High-conductivity high-temperature-resistant copper-chromium-zirconium alloy plate as well as preparation method and application thereof

Abstract

The invention discloses a high-conductivity high-temperature-resistant copper-chromium-zirconium alloy plate and a preparation method and application thereof.The high-conductivity high-temperature-resistant copper-chromium-zirconium alloy plate is prepared from, by mass, 0.50 wt%-1.50 wt% of Cr, 0.08 wt%-0.30 wt% of Zr and 98.2 wt%-99.4 wt% of Cu; the structure of the high-conductivity high-temperature-resistant copper-chromium-zirconium alloy plate comprises an S-shaped texture and a Cube-shaped texture, and the volume percent of the S-shaped texture and the volume percent of the Cube-shaped texture are gradually increased in a gradient mode from the inner layer to the surface layer of the high-conductivity high-temperature-resistant copper-chromium-zirconium alloy plate.

Description

Technical Field

[0001] The present invention belongs to the technical field of copper alloys, and particularly relates to a high-conductivity and high-temperature-resistant copper-chromium-zirconium alloy plate and its preparation method and application. Background Art

[0002] The chromium-zirconium-copper alloy system is a typical age-hardening alloy. At present, many patents have reported that by optimizing the aging process, the control of dispersed precipitates is achieved, and then a strength greater than 400 MPa and a conductivity greater than 75% IACS are obtained.

[0003] Chromium-zirconium-copper alloy materials are currently widely used in components such as welding machine electrodes and mold backplates that are used at high temperatures. However, as the heating temperature of equipment such as welding machines becomes higher and higher, not only is it required that the matrix material has good electrical and thermal conductivity to meet its operating conditions, but also the material is required to have high hardness and high-temperature resistance to reduce the deformation of the material under high-temperature use conditions and improve its service life. To obtain a chromium-zirconium-copper alloy plate with both high electrical conductivity, thermal conductivity, and high-temperature resistance, the current mainstream solution is to use a large deformation amount to increase the material hardness and cooperate with an over-aging process for processing.

[0004] The invention patent application with the publication number CN110835699A discloses a high-strength and high-conductivity copper-chromium-zirconium alloy material and its preparation method. The weight percentage composition of this material is: Cr: 0.5 - 1.5%, Zr: 0.05 - 0.3%, Mg: 0.02 - 0.1%, Si: 0.005 - 0.01%, Fe: 0.002 - 0.005%, and the rest is Cu. In addition, the alloy also includes two of the four elements Ti, La, B, and Ca, and the content of each element is 0.001 - 0.005%, and the total content of alloy elements is 0.005 - 0.01%. This material is prepared through melting and casting, hot rolling, surface milling, rough rolling, intermediate annealing, medium rolling, high-temperature rapid solution treatment, finish rolling, and aging treatment.

[0005] The invention patent application with the publication number CN113718129A discloses a chromium-zirconium-copper alloy, characterized in that the mass percentage composition of this chromium-zirconium-copper is Cr: 0.5 - 1.1 wt%, Zr: 0.05 - 0.12 wt%, Si: 0.01 - 0.05 wt%, Mg: 0.005 - 0.01 wt%, and the balance is Cu and unavoidable impurities. The present invention adds Mg and Si on the basis of the traditional chromium-zirconium-copper alloy to refine the material matrix. Its plastic deformation can be dispersed on more grains for more sufficient coordinated deformation, the internal stress is reduced, and the increase in grain boundaries can increase the difficulty of dislocation slip. And it can control the position and size of the precipitates during the aging process of the material to obtain more dispersed and finer precipitates, increasing its strength, plasticity, and high-temperature softening resistance temperature.

[0006] However, for parts with a chromium-zirconium-copper alloy plate prepared by the process disclosed in the above patent application as the substrate, their performance is indeed excellent in the initial stage of use. However, when used under the condition of repeated heating and cooling, due to the relatively large precipitated phases formed by over-aging, the surface hardness will gradually decrease, causing the parts to warp or bend, and ultimately leading to the failure of the components.

[0007] In response to the above problems, microalloying treatment has been carried out on chromium-zirconium-copper materials at home and abroad. However, the addition method, addition quantity, and proportion of the microalloying elements in this method need to be strictly controlled, the stability of industrial production is poor, and the processing cost is additionally increased.

[0008] Therefore, the present invention aims to develop a preparation method for tissue texture regulation to solve the problem of the decrease in hardness of the surface layer of chromium-zirconium-copper plates caused by repeated heating, and further obtain a chromium-zirconium-copper material that takes into account conductivity, high hardness, and good heat resistance to meet the use requirements of welding machine electrodes, mold back plates, etc. Summary of the Invention

[0009] The present invention provides a chromium-zirconium-copper alloy with high conductivity, high hardness, and good heat resistance.

[0010] To solve the above technical problems, the present invention provides a high-conductivity and high-temperature-resistant copper-chromium-zirconium alloy plate. By mass percentage, the components of the high-conductivity and high-temperature-resistant copper-chromium-zirconium alloy plate include Cr: 0.50 - 1.50 wt%, Zr: 0.08 - 0.30 wt%, and Cu: 98.2 - 99.4 wt%.

[0011] The structure of the high-conductivity and high-temperature-resistant copper-chromium-zirconium alloy plate includes S-type texture and Cube-type texture.

[0012] From the inner layer to the surface layer of the high-conductivity and high-temperature-resistant copper-chromium-zirconium alloy plate, the volume percentage ratio of the S-type texture to the Cube-type texture shows a gradient increase.

[0013] As the substrate of the mold back plate, the copper-chromium-zirconium alloy plate prepared by the present invention should have good heat resistance, especially the surface layer should withstand high temperatures for a long time. Otherwise, once the material softens and bends, it will bring great potential safety hazards in use. Compared with the Cube-type texture, the S-type texture has better high-temperature resistance. Therefore, the present invention improves the volume ratio of the S-type texture on the surface layer, so as to obtain better high-temperature resistance on the surface layer of the material.

[0014] Preferably, on the surface layer of the high-conductivity and high-temperature-resistant copper-chromium-zirconium alloy plate, the ratio of the volume percentage of the S-type texture to the Cube-type texture is 1.1 - 1.8.

[0015] In the inner layer of the high-conductivity and high-temperature-resistant copper-chromium-zirconium alloy sheet, the ratio of the volume percentages of the S-type texture and the Cube-type texture is 0.4 - 1.0.

[0016] In the present invention, by controlling the S-type texture in the surface layer within a relatively high content range, the chromium-zirconium alloy sheet provided by the present invention has relatively high strength, hardness, and high-temperature softening resistance performance. If the S-type texture in the surface layer is too high, it will lead to too large a difference in hardness and strength between the surface layer and the inner layer, and there will be processing stress inside the material, which is more likely to cause bending deformation at high temperatures. By controlling the content of the Cube-type texture in the inner layer, the chromium-zirconium alloy sheet provided by the present invention has relatively high conductivity. If the content of the Cube-type texture in the inner layer is too much, the hardness and strength of the inner layer of the material are relatively low, and the uniformity of the material performance is poor, which cannot meet the usage requirements of the product.

[0017] Further preferably, in the surface layer of the high-conductivity and high-temperature-resistant copper-chromium-zirconium alloy sheet, the ratio of the volume percentages of the S-type texture and the Cube-type texture is 1.4 - 1.6, and in the inner layer of the high-conductivity and high-temperature-resistant copper-chromium-zirconium alloy sheet, the ratio of the volume percentages of the S-type texture and the Cube-type texture is 0.5 - 0.8. Under the condition of this ratio range, the high-temperature softening temperature of the material is higher.

[0018] Preferably, in the thickness direction, the surface layer of the high-conductivity and high-temperature-resistant copper-chromium-zirconium alloy sheet is from the sheet surface to -1 / 4T;

[0019] In the thickness direction, the inner layer of the high-conductivity and high-temperature-resistant copper-chromium-zirconium alloy sheet is from 1 / 4T to 3 / 4T, excluding the 1 / 4T and 3 / 4T positions;

[0020] Wherein, T is the thickness of the sheet.

[0021] Preferably, in the high-conductivity and high-temperature-resistant copper-chromium-zirconium alloy sheet, the volume percentage of the S-type texture is 25 - 40%, and the volume percentage of the Cube-type texture is 40 - 60%.

[0022] Preferably, the tensile strength of the high-conductivity and high-temperature-resistant copper-chromium-zirconium alloy sheet is 400 - 490 MPa, the hardness is 125 - 145 HB, the conductivity is 83 - 87% IACS, and the high-temperature softening temperature is 580 °C

[0023] On the other hand, the present invention also provides a preparation method of a high-conductivity and high-temperature-resistant copper-chromium-zirconium alloy sheet. The technological process of the preparation method includes: melting → semi-continuous casting → milling → hot forging → solution treatment → first cold forging → aging treatment → second cold forging → surface machining;

[0024] Among them, batching and melting are carried out according to the mass percentages of the components of the high-conductivity and high-temperature-resistant copper-chromium-zirconium alloy sheet;

[0025] The temperature of the hot forging is 820 - 900 °C, the processing rate of the first cold forging is 15 - 35%, and the processing rate of the second cold forging is 5 - 15%.

[0026] In the present invention, by controlling the temperature of the hot forging, the casting texture inside the blank is transformed into a recrystallization texture (Cube texture), laying a foundation for the subsequent adjustment of the texture. If the temperature of the hot forging is too low, it is not sufficient to transform the casting texture. If the temperature of the hot forging is too high, the proportion of the recrystallization texture is too high, and sufficient processing texture (S-type texture) cannot be obtained during the subsequent cold forging process, resulting in the mechanical properties of the material not meeting the requirements.

[0027] In the present invention, by controlling the processing rate of the first cold forging within a relatively high range, the structure of the blank after solution treatment is elongated along the processing direction, and part of the Cube texture is transformed into an S-type texture. By controlling the processing rate of the second cold forging at a relatively low level, the proportion of the S-type texture on the surface of the blank is relatively high, and the influence on the inner-layer Cube texture is small. Due to the high proportion of the S-type texture on the surface of the blank, the obtained sheet has high strength, hardness, and heat resistance. Also, due to the relatively high proportion of the Cube texture inside the sheet, the conductivity of the sheet is relatively high.

[0028] In the present invention, by controlling the processing rate of the second cold forging at a relatively low level, on the basis of not significantly reducing the electrical conductivity of the material, the high-temperature resistance of the material surface layer is improved. After the above-mentioned second cold forging process, the proportion of the S-type texture in the outer layer in the thickness direction of the material increases, the hardness of the material is increased by 20 - 30 HB, and the high-temperature resistance is better. The high-temperature softening temperature can reach 580 °C, which is higher than 550 °C of the chromium zirconium copper material treated by ordinary aging treatment. And the texture ratio in the inner layer in the thickness direction has no obvious change, ensuring that the electrical conductivity of the material will not decrease significantly.

[0029] When the processing rate of the second cold forging is less than 5%, the change in the proportion of the S-type texture is not significant, and the improvement in the hardness and high-temperature resistance of the material is limited. When the cold forging processing rate is greater than 15%, due to the limited plastic deformation ability of the chromium zirconium copper plate, the material will crack. In summary, the present invention adopts a cold forging processing rate of 5 - 15% to effectively control the proportion of the S-type texture and the Cube texture, thereby improving the high-temperature resistance of the sheet.

[0030] Preferably, the processing rate of the hot forging is 45 - 75%.

[0031] Preferably, the auxiliary tooling and die for the hot forging are preheated to above 250 °C.

[0032] Preferably, the temperature of the solution treatment is 920 - 980 °C.

[0033] The aging effect of copper-chromium-zirconium alloy is closely related to the solution effect. In the present invention, by controlling the temperature of the solution treatment, the Cr element and the Zr element can be fully dissolved, while avoiding obvious grain growth of the material. After the grains become coarse, the performance of the material will significantly decline.

[0034] Preferably, the temperature of the aging treatment is 420 - 500 °C.

[0035] In the present invention, by controlling the temperature of the aging treatment, the Cr element can precipitate to form a strengthening phase, improving the hardness and strength of the material. At the same time, part of the S-type texture in the internal structure can be transformed into Cube texture, so as to increase the content of Cube texture in the inner layer of the blank, thereby improving the conductivity of the sheet; it can also avoid excessive transformation of the S-type texture, resulting in a significant decline in high-temperature resistance.

[0036] Preferably, the charging sequence for melting is as follows: first add electrolytic copper plates, then add copper-chromium and copper-zirconium master alloys required by the composition requirements. Subsequently, heat up to 1250 - 1350 °C. After all the above materials are melted, cover the surface with red-hot charcoal for diffusion deoxidation. Then cool down to 1200 - 1300 °C and conduct direct-reading spectral testing. After the composition is qualified, carry out casting.

[0037] The present invention uses a non-vacuum method to cast copper-chromium-zirconium alloy ingots. Currently, the mainstream copper-chromium-zirconium alloys use vacuum casting, but the vacuum furnace has low production efficiency and high production cost. Moreover, due to the small self-weight of the ingot, it is impossible to manufacture large-size parts. The semi-continuous casting method adopted in the present invention has two major advantages. One is that the self-weight of the ingot can reach more than 3 tons, enabling the processing of large-size parts; the other is that the Zr element is added to the chute in the form of a copper-chromium master alloy during the casting process, solving the problem of Zr element burning loss in non-vacuum casting, ensuring the uniformity of the Zr element in the ingot, and also laying a foundation for subsequent microstructure control; the third is that copper-chromium-zirconium alloys are prone to subcutaneous inclusions during casting, mainly due to the formation of oxides containing Cr or Zr during casting. However, in the present invention, the slag on the upper edge of the mold can be removed in time during casting, greatly reducing the occurrence probability of subcutaneous inclusions in the ingot.

[0038] On the other hand, the present invention also provides the application of the high-conductivity and high-temperature-resistant copper-chromium-zirconium alloy sheet in welding machine electrodes, mold back plates or high-precision mold materials.

[0039] Compared with the prior art, the beneficial effects of the present invention are as follows:

[0040] In the present invention, by controlling the volume percentage of S-type texture and Cube texture, which shows a gradient increasing change from the inner layer to the surface layer of the sheet, the content of S-type texture in the surface layer is relatively high, which is beneficial to improving the strength, hardness and heat resistance of the sheet. At the same time, the content of Cube texture in the inner layer is relatively high, which is beneficial to improving the conductivity of the sheet.

[0041] By controlling the hot forging temperature, a large number of Cube textures are formed inside the blank, laying a foundation for subsequent texture control. By controlling the processing rate of the first cold forging, a partial S-type texture is obtained. Then, through the second cold forging with a lower processing rate, the S-type texture on the surface layer of the sheet is significantly increased, but the influence on the Cube texture of the inner layer of the sheet is minimized as much as possible. Thus, from the inner layer to the surface layer, the mass percentage of the S-type texture and the Cube texture shows a gradient increasing change, which is beneficial to obtaining a chromium-zirconium copper material that takes into account electrical conductivity, high hardness, and good high-temperature resistance performance. Description of the Drawings

[0042] Figure 1 It is a distribution diagram of (A) Cube texture and (B) S-type texture in the outer layer in the thickness direction and (C) Cube texture and (D) S-type texture in the inner layer in the thickness direction of the high-conductivity and high-temperature-resistant copper-chromium-zirconium alloy sheet prepared in Example 1 of the present invention;

[0043] Figure 2 It is a metallographic diagram of the high-conductivity and high-temperature-resistant copper-chromium-zirconium alloy sheet prepared in Example 1 of the present invention. Detailed Embodiments

[0044] The present invention will be further described in detail below in conjunction with the embodiments of the drawings.

[0045] The present invention selects 10 examples and 10 comparative examples for illustration. The mass percentage contents of the chemical components of each example and comparative example are shown in Table 1.

[0046] The examples are prepared according to the following steps:

[0047] 1) Melting: Charge materials according to the charging sequence in the invention content. First, add electrolytic copper plates, and then add copper-chromium and copper-zirconium master alloys required by the component requirements. After the Cr element reaches the specified range, casting is carried out. During melting, first cover with charcoal for diffusion deoxidation, and always keep the charcoal covering the copper melt during melting and casting to inhibit the absorption of gas by the copper melt at high temperatures;

[0048] 2) Semi-continuous casting: The casting temperature is 1200 - 1300 °C, and the casting speed is 60 - 100 mm / min;

[0049] 3) Milling: Each of the upper and lower surfaces of the ingot is milled by 0.5 - 1 mm to remove foreign matters such as oxide scales on the surface layer of the ingot;

[0050] 4) Hot forging: Heat the ingot to 820 - 900 °C and keep it warm for 1 - 2 h, and then carry out hot forging and drawing processing;

[0051] 5) Solution treatment: Heat the hot-forged blank to 920 - 980 °C and hold for 0.5 - 1.5 h, then quickly place it in a water tank with circulating water. It can be taken out of the water tank only when the temperature tested by a handheld temperature gun is lower than 60 °C;

[0052] 6) First cold forging: Perform cold forging and drawing processing with a reduction of 15 - 35% on the solution-treated blank. After processing, use a grinding machine to grind off the heterogeneous points on the surface;

[0053] 7) Aging treatment: Heat the cold-forged blank to 420 - 500 °C, hold for 6 - 18 h, and use a nitrogen atmosphere;

[0054] 8) Second cold forging: Perform cold forging and pressing processing with a reduction of 5 - 15% on the blank after aging treatment;

[0055] 9) Surface processing: According to the part requirements, use turning, milling, sawing, grinding, etc. to process the blank to the required dimensions.

[0056] Table 1 Chemical compositions of examples and comparative examples / wt%

[0057]

[0058]

[0059] Details of the key process operation parameters of the present invention are shown in Table 2, and details of the performance test data of the alloy strip are shown in Table 3.

[0060] The difference between Comparative Example 1 and Example 1 is that the content of Cr element is 5.00 wt%;

[0061] The difference between Comparative Example 2 and Example 1 is that the content of Zr element is 1.00 wt%;

[0062] The difference between Comparative Example 3 and Example 1 is that the hot forging temperature is 950 °C;

[0063] The difference between Comparative Example 4 and Example 1 is that the hot forging reduction rate is 90%;

[0064] The difference between Comparative Example 5 and Example 1 is that the solution temperature is 900 °C;

[0065] The difference between Comparative Example 6 and Example 1 is that the reduction rate of the first cold forging is 10%;

[0066] The difference between Comparative Example 7 and Example 1 is that the reduction rate of the first cold forging is 40%;

[0067] The difference between Comparative Example 8 and Example 1 is that the aging temperature is 400 °C;

[0068] The difference between Comparative Example 9 and Example 1 lies in that the aging temperature is 550°C;

[0069] The difference between Comparative Example 10 and Example 1 lies in that the second cold forging reduction rate is 2%.

[0070] Table 2 Key process parameter control of examples and comparative examples

[0071]

[0072]

[0073] Table 3 Properties of examples and comparative examples

[0074]

[0075]

[0076] The tensile strength, hardness, conductivity, softening temperature and texture ratio of the above examples and comparative examples were analyzed.

[0077] Tensile strength test: Dumbbell-shaped specimens were used and tested on an electronic universal mechanical property testing machine in accordance with "GB / T 228.1-2010 Metallic materials - Tensile testing - Part 1: Method of test at room temperature", and the tensile speed was 5 mm / min.

[0078] Hardness test: Block specimens were used, the specimen size was 2 cm × 2 cm × 2 cm, and after surface polishing, the test was carried out in accordance with "GB / T 231.1-2018 Metallic materials - Brinell hardness test - Part 1: Test method".

[0079] Conductivity test: After the specimen surface was polished, the test was carried out in accordance with "GB / T 32791-2016 Eddy current testing method for electrical conductivity of copper and copper alloys".

[0080] Softening temperature test: Sampling and testing were carried out in accordance with the standard requirements of "GB / T 33370-2016 Test method for softening temperature of copper and copper alloys".

[0081] Average grain size test: Sampling and testing were carried out in accordance with "GB / T 6394-2017 Metallic materials - Determination of average grain size".

[0082] Texture ratio detection: The test was carried out using a FEI Verios G4 field emission scanning electron microscope equipped with an Oxford Symmetry EBSD detector, and the test specimen size was 10 mm × 10 mm × 2 mm.

[0083] Figure 1Distribution diagrams of the Cube texture and S texture in the outer layer in the thickness direction and the corresponding textures in the inner layer in Example 1 Figure 1 For A and B in Figure 1 , the Cube texture ( Figure 1 A in Figure 1 ) and S texture ( Figure 1 B in Figure 1 ) in the outer layer of the plate prepared in Example 1 from the surface to the 1 / 4 thickness in the thickness direction are shown in the distribution diagrams. Figure 1 For C and D in Figure 1 , the Cube texture ( Figure 1 C in Figure 1 ) and S texture ( Figure 1 D in Figure 1 ) in the inner layer of the plate prepared in Example 1, that is, in the thickness range of 1 / 4 thickness - 3 / 4 thickness in the thickness direction (excluding 1 / 4 thickness and 3 / 4 thickness), are shown in the distribution diagrams. According to the EBSD analysis software Channel 5, the volume fraction ratio of the corresponding Cube texture and S texture in the outer layer and inner layer in the thickness direction is calculated to be 1.8 and 1.0 respectively. The chromium zirconium copper alloy plate has good comprehensive properties.

[0084] Figure 2 Microstructure and Cr particle morphology of Example 1 are shown. It can be seen from the figure that the average grain size of the chromium zirconium copper plate is 90 μm. The black particles marked in the figure are Cr particles, and it can be found that the Cr particles are uniformly distributed in a dispersed state in the copper matrix.

[0085] From Comparative Example 1, it can be seen that due to the high content of Cr element, the hardness and strength of the material increase significantly, but the conductivity decreases significantly.

[0086] From Comparative Example 2, it can be seen that although the addition of Zr element has little effect on the properties of the material, serious subsurface slag inclusion occurs during casting, which is not conducive to subsequent hot forging and cold forging processing.

[0087] From Comparative Example 3, it can be seen that when the hot forging temperature is 950 °C, the strength, hardness and high-temperature softening temperature of the material decrease. This is because after the hot forging temperature is too high, obvious grain growth occurs, and the proportion of the S texture also decreases slightly.

[0088] From Comparative Example 4, it can be seen that when the hot forging reduction rate is 90%, cracks occur during hot forging of the material, which does not meet the processing requirements.

[0089] From Comparative Example 5, it can be seen that when the solution temperature is 900 °C, the hardness and strength of the material both decrease. This is because the solid solution effect of the Cr element is poor, and the size of the aging precipitation phase particles is large, so the aging strengthening effect cannot be fully exerted.

[0090] From Comparative Example 6, it can be seen that if the first cold forging reduction rate is 10%, due to the low proportion of the S texture on the surface layer, the hardness and softening temperature of the material are low.

[0091] As can be seen from Comparative Example 7, when the cold forging reduction rate in the first time is 40%, since the proportion of the S-type texture on the surface layer is higher than that of the Cube-type texture, the hardness and strength of the material are higher, but the conductivity decreases significantly and the softening temperature also decreases slightly.

[0092] As can be seen from Comparative Example 8, when the aging temperature is 400 °C, since fewer Cr particles precipitate and the aging effect cannot be fully exerted, the hardness and strength of the material are lower.

[0093] As can be seen from Comparative Example 9, when the aging temperature is 550 °C, the S-type texture on the surface layer will transform into a Cube texture, resulting in a decrease in the ratio of the two on the surface layer and a decrease in the softening temperature of the material.

[0094] As can be seen from Comparative Example 10, when the cold forging reduction rate in the second time is 2%, the proportion of the S-type texture in the outer layer in the thickness direction of the material is relatively low, and both the hardness and the high-temperature softening resistance temperature of the material are low.

Claims

1. A high-conductivity, high-temperature-resistant copper-chromium-zirconium alloy sheet, characterized in that: In terms of mass percentage, the components of the high-conductivity and high-temperature-resistant copper-chromium-zirconium alloy plate include Cr: 0.50-1.50wt%, Zr: 0.08-0.30wt%, and Cu: 98.2-99.4wt%; The microstructure of the high-conductivity and high-temperature-resistant copper-chromium-zirconium alloy plate includes an S-type texture and a Cube-type texture; From the inner layer to the surface layer of the high-conductivity and high-temperature-resistant copper-chromium-zirconium alloy plate, the volume percentages of the S-type texture and the Cube-type texture increase gradually.

2. The high-conductivity, high-temperature-resistant copper-chromium-zirconium alloy sheet according to claim 1, characterized in that: In the surface layer of the high-conductivity and high-temperature-resistant copper-chromium-zirconium alloy plate, the volume percentage ratio of the S-type texture to the Cube-type texture is 1.1-1.8; In the inner layer of the high-conductivity and high-temperature-resistant copper-chromium-zirconium alloy plate, the volume percentage ratio of the S-type texture to the Cube-type texture is 0.4-1.

0.

3. The high-conductivity, high-temperature-resistant copper-chromium-zirconium alloy sheet material according to claim 2, characterized in that: In the surface layer of the high-conductivity and high-temperature-resistant copper-chromium-zirconium alloy plate, the volume percentage ratio of the S-type texture to the Cube-type texture is 1.4-1.6, and in the inner layer of the high-conductivity and high-temperature-resistant copper-chromium-zirconium alloy plate, the volume percentage ratio of the S-type texture to the Cube-type texture is 0.5-0.

8.

4. The high-conductivity, high-temperature-resistant copper-chromium-zirconium alloy sheet material according to claim 1, characterized in that: In the thickness direction, the surface layer of the high-conductivity and high-temperature-resistant copper-chromium-zirconium alloy plate is the plate surface - 1 / 4T; In the thickness direction, the inner layer of the high-conductivity and high-temperature-resistant copper-chromium-zirconium alloy plate is 1 / 4T-3 / 4T, excluding 1 / 4T and 3 / 4T; Where T is the thickness of the plate.

5. The high-conductivity, high-temperature-resistant copper-chromium-zirconium alloy sheet according to claim 1, characterized in that: In the high-conductivity and high-temperature-resistant copper-chromium-zirconium alloy plate, the volume percentage of the S-type texture is 25-40%, and the volume percentage of the Cube-type texture is 40-60%.

6. A method for preparing a high-conductivity, high-temperature-resistant copper-chromium-zirconium alloy sheet according to any one of claims 1 to 5, characterized in that: The process flow of the preparation method includes: smelting → semi-continuous casting → milling → hot forging → solution treatment → first cold forging → aging treatment → second cold forging → surface processing; Wherein, the ingredients are prepared and smelted according to the mass percentage of each component of the high-conductivity and high-temperature-resistant copper-chromium-zirconium alloy plate according to any one of claims 1 to 5; The temperature of the hot forging is 820-900° C., the processing rate of the first cold forging is 15-35%, and the processing rate of the second cold forging is 5-15%.

7. The method for preparing the high-conductivity and high-temperature-resistant copper-chromium-zirconium alloy sheet according to claim 6, characterized in that: The processing rate of the hot forging is 45-75%.

8. The method for preparing the high-conductivity and high-temperature-resistant copper-chromium-zirconium alloy sheet according to claim 6, characterized in that: The temperature of the solution treatment is 920-980°C.

9. The method for preparing the high-conductivity and high-temperature-resistant copper-chromium-zirconium alloy sheet according to claim 6, characterized in that: The temperature of the aging treatment is 420-500°C.

10. Use of the high-conductivity and high-temperature-resistant copper-chromium-zirconium alloy plate according to any one of claims 1 to 5 in welding machine electrodes, crystallizer back plates or high-precision mold materials.

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