CN116356228A - Technological method for improving performance of copper-chromium-zirconium alloy based on high-drive deformation treatment - Google Patents

Technological method for improving performance of copper-chromium-zirconium alloy based on high-drive deformation treatment Download PDF

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CN116356228A
CN116356228A CN202310064395.0A CN202310064395A CN116356228A CN 116356228 A CN116356228 A CN 116356228A CN 202310064395 A CN202310064395 A CN 202310064395A CN 116356228 A CN116356228 A CN 116356228A
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胡剑
陈永诚
邱靖
陈绵
侯旭
张文斌
衣玉玮
丁正
黄海
彭逸茹
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East China Jiaotong University
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Abstract

The invention provides a process method for improving the performance of copper-chromium-zirconium alloy based on high-drive deformation treatment, which comprises the following steps: heating a copper-chromium-zirconium alloy sample to a proper temperature and keeping the temperature for a certain time, and then quenching the sample to room temperature through water; then rolling the surface of the copper-chromium-zirconium alloy sample subjected to solution treatment at a high speed and for multiple times by using high-drive rolling equipment, so that a gradient structure deformation layer formed by collocating three different scale grains of nano crystals, superfine crystals and coarse crystals is formed from the surface layer of the copper-chromium-zirconium alloy sample to the core part; and finally, aging the copper-chromium-zirconium alloy sample subjected to high-drive surface rolling treatment under the protection of inert gas, and then air-cooling to room temperature. Compared with the traditional heat treatment and severe plastic deformation treatment, the method provided by the invention has the advantages of simple and controllable process, environmental protection and high efficiency, and the obtained copper-chromium-zirconium alloy has excellent strength plastic matching, corrosion resistance and wear resistance, and can meet the service requirement under certain severe conditions.

Description

Technological method for improving performance of copper-chromium-zirconium alloy based on high-drive deformation treatment
Technical Field
The invention belongs to the field of copper alloy processing and application, and particularly relates to a process method for improving copper-chromium-zirconium alloy performance based on high-drive deformation treatment.
Background
Copper-chromium-zirconium alloy is a precipitation-strengthened alloy, which is of interest because of its better strength-conductivity matching and softening temperature resistance compared to pure copper, and is widely used as a conductive alloy material. Along with the rapid development of advanced equipment such as a high-speed railway contact net system, the requirements on comprehensive properties such as strong plastic matching, corrosion resistance, wear resistance and the like of copper alloy are increasingly raised.
In recent years, efforts have been made to obtain copper-chromium-zirconium alloys with high dislocation density, ultra-fine grains, nano-precipitated phases by plastic deformation methods in order to obtain higher overall properties. However, the traditional rolling and other integral plastic deformation methods can obviously reduce the plasticity and the conductivity while improving the strength, and after integral plastic deformation treatment, the alloy surface has poorer flatness, and post-treatment means such as polishing and polishing are needed to obtain a flat and smooth surface state, so that the integral process is complex and the wear resistance is not obviously improved; on the other hand, research shows that the nano structure can remarkably accelerate the diffusion of chromium along the interface, but the traditional large plastic deformation cannot refine the grain size to the nano scale, so that the aging post-treatment is difficult to lead the chromium to be segregated to the surface/interface sufficiently, and the corrosion resistance cannot be remarkably improved.
Disclosure of Invention
Aiming at the defects of the prior art, the invention aims to provide a process method for improving the performance of the copper-chromium-zirconium alloy based on high-drive deformation treatment, which solves the problems that the surface quality of the copper-chromium-zirconium alloy prepared by the prior art is poor, the strong plasticity is not well matched, the grain size is difficult to refine to the nano-scale, the wear resistance and the corrosion resistance are not obviously improved, and the like.
In order to achieve the above purpose, the invention provides a process method for improving the performance of copper-chromium-zirconium alloy based on high-drive deformation treatment, which comprises the steps of sequentially carrying out solution treatment, high-drive surface rolling treatment and aging post-treatment on a copper-chromium-zirconium alloy sample;
in the copper-chromium-zirconium alloy, the mass percentages of the components of CuCrZr are as follows; 0.5 to 1.5 percent of Cr, 0.05 to 0.2 percent of Zr, and the balance of Cu and unavoidable impurities. The solid solution treatment is to heat the copper-chromium-zirconium alloy sample to a proper temperature and keep for a certain time, and then quench the sample to room temperature through water, so that the sample forms a uniform solid solution and has good processing performance; in the copper-chromium-zirconium alloy, the mass percentages of the components of CuCrZr are as follows; 0.5 to 1.5 percent of Cr, 0.05 to 0.2 percent of Zr, and the balance of Cu and unavoidable impurities.
The high-drive surface rolling treatment is as follows: carrying out high-speed and multi-pass rolling on the surface of the copper-chromium-zirconium alloy sample subjected to solution treatment by using high-drive rolling equipment, forming a compact nanocrystalline layer on the surface of the sample, and forming a gradient structure deformation layer formed by collocating three kinds of grains with different scales, such as nanocrystalline, superfine crystal, coarse crystal and the like from the surface layer to the core part; the surface of the sample after the rolling treatment is smooth and bright. The sample has a thicker gradient nanostructure deformation layer and better strong plastic matching.
The aging post-treatment is as follows: and (3) aging the copper-chromium-zirconium alloy sample subjected to the high-drive surface rolling treatment under the protection of inert gas, and then air-cooling to room temperature. After aging, the Cr element and the nano Cr-rich phase segregate at the boundary/surface, so that the strength, the wear resistance and the corrosion resistance of the sample are further improved.
Further, the process method of the invention comprises the following steps:
in the solid solution treatment, the heating temperature is 950-1050 ℃, and the heat preservation time is 60-120 minutes.
In the high-drive surface rolling treatment, the feeding speed of a rolling cutter head is 4000-6000 mm/min, and high-frequency oil injection treatment of 0.5-1L/min is applied to a processing part, wherein the rolling reduction of each pass is 20 mu m, and the rolling passes are 10.
After the high-drive surface rolling treatment, the thickness of the copper-chromium-zirconium alloy sample deformation layer is 0.3-0.8 mm.
In the aging post-treatment, the temperature is 400-500 ℃, and the temperature is kept for 30 minutes.
The invention has the following beneficial effects:
(1) The invention adopts high-driving surface plastic deformation to prepare thicker nanocrystalline and superfine crystal layers on the surface layer and the subsurface layer of the copper-chromium-zirconium alloy, and the structure gradually changes into coarse crystal from the core part of the sample, thus the invention shows excellent strong plastic matching and wear resistance; the characteristic of high diffusion rate of chromium in the nano structure is utilized, so that a large amount of chromium elements are enriched on the surfaces of the plate and the rod-shaped copper-chromium-zirconium alloy after aging treatment, the corrosion resistance of the copper-chromium-zirconium alloy is obviously improved, and the copper-chromium-zirconium alloy has great significance for development of the fields of electric power, transportation and the like.
(2) The copper-chromium-zirconium alloy prepared by the method has smooth and flat surface, no defects such as fine lines, flaking, hollows and the like, and has surface roughness (R) a ) Less than or equal to 0.3 mu m, and post-treatment such as grinding, polishing and the like is not needed. Compared with the traditional heat treatment and severe plastic deformation treatment, the process realizes simplicity, controllability, environmental protection and energy saving.
Drawings
FIG. 1 is an XRD pattern of the CuCrZr alloy treated in example 5 according to comparative example 5.
FIG. 2 is a SIMS spectrum of the Cr element in the CuCrZr alloy treated in comparative example 6 and example 5 according to the depth.
FIG. 3 is a cross-sectional profile of a sample of the treated CuCrZr alloy according to example 4.
FIG. 4 is an SEM photograph of the wear morphology of the CuCrZr alloys treated in comparative examples 5 to 6 and example 5.
Detailed Description
The design thought of the invention is mainly to treat after high driving deformation and aging; firstly, adopting high-driving surface rolling treatment for high-driving deformation, and focusing on a processing mode of combining the high-speed feeding speed of a processing tool bit with the oil spraying speed to treat the surface of a sample; secondly, the aging process of different temperatures and time periods is carried out on the sample by utilizing the characteristic of high diffusion rate of chromium element in the nano structure, so that the surface/interface of the copper-chromium-zirconium alloy after aging treatment is enriched with chromium element. The process method of the invention is simple, controllable, environment-friendly and efficient, and the high-driving treatment surface is smooth and flat, and the surface roughness (R a ) Less than or equal to 0.3 mu m, and post-treatment such as grinding, polishing and the like is not needed. The copper-chromium-zirconium alloy treated by the process method has good strong plastic matching, corrosion resistance and wear resistance. Can meet the requirements of service under certain severe conditions.
The invention will now be described in more detail with reference to the drawings and examples, which are not intended to limit the invention in any way.
The samples used in comparative examples 1 to 4 and examples 1 to 3 were copper-chromium-zirconium alloys which were solution treated at 1000℃for 60 minutes and then water-quenched, and the compositions thereof were 98.7% by mass of Cu, 0.1% by mass of Cr, 0.01% by mass of Zr, and the balance being unavoidable impurities. And the high-drive rolling equipment is used for carrying out high-drive surface rolling treatment on the surface of the copper-chromium-zirconium alloy sample subjected to the solution treatment according to the following technological conditions.
Comparative example 1
Fixing the sample on an operation table, processing and deforming according to a feeding speed of 3000mm/min, maintaining high-frequency oil injection of 1L/min during the period, and carrying out ultrasonic cleaning on dichloromethane for 10min after continuous rolling for 10 times with a rolling reduction of 20 mu m for each time to obtain the high-driving deformation sample.
Comparative example 2
The sample is fixed on a console to process deformation according to a feeding speed of 7000mm/min, high-frequency oil injection of 0.5L/min is maintained during the deformation, and dichloromethane is subjected to ultrasonic cleaning for 10min after continuous rolling for 10 times at a rolling reduction of 20 mu m for each time to obtain a high-driving deformation sample.
Comparative example 3
The sample is fixed on an operation table to process deformation according to the feeding speed of 4000mm/min, high-frequency oil injection of 1.5L/min is maintained during the deformation, and dichloromethane is subjected to ultrasonic cleaning for 10min after continuous rolling for 10 times at the rolling reduction of 20 mu m for each time, so that the high-driving deformation sample is obtained.
Comparative example 4
Fixing the sample on an operation table, processing and deforming according to a feeding speed of 5000mm/min, maintaining high-frequency oil injection of 0.2L/min during the period, and carrying out ultrasonic cleaning on dichloromethane for 10min after continuous rolling for 10 times with a rolling reduction of 20 mu m for each time to obtain the high-driving deformation sample.
Example 1
The sample is fixed on an operation table to process deformation according to the feeding speed of 4000mm/min, high-frequency oil injection of 1L/min is maintained during the deformation, and dichloromethane is subjected to ultrasonic cleaning for 10min after continuous rolling for 10 times at the rolling reduction of 20 mu m for each time to obtain the high-driving deformation sample.
Example 2
The sample is fixed on an operation table to process deformation according to a feeding speed of 5000mm/min, high-frequency oil injection of 0.5L/min is maintained during the deformation, and dichloromethane is subjected to ultrasonic cleaning for 10min after continuous rolling for 10 times at a rolling reduction of 20 mu m for each time to obtain a high-driving deformation sample.
Example 3
Fixing the sample on an operation table, processing and deforming according to the feeding speed of 6000mm/min, maintaining high-frequency oil injection of 0.5L/min during the period, and carrying out ultrasonic cleaning on dichloromethane for 10min after continuous rolling for 10 times with the rolling reduction of 20 mu m for each time to obtain the high-driving deformation sample.
After the above-mentioned high-drive surface rolling treatment, the surface roughness was measured by a white light interferometer as shown in table 1.
TABLE 1 high drive deformation comparative examples 1 to 4 and the alloy surface roughness test results of examples 1 to 3
Numbering device R a (nm)
Comparative example 1 543.6±140.1
Comparative example 2 418.8±46.5
Comparative example 3 430.1±115.1
Comparative example 4 475.9±103.8
Example 1 280.3±105.1
Example 2 356.8±78.4
Example 3 296.4±95.3
From comparative examples 1 to 4 and examples 1 to 3, it was found that the apparatus feed speed and the oil injection frequency can affect the surface quality of the treated samples. When the feeding speed of the equipment is 3000mm/min, the phenomena of fine grain sprouting and peeling appear on the surface in the treatment process, and the surface roughness is increased due to continuous expansion along with the increase of the pass, and when the feeding speed of the equipment is 7000mm/min, the excessive high-speed rolling treatment causes excessive deformation of the surface of the sample, and the overall flatness of the sample is affected; when the oil injection is not enough, the cutter head is easy to generate heat in the high-speed running process of the equipment, and the surface quality of subsequent treatment is affected; when the oil injection is controlled excessively, the rolling efficiency is not high in the treatment process, and the situation can lead to the slipping of the cutter head in the deformation process, so that the high driving performance cannot be fully exerted. In summary, the invention clearly determines that the feeding speed of the machine tool is controlled to 4000-6000 mm/min in the high-driving deformation process, and each pass does not need interval time and maintains high-frequency oil injection treatment of 1L/min.
The samples used in comparative examples 5 to 6 and examples 4 to 8 below were each composed of 98.7% by mass of Cu, 0.1% by mass of Cr, 0.01% by mass of Zr, and the balance being unavoidable impurities.
Comparative example 5
The copper-chromium-zirconium alloy is kept in a whole argon atmosphere, subjected to homogenization treatment at 1000 ℃ for 60 minutes, then subjected to water quenching, subjected to surface grinding and polishing by using 2000# SiC sand paper after the heat treatment, and subjected to dichloromethane ultrasonic cleaning for 10 minutes.
Comparative example 6
The copper-chromium-zirconium alloy is kept in a whole argon atmosphere, subjected to homogenization treatment at 1000 ℃ for 60 minutes, then is quenched by water, fixed on a treatment table, and subjected to high-drive deformation process of continuous rolling for 10 times with 20 mu m of rolling reduction per time by adopting 5000mm/min feeding speed and 1L/min high-frequency oil injection, and dichloromethane is subjected to ultrasonic cleaning for 10 minutes after the treatment.
Example 4
The copper-chromium-zirconium alloy is kept in a whole argon atmosphere, subjected to homogenization treatment at 1000 ℃ for 60 minutes, then is quenched by water, fixed on a treatment table, and subjected to high-drive deformation process of continuous rolling for 10 times with 20 mu m of rolling reduction per time by adopting 4000mm/min feeding speed and 1L/min high-frequency oil injection, and dichloromethane is subjected to ultrasonic cleaning for 10 minutes after the treatment. And then the deformation sample is placed into a quartz tube filled with argon atmosphere for sealing, the whole argon atmosphere is kept, and the whole argon atmosphere is subjected to aging treatment at 400 ℃ for 30 minutes and then air cooling is carried out to room temperature.
Example 5
The copper-chromium-zirconium alloy is kept in a whole argon atmosphere, subjected to homogenization treatment at 1000 ℃ for 60 minutes, then is quenched by water, fixed on a treatment table, and subjected to high-drive deformation process of continuous rolling for 10 times with 20 mu m of rolling reduction per time by adopting 5000mm/min feeding speed and 1L/min high-frequency oil injection, and dichloromethane is subjected to ultrasonic cleaning for 10 minutes after the treatment. And then the deformation sample is placed into a quartz tube filled with argon atmosphere for sealing, the whole argon atmosphere is kept, and the whole argon atmosphere is subjected to aging treatment at 400 ℃ for 30 minutes and then air cooling is carried out to room temperature.
Example 6
The copper-chromium-zirconium alloy is kept in a whole argon atmosphere, subjected to homogenization treatment at 1000 ℃ for 60 minutes, then is quenched by water, fixed on a treatment table, and subjected to high-drive deformation process of continuous rolling for 10 times with 20 mu m of rolling reduction per time by adopting 6000mm/min feeding speed and 1L/min high-frequency oil injection, and dichloromethane is subjected to ultrasonic cleaning for 10 minutes after the treatment. And then the deformation sample is placed into a quartz tube filled with argon atmosphere for sealing, the whole argon atmosphere is kept, and the whole argon atmosphere is subjected to aging treatment at 400 ℃ for 30 minutes and then air cooling is carried out to room temperature.
Example 7
The copper-chromium-zirconium alloy is kept in a whole argon atmosphere, subjected to homogenization treatment at 1000 ℃ for 60 minutes, then is quenched by water, fixed on a treatment table, and subjected to high-drive deformation process of continuous rolling for 10 times with 20 mu m of rolling reduction per time by adopting 5000mm/min feeding speed and 1L/min high-frequency oil injection, and dichloromethane is subjected to ultrasonic cleaning for 10 minutes after the treatment. And then the deformation sample is placed into a quartz tube filled with argon atmosphere for sealing, the whole argon atmosphere is kept, and the whole argon atmosphere is subjected to aging treatment at 500 ℃ for 30 minutes and then air cooling is carried out to room temperature.
Example 8
The copper-chromium-zirconium alloy is kept in a whole argon atmosphere, subjected to homogenization treatment at 1000 ℃ for 60 minutes, then is quenched by water, fixed on a treatment table, and subjected to high-drive deformation process of continuous rolling for 10 times with 20 mu m of rolling reduction per time by adopting 6000mm/min feeding speed and 1L/min high-frequency oil injection, and dichloromethane is subjected to ultrasonic cleaning for 10 minutes after the treatment. And then the deformation sample is placed into a quartz tube filled with argon atmosphere for sealing, the whole argon atmosphere is kept, and the whole argon atmosphere is subjected to aging treatment at 500 ℃ for 30 minutes and then air cooling is carried out to room temperature.
The alloys treated in the comparative examples and examples were subjected to X-ray diffraction (XRD) scanning, secondary Ion Mass Spectrometry (SIMS) scanning, deformation layer thickness testing, tensile properties, abrasion resistance and corrosion resistance, respectively, as follows:
1X-ray diffraction (XRD) scanning
The alloy surfaces described in comparative example 5 and example 5 were subjected to ultrasonic cleaning with absolute ethyl alcohol and blow-dried before testing, and the non-test surface was sealed with plasticine. In the test process, the copper target wavelength is set to 1.54056A, the scanning speed of 3 degrees/min is adopted to scan 40 degrees to 100 degrees, and the scanning step length is 2θ=0.02 degrees. The XRD pattern of the CuCrZr alloy is shown in figure 1, and the crystal grain refinement of the surface layer is obvious through the process of the invention.
2 Secondary Ion Mass Spectrometry (SIMS) scanning
The cu element distribution along the depth of the CuCrZr alloys described in comparative example 6 and example 5 was tested. The length and width of the sample are controlled to be 10mm or 10mm, the thickness is 3mm, the surface roughness of the sample is kept consistent before testing, and other surfaces are smooth and clean without stains. The sputtering rate was controlled at 1nm/s to perform scanning in the depth direction. The SIMS spectrum of the Cr element in the CuCrZr alloy along with the depth change is shown in figure 2, and the enrichment of the Cr element at the surface layer of the sample due to the diffusion effect of the nano structure can be seen.
3 deformation layer thickness test
The deformation layer thicknesses of comparative example 6 and examples 4-8 were tested using two common methods. Firstly, because the deformation layer of the sample is strong and has high hardness, the thickness of the deformation layer is determined by adopting a method for testing the section hardness of the sample by adopting a sclerometer. And plating a pure Ni protective layer on the cross section area of the sample before the test, and then fixing and sealing by using cold embedding liquid. After the cold insert liquid is air-dried, sequentially finishing the grinding process by using 1200# SiC sand paper, 2000# SiC sand paper and 3000# SiC sand paper, and confirming the spot hardness by adopting an array method, wherein the corresponding test result of the thickness of the deformation layer is shown in table 2; secondly, photographing was performed by a Scanning Electron Microscope (SEM). Plating a pure Ni protective layer on the section of the sample before shooting, fixing and sealing by using cold embedding liquid, grinding, and carrying out electrolytic polishing at 10-25 ℃. The cross-sectional morphology of example 4 is shown in FIG. 3, showing that the thickness of the deformation layer is 420 μm, and at the same time, it can be seen that the deformation layer has a gradient structure composed of three different-scale grains of nanocrystalline, ultrafine grain and coarse grain.
4 tensile property test:
(1) Comparative examples 5 to 6 were cut, and the alloys described in examples 4 to 8 were "dog bone" shaped specimens in which the gauge length portion was 5mm and the gauge width was 2mm, the thickness was 0.8mm, the grip section width was 4mm, and the total length of the specimens was 17mm, respectively.
(2) Before unidirectional tensile testing of the small metal test sample, the surface roughness of the gauge length of the test sample of comparative examples 5-6 is kept consistent with that of the gauge length of the test sample of high-drive surface rolling deformation of examples 4-8. However, in order to eliminate the cutting trace left on the side surface of the gauge length section by the wire electric discharge machine, the process from coarse grinding to fine grinding needs to be completed by sequentially using 1200# SiC abrasive paper, 2000# SiC abrasive paper and 3000# SiC abrasive paper, and the damage to a tensile sample caused by external force in the grinding process is avoided. The corresponding data for the tensile properties test are shown in table 3.
5 corrosion resistance test:
comparative examples 5 to 6 were cut out and the alloys described in examples 4 to 8 were
Figure BDA0004062109310000061
The comparative samples were mechanically sanded and polished to maintain a roughness consistent with the samples of examples 4-8. Then using an electrochemical workstation to respectively carry out 3.5wt.% NaCl and 1mol/L H at normal temperature 2 SO 4 And (3) testing the electrokinetic polarization curves of different samples of the solution medium to obtain corrosion potential and corrosion current density, so as to evaluate the electrochemical performances of different samples under different corrosion mediums. The potential scanning range in the test process is-2.0-1.0V, and the speed is 0.5mV/s. The corresponding data for the corrosion resistance test are shown in table 4.
6, abrasion resistance test:
comparative examples 5 to 6 were cut out and the alloys described in examples 4 to 8 were
Figure BDA0004062109310000062
The comparative samples were mechanically sanded and polished to maintain the same roughness as the samples of examples 4-8. And performing a friction and wear test on the sample by using a multifunctional white light interference friction and wear testing machine. The ball-plate contact experiment mode is adopted, the load is set to be 30N, the rotating speed is 120rpm, and the counter grinding pair isThe test duration of the WC-Co hard alloy ball with the thickness of 10mm is kept for 2 hours, and the abrasion volume is calculated by a white light interferometer in the friction test process. The corresponding data for the abrasion resistance test are shown in table 3. In order to more intuitively reflect the friction characteristics of the sample, the abrasion morphology of the sample is observed by using a Scanning Electron Microscope (SEM), and fig. 4 is SEM pictures of the abrasion morphologies of comparative examples 5 to 6 and example 5, and it can be clearly seen that the abrasion exfoliation is significantly reduced and the abrasion resistance is improved after the process.
Table 2 comparative examples 5 to 6, examples 4 to 8 show alloy deformation layer thicknesses
Numbering device Thickness/mm
Comparative example 6 0.56
Example 4 0.42
Example 5 0.64
Example 6 0.55
Example 7 0.70
Example 8 0.51
Table 3 mechanical Properties of the alloys according to comparative examples 5 to 6 and examples 4 to 8
Numbering device Tensile strength/MPa Extensibility/% Wear rate (10) -5 mm 3 ·N -1 ·m -1 )
Comparative example 5 224.41 43.21 4.340
Comparative example 6 410.00 12.21 0.404
Example 4 501.23 18.32 0.265
Example 5 509.91 17.95 0.223
Example 6 493.83 17.25 0.279
Example 7 616.63 17.12 0.782
Example 8 593.57 18.12 0.692
Table 4 comparative examples 5 to 6, corrosion resistance of alloys according to examples 4 to 8
Figure BDA0004062109310000071
As can be seen from the above table and the attached drawings, the copper-chromium-zirconium alloy prepared by the invention has smooth and flat surface, no defects such as fine lines, flaking, hollows and the like, and has surface roughness (R a ) Less than or equal to 0.3 mu m, no post-treatment such as grinding, polishing and the like is needed, and the simple and controllable process, environmental protection and energy saving are realized. The friction material has good strong plastic matching in terms of mechanical property, the peeling in the friction process is obviously reduced, and the abrasion rate reaches (2.23-7.82) multiplied by 10 -6 mm 3 ·N -1 ·m -1 The method comprises the steps of carrying out a first treatment on the surface of the In terms of corrosion resistance, the corrosion current density of the sample under the condition of 3.5wt.% NaCl solution medium can reach 0.303-0.743 mu A/cm 2 ，1mol/L H 2 SO 4 The corrosion current density of the sample under the acidic environment can reach 0.393 to 3.251 mu A/cm 2 . The copper-chromium-zirconium alloy has excellent strong plastic matching, good wear resistance and corrosion resistance, and can meet the service requirement of the copper-chromium-zirconium alloy under severe conditions.
While the foregoing has been described in terms of specific embodiments of the invention, the present invention is not limited to the details of the process and the technical requirements, but rather is limited to those embodiments for better understanding of the process and the spirit of the invention. Variations that are based on modifications made by the process of the present invention are within the scope of the present invention.

Claims (5)

1. The process method for improving the performance of the copper-chromium-zirconium alloy based on the high-drive deformation treatment is characterized by comprising the steps of sequentially carrying out solution treatment, high-drive surface rolling treatment and aging post-treatment on a copper-chromium-zirconium alloy sample;
the solution treatment is to heat the copper-chromium-zirconium alloy sample to a proper temperature and keep for a certain time, and then quench the sample to room temperature through water; in the copper-chromium-zirconium alloy, the mass percentages of the components of CuCrZr are as follows; 0.5 to 1.5 percent of Cr, 0.05 to 0.2 percent of Zr, and the balance of Cu and unavoidable impurities;
the high-drive surface rolling treatment is as follows: the surface of the copper-chromium-zirconium alloy sample after solution treatment is rolled at high speed and multiple times by using high-drive rolling equipment, so that a gradient structure deformation layer formed by collocating three different scale grains of nano crystals, ultra-fine crystals and coarse crystals is formed from the surface layer to the core part of the copper-chromium-zirconium alloy sample
The aging post-treatment is as follows: and (3) aging the copper-chromium-zirconium alloy sample subjected to the high-drive surface rolling treatment under the protection of inert gas, and then air-cooling to room temperature.
2. The process according to claim 1, wherein in the solid solution treatment, the heating temperature is 950-1050 ℃ and the holding time is 60-120 minutes.
3. The process according to claim 1, wherein in the high-drive surface rolling treatment, the feeding speed of the rolling cutter head is 4000-6000 mm/min, and the high-frequency oil spraying treatment of 0.5-1L/min is applied to the processing part, the rolling reduction of each pass is 20 μm, and the rolling pass is 10 passes.
4. The process according to claim 1, wherein the deformation layer has a thickness of 0.3 to 0.8mm.
5. The process according to claim 1, wherein in the aging post-treatment, the temperature is 400-500 ℃, and the temperature is kept for 30 minutes.
CN202310064395.0A 2023-01-18 2023-01-18 Technological method for improving performance of copper-chromium-zirconium alloy based on high-drive deformation treatment Pending CN116356228A (en)

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