CN114107713A - Preparation method of high-temperature-resistant CuCrNb alloy - Google Patents
Preparation method of high-temperature-resistant CuCrNb alloy Download PDFInfo
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- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 109
- 239000000956 alloy Substances 0.000 title claims abstract description 109
- 238000002360 preparation method Methods 0.000 title claims abstract description 27
- 238000005245 sintering Methods 0.000 claims abstract description 78
- 239000000843 powder Substances 0.000 claims abstract description 54
- 238000000034 method Methods 0.000 claims abstract description 44
- 238000005098 hot rolling Methods 0.000 claims abstract description 24
- 230000008569 process Effects 0.000 claims abstract description 20
- 238000009689 gas atomisation Methods 0.000 claims abstract description 19
- 230000032683 aging Effects 0.000 claims abstract description 16
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims abstract description 7
- 229910002804 graphite Inorganic materials 0.000 claims abstract description 7
- 239000010439 graphite Substances 0.000 claims abstract description 7
- 238000005303 weighing Methods 0.000 claims abstract description 5
- 238000011068 loading method Methods 0.000 claims abstract description 4
- 238000004321 preservation Methods 0.000 claims description 14
- 239000010955 niobium Substances 0.000 claims description 8
- 239000007789 gas Substances 0.000 claims description 7
- 230000008859 change Effects 0.000 claims description 6
- 239000011651 chromium Substances 0.000 claims description 6
- 239000010949 copper Substances 0.000 claims description 6
- 238000002490 spark plasma sintering Methods 0.000 claims description 6
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 claims description 5
- 239000001301 oxygen Substances 0.000 claims description 5
- 229910052760 oxygen Inorganic materials 0.000 claims description 5
- 238000005096 rolling process Methods 0.000 claims description 5
- 239000012300 argon atmosphere Substances 0.000 claims description 4
- 229910052804 chromium Inorganic materials 0.000 claims description 4
- 229910052802 copper Inorganic materials 0.000 claims description 4
- 238000002844 melting Methods 0.000 claims description 4
- 230000008018 melting Effects 0.000 claims description 4
- 229910052758 niobium Inorganic materials 0.000 claims description 4
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 claims description 3
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 claims description 3
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 claims description 3
- 238000012216 screening Methods 0.000 claims description 3
- 229910000881 Cu alloy Inorganic materials 0.000 abstract description 16
- 238000012545 processing Methods 0.000 abstract description 5
- 238000005516 engineering process Methods 0.000 abstract description 3
- 238000010438 heat treatment Methods 0.000 description 11
- 238000011056 performance test Methods 0.000 description 8
- 229910017813 Cu—Cr Inorganic materials 0.000 description 5
- 238000001816 cooling Methods 0.000 description 4
- 239000006104 solid solution Substances 0.000 description 4
- 238000005728 strengthening Methods 0.000 description 4
- 238000012360 testing method Methods 0.000 description 4
- 230000000052 comparative effect Effects 0.000 description 3
- 238000011161 development Methods 0.000 description 3
- 230000018109 developmental process Effects 0.000 description 3
- 239000000463 material Substances 0.000 description 3
- 230000007246 mechanism Effects 0.000 description 3
- 238000002156 mixing Methods 0.000 description 3
- 238000001556 precipitation Methods 0.000 description 3
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 238000002474 experimental method Methods 0.000 description 2
- 239000011159 matrix material Substances 0.000 description 2
- 238000005259 measurement Methods 0.000 description 2
- 239000007787 solid Substances 0.000 description 2
- 229910017755 Cu-Sn Inorganic materials 0.000 description 1
- 229910017770 Cu—Ag Inorganic materials 0.000 description 1
- 229910017824 Cu—Fe—P Inorganic materials 0.000 description 1
- 229910017818 Cu—Mg Inorganic materials 0.000 description 1
- 229910017876 Cu—Ni—Si Inorganic materials 0.000 description 1
- 229910017927 Cu—Sn Inorganic materials 0.000 description 1
- 229910052786 argon Inorganic materials 0.000 description 1
- 239000012298 atmosphere Substances 0.000 description 1
- 238000000889 atomisation Methods 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 229910002056 binary alloy Inorganic materials 0.000 description 1
- 238000006555 catalytic reaction Methods 0.000 description 1
- 238000002485 combustion reaction Methods 0.000 description 1
- 150000001875 compounds Chemical class 0.000 description 1
- KUNSUQLRTQLHQQ-UHFFFAOYSA-N copper tin Chemical compound [Cu].[Sn] KUNSUQLRTQLHQQ-UHFFFAOYSA-N 0.000 description 1
- 230000007423 decrease Effects 0.000 description 1
- 230000004927 fusion Effects 0.000 description 1
- 230000017525 heat dissipation Effects 0.000 description 1
- 230000006872 improvement Effects 0.000 description 1
- 229910001068 laves phase Inorganic materials 0.000 description 1
- 238000004519 manufacturing process Methods 0.000 description 1
- 230000000087 stabilizing effect Effects 0.000 description 1
- 229910052726 zirconium Inorganic materials 0.000 description 1
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- B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
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Abstract
The invention discloses a preparation method of a high-temperature-resistant CuCrNb alloy, which comprises the following steps: s1, preparing CuCrNb alloy powder by a plasma rotation gas atomization method to obtain gas atomization CuCrNb alloy powder; s2, weighing the gas atomized CuCrNb alloy powder prepared in the step S1 according to the designed weight, loading the weighed powder into a graphite die, and sintering according to a sintering process to obtain a sintered sample block; s3, carrying out hot rolling treatment on the sintered sample block to obtain a CuCrNb alloy hot rolling sample plate; and S4, carrying out aging treatment on the CuCrNb alloy hot-rolling sample plate to obtain the CuCrNb alloy. The invention has simple processing technology and strong operability, has better conductivity and strength in high temperature environment compared with the prior high-strength high-conductivity copper alloy, has outstanding high temperature softening resistance and plays a great role in the field of high temperature application.
Description
Technical Field
The invention relates to the technical field of copper alloy preparation, in particular to a preparation method of a high-temperature-resistant CuCrNb alloy.
Background
The high-strength and high-conductivity copper alloy is widely applied to various high-tech fields such as integrated circuit lead frames, high-speed railway contact network cables, nuclear fusion heat dissipation materials and the like due to excellent performance. The strengthening mechanism of the high-strength and high-conductivity copper alloy mainly comprises the following two mechanisms: (1) solid solution strengthened copper alloys such as Cu-Sn, Cu-Ag, Cu-Mg alloys, etc.; (2) precipitation-strengthened copper alloys such as Cu-Cr, Cu-Fe-P, Cu-Ni-Si alloys, and the like. Due to the influence of solid solution atoms in the matrix, it is difficult to simultaneously achieve high strength and high conductivity in the solid solution strengthened copper alloy. In contrast, precipitation-strengthened copper alloys have better performance due to the contribution of the Orowan strengthening mechanism and the precipitation of solid solution atoms from the matrix after aging, which can improve the strength and conductivity of the alloy.
However, with the rapid development of the aerospace field, more stringent requirements are placed on the performance of copper alloys, and not only good electrical conductivity and thermal conductivity, but also excellent high temperature resistance and the like are required. The Cu-Cr alloy is a typical precipitation strengthening copper alloy, and has excellent comprehensive performance due to precipitation of Cr after aging. However, at high temperature, the structure is rapidly coarsened, so that the softening resistance is poor, and the application field and range are limited. The addition of Zr element can raise the softening resisting temperature of the alloy to 500 deg.c, but its strength decreases sharply with the raising of the temperature.
It is reported that Nb is added into Cu-Cr alloy, which can inhibit the catalysis of Cu-Cr alloy; no intermediate compound is generated in a Cu-Nb binary system, and the solid solubility of Nb in Cu at room temperature is low. Whereas Cr and Nb in Cu-Cr alloys can only form the Laves phase Cr2 Nb. Cr2Nb is stable below 1700 ℃ and insoluble in solid Cu. The formed Cr2Nb strengthening phase can refine the grain size, thereby further improving the strength of the copper alloy. Therefore, the CuCrNb serving as a novel high-temperature-resistant copper alloy has very great development potential in various fields, particularly in a high-temperature environment, and the application field and range of the copper alloy can be further expanded.
The material is developed in many developed countries, widely applied to the field of aerospace, and related technologies are blocked. Therefore, the technical problem is urgently needed to be overcome, and the preparation of the novel high-temperature-resistant CuCrNb alloy makes a contribution to the development of the aerospace field.
Disclosure of Invention
In order to solve the technical problem, the invention provides a preparation method of a high-temperature-resistant CuCrNb alloy.
The technical scheme of the invention is as follows: a preparation method of a high-temperature-resistant CuCrNb alloy comprises the following steps:
s1 preparation of CuCrNb alloy powder by plasma rotary gas atomization
Preparing CuCrNb alloy powder by a plasma rotary gas atomization method, assembling the prepared CuCrNb alloy electrode rod into a feeding device, melting the alloy in a high-vacuum argon atmosphere, and preparing alloy powder by high-speed rotation to obtain gas atomized CuCrNb alloy powder;
s2 spark plasma sintering
Weighing the gas atomized CuCrNb alloy powder prepared in the step S1 according to the designed weight, loading the weighed powder into a graphite die, and sintering according to a sintering process to obtain a sintered sample block;
s3 Hot Rolling
Preserving the temperature of the sintered sample block at 800-900 ℃ for 30-50min, carrying out hot rolling treatment after the preservation time is up, and obtaining a CuCrNb alloy hot rolling sample plate by carrying out single-pass rolling with the deformation of 53%;
s4 aging treatment
And (3) carrying out aging treatment on the CuCrNb alloy hot-rolling sample plate according to the temperature of 400-.
Further, the step S1 of preparing the CuCrNb alloy powder by the plasma rotary gas atomization method specifically includes processing a CuCrNb alloy ingot into a CuCrNb alloy electrode rod, heating and melting the CuCrNb alloy electrode rod in a high vacuum argon atmosphere by matching with a feeding device of a plasma rotary atomization powder preparation device, rotating the CuCrNb alloy electrode rod at a high speed, finally obtaining spherical powder with two specifications of less than 50 μm and 50-150 μm by screening, preparing the CuCrNb alloy powder by plasma rotary gas atomization, wherein the prepared powder has a high sphericity, so that a CuCrNb alloy with better performance is obtained in subsequent sintering preparation, and the density of a sintered sample block after powder sintering can be effectively improved by doping and mixing the spherical powder with the two specifications.
Further, the air-atomized CuCrNb alloy powder in the step S2 is prepared by the following steps by weight: 3 wt.% of chromium, 2.5 wt.% of niobium and the balance of copper, and the CuCrNb alloy powder prepared by adopting the mass ratio has better conductivity and use effect.
Further, the preparation parameters of the powder prepared by the plasma rotary gas atomization method in the step S1 are as follows: 13000-18000r/min, 2400-2600A, 1.2-1.6mm/s of feeding speed and 0.55-0.60ppm of oxygen, and spherical powder with high sphericity and two specifications of granularity of less than 50 μm and 50-150 μm can be stably obtained by the preparation parameters.
Further, in the step S2, the diameter of the graphite mold in spark plasma sintering is
The powder amount is 176g, and the sintering process comprises the following steps: the sintering pressure is 45-60bar, the sintering temperature is 700-.
Furthermore, the sintering process specifically comprises the following steps: and (3) pressurizing at 55 +/-0.5 bar for 10min at the beginning of sintering, then reducing the pressure to 45 +/-0.5 bar for carrying out pressure stabilizing sintering treatment, and increasing the pressure to 60 +/-0.5 bar 3min before the end of sintering until the end of sintering, wherein in the sintering treatment, the sintering treatment is carried out by changing the sintering pressure, so that the performances of density, conductivity and the like of a sintered sample block obtained by the sintering treatment can be enhanced according to the continuation of the sintering stage.
Furthermore, the sintering temperature of the sintering process is dynamically adjusted according to a sintering pressure variation curve, wherein the dynamic adjustment of the temperature along with the pressure variation curve satisfies the following formula, specifically:
wherein C represents the sintering temperature, P represents the sintering pressure, Pv represents the vacuum degree, j represents a constant, and the value is 2. According to the test, the dynamic temperature adjustment along with the sintering pressure change curve can keep the CuCrNb alloy powder in a better sintering temperature range under the corresponding sintering pressure condition, so that the electrical conductivity and other properties of the prepared CuCrNb alloy are obviously improved.
Further, the density of the sintered sample block obtained in the step S2 spark plasma sintering is greater than 99.5%.
The invention has the beneficial effects that: according to the preparation method of the high-temperature-resistant CuCrNb alloy, the produced CuCrNb alloy is simple in processing technology and strong in operability, and has better conductivity and strength in a high-temperature environment compared with the existing high-strength high-conductivity copper alloy such as the CuCrZr alloy; the high-temperature-resistant copper alloy has outstanding high-temperature-resistant softening capability, exerts excellent performance in a high-temperature environment, can replace the traditional high-strength high-conductivity copper alloy, and plays a great role in the field of high-temperature application, such as being used as a lining material of a rocket engine combustion chamber and the like.
Drawings
FIG. 1 is a flow chart of a preparation method of the high temperature resistant CuCrNb alloy.
Detailed Description
The present invention will be described in further detail with reference to specific embodiments thereof for better understanding the advantages of the invention.
Example 1
A preparation method of a high-temperature resistant CuCrNb alloy is shown in figure 1 and comprises the following steps:
s1 preparation of CuCrNb alloy powder by plasma rotary gas atomization
Processing a CuCrNb alloy ingot into a CuCrNb alloy electrode rod, preparing CuCrNb alloy powder by a plasma rotary gas atomization method, assembling the prepared CuCrNb alloy electrode rod into a feeding device, melting the alloy under the atmosphere of high vacuum argon gas, preparing alloy powder by high-speed rotation, finally obtaining spherical powder with two specifications of less than 50 mu m and 50-150 mu m by screening, and mixing the spherical powder with equal mass ratio to obtain gas atomized CuCrNb alloy powder; the CuCrNb alloy powder is prepared by adopting plasma rotary gas atomization, the prepared powder has high sphericity, so that CuCrNb alloy with better performance is obtained in subsequent sintering preparation, and the density of a sintered sample block after powder sintering can be effectively improved by doping and mixing spherical powder with two specifications;
wherein the preparation parameters of the powder prepared by the plasma rotary gas atomization method are as follows: the rotating speed is 15000r/min, the current is 2500A, the feeding speed is 1.5mm/s, the oxygen content is 0.58ppm, and spherical powder with high sphericity and granularity of less than 50 μm and 50-150 μm can be stably obtained through the preparation parameters;
s2 spark plasma sintering
Weighing the gas atomized CuCrNb alloy powder prepared in the step S1 according to the designed weight, wherein the weight percentages are as follows: weighing 3 wt.% of chromium, 2.5 wt.% of niobium and the balance of copper, then loading into a graphite die, and sintering according to a sintering process to obtain a sintered sample block; by adopting the mass ratio of the CuCrNb alloy powder, the prepared CuCrNb alloy has better conductivity and use effect;
wherein the graphite mold has a diameter of
The powder amount is 176g, and the sintering process comprises the following steps: sintering at 850 deg.c under 50bar pressure for 5min and 0.6bar vacuum degree to obtain sintered sample block with density over 99.5%;
s3 Hot Rolling
Keeping the temperature of the sintered sample block at 850 ℃ for 40min, carrying out hot rolling treatment after the heat preservation time is up, carrying out single-pass rolling with the deformation of 53%, and carrying out hot rolling only once to obtain a CuCrNb alloy hot rolling sample plate;
s4 aging treatment
And (4) carrying out aging treatment on the CuCrNb alloy hot-rolling sample plate according to the temperature of 430 ℃ and the heat preservation time of 4h, and cooling along with the furnace after the heat preservation time is up to obtain the CuCrNb alloy.
Example 2
This example is substantially the same as example 1, except that the pressure in the sintering process is changed according to the sintering time, specifically: the sintering starts to be pressurized at 55bar for 10min, then the pressure is reduced to 45bar, the pressure is increased to 60bar for 3min before the sintering is finished, and the sintering is carried out by changing the sintering pressure in the sintering treatment, so that the performances of density, conductivity and the like of a sintered sample block obtained by the sintering treatment can be enhanced according to the continuity of the sintering stage;
the sintering temperature of the sintering process is dynamically adjusted according to a sintering pressure change curve, wherein the temperature is dynamically adjusted along with the pressure change curve to meet the following formula, and the formula is specifically as follows:
wherein C represents sintering temperature, P represents sintering pressure, Pv represents vacuum degree, j represents constant, and the value is 2; according to the test, the dynamic temperature adjustment along with the sintering pressure change curve can keep the CuCrNb alloy powder in a better sintering temperature range under the corresponding sintering pressure condition, so that the electrical conductivity and other properties of the prepared CuCrNb alloy are obviously improved.
Example 3
This example is substantially the same as example 1, except that the plasma rotary gas atomization method is used to prepare the powder according to the following preparation parameters: 13000r/min of rotation speed, 2400A of current, 1.2mm/s of feeding speed and 0.55ppm of oxygen content.
Example 4
This example is substantially the same as example 1, except that the plasma rotary gas atomization method is used to prepare the powder according to the following preparation parameters: 18000r/min, 2600A current, 1.6mm/s feeding speed and 0.60ppm oxygen content.
Example 5
This example is substantially the same as example 1, except that the sintering process is: sintering pressure is 45bar, sintering temperature is 700 ℃, heat preservation time is 3min, vacuum degree is 0.5bar, and sintering sample blocks with density of more than 99.5% are prepared through the sintering process.
Example 6
This example is substantially the same as example 1, except that the sintering process is: sintering pressure is 60bar, sintering temperature is 1100 ℃, heat preservation time is 8min, vacuum degree is 0.8bar, and sintering sample blocks with density of more than 99.5% are prepared through the sintering process.
Example 7
This example is substantially the same as example 1, except that S3, hot rolling treatment: and (3) preserving the temperature of the sintered sample block at 800 ℃ for 30min, carrying out hot rolling treatment after the preservation time is up, carrying out single-pass rolling with the deformation of 53%, and carrying out hot rolling only once to obtain the CuCrNb alloy hot rolling sample plate.
Example 8
This example is substantially the same as example 1, except that S3, hot rolling treatment: and (3) preserving the temperature of the sintered sample block at 900 ℃ for 50min, carrying out hot rolling treatment after the preservation time is up, carrying out single-pass rolling with the deformation of 53%, and carrying out hot rolling only once to obtain the CuCrNb alloy hot rolling sample plate.
Example 9
This example is substantially the same as example 1, except that S4 and the aging treatment: and (3) carrying out aging treatment on the CuCrNb alloy hot-rolling sample plate according to the temperature of 400 ℃ and the heat preservation time of 3h, and cooling along with the furnace after the heat preservation time is up to obtain the CuCrNb alloy.
Example 10
This example is substantially the same as example 1, except that S4 and the aging treatment: and (3) carrying out aging treatment on the CuCrNb alloy hot-rolling sample plate according to the temperature of 500 ℃ and the heat preservation time of 5h, and cooling along with the furnace after the heat preservation time is up to obtain the CuCrNb alloy.
Examples of the experiments
Alloy samples were prepared by taking example 1 as an example, and the properties of the CuCrNb alloy before and after the high temperature heat treatment were compared while aging the cold-forged CuCrZr ingot in step S4 of example 1 as comparative example 1,
wherein, the CuCrZr cast ingot is CuCr1Zr with German standard mark, Cr: 0.7-1.1%, Zr: 0.04-0.15%, the balance less than or equal to 0.2%, Cu: the balance of the weight percentage is as follows,
performing high-temperature heat treatment on the CuCrNb alloy aging sample plate at 950 ℃ for 25min, and cooling along with the furnace after the heat treatment time is up to obtain each alloy sample; the performance test results are shown in the following table 1:
table 1 results of performance test of samples of example 1 and comparative example 1
And (4) conclusion: as can be seen from the comparison in Table 1, the samples in example 1 have higher Brinell hardness and conductivity than those in comparative example 1 after the high temperature heat treatment, and thus, example 1 has better high temperature resistance.
Meanwhile, in order to further explore the influence of different process steps on the performance of the prepared CuCrNb alloy, the following exploration experiments are carried out:
explore 1 the influence of different sintering processes on the performance of the CuCrNb alloy
Taking examples 1 and 2 as examples, alloy samples were prepared and tested according to the same method as above, and the performance test results are shown in table 2 below:
table 2 results of performance tests of samples of examples 1 and 2
And (4) conclusion: as shown by the comparison in Table 2, the sample of example 2 has higher Brinell hardness and conductivity than those of example 1 after the high temperature heat treatment, and thus, example 2 has better high temperature resistance.
The influence of the preparation parameters of 2 different plasma rotary gas atomization methods for preparing the powder on the performance of the CuCrNb alloy is explored
Taking examples 1, 3 and 4 as examples, alloy samples were prepared and tested according to the same method as above, and the performance test results are shown in table 3 below:
table 3 results of performance tests of samples of examples 1, 3 and 4
And (4) conclusion: as can be seen from the comparison in table 3 above, the sample of example 1 has higher brinell hardness and conductivity than those of examples 3 and 4 after high temperature heat treatment, and thus, example 1 has better high temperature resistance.
The influence of different sintering process parameters on the performance of the CuCrNb alloy is explored 3
Taking examples 1, 5 and 6 as examples, alloy samples were prepared and tested according to the same method as above, and the performance test results are shown in table 4 below:
table 4 results of property measurements of samples of examples 1, 5 and 6
And (4) conclusion: as can be seen from the comparison in table 4 above, the brinell hardness and the electrical conductivity of the sample of example 1 after the high temperature heat treatment are both higher than those of example 5, and the brinell hardness and the electrical conductivity of the samples of examples 6 and 1 after the high temperature heat treatment are both improved, but the improvement is not obvious, and the sample of example 1 is better from the economic point of the production process cost and the like.
The influence of 4 different hot rolling processing parameters on the performance of the CuCrNb alloy is explored
Taking examples 1, 7 and 8 as examples, alloy samples were prepared and tested for their properties in the same manner as described above, and the results of the property tests are shown in table 5 below:
table 5 results of performance test of samples of examples 1, 7 and 8
And (4) conclusion: as shown by the comparison in Table 5, the samples in example 1 have higher Brinell hardness and conductivity than those in examples 7 and 8 after high temperature heat treatment, so that example 1 has better high temperature resistance.
The influence of different aging treatment parameters on the performance of the CuCrNb alloy is explored 5
Taking examples 1 and 9, 10 as examples, alloy samples were prepared and tested for their properties in the same manner as described above, and the results of the property tests are shown in table 6 below:
table 6 results of property measurements of samples of examples 1, 9 and 10
And (4) conclusion: as shown by the comparison in Table 6, the samples in example 1 have higher Brinell hardness and conductivity than those in examples 9 and 10 after heat treatment at high temperature, so that example 1 has better high temperature resistance.
Claims (9)
1. The preparation method of the high-temperature-resistant CuCrNb alloy is characterized by comprising the following steps of:
s1 preparation of CuCrNb alloy powder by plasma rotary gas atomization
Preparing CuCrNb alloy powder by a plasma rotary gas atomization method, assembling the prepared CuCrNb alloy electrode rod into a feeding device, melting the alloy in a high-vacuum argon atmosphere, and preparing alloy powder by high-speed rotation to obtain gas atomized CuCrNb alloy powder;
s2 spark plasma sintering
Weighing the gas atomized CuCrNb alloy powder prepared in the step S1 according to the designed weight, loading the weighed powder into a graphite die, and sintering according to a sintering process to obtain a sintered sample block;
s3 Hot Rolling
Preserving the temperature of the sintered sample block at 800-900 ℃ for 30-50min, carrying out hot rolling treatment after the preservation time is up, and obtaining a CuCrNb alloy hot rolling sample plate by carrying out single-pass rolling with the deformation of 53%;
s4 aging treatment
And (3) carrying out aging treatment on the CuCrNb alloy hot-rolling sample plate according to the temperature of 400-.
2. The method for preparing the high-temperature-resistant CuCrNb alloy according to claim 1, wherein the step S1 of preparing the CuCrNb alloy powder by the plasma rotary gas atomization method is to process a CuCrNb alloy ingot into a CuCrNb alloy electrode rod, to heat and melt the CuCrNb alloy electrode rod in a high-vacuum argon atmosphere by matching with a feeding device, to rotate at a high speed, and to obtain spherical powder with two specifications of less than 50 μm and 50-150 μm by screening.
3. The method for preparing the high-temperature-resistant CuCrNb alloy as recited in claim 1, wherein in the step S2, the air-atomized CuCrNb alloy powder comprises the following components in percentage by mass: 3 wt.% chromium, 2.5 wt.% niobium, and balance copper.
4. The method for preparing the high-temperature-resistant CuCrNb alloy according to claim 1, wherein the preparation parameters of the powder prepared by the plasma rotary gas atomization method in the step S1 are as follows: 13000-18000r/min, 2400-2600A, 1.2-1.6mm/s of feeding speed and 0.55-0.60ppm of oxygen content.
5. The method for preparing the high-temperature-resistant CuCrNb alloy according to claim 1, wherein the diameter of the graphite mold in the step S2 of spark plasma sintering is equal to
The powder amount is 176g, and the sintering process comprises the following steps: the sintering pressure is 45-60bar, the sintering temperature is 700-1100 ℃, the heat preservation time is 3-8min, and the vacuum degree is 0.5-0.8 bar.
6. The preparation method of the high-temperature-resistant CuCrNb alloy according to claim 5, characterized in that the sintering process specifically comprises the following steps: pressurizing at 55 + -0.5 bar for 10min at the beginning of sintering, then reducing the pressure to 45 + -0.5 bar for steady-pressure sintering treatment, and increasing the pressure to 60 + -0.5 bar 3min before sintering till the end of sintering.
7. The method for preparing the high-temperature-resistant CuCrNb alloy according to claim 6, characterized in that the sintering temperature of the sintering process is dynamically adjusted according to a sintering pressure change curve, wherein the dynamic adjustment of the temperature along with the pressure change curve satisfies the following formula, and specifically comprises the following steps:
wherein C represents the sintering temperature, P represents the sintering pressure, Pv represents the vacuum degree, j represents a constant, and the value is 2.
8. The method for preparing the high-temperature-resistant CuCrNb alloy according to claim 1, wherein the compactness of the sintered sample block obtained in the step S2 discharge plasma sintering is more than 99.5%.
9. The method for preparing the high-temperature-resistant CuCrNb alloy as recited in claim 1, wherein the high-speed rotation speed for preparing the CuCrNb alloy powder by the plasma rotary gas atomization method is 13000-18000 r/min.
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