Wear-resistant and electric-corrosion-resistant CuFeCeYAg in-situ composite material and preparation method thereof

Abstract

The invention discloses a wear-resistant and electric-corrosion-resistant CuFe-based in-situ composite material and a preparation method, and relates to the field of high-strength and high-conductivity copper alloy preparation.The preparation method comprises the steps that firstly, optimization design is conducted on formula optimization, Fe solid solution precipitation is promoted through microalloying, and the wear resistance and corrosion resistance of the material are enhanced; in addition, cold spraying parameters are optimized, the oxidation rate is reduced, and uniform distribution of Fe elements is promoted; and finally, optimizing a temperature gradient and a deformation gradient in a large deformation process, and promoting the Fe fibers to be refined, oriented and uniformly arranged, so as to obtain the CuFeCeYAg in-situ fiber reinforced composite material. The method has the advantages of high component control precision, high process stability and high repeatability, and excellent wear resistance and electric corrosion resistance of the in-situ composite material can be realized.

Description

Technical Field

[0001] This application relates to the field of high-strength and high-conductivity copper alloy preparation, especially its application in contact wires on high-speed electrified railways, specifically wear-resistant and galvanic corrosion-resistant CuFeCeYAg in-situ composite materials and their preparation methods. Background Technology

[0002] With the development of long-pulse strong magnetic field technology and high-speed electrified railways, new requirements have been placed on the performance of magnetic field conductors and electric contact wires. These materials are required not only to possess high strength, high electrical conductivity, and high thermal conductivity, but also excellent resistance to friction and arc erosion, especially since arc erosion occurs during the opening / closing process of contact wires and contact networks. Under the action of an arc, the local temperature of the electrical contact surface exceeds the material's phase transition temperature, causing the material to melt, evaporate, or even splash, severely affecting electrical contact performance and shortening the material's service life. Cu-Fe in-situ composite materials, with their low price and excellent strength, electrical conductivity, wear resistance, and arc erosion resistance, have become one of the best materials. However, the casting process and subsequent large deformations can lead to severe segregation or distortion of the microstructure, affecting the solid solution of Fe in the in-situ composite material and resulting in uneven Fe fiber distribution. This, in turn, determines the mechanical properties, electrical conductivity, wear resistance, and arc erosion resistance of Cu-Fe in-situ materials. Summary of the Invention

[0003] To address the issues of poor electrical conductivity, low resistance to friction and wear, and low resistance to arc erosion in Cu-Fe in-situ composite materials, which limit their engineering applications, this application provides a wear-resistant and arc-erosion-resistant CuFeCeYAg in-situ composite material and its preparation method to ensure the forming stability and dimensional integrity of the deposit during the deposition stage.

[0004] To achieve the above objectives, this application adopts the following technical solution: In a first aspect, this application provides a method for preparing a wear-resistant and electro-erosion-resistant in-situ CuFeCeYAg composite material, comprising the following steps: Using Cu powder, Fe powder, Ce powder, Y powder, and Ag powder as raw materials, with Fe accounting for 10-20 wt%, Ce for 0.02-0.05 wt%, Y for 0.02-0.06 wt%, Ag for 0.05-0.10 wt%, and the balance being Cu, the raw materials are mechanically mixed to obtain cold spray pre-formed powder. The surface of the aluminum alloy substrate is successively ground, polished, cleaned, dried, and sandblasted to obtain the coating substrate; The cold spray pre-powder is deposited on the surface of the spray substrate using a low-pressure cold spray method to form a CuFeCeYAg deposit, and the CuFeCeYAg deposit is processed to obtain a deposit blank. The deposited material is subjected to heat treatment and large deformation processing to form and uniformly distribute the Fe fibrous phase in the Cu matrix, thereby obtaining wear-resistant and electro-erosion-resistant CuFeCeYAg in-situ composite wires or rods.

[0005] As a further improvement to this application, the powder particle size in the raw material is 18-30 μm.

[0006] As a further improvement of this application, the obtained cold spray pre-powder is dried by keeping it at 70~90 ℃ for 20~40 min before spraying.

[0007] As a further improvement to this application, the raw materials are formulated in any of the following proportions by weight percentage: The composition is 14 wt% Fe, 0.02 wt% Ce, 0.05 wt% Y, 0.10 wt% Ag, and the balance Cu. The composition is 14 wt% Fe, 0.05 wt% Ce, 0.05 wt% Y, 0.10 wt% Ag, and the balance Cu. The composition is 14 wt% Fe, 0.02 wt% Ce, 0.05 wt% Y, 0.05 wt% Ag, and the balance is Cu. The composition is 14 wt% Fe, 0.04 wt% Ce, 0.06 wt% Y, 0.05 wt% Ag, and the balance is Cu.

[0008] As a further improvement to this application, the low-pressure cold spraying method is specifically as follows: Compressed air is used as the carrier gas, with a carrier gas pressure of 0.2-0.6 MPa, a carrier gas temperature of 200-600 ℃, a nozzle distance of 50-150 mm from the substrate, and a spraying speed of 20-50 g / min.

[0009] As a further improvement to this application, the heat treatment and large deformation processing of the deposited billet includes: Preliminary processing: hot-rolled to Φ15 mm at 940 ℃, and then preliminarily annealed at 850-940 ℃ for 3-4 hours under argon atmosphere protection; Pre-deformation: hot-rolled to Φ12 mm at 940 ℃, and then annealed at 750-850 ℃ for 1-2 h under argon atmosphere protection, followed by cold rolling to Φ9 mm at room temperature; Final deformation: The material is cold-drawn from Φ9 mm to Φ4.5 mm and Φ2.92 mm at room temperature, then annealed three times at 650-750 ℃ ​​for 40-60 min, and then cold-drawn again at room temperature to Φ2.92 mm, Φ1.07 mm, Φ0.39 mm and Φ0.24 mm, and finally annealed at 400-650 ℃ for 20-40 min under argon atmosphere protection.

[0010] As a further improvement of this application, the cold deformation strain is η=ln(A0 / Af), where A0 is the cross-sectional area before deformation and Af is the cross-sectional area after deformation. The cold deformation strain η of the Ф2.92 mm, Ф1.07 mm, Ф0.39 mm and Ф0.24 mm specimens are 1, 2, 4 and 6, respectively.

[0011] As a further improvement to this application, the deposited body blank is cut into a cuboid by wire cutting.

[0012] As a further improvement to this application, after forming the CuFeCeYAg deposit, the composition is also detected by a spectrometer. When the iron content deviation exceeds 0.5wt%, powder needs to be added for adjustment.

[0013] Secondly, this application provides a wear-resistant and electro-erosion-resistant CuFeCeYAg in-situ composite material, prepared by the aforementioned method. The CuFeCeYAg in-situ composite material has a fiber composite structure, conductivity ≥50% IACS, tensile strength ≥650 MPa, and wear amount in a sliding friction test ≤1.4 μg·cm. -2 ·h -1 Arc ablation test ablation weight loss ≤ 89.6 μg·cm -2 ·h -1 .

[0014] Compared with existing technologies, this application has the following features and advantages: This application utilizes large deformation to generate Fe fibers in situ within a copper substrate, thereby strengthening the copper substrate's strength and hardness. However, the Fe dissolved in the substrate severely affects the coating's conductivity, significantly degrading its performance. Furthermore, the refinement and uniform distribution of the Fe fiber phase within the substrate directly impacts its wear resistance and arc erosion resistance. Therefore, this application employs multi-element microalloying technology to optimize and improve the Fe solid solution and the refinement and uniform distribution of the fibers, thereby enhancing its conductivity, wear resistance, and corrosion resistance. Attached image description: To more clearly illustrate the implementation examples of this application and the technical solutions of the prior art, the drawings used in the description of the embodiments or the prior art will be briefly introduced below. Obviously, the drawings described below are only some embodiments of this application.

[0015] Figure 1 Example 2: Tissue with a deformation amount of η=4; Figure 2 Example 2: Friction morphology with a deformation of η=4; Figure 3 Example 2: Electro-erosion morphology with a deformation amount of η=4. Detailed Implementation

[0016] To make the technical problems, technical solutions, and beneficial effects of this application clearer, the following detailed description is provided in conjunction with embodiments. It should be understood that the specific embodiments described herein are merely illustrative and not intended to limit the scope of this application.

[0017] In this application, the term "and / or" describes the relationship between related objects, indicating that three relationships can exist. For example, A and / or B can represent: A existing alone, A and B existing simultaneously, or B existing alone. A and B can be singular or plural. The character " / " generally indicates that the preceding and following related objects have an "or" relationship.

[0018] In this application, "at least one" means one or more, and "more than one" means two or more. "At least one of the following" or similar expressions refer to any combination of these items, including any combination of single or multiple items. For example, "at least one of a, b, or c", or "at least one of a, b, and c", can both mean: a, b, c, ab (i.e., a and b), ac, bc, or abc, where a, b, and c can be single or multiple.

[0019] It should be understood that in the various embodiments of this application, the order of the above processes does not imply the order of execution. Some or all steps may be executed in parallel or sequentially. The execution order of each process should be determined by its function and internal logic, and should not constitute any limitation on the implementation process of the embodiments of this application.

[0020] The terminology used in the embodiments of this application is for the purpose of describing particular embodiments only and is not intended to be limiting of this application. The singular forms “a,” “the,” and “the” used in the embodiments of this application and the appended claims are also intended to include the plural forms unless the context clearly indicates otherwise.

[0021] The weights of the relevant components mentioned in the embodiments of this application can refer not only to the specific content of each component, but also to the proportional relationship between the weights of the components. Therefore, as long as the content of the relevant components is scaled up or down proportionally according to the embodiments of this application, it is within the scope disclosed in the embodiments of this application. Specifically, the mass in the embodiments of this application can be a mass unit known in the chemical industry, such as µg, mg, g, or kg.

[0022] The terms "first" and "second" are used for descriptive purposes only, to distinguish objects, such as substances, from one another, and should not be construed as indicating or implying relative importance or implicitly specifying the number of technical features indicated. For example, without departing from the scope of the embodiments of this application, "first XX" may also be referred to as "second XX," and similarly, "second XX" may also be referred to as "first XX." Thus, features defined with "first" and "second" may explicitly or implicitly include one or more of that feature.

[0023] This application addresses the problems of poor electrical conductivity, low resistance to friction and wear, and low resistance to arc erosion in Cu-Fe in-situ composite materials, which limit their engineering applications. It provides a wear-resistant and arc-erosion-resistant CuFeCeYAg in-situ composite material and its preparation method.

[0024] A wear-resistant and electro-erosion-resistant in-situ CuFeCeYAg composite material and its preparation method, comprising the following steps: 1) In the raw material formulation and pretreatment stage, the main materials are Cu powder, Fe powder, Ce powder, and Y powder, which are formulated according to the target ratio by weight percentage, such as Fe: 10-20 wt%, Ce: 0.02-0.05 wt%, Y: 0.02-0.06 wt%, Ag: 0.05-0.10 wt%, with the remainder being Cu. After mechanically mixing the formulated powders for 8 hours, a cold spray pre-mixed powder is obtained. Before spraying, the powder is dried and held at a set temperature of 80 ℃ in a box-type resistance furnace (KSL-1100X-L) for 30 minutes. In addition, the surface of the 6061-T6 aluminum alloy is ground, polished, cleaned, dried, and sandblasted to obtain the spray substrate.

[0025] 2) Preform preparation stage: The cold spray pre-powder is cold sprayed onto the 6061-T6 aluminum substrate under low pressure, and the cold spray CuFeCeYAg deposit is cut into cuboids with dimensions of 50 mm × 20 mm × 15 mm by wire cutting.

[0026] 3) Large deformation stage: The CuFeCeYAg deposit is pre-deformed (hot rolling, cold rolling) and heat-treated to process the sample to the specified size; finally, the wear-resistant and electro-erosion-resistant CuFeCeYAg in-situ composite material is obtained by drawing.

[0027] This application utilizes rare earth elements to promote the solid solution precipitation of Fe, reducing the amount of Fe phase dissolved into the Cu matrix during the Cu-Fe alloy billet preparation process. This improves the mechanical and electrical properties of Cu-Fe in-situ composite materials while meeting their service requirements for wear resistance and arc erosion resistance. Furthermore, cold spraying technology and temperature gradient and deformation gradient treatment techniques during large deformation heat treatment can reduce the oxygen content of the powder / deposit, inhibit oxidation during spraying, improve interfacial bonding, and promote Fe precipitation and the formation of a uniformly distributed fibrous phase. Ultimately, this broadens the application of Cu-Fe in-situ composite materials in high-strength, high-conductivity, wear-resistant, and arc-erosion-resistant environments.

[0028] This application provides technical solutions for the performance of in-situ composite materials in applications such as railway contact wires, integrated circuit lead frames, resistance welding electrode materials, and thermonuclear reactor components. In this application, a 6061-T6 aluminum alloy substrate is used to provide temporary load-bearing and support for the CuFeCeYAg deposit during low-pressure cold spraying, ensuring the stability and dimensional integrity of the deposit during the deposition stage. After low-pressure cold spraying deposition, the deposit is processed by wire cutting to obtain a deposit blank that meets the requirements for subsequent large deformation processing. This deposit blank serves as the starting material for subsequent hot rolling / cold rolling / cold drawing processes. The final wear-resistant and galvanic corrosion-resistant CuFeCeYAg in-situ composite wire or rod material is based on the microstructure of the CuFeCeYAg deposit after heat treatment and large deformation processing; the 6061-T6 aluminum alloy substrate is not used as the service material for the final product.

[0029] As a further improvement to this application, in step 2), the preparation process of the deposited body employs a low-pressure cold spraying system to prepare a CuFeCeYAg deposited body on a 6061-T6 aluminum alloy substrate. The cold-sprayed CuFeCeYAg deposited body is then cut into cuboids with dimensions of 50 mm × 20 mm × 15 mm using wire cutting. The overall range of the low-pressure cold spraying process parameters is as follows: compressed air as the carrier gas, carrier gas pressure 0.2-0.6 MPa, carrier gas temperature 200-600 ℃, nozzle distance from the substrate 100-150 mm, and spraying speed 20-50 g / min.

[0030] As a further improvement of this application, in step 3), the large deformation process is optimized by using temperature gradient technology for heat treatment, which achieves uniform distribution of alloying elements through segmented temperature and time control; and by using gradient technology for deformation amount, which achieves uniform deformation and distribution of Fe fibers in the coating through different deformation amounts. Preliminary processing: Hot rolling to Ф15 mm at 940 ℃ → Preliminary annealing at 850-940 ℃ for 3-4 h in an argon atmosphere-protected furnace; Pre-deformation: Hot rolling to Ф12 mm at 940 ℃ → Secondary annealing at 750-850 ℃ for 1-2 h in an argon atmosphere-protected furnace → Cold rolling to Ф9 mm at room temperature; Final deformation: Ф9 mm → Cold drawing to Ф4.5 mm at room temperature → Cold drawing to Ф2.92 mm at room temperature → Third annealing at 650-750 ℃ ​​for 40-60 min → Cold drawing to Ф2.92 mm, Ф1.07 mm, Ф0.39 mm and Ф0.24 mm at room temperature → Final annealing at 400-650 ℃ for 20-40 min under argon protection.

[0031] Furthermore, the cold deformation strain is η = In(A0 / A f ), where A0 is the cross-sectional area before deformation, A f After deformation, the cold deformation strain η of the Ф2.92 mm, Ф1.07 mm, Ф0.39 mm and Ф0.24 mm specimens is approximately 1, 2, 4 and 6, respectively.

[0032] As a further improvement to this application, the formulation and preparation process of the wear-resistant and electro-erosion-resistant CuFeCeYAg in-situ composite material are provided. The obtained CuFeCeYAg in-situ composite material has a typical fiber composite structure, and the conductivity of the in-situ composite material is ≥50% IACS; the tensile strength of the in-situ composite material is ≥750 MPa; and the wear amount in the sliding friction test is ≤1.4 μg·cm. -2 ·h -1 Arc ablation test showed an ablation weight loss of ≤89.6 μg·cm⁻¹. -2 ·h -1 .

[0033] Furthermore, several typical formulation combinations are defined to meet the needs of different application scenarios. For example: The composition is 14 wt% Fe, 0.02 wt% Ce, 0.05 wt% Y, 0.10 wt% Ag, and the balance Cu. The composition is 14 wt% Fe, 0.05 wt% Ce, 0.05 wt% Y, 0.10 wt% Ag, and the balance Cu. The composition is 14 wt% Fe, 0.02 wt% Ce, 0.05 wt% Y, 0.05 wt% Ag, and the balance is Cu. The composition is 14 wt% Fe, 0.04 wt% Ce, 0.06 wt% Y, 0.05 wt% Ag, and the balance is Cu.

[0034] The above formulation has been experimentally verified to achieve optimal overall performance while maintaining good plasticity. In practical applications, the Ag ratio can be adjusted according to the service environment to balance cost and performance; this application does not limit this adjustment.

[0035] Traditional Cu-Fe composite materials are typically prepared using a combination of casting and high-strength machining. During solidification, Fe dendrites are initially formed, which are then transformed into a fibrous structure through machining processes such as drawing, rolling, and extrusion. However, as a typical immiscible alloy, Cu-Fe alloys are prone to liquid-liquid phase separation during casting, often leading to severe macroscopic segregation and significantly impairing their mechanical properties. Therefore, this application utilizes cold spraying technology to replace the traditional casting process for preparing Cu-Fe alloys. The cold spraying technology overcomes the tendency for liquid-liquid phase separation during casting of traditional Cu-Fe alloys, avoiding severe macroscopic segregation and significantly reducing performance degradation. Furthermore, by utilizing deformation gradients, heat treatment temperature gradients, and time gradients, Fe dendrites are oriented and uniformly distributed into a fibrous phase.

[0036] The CuFeCeYAg deposit is formed layer by layer on the surface of the substrate using a low-pressure cold spraying method. Stable accumulation and dense formation of the deposit are achieved by controlling process parameters such as carrier gas pressure, carrier gas temperature, nozzle distance, and spraying speed. Reciprocating scanning and multi-pass deposition methods can be used during the deposition process to ensure the deposit reaches the required thickness and volume for processing into blanks of specified dimensions. To ensure the consistency of the chemical composition and formulation of the deposit, compositional analysis is performed. When the deviation of key elements exceeds a preset threshold, the cold-sprayed pre-powder ratio is adjusted to compensate and improve the compositional control accuracy and batch stability of the deposit. This application studies Cu-Fe in-situ composite materials through processes such as alloy material formulation adjustment, cold-sprayed blank preparation, heat treatment temperature gradient adjustment, and deformation gradient technology. By adjusting the optimal formulation ratio, spraying process, solution temperature and time, hot-rolled / cold-rolled dimensions, and final cold-drawn dimensions (deformation), a Cu-Fe in-situ composite material with optimal wear resistance and electrical corrosion resistance is obtained. This composite material has the advantages of high compositional control accuracy, strong process stability, and high repeatability.

[0037] The properties of the wear-resistant and electro-erosion-resistant in-situ composite materials prepared in the following examples are shown in Table 1.

[0038] Example 1 1) Optimize the process formula and pretreatment. Use Cu powder, Fe powder, Ce powder, Y powder, and Ag powder, all with particle sizes of 18-30 μm, an average of 24 μm, and a purity of 99 wt%. Mix them according to the following proportions: Fe: 14 wt%, Ce: 0.02 wt%, Y: 0.05 wt%, Ag: 0.10 wt%, with the remainder being Cu. After mixing the proportioned ingredients in a mechanical mixer, preheat the powder in a box-type resistance furnace (KSL-1100X-L) at 80℃ for 30 min. Additionally, perform surface treatment on the 6061-T6 aluminum substrate, sequentially grinding, polishing, cleaning, drying, and sandblasting to obtain the substrate to be coated.

[0039] 2) Optimize the cold spraying process. Using compressed air as the carrier gas (pressure 0.5 MPa, temperature 300 ℃), with a nozzle distance of 100 mm from the substrate and a spraying speed of 50 g / min, a CuFeCeYAg deposit was prepared on a 6061-T6 aluminum alloy substrate. The cold-sprayed CuFeCeYAg deposit was then cut into cuboids with dimensions of 50 mm × 20 mm × 15 mm using wire cutting.

[0040] 3) Preliminary processing: The deposit is hot-rolled to Ф15 mm at 940℃ → annealed at 940℃ for 4 h in an argon atmosphere-protected furnace; Pre-deformation: hot-rolled to Ф12 mm at 940℃ → annealed at 850℃ for 2 h in an argon atmosphere-protected furnace → cold-rolled to Ф9 mm at room temperature; Final deformation: Ф9 mm → rough cold-drawn to Ф4.5 mm at room temperature → rough cold-drawn to Ф2.92 mm → annealed for 60 min at 750℃ → fine cold-drawn to Ф1.07 mm at room temperature (deformation η=2) → final annealing at 650℃ for 30 min.

[0041] Example 2 1) Optimize the process formulation and pretreatment. Use Cu powder, Fe powder, Ce powder, Y powder, and Ag powder, all with particle sizes of 18-30 μm, an average of 24 μm, and a purity of 99 wt%. Mix them according to the following proportions: Fe: 14 wt%, Ce: 0.05 wt%, Y: 0.05 wt%, Ag: 0.10 wt%, with the remainder being Cu. After mixing the proportioned ingredients in a mechanical mixer, preheat the powder in a box-type resistance furnace (KSL-1100X-L) at 80 ℃ for 30 min. Additionally, perform surface treatment on the 6061-T6 aluminum substrate, sequentially grinding, polishing, cleaning, drying, and sandblasting to obtain the substrate to be coated.

[0042] 2) Optimize the cold spraying process. Using compressed air as the carrier gas (pressure 0.5 MPa, temperature 300 ℃), with a nozzle distance of 100 mm from the substrate and a spraying speed of 50 g / min, a CuFeCeYAg deposit was prepared on a 6061-T6 aluminum alloy substrate. The composition was analyzed using a spectrometer; when the iron content deviation exceeded 0.5 wt%, powder was added for adjustment. The cold-sprayed CuFeCeYAg deposit was then cut into cuboids with dimensions of 50 mm × 20 mm × 15 mm using wire cutting.

[0043] 3) Preliminary processing: The deposit is hot-rolled to Ф15 mm at 940℃ → annealed at 900℃ for 3 hours in an argon atmosphere-protected furnace; Pre-deformation: hot-rolled to Ф12 mm at 940℃ → annealed at 800℃ for 1.5 hours in an argon atmosphere-protected furnace → cold-rolled to Ф9 mm at room temperature; Final deformation: Ф9 mm → rough cold-drawn to Ф4.5 mm at room temperature → rough cold-drawn to Ф2.92 mm → annealed for 45 minutes at 700℃ → fine cold-drawn to Ф0.39 mm at room temperature (deformation η=4) → final annealing at 600℃ for 20 minutes.

[0044] Figure 1 (Microstructure diagram with deformation η=4) As a microstructure diagram, it reflects the internal structure of CuFeCeYAg composite material. Combined with the technical solution of this application (large deformation gradient + temperature gradient process) and the formulation of Example 2, it can be observed that: the material forms a typical Fe fiber reinforced composite structure: Fe fibers are oriented and uniformly distributed in the Cu matrix, without obvious agglomeration, segregation or coarse impurity phases; Fe fiber size is refined: through the synergistic effect of large deformation strain (η=4) and segmented annealing, Fe dendrites have been completely transformed into slender fibers, and the fiber interface with the Cu matrix is ​​tightly bonded, without obvious pores, oxide inclusions or interface separation defects.

[0045] These microscopic features directly confirm that this application has solved the "macro-segregation" problem in the traditional Cu-Fe alloy casting process (the advantages of cold spraying replacing casting + gradient deformation process). The uniform and refined Fe fibers provide a "strengthening mechanism" (fiber strengthening effect) for the material, which is the microscopic basis for the tensile strength of 750 MPa in Example 2 (far exceeding the minimum standard of ≥650 MPa) and the surface hardness of 421 Hv0.1. The directional arrangement of fibers and the absence of severe solid solution segregation ensure the smooth flow of electron transport channels, providing structural support for the conductivity of 68% IACS (far exceeding the minimum standard of ≥50% IACS).

[0046] Figure 2 (Friction morphology diagram with deformation η=4) shows the surface morphology after the sliding friction test, combined with the wear amount (0.58 μg·cm) in Example 2.- ²·h - ¹, far below ≤1.4 μg·cm - ²·h - ¹ (upper limit), it can be observed that: the friction surface is flat and smooth, without obvious furrows, adhesive wear marks or large-area peeling; the wear area only has slight wear marks, without "local stress concentration wear" caused by uneven Fe phase distribution (such as pits formed by the shedding of coarse Fe phase). The uniform distribution of Fe fibers forms "hard phase support", reducing plastic deformation and material loss during the friction process; the synergistic effect of multi-element microalloys (Ce, Y, Ag) (promoting Fe solid solution precipitation and improving interfacial bonding) reduces oxidative wear and adhesive wear during the friction process, giving the material low wear characteristics and meeting the application requirements of high-frequency friction scenarios such as railway contact wires.

[0047] Figure 3 (Electro-erosion morphology diagram with deformation η=4) shows the surface morphology after the arc ablation test, combined with the ablation weight loss (22.2 μg·cm) of Example 2. - ²·h - ¹, far below ≤89.6 μg·cm - ²·h - ¹ (upper limit), it can be observed that: there are no obvious melting spatter marks, large-area pits or oxide peeling layers on the electro-eroded surface; only slight surface oxidation marks exist in the ablation area, without "localized severe ablation" caused by component segregation or structural defects (such as concentrated ablation caused by Fe phase agglomeration in traditional Cu-Fe alloys). The cold spraying process reduces the oxygen content of the material, reducing the aggravation of oxidation reaction during the ablation process; the addition of rare earth elements (Ce, Y) optimizes the oxidation resistance of the Cu matrix and inhibits melting and evaporation at high arc temperatures; the uniformly distributed Fe fibers improve the high-temperature stability of the material, avoid material spatter caused by local thermal stress concentration, and enable the material to withstand arc erosion during the "open / close" process of the contact line, thus extending its service life.

[0048] Figures 1-3 This demonstrates that the combination of the multi-element microalloying formula (CuFeCeYAg), cold spraying forging, and gradient deformation + temperature gradient heat treatment technology in this application successfully achieved a closed loop of "microstructure optimization → macroscopic performance improvement." In Example 2, the deformation amount η=4, and its corresponding... Figures 1-3The material exhibits the best microstructure (most uniform fiber distribution, slightest friction / electro-erosion marks) and the best overall macroscopic properties (conductivity 68% IACS, tensile strength 750 MPa, wear amount 0.58, ablation weight loss 22.2%) among the four examples. This demonstrates that when the cold deformation strain η=4, the material's microstructure and macroscopic properties reach optimal balance, providing intuitive experimental evidence for the "process parameter optimization" of this application. None of the three attached figures show typical defects of traditional Cu-Fe alloys (such as Fe phase segregation, severe wear on the friction surface, and intense melting of the electro-erosion surface), directly proving that this application effectively solves the core problems of "uneven Fe element solid solution, disordered fiber distribution, and low wear and electro-erosion resistance" in the background technology, demonstrating significant technological advancement.

[0049] Example 3 1) Optimize the process formulation and pretreatment. Use Cu powder, Fe powder, Ce powder, Y powder, and Ag powder, all with particle sizes of 18-30 μm, an average of 24 μm, and a purity of 99 wt%. Mix them according to the following ratio: Fe: 14 wt%, Ce: 0.02 wt%, Y: 0.05 wt%, Ag: 0.05 wt%, with the remainder being Cu. After mixing the proportioned ingredients in a mechanical mixer, preheat the powder in a box-type resistance furnace (KSL-1100X-L) at 80℃ for 30 min. Additionally, perform surface treatment on the 6061-T6 aluminum substrate, sequentially grinding, polishing, cleaning, drying, and sandblasting to obtain the substrate to be coated.

[0050] 2) Optimize the cold spraying process. Using compressed air as the carrier gas (pressure 0.5 MPa, temperature 300 ℃), with a nozzle distance of 100 mm from the substrate and a spraying speed of 50 g / min, a CuFeCeYAg deposit was prepared on a 6061-T6 aluminum alloy substrate. The cold-sprayed CuFeCeYAg deposit was then cut into cuboids with dimensions of 50 mm × 20 mm × 15 mm using wire cutting.

[0051] 3) Preliminary processing: After hot rolling at 940 ℃, the surface is peeled and processed to Ф15 mm → annealing at 850 ℃ for 2 h in an argon atmosphere protected furnace; Pre-deformation: hot rolling at 940 ℃ to Ф12 mm → secondary annealing at 750 ℃ ​​for 1 h in an argon atmosphere protected furnace → cold rolling at room temperature to Ф9 mm; Final deformation: Ф9 mm → rough cold drawing at room temperature to Ф4.5 mm → rough cold drawing to Ф2.92 mm → annealing at 650 ℃ for 30 min for the third time → fine cold drawing at room temperature to Ф0.24 mm (deformation amount η=6) → final annealing at 450 ℃ for 20 min.

[0052] Example 4 1) Optimize the process formulation and pretreatment. Use Cu powder, Fe powder, Ce powder, Y powder, and Ag powder, all with particle sizes of 18-30 μm, an average of 24 μm, and a purity of 99 wt%. Produce the following proportions: Fe: 14 wt%, Ce: 0.04 wt%, Y: 0.06 wt%, Ag: 0.05 wt%, with the remainder being Cu. After mixing the proportioned ingredients in a mechanical mixer, preheat the powder in a box-type resistance furnace (KSL-1100X-L) at 80 ℃ for 30 min. Additionally, perform surface treatment on the 6061-T6 aluminum substrate, sequentially grinding, polishing, cleaning, drying, and sandblasting to obtain the substrate to be coated.

[0053] 2) Optimize the cold spraying process. Using compressed air as the carrier gas (pressure 0.5 MPa, temperature 300 ℃), with a nozzle distance of 100 mm from the substrate and a spraying speed of 50 g / min, a CuFeCeYAg deposit was prepared on a 6061-T6 aluminum alloy substrate. The cold-sprayed CuFeCeYAg deposit was then cut into cuboids with dimensions of 50 mm × 20 mm × 15 mm using wire cutting.

[0054] 3) Preliminary processing: The deposit is hot-rolled to Ф15 mm at 940 ℃ → annealed at 880 ℃ for 2 h in an argon atmosphere protected furnace; Pre-deformation: hot-rolled to Ф12 mm at 940 ℃ → annealed again at 780 ℃ for 1 h in an argon atmosphere protected furnace → cold-rolled to Ф9 mm at room temperature; Final deformation: Ф9 mm → rough cold-drawn to Ф4.5 mm at room temperature → rough cold-drawn to Ф2.92 mm → annealed for 30 min at 680 ℃ → fine cold-drawn to Ф1.07 mm at room temperature (deformation η=2) → final annealing at 480 ℃ for 20 min.

[0055] The performance testing of the wear-resistant and electro-erosion-resistant CuFeCeYAg in-situ composite material in this application can be characterized as follows: conductivity is measured at room temperature using a conductivity testing device and converted to IACS according to the IACS system; tensile strength is obtained by room temperature tensile testing; surface hardness is characterized using a microhardness tester in the Hv0.1 manner; wear resistance is obtained by sliding friction testing, and the wear amount per unit area per unit time (μg·cm) is calculated by combining the mass difference or volume loss of the sample before and after wear with the contact area and test time. -2 ·h -1 The resistance to electrical corrosion was determined using an arc ablation test. The mass difference of the sample before and after ablation, combined with the ablated area and test time, was used to calculate the ablation weight loss per unit area per unit time (μg·cm). -2 ·h -1The above test results are used to compare the overall variation patterns of material strength, conductivity, wear resistance, and electrical erosion resistance under different formulations and deformation conditions.

[0056] The performance parameters of the in-situ composite materials prepared in Examples 1-4 are shown in Table 1: Table 1

[0057] The table above shows that the prepared CuFeCeYAg in-situ composite material / deposit / wire has a fiber-reinforced structure. The conductivity of the in-situ composite material is ≥50% IACS; the tensile strength of the in-situ composite material is ≥650MPa; and the wear amount in the sliding friction test is ≤1.4μg·cm. -2 ·h -1 Arc ablation test: ablation weight loss ≤ 89.6 μg·cm³ -2 ·h -1 .

[0058] Example 5 1) Optimize the process formulation and pretreatment. Use Cu powder, Fe powder, Ce powder, Y powder, and Ag powder, all with particle sizes of 18-30 μm, an average of 24 μm, and a purity of 99 wt%. Mix them according to the following ratio: Fe: 10 wt%, Ce: 0.03 wt%, Y: 0.02 wt%, Ag: 0.06 wt%, with the remainder being Cu. After mixing the proportioned ingredients in a mechanical mixer, preheat the powder in a box-type resistance furnace (KSL-1100X-L) at 85℃ for 40 min. Additionally, perform surface treatment on the 6061-T6 aluminum substrate, sequentially grinding, polishing, cleaning, drying, and sandblasting to obtain the substrate to be coated.

[0059] 2) Optimize the cold spraying process. Using compressed air as the carrier gas (pressure 0.6 MPa, temperature 200 ℃), with a nozzle distance of 50 mm from the substrate and a spraying speed of 20 g / min, a CuFeCeYAg deposit was prepared on a 6061-T6 aluminum alloy substrate. The cold-sprayed CuFeCeYAg deposit was then cut into cuboids with dimensions of 50 mm × 20 mm × 15 mm using wire cutting.

[0060] 3) Preliminary processing: After hot rolling at 940 ℃, the surface is peeled and processed to Ф15 mm → annealing at 900 ℃ for 2 h in an argon atmosphere protected furnace; Pre-deformation: hot rolling at 940 ℃ to Ф12 mm → secondary annealing at 780 ℃ for 1 h in an argon atmosphere protected furnace → cold rolling at room temperature to Ф9 mm; Final deformation: Ф9 mm → rough cold drawing at room temperature to Ф4.5 mm → rough cold drawing to Ф2.92 mm → annealing at 680 ℃ for 30 min for the third time → fine cold drawing at room temperature to Ф0.24 mm (deformation amount η=6) → final annealing at 550 ℃ for 20 min.

[0061] Example 6 1) Optimize the process formulation and pretreatment. Use Cu powder, Fe powder, Ce powder, Y powder, and Ag powder, all with particle sizes of 18-30 μm, an average of 24 μm, and a purity of 99 wt%. Produce the following proportions: Fe: 20 wt%, Ce: 0.05 wt%, Y: 0.05 wt%, Ag: 0.1 wt%, with the remainder being Cu. After mixing the proportioned ingredients in a mechanical mixer, preheat the powder in a box-type resistance furnace (KSL-1100X-L) at 70℃ for 40 min. Additionally, perform surface treatment on the 6061-T6 aluminum substrate, sequentially grinding, polishing, cleaning, drying, and sandblasting to obtain the substrate to be coated.

[0062] 2) Optimize the cold spraying process. Using compressed air as the carrier gas (pressure 0.6 MPa, temperature 600 ℃), a nozzle distance of 150 mm from the substrate, and a spraying speed of 30 g / min, a CuFeCeYAg deposit was prepared on a 6061-T6 aluminum alloy substrate. The cold-sprayed CuFeCeYAg deposit was then cut into cuboids with dimensions of 50 mm × 20 mm × 15 mm using wire cutting.

[0063] 3) Preliminary processing: The deposit is hot-rolled to Ф15 mm at 940 ℃ → annealed at 940 ℃ for 2 h in an argon atmosphere protected furnace; Pre-deformation: hot-rolled to Ф12 mm at 940 ℃ → annealed at 850 ℃ for 1 h in an argon atmosphere protected furnace → cold-rolled to Ф9 mm at room temperature; Final deformation: Ф9 mm → rough cold-drawn to Ф4.5 mm at room temperature → rough cold-drawn to Ф2.92 mm → annealed for 60 min at 750 ℃ ​​→ fine cold-drawn to Ф1.07 mm at room temperature (deformation η=2) → final annealing at 650 ℃ for 40 min.

[0064] Example 7 1) Optimize the process formulation and pretreatment. Use Cu powder, Fe powder, Ce powder, Y powder, and Ag powder, all with particle sizes of 18-30 μm, an average of 24 μm, and a purity of 99 wt%. Mix them according to the following ratio: Fe: 18 wt%, Ce: 0.02 wt%, Y: 0.04 wt%, Ag: 0.08 wt%, with the remainder being Cu. After mixing the proportioned ingredients in a mechanical mixer, preheat the powder in a box-type resistance furnace (KSL-1100X-L) at 80℃ for 30 min. Additionally, perform surface treatment on the 6061-T6 aluminum substrate, sequentially grinding, polishing, cleaning, drying, and sandblasting to obtain the substrate to be coated.

[0065] 2) Optimize the cold spraying process. Using compressed air as the carrier gas (pressure 0.5 MPa, temperature 300 ℃), with a nozzle distance of 100 mm from the substrate and a spraying speed of 50 g / min, a CuFeCeYAg deposit was prepared on a 6061-T6 aluminum alloy substrate. The cold-sprayed CuFeCeYAg deposit was then cut into cuboids with dimensions of 50 mm × 20 mm × 15 mm using wire cutting.

[0066] 3) Preliminary processing: The deposit is hot-rolled to Ф15 mm at 940℃ → annealed at 850℃ for 3 h in an argon atmosphere-protected furnace; Pre-deformation: hot-rolled to Ф12 mm at 940℃ → annealed again at 750℃ for 1 h in an argon atmosphere-protected furnace → cold-rolled to Ф9 mm at room temperature; Final deformation: Ф9 mm → rough cold-drawn to Ф4.5 mm at room temperature → rough cold-drawn to Ф2.92 mm → annealed for 3 times at 650℃ for 45 min → fine cold-drawn to Ф1.07 mm at room temperature (deformation η=2) → final annealing at 400℃ for 35 min.

[0067] Example 8 1) Optimize the process formulation and pretreatment. Use Cu powder, Fe powder, Ce powder, Y powder, and Ag powder, all with particle sizes of 18-30 μm, an average of 24 μm, and a purity of 99 wt%. Mix them according to the following ratio: Fe: 15 wt%, Ce: 0.02 wt%, Y: 0.04 wt%, Ag: 0.10 wt%, with the remainder being Cu. After mixing the proportioned ingredients in a mechanical mixer, preheat the powder in a box-type resistance furnace (KSL-1100X-L) at 80 ℃ for 30 min. In addition, perform surface treatment on the 6061-T6 aluminum substrate, sequentially grinding, polishing, cleaning, drying, and sandblasting to obtain the substrate to be coated.

[0068] 2) Optimize the cold spraying process. Using compressed air as the carrier gas (pressure 0.3 MPa, temperature 350 ℃), with a nozzle distance of 80 mm from the substrate and a spraying speed of 30 g / min, a CuFeCeYAg deposit was prepared on a 6061-T6 aluminum alloy substrate. The composition was analyzed using a spectrometer; when the iron content deviation exceeded 0.5 wt%, powder was added for adjustment. The cold-sprayed CuFeCeYAg deposit was then cut into cuboids with dimensions of 50 mm × 20 mm × 15 mm using wire cutting.

[0069] 3) Preliminary processing: The deposit is hot-rolled to Ф15 mm at 940℃ → annealed at 920℃ for 3 hours in an argon atmosphere-protected furnace; Pre-deformation: hot-rolled to Ф12 mm at 940℃ → annealed at 820℃ for 1.5 hours in an argon atmosphere-protected furnace → cold-rolled to Ф9 mm at room temperature; Final deformation: Ф9 mm → rough cold-drawn to Ф4.5 mm at room temperature → rough cold-drawn to Ф2.92 mm → annealed for 45 minutes at 730℃ → fine cold-drawn to Ф0.39 mm at room temperature (deformation η=4) → final annealing at 500℃ for 20 minutes.

[0070] The above description is only a preferred embodiment of this application. It should be noted that for those skilled in the art, several improvements and modifications can be made without departing from the principle of this application, and these improvements and modifications should also be considered within the scope of protection of this application.

Claims

1. A method for preparing a wear-resistant and electro-erosion-resistant in-situ CuFeCeYAg composite material, characterized in that, Includes the following steps: Using Cu powder, Fe powder, Ce powder, Y powder, and Ag powder as raw materials, with Fe accounting for 10-20 wt%, Ce for 0.02-0.05 wt%, Y for 0.02-0.06 wt%, Ag for 0.05-0.10 wt%, and the balance being Cu, the raw materials are mechanically mixed to obtain cold spray pre-formed powder. The surface of the aluminum alloy substrate is successively ground, polished, cleaned, dried, and sandblasted to obtain the coating substrate; The cold spray pre-powder is deposited on the surface of the spray substrate using a low-pressure cold spray method to form a CuFeCeYAg deposit, and the CuFeCeYAg deposit is processed to obtain a deposit blank. The deposited material is subjected to heat treatment and large deformation processing to form and uniformly distribute the Fe fibrous phase in the Cu matrix, thereby obtaining wear-resistant and electro-erosion-resistant CuFeCeYAg in-situ composite wires or rods.

2. The method for preparing a wear-resistant and electro-erosion-resistant CuFeCeYAg in-situ composite material according to claim 1, characterized in that, The powder particle size of the raw material is 18-30 μm.

3. The method for preparing a wear-resistant and electro-erosion-resistant CuFeCeYAg in-situ composite material according to claim 1, characterized in that, Before spraying, the obtained cold spray pre-powder is dried by keeping it at 70~90 ℃ for 20~40 min.

4. The method for preparing a wear-resistant and electro-erosion-resistant CuFeCeYAg in-situ composite material according to claim 1, characterized in that, The proportions of the raw materials are any of the following: The composition is 14 wt% Fe, 0.02 wt% Ce, 0.05 wt% Y, 0.10 wt% Ag, and the balance Cu. The composition is 14 wt% Fe, 0.05 wt% Ce, 0.05 wt% Y, 0.10 wt% Ag, and the balance Cu. The composition is 14 wt% Fe, 0.02 wt% Ce, 0.05 wt% Y, 0.05 wt% Ag, and the balance is Cu. The composition is 14 wt% Fe, 0.04 wt% Ce, 0.06 wt% Y, 0.05 wt% Ag, and the balance is Cu.

5. The method for preparing a wear-resistant and electro-erosion-resistant CuFeCeYAg in-situ composite material according to claim 1, characterized in that, The low-pressure cold spraying method is specifically as follows: Compressed air is used as the carrier gas, with a carrier gas pressure of 0.2-0.6 MPa, a carrier gas temperature of 200-600 ℃, a nozzle distance of 50-150 mm from the substrate, and a spraying speed of 20-50 g / min.

6. The method for preparing a wear-resistant and electro-erosion-resistant CuFeCeYAg in-situ composite material according to claim 1, characterized in that, The heat treatment and large deformation processing of the deposited billet includes: Preliminary processing: hot-rolled to Φ15 mm at 940 ℃, and then preliminarily annealed at 850-940 ℃ for 3-4 h under argon atmosphere protection; Pre-deformation: hot-rolled to Φ12 mm at 940 ℃, and then annealed at 750-850 ℃ for 1-2 h under argon atmosphere protection, followed by cold rolling to Φ9 mm at room temperature; Final deformation: The material is cold-drawn from Φ9 mm to Φ4.5 mm and Φ2.92 mm at room temperature, then annealed three times at 650-750 ℃ ​​for 40-60 min, and then cold-drawn again at room temperature to Φ2.92 mm, Φ1.07 mm, Φ0.39 mm and Φ0.24 mm, and finally annealed at 400-650 ℃ for 20-40 min under argon atmosphere protection.

7. The method for preparing a wear-resistant and electro-erosion-resistant CuFeCeYAg in-situ composite material according to claim 6, characterized in that, For specimens cold-drawn at room temperature to Φ2.92 mm, Φ1.07 mm, Φ0.39 mm and Φ0.24 mm, the cold deformation strain is η=ln(A0 / Af), where A0 is the cross-sectional area before deformation and Af is the cross-sectional area after deformation; the cold deformation strain η of the Φ2.92 mm, Φ1.07 mm, Φ0.39 mm and Φ0.24 mm specimens are 1, 2, 4 and 6, respectively.

8. The method for preparing a wear-resistant and electro-erosion-resistant CuFeCeYAg in-situ composite material according to claim 1, characterized in that, The deposited material is cut into cuboids by wire cutting.

9. The method for preparing a wear-resistant and electro-erosion-resistant CuFeCeYAg in-situ composite material according to claim 1, characterized in that, After the CuFeCeYAg deposit is formed, the composition is also detected by a spectrometer. If the iron content deviation exceeds 0.5wt%, powder needs to be added for adjustment.

10. A wear-resistant and electro-erosion-resistant CuFeCeYAg in-situ composite material, characterized in that, The CuFeCeYAg in-situ composite material, prepared by any one of claims 1 to 9, has a fiber composite structure, electrical conductivity ≥50% IACS, tensile strength ≥650 MPa, and wear amount ≤1.4 μg·cm in sliding friction test. -2 ·h -1 Arc ablation test ablation weight loss ≤ 89.6 μg·cm -2 ·h -1 .

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