Table 1.
Comparative example 3-1
The difference from example 3 is that the first stage aging process is omitted, and the alloy product is obtained, and the performance indexes are shown in table 1 after detection.
Example 4
The alloy adopted by the invention is prepared by a vacuum induction furnace and then is subjected to thermal deformation to obtain a block alloy with the thickness of 30mm, and the composition and the ratio (mass%) are as follows: 0.7 percent of Cr0.19 percent, 0.19 percent of Zr0 percent and the balance of copper;
(1) solution treatment, heat preservation at 950 ℃ for 2h, and quenching;
(2) the processing technology comprises the following steps: cold rolling, namely rolling the block alloy with the thickness of 30mm to 1mm, wherein the reduction is 96%;
(3) first-stage aging heat treatment: keeping the temperature at 120 ℃ for 5.5h, and quenching;
(4) and (3) secondary aging heat treatment: keeping the temperature at 400 ℃ for 2.5h, and quenching;
the results of the comprehensive property tests of the test alloy and the comparative alloy after the above-mentioned thermomechanical treatment process are shown in Table 1.
Comparative example 4-1
The difference from example 4 is that the first stage aging process is omitted, and the alloy product is obtained, and the performance indexes are shown in table 1 after detection.
Example 5
The alloy adopted by the invention is prepared by a vacuum induction furnace and then is subjected to thermal deformation to obtain a block alloy with the thickness of 30mm, and the composition and the ratio (mass%) are as follows: 0.7 percent of Cr0.19 percent, 0.19 percent of Zr0 percent and the balance of copper;
(1) solution treatment, keeping the temperature at 960 ℃ for 1h, and quenching;
(2) the processing technology comprises the following steps: cold rolling, namely rolling the block alloy with the thickness of 30mm to 1mm, wherein the reduction is 96%;
(3) first-stage aging heat treatment: keeping the temperature at 150 ℃ for 5h, and quenching;
(4) and (3) secondary aging heat treatment: keeping the temperature at 425 ℃ for 2h, and quenching;
the results of the comprehensive property tests of the test alloy and the comparative alloy after the above-mentioned thermomechanical treatment process are shown in Table 1.
Comparative example 5-1
The difference from example 5 is that the first stage aging process is omitted, and the alloy product is obtained, and the performance indexes are shown in table 1 after detection.
Comparative examples 5 to 2
The difference from example 5 is that the primary aging temperature is 50 ℃ and the time is 5h, the product of strength and elongation is as low as 6292 after detection, the rest performance data lines are detailed in table 1, and analysis shows that the primary aging temperature is too low, so that only recovery occurs in the alloy matrix, and the atomic diffusion rate is too slow at low temperature and the nucleation rate is too low, so that the product of strength and elongation is obviously reduced.
Comparative examples 5 to 3
The difference from example 5 is that the primary aging temperature is 250 ℃, the time is 5h, the product of strength and elongation is as low as 6852 after detection, and the rest performance data lines are detailed in table 1, and analysis shows that the reason is that the primary aging temperature is too high, annihilation of dislocation is promoted, the nucleation rate of the second phase is reduced, and the product of strength and elongation is remarkably reduced.
Example 6
The alloy adopted by the invention is prepared by a vacuum induction furnace and then is subjected to thermal deformation to obtain a block alloy with the thickness of 30mm, and the composition and the ratio (mass%) are as follows: 0.7 percent of Cr0.19 percent, 0.19 percent of Zr0 percent and the balance of copper;
(1) solution treatment, keeping the temperature at 960 ℃ for 1h, and quenching;
(2) the processing technology comprises the following steps: cold rolling, namely rolling the block alloy with the thickness of 30mm to 1mm, wherein the reduction is 96%;
(3) first-stage aging heat treatment: keeping the temperature at 180 ℃ for 4.5h, and quenching;
(4) and (3) secondary aging heat treatment: keeping the temperature at 450 ℃ for 1.5h, and quenching;
the results of the comprehensive property tests of the test alloy and the comparative alloy after the above-mentioned thermomechanical treatment process are shown in Table 1.
Comparative example 6-1
The difference from example 6 is that the first stage aging process is omitted, and the alloy product is obtained, and the performance indexes are shown in table 1 after detection.
Example 7
The alloy adopted by the invention is prepared by a vacuum induction furnace and then is subjected to thermal deformation to obtain a block alloy with the thickness of 30mm, and the composition and the ratio (mass%) are as follows: 0.7 percent of Cr0.19 percent, 0.19 percent of Zr0 percent and the balance of copper;
(1) solution treatment, keeping the temperature at 960 ℃ for 1h, and quenching;
(2) the processing technology comprises the following steps: cold rolling, namely rolling the block alloy with the thickness of 30mm to 1mm, wherein the reduction is 96%;
(3) first-stage aging heat treatment: keeping the temperature at 200 ℃ for 4h, and quenching;
(4) and (3) secondary aging heat treatment: keeping the temperature at 475 ℃ for 1h, and quenching;
the results of the comprehensive property tests of the test alloy and the comparative alloy after the above-mentioned thermomechanical treatment process are shown in Table 1.
Comparative example 7-1
The difference from example 7 is that the first stage aging process is omitted, and alloy products are obtained, and the performance indexes of the alloy products are shown in table 1 after detection.
Example 8
The alloy adopted by the invention is prepared by a vacuum induction furnace and then is subjected to thermal deformation to obtain a block alloy with the thickness of 30mm, and the composition and the ratio (mass%) are as follows: 0.9 percent of Cr0.24 percent of Zr0.24 percent, and the balance of copper;
(1) solution treatment, keeping the temperature at 960 ℃ for 1h, and quenching;
(2) the processing technology comprises the following steps: cold rolling, namely rolling the block alloy with the thickness of 30mm to 1mm, wherein the reduction is 96%;
(3) first-stage aging heat treatment: keeping the temperature at 150 ℃ for 5h, and quenching;
(4) and (3) secondary aging heat treatment: keeping the temperature at 425 ℃ for 2h, and quenching;
the results of the comprehensive property tests of the test alloy and the comparative alloy after the above-mentioned thermomechanical treatment process are shown in Table 1.
Comparative example 8-1
The difference from example 8 is that the first stage aging process is omitted, and the alloy product is obtained, and the performance indexes are shown in table 1 after detection.
Example 9
The alloy adopted by the invention is prepared by a vacuum induction furnace and then is subjected to thermal deformation to obtain a block alloy with the thickness of 30mm, and the composition and the ratio (mass%) are as follows: 0.9 percent of Cr0.24 percent of Zr0.24 percent, and the balance of copper;
(1) solution treatment, heat preservation at 950 ℃ for 2h, and quenching;
(2) the processing technology comprises the following steps: cold rolling, namely rolling the block alloy with the thickness of 30mm to 1mm, wherein the reduction is 96%;
(3) first-stage aging heat treatment: keeping the temperature at 120 ℃ for 5.5h, and quenching;
(4) and (3) secondary aging heat treatment: keeping the temperature at 400 ℃ for 2.5h, and quenching;
the results of the comprehensive property tests of the test alloy and the comparative alloy after the above-mentioned thermomechanical treatment process are shown in Table 1.
Comparative example 9-1
The difference from example 9 is that the first stage aging process is omitted, and the alloy product is obtained, and the performance indexes are shown in table 1 after detection.
The above examples 1-8 and the comparative preparation process parameters and the overall properties of the prepared alloy products are shown in Table 1 below.
TABLE 1
In the table, D is the meaning of the comparative example, and the unit of heat treatment, solid solution and twice aging is h; the unit of the product of strength and elongation is MPa, the unit of tensile strength is MPa, the unit of elongation is HV0.2, and the unit of conductivity is ACS.
Claims (10)
1. A method for preparing a CuCrZr alloy by a two-stage aging process is characterized by comprising the following steps:
(1) smelting a CuCrZr bulk alloy according to the mass ratio, wherein the CuCrZr bulk alloy comprises the following components in percentage by mass: 0.3 to 0.9 percent of Cr, 0.1 to 0.3 percent of Zr and the balance of copper;
(2) sequentially carrying out thermal deformation and solid solution treatment on the CuCrZr bulk alloy to obtain a solid solution alloy;
(3) after cooling the solid solution alloy, cold rolling to obtain a cold-rolled alloy;
(4) and performing two-stage aging treatment on the alloy after cold rolling to prepare the CuCrZr alloy, wherein the two-stage aging treatment comprises first-stage aging treatment and second-stage aging treatment, and the temperature of the first-stage aging treatment is 100-200 ℃.
2. The method for preparing the CuCrZr alloy by the double-stage aging process according to claim 1, wherein in the step (1), the CuCrZr bulk alloy comprises the following components in percentage by mass: 0.7% of Cr, 0.19% of Zr and the balance of copper.
3. The method for preparing the CuCrZr alloy by the two-stage aging process according to claim 1, wherein in the step (2), the thermal deformation temperature is 700-900 ℃, and the heat preservation time is 1-2h, so as to obtain the thermal deformation alloy; the solid solution treatment is carried out in a muffle furnace, the solid solution temperature is 950-.
4. The method for preparing the CuCrZr alloy by the double-stage aging process according to claim 1, wherein in the step (3), the solid solution alloy cooling mode is water quenching cooling, and the scalping treatment is carried out before cold rolling to remove an oxide layer; the cold rolling single-pass pressure is 10-35%, and the total pressure is 90-97%.
5. The method for preparing the CuCrZr alloy by the double-stage aging process according to claim 1, wherein in the step (4), the first-stage aging is carried out in a salt bath furnace, the second-stage aging is carried out in a muffle furnace, and the alloy after the first-stage aging is cooled by water quenching and then subjected to the second-stage aging.
6. The method for preparing the CuCrZr alloy by the two-stage aging process according to claim 1, wherein in the step (4), the first-stage aging time is 4-6h, the second-stage aging treatment temperature is 385-475 ℃, and the second-stage aging time is 1-2.5 h.
7. The method for preparing CuCrZr alloy by the two-stage aging process as claimed in claim 6, wherein in the step (4), the temperature of the first-stage aging treatment is 120-180 ℃, and the temperature of the second-stage aging treatment is 400-450 ℃.
8. The method for preparing the CuCrZr alloy by the double-stage aging process according to claim 7, wherein in the step (4), the temperature of the first-stage aging treatment is 150 ℃, and the temperature of the second-stage aging treatment is 425 ℃.
9. The method for preparing CuCrZr alloy by the two-stage aging process as claimed in claim 1, wherein in the step (4), the CuCrZr alloy has a strength and elongation of 6534-8760MPa, a tensile strength of 542-603MPa, an elongation of 11-15%, a hardness of 162-199HV0.2, and an electrical conductivity of 77-81% IACS.
10. The method for preparing CuCrZr alloy by the two-stage aging process according to claim 9, wherein in the step (4), the CuCrZr alloy has a product strength and elongation of 6996-8760 MPa%.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202111201564.8A CN113832367B (en) | 2021-10-15 | 2021-10-15 | Method for preparing CuCrZr alloy by two-stage aging process |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202111201564.8A CN113832367B (en) | 2021-10-15 | 2021-10-15 | Method for preparing CuCrZr alloy by two-stage aging process |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN113832367A true CN113832367A (en) | 2021-12-24 |
| CN113832367B CN113832367B (en) | 2022-08-23 |
Family
ID=78969061
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN202111201564.8A Active CN113832367B (en) | 2021-10-15 | 2021-10-15 | Method for preparing CuCrZr alloy by two-stage aging process |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN113832367B (en) |
Citations (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1928145A (en) * | 2006-09-20 | 2007-03-14 | 苏州有色金属加工研究院 | Process for preparing Cu-Cr-Zr alloy slat |
| CN101376955A (en) * | 2008-09-25 | 2009-03-04 | 苏州有色金属研究院有限公司 | Preparation technique capable of effectively controlling Cu-Cr-Zr sheet alloy texture distribution |
| CN102534291A (en) * | 2010-12-09 | 2012-07-04 | 北京有色金属研究总院 | CuCrZr alloy with high strength and high conductivity, and preparation and processing method thereof |
| CN106381414A (en) * | 2016-09-30 | 2017-02-08 | 陕西科技大学 | Copper-based in-situ composite alloy and preparing method thereof |
| CN108359842A (en) * | 2018-05-31 | 2018-08-03 | 华北水利水电大学 | A kind of polynary cast copper alloy of impeller high-performance and its manufacturing method and application |
| CN111575525A (en) * | 2020-04-16 | 2020-08-25 | 陕西斯瑞新材料股份有限公司 | Method for manufacturing Cu-Cr-Zr alloy contact line for electrified railway |
| 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 |
| US20200377986A1 (en) * | 2017-11-28 | 2020-12-03 | Poongsan Corporation | Method for producing copper-titanium based copper alloy material for automobile and electronic parts and copper alloy material produced therefrom |
-
2021
- 2021-10-15 CN CN202111201564.8A patent/CN113832367B/en active Active
Patent Citations (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1928145A (en) * | 2006-09-20 | 2007-03-14 | 苏州有色金属加工研究院 | Process for preparing Cu-Cr-Zr alloy slat |
| CN101376955A (en) * | 2008-09-25 | 2009-03-04 | 苏州有色金属研究院有限公司 | Preparation technique capable of effectively controlling Cu-Cr-Zr sheet alloy texture distribution |
| CN102534291A (en) * | 2010-12-09 | 2012-07-04 | 北京有色金属研究总院 | CuCrZr alloy with high strength and high conductivity, and preparation and processing method thereof |
| CN106381414A (en) * | 2016-09-30 | 2017-02-08 | 陕西科技大学 | Copper-based in-situ composite alloy and preparing method thereof |
| US20200377986A1 (en) * | 2017-11-28 | 2020-12-03 | Poongsan Corporation | Method for producing copper-titanium based copper alloy material for automobile and electronic parts and copper alloy material produced therefrom |
| CN108359842A (en) * | 2018-05-31 | 2018-08-03 | 华北水利水电大学 | A kind of polynary cast copper alloy of impeller high-performance and its manufacturing method and application |
| CN111575525A (en) * | 2020-04-16 | 2020-08-25 | 陕西斯瑞新材料股份有限公司 | Method for manufacturing Cu-Cr-Zr alloy contact line for electrified railway |
| 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 |
Also Published As
| Publication number | Publication date |
|---|---|
| CN113832367B (en) | 2022-08-23 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN108486508B (en) | Efficient creep age forming method for aluminum alloy | |
| CN106636734B (en) | High-intensitive, highly conductive, high resistance to stress relaxation copper alloy elastic material and preparation method thereof | |
| CN105609155B (en) | A kind of high-conductivity hard aluminum wire monofilament and preparation method thereof | |
| CN113943874B (en) | Copper alloy material for 5G base station power connector and preparation method thereof | |
| CN108359863B (en) | GIS pipe shell production process | |
| CN109811182A (en) | A kind of aerospace high-intensitive, high conductivity copper alloy stranded conductor and preparation method thereof | |
| CN113817932A (en) | High-strength heat-resistant stress relaxation-resistant copper alloy material and preparation method thereof | |
| CN112011708A (en) | 6-series aluminum alloy material and preparation method thereof | |
| CN114318032B (en) | Preparation method of high-strength high-conductivity copper alloy Cu-Cr-Zr-Nb | |
| CN102586655B (en) | Process for strengthening Al-Sc-Zr conduction alloy and optimizing conductivity | |
| CN113106286B (en) | High-conductivity beryllium copper alloy rod for 5G communication and preparation process thereof | |
| CN107739876A (en) | A kind of polynary low beryllium content copper alloy and preparation method thereof | |
| CN113832367B (en) | Method for preparing CuCrZr alloy by two-stage aging process | |
| CN105838915B (en) | Copper alloy bar, the high current electronic component and heat transmission electronic component for possessing the copper alloy bar | |
| CN113981267B (en) | Copper alloy lead frame material | |
| CN114855026B (en) | High-performance precipitation strengthening type copper alloy and preparation method thereof | |
| CN115261666B (en) | Lead-free high-strength high-conductivity beryllium bronze bar and manufacturing method and application thereof | |
| CN111020277A (en) | Cu-Fe-Co-Ti alloy with high-strength conductivity, softening resistance and stress relaxation resistance | |
| CN110079700A (en) | A kind of TiAl alloy and preparation method thereof | |
| CN112501472B (en) | High-performance copper alloy strip and preparation method thereof | |
| CN111945088B (en) | Heat treatment method of low-alloying Al-Mg-Si alloy | |
| CN113930638B (en) | Preparation method of microalloyed CuCrZr alloy with excellent uniform elongation | |
| CN110306078A (en) | A kind of high strength and high conductivity Cutting free C97 alloy material and preparation method thereof | |
| CN111979447B (en) | High-conductivity copper alloy material and preparation method thereof | |
| CN113403499A (en) | Conductive elastic Cu-Ti-Ni-V alloy and preparation method thereof |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| PB01 | Publication | ||
| PB01 | Publication | ||
| SE01 | Entry into force of request for substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| GR01 | Patent grant | ||
| GR01 | Patent grant |