Copper-iron alloy material with high saturation magnetization as well as preparation method and application of copper-iron alloy material

Abstract

The invention discloses a high-saturation magnetization copper-iron alloy material and a preparation method and application thereof, and belongs to the technical field of copper-iron alloys. The invention relates to a copper-iron alloy material with high saturation magnetization, which comprises the following components in percentage by weight: 15-30% of Fe and the balance of Cu and inevitable impurities. According to the preparation method, an equal-channel angular pressing (ECAP) preprocessing and multi-stage variable-temperature rotary swaging synergistic composite machining system is adopted, and the alloy strength, the electric conductivity and the saturation magnetization are synchronously improved within short-time machining. The saturation magnetization of the prepared Cu-Fe alloy can reach 70 emu / g or above, meanwhile, the Cu-Fe alloy has good strength and conductivity, the experimental scheme is simple and easy to operate, the sizes of power electronic components can be effectively reduced through the advantages, the stability of the power electronic components in the working process is improved, and the development requirement of the power and electrical industry is met.

Description

Technical Field

[0001] The invention relates to a copper-iron alloy material with high saturation magnetization intensity and a preparation method and application thereof, belonging to the technical field of copper-iron alloys. Background Art

[0002] With the rapid development of power, electrical and microwave communication technologies, advanced systems have put forward higher requirements for device miniaturization, integration and stability. Driving materials need to meet the comprehensive performance requirements of high strength, high conductivity and high saturation magnetization. Copper is widely used in key fields such as high-voltage wires, integrated circuit lead frames, pulse magnet conductors and high-speed rail contact lines due to its excellent electrical conductivity, thermal conductivity and processing performance. It also occupies an important position in electromagnetic shielding applications. However, pure copper has low strength, and as a diamagnetic material, its inherent zero saturation magnetization characteristics seriously restrict its application in dynamic electromagnetic field environments. Copper-iron alloys show great application potential by synergizing the electrical / thermal conductivity of the copper matrix with the high strength and high saturation magnetization of the iron phase. It has become a new generation of electromagnetic shielding conductor candidate materials that have attracted much attention in the fields of power transmission, communication base stations and rail transportation.

[0003] Current research on copper-iron alloys mainly focuses on the coordinated optimization of strength and conductivity, but as electromagnetic functional materials, magnetic property regulation is also crucial. High saturation magnetization can effectively suppress the flux attenuation and eddy current heating when the device is working, ensuring long-term operational stability. Although the traditional cold rolling / cold drawing process can improve the strength, it is difficult to achieve the dispersion precipitation of the Fe phase, resulting in limited improvement in magnetic properties. Existing technologies mostly rely on long-term aging heat treatment to promote the diffusion and precipitation of Fe atoms. However, there are two major defects: on the one hand, long-term aging will destroy the strength of the alloy and some nano-precipitated phases are FCC-structured γ-Fe, whose saturation magnetization is significantly lower than that of BCC-structured α-Fe; on the other hand, the extended production cycle leads to a significant increase in energy consumption and cost. Therefore, there is an urgent industrial need to develop a short-process, low-cost copper-iron alloy preparation technology that combines high strength, high conductivity and ultra-high saturation magnetization.

[0004] The mainstream of the industry adopts the in-situ composite method of deformation to prepare high-strength and high-conductivity copper-iron alloys, that is, the Fe phase is fiberized by large-strain drawing / rolling, and the performance is adjusted by annealing. However, the magnetic property regulation mechanism has not been introduced, and the saturation magnetization intensity of the alloy has received little attention. How to improve the saturation magnetization intensity of copper-iron alloys while maintaining good strength and conductivity is a technical bottleneck that needs to be overcome urgently. Summary of the invention

[0005] To solve the above problems, the object of the present invention is to provide a copper-iron alloy material with high saturation magnetization intensity, which can improve the saturation magnetization intensity of the copper-iron alloy while maintaining good strength and conductivity, and is suitable for electromagnetic shielding materials and power electrical components such as PCB circuit boards, sensors, and inductors with miniaturization, high integration, and high stability.

[0006] Meanwhile, the present invention provides a preparation method for the copper-iron alloy material with high saturation magnetization intensity.

[0007] Meanwhile, the present invention provides an application of the copper-iron alloy material with high saturation magnetization intensity.

[0008] To solve the above technical problems, the technical solution adopted by the present invention is as follows:

[0009] A copper-iron alloy material with high saturation magnetization intensity, specifically a Cu-Fe alloy material with a combination of high saturation magnetization intensity, good strength, and conductivity, wherein the Fe content is 15-30 wt.%, and the balance is Cu and inevitable impurities. The introduction of the Fe phase endows the material with better saturation magnetization intensity, making the material transform into a paramagnetic material and exhibit typical soft magnetic material characteristics.

[0010] A preparation method for the copper-iron alloy material with high saturation magnetization intensity, specifically the preparation method for the copper-iron alloy material with high saturation magnetization intensity and good strength and conductivity mentioned above, includes the following steps:

[0011] Step 1: The composition of the copper-iron alloy is Cu-XFe. The raw material metals are proportioned according to the ratio, and the Fe content is 15-30 wt.%, and the balance is Cu and inevitable impurities;

[0012] Step 2: Put the raw materials into a ceramic crucible, evacuate to below 10 -1 Pa, introduce argon to atmospheric pressure and then heat and melt; preferably, the ceramic crucible is pre-baked and pre-heated; after introducing argon to atmospheric pressure, evacuate to below 10 -1 Pa and start heating and melting (this step is mainly to ensure that there is no oxygen during melting, or it can be directly simplified to only evacuate);

[0013] Step 3: Remelt the material 3-5 times to ensure the uniformity of the melt, then heat it to 30-50 K above the liquidus and hold for 3-5 min before casting to obtain an ingot;

[0014] Step 4: Perform homogenization treatment on the ingot. After raising the temperature of the muffle furnace to 700-950 °C, put the ingot in, hold for 120-300 min and then take it out and quench it with water to obtain a homogenized alloy ingot;

[0015] Step 5: Subject the homogenized alloy ingot to rotary die equal-channel angular pressing and variable-temperature rotary forging deformation at 300°C to 550°C. The process is as follows:

[0016] S01, Equal-channel angular pressing: After grinding the homogenized alloy ingot to remove oxide scales and burrs, perform continuous equal-channel angular pressing at 300°C to 550°C, with an angle of 90° to 120°, an extrusion path of Ba, and 1 - 8 extrusion passes. Then quench it with water to obtain an extruded specimen.

[0017] S02, Variable-temperature rotary forging: Cut the specimen after rotary die equal-channel angular pressing using a wire electrical discharge machine to remove edge defects and grind to remove oxide scales and burrs. Then perform rotary forging at temperatures of 800°C to 950°C, 300°C to 550°C, and room temperature respectively. The single-pass reduction is 0.1 mm to 0.5 mm. The strain for rotary forging at 800°C to 950°C is 0.1 to 0.2; the strain for rotary forging at 300°C to 550°C is 0.2 to 0.3; the strain for rotary forging at room temperature is 0.7 to 1.0; the cumulative rotary forging strain is 1.0 - 1.5 to obtain an extruded + rotary forged specimen.

[0018] As a preferred technical solution of the present invention, in Step 1, the purity of Cu and Fe is not less than 99.99 wt.%.

[0019] As a preferred technical solution of the present invention, in Step 2, the heating and melting is carried out using an intermediate frequency induction furnace to heat to 1350 - 1550°C for melting.

[0020] As a preferred technical solution of the present invention, in Step 5, during the rotary die equal-channel angular pressing process, the extrusion temperature is 300°C to 550°C, and the sample is insulated every 4 passes. The sample insulation time is 5 - 30 min.

[0021] As a preferred technical solution of the present invention, in Step 5, the rotary forging temperatures are 800°C to 950°C, 300°C to 550°C, and room temperature respectively, and the cumulative rotary forging strain is 1.5.

[0022] As a preferred technical solution of the present invention, the high saturation magnetization Cu-Fe alloy material obtained by any of the methods described above has a saturation magnetization greater than 35emu / g. The rotary die equal channel angular hot extrusion not only increases the dislocation density in the Cu matrix, provides a point for the precipitation of Fe atoms, and the higher temperature also provides a driving force for the diffusion and precipitation of Fe atoms. In addition, the higher extrusion temperature causes the Cu supersaturated solid solution to undergo spinodal decomposition, so that the Fe atoms precipitate as a γ-Fe phase with an FCC structure. On this basis, the subsequent variable temperature rotary forging deformation further causes the precipitation of Fe atoms and the elongation of the Fe phase, and promotes the phase transformation of the γ-Fe phase into the α-Fe phase with a BCC structure, and finally obtains a slender α-Fe phase that is parallelly distributed in a fibrous shape along the axial direction, thereby achieving a simultaneous improvement in material strength, electrical conductivity, and saturation magnetization.

[0023] At the same time, the present invention provides an application of a Cu-Fe alloy material with high saturation magnetization, good strength and conductivity, specifically, it is applied to electromagnetic shielding materials and miniaturized, highly integrated, and highly stable power electrical components such as PCB circuit boards, sensors, and inductors.

[0024] The invention discloses an application of a copper-iron alloy material with high saturation magnetization intensity in electric power components and electromagnetic shielding materials.

[0025] Power electrical components and electromagnetic shielding materials include electromagnetic compatibility components, lead frames for integrated circuits, and pulse magnet conductor materials.

[0026] An electric power component and an electromagnetic shielding material are prepared from a copper-iron alloy material with high saturation magnetization intensity according to the present invention.

[0027] The present invention is beneficial in that:

[0028] In the variable temperature rotary forging process of the present invention, the purpose of high temperature (800°C-950°C) is to accelerate atomic diffusion, improve the plastic deformation ability of the alloy to quickly elongate the rod and decompose the supersaturated Cu solid solution; the purpose of medium temperature (300°C-550°C) is to reduce the solid solubility of Fe in Cu, further promote the precipitation of Fe atoms and release lattice distortion energy, avoid recrystallization of copper grains due to room temperature deformation, thereby improving the electrical conductivity of the alloy; the purpose of low temperature (room temperature) is to further elongate and refine the Fe phase and Cu matrix structure and increase the dislocation density to improve the strength of the alloy.

[0029] In view of the industry problem that traditional Cu-Fe alloys have low saturation magnetization and limited electromagnetic stability due to the slow precipitation kinetics of Fe phase, the core innovation of the present invention lies in the construction of a composite processing system that coordinates equal channel angular pressing (ECAP) pre-processing and multi-stage variable temperature rotary forging, so as to achieve the simultaneous improvement of alloy strength, conductivity and saturation magnetization in a short time. The invention uses high-temperature rotary die ECAP to achieve dual-path coordinated precipitation of Fe phase: on the one hand, a nucleated and grown α-Fe phase is formed at the grain boundary, and on the other hand, a dispersed γ-Fe phase is formed in the Cu matrix through amplitude modulation decomposition. On this basis, through a multi-stage variable temperature rotary forging process, the temperature-stress synergy is utilized to enhance the diffusion and precipitation behavior of Fe atoms and trigger the transformation of the γ-Fe phase of FCC structure into the α-Fe phase of BCC structure, and simultaneously realize the nano-elongation and dispersion optimization of Fe phase, and finally obtain a Cu-Fe alloy material with high strength, high conductivity and ultra-high saturation magnetization. The present invention breaks through the limitations of traditional processes and innovatively matches the parameters of ECAP and rotary forging to simultaneously solve the three major technical problems of slow Fe phase precipitation kinetics, uneven distribution and poor structural stability. The performance of the resulting Cu-15Fe alloy material is significantly improved, with a saturation magnetization of 74emu / g (nearly double that of traditional processes), a tensile strength of 654MPa, and a conductivity of 65%IACS. This process does not require long-term aging heat treatment, significantly shortens the processing cycle, and realizes precise distribution control of the α / γ-Fe phase, providing a new idea for the development of high-performance electromagnetic shielding materials.

[0030] The saturation magnetization intensity of the Cu-Fe alloy prepared by the present invention can reach more than 70emu / g, and it has good strength and conductivity, and the experimental scheme is simple and easy to operate. These advantages can effectively reduce the size of power electronic components and improve their stability during operation, meeting the development needs of the power and electrical industry. BRIEF DESCRIPTION OF THE DRAWINGS

[0031] Figure 1 It is a process flow chart of the present invention;

[0032] Figure 2 It is the mechanism diagram of temperature-variable rotary forging in the present invention;

[0033] Figure 3 It is the strength, conductivity and saturation magnetization of the alloy after being treated by different processes in the present invention. DETAILED DESCRIPTION

[0034] The present invention will be further described in detail below in conjunction with the accompanying drawings and specific embodiments. The following embodiments are only used to illustrate the present invention and are not intended to limit the scope of the present invention.

[0035] Example 1

[0036] like Figures 1 to 2As shown, a preparation method of a copper-iron alloy material with high saturation magnetization, that is, a preparation method of a high-strength, high-conductivity and high-saturation magnetization copper-iron alloy material, includes the following steps:

[0037] Step 1: The copper-iron alloy composition is Cu-Fe. The raw material metals are proportioned according to the ratio. The content of Fe is 15 wt.%, and the balance is Cu and inevitable impurities; the purity of both Cu and Fe is not less than 99.99 wt.%.

[0038] Step 2: Put the raw materials Cu and Fe into a ceramic crucible, evacuate to below 10 -1 Pa, then introduce argon to normal pressure, and heat to 1350 °C for melting using an intermediate frequency induction furnace.

[0039] Step 3: Remelt the material 4 times to ensure the melt is uniform, then heat to 40 K above the liquidus and hold for 3 min before casting to obtain an ingot.

[0040] Step 4: Perform homogenization treatment on the ingot. After raising the temperature of the muffle furnace to 900 °C, put the ingot in, hold for 120 min and then take it out and quench it with water to eliminate the macroscopic segregation of elements in the as-cast structure and obtain a homogenized alloy ingot.

[0041] Step 5: Apply rotary die equal-channel angular pressing and variable-temperature rotary forging deformation to the homogenized alloy ingot. The process is as follows:

[0042] S01, Equal-channel angular pressing: Grind the homogenized alloy ingot to remove the oxide scale and burrs, then perform continuous equal-channel angular pressing at 550 °C, the angle is 90°, the number of pressing passes is 8, keep the sample warm every 4 passes, the sample holding time is 5 min, and then quench it with water to obtain an extruded sample.

[0043] S02, Variable-temperature rotary forging: Cut the sample after rotary die equal-channel angular pressing using a wire electrical discharge machine to remove the edge defects and grind to remove the oxide scale and burrs, then perform rotary forging at 900 °C, 550 °C and room temperature respectively. The rotary forging strains are 0.2, 0.3 and 1.0 respectively, and the cumulative rotary forging strain is 1.5 to obtain an extruded + rotary forged sample, that is, the 8P+RS-1.5 sample as shown in Figure 3 the figure.

[0044] Application of a Cu-Fe alloy material with high saturation magnetization, good strength and conductivity combination in electrical and electronic components and electromagnetic shielding materials.

[0045] Electrical and electronic components and electromagnetic shielding materials include high-voltage electric wires, lead frames for integrated circuits, pulse magnet conductor materials, catenary wires for electrified high-speed railways, and electromagnetic shielding materials.

[0046] A power electrical component and an electromagnetic shielding material, comprising a Cu-Fe alloy material with a high saturation magnetization intensity, good strength, and conductivity combination in this embodiment.

[0047] In this embodiment, the power electrical component and the electromagnetic shielding material are materials with high strength, high conductivity, and high saturation magnetization intensity.

[0048] Using this solution to prepare a copper-iron alloy can obtain an extremely high saturation magnetization intensity while ensuring a good combination of strength and conductivity, as Figure 3 shown. When only conventional room-temperature rolling (R85%) is performed on the sample, the strength and saturation magnetization intensity of the alloy increase, but the conductivity decreases, and the saturation magnetization intensity is not excellent. When the sample is extruded 8 times, its strength, conductivity, and saturation magnetization intensity all increase to a certain extent, but the increase amplitude is small. After the channel angular extrusion state material such as rotary die is subjected to variable-temperature rotary forging, the strength and conductivity of the material can be improved simultaneously, and an extremely high saturation magnetization intensity is exhibited. After being treated by the composite process, the strength, conductivity, and saturation magnetization intensity of the alloy are 654 MPa, 65% IACS, and 74 emu / g respectively.

[0049] The strength and conductivity data of the high-strength and high-conductivity copper-iron alloys obtained in Examples 1 to 3 and Comparative Examples 1 to 5 of the present invention are shown in Table 1 below.

[0050] Table 1 Performance table of copper-iron alloys with high saturation magnetization intensity

[0051]

[0052]

[0053] The test method for strength is: the material strength is the tensile strength of the material. After the deformed specimen is processed into a dog-bone-shaped tensile specimen with a gauge length of 6 mm by a wire cutting machine, it is polished to remove oxidation products and burrs to ensure that the shape of the tensile specimen is uniform and stress concentration is avoided, and then a tensile test is performed to obtain its tensile strength, and the tensile speed is 0.36 mm / min.

[0054] The test method for conductivity is: the specimen is processed into a cylindrical specimen by a wire cutting machine, and its resistance is measured by a QJ36S DC resistance tester, and then it is converted into conductivity using the formula (1.7241*L) / (Rx*S)*100%, where L is the length of the measured specimen, Rx is the resistance measured of the specimen, and S is the cross-sectional area of the measured specimen.

[0055] The test method for saturation magnetization intensity is as follows: The specimen is processed into a sheet with dimensions of 2 * 2 * 2 mm using a wire cutting machine, and then its thickness is thinned to 0.1 μm using sandpaper and its weight is measured using a precision electronic balance. The saturation magnetization intensity of the specimen is measured using a Lake Shore-7407 vibrating sample magnetometer, and the temperature is maintained at 20 °C during the measurement.

[0056] Comparative Example 1

[0057] The difference between this comparative example and Example 1 is only that: In this comparative example, only the homogenized alloy ingot is obtained by adopting Steps 1 to 4, which is the HH specimen in Figure 3 .

[0058] Comparative Example 2

[0059] The difference between this comparative example and Example 1 is only that: After the homogenized alloy ingot is obtained by adopting Steps 1 to 4 in this comparative example, the specimen is obtained by adopting a conventional room temperature rolling process.

[0060] The conventional room temperature rolling process is as follows: After the homogenized alloy ingot is polished to remove the oxide scale and burrs, it is rolled at room temperature, and the rolling reduction is 85%, obtaining the R85% specimen in Figure 3 .

[0061] Comparative Example 3

[0062] The difference between this comparative example and Example 1 is only that: After the homogenized alloy ingot is obtained by adopting Steps 1 to 4 in this comparative example, only the equal-channel angular extrusion process in S01 is adopted to obtain the 8P specimen as shown in Figure 3 .

[0063] Comparative Example 4

[0064] The difference between this comparative example and Example 1 is only that: After the homogenized alloy ingot is obtained by adopting Steps 1 to 4 in this comparative example, only the variable-temperature rotary forging process in S02 is adopted to obtain the RS-1.5 specimen as shown in Figure 3 .

[0065] Comparative Example 5

[0066] The difference between this comparative example and Example 1 is only that: After the homogenized alloy ingot is obtained by adopting Steps 1 to 4 in this comparative example, after adopting the equal-channel angular extrusion process in S01, room temperature rolling is then carried out with a rolling reduction of 85% to obtain the 8P + R85% specimen in Figure 3 .

[0067] Example 2

[0068] A preparation method of a copper-iron alloy material with high saturation magnetization, namely a preparation method of a high-strength, high-conductivity and high-saturation magnetization copper-iron alloy material, includes the following steps:

[0069] Step 1: The copper-iron alloy composition is Cu-Fe. The raw material metals are proportioned according to the ratio. The content of Fe is 30wt.%, and the balance is Cu and inevitable impurities. The purity of both Cu and Fe is not less than 99.99wt.%.

[0070] Step 2: Put the raw materials Cu and Fe into a ceramic crucible. Vacuumize to below 10 -1 Pa, and after introducing argon to normal pressure, heat to 1550°C for melting using an intermediate frequency induction furnace.

[0071] Step 3: Remelt the material 3 times to ensure the melt is uniform. Then heat to 30K above the liquidus and hold for 5min before casting to obtain an ingot.

[0072] Step 4: Perform homogenization treatment on the ingot. After raising the temperature of the muffle furnace to 700°C, put the ingot in, hold for 300min and then take it out and quench it with water to eliminate the macroscopic segregation of elements in the as-cast structure and obtain a homogenized alloy ingot.

[0073] Step 5: Apply rotary die equal-channel angular pressing and variable-temperature rotary forging deformation to the homogenized alloy ingot. The process is as follows:

[0074] S01, Equal-channel angular pressing: Grind the homogenized alloy ingot to remove the oxide scale and burrs, and then perform continuous equal-channel angular pressing at 300°C, with an angle of 120°, 4 pressing passes. After pressing is completed, keep the sample warm for 30min, and then quench it with water to obtain an extruded sample.

[0075] S02, Variable-temperature rotary forging: Cut the sample after rotary die equal-channel angular pressing using a wire electrical discharge machine to remove the edge defects and grind to remove the oxide scale and burrs, and then perform rotary forging at 800°C, 300°C and room temperature respectively. The rotary forging strains are 0.1, 0.2 and 0.7 respectively, and the cumulative rotary forging strain is 1.0 to obtain an extruded + rotary forged sample.

[0076] Application of a Cu-Fe alloy material with high saturation magnetization, good strength and conductivity combination in power electrical components and electromagnetic shielding materials.

[0077] Power electrical components and electromagnetic shielding materials include high-voltage electric wires, lead frames for integrated circuits, pulse magnet conductor materials, catenaries for electrified high-speed railways, and electromagnetic shielding materials.

[0078] An electrical and electronic component and an electromagnetic shielding material, comprising a Cu-Fe alloy material with high saturation magnetization, good strength and conductivity combination of this embodiment.

[0079] Example 3

[0080] A preparation method of a copper-iron alloy material with high saturation magnetization, that is, a preparation method of a high-strength, high-conductivity and high-saturation magnetization copper-iron alloy material, comprising the following steps:

[0081] Step 1, the copper-iron alloy composition is Cu-Fe, the raw material metals are proportioned, the content of Fe is 20wt.%, and the balance is Cu and unavoidable impurities; the purity of Cu and Fe is not less than 99.99wt.%;

[0082] Step 2, put the raw materials Cu and Fe into a ceramic crucible, evacuate to below 10 -1 Pa, after introducing argon to normal pressure, heat to 1450 °C for melting by using an intermediate frequency induction furnace;

[0083] Step 3, remelt the material 5 times to ensure the melt is uniform, then heat to 50K above the liquidus and hold for 4 min before casting to obtain an ingot;

[0084] Step 4, homogenize the ingot. After raising the temperature of the muffle furnace to 950 °C, put the ingot in, take it out after holding for 200 min and quench it with water to eliminate the macroscopic segregation of elements in the as-cast structure and obtain a homogenized alloy ingot;

[0085] Step 5, apply rotary die equal-channel angular extrusion and variable-temperature rotary forging deformation to the homogenized alloy ingot. The process is as follows:

[0086] S01, equal-channel angular extrusion: Grind the homogenized alloy ingot to remove the oxide scale and burrs, then perform continuous equal-channel angular extrusion at 450 °C, the angle is 90°, the extrusion pass is 1, after extrusion, keep the sample warm, the sample holding time is 15 min, and then quench it with water to obtain an extruded sample,

[0087] S02, variable-temperature rotary forging: Cut the sample after rotary die equal-channel angular extrusion by using a wire electrical discharge machining cutter, remove the edge defects and grind to remove the oxide scale and burrs, then perform rotary forging at 950 °C, 450 °C and room temperature respectively, the rotary forging strains are 0.1, 0.3 and 0.8 respectively, and the cumulative rotary forging strain is 1.2 to obtain an extruded + rotary forged sample.

[0088] Application of a Cu-Fe alloy material with high saturation magnetization, good strength and conductivity combination in electrical and electronic components and electromagnetic shielding materials.

[0089] Power electrical components and electromagnetic shielding materials include high-voltage electric wires, lead frames for integrated circuits, pulse magnet conductor materials, catenaries for electrified high-speed railways, and electromagnetic shielding materials.

[0090] A power electrical component and an electromagnetic shielding material, comprising a Cu-Fe alloy material with high saturation magnetization intensity, good strength and conductivity combination in this embodiment.

[0091] Finally, it should be noted that the above embodiments are only for illustrating the technical concept and features of the present invention, and do not limit it. For different preparation methods, it can still be modified according to this technical solution, and the modified technical solution cannot deviate from the spirit of the technical solution of the present invention.

[0092] It should be understood that, in order to streamline the present disclosure and assist in understanding one or more of the various aspects of the invention, in the foregoing description of the exemplary embodiments of the invention, the various features of the invention are sometimes grouped together in a single embodiment, figure, or description thereof. However, the disclosed method should not be construed as reflecting an intention that the claimed invention requires more features than are expressly recited in each claim. Rather, as the claims reflect, the aspects of the invention lie in less than all of the features of the foregoing disclosed embodiments. Thus, the claims following the detailed description are hereby expressly incorporated into the detailed description, with each claim standing on its own as a separate embodiment of the invention.

[0093] Although the present invention has been described in terms of a limited number of embodiments, those skilled in the art within this technology field, having the benefit of the foregoing description, will appreciate that other embodiments can be contemplated within the scope of the invention as thus described. In addition, it should be noted that the language used in this specification has been principally selected for readability and instructional purposes, rather than to limit or define the subject matter of the invention. Accordingly, many modifications and variations will be apparent to those of ordinary skill in the art without departing from the scope and spirit of the appended claims. The disclosure of the present invention is illustrative, not restrictive, and the scope of the invention is defined by the appended claims.

[0094] The above are only the preferred embodiments of the present invention. It should be pointed out that for those of ordinary skill in the art, without departing from the principle of the present invention, several improvements and refinements can still be made, and these improvements and refinements should also be regarded as the protection scope of the present invention.

Claims

1. A copper-iron alloy material with high saturation magnetization intensity, characterized in that, The content of Fe is 15-30 wt.%, and the balance is Cu and inevitable impurities.

2. The preparation method of a copper-iron alloy material with high saturation magnetization intensity according to claim 1, characterized in that, The following steps are involved: Step 1, mixing raw materials Cu and Fe metals according to the proportion; Step 2: Put the raw materials into a ceramic crucible, evacuate to below 10 -1 Pa, and heat for melting; Step 3, remelting the material 3 to 5 times to ensure that the melt is uniform, then heating to 30 to 50 K above the liquidus and keeping it warm for 3 to 5 minutes before casting to obtain an ingot; Step 4, homogenizing the ingot, raising the temperature of the muffle furnace to 700-950° C., placing the ingot in the muffle furnace, keeping the temperature for 120-300 minutes, taking it out and quenching it with water to obtain a homogenized alloy ingot; Step 5: subjecting the homogenized alloy ingot to rotary die equal channel angular extrusion and temperature-variable rotary forging deformation, the process is as follows: S01, rotary die equal channel angular extrusion processing: after the homogenized alloy ingot is polished, it is subjected to continuous rotary die equal channel angular extrusion at 300℃~550℃, the die angle is 90°~120°, the extrusion pass is 1-8, and then it is quenched with water to obtain the extruded sample. S02, variable temperature rotary forging: after removing the oxide scale and burrs from the sample after rotary die equal channel angular extrusion, it is rotary forged at a gradient temperature with a rotary forging strain of 1.0 to 1.5 to obtain an extruded + rotary forged sample.

3. The preparation method according to claim 2, characterized in that, In step 1, the purity of Cu and Fe is not less than 99.99wt.%.

4. The preparation method according to claim 2, characterized in that, In step 2, heating and smelting are performed by heating to 1350-1550° C. in a medium frequency induction furnace.

5. The preparation method according to claim 2, wherein In S01, during the rotary die equal channel angular extrusion process, the sample was kept warm every 4 passes, and the sample keeping time was 5 to 30 min.

6. The preparation method according to claim 2, characterized in that, In S02, the gradient temperatures are 800℃~950℃, 300℃~550℃ and room temperature respectively; the strain of rotary forging at 800℃~950℃ is 0.1~0.2; the strain of rotary forging at 300℃~550℃ is 0.2~0.3; the strain of rotary forging at room temperature is 0.7~1.

0.

7. Application of the high saturation magnetization copper-iron alloy material according to claim 1 in power electrical components and electromagnetic shielding materials.

8. The application according to claim 7, characterized in that Power electrical components and electromagnetic shielding materials include electromagnetic compatibility components, lead frames for integrated circuits, and pulse magnet conductor materials.

9. An electric and electrical component and an electromagnetic shielding material, characterized in that It is prepared from the copper-iron alloy material with high saturation magnetization intensity as described in claim 1.

Images