Cu-Fe-Re alloy based on regulation of deformation amount and preparation method thereof

Abstract

This invention relates to the field of copper alloy materials technology, and more particularly to a Cu-Fe-Re alloy based on controlled deformation and its preparation method. The alloy composition, by weight percentage, includes: 10%~20% iron, 0.2%~1.0% rare earth elements, and the balance being copper and unavoidable impurities; the rare earth elements are selected from one or more of cerium, lanthanum, and yttrium. Based on rare earth refinement, this invention, through precise control of the deformation amount, transforms the precipitated iron phase from coarse dendrites to dispersed droplets, which, after further deformation, evolve into a fibrous structure. The gaps between iron phases are significantly reduced, and the distribution becomes more compact. The optimized selection of the deformation amount achieves the best match between dislocation strengthening and second-phase strengthening. Simultaneously, in terms of electrical conductivity, by controlling the dislocation density and second-phase morphology, the electron scattering effect is minimized, achieving a synergistic improvement in strength and conductivity. The introduction of rare earth elements can purify grain boundaries, refine the as-cast structure, and improve the distribution of the second phase.

Description

Technical Field

[0001] This invention relates to the field of copper alloy materials technology, and in particular to a Cu-Fe-Re alloy based on controlled deformation and its preparation method. Background Technology

[0002] Copper-iron alloys, as a structural and functional integrated material, possess excellent mechanical properties, good electrical conductivity, outstanding corrosion resistance, and low raw material costs. They have broad application prospects in shipbuilding, machinery manufacturing, power equipment, and the electronics industry. This alloy can be used to manufacture high-quality mechanical parts such as engines, structural components, and housings, and is one of the important candidate materials for achieving lightweight and high-reliability designs.

[0003] A search revealed existing methods for preparing copper-iron alloys. For example, patent document CN107201461B discloses a high-strength, high-ductility, dual-phase synergistic precipitation Cu-Fe-CP alloy material, which induces a martensitic transformation of the Fe-C phase through ultra-low temperature cold rolling deformation, resulting in a tensile strength exceeding 650 MPa. However, this technology relies on ultra-low temperature rolling (such as liquid nitrogen temperature), requiring sophisticated equipment, incurring high production costs, and involving complex processes, making stable industrial production difficult. Another existing method involves preparing copper-iron alloys through triaxial multi-pass compression deformation, which can achieve a fine twinned structure, but it does not involve the addition of rare earth elements and the synergistic control of deformation amount, making it difficult to achieve an optimal balance between strength and conductivity.

[0004] Deformation amount control, as a core means of strain strengthening, has a decisive influence on the microstructure evolution and comprehensive properties of copper-iron alloys. With changes in deformation amount, the grain size, dislocation density, and morphology, size, and distribution of the second phase (Fe phase) within the alloy all undergo significant changes, thereby directly controlling the material's mechanical behavior and corrosion response. Studies have shown that deformation amount determines the dispersion degree and interface characteristics of the strengthening phase by influencing the fragmentation, refinement, and redistribution processes of the ferrous phase. Simultaneously, crystal defects introduced by deformation (such as dislocations and subgrain boundaries) alter the electrochemical activity and passivation behavior of the alloy surface. Appropriate deformation amount can achieve uniform refinement of the ferrous phase and optimized configuration of dislocation density, maintaining good conductivity while improving strength; however, excessive deformation amount may lead to excessively high dislocation density and over-refinement of the second phase, exacerbating electron scattering and significantly reducing conductivity. Therefore, precise control of deformation amount is a key technological path to achieve synergistic optimization of the mechanical and electrical properties of copper-iron alloys.

[0005] Based on this, this paper proposes a Cu-Fe-Re alloy based on controlled deformation. By introducing trace amounts of rare earth element (Re) into the copper-iron system, its effects on purifying grain boundaries, refining microstructure, and improving the distribution of the second phase are utilized to further enhance the optimization effect of deformation control on the microstructure. The evolution of the microstructure of Cu-Fe-Re alloy under different deformation conditions is systematically studied, revealing the influence mechanism of deformation on microscopic features such as grain structure, iron phase morphology and distribution, and dislocation configuration, and establishing the intrinsic relationship between deformation and mechanical and electrical properties. The focus is on elucidating the mechanism of deformation control on the mechanical properties of the alloy, including its influence on grain size, dislocation density and distribution, and the morphology and distribution of the second phase (Fe phase).

[0006] This study aims to construct a synergistic control framework for deformation amount, microstructure, and comprehensive properties, providing theoretical basis and process guidance for developing novel copper-iron alloys with both high strength and good electrical conductivity, and promoting their engineering applications in fields such as power electronics and high-end equipment manufacturing. Therefore, a Cu-Fe-Re alloy based on deformation amount control and its preparation method are needed to solve the above problems. Summary of the Invention

[0007] The purpose of this invention is to solve the problems mentioned in the background section.

[0008] To achieve the above objectives, the present invention adopts the following technical solution: A Cu-Fe-Re alloy based on controlled deformation and its preparation method, wherein the alloy composition by weight percentage includes: 10%~20% iron, 0.2%~1.0% rare earth elements, and the balance being copper and unavoidable impurities; The rare earth element is selected from one or more of cerium, lanthanum, and yttrium.

[0009] Preferably, the alloy achieves synergistic optimization of mechanical and electrical properties by controlling the amount of deformation to ensure that the iron phase in its microstructure is uniformly distributed in a fibrous manner.

[0010] Preferably, the content of the rare earth element is 0.5% to 0.8%.

[0011] Preferably, the alloy has a tensile strength ≥550MPa and a conductivity ≥56%IACS.

[0012] Preferably, the iron phase in the microstructure of the alloy is uniformly distributed in a fibrous manner, with reduced gaps between the iron phases and a dense distribution.

[0013] A method for preparing Cu-Fe-Re alloy based on controlled deformation includes the following steps: Step 1: Take iron with a purity ≥99.96%, copper with a purity ≥99.9%, and rare earth copper alloy according to the design, place them in a vacuum high-frequency induction furnace, and melt them at 1150~1200℃ under an argon atmosphere to obtain the alloy melt. Step 2: The melt is cast into a solid shape at a casting temperature of 1100~1150℃ to obtain a copper alloy ingot. Step 3: Homogenize the ingot at 900~1000℃ for 3~5 hours, and then remove surface defects; Step 4: Hot forge the homogenized ingot at 900~950℃ into a thick bar with a thickness of 8mm. Step 5: The hot-forged bar is subjected to multiple cold rolling passes to obtain strip.

[0014] Preferably, the pressure of the argon atmosphere in step one is 0.06~0.08 MPa.

[0015] Preferably, the thickness of the strip after multiple cold rolling passes in step five is 1 mm, 0.8 mm, 0.5 mm, or 0.1 mm.

[0016] Preferably, the deformation control of the multi-pass cold rolling in step five causes the iron phase in the strip to change from dendritic to droplet-like, and further evolve into a fibrous structure.

[0017] The present invention has at least the following beneficial effects: 1. The introduction of rare earth elements can purify grain boundaries, refine the as-cast structure, improve the distribution of the second phase, reduce the adverse effects of impurity elements on electrical conductivity, and lay a good microstructure foundation for subsequent heat treatment and deformation processing.

[0018] 2. Building upon rare earth element refinement, precise control of deformation amounts transforms the precipitated iron phase from coarse dendrites into dispersed droplets. Further deformation processing then evolves this into a fibrous structure, significantly reducing the gaps between iron phases and resulting in a denser distribution. Optimized selection of deformation amounts achieves an optimal match between dislocation strengthening and second-phase strengthening. Simultaneously, by controlling dislocation density and second-phase morphology, electron scattering effects are minimized, achieving a synergistic improvement in both strength and conductivity.

[0019] 3. Compared to untreated copper-iron alloys, Cu-Fe-Re alloy strips with synergistic regulation of rare earth elements and deformation exhibit significant improvements in both mechanical and electrical properties. In terms of mechanical properties, optimized deformation achieves a good balance between strength and plasticity, resulting in excellent overall mechanical properties. Regarding electrical conductivity, the addition of rare earth elements purifies the matrix and reduces solid solution scattering of impurity elements, while the optimized deformation effectively controls dislocation density and second-phase morphology, minimizing electron scattering. This achieves high conductivity while maintaining high strength, meeting the dual requirements of structural-functional integrated materials for both mechanical and electrical properties.

[0020] 4. The synergistic optimization of the microstructure and properties of Cu-Fe-Re alloys enables them to adapt to different service environments. This alloy combines high strength, good electrical conductivity, excellent corrosion resistance, and cost advantages, and can be widely used in shipbuilding, marine engineering, machinery manufacturing, power equipment, and the electronics industry. In particular, it shows outstanding comprehensive advantages in applications such as power equipment, electronic components, and high-load transmission parts where both electrical conductivity and mechanical properties are required. This provides reliable support for expanding the engineering applications of copper-iron alloys in high-end equipment manufacturing and the electronics and electrical fields. Attached Figure Description

[0021] To more clearly illustrate the technical solutions of the embodiments of the present invention, the drawings used in the following description of the embodiments will be briefly introduced. Obviously, the drawings described below are some embodiments of the present invention. For those skilled in the art, other drawings can be obtained based on these drawings without creative effort.

[0022] Figure 1 Schematic diagram of 0.1mm Cu-15Fe-Re alloy strip with different rare earth contents; Figure 2 This is a schematic diagram comparing the performance of different embodiments and comparative examples. Detailed Implementation

[0023] To make the objectives, technical solutions, and advantages of this invention clearer, the invention will be further described in detail below with reference to the accompanying drawings and embodiments. It should be understood that the specific embodiments described herein are merely illustrative and not intended to limit the invention.

[0024] The technical concept of this invention is based on the following theoretical understanding: deformation control, by influencing the fragmentation, refinement, and redistribution of the ferrous phase, determines the dispersion degree and interface characteristics of the strengthening phase. Studies have shown that the combined effects of deformation strengthening, grain refinement strengthening, and multi-scale synergistic precipitation strengthening of micron-, submicron-, and nano-scale Fe phases can significantly improve the strength and electrical conductivity of Cu-Fe alloys. Based on this, this invention introduces rare earth elements to further enhance the synergistic effect of the aforementioned multiple strengthening mechanisms.

[0025] Figure 1 Microstructure of 0.1 mm Cu-15Fe-Re alloy strips with different rare earth contents; (a) rare earth content 0.2%, (b) rare earth content 0.5%, (c) rare earth content 0.8%, (d) rare earth content 1.0%.

[0026] The rare earth copper alloys (Cu-La), (Cu-Ce), or (Cu-Y) described in this application are all commercially available rare earth copper master alloys, wherein the rare earth elements, lanthanum, cerium, or yttrium, constitute 10% to 20% by mass, with the balance being copper and unavoidable impurities. Selecting master alloys within this composition range ensures uniform dispersion of rare earth elements during smelting, avoiding localized enrichment; furthermore, master alloys within this composition range have a moderate melting point (approximately 900–1000 °C) and good metallurgical compatibility with the copper matrix, which is beneficial for improving rare earth yield.

[0027] Reference Figures 1-2 A Cu-Fe-Re alloy based on controlled deformation, wherein the alloy composition by weight percentage includes: 10%~20% iron, 0.2%~1.0% rare earth elements, and the balance being copper and unavoidable impurities; the rare earth elements are selected from one or more of cerium, lanthanum, and yttrium.

[0028] By controlling the amount of deformation, the iron phase in the microstructure of the alloy is uniformly distributed in a fibrous manner, thereby achieving synergistic optimization of mechanical and electrical properties.

[0029] The content of rare earth elements is 0.5%~0.8%.

[0030] The alloy has a tensile strength ≥550MPa and an electrical conductivity ≥56%IACS.

[0031] In the microstructure of the alloy, the iron phase is uniformly distributed in a fibrous manner, with reduced interphase spacing and a dense distribution.

[0032] A method for preparing Cu-Fe-Re alloy based on controlled deformation includes the following steps: Step 1: Take iron with a purity ≥99.96%, copper with a purity ≥99.9%, and rare earth copper alloy according to the design, place them in a vacuum high-frequency induction furnace, and melt them at 1150~1200℃ under an argon atmosphere to obtain the alloy melt. Step 2: The melt is cast into a solid shape at a casting temperature of 1100~1150℃ to obtain a copper alloy ingot. Step 3: Homogenize the ingot at 900~1000℃ for 3~5 hours, and then remove surface defects; Step 4: Hot forge the homogenized ingot at 900~950℃ into a thick bar with a thickness of 8mm. Step 5: The hot-forged bar is subjected to multiple cold rolling passes to obtain strip.

[0033] In step one, the pressure of the argon atmosphere is 0.06~0.08MPa.

[0034] The thickness of the strip after multiple cold rolling passes in step five is 1 mm, 0.8 mm, 0.5 mm or 0.1 mm.

[0035] In step five, the deformation control of multi-pass cold rolling causes the iron phase in the strip to change from dendritic to droplet-like, and further evolve into fibrous structure.

[0036] The present invention will be further illustrated by the following embodiments: Example 1; This embodiment provides a method for preparing Cu-15Fe-Re alloy, and the specific steps are as follows: Step 1, Raw material preparation: 100kg of 99.99% pure electrolytic copper, 18.4kg of 99.96% pure iron, and 2.54kg of rare earth copper alloy (Cu-Y, containing 15% yttrium), with the total amount of rare earth elements controlled at around 0.5%. Calculations show that 2.54 kg × 15% ÷ (100 + 18.4 + 2.54) kg ≈ 0.5%. Choosing Cu-Y master alloy as the rare earth source has the following advantages: Yttrium has high chemical activity, effectively purifying impurities such as oxygen and sulfur in copper-iron alloy melts; simultaneously, the compounds formed by yttrium with iron and copper have high thermal stability, which is beneficial for maintaining the dispersed distribution of the second phase during subsequent deformation.

[0037] Step 2, smelting: Electrolytic copper is added to a vacuum high-frequency induction furnace and heated to 1150~1200℃. After the copper is completely melted, pure iron and rare earth copper alloy are added and stirred evenly under an argon atmosphere (0.06~0.08MPa) to obtain the alloy melt. The key to this smelting process is that vacuum and argon protection can effectively prevent the oxidation and burning of rare earth elements, ensuring the rare earth yield; the smelting temperature of 1150~1200℃ ensures that all components are fully melted, while avoiding element volatilization and furnace lining erosion caused by excessively high temperatures.

[0038] Step 3, casting: The molten material is introduced into the mold through the runner, and the casting temperature is controlled at 1100~1150℃ to make an ingot with a diameter of 20mm. The selection of this casting temperature helps to obtain an ingot with uniform structure and small compositional segregation, which provides a good microstructure basis for subsequent deformation treatment.

[0039] Step 4, homogenization treatment: The ingot is kept at 950℃ for 3 hours for homogenization treatment, and then the surface oxide scale and defects are removed. The purpose of homogenization treatment is to eliminate dendritic segregation inside the ingot, so that the iron phase and rare earth elements are evenly distributed in the matrix, while reducing the internal stress of the ingot and improving the hot working performance.

[0040] Step 5, hot forging: The treated ingot is hot forged at 900℃ into a thick bar with a thickness of 8mm. The choice of hot forging temperature takes into account both the high-temperature plasticity and microstructure stability of the alloy. Hot forging at 900℃ can cause the iron phase to undergo initial fragmentation, laying the foundation for subsequent cold rolling refinement.

[0041] Step Six, Cold Rolling: The hot-forged bar is cold-rolled in multiple passes to obtain strips with thicknesses of 1mm, 0.8mm, 0.5mm, and 0.1mm, respectively, corresponding to different cumulative deformation amounts. The cold rolling process achieves precise control of the deformation amount by accurately controlling the reduction in each pass.

[0042] Beneficial effects and technical significance of Example 1: The Cu-15Fe-Re alloy strip prepared by the above method exhibits a tensile strength ≥580MPa and an electrical conductivity ≥60%IACS at a thickness of 0.1mm. The iron phase is uniformly distributed in a fibrous pattern, resulting in a dense microstructure. This example fully demonstrates that under the condition of 0.5% rare earth addition, by controlling the deformation amount (cold rolling to 0.1mm), sufficient refinement and uniform distribution of the iron phase can be achieved, enabling the alloy to achieve significantly improved tensile strength while maintaining high electrical conductivity. The process parameters selected in this example are typical and repeatable, providing clear technical guidance for those skilled in the art.

[0043] Example 2; The difference between this embodiment and Embodiment 1 is that the rare earth copper alloy used is Cu-La (copper-lanthanum master alloy containing 10%~20% lanthanum), the rare earth addition is controlled at 0.2%, and the other process parameters are the same as in Embodiment 1.

[0044] The beneficial effects and technical significance of Example 2: According to the test, the 0.1 mm thick strip prepared in this embodiment has a tensile strength of 520 MPa and a conductivity of 62% IACS. Compared with Example 1, the tensile strength is slightly lower when the rare earth content is lower, but the conductivity is slightly higher. This embodiment demonstrates that even when the rare earth content is at the lower limit of the scope of this invention (0.2%), it is still possible to obtain better overall performance than the comparative example without rare earth, verifying that rare earth elements still have significant grain boundary purification and microstructure refinement effects at an addition amount of 0.2%.

[0045] Example 3; The difference between this embodiment and Embodiment 1 is that the rare earth copper alloy used is Cu-Ce (copper-cerium master alloy, containing 15% cerium), the rare earth addition is controlled at 0.8%, and the addition amount is adjusted to about 3.8 kg. The other process parameters are the same as in Embodiment 1.

[0046] Beneficial effects and technical significance of Example 3: Tests showed that the 0.1 mm thick strip prepared in this embodiment had a tensile strength of 610 MPa and a conductivity of 58% IACS. Compared with Example 1, when the rare earth content was increased to 0.8%, the tensile strength was further improved, and the conductivity decreased slightly but was still within an acceptable range. This embodiment demonstrates that appropriately increasing the rare earth content can further refine the microstructure and enhance the strengthening effect of the second phase, which is an effective way to obtain high-strength alloys.

[0047] Example 4; The difference between this embodiment and Embodiment 1 is that the rare earth copper alloy uses a mixture of Cu-Y, Cu-La, and Cu-Ce, each accounting for 1 / 3, with a total rare earth content of 15%, and the total rare earth addition is controlled at 1.0% (accounting for 1.0% of the total weight of the alloy). The addition amount is adjusted to about 4.75 kg, and the remaining process parameters are the same as in Embodiment 1.

[0048] Beneficial effects and technical significance of Example 4: Testing showed that the 0.1 mm thick strip prepared in this embodiment had a tensile strength of 620 MPa and a conductivity of 56% IACS. This embodiment demonstrates that when the rare earth content reaches the upper limit of the scope of this invention (1.0%), the alloy's tensile strength reaches its maximum value, but the conductivity decreases accordingly. The use of mixed rare earth elements can leverage the synergistic effects of different rare earth elements, such as yttrium's strong deoxidizing ability, lanthanum's grain-refining effect, and cerium's grain boundary purification effect, thereby comprehensively optimizing the alloy microstructure.

[0049] Comparative Example 1; The difference between this comparative example and Example 1 is that no rare earth elements are added, while the other process parameters are the same as in Example 1.

[0050] The beneficial effects and technical significance of Comparative Example 1: Testing showed that the 0.1 mm thick strip prepared in this comparative example had a tensile strength of 480 MPa and a conductivity of 52% IACS. Compared with Examples 1 to 4, the alloy without rare earth elements exhibited significantly lower tensile strength and conductivity under the same deformation conditions, and the iron phase in the microstructure was coarse-grained and unevenly distributed. This comparative example, from the opposite perspective, verifies the crucial role of rare earth elements in purifying the matrix, refining the microstructure, and improving the distribution of the second phase, proving that rare earth addition is an indispensable component of the technical solution of this invention.

[0051] Comparative Example 2; The difference between this comparative example and Example 1 is that it is not cold-rolled after hot forging, i.e., it maintains an 8mm thickness. The other process parameters are the same as those in Example 1.

[0052] The beneficial effects and technical significance of Comparative Example 2: Testing revealed that the 8mm thick rod prepared in this comparative example had a tensile strength of only 350MPa and a conductivity of 70% IACS. Although the conductivity was relatively high, the tensile strength was far lower than that of Examples 1 to 4, failing to meet the mechanical performance requirements of the structural components. The iron phase in the microstructure is coarse and blocky, and unevenly distributed. This comparative example verifies from the opposite perspective the decisive influence of deformation amount control on the mechanical properties of the alloy, proving that multi-pass cold rolling deformation in this invention is a key process step for achieving synergistic optimization of strength and conductivity.

[0053] A comprehensive comparative analysis of the examples and comparative examples; By comparing and analyzing the performance data of the above embodiments and comparative examples, the following conclusions can be drawn: Taking Example 1 as an example, the effect of deformation on performance: as the strip thickness decreases from 1.0 mm to 0.1 mm, i.e. the deformation increases, the tensile strength increases from 420 MPa to 580 MPa, an increase of approximately 38%; The conductivity decreased from 68% IACS to 60% IACS, a drop of approximately 12%, but remained at a high level. The morphology of the iron phase gradually evolved from droplet-like to fibrous, and the microstructure changed from relatively uniform distribution to highly dense. This indicates that, based on the addition of rare earth elements, an optimal balance between strength and conductivity can be achieved by precisely controlling the deformation amount.

[0054] The effect of rare earth content on performance, taking a thickness of 0.1 mm as an example: when the rare earth content increases from 0.2% to 0.8%, the tensile strength increases from 520 MPa to 610 MPa, while the conductivity decreases from 62% IACS to 58% IACS; when the rare earth content further increases to 1.0%, the tensile strength slightly increases to 620 MPa, but the conductivity decreases to 56% IACS. The optimal range for overall performance is a rare earth content of 0.5% to 0.8%. Within this range, the alloy achieves significantly improved tensile strength while maintaining high conductivity, fully demonstrating the synergistic optimization effect of rare earth addition and deformation control.

[0055] Comparison of Examples and Comparative Examples: In Comparative Example 1, the tensile strength and conductivity of the sample without rare earth elements were lower than those of the examples, proving that the addition of rare earth elements plays an irreplaceable role in microstructure optimization and performance improvement. Comparative Example 2 shows that the tensile strength of the material without cold rolling deformation is significantly insufficient, proving that deformation control is a key process step in achieving alloy strengthening. Example 1, with 0.5% rare earth and 0.1mm strip, achieved a good match between 580MPa tensile strength and 60% IACS conductivity, with overall performance significantly better than the two comparative examples.

[0056] The preparation method of this invention can be carried out under conventional industrial plant conditions. To ensure process stability and product consistency, and to ensure that those skilled in the art can reproduce the technical solution of this invention without creative effort, it is recommended to operate under the following environmental conditions: 1. Smelting process (Step 1); The melting process takes place in a vacuum high-frequency induction furnace, with argon gas introduced as a protective atmosphere at a pressure of 0.06~0.08MPa. Since the furnace interior is isolated from the external environment, the temperature and humidity of the external environment have no significant impact on the melting process. The vacuum system can effectively remove moisture from the furnace, and argon gas is a dry and inert gas. Therefore, this process does not require special control of the ambient temperature and humidity.

[0057] 2. Casting process (step two); The casting temperature is 1100~1150℃. Metal molds are used. To avoid casting defects such as component segregation and shrinkage cavities caused by the melt cooling too quickly due to the mold temperature being too low, the metal mold should be preheated to 200~300℃ before casting. At the same time, if the ambient humidity is too high, water vapor may condense on the mold surface. During casting, the water vapor will quickly vaporize and may cause defects such as porosity and inclusions on the surface of the ingot. Therefore, the casting area should be kept dry. It is recommended that the relative humidity be ≤65%, and the mold should be thoroughly dried before casting.

[0058] 3. Homogenization process (step three); The homogenization process is carried out in a closed heat treatment furnace. The furnace temperature is precisely regulated by the control system. The influence of ambient temperature on the furnace temperature is negligible. This process is not sensitive to ambient temperature and humidity and requires no special control.

[0059] 4. Hot forging process (step four); The hot forging temperature is 900~950℃. The billet is forged after being removed from the heating furnace. If the ambient temperature is too low (such as in winter), the billet cools down faster, which may shorten the forgeable time window. To ensure hot working plasticity, it is recommended to appropriately shorten the transfer time of the billet from the heating furnace to the forging equipment. If necessary, the upper limit of the heating temperature can be appropriately increased to 950℃. Humidity has a limited impact on the hot forging process and does not require special control.

[0060] 5. Cold rolling process (step five); Cold rolling is carried out at room temperature using a multi-pass rolling process. Low ambient temperatures (e.g., below 15°C) may reduce material plasticity and increase the risk of edge cracking, especially during rolling with large deformations, such as when rolling to a thickness of 0.1 mm. Excessive ambient humidity can cause moisture to adsorb onto the strip surface, affecting rolling lubrication and potentially leading to surface corrosion. Therefore, it is recommended that the cold rolling process be carried out at an ambient temperature of 15-30℃ and a relative humidity of ≤65%. After rolling, the strip should be dried and packaged promptly to prevent surface oxidation or corrosion.

[0061] Those skilled in the art, based on the above guidance and considering the actual conditions of the production site, such as seasonal changes and regional differences, can achieve stable reproduction of the technical solution of this invention without creative effort through conventional process adjustments, such as mold preheating, controlling transfer time, and regulating workshop temperature and humidity. The aforementioned environmental control conditions are all conventional technical means in the field and do not affect the sufficiency of the disclosure of the technical solution of this invention.

[0062] The mold preheating temperature (200~300℃) and casting temperature (1100~1150℃) settings in the above environmental control conditions are consistent with the conventional parameter ranges in existing copper alloy preparation processes and are common knowledge to those skilled in the art. The selection of vacuum melting equipment and the use of argon as a protective atmosphere are also conventional technical means in copper alloy melting. Therefore, under the above guidance and in conjunction with the actual conditions of the production site, those skilled in the art can stably reproduce the technical solution of this invention without creative effort.

[0063] The foregoing has shown and described the basic principles, main features, and advantages of the present invention. Those skilled in the art should understand that the present invention is not limited to the above embodiments. The embodiments and descriptions in the specification are merely principles of the invention. Various changes and modifications can be made to the invention without departing from its spirit and scope, and all such changes and modifications fall within the scope of the claimed invention. The scope of protection claimed by the appended claims and their equivalents is defined.

Claims

1. A Cu-Fe-Re alloy based on controlled deformation, characterized in that, The alloy composition, by weight percentage, includes: 10%~20% iron, 0.2%~1.0% rare earth elements, and the balance being copper and unavoidable impurities; The rare earth element is selected from one or more of cerium, lanthanum, and yttrium.

2. The Cu-Fe-Re alloy based on controlled deformation according to claim 1, characterized in that, The iron phase in the microstructure of the alloy is uniformly distributed in a fibrous manner, thereby achieving synergistic optimization of mechanical and electrical properties.

3. The Cu-Fe-Re alloy based on controlled deformation according to claim 1, characterized in that, The content of rare earth elements is 0.5% to 0.8%.

4. The Cu-Fe-Re alloy based on controlled deformation according to claim 1, characterized in that, The alloy has a tensile strength ≥550MPa and a conductivity ≥56%IACS.

5. A Cu-Fe-Re alloy based on controlled deformation according to claim 1, characterized in that, In the microstructure of the alloy, the iron phase is uniformly distributed in a fibrous manner, with reduced gaps between the iron phases and a dense distribution.

6. The method for preparing Cu-Fe-Re alloy according to any one of claims 1-5, characterized in that, Includes the following steps: Step 1: Take iron with a purity ≥99.96%, copper with a purity ≥99.9%, and rare earth copper alloy according to the design, place them in a vacuum high-frequency induction furnace, and melt them at 1150~1200℃ under an argon atmosphere to obtain the alloy melt. Step 2: The melt is cast into a solid shape at a casting temperature of 1100~1150℃ to obtain a copper alloy ingot. Step 3: Homogenize the ingot at 900~1000℃ for 3~5 hours, and then remove surface defects; Step 4: Hot forge the homogenized ingot at 900~950℃ into a thick bar with a thickness of 8mm. Step 5: The hot-forged bar is subjected to multiple cold rolling passes to obtain strip.

7. The method for preparing Cu-Fe-Re alloy based on controlled deformation according to claim 6, characterized in that, The pressure of the argon atmosphere in step one is 0.06~0.08MPa.

8. The method for preparing Cu-Fe-Re alloy based on controlled deformation according to claim 6, characterized in that, The thickness of the strip after multiple cold rolling processes in step five is 1 mm, 0.8 mm, 0.5 mm, or 0.1 mm.

9. The method for preparing Cu-Fe-Re alloy based on controlled deformation according to claim 6, characterized in that, The deformation control of the multi-pass cold rolling in step five causes the iron phase in the strip to change from dendritic to droplet-like, and further evolve into fibrous structure.

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