WO2022052865A1 - 一种铜合金材料及其制备方法和应用 - Google Patents

一种铜合金材料及其制备方法和应用 Download PDF

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WO2022052865A1
WO2022052865A1 PCT/CN2021/116353 CN2021116353W WO2022052865A1 WO 2022052865 A1 WO2022052865 A1 WO 2022052865A1 CN 2021116353 W CN2021116353 W CN 2021116353W WO 2022052865 A1 WO2022052865 A1 WO 2022052865A1
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copper alloy
temperature
alloy material
source
preparation
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PCT/CN2021/116353
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English (en)
French (fr)
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杨桂香
杨景周
杨景浩
马明
杨东娜
陈海深
杨东华
余小芳
王梦珂
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河北励恩新材料科技有限公司
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Publication of WO2022052865A1 publication Critical patent/WO2022052865A1/zh
Priority to ZA2022/03714A priority Critical patent/ZA202203714B/en

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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C9/00—Alloys based on copper
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F9/00—Making metallic powder or suspensions thereof
    • B22F9/02—Making metallic powder or suspensions thereof using physical processes
    • B22F9/14—Making metallic powder or suspensions thereof using physical processes using electric discharge
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B33—ADDITIVE MANUFACTURING TECHNOLOGY
    • B33Y—ADDITIVE MANUFACTURING, i.e. MANUFACTURING OF THREE-DIMENSIONAL [3-D] OBJECTS BY ADDITIVE DEPOSITION, ADDITIVE AGGLOMERATION OR ADDITIVE LAYERING, e.g. BY 3-D PRINTING, STEREOLITHOGRAPHY OR SELECTIVE LASER SINTERING
    • B33Y70/00—Materials specially adapted for additive manufacturing

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  • the invention belongs to the technical field of additive manufacturing, and in particular relates to a copper alloy material and a preparation method and application thereof.
  • High-temperature resistant copper alloys that meet the requirements of aerospace-grade components, such as: CuZr copper alloy, whose chemical composition is Cu-Zr 0.15-0.3%, and CuAgZr copper alloy chemical composition is Cu-Ag 3.0%-Zr 0.5 %.
  • These high temperature resistant copper alloy materials are binary alloys or ternary alloys, which are mostly produced by traditional centrifugal casting or forging spinning methods, and are mainly used in the lining of thrust chamber combustion chambers.
  • the wall of the thrust chamber of the hydrogen-oxygen rocket engine has comb-shaped cracks after several thermal tests, and the cracks expand slightly in the subsequent thermal tests, and the inner wall of the channel bulges toward the combustion chamber. Since high temperature creep occurs in the inner wall, the cooling channel has degeneration and failure, and finally the inner wall of the combustion chamber is fractured and damaged. It can be seen that the high-temperature mechanical properties of the existing copper alloy materials are poor and need to be further improved.
  • the purpose of the present invention is to provide a copper alloy material and its preparation method and application.
  • the copper alloy material provided by the invention has good high temperature mechanical properties.
  • the invention provides a copper alloy material, comprising the following components by mass percentage:
  • the RE includes components in the following mass percentages: La 88-93%, Ce 6-9%, Pr 1.5-1.9% and Nd ⁇ 0.3%, and the total mass is 100%.
  • the copper alloy material includes the following components by mass percentage:
  • the RE includes the following components by mass percentage: La 90%, Ce 8%, Pr 1.7% and Nd 0.3%.
  • the present invention also provides a method for preparing the copper alloy material described in the above technical solution, comprising the following steps:
  • the RE source contains La, Ce, Pr and Nd elements
  • the copper alloy material is obtained by using the copper alloy electrode rod as an anode, and atomizing the plasma spheroidized rotating electrode in a vacuum and a protective atmosphere.
  • the heating process of the vacuum induction melting includes: heating from room temperature to a first temperature at a first heating rate to perform a first heat preservation, and then heating from the first temperature to the second temperature at a second heating rate after the first heat preservation.
  • the second temperature is maintained for a second temperature, and the temperature is raised from the second temperature to the final temperature at a third heating rate after the second insulation;
  • the first heating rate is 8 ⁇ 12°C/min, the first temperature is 1200 ⁇ 1250°C, and the first heat preservation time is 8 ⁇ 10min;
  • the second heating rate is 6-8°C/min, the second temperature is 1280-1300°C, and the second holding time is 5-8min;
  • the third heating rate is 6-8°C/min, and the final temperature is 1500-1550°C.
  • the diameter of the copper alloy rod is 55-85 mm, and the length is 900-1300 mm.
  • the plasma arc current intensity of the atomized plasma spheroidizing rotating electrode is 1200-1900A, and the voltage is 35-115V.
  • the rotating speed of the electric motor for atomization of the plasma spheroidizing rotating electrode is 12000-18000 r/min
  • the distance between the plasma torch and the end face of the copper alloy rod is 2-3 mm
  • the feeding speed is 0.5-1.0 mm/min. s.
  • the atomizing pressure of the plasma spheroidizing rotating electrode is 0.12-0.16 MPa.
  • the present invention also provides the application of the copper alloy material described in the above technical solution or the copper alloy material prepared by the preparation method described in the above technical solution in the preparation of high temperature resistant parts.
  • the copper alloy material provided by the present invention includes the following components by mass percentage: Cr 2.0-7.0%, Nb 1.0-5.0%, Ag 0.1-2.0%, Zr 0.1-0.7%, RE 0.02-0.3% and the balance Cu; the RE includes the following components by mass percentage: La 88-93%, Ce 6-9%, Pr 1.5-1.9% and Nd ⁇ 0.3%, and the total mass is 100%.
  • Cu is used as the base metal, so that the copper alloy has excellent high-temperature mechanical properties, and Cr and Ag have a solid solution strengthening effect on the copper alloy, which can further improve the high-temperature mechanical properties of the copper alloy material;
  • the synergistic effect between Cr, Ag, Cu, Nb, Zr and RE can effectively improve the thermal conductivity, high temperature creep performance, high temperature strength and high temperature fatigue of copper alloy materials, and solve the high temperature of copper alloy materials existing in the prior art. poor mechanical properties.
  • FIG. 1 is an optical microscope photograph of the copper alloy material prepared in Example 1.
  • FIG. 1 is an optical microscope photograph of the copper alloy material prepared in Example 1.
  • the invention provides a copper alloy material, comprising the following components by mass percentage:
  • the copper alloy material provided by the present invention includes Cr with a mass percentage of 2.0-7.0%, preferably 3.0-5.0%, and more preferably 4.0%.
  • Cr can not only play a role of solid solution strengthening on Cu, improve the high temperature strength, high wear resistance and corrosion resistance of copper alloy materials, but also refine the crystal grains of the prepared copper alloy.
  • the copper alloy material provided by the present invention includes 1.0-5.0% by mass of Nb, preferably 1.5-3.5%, more preferably 2.0%.
  • Nb can effectively improve the high temperature strength, high temperature creep resistance, high temperature fatigue and thermal conductivity of the copper alloy material.
  • the copper alloy material provided by the present invention includes Ag with a mass percentage content of 0.1-2.0%, preferably 0.5-1.5%, and more preferably 1.0%.
  • Ag can play the role of solid solution strengthening and improve the high temperature strength, electrical conductivity, recrystallization temperature, high temperature creep and high temperature fatigue resistance of the copper alloy material.
  • the copper alloy material provided by the present invention includes a mass percentage of 0.1-0.7% Zr, preferably 0.2-0.5%, more preferably 0.4%.
  • Zr can effectively increase the recrystallization temperature and high temperature strength of the copper alloy material.
  • the content of Zr can inhibit the growth of the Cr phase, ensure that the grain size in the prepared copper alloy material is small, and effectively improve the mechanical properties and electrical conductivity of the copper alloy material.
  • the copper alloy material provided by the present invention comprises a mass percentage of 0.02-0.3% RE, preferably 0.05-0.2% RE, more preferably 0.07-0.15%.
  • the RE includes the following components by mass percentage: La 88-93%, Ce 6-9%, Pr 1.5-1.9% and Nd ⁇ 0.3%, the sum of the mass is 100%, preferably including La 90%, Ce 8%, Pr 1.7% and Nd 0.3%.
  • RE can not only form a high melting point intermediate phase (CuRE) with the Cu matrix, form a large number of non-uniform nucleation particles, increase the nucleation rate, and make the metallographic grains of the prepared copper alloy material refined, uniform and dense, and The chemical properties of rare earth elements are extremely active and have strong reducibility.
  • CuRE high melting point intermediate phase
  • the high melting point compound enters the slag to improve the high temperature strength and electrical conductivity of the copper alloy material.
  • the copper alloy material provided by the present invention includes the balance of copper.
  • Cu has high thermal conductivity, excellent creep properties and high temperature strength.
  • the present invention also provides a method for preparing the copper alloy material described in the above technical solution, comprising the following steps:
  • the copper alloy material is obtained by using the copper alloy electrode rod as an anode, and atomizing the plasma spheroidized rotating electrode in a vacuum and a protective atmosphere.
  • the Cu source, the Cr source, the Nb source, the Zr source, the Ag source and the RE source are mixed, followed by vacuum induction melting and pouring to obtain a copper alloy rod.
  • the Cu source is preferably electrolytic copper, and the source of the electrolytic copper is not particularly limited in the present invention, and can be obtained by using conventional commercially available products in the art or electrolytic methods well known to those skilled in the art .
  • the source of the Cr source is preferably a CuCr alloy, and the CuCr alloy preferably contains the following components by mass percentage: 70% Cu and 30% Cr.
  • the source of the Nb source is preferably a CuNb alloy, and the CuNb alloy preferably contains the following components by mass percentage: 80% Cu and 20% Nb.
  • the source of the Zr source is preferably a CuZr alloy, and the CuZr alloy preferably contains the following components by mass percentage: 85% Cu and 15% Zr.
  • the source of the Ag source is preferably industrial Ag.
  • the source of the RE source is preferably RE alloy; the RE alloy preferably includes the following components by mass percentage: La 88-93%, Ce 6-9%, Pr 1.5-1.9% and Nd ⁇ 0.3%, the sum of mass is 100%.
  • the source of the RE alloy is not particularly limited in the present invention, and it can be prepared by using conventional commercial products in the art or methods well known to those skilled in the art.
  • the Cr source, Nb source and Zr source are added in the form of CuCr alloy, CuNb alloy and CuZr alloy, so as to avoid serious burning loss of metal elemental Cr, Nb and Zr during high temperature smelting, and further Defects such as inclusions contaminate the alloy liquid are generated, so that the prepared copper alloy material has high purity, no impurities, uniform and dense metallographic structure, and high comprehensive mechanical properties.
  • the prepared copper alloy material can meet the requirements of aerospace grade application standards. .
  • the mixing is preferably carried out in a vacuum induction furnace.
  • the present invention does not have a special limitation on the mixing method, and a mixing method well known to those skilled in the art can be adopted.
  • the vacuum degree in the vacuum induction furnace is preferably pumped to 0.01Pa, and then an inert gas is introduced; the inert gas is preferably a mixed gas of argon and helium, and the volume ratio of the argon and helium is preferably 1:1.
  • the heating process of the vacuum induction melting preferably includes: raising the temperature from room temperature to a first temperature at a first heating rate to perform a first heat preservation, and then increasing the temperature from the first temperature at a second heating rate after the first heat preservation.
  • the temperature is raised to a second temperature for a second heat preservation, and after the second heat preservation, the temperature is raised from the second temperature to the final temperature at a third temperature increase rate;
  • the first temperature increase rate is preferably 8 to 12°C/min, more preferably 10°C/min;
  • the first temperature is preferably 1200-1250°C, more preferably 1220-1240°C;
  • the first heat preservation time is preferably 8-10min, more preferably 9min;
  • the second heating rate is preferably is 6-8 °C/min, more preferably 7 °C/min;
  • the second temperature is preferably 1280-1300 °C, more preferably 1290 °C;
  • the second holding time is preferably 5-8 min, more preferably 6min;
  • the third heating rate is preferably 6-8°C/min, more preferably 7°C/min;
  • the final temperature is 1500-1550°C, more preferably 1520-1530°C.
  • the vacuum induction melting is directly poured when the temperature reaches the final temperature.
  • the present invention does not have a special limitation on the casting method, and a casting method well known to those skilled in the art can be adopted.
  • the diameter of the copper alloy rod is preferably 55 to 85 mm, and the length of the copper alloy rod is preferably 900 to 1300 mm.
  • the copper alloy electrode rod is obtained after the copper alloy rod is machined.
  • the machining method is preferably to sequentially perform turning, rough polishing and fine polishing of the copper alloy electrode rod.
  • the depth of the turning is preferably 1 to 2 mm.
  • the present invention does not have a special limitation on the methods of rough polishing and fine polishing, and the rough polishing and fine polishing methods well known to those skilled in the art can be used.
  • the present invention uses the copper alloy electrode rod as an anode, and performs plasma spheroidization and rotary electrode atomization under vacuum and protective atmosphere to obtain the copper alloy material.
  • the plasma spheroidizing rotating electrode atomization is preferably performed in an atomizing device.
  • the vacuum degree of the atomization chamber of the atomization device is evacuated to 10 ⁇ 10 -3 Pa, and then filled with inert gas.
  • the inert gas is preferably a mixed gas of argon and helium, and the volume ratio of the argon and helium is preferably 1:1.
  • the current intensity of the plasma arc atomized by the plasma spheroidizing rotating electrode is preferably 1200-1900A, more preferably 1500A; the voltage of the plasma arc is preferably 35-115V, more preferably 70V; the The rotating speed of the motor for atomization by the plasma spheroidizing rotating electrode is preferably 12000-18000 r/min, more preferably 15000 r/min; the distance between the plasma torch atomized by the plasma spheroidizing rotating electrode and the end face of the copper alloy rod is preferably is 2-3 mm; the feeding speed of the atomization of the plasma spheroidizing rotary electrode is preferably 0.5-1.0 mm/s.
  • a plasma torch is preferably used to heat and melt the end face of the copper alloy rod rotating at a high speed, and the molten droplets are centrifuged and condensed into spherical copper alloy material powder in the atomization chamber.
  • the invention utilizes the plasma spheroidization rotary electrode atomization process to prepare the copper alloy material, and can obtain the copper alloy material with high sphericity, good purity, excellent fluidity, low oxygen content and uniform composition.
  • the pressure in the atomizing chamber is preferably 0.12-0.16 MPa, which can prevent the atmosphere from entering the atomizing chamber, and maintain the vacuum degree, which is conducive to the control of the gas flow direction and the cooling of the spherical powder.
  • the present invention preferably sequentially cools, sieves and vacuum packs the spherical copper alloy powder obtained by the atomization of the plasma spheroidized rotating electrode to obtain the copper alloy material.
  • the present invention does not specifically limit the cooling method, and a cooling method well known to those skilled in the art may be adopted.
  • the present invention does not have a special limitation on the screening method, and a screening method well known to those skilled in the art may be adopted.
  • the particle size of the copper alloy material is preferably 15-45 ⁇ m; the sphericity of the copper alloy material is preferably 99.90-99.96%; the oxygen content of the copper alloy material is preferably 35-40 ppm;
  • the bulk density of the copper alloy material is preferably 5.0-5.5 g/cm 3 ; the tap density of the copper alloy material is preferably 6.4-6.6 g/cm 3 ; the fluidity of the copper alloy material is preferably 5s/50g.
  • the present invention also provides the application of the copper alloy material described in the above technical solution or the copper alloy material prepared by the preparation method described in the above technical solution in the preparation of high temperature resistant parts.
  • the copper alloy material is preferably suitable for use in gas turbine engines, aerodynamic heating devices, steam turbine power, high pressure steam equipment, aerospace engines or petrochemical high temperature equipment.
  • the application method is preferably: 3D printing the copper alloy material in an FS421M industrial-grade metal additive manufacturing (3D printing) equipment to obtain the high temperature resistant part.
  • the copper alloy material provided by the invention has small particle size, narrow particle size distribution, 20-30 ⁇ m, low oxygen content, little/no spheroidization in the process of additive manufacturing, no agglomeration, and consistency and uniformity of additive manufacturing. It is fully guaranteed; and the copper alloy material has high sphericity, good fluidity, high bulk density, and good powder uniformity.
  • the metallographic structure of the product obtained by additive manufacturing is uniform and dense, and has excellent high-temperature mechanical properties, which can meet the needs of use. Standard requirements for printing complex aerospace-grade high-mechanical performance parts for industrial and scientific-grade metal additive manufacturing (3D printing) equipment.
  • the vacuum induction furnace After the vacuum induction furnace is evacuated to 0.01Pa, it is filled with inert gas (a mixture of argon and helium, the volume ratio is 1:1), and the temperature is raised from room temperature to 1250°C at 10°C/min, and kept for 10min; 7°C/min, heat up from 1250°C to 1300°C, hold for 8 minutes; heat up from 1300°C to 1550°C at 7°C/min, perform vacuum induction melting to obtain a melt, cast the melt to obtain a copper alloy rod, Diameter 55 ⁇ 85mm, length 900 ⁇ 1300mm;
  • inert gas a mixture of argon and helium, the volume ratio is 1:1
  • the prepared copper alloy bar is removed with a lathe to a depth of 1-2 mm from the skin of the copper alloy bar, and after rough polishing and fine polishing are performed in sequence, the copper alloy bar is obtained;
  • the prepared copper alloy rod is placed in the atomization equipment as an anode, and the atomization chamber is evacuated to a vacuum of 10 ⁇ 10 -3 , and then filled with an inert gas (a mixture of argon and helium, with a volume ratio of 1:1), carry out the atomization of the plasma spheroidizing rotating electrode, the plasma arc current intensity is 1900A, the voltage is 115V, the motor speed is 18000r/min, the distance between the plasma torch and the end face of the bar is 3mm, and the feed rate is 1.0mm /s, the pressure of the atomization chamber is 0.16MPa, and the copper alloy material is obtained.
  • an inert gas a mixture of argon and helium, with a volume ratio of 1:1
  • the preparation method in this comparative example is the same as that of Example 1, the difference is only that the mass percentage content ratio of each metal element in the copper alloy material is different, and does not contain rare earth.
  • Fig. 1 is an optical microscope photograph of the copper alloy material prepared in Example 1, and the scale in the figure is 50 ⁇ m. It can be seen from the figure that the surface cleanliness of the copper alloy material particles is high, and there is no hollow powder and satellite powder. The sphericity of the particles is high, 99.94%, the spherical powder is uniform, the oxygen content is 35ppm, the bulk density is 5.2g/ cm3 , the tap density is 6.4g/ cm3 , and the flowability of the spherical powder is 5s/50g.
  • the high-temperature tensile mechanical properties test standard is: GB/T4338-2006 "High-temperature Tensile Test of Metal Materials”. Standard high-temperature tensile samples are printed respectively, and standard tensile samples are obtained after post-processing. Tensile tests were carried out on a tensile testing machine. The samples were stretched under the parameters of temperature 785K and strain rate of 5mm/min respectively. The test results are shown in Table 2.
  • the electrical conductivity test standard is GB/T32791-2016 "Eddy Current Testing Method for Electrical Conductivity of Copper and Copper Alloys", and the standard samples of Examples 1 to 8 and Comparative Examples and CuAgZr alloys were prepared respectively.
  • the detection surface was flat, and the surface roughness of the samples was ⁇ 5 ⁇ m, use 800 and 1200 grit sandpaper for rough polishing and fine polishing in turn, and use Sigma2008A eddy current conductivity meter to test the samples respectively.
  • the temperature of the sample is consistent, turn on the instrument, calibrate the instrument, the probe surface is parallel to the detection surface, and the probe is more than 5mm away from the edge of the detection surface. Select 3 detection parts for each sample for detection, and take the average value as the final detection. result.
  • the electrical conductivity of the comparative example and the samples of Examples 1 to 2 is basically the same as that of the CuAgZr alloy. Under the same test conditions, the electrical conductivity of the samples of Examples 3 to 8 is significantly improved.
  • the high temperature fatigue test standard is HB7680-2019 "Test Method for High Temperature Fatigue Crack Growth Rate of Metal Materials", and FS421M metal additive manufacturing (3D printing) equipment is used to print and prepare samples that meet the requirements of the high temperature fatigue test standard.
  • the test shows that the sample prepared in Example 6 is fatigue-resistant.
  • the service life is higher than that of the comparative alloy to varying degrees, such as 49.6% higher than the comparative alloy at 850K, 61% higher at 750K, 63% higher at 700K, and 65% higher than the comparative alloy at 650K, indicating that the stress and temperature of the two alloys are at Under the same conditions, the high temperature cycle fatigue life of the copper alloy material provided by the present invention is obviously better than that of the CuAgZr alloy, and the test results are shown in Table 3.
  • the high temperature creep performance test standard is HB5151-96 "Metal High Temperature Tensile Creep Test Method", and the FS421M additive manufacturing (3D printing) equipment is used to print the samples that meet the high temperature creep test standard requirements.
  • the samples were respectively subjected to high temperature creep test on the RC-1130 (425A) type high temperature creep testing machine. Record the strain amount of the creep sample at different times. After heating the testing machine to the specified temperature, load the sample into the sample. After reaching the specified temperature for 8-10 minutes, carry out the high-temperature creep test. The tensile time of the creep test is set to 1h. , the test time of each sample is 1h and then taken out and cooled. The creep rates of the samples at different stress levels at temperatures of 600K, 700K, 800K, and 900K, respectively, at the same temperature, with the increase of stress, the initial strain and initial creep rate gradually increased. The initial strain and initial creep rate of the sample prepared in Example 6 are smaller than those of the CuAgZr alloy.
  • the total strain of the sample prepared in Example 6 is 0.561%, while the total strain of the CuAgZr alloy reaches 0.98%, which is higher than that of the sample prepared in Example 6.
  • the sample is 74.68% higher than that of the original one.
  • the test shows that the high temperature creep resistance of the copper alloy material provided by the present invention is obviously better than that of the CuAgZr alloy.
  • the test results are shown in Table 5.
  • the FS421M additive manufacturing (3D printing) equipment was used to print the samples that met the requirements of the corrosion resistance test standard. /LH 2 O 2 mixed solution soak the sample, weigh it regularly, calculate the mass loss rate, and replace it with a new corrosive solution. Corrosion by FeCl 3 alcohol solution, cleaning and drying, and then placing under a microscope to measure the corrosion depth. According to the mass weight loss rate and average corrosion depth, the corrosion resistance of each sample was compared.
  • Specimens were prepared using FS421M additive manufacturing (3D printing) equipment.
  • the size of the sample is 10mm ⁇ 10mm ⁇ 20mm, and the alloy of the present invention and the CuAgZr alloy sample are respectively subjected to the wear resistance test on the M200 wear tester.
  • the grinding wheel (friction pair) is GCr steel, and the surface roughness of the sample and the friction pair are both 1.61.
  • the test shows that under the friction condition of 20kg load and oil lubrication, the running-in mileage of each sample is basically the same as 0.2km, and the mileage of each sample is taken as 1.5km for the comparative wear test.
  • the wear resistance of the comparative example, the samples of Examples 1 to 2 and the CuAgZr alloy has no significant difference, and the wear resistance of the samples of Examples 3 to 8 is significantly improved, which is obviously better than that of the CuAgZr alloy, the comparative example and the examples 1 to 1. 2 samples, the test results are shown in Table 6.
  • Example 1 >3.0 0.46 0.291
  • Example 2 >3.3 0.48 0.301
  • Example 3 ⁇ 1 0.12 0.081
  • Example 4 ⁇ 0.9 0.12 0.080
  • Example 5 ⁇ 0.8 0.1 0.067
  • Example 6 ⁇ 0.7 0.1 0.060
  • Example 7 ⁇ 0.9 0.11 0.069
  • Example 8 ⁇ 1 0.13 0.081 Comparative ratio >3.2 0.44 0.297

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Abstract

本发明提供了一种铜合金材料及其制备方法和应用，属于增材制造技术领域。本发明提供的铜合金材料，包括以下质量百分含量的组分：Cr 2.0～7.0％、Nb 1.0～5.0％、Ag 0.1～2.0％、Zr 0.1～0.7％、RE 0.02～0.3％和余量Cu；所述RE包括以下质量百分含量的组分：La 88～93％、Ce 6～9％、Pr 1.5～1.9％和Nd≤0.3％，质量之和为100％。本发明中RE、Cr、Nb、Ag、Zr和Cu之间的协同作用，有效提高铜合金材料的导热性能、高温蠕变性能、高温强度和高温疲劳，解决了现有技术中存在的铜合金材料的高温力学性能较差的问题。

Description

一种铜合金材料及其制备方法和应用
本申请要求于2020年09月08日提交中国专利局、申请号为202010932945.2、发明名称为“一种铜合金材料及其制备方法和应用”的中国专利申请的优先权，其全部内容通过引用结合在本申请中。
技术领域
本发明属于增材制造技术领域，尤其涉及一种铜合金材料及其制备方法和应用。
背景技术
现代航空航天级部件要求具有高导热、抗高温蠕变、高温强度、高温疲劳和高力学性能。目前现有满足航空航天级部件要求的耐高温铜合金牌号较少，如：CuZr铜合金，其化学成分为Cu-Zr 0.15-0.3％，CuAgZr铜合金化学成分为Cu-Ag 3.0％-Zr 0.5％。这些耐高温铜合金材料均为二元合金或三元合金，多采用传统的离心铸造或锻造旋压方法制作得到，主要应用于推力室燃烧室内衬。
但在实际氢氧火箭发动机的热试验中，常常发现氢氧火箭发动机推力室内壁在经过多次热试车后出现梳状裂纹，并在后续热试车中裂纹略有扩展，通道内壁向燃烧室内鼓起，内壁出现高温蠕变、冷却通道发生鼔形退化失效，最终导致燃烧室内壁断裂破坏。可见，现有铜合金材料高温力学性能较差，仍待进一步提高。
发明内容
鉴于此，本发明的目的在于提供一种铜合金材料及其制备方法和应用。本发明提供的铜合金材料具有良好的高温力学性能。
为了实现上述发明目的，本发明提供以下技术方案：
本发明提供了一种铜合金材料，包括以下质量百分含量的组分：
Cr 2.0～7.0％、Nb 1.0～5.0％、Ag 0.1～2.0％、Zr 0.1～0.7％、RE 0.02～0.3％和余量Cu；
所述RE包括以下质量百分含量的组分：La 88～93％、Ce 6～9％、Pr  1.5～1.9％和Nd≤0.3％，质量之和为100％。
优选地，所述的铜合金材料，包括以下质量百分含量的组分：
Cr 3.0～5.0％、Nb 1.5～3.5％、Ag 0.5～1.5％、Zr 0.2～0.5％、RE 0.03～0.2％和余量Cu。
优选地，所述RE包括以下质量百分含量的组分：La 90％，Ce 8％，Pr 1.7％和Nd 0.3％。
本发明还提供了上述技术方案所述铜合金材料的制备方法，包括以下步骤：
将Cu源、Cr源、Nb源、Zr源、Ag源和RE源混合，依次进行真空感应熔炼和浇注，得到铜合金棒材；所述RE源包含La、Ce、Pr和Nd元素；
将所述合铜金棒材机加工后，得到铜合金电极棒；
以所述铜合金电极棒为阳极，在真空、保护气氛下进行等离子球化旋转电极雾化，得到所述铜合金材料。
优选地，所述真空感应熔炼的升温过程包括：以第一升温速率由室温升温至第一温度进行第一保温，所述第一保温后以第二升温速率由所述第一温度升温至第二温度进行第二保温，所述第二保温后以第三升温速率由所述第二温度升温至最终温度；
所述第一升温速率为8～12℃/min，第一温度为1200～1250℃，第一保温的时间为8～10min；
所述第二升温速率为6～8℃/min，第二温度为1280～1300℃，第二保温的时间为5～8min；
所述第三升温速率为6～8℃/min，最终温度为1500～1550℃。
优选地，所述铜合金棒材的直径为55～85mm，长度为900～1300mm。
优选地，所述等离子球化旋转电极雾化的等离子弧电流强度为1200～1900A，电压为35～115V。
优选地，所述等离子球化旋转电极雾化的电机转速为12000～18000r/min，等离子体炬离所述铜合金棒材的端面的距离为2～3mm，进给速度为0.5～1.0mm/s。
优选地，所述等离子球化旋转电极雾化的压力为0.12～0.16MPa。
本发明还提供了上述技术方案所述铜合金材料或由上述技术方案所述制备方法制得的铜合金材料在耐高温部件的制备中的应用。
本发明提供的铜合金材料，包括以下质量百分含量的组分：Cr 2.0～7.0％、Nb 1.0～5.0％、Ag 0.1～2.0％、Zr 0.1～0.7％、RE 0.02～0.3％和余量Cu；所述RE包括以下质量百分含量的组分：La 88～93％、Ce 6～9％、Pr 1.5～1.9％和Nd≤0.3％，质量之和为100％。在本发明中，以Cu为基体金属，使铜合金具有优异的高温力学性能，Cr和Ag对铜合金起到固溶强化的作用，可进一步提高铜合金材料的高温力学性能；铜合金材料中Cr、Ag、Cu、Nb、Zr和RE之间的协同作用，可有效提高铜合金材料的导热性能、高温蠕变性能、高温强度和高温疲劳，解决现有技术中存在的铜合金材料的高温力学性能较差的问题。
附图说明
图1为实施例1制得的铜合金材料的光学显微镜照片。
具体实施方式
本发明提供了一种铜合金材料，包括以下质量百分含量的组分：
Cr 2.0～7.0％、Nb 1.0～5.0％、Ag 0.1～2.0％、Zr 0.1～0.7％、RE 0.02～0.3％和余量Cu。
以质量百分含量计，本发明提供的铜合金材料包括质量百分含量为2.0～7.0％的Cr，优选为3.0～5.0％，进一步优选为4.0％。在本发明中，Cr不仅能够对Cu起到固溶强化的作用，提高铜合金材料的高温强度、高耐磨性能和耐腐蚀性能，还可以使制备得到的铜合金的晶粒得到细化。
本发明提供的铜合金材料包括质量百分含量为1.0～5.0％的Nb，优选为1.5～3.5％，进一步优选为2.0％。在本发明中，Nb可有效提高铜合金材料的高温强度、抗高温蠕变性能、高温疲劳和导热性能。
本发明提供的铜合金材料包括质量百分含量为0.1～2.0％的Ag，优选为0.5～1.5％，进一步优选为1.0％。在本发明中，Ag能够起到固溶强化的作用，提高铜合金材料的高温强度、导电率、再结晶温度、高温蠕变和抗高温疲劳性能。
本发明提供的铜合金材料包括质量百分含量为0.1～0.7％Zr，优选为0.2～0.5％，进一步优选为0.4％。在本发明中，Zr能够有效提高铜合金材 料的再结晶温度和高温强度。在本发明中，所述Zr的含量能够抑制Cr相长大，保证制备得到的铜合金材料中的晶粒尺寸小，有效的提高了铜合金材料的力学性能和导电性能。
本发明提供的铜合金材料包括质量百分含量为0.02～0.3％RE，优选为RE 0.05～0.2％，进一步优选为0.07～0.15％。在本发明中，所述RE包括以下质量百分含量的组分：La 88～93％、Ce 6～9％、Pr 1.5～1.9％和Nd≤0.3％，质量之和为100％，优选包括La 90％，Ce 8％，Pr 1.7％和Nd 0.3％。在本发明中，RE不仅能够与Cu基体形成高熔点中间相(CuRE)，形成大量非均匀形核质点，增加形核率，使制备得到的铜合金材料的金相晶粒细化、均匀致密，且稀土元素化学性质极为活泼，具有强还原性，在熔炼过程中，能优先与合金中含有的O、P、S等元素发生氧化还原反应生成高熔点化合物(PrP、CeO 2、CeS和La 2S 3)，高熔点化合物进入熔渣中，提高铜合金材料的高温强度和导电性能。
本发明提供的铜合金材料包括余量的铜。在本发明中，Cu具有高导热性能、优异的蠕变性能和高温强度。
本发明还提供了上述技术方案所述铜合金材料的制备方法，包括以下步骤：
将Cu源、Cr源、Nb源、Zr源、Ag源和RE源混合，依次进行真空感应熔炼和浇注，得到铜合金棒材；
将所述合铜金棒材机加工后，得到铜合金电极棒；
以所述铜合金电极棒为阳极，在真空、保护气氛下进行等离子球化旋转电极雾化，得到所述铜合金材料。
本发明将Cu源、Cr源、Nb源、Zr源、Ag源和RE源混合，依次进行真空感应熔炼和浇注，得到铜合金棒材。
在本发明中，所述Cu源优选为电解铜，本发明对所述电解铜的来源没有特殊的限定，采用本领域常规市售产品或本领域技术人员熟知的电解方法制得的产品均可。在本发明中，所述Cr源的来源优选为CuCr合金，所述CuCr合金优选包含以下质量百分含量的组分：70％Cu和30％Cr。在本发明中，所述Nb源的来源优选为CuNb合金，所述CuNb合金优选包含以下质量百分含量的组分：80％Cu和20％Nb。在本发明中，所述 Zr源的来源优选为CuZr合金，所述CuZr合金优选包含以下质量百分含量的组分：85％Cu和15％Zr。在本发明中，所述Ag源的来源优选为工业Ag。在本发明中，所述RE源的来源优选为RE合金；所述RE合金优选包括以下质量百分含量的组分：La 88～93％、Ce 6～9％、Pr 1.5～1.9％和Nd≤0.3％，质量之和为100％。本发明对所述RE合金的来源没有特殊的限定，采用本领域常规市售产品或本领域技术人员熟知的方法制备得到均可。
在本发明中，所述Cr源、Nb源和Zr源，以CuCr合金、CuNb合金和CuZr合金的形式加入，避免了金属单质Cr、Nb和Zr在高温熔炼过程中发生严重的烧损，进而产生夹杂物污染合金液等缺陷，使制备得到的铜合金材料的纯净度高、不含杂质，金相组织均匀致密，综合力学性能高，制备得到的铜合金材料能达到航空航天级别应用标准要求。
在本发明中，所述混合优选在真空感应炉中进行。本发明对所述混合的方式没有特殊的限定，采用本领域技术人员熟知的混合方式即可。本发明优选将所述真空感应炉内的真空度抽至0.01Pa后，再通入惰性气体；所述惰性气体优选为氩气和氦气混合气体，所述氩气和氦气的体积比优选为1:1。
在本发明中，所述真空感应熔炼的升温过程优选包括：以第一升温速率由室温升温至第一温度进行第一保温，所述第一保温后以第二升温速率由所述第一温度升温至第二温度进行第二保温，所述第二保温后以第三升温速率由所述第二温度升温至最终温度；所述第一升温速率优选为8～12℃/min，进一步优选为10℃/min；所述第一温度优选为1200～1250℃，进一步优选为1220～1240℃；所述第一保温的时间优选为8～10min，进一步优选为9min；所述第二升温速率优选为6～8℃/min，进一步优选为7℃/min；所述第二温度优选为1280～1300℃，进一步优选为1290℃；所述第二保温的时间优选为5～8min，进一步优选为6min；所述第三升温速率优选为6～8℃/min，进一步优选为7℃/min；所述最终温度为至1500～1550℃，进一步优选为1520～1530℃。
本发明优选所述真空感应熔炼的温度达到最终温度时直接进行浇注。本发明对所述浇注的方式没有特殊的限定，采用本领域技术人员熟知的浇 注方式即可。
在本发明中，所述铜合金棒材的直径优选为55～85mm，所述铜合金棒材的长度优选为900～1300mm。
得到铜合金棒材后，本发明将所述合铜金棒材机加工后，得到铜合金电极棒。
在本发明中，所述机加工的方式优选为将所述铜合金电极棒的依次进行车削、粗抛光和细抛光。在本发明中，所述车削的深度优选为1～2mm。本发明对所述粗抛光和细抛光的方式没有特殊的限定，采用本领域技术人员熟知的粗抛光和细抛光方式均可。
得到铜合金电极棒后，本发明以所述铜合金电极棒为阳极，在真空、保护气氛下进行等离子球化旋转电极雾化，得到所述铜合金材料。
在本发明中，所述等离子球化旋转电极雾化优选在雾化设备中进行。本发明优选将所述雾化设备的雾化室的真空度抽至10×10 -3Pa后，再充入惰性气体。在本发明中，所述惰性气体优选为氩气和氦气混合气体，所述氩气和氦气的体积比优选为1:1。
在本发明中，所述等离子球化旋转电极雾化的等离子弧的电流强度优选为1200～1900A，进一步优选为1500A；所述等离子弧的电压优选为35～115V，进一步优选为70V；所述等离子球化旋转电极雾化的电机转速优选为12000～18000r/min，进一步优选为15000r/min；所述等离子球化旋转电极雾化的等离子体炬离所述铜合金棒材的端面的距离优选为2～3mm；所述等离子球化旋转电极雾化的进给速度优选为0.5～1.0mm/s。本发明优选利用等离子体炬加热熔化高速旋转的铜合金棒材端面，熔化的液滴在雾化室离心冷凝为球形铜合金材料粉末。本发明利用等离子球化旋转电极雾化工艺制备铜合金材料能够得到球形度高、纯净度好、流动性优异、含氧量低、成分均匀的铜合金材料。
在本发明中，所述雾化室内压力优选为0.12～0.16MPa，能够防止大气进入雾化室内，保持真空度利于气体流动方向控制，有利于球形粉体冷却。
所述等离子球化旋转电极雾化完成后，本发明优选将等离子球化旋转电极雾化得到的球形铜合金粉末依次进行冷却、筛分和真空包装，得到所 述铜合金材料。本发明对所述冷却的方式没有特殊的限定，采用本领域技术人员熟知的冷却方式即可。本发明对所述筛分方式没有特殊的限定，采用本领域技术人员熟知的筛分方式即可。
在本发明中，所述铜合金材料的粒径优选为15～45μm；所述铜合金材料的球形率优选为99.90～99.96％；所述铜合金材料的氧含量优选为35～40ppm；所述铜合金材料的松装密度优选为5.0～5.5g/cm 3；所述铜合金材料的振实密度优选为6.4～6.6g/cm 3；所述铜合金材料的流动性优选为5s/50g。
本发明还提供了上述技术方案所述铜合金材料或由上述技术方案所述制备方法制得的铜合金材料在耐高温部件的制备中的应用。
在本发明中，所述铜合金材料优选适用于燃气涡轮发动机、空气动力加热装置，汽轮动力、高压蒸汽设备、航空航天发动机或石油化工高温设备。
在本发明中，所述应用的方法优选为：将所述铜合金材料在FS421M工业级金属增材制造(3D打印)设备中进行3D打印，得到所述耐高温部件。
本发明提供的铜合金材料粒径小，粒度分布窄，为20～30μm，含氧量低，在增材制造过程中少/无球化，无团聚现象，增材制造的一致性与均匀性得到充分保障；且铜合金材料的球形度高、流动性好、松散密度高、铺粉均匀性好，增材制造得到的制品金相组织均匀致密、并具有优异的高温力学性能，能满足用于工业级和科研级金属增材制造(3D打印)设备，打印结构复杂航空航天级高力学性能零部件的标准要求。
下面结合实施例对本发明提供的铜合金材料及其制备方法和应用进行详细的说明，但是不能把它们理解为对本发明保护范围的限定。
实施例1～8
按铜合金材料中各金属元素的质量百分含量比(具体含量参见表1)，称取电解铜粉末、CuCr合金粉末(Cu 70％-Cr 30％)、CuNb合金粉末(Cu 80％-Nb 20％)、CuZr合金粉末(Cu 85％-Zr 15％)、工业纯Ag粉末、RE合金粉末(La 90％-Ce 8％-Pr 1.7％-Nd 0.3％)，将上述粉末加入真空感应炉内；
将真空感应炉内抽真空至0.01Pa后，充入惰性气体(氩气和氦气混合气体，体积比为1:1)，以10℃/min，由室温升温至1250℃，保温10min；以7℃/min，由1250℃升温至1300℃，保温8min；以7℃/min，由1300℃升温至1550℃，进行真空感应熔化得到熔液，将熔液进行浇铸，得到铜合金棒材，直径55～85mm，长度900～1300mm；
将制备得到的铜合金棒材用车床车去铜合金棒材表皮深度1～2mm，依次进行粗抛光和细抛光后，得到铜合金棒；
将制备得到的铜合金棒做为阳极置于雾化设备中，将雾化室抽真空至真空度为10×10 -3后，充入惰性气体(氩气和氦气混合气体，体积比为1:1)，进行等离子球化旋转电极雾化，等离子弧电流强度为1900A，电压为115V，电机转速为18000r/min，等离子体炬离棒材端面的距离为3mm，进给速度为1.0mm/s，雾化室的压力为0.16MPa，得到所述铜合金材料。
对比例
本对比例中的制备方法与实施例1相同，区别仅在于铜合金材料中各金属元素的质量百分含量比不同，不含稀土，具体含量参见表1。
表1实施例1～8及对比例中铜合金材料中各金属元素的质量百分含量比
Figure PCTCN2021116353-appb-000001
图1为实施例1制得的铜合金材料的光学显微镜照片图，图中标尺大小为50μm，从图中可以看出，铜合金材料颗粒的表面洁净度高，不存在 空心粉和卫星粉，颗粒的球形度高，为99.94％，球形粉体成分均匀，氧含量为35ppm，松装密度为5.2g/cm 3，振实密度为6.4g/cm 3，球形粉体流动性5s/50g。
高温拉伸力学性能试验
将实施例1～8以及对比例制备得到的铜合金材料、常规市售的Cu-Ag3.0-Zr0.5(CuAgZr)铜合金材料，采用FS421M增材制造(3D打印)设备，打印的部件进行高温拉伸力学性能试验。
高温拉伸力学性能试验标准为：GB/T4338-2006《金属材料高温拉伸试验》，分别打印标准高温拉伸试样，经后处理得到标准拉伸试样，在ETM4504GD型金属材料高低温拉伸试验机上进行拉伸试验。将试样分别在温度785K、应变速率为5mm/min的参数下进行拉伸，试验结果见表2。
导电性能测试
导电率测试标准为GB/T32791-2016《铜及铜合金导电率涡流检测方法》，分别制备实施例1～8以及对比例、CuAgZr合金的标准试样，检测面为平面，试样表面粗糙度＜5μm，用800和1200号砂纸依次进行粗抛光和细抛光，利用Sigma2008A型涡流导电仪，分别对试样进行检测，环境温度18～22℃范围内，并且探头、仪器、标准试块和试样的温度均达到一致，开启仪器、对仪器进行校准，探头表面与检测面平行紧贴，探头离检测面边缘5mm以上，每个试样选择3个检测部位进行检测，以平均值为最终检测结果。
表2实施例1～8以及对比例、CuAgZr合金的高温拉伸力学性能以及导电性能试验结果
Figure PCTCN2021116353-appb-000002
Figure PCTCN2021116353-appb-000003
由上述实验数据可知，对比例以及实施例1～2试样的高温拉伸力学性能稍高于CuAgZr合金，实施例3～8试样的高温拉伸力学性能相较于CuAgZr合金和实施例1～2试样的高温拉伸力学性能，显著提高，说明本发明提供的铜合金材料中各金属组分含量，能够显著提高铜合金材料的高温力学性能。
对比例以及实施例1～2试样与CuAgZr合金的导电率基本相同，在相同试验条件下，实施例3～8试样的导电率显著提高。
高温疲劳性能试验
高温疲劳试验标准为HB7680-2019《金属材料高温疲劳裂纹扩展速率试验方法》，采用FS421M金属增材制造(3D打印)设备，分别打印制备成符合高温疲劳试验标准要求的试样。
用实施例6制备得到的试样与CuAgZr合金进行高温疲劳性能对比。在FLPL105G金属材料高温疲劳试验机上进行，试验温度范围650～850K，频率95Hz，采用拉力加载方式应力比R＝0.1，在实验室静态环境下，测定不同温度、不同应力下的疲劳寿命。
A(1)选取应力150MPa、在相同阶梯温度下，选取温度分别为650K、700K、750K、850K，对两种合金进行疲劳寿命对比，经测试得知，实施例6制备得到的试样是疲劳寿命均不同程度高于对比例合金，如在850K高于对比例合金49.6％，750K高于61％，700K高于63％，650K高于对比例合金65％，说明两种合金应力、温度在相同条件下，本发明提供的铜合金材料的高温循环疲劳寿命明显优于CuAgZr合金，试验结果见表3。
A(2)选取应力250MPa、在相同阶梯温度下，选取温度分别为650K、700K、750K、850K，随着应力的增加，两种合金疲劳寿命均不同程度有所下降，对两种合金进行疲劳寿命对比，经测试得知，实施例6制备得到的试样的疲劳寿命均不同程度的高于CuAgZr合金，如在850K高于对比例30％，750K高于45％，700K高于47％，650K高于对比例53％；通过 试验表明，本发明提供的铜合金材料的疲劳寿命明显优于CuAgZr合金，试验结果见表4。
表3高温疲劳性能试验结果
Figure PCTCN2021116353-appb-000004
表4高温疲劳性能试验结果
Figure PCTCN2021116353-appb-000005
高温蠕变性能试验
高温蠕变性能试验标准为HB5151-96《金属高温拉伸蠕变试验方法》，采用FS421M增材制造(3D打印)设备，分别打印符合高温蠕变测试标 准要求的试样。
将试样分别在RC-1130(425A)型高温蠕变实验机上进行高温蠕变试验，温度为600～900K范围值，载荷的范围值50MPa～270MPa。记录蠕变试样不同时刻的应变量，将试验机加热至规定温度后，装入试样，达到规定温度下保温8～10min后，进行高温蠕变试验，蠕变试验拉伸时间设定1h，各试样试验时间均为1h后取出冷却。将试样分别在600K、700K、800K、900K温度下不同应力水平的蠕变速率，在同一温度下，随应力的增加，初始应变及初始蠕变速率逐渐增加，从试验结果得知，本发明实施例6制备得到的试样，初始应变及初始蠕变速率均小于CuAgZr合金。在同一温度、同一应力下(均在240MPa)，在规定高温蠕变时间内，实施例6制备得到的试样总应变为0.561％，而CuAgZr合金总应变达到0.98％，比实施例6制备得到的试样高出74.68％，通过试验表明，本发明提供的铜合金材料的抗高温蠕变性能，明显优于CuAgZr合金，试验结果见表5。
表5高温蠕变性能试验结果
Figure PCTCN2021116353-appb-000006
耐腐蚀性能测试
采用FS421M增材制造(3D打印)设备，打印符合耐腐蚀性能测试标准要求的试样，试样尺寸为20mm×20mm×20mm，经研磨抛光清洗烘干处理后用0.1mol/L HCl+0.1mol/L H 2O 2混合液浸泡试样，定期称重，计算质量损失率，并更换新的腐蚀液。经FeCl 3酒精溶液腐蚀，清洗烘干处 理后置于显微镜下，测定其腐蚀深度，根据质量失重率和平均腐蚀深度，分别对各试样耐腐蚀性能进行比较。
对比例以及实施例1～2试样和CuAgZr合金的耐腐蚀性能未明显差异，实施例3～8试样的耐腐蚀性能显著提高，明显优于CuAgZr合金、对比例以及实施例1～2试样，试验结果见表6。
耐磨损性能试验
采用FS421M增材制造(3D打印)设备，制备试样。
试样尺寸为10mm×10mm×20mm，本发明的合金和CuAgZr合金试样分别在M200磨损试验机上进行耐磨损试验。磨轮(摩擦副)为GCr钢，试样和摩擦副的表面粗糙度均为1.61。试验表明在20kg载荷和油润滑的摩擦条件下，各试样跑合里程基本一致0.2km，对各试样的对比磨损试验里程取1.5km。
对比例以及实施例1～2试样和CuAgZr合金，耐磨损性能无明显差异，实施例3～8试样的耐磨损性能显著提高，明显优于CuAgZr合金、对比例以及实施例1～2试样，试验结果见表6。
表6耐腐蚀性能和耐磨损性能试验结果
试样 平均腐蚀深度μm 质量失重率％ 磨损量mm 3
CuAgZr ＞3.5 0.52 0.351
实施例1 ＞3.0 0.46 0.291
实施例2 ＞3.3 0.48 0.301
实施例3 ＜1 0.12 0.081
实施例4 ＜0.9 0.12 0.080
实施例5 ＜0.8 0.1 0.067
实施例6 ＜0.7 0.1 0.060
实施例7 ＜0.9 0.11 0.069
实施例8 ＜1 0.13 0.081
对比例 ＞3.2 0.44 0.297
以上所述仅是本发明的优选实施方式，应当指出，对于本技术领域的普通技术人员来说，在不脱离本发明原理的前提下，还可以做出若干改进 和润饰，这些改进和润饰也应视为本发明的保护范围。

Claims (13)

  1. 一种铜合金材料，包括以下质量百分含量的组分：
    Cr 2.0～7.0％、Nb 1.0～5.0％、Ag 0.1～2.0％、Zr 0.1～0.7％、RE 0.02～0.3％和余量Cu；
    所述RE包括以下质量百分含量的组分：La 88～93％、Ce 6～9％、Pr 1.5～1.9％和Nd≤0.3％，质量之和为100％。
  2. 根据权利要求1所述的铜合金材料，其特征在于，包括以下质量百分含量的组分：
    Cr 3.0～5.0％、Nb 1.5～3.5％、Ag 0.1～2.0％、Zr 0.1～0.7％、RE 0.02～0.3％和余量Cu。
  3. 根据权利要求2所述的铜合金材料，其特征在于，包括以下质量百分含量的组分：
    Cr 3.0～5.0％、Nb 1.5～3.5％、Ag 0.5～1.5％、Zr 0.2～0.5％、RE 0.03～0.2％和余量Cu。
  4. 根据权利要求1或2或3所述的铜合金材料，其特征在于，所述RE包括以下质量百分含量的组分：La 90％，Ce 8％，Pr 1.7％和Nd 0.3％。
  5. 权利要求1～4任一项所述铜合金材料的制备方法，包括以下步骤：
    将Cu源、Cr源、Nb源、Zr源、Ag源和RE源混合，依次进行真空感应熔炼和浇注，得到铜合金棒材；所述RE源包含La、Ce、Pr和Nd元素；
    将所述合铜金棒材机加工后，得到铜合金电极棒；
    以所述铜合金电极棒为阳极，在真空、保护气氛下进行等离子球化旋转电极雾化，得到所述铜合金材料。
  6. 根据权利要求5所述的制备方法，其特征在于，所述Cr源、Nb源和Zr源以CuCr合金、CuNb合金和CuZr合金的形式加入。
  7. 根据权利要求5所述的制备方法，其特征在于，所述真空感应熔炼的升温过程包括：以第一升温速率由室温升温至第一温度进行第一保温，所述第一保温后以第二升温速率由所述第一温度升温至第二温度进行第二保温，所述第二保温后以第三升温速率由所述第二温度升温至最终温度；
    所述第一升温速率为8～12℃/min，第一温度为1200～1250℃，第一保温的时间为8～10min；
    所述第二升温速率为6～8℃/min，第二温度为1280～1300℃，第二保温的时间为5～8min；
    所述第三升温速率为6～8℃/min，最终温度为1500～1550℃。
  8. 根据权利要求5所述的制备方法，其特征在于，所述铜合金棒材的直径为55～85mm，长度为900～1300mm。
  9. 根据权利要求5所述的制备方法，其特征在于，所述等离子球化旋转电极雾化的等离子弧电流强度为1200～1900A，电压为35～115V。
  10. 根据权利要求5或9所述的制备方法，其特征在于，所述等离子球化旋转电极雾化的电机转速为12000～18000r/min，等离子体炬离所述铜合金棒材的端面的距离为2～3mm，进给速度为0.5～1.0mm/s。
  11. 根据权利要求5所述的制备方法，其特征在于，所述等离子球化旋转电极雾化的压力为0.12～0.16MPa。
  12. 权利要求1～4任一项所述铜合金材料或权利要求5～11任一项所述制备方法制得的铜合金材料在耐高温部件的制备中的应用。
  13. 根据权利要求12所述的应用，其特征在于，包括以下步骤：将所述铜合金材料在FS421M工业级金属增材制造设备中进行3D打印，得到所述耐高温部件。
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