Preparation method for high-strength and high-conductivity cu-cr-zr-series alloy

Abstract

The present disclosure relates to the technical field of copper alloy processing. Provided in the embodiments of the present disclosure is a preparation method for a high-strength and high-conductivity Cu-Cr-Zr-series alloy. The preparation method comprises: subjecting an alloy to vacuum casting, a hot forging treatment and an aging treatment, wherein the alloy comprises the following components in percentages by mass: 0.50-1.20% of Cr, 0.08-0.25% of Zr, 0.01-0.10% of Nb, and the balance of Cu. The alloy prepared by using the preparation method has both a high strength and a high conductivity. The preparation method of the present disclosure is simple in terms of process, and is easy to operate and implement; and on the premise of shortening the preparation process of the alloy, the method reduces the production cost, and facilitates industrial production and promotion.

Description

Preparation method of high-strength and high-conductivity Cu-Cr-Zr alloy

[0001] Cross-reference to Related Applications

[0002] The present disclosure claims the priority of the Chinese patent application No. 202410523310.5, entitled "Preparation process for improving hardness and electrical conductivity of Cu-Cr-Zr alloy", filed on April 28, 2024 with the China Patent Office, the whole content of which is incorporated herein by reference. TECHNICAL FIELD

[0003] The present disclosure relates to the technical field of copper alloy processing, in particular to a preparation method of high-strength and high-conductivity Cu-Cr-Zr alloy. BACKGROUND

[0004] Cu-Cr-Zr alloy has an inverted relationship between strength and electrical conductivity in terms of important performance indicators, that is, the higher the strength of the alloy, the lower the electrical conductivity. How to make the alloy have high strength and electrical conductivity at the same time is one of the technical problems to be solved at present.

[0005] In view of this, the present disclosure is proposed.

[0006] SUMMARY

[0007] The present disclosure aims to provide a preparation method of high-strength and high-conductivity Cu-Cr-Zr alloy to solve the above technical problems.

[0008] The present disclosure is implemented in this way:

[0009] In a first aspect, the present disclosure provides a preparation method of high-strength and high-conductivity Cu-Cr-Zr alloy, which comprises vacuum melting and casting, hot forging treatment and aging treatment of the alloy; the temperature of vacuum melting and casting is 1200-1400℃, and the time is 1-3h; the temperature of hot forging treatment is 900-1000℃, and the time is 1-3h; the temperature of aging treatment is 370-520℃, and the time is 0.5-10h; the composition of the alloy, by mass fraction, is 0.50-1.20% of Cr, 0.08-0.25% of Zr, 0.01-0.10% of Nb and the balance of Cu.

[0010] The present disclosure has the following beneficial effects:

[0011] The preparation method of the high-strength and high-conductivity Cu-Cr-Zr alloy provided by the present disclosure comprises vacuum melting and casting, hot forging treatment and aging treatment of the alloy, and the prepared alloy has high strength and high conductivity. The preparation method provided by the present disclosure has a simple process and is easy to operate and implement. The preparation process of the alloy is shortened, the production cost is reduced, and the method is easy to industrialize and popularize. BRIEF DESCRIPTION OF DRAWINGS

[0012] In order to more clearly illustrate the technical solutions of the embodiments of the present disclosure, the drawings needed in the embodiments will be briefly introduced as follows. It should be understood that the following drawings only show some embodiments of the present disclosure, and therefore should not be regarded as a limitation on the scope. Other related drawings can also be obtained by those skilled in the art without creative labor on the basis of these drawings.

[0013] Fig. 1 is a schematic diagram of the crystal phase structure of the alloy: (a) before aging treatment, (b) after aging treatment;

[0014] Fig. 2 is a graph of the Rockwell hardness curve and the conductivity curve of the alloy under different vacuum melting and casting temperatures;

[0015] Fig. 3 is a graph of the Rockwell hardness curve and the conductivity curve of the alloy under different hot forging treatment temperatures;

[0016] Fig. 4 is a graph of the Rockwell hardness curve and the conductivity curve of the alloy under different aging treatment temperatures;

[0017] Fig. 5 is a graph of the Rockwell hardness curve and the conductivity curve of the alloy under different aging times. DETAILED DESCRIPTION

[0018] In order to make the purpose, technical solutions and advantages of the embodiments of the present disclosure more clear, the technical solutions in the embodiments of the present disclosure will be clearly and completely described below. If the specific conditions are not specified in the embodiments, the conventional conditions or the conditions recommended by the manufacturer are used. If the reagents or instruments used are not specified by the manufacturer, they are all conventional products that can be purchased on the market.

[0019] The Cu-Cr-Zr alloy is a typical precipitation strengthening alloy. After corresponding aging treatment, Cr particles can be precipitated in the alloy, which plays a role of precipitation strengthening, effectively improves the comprehensive performance, and makes the alloy have high strength and high conductivity.

[0020] The prior art CN107604200B discloses a preparation method of a CuCr alloy with aging enhancement, which utilizes induction melting, atomization powdering, hot pressing sintering and aging treatment to prepare a CuCr alloy, and fine grain structure is obtained in the alloy, so that the electrical conductivity of the alloy reaches 70% IACS-80% IACS, and the hardness reaches 67HRB-70HRB. The prior art CN113832367B discloses a method for preparing a Cu-Cr-Zr alloy by double-stage aging, which utilizes hot deformation, solid solution, cold rolling and double-stage aging treatment to prepare a Cu-Cr-Zr alloy, so as to improve the strength of the alloy and improve the elongation of the alloy, and the electrical conductivity of the alloy is steadily improved.

[0021] Zhao Pengcheng et al. aged Cu-0.8Cr-0.14Zr-0.06Mg at 450℃ for 3h, and the hardness of the alloy reached 78HRB and the electrical conductivity reached 78.5% IACS (Zhao Pengcheng, Chen Jiupang, Lu Ping, Study on Aging Characteristics of Cu-0.8Cr-0.14Zr-0.06Mg Alloy, Metal Functional Materials, 2011, 18(03):25-27.). Wang Jie et al. found that when Cu-0.6Cr-0.09Zr-0.08Mg alloy was aged at 420℃ for 3h, a large number of Cr particles were precipitated in the alloy, so that the hardness of the alloy reached 81HRB while maintaining a high electrical conductivity, and the electrical conductivity reached 76.5% IACS (Wang Jie, Chen Jiupang, Zhao Pengcheng, et al. Effect of Heat Treatment on Properties of Cu-0.6Cr-0.09Zr-0.08Mg Alloy, Heat Treatment Technology, 2011, 40(18):185-187.). Kulczyk et al. aged Cu-Cr-Zr alloy at 480℃ for 1h, due to severe plastic deformation and migration and annihilation of defects, subgrains were transformed into fine grains, and a ultra-fine grain structure was formed in the alloy, the tensile strength of the alloy increased to 625MPa, and the electrical conductivity of the alloy maintained at 78% IACS (Kulczyk M, Pachla W, Godek J, et al. Improved compromise between the electrical conductivity and hardness of the thermo-mechanically treated CuCrZr alloy, Materials Science and Engineering:A, 2018, 724:45-52.).

[0022] The above achievements all adopt aging treatment to improve the comprehensive performance of the Cu-Cr-Zr alloy, but the preparation process is relatively complex, the cost is relatively high, and the aging treatment process period is relatively long and is not easy for industrialized production. Therefore, there are certain limitations and difficulties in actual production and application. It is also one of the technical problems to be solved at present to make the alloy have high strength and high conductivity at the same time.

[0023] In a first aspect, the present disclosure provides a preparation method of a high-strength and high-conductivity Cu-Cr-Zr alloy, which comprises vacuum melting and casting, hot forging treatment and aging treatment of the alloy; the temperature of the vacuum melting and casting is 1200-1400℃, and the time is 1-3h; the temperature of the hot forging treatment is 900-1000℃, and the time is 1-3h; the temperature of the aging treatment is 370-520℃, and the time is 0.5-10h; the composition of the alloy, in terms of mass fraction, is 0.50-1.20% of Cr, 0.08-0.25% of Zr, 0.01-0.10% of Nb and the balance of Cu.

[0024] In an optional embodiment of the present disclosure, the temperature of the vacuum melting and casting can be selected from 1200℃, 1250℃, 1300℃, 1350℃, 1400℃, or other temperature values in the range of 1200-1400℃; the time of the vacuum melting and casting can be selected from 1h, 1.5h, 2h, 2.5h, 3h, or other time values in the range of 1-3h.

[0025] The temperature of the hot forging treatment can be selected from 900℃, 910℃, 930℃, 940℃, 980℃, 1000℃, or other temperature values in the range of 900-1000℃; the time of the hot forging treatment can be selected from 1h, 1.5h, 2h, 2.5h, 3h, or other time values in the range of 1-3h.

[0026] The temperature of the aging treatment can be selected from 370℃, 400℃, 460℃, 490℃, 500℃, 520℃, or other temperature values in the range of 370-520℃; the time of the aging treatment can be selected from 0.5h, 1h, 2h, 4h, 8h, 10h, or other time values in the range of 0.5-10h.

[0027] Vacuum melting is a special melting technology of metal and alloy under vacuum condition, mainly including vacuum induction melting, vacuum arc remelting and electron beam melting. Through strict composition control, vacuum melting can effectively remove gas and reduce non-metallic inclusions, and can volatilize and remove part of harmful metal impurities, so that the purity of the alloy is obviously improved, and the physical and mechanical properties of the steel and alloy are improved. In addition, the temperature of vacuum melting will also have an important influence on the performance of the alloy. If the temperature is lower than the set range, it will cause insufficient reaction of each component in the melt, and if the temperature is higher than the set range, it will cause overburning. The vacuum degree of vacuum melting is 1x10 -3 Pa.

[0028] It should be noted that when the alloy is vacuum melted in the present disclosure, the electrolytic Cu plate is added first, then the Cu-Cr intermediate alloy, the Cu-Zr intermediate alloy and the Cu-Nb intermediate alloy are added, and finally the Nb particles and the Zr particles are added, so as to ensure that all the alloy raw materials are melted as appropriate. The order of adding the Cu-Cr intermediate alloy, the Cu-Zr intermediate alloy and the Cu-Nb intermediate alloy, or the order of adding the Nb particles and the Zr particles can be reasonably adjusted, the main purpose being to melt all the alloy raw materials.

[0029] The present disclosure does not make special limitation on the melting form, which can be reasonably selected according to the actual situation, such as vacuum induction melting, vacuum arc remelting and electron beam remelting, etc. In an optional embodiment of the present disclosure, the equipment for vacuum melting is a vacuum induction melting equipment, and the vacuum induction melting technology is adopted.

[0030] In an optional embodiment of the present disclosure, the vacuum melting adopts inert atmosphere to protect the alloy, and the inert gas used is argon. The inert gas can also be selected from other gases according to actual needs, such as nitrogen, etc.

[0031] Hot forging, also known as hot die forging, is a forging process performed above the recrystallization temperature of the metal. Hot forging treatment can improve the plasticity of the metal, reduce the deformation resistance, make it easy to flow and form, and obtain good forged structure. Therefore, the temperature limit of hot forging treatment is relatively important, and above this temperature range, overheating phenomenon will occur in the growth of the grain size in the alloy, and below this temperature range, the plasticity of the forged piece is poor, and the subsequent deformation is difficult.

[0032] Aging treatment is a heat treatment process, which is mainly to improve the performance of metal and alloy materials. Generally speaking, after aging treatment, the hardness and strength of the material increase, and the plasticity, toughness and internal stress decrease. The temperature and time of aging treatment also have important influence on the performance of the alloy. If the temperature is lower than the set range, the precipitated phase is not easy to precipitate; if the temperature is higher than the set range, the precipitated phase is easy to coarsen. If the time of aging treatment is short, the precipitated phase in the alloy has not been completely precipitated, and the conductivity of the alloy is low; if the time is long, the precipitated phase in the alloy coarsens, which reduces the hardness of the alloy.

[0033] In an optional embodiment of the present disclosure, the temperature of the aging treatment is 400-490℃, and the time is 1-9h.

[0034] In an optional embodiment of the present disclosure, the composition of the alloy is 0.50-0.80% of Cr, 0.08-0.15% of Zr, 0.01-0.03% of Nb and the balance of Cu in terms of mass fraction.

[0035] In an optional embodiment of the present disclosure, the raw materials of each element in the alloy are selected from at least one of electrolytic Cu plate, Cu-Cr intermediate alloy, Cu-Zr intermediate alloy, Cu-Nb intermediate alloy, Nb particles and / or Nb wire, Zr particles and / or Zr wire.

[0036] It should be noted that the addition of Nb element can improve the hardness of Cu-Cr-Zr alloy without sacrificing too much conductivity of the alloy.

[0037] In an optional embodiment of the present disclosure, after the hot forging treatment of the alloy, the alloy is further subjected to solid solution treatment; further, the temperature of the hot forging treatment is 920-970℃, and the time is 1-2h; the temperature of the solid solution treatment is 940-960℃, and the time is 1-2h.

[0038] The solid solution treatment has the following characteristics: adjusting the organizational structure of the material, such as particle size, grain size and lattice stress, to improve the comprehensive performance of the material; improving the plasticity and toughness of the material, preparing for the subsequent precipitation hardening treatment, and improving the strength and hardness of the material; fully dissolving various phases in the material, strengthening the solid solution, and improving the toughness and corrosion resistance of the material, preparing for the subsequent processing and use.

[0039] In addition, the selection of the solid solution treatment temperature should be based on the precipitation and dissolution rules of the phases in the alloy and the use requirements, so as to ensure that the main strengthening phase precipitates under the necessary conditions and maintains appropriate grain size; or adjust the solid solution treatment temperature according to the specific metal material and the required properties, so as to achieve the best structure and performance.

[0040] Specifically, the copper alloy in the present disclosure is treated at the temperature range, so that the microstructure of the material can be effectively adjusted, and the comprehensive performance of the material can be improved. If the temperature is lower than the range, it is difficult to make the alloy achieve excellent performance after subsequent aging treatment; if the temperature is higher than the range, overburning occurs, which reduces the toughness of the alloy.

[0041] In an optional embodiment of the present disclosure, after the solid solution treatment of the alloy, the alloy is further subjected to water quenching treatment and drawing treatment; further, the temperature of the drawing treatment is room temperature.

[0042] It should be noted that the water quenching treatment is carried out at a suitable temperature and speed, which can improve the mechanical properties of the alloy, such as high hardness, high strength and high toughness, etc., and can also avoid deformation and cracking of the alloy. If the water quenching speed is too fast, the alloy is prone to brittleness and internal stress. In the present disclosure, the temperature for water quenching treatment of the alloy casting blank is 930-960℃.

[0043] The drawing treatment of the alloy is to refine it in the radial direction; the refinement in the radial direction and the elongation in the axial direction are beneficial to improve the strength of the material, and are also beneficial to improve the electrical conductivity. In the present disclosure, the drawing treatment is carried out at room temperature, which avoids heating or cooling treatment of the alloy, and can save a lot of energy and processing cost.

[0044] In an optional embodiment of the present disclosure, the deformation amount of the drawing treatment is 30%-40%; the diameter of the alloy rod is 10-20mm.

[0045] The present disclosure does not particularly limit the specific deformation amount of the drawing treatment of the alloy and the diameter of the finally prepared alloy rod, which is related to the equipment specifications used in the subsequent process. However, if the deformation amount is greater than the range, cracks may occur on the surface of the alloy rod, which will affect the performance of the alloy; if the deformation amount is too small, the defects introduced into the alloy are insufficient, and it is difficult to achieve excellent performance after subsequent treatment.

[0046] In an optional embodiment of the present disclosure, the alloy rod is subjected to cutting treatment, and the cutting length is 8-15mm; then the cut alloy rod is subjected to aging treatment.

[0047] In an optional embodiment of the present disclosure, the Rockwell hardness of the alloy is ≥80HRB, and the electrical conductivity is ≥80%IACS.

[0048] In the present disclosure, the preparation method of the Cu-Cr-Zr alloy is comprehensively adjusted, and the prepared alloy has high strength and high electrical conductivity.

[0049] The features and performances of the present disclosure are further described in detail below in combination with embodiments.

[0050] Example 1

[0051] The present embodiment provides a preparation method of a high-strength and high-conductivity Cu-Cr-Zr alloy, which comprises the following preparation steps:

[0052] S1. Selecting electrolytic Cu plate, Cu-Cr intermediate alloy, Nb and Zr particles as raw materials, and performing vacuum casting at a temperature of 1300°C and a vacuum degree of 1x10 -3 Pa, and selecting Ar gas as a protective atmosphere to prepare a Cu-Cr-Zr-Nb alloy cast blank;

[0053] According to the mass fraction, the element composition in the alloy raw material is 0.55% Cr, 0.10% Zr, 0.02% Nb, and the balance of copper.

[0054] S2. The alloy cast blank prepared in step S1 is subjected to hot forging treatment, and the temperature of the hot forging treatment is 940°C and the time is 1h.

[0055] S3. The alloy after the hot forging treatment in step S2 is subjected to solid solution treatment, and the temperature of the solid solution treatment is 960°C and the time is 2h, and then water quenching treatment is performed.

[0056] S4. The alloy after the water quenching treatment in step S3 is subjected to drawing treatment at room temperature to prepare an alloy rod, and the deformation amount of the drawing treatment is 36%, and the diameter of the prepared alloy rod is 16mm.

[0057] S5. The alloy rod prepared in step S4 is subjected to cutting treatment to cut into cylinders with a length of 10mm for standby.

[0058] S6. The cut cylinder in step S5 is subjected to aging treatment, and the temperature of the aging treatment is 460°C and the time is 4h, and the furnace is cooled to room temperature;

[0059] Then, the prepared Cu-Cr-Zr-Nb alloy is subjected to performance test.

[0060] Example 2

[0061] The present embodiment provides a preparation method of a high-strength and high-conductivity Cu-Cr-Zr alloy, which is different from example 1 only in that the temperature of the aging treatment in step S6 is 460°C and the time is 0.5h.

[0062] Example 3

[0063] The present embodiment provides a preparation method of a high-strength and high-conductivity Cu-Cr-Zr alloy, which is different from example 1 only in that the temperature of the aging treatment in step S6 is 460°C and the time is 8h.

[0064] Example 4

[0065] The embodiment provides a preparation method of a high-strength and high-conductivity Cu-Cr-Zr alloy, which is different from the embodiment 1 only in that the aging treatment temperature in the step S6 is 460 DEG C, and the time is 10h.

[0066] Embodiment 5

[0067] The embodiment provides a preparation method of a high-strength and high-conductivity Cu-Cr-Zr alloy, which is different from the embodiment 1 only in that the aging treatment temperature in the step S6 is 490 DEG C, and the time is 4h.

[0068] Embodiment 6

[0069] The embodiment provides a preparation method of a high-strength and high-conductivity Cu-Cr-Zr alloy, which is different from the embodiment 1 only in that the aging treatment temperature in the step S6 is 400 DEG C, and the time is 4h.

[0070] Embodiment 7

[0071] The embodiment provides a preparation method of a high-strength and high-conductivity Cu-Cr-Zr alloy, which is different from the embodiment 1 only in that the vacuum melting temperature in the step S1 is 1350 DEG C.

[0072] Embodiment 8

[0073] The embodiment provides a preparation method of a high-strength and high-conductivity Cu-Cr-Zr alloy, which is different from the embodiment 1 only in that the vacuum melting temperature in the step S1 is 1200 DEG C.

[0074] Embodiment 9

[0075] The embodiment provides a preparation method of a high-strength and high-conductivity Cu-Cr-Zr alloy, which is different from the embodiment 1 only in that the hot forging temperature in the step S2 is 920 DEG C.

[0076] Embodiment 10

[0077] The embodiment provides a preparation method of a high-strength and high-conductivity Cu-Cr-Zr alloy, which is different from the embodiment 1 only in that the hot forging temperature in the step S2 is 970 DEG C.

[0078] Embodiment 11

[0079] The embodiment provides a preparation method of a high-strength and high-conductivity Cu-Cr-Zr alloy, which is different from the embodiment 1 only in that the element components in the step S1 alloy raw material are 0.78% Cr, 0.17% Zr, 0.03% Nb and the balance copper in terms of mass fraction.

[0080] Comparative Example 1

[0081] The embodiment provides a preparation method of a high-strength and high-conductivity Cu-Cr-Zr alloy, which is different from the embodiment 1 only in that Nb element is not used in the step S1, and electrolytic Cu plates, Cu-Cr intermediate alloy and Zr particles are used as raw materials to prepare a Cu-Cr-Zr alloy cast blank.

[0082] The element content of the alloy raw material is 0.60% of Cr, 0.10% of Zr and the balance of copper in terms of mass fraction.

[0083] Comparative Example 2

[0084] The comparative example provides a preparation method of a high-strength and high-conductivity Cu-Cr-Zr alloy, which is different from the embodiment 1 only in that the step S6 is not used, and the alloy is not subjected to aging treatment.

[0085] Test Example 1

[0086] The Cu-Cr-Zr-Nb alloy prepared in the embodiments 1-6 and the Cu-Cr-Zr alloy prepared in the comparative example 1 are subjected to element content determination, and the determination equipment is an inductively coupled plasma atomic emission spectrometer, and the specific setting parameters are as follows: voltage 220 Hv and frequency 50 Hz.

[0087] Test Example 2

[0088] The crystal phase structure of the Cu-Cr-Zr-Nb alloy prepared in the embodiments 1 and 2 is tested, the testing equipment is a LEICA DMI 3000M optical microscope, and the testing setting parameter is 25 DEG C (room temperature). The related results are shown in Fig. 1.

[0089] As shown in Fig. 1, compared with the sample without aging treatment (comparative example 2, Fig. 1a), the Cr particles are uniformly distributed in the alloy after aging treatment (embodiment 1, Fig. 1b), so that the hardness of the alloy is improved, and the precipitation strengthening effect is achieved.

[0090] Test Example 3

[0091] The Cu-Cr-Zr-Nb alloy prepared in the embodiments 1-11 and the Cu-Cr-Zr alloy prepared in the comparative examples 1-2 are subjected to Rockwell hardness and conductivity performance tests, and the test results are shown in Table 2.

[0092] The equipment used for the Rockwell hardness test is an HR-150A Rockwell hardness tester, and the testing setting parameters are as follows: the indenter is a Rockwell B indenter, the test force is 980 N, and the loading time is 15 s; the equipment used for the conductivity test is an FD-101 eddy current conductivity meter, and the testing setting parameters are as follows: the test is conducted at room temperature (25 DEG C).

[0093] Table 2 Alloy performance

[0094] As can be seen from the data of Table 2 Alloy performance, the preparation method of high-strength and high-conductivity Cu-Cr-Zr alloy provided by the present disclosure has greatly improved the performance of the prepared alloy, wherein the addition of Nb element increases the hardness of the Cu-Cr-Zr alloy by 5.5 HRB and reduces the electrical conductivity by 1.2% IACS; after aging treatment, the Rockwell hardness of Example 1 is 19.0 HRB higher than that of Comparative Example 2, and the electrical conductivity of Example 1 is 41.6% IACS higher than that of Comparative Example 2.

[0095] Under different vacuum melting and casting temperatures, the Rockwell hardness of the alloy is maintained at 77.6-84.3 HRB, and the electrical conductivity is maintained at 78.4-83.5% IACS. When the melting and casting temperature is too high (1350℃), overburning occurs, resulting in an alloy Rockwell hardness of only 77.6 HRB (Example 7). When the melting and casting temperature is 1200℃ (Example 8), the components in the melt do not fully react, and the alloy Rockwell hardness is 78.2 HRB. Among them, the alloy has the best performance when melted and cast at 1300℃ (Example 1), with a Rockwell hardness of 84.3 HRB and an electrical conductivity of 83.5% IACS.

[0096] Under different hot forging treatment temperatures, the Rockwell hardness of the alloy is maintained at 77.9-84.3 HRB, and the electrical conductivity is maintained at 79.7% IACS-83.5% IACS. When the hot forging temperature is too high (970℃), the alloy Rockwell hardness decreases to 78.6 HRB. When the hot forging temperature is lower (920℃), the alloy hardness does not reach 80 HRB, only 77.9 HRB. Among them, the alloy has a Rockwell hardness of 84.3 HRB and an electrical conductivity of 83.5% IACS when hot forged at 940℃ (Example 1).

[0097] Under different aging time treatments, the Rockwell hardness of the alloy first increases and then decreases with the increase of the aging time, and the Rockwell hardness reaches 84.3 HRB when the aging treatment time is 4h; under the same aging treatment temperature, the electrical conductivity first increases and then remains stable with the increase of the aging time, and the electrical conductivity reaches 85.1% IACS. For aging treatment temperatures exceeding the set temperature range, the Rockwell hardness and electrical conductivity of the alloy are greatly affected, and it cannot be guaranteed that the hardness of the alloy reaches more than 80 HRB while the electrical conductivity reaches 80% IACS.

[0098] In summary, the disclosure provides a preparation method of a high-strength and high-conductivity Cu-Cr-Zr alloy. The method has a simple process and is easy to operate and implement. Under the comprehensive regulation of vacuum melting, hot forging, solid solution, drawing and aging treatment, the alloy has a Rockwell hardness of 80HRB or more and a conductivity of 80%IACS or more, and a high-strength and high-conductivity Cu-Cr-Zr alloy is prepared. The disclosure shortens the preparation process of the alloy, ensures that the alloy has high strength and conductivity at the same time, reduces production costs, and is easy to industrialize and promote.

[0099] The above only describes preferred embodiments of the disclosure and does not limit the disclosure. Those skilled in the art can make various modifications and changes to the disclosure. Any modifications, equivalent replacements, improvements, etc. made within the spirit and principles of the disclosure shall be included in the protection scope of the disclosure. Industrial applicability

[0100] In summary, the Cu-Cr-Zr alloy provided by the disclosure has high strength and high conductivity, the preparation method thereof has a simple process and is easy to operate and implement, the preparation process of the alloy is shortened, production costs are reduced, and the alloy is easy to industrialize and promote.

Claims

1. A method for producing a high-strength high-conductivity Cu-Cr-Zr alloy, characterized by, The preparation method comprises vacuum melting and casting, hot forging and aging treatment of the alloy; The temperature of the vacuum melting and casting is 1200-1400 DEG C, and the time is 1-3 hours; The temperature of the hot forging is 900-1000 DEG C, and the time is 1-3 hours; The temperature of the aging treatment is 370-520 DEG C, and the time is 0.5-10 hours; The alloy comprises 0.50-1.20% of Cr, 0.08-0.25% of Zr, 0.01-0.10% of Nb and the rest of Cu by mass fraction.

2. The production method according to claim 1, characterized by, The alloy comprises 0.50-0.80% of Cr, 0.08-0.15% of Zr, 0.01-0.03% of Nb and the rest of Cu by mass fraction.

3. The production method according to claim 2, characterized by, The raw materials of the elements in the alloy are selected from at least one of electrolytic Cu plate, Cu-Cr intermediate alloy, Cu-Zr intermediate alloy, Cu-Nb intermediate alloy, Nb particles and / or Nb wire and Zr particles and / or Zr wire.

4. The method of claim 1, wherein, The alloy after the hot forging treatment further comprises solid solution treatment of the alloy.

5. The preparation method according to claim 4, characterized in that, The temperature of the hot forging of the alloy is 920-970 DEG C, and the time is 1-2 hours.

6. The preparation method according to claim 4, characterized in that, The temperature of the solid solution treatment is 940-960 DEG C, and the time is 1-2 hours.

7. The production method according to claim 6, wherein The alloy after the solid solution treatment further comprises water quenching treatment and drawing treatment of the alloy.

8. The preparation method according to claim 7, characterized in that, The temperature of the drawing treatment is room temperature.

9. The preparation method according to claim 7, characterized in that, The deformation of the drawing treatment is 30-40%, and the alloy rod is prepared through the drawing treatment.

10. The method of claim 9, wherein, The diameter of the alloy rod is 10-20 mm.

11. The preparation method according to claim 9, characterized in that, The alloy rod is subjected to cutting treatment, and the cutting length is 8-15 mm; then the cut alloy rod is subjected to aging treatment.

12. The method of claim 11, wherein, The temperature of the aging treatment is 400-490 DEG C, and the time is 1-9 hours.

13. The method of any one of claims 1-12, wherein, The Rockwell hardness of the alloy is greater than or equal to 80 HRB, and the electrical conductivity is greater than or equal to 80% IACS.

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