Iron-based amorphous alloy ribbon with high tensile plasticity and work hardening capability and method of making

Abstract

The application discloses an iron-based amorphous alloy strip with large tensile plasticity and work hardening capacity and a preparation method thereof. T g ~0.9 T g The yield ratio of the obtained iron-based amorphous alloy strip is 0.6-0.9 in the temperature range of 0.65 T g ~0.9 T g The yield ratio of the obtained iron-based amorphous alloy strip is 0.6-0.9 in the temperature range of 0.65 T g ~0.9 T g The yield ratio of the obtained iron-based amorphous alloy strip is 0.6-0.9 in the temperature range of 0.65 The application significantly improves the tensile plasticity of the iron-based amorphous alloy strip through cold-heat cycle treatment, and the work hardening capacity of the obtained iron-based amorphous alloy strip is obviously improved, the yield ratio of the iron-based amorphous alloy strip is 0.6-0.9 in the temperature range of 0.65

Description

Technical Field

[0001] This invention belongs to the field of amorphous soft magnetic materials technology, specifically relating to iron-based amorphous alloy strips with both high tensile plasticity and work hardening ability, and their preparation method. Background Technology

[0002] Ferro-based amorphous alloys possess excellent soft magnetic properties such as high saturation magnetic induction, high initial permeability, and low mid-to-high frequency losses, leading to their widespread application in power electronics, information and communication, and new energy vehicles. They also hold potential applications in high-tech fields such as national defense and aerospace. However, ferro-based amorphous alloys generally lack macroscopic plastic deformation capabilities, limiting their machinability and affecting their stability during core manufacturing and use. Therefore, obtaining ferro-based amorphous soft magnetic alloys that combine excellent toughness and plasticity with comprehensive soft magnetic properties is of great value for practical applications, prompting researchers to conduct numerous studies in this area.

[0003] Patent CN104131243B discloses an annealed non-brittle iron-based amorphous alloy and its preparation method. This invention improves the annealing toughness of the iron-based amorphous alloy by adding Ni and M elements (M = Nb, V, Ta, Ti), so that the amorphous alloy strip does not break when folded after annealing. However, the addition of these elements will reduce the saturation magnetic induction intensity of the iron-based amorphous alloy.

[0004] Patent CN112553545B discloses a high-toughness, short-circuit-resistant iron-based amorphous soft magnetic alloy, its preparation method, and its application. This invention adds 0.05–1.5 at% of one or two elements from Dy, Er, and Yb to the raw material composition to prepare an amorphous soft magnetic alloy with both low loss and high toughness. The strip can be folded 180° without breaking, ensuring that the amorphous transformer does not break into fragments during a sudden short circuit. However, the addition of rare earth elements in this method leads to higher costs, and the strip toughness ε measured by the plate bending method is only about 14% higher than that of the comparative method, with limited improvement in strip plasticity.

[0005] Patent CN112725709A discloses a surface modification method to improve the room temperature plasticity of iron-based amorphous alloys. This invention improves and enhances the room temperature plasticity of iron-based amorphous alloys by shot peening the surface of the iron-based amorphous alloy. However, this patent is prone to forming microcracks on the sample surface, which leads to relaxation or redistribution of the residual stress field after shot peening, and it cannot be applied to iron-based amorphous alloy strips.

[0006] Patent CN115433812A discloses a method for improving the tensile plasticity of toughened iron-based amorphous soft magnetic alloy strips. The prepared iron-based amorphous soft magnetic alloy strips are subjected to alternating hot and cold cycles. However, the iron-based amorphous soft magnetic alloy strips obtained by this patent can only achieve tensile plasticity of more than 4% when the temperature reaches 643K and 693K, and the saturation magnetic induction intensity is relatively low, about 1.0T.

[0007] Therefore, it is urgent to solve the brittleness problem of iron-based amorphous alloys caused by traditional annealing, the problem that affects their processing performance and causes brittle fracture and debris during use due to this brittleness, and the problem of core loss during the preparation process. Summary of the Invention

[0008] Purpose of the invention: To address the problems existing in the prior art, the technical problem to be solved by the present invention is to provide a ferro-based amorphous alloy strip with both high tensile plasticity and work hardening ability and its preparation method. The aim is to solve the problem that traditional annealing treatment causes ferro-based amorphous alloys to become brittle, thereby affecting their processing performance and causing brittle fracture and debris generation during use. Moreover, the present invention can significantly reduce the core loss in the preparation of ferro-based amorphous alloy strips and obtain excellent comprehensive soft magnetic properties.

[0009] The technical problem to be solved by this invention is to prepare an iron-based amorphous alloy strip with high tensile plasticity, work hardening ability and excellent comprehensive soft magnetic properties using this method.

[0010] Technical Solution: To solve the above-mentioned technical problems, this invention provides a method for preparing iron-based amorphous alloy strips with both high tensile plasticity and work hardening capability. The method includes alternatingly placing the iron-based amorphous alloy strips in an oil bath and liquid nitrogen for multiple thermal cycles. Each cycle consists of a 5-5 minute oil bath treatment followed by a 5-5 minute liquid nitrogen treatment. The oil bath temperature is 0.45°C. g ~0.75T g (T g (This refers to the glass transition temperature).

[0011] Among them, the iron-based amorphous alloy strip after the cold and hot cycling treatment is at 0.65T g ~0.9T g (T g Tensile plasticity is greater than 2% within the temperature range of glass transition temperature.

[0012] Furthermore, the iron-based amorphous alloy strip after the cold and hot cycling treatment is subjected to a temperature of 0.65T. g ~0.9T g The yield strength ratio is 0.6 to 0.9 within the temperature range.

[0013] Furthermore, after the thermal cycling treatment, the saturation magnetic induction intensity of the iron-based amorphous alloy strip is 1.4T to 1.7T.

[0014] Furthermore, the oil viscosity of the oil bath is 50 cst to 200 cst, for example, it can be 50 cst, 100 cst, 200 cst, etc., but is not limited to the listed values. Other unlisted values ​​within this range are also applicable.

[0015] The total duration of the multiple hot and cold cycles is 10 min to 120 min. Preferably, the total duration of the multiple hot and cold cycles is 15 min to 90 min, for example, 15 min, 30 min, 40 min, 50 min, 90 min, etc., but not limited to the listed values. Other unlisted values ​​within this range are also applicable.

[0016] The single oil bath treatment time of the hot and cold cycle treatment is 10s to 3min. Preferably, the single liquid nitrogen treatment time of the hot and cold cycle treatment is 10s to 3min.

[0017] The chemical composition of the iron-based amorphous soft magnetic alloy strip is Fe. a Co b Si c M d Where a, b, c, and d represent the atomic percentages of the corresponding elements, M is one or more of the elements B, P, or C, 67≤a≤83, 0≤b≤16, 2≤c≤7, 10≤d≤15, and a+b+c+d=100.

[0018] Furthermore, the thickness of the iron-based amorphous alloy strip is 15μm to 30μm, for example, it can be 15μm, 18μm, 20μm, 22μm, 26μm, 30μm, etc., but is not limited to the listed values. Other unlisted values ​​within this range are also applicable.

[0019] The preparation method of the iron-based amorphous alloy strip includes the following steps: raw materials containing Fe, Co, Si and M elements are induction melted under high-purity argon protection, and after cooling, a master alloy ingot with uniform composition is obtained. The master alloy ingot is then prepared into an iron-based amorphous alloy strip using a single-roll quenching method, wherein M is one or more of B, P or C elements.

[0020] The preparation method further includes ultrasonically cleaning the prepared amorphous alloy strip in an alcohol solution and drying it to obtain an iron-based amorphous alloy strip. Preferably, the ultrasonic cleaning time is 10 min to 30 min. For example, it can be 10 min, 12 min, 15 min, 20 min, 30 min, etc., but is not limited to the listed values. Other unlisted values ​​within this range are also applicable.

[0021] The iron-based amorphous alloy strip prepared by the preparation method described in this invention.

[0022] The present invention discloses a ferro-based amorphous alloy strip with both high tensile plasticity and work hardening capability, and a method for preparing the same, specifically comprising the following steps:

[0023] Step 1: The prepared raw materials are induction melted under the protection of high-purity argon gas. After cooling, a master alloy ingot with uniform composition is obtained. The master alloy ingot is then processed into iron-based amorphous alloy strip using a single-roll quenching method.

[0024] Step 2: The amorphous alloy strip is alternately placed in an oil bath and liquid nitrogen for thermal cycling treatment; one cycle of the thermal cycling treatment consists of first undergoing oil bath treatment for 5 seconds to 5 minutes, followed by liquid nitrogen treatment for 5 seconds to 5 minutes, wherein the oil bath treatment temperature is 0.45T. g ~0.75T g ;

[0025] Step 3: Place the amorphous alloy strip obtained in Step 2 in an alcohol solution for ultrasonic cleaning and drying to obtain the iron-based amorphous alloy strip.

[0026] Beneficial Effects: Compared with the prior art, the present invention has the following advantages: The present invention provides an iron-based amorphous alloy strip with both high tensile plasticity and work hardening ability, and a method for preparing the same, significantly optimizing the tensile properties of the iron-based amorphous alloy strip, and significantly reducing the core loss during the preparation of the iron-based amorphous alloy strip. Specifically, this includes the following aspects:

[0027] (1) This invention significantly improves the tensile plasticity of iron-based amorphous alloy strips through hot and cold cycling treatment, and the resulting iron-based amorphous alloy strips exhibit significant work hardening ability at 0.65T. g ~0.9T g The yield strength ratio is 0.6 to 0.9 within the temperature range.

[0028] (2) This invention significantly improves the tensile plasticity of iron-based amorphous alloy strips through hot and cold cycling treatment, while maintaining its excellent soft magnetic properties. The saturation magnetic induction intensity reaches 1.4T to 1.7T, and the loss is significantly reduced.

[0029] (3) The present invention has a non-destructive amorphous alloy sample morphology, short processing time, and strong applicability, which can greatly expand the application prospects of iron-based amorphous soft magnetic alloys as structural functional materials. Attached Figure Description

[0030] Figure 1 X-ray diffraction patterns of the amorphous alloy strips prepared in Examples 1, 2 and Comparative Example 1;

[0031] Figure 2 The tensile stress-strain curves of the amorphous alloy strips prepared in Example 1 and Comparative Example 1 at 533 K are shown.

[0032] Figure 3 The following are DSC curves of the amorphous alloy strips prepared in Example 2 and Comparative Example 1;

[0033] Figure 4 Hysteresis loop curves of the amorphous alloy strips prepared in Examples 1, 2 and Comparative Example 1;

[0034] Figure 5 The graphs show the variation of loss with magnetic flux density at 50Hz for the amorphous alloy strips prepared in Examples 1, 2 and Comparative Example 1.

[0035] Figure 6 The graphs show the variation of loss with magnetic flux density at 1 kHz after the amorphous alloy strips prepared in Examples 1, 2 and Comparative Example 1 are wound into iron cores. Detailed Implementation

[0036] To further illustrate the content of this invention, the invention will be described in detail below with reference to the accompanying drawings and embodiments.

[0037] Unless otherwise stated, all technical and scientific terms used herein have the same meaning as commonly understood by one of ordinary skill in the art. While only preferred methods and materials have been described herein, any methods and materials similar to or equivalent to those described herein may be used in the implementation or testing of this invention.

[0038] Various improvements and variations can be made to the specific embodiments described in this specification without departing from the scope or spirit of the invention, which will be obvious to those skilled in the art. The specification and embodiments of this invention are merely exemplary, and any variations or substitutions that can be easily conceived by those skilled in the art within the scope of the technology disclosed in this invention fall within the protection and disclosure scope of this invention. The terms "comprising," "having," etc., as used herein are open-ended terms, meaning they include but are not limited to.

[0039] Example 1: Preparation of Fe by cold and hot cycling treatment 75 Co8B 10 Si3C3P1 iron-based amorphous alloy

[0040] A method for preparing iron-based amorphous alloy strips possessing high tensile plasticity, work hardening ability, and excellent comprehensive soft magnetic properties, comprising the following specific steps:

[0041] (1) Iron blocks, cobalt blocks, boron particles, silicon particles, and iron phosphide particles (with a phosphorus content of 26.4%) with a purity greater than 99 wt.% purchased from Zhongnuo New Materials (Beijing) Technology Co., Ltd., and iron-carbon blocks (with a carbon content of 5%) purchased from Beijing Zhongjinyan New Materials Technology Co., Ltd., were respectively processed according to formula Fe75 Co8B 10 20g of a mixture was obtained by adjusting the atomic percentage of Si3C3P1. The mixture was then melted in an induction melting furnace under argon protection (melting temperature 1250℃~1350℃) to obtain a homogeneous master alloy ingot.

[0042] (2) After the master alloy ingot is broken, it is put into a quartz tube with a nozzle at the bottom. The quartz tube is fixed in the induction coil. Under the protection of high-purity argon, the small alloy ingot is rapidly melted by induction heating. Then the heating power is turned off. After the alloy melt cools down to a state of slight surface shaking (1080℃~1130℃), the molten alloy liquid is rapidly sprayed onto the surface of a high-speed rotating copper roller by the pressure difference between the inside of the quartz tube and the cavity using the single roller rapid cooling method to rapidly cool it. Amorphous alloy strip with a thickness of about 16μm is prepared.

[0043] (3) The amorphous alloy strip was alternately placed in an oil bath and liquid nitrogen for thermal cycling treatment; one cycle of thermal cycling treatment consisted of 30 seconds of oil bath treatment followed by 30 seconds of liquid nitrogen treatment, wherein the oil bath treatment temperature was 463K (0.69T). g The oil in the oil bath had a viscosity of 100 cSt, and then underwent repeated hot and cold cycling treatment for a total duration of 30 minutes. Afterwards, it was allowed to naturally return to room temperature in air.

[0044] (4) The amorphous alloy strip after the cold and hot cycle treatment is placed in an alcohol solution for ultrasonic cleaning for 10 minutes and then dried.

[0045] Example 2: Preparation of Fe by cold and hot cycling treatment 75 Co8B 10 Si3C3P1 iron-based amorphous alloy

[0046] A method for preparing iron-based amorphous alloy strips possessing high tensile plasticity, work hardening ability, and excellent comprehensive soft magnetic properties, comprising the following specific steps:

[0047] (1) Iron blocks, cobalt blocks, boron particles, silicon particles, and iron phosphide particles (with a phosphorus content of 26.4%) with a purity greater than 99 wt.% purchased from Zhongnuo New Materials (Beijing) Technology Co., Ltd., and iron-carbon blocks (with a carbon content of 5%) purchased from Beijing Zhongjinyan New Materials Technology Co., Ltd., were respectively processed according to formula Fe 75 Co8B 10 20g of a mixture was obtained by adjusting the atomic percentage of Si3C3P1. The mixture was then melted in an induction melting furnace under argon protection (melting temperature 1250℃~1350℃) to obtain a homogeneous master alloy ingot.

[0048] (2) After the master alloy ingot is broken, it is put into a quartz tube with a nozzle at the bottom. The quartz tube is fixed in the induction coil. Under the protection of high-purity argon, the small alloy ingot is rapidly melted by induction heating. Then the heating power is turned off. After the alloy melt cools down to a state of slight surface shaking (1080℃~1130℃), the molten alloy liquid is rapidly sprayed onto the surface of a high-speed rotating copper roller by the pressure difference between the inside of the quartz tube and the cavity using the single roller rapid cooling method to rapidly cool it. Amorphous alloy strip with a thickness of about 16μm is prepared.

[0049] (3) The amorphous alloy strip was alternately placed in an oil bath and liquid nitrogen for thermal cycling treatment; one cycle of thermal cycling treatment consisted of 15 seconds of oil bath treatment followed by 15 seconds of liquid nitrogen treatment, wherein the oil bath treatment temperature was 463K (0.69T). g The oil in the oil bath had a viscosity of 100 cSt, and then underwent repeated hot and cold cycling treatment for a total duration of 30 minutes. Afterwards, it was allowed to naturally return to room temperature in air.

[0050] (4) After the cold and hot cycling treatment, the amorphous alloy strip is placed in an alcohol solution for ultrasonic cleaning for 30 minutes and then dried.

[0051] Comparative Example 1: Preparation of Fe 75 Co8B 10 Si3C3P1 iron-based amorphous alloy

[0052] The preparation process of Comparative Example 1 is the same as that of Example 1, except that the hot and cold cycling treatment is not performed (i.e., steps 3 and 4 are omitted), and the rest is the same as that of Example 1.

[0053] The structures of the alloy strips prepared in Examples 1, 2, and Comparative Example 1 were determined by X-ray diffraction (XRD), as follows: Figure 1 As shown, the amorphous alloy samples prepared in Examples 1, 2 and Comparative Example 1 all have only one diffuse diffraction peak, indicating that the cold and hot cycling treatment did not change the amorphous structure of the samples.

[0054] The thermal properties of the amorphous alloy strips prepared in Example 2 and Comparative Example 1 were detected using differential scanning calorimetry (DSC) at a heating rate of 20 K / min. Figure 2 As shown, the glass transition temperature T of the sample before and after thermal cycling. g and crystallization temperature T x The absence of significant changes indicates that the hot and cold cycling treatment did not alter the thermal properties of the sample.

[0055] The tensile stress-strain curves of the amorphous alloy strips prepared in Example 1 and Comparative Example 1 at 533 K were measured using a dynamic mechanical analyzer (DMA), as shown below. Figure 3As shown, the tensile plasticity of the quenched amorphous alloy strip prepared in Comparative Example 1 was 2.8%, while the tensile plasticity of the amorphous alloy prepared in Example 1 after thermal cycling treatment was increased to 10% and it had excellent work hardening ability and a yield strength ratio of 0.67. This indicates that thermal cycling treatment can significantly improve the mechanical properties of iron-based amorphous alloy strips.

[0056] The saturation magnetic induction intensity and loss at 1 kHz of the samples from Examples 1, 2 and Comparative Example 1 were tested using a vibrating sample magnetometer and an AC hysteresis loop measuring instrument. Figure 4 The hysteresis loop curves of the amorphous alloy strip samples are shown. The saturation magnetic induction in samples of Example 1 and Example 2 are 1.68T and 1.70T, respectively, which is an improvement compared to the saturation magnetic induction induction of 1.65T in Comparative Example 1. Figure 5 The curves showing the loss of the samples from Examples 1, 2, and Comparative Example 1 as a function of magnetic flux density at 1 kHz are shown. The losses of the samples from Examples 1 and 2 are significantly lower than those of the sample from Comparative Example 1, indicating that the method of the present invention is beneficial to improving the overall soft magnetic properties of iron-based amorphous alloy strips.

[0057] Comparative Example 2

[0058] The preparation method of Comparative Example 2 is exactly the same as that of Example 2, except that the oil bath temperature in step (3) is 563K (0.84T). g ).

[0059] Due to the excessively high oil bath treatment temperature, the amorphous alloy exhibited excessive relaxation, resulting in excessive annihilation of free volume, which was detrimental to the mechanical properties of the strip. DSC testing revealed that the relaxation enthalpy of the amorphous alloy prepared in Comparative Example 2 was 296 J / mol, a 48% decrease compared to the relaxation enthalpy of the same composition sample that had not undergone thermal cycling treatment. Testing showed that the amorphous alloy strip exhibited a tensile plasticity of 2.1% and a yield strength ratio of 0.91 at 533 K, indicating a decrease in tensile plasticity compared to the sample.

[0060] Example 3: Preparation of Fe by cold and hot cycling treatment 80 Si6B 13 C1 iron-based amorphous alloy

[0061] (1) Iron blocks, boron particles, and silicon particles with a purity greater than 99 wt.% purchased from Zhongnuo New Materials (Beijing) Technology Co., Ltd., and iron-carbon blocks (carbon mass percentage of 5%) purchased from Beijing Zhongjinyan New Materials Technology Co., Ltd., were respectively processed according to formula Fe 80 Si6B 13 The C1 atomic percentage was used to obtain a mixture of 20g. The mixture was then melted in an induction melting furnace under argon protection (melting temperature 1250℃~1350℃) to obtain a master alloy ingot with uniform composition.

[0062] (2) After the master alloy ingot is broken, it is put into a quartz tube with a nozzle at the bottom. The quartz tube is fixed in the induction coil. Under the protection of high-purity argon, the small alloy ingot is rapidly melted by induction heating. Then the heating power is turned off. After the alloy melt cools down to a state of slight surface shaking (1080℃~1130℃), the molten alloy liquid is rapidly sprayed onto the surface of a high-speed rotating copper roller by the pressure difference between the inside of the quartz tube and the cavity using the single-roller rapid cooling method to rapidly cool it. Amorphous alloy strip with a thickness of about 22μm is prepared.

[0063] (3) The amorphous alloy strip was alternately subjected to a hot and cold cycle treatment in an oil bath and liquid nitrogen. One cycle of the hot and cold cycle treatment consisted of 60 seconds of oil bath treatment followed by 60 seconds of liquid nitrogen treatment. The oil bath treatment temperature was 436 K (0.60 T). g The oil in the oil bath had a viscosity of 50 cSt, and then underwent repeated hot and cold cycling treatment for a total duration of 60 minutes. Afterwards, it was allowed to naturally return to room temperature in air.

[0064] (4) After the cold and hot cycling treatment, the amorphous alloy strip is placed in an alcohol solution for ultrasonic cleaning for 10 minutes and then dried.

[0065] The amorphous alloy strip prepared in this embodiment has a tensile plasticity of 3.3% at 453K, a yield strength ratio of 0.82, and a saturation magnetic induction intensity of 1.56T.

[0066] Comparative Example 3

[0067] The preparation method of Comparative Example 3 is exactly the same as that of Example 2, except that the oil bath temperature in step (3) is 298K (0.41T). g ).

[0068] Due to the excessively low oil bath treatment temperature, the atomic diffusion rate during the oil bath treatment is low, which is not conducive to the effect of increasing the inhomogeneity of the amorphous alloy structure through hot and cold cycling. Tests showed that the tensile plasticity of this amorphous alloy strip at 453K was 1.6%, and the yield strength ratio was 0.9, which is lower than the tensile plasticity of the sample.

[0069] Example 4: Preparation of Fe by cold and hot cycling treatment 83 B 10 Si3C3P1 iron-based amorphous alloy

[0070] (1) Iron blocks, boron particles, silicon particles, and iron phosphide particles (with a phosphorus content of 26.4%) with a purity greater than 99 wt.% purchased from Zhongnuo New Materials (Beijing) Technology Co., Ltd., and iron-carbon blocks (with a carbon content of 5%) purchased from Beijing Zhongjinyan New Materials Technology Co., Ltd., were respectively processed according to formula Fe 83 B 1020g of a mixture was obtained by adjusting the atomic percentage of Si3C3P1. The mixture was then melted in an induction melting furnace under argon protection (melting temperature 1250℃~1350℃) to obtain a homogeneous master alloy ingot.

[0071] (2) After the master alloy ingot is broken, it is put into a quartz tube with a nozzle at the bottom. The quartz tube is fixed in the induction coil. Under the protection of high-purity argon, the small alloy ingot is rapidly melted by induction heating. Then the heating power is turned off. After the alloy melt cools down to a state of slight surface shaking (1080℃~1130℃), the molten alloy liquid is rapidly sprayed onto the surface of a high-speed rotating copper roller by the pressure difference between the inside of the quartz tube and the cavity using the single roller rapid cooling method to rapidly cool it. Amorphous alloy strip with a thickness of about 30μm is prepared.

[0072] (3) The amorphous alloy strip was alternately placed in an oil bath and liquid nitrogen for thermal cycling treatment. One cycle of thermal cycling treatment consisted of 60 seconds of oil bath treatment followed by 60 seconds of liquid nitrogen treatment. The oil bath treatment temperature was 507K (0.75T). g The oil in the oil bath has a viscosity of 200 cst, and then it undergoes repeated hot and cold cycling treatment for a total duration of 30 min, after which it is allowed to naturally return to room temperature in the air.

[0073] (4) After the cold and hot cycling treatment, the amorphous alloy strip is placed in an alcohol solution for ultrasonic cleaning for 15 minutes and then dried.

[0074] The amorphous alloy strip prepared in this embodiment has a tensile plasticity of 3.5% at 473K, a yield strength ratio of 0.81, and a saturation magnetic induction intensity of 1.59T.

[0075] Comparative Example 4

[0076] The preparation method of Comparative Example 4 is exactly the same as that of Example 3. The only difference is that in step (3), one cycle of the hot and cold cycle treatment is first a liquid nitrogen treatment for 60 seconds, and then an oil bath treatment for 60 seconds.

[0077] Because the final step of the thermal cycling process is an oil bath treatment, the amorphous alloy strip is allowed to cool naturally to room temperature in air, which prevents some reversible relaxation from being activated. Testing showed that the amorphous alloy strip exhibited a tensile plasticity of 1.8% and a yield strength ratio of 0.89 at 473K.

[0078] Example 5: Preparation of a product with the molecular formula Fe after cold and hot cycling treatment. 67 Co 16 B 10 The steps for producing Si3C3P1 iron-based amorphous alloy are as follows:

[0079] (1) Iron blocks, cobalt blocks, boron particles, silicon particles, and iron phosphide particles (with a phosphorus content of 26.4%) with a purity greater than 99 wt.% purchased from Zhongnuo New Materials (Beijing) Technology Co., Ltd., and iron-carbon blocks (with a carbon content of 5%) purchased from Beijing Zhongjinyan New Materials Technology Co., Ltd., were respectively processed according to formula Fe 67 Co 16 B 10 20g of a mixture was obtained by adjusting the atomic percentage of Si3C3P1. The mixture was then melted in an induction melting furnace under argon protection (melting temperature 1250℃~1350℃) to obtain a homogeneous master alloy ingot.

[0080] (2) After the master alloy ingot is broken, it is put into a quartz tube with a nozzle at the bottom. The quartz tube is fixed in the induction coil. Under the protection of high-purity argon, the small alloy ingot is rapidly melted by induction heating. Then the heating power is turned off. After the alloy melt cools down to a state of slight surface shaking (1080℃~1130℃), the molten alloy liquid is rapidly sprayed onto the surface of a high-speed rotating copper roller by the pressure difference between the inside of the quartz tube and the cavity using the single roller rapid cooling method to rapidly cool it. Amorphous alloy strip with a thickness of about 15μm is prepared.

[0081] (3) The amorphous alloy strip was alternately placed in an oil bath and liquid nitrogen for thermal cycling treatment. One cycle of thermal cycling treatment consisted of 2 minutes of oil bath treatment followed by 2 minutes of liquid nitrogen treatment. The oil bath treatment temperature was 507K (0.75T). g The oil in the oil bath has a viscosity of 150 cst, and then it undergoes repeated hot and cold cycling treatment for a total duration of 120 min, after which it is allowed to naturally return to room temperature in the air.

[0082] (4) After the cold and hot cycling treatment, the amorphous alloy strip is placed in an alcohol solution for ultrasonic cleaning for 15 minutes and then dried.

[0083] The amorphous alloy strip prepared in this embodiment has a tensile plasticity of 2.5% at 433K, a yield strength ratio of 0.85, and a saturation magnetic induction intensity of 1.73T.

[0084] Comparative Example 5

[0085] The preparation method of Comparative Example 5 is exactly the same as that of Example 4. The only difference is that the single liquid nitrogen treatment time in step (3) is 10 min and the single oil bath treatment time is 10 min.

[0086] Due to the excessively long duration of single liquid nitrogen and oil bath treatments, the number of thermal cycles is reduced, increasing the relaxation degree of the amorphous alloy and limiting the effectiveness of thermal cycling in enhancing the structural inhomogeneity of the amorphous alloy. Tests showed that the amorphous alloy strip exhibited a tensile plasticity of 1.6% and a yield strength ratio of 0.91 at 433K.

[0087] Example 6: Preparation of a product with the molecular formula Fe after cold and hot cycling treatment. 67 Co 16 B 10 The steps for producing Si3C3P1 iron-based amorphous alloy are as follows:

[0088] (1) Iron blocks, cobalt blocks, boron particles, silicon particles, and iron phosphide particles (with a phosphorus content of 26.4%) with a purity greater than 99 wt.% purchased from Zhongnuo New Materials (Beijing) Technology Co., Ltd., and iron-carbon blocks (with a carbon content of 5%) purchased from Beijing Zhongjinyan New Materials Technology Co., Ltd., were respectively processed according to formula Fe 67 Co 16 B 10 20g of a mixture was obtained by adjusting the atomic percentage of Si3C3P1. The mixture was then melted in an induction melting furnace under argon protection (melting temperature 1250℃~1350℃) to obtain a homogeneous master alloy ingot.

[0089] (2) After the master alloy ingot is broken, it is put into a quartz tube with a nozzle at the bottom. The quartz tube is fixed in the induction coil. Under the protection of high-purity argon, the small alloy ingot is rapidly melted by induction heating. Then the heating power is turned off. After the alloy melt cools down to a state of slight surface shaking (1080℃~1130℃), the single-roller rapid cooling and spinning technology is used to rapidly spray the molten alloy liquid onto the surface of the high-speed rotating copper roller for rapid cooling, thus preparing an amorphous alloy strip with a thickness of about 30μm.

[0090] (3) The amorphous alloy strip was alternately placed in an oil bath and liquid nitrogen for thermal cycling treatment. One cycle of thermal cycling treatment consisted of 15 seconds of oil bath treatment followed by 15 seconds of liquid nitrogen treatment. The oil bath treatment temperature was 378K (0.57T). g The oil in the oil bath has a viscosity of 100 cst, and then it undergoes repeated hot and cold cycling treatment for a total duration of 10 min, after which it is allowed to naturally return to room temperature in the air.

[0091] (4) After the cold and hot cycling treatment, the amorphous alloy strip is placed in an alcohol solution for ultrasonic cleaning for 15 minutes and then dried.

[0092] The amorphous alloy strip prepared in this embodiment has a tensile plasticity of 3.0% at 503K, a yield strength ratio of 0.79, and a saturation magnetic induction intensity of 1.73T.

[0093] Comparative Example 6

[0094] The preparation method of Comparative Example 6 is exactly the same as that of Example 5. The only difference is that the single liquid nitrogen treatment time in step (3) is 3s and the single oil bath treatment time is 3s.

[0095] Due to the short duration of each liquid nitrogen and oil bath treatment, the temperature distribution of the sample was uneven during the thermal cycling process, and the time was insufficient for the strip to reach the oil bath / liquid nitrogen temperature during the thermal cycling process. Testing revealed that the amorphous alloy strip exhibited a tensile plasticity of 1.5% and a yield strength ratio of 0.9 at 503K.

Claims

1. A method for preparing iron-based amorphous alloy strips possessing both high tensile plasticity and work hardening capability, characterized in that, The specific steps are as follows: (1) Iron blocks, cobalt blocks, boron particles, silicon particles, iron phosphide particles, and iron-carbon blocks with a purity greater than 99 wt.% are respectively processed according to formula Fe 75 Co8B 10 The Si3C3P1 atomic percentage was used to obtain a mixture, which was then melted in an induction melting furnace under argon protection at a melting temperature of 1250℃~1350℃ to obtain a master alloy ingot with uniform composition. (2) After the master alloy ingot is broken, it is put into a quartz tube with a nozzle at the bottom. The quartz tube is fixed in the induction coil. Under the protection of high-purity argon, the small alloy ingot is rapidly melted by induction heating. Then the heating power is turned off. When the alloy melt cools down to a state of slight surface shaking, the temperature is 1080℃ ~ 1130℃. The single-roller rapid cooling strip method is used to rapidly spray the molten alloy liquid onto the surface of the high-speed rotating copper roller for rapid cooling by utilizing the pressure difference between the inside of the quartz tube and the cavity. Amorphous alloy strip is thus prepared. (3) The amorphous alloy strip was alternately placed in an oil bath and liquid nitrogen for thermal cycling treatment; one cycle of thermal cycling treatment consisted of 30 s of oil bath treatment followed by 30 s of liquid nitrogen treatment, wherein the oil bath treatment temperature was 463 K (0.69 T g The oil in the oil bath has a viscosity of 100 cst, and then it undergoes repeated hot and cold cycling treatment for a total duration of 30 minutes, after which it is allowed to naturally return to room temperature in the air. (4) The amorphous alloy strip after the cold and hot cycle treatment is placed in an alcohol solution for ultrasonic cleaning for 10 min and then dried.

2. The method for preparing iron-based amorphous alloy strip with both high tensile plasticity and work hardening ability according to claim 1, characterized in that, The tensile test temperature is 0.65°C. T g ~0.9 T g .

3. The iron-based amorphous alloy strip prepared by the preparation method according to any one of claims 1 to 2.

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