Amorphous magnetically soft alloy material, amorphous magnetically soft alloy iron core and preparation method

Abstract

The invention provides an amorphous magnetically soft alloy material, an amorphous magnetically soft alloy iron core and a preparation method. The chemical expression of component atoms of the alloy material is Fe Si Al < c > V < d > Mn < e > Cr < f > B < x > Mg < y > N < h > O , in the formula, 80 < = a < = 85, 3 < = b < = 5, 1 < = c < = 3, 0.5 < = d < = 1.5, 1 < = e < = 2, 1 < = f < = 2, 3 < = x < = 5, 0.5 < = y < = 1.5, 0.5 < = h < = 1.0, 0.1 < = i < = 0.3, and a + b + c + d + e + f + x + y + h + i = 100. The amorphous magnetically soft alloy material has high saturation flux density and magnetic conductivity, can significantly reduce eddy current loss under high frequency, and has good mechanical properties and corrosion resistance.

Description

Technical Field

[0001] The present invention relates to the technical field of manufacturing soft magnetic alloys, and specifically provides an amorphous soft magnetic alloy material, an amorphous soft magnetic alloy core, and a preparation method thereof. Background Art

[0002] In the fields of high-efficiency power transmission, stepping motors, transformers, and inductors, etc., the performance of soft magnetic materials significantly affects the working efficiency and service life of equipment. Traditional soft magnetic materials (such as silicon steel, iron-nickel alloys) perform well in low-frequency applications, but in high-frequency and high-magnetic-field applications, their performance is limited due to relatively high eddy current losses and hysteresis losses. At the same time, although traditional amorphous soft magnetic alloys have good magnetic permeability and low-loss characteristics, their saturation magnetic induction intensity is relatively low, which limits their wide use in high-power and high-magnetic-field applications.

[0003] To solve these problems, researchers have continuously tried to develop amorphous soft magnetic alloys with high saturation magnetic induction intensity, low losses, and excellent mechanical properties by optimizing chemical compositions and melting processes. Although adding some alloying elements such as silicon, aluminum, vanadium, etc. can improve magnetic and mechanical properties to a certain extent.

[0004] However, there are still bottlenecks in further improving the saturation magnetic induction intensity, reducing high-frequency losses, improving mechanical strength and ductility, etc. in the prior art. Summary of the Invention

[0005] The purpose of the present invention is to solve the problem of poor comprehensive performance of existing amorphous soft magnetic alloy materials.

[0006] The purpose of the present invention is achieved by adopting the following technical solutions: The present invention provides an amorphous soft magnetic alloy material, and the component atomic chemical expression of the alloy material is: Fe a Si b Al c V d Mn e Cr f B x Mg y N h O i ; where 80 ≤ a ≤ 85, 3 ≤ b ≤ 5, 1 ≤ c ≤ 3, 0.5 ≤ d ≤ 1.5, 1 ≤ e ≤ 2, 1 ≤ f ≤ 2, 3 ≤ x ≤ 5, 0.5 ≤ y ≤ 1.5, 0.5 ≤ h ≤ 1.0, 0.1 ≤ i ≤ 0.3, and a + b + c + d + e + f + x + y + h + i = 100.

[0007] Based on the same inventive concept, the present invention also provides a preparation method of an amorphous soft magnetic alloy material, including: Raw material preparation: Weigh the raw materials of each element according to the component ratio of the amorphous soft magnetic alloy material. The elements iron, silicon, aluminum, vanadium, manganese, and chromium in the raw materials are introduced in the form of single substances, and the remaining elements are introduced in the form of boromagnesium compounds, nitrides, and oxides; First-stage melting: Put the raw materials except the boromagnesium compound into a high-frequency induction melting furnace. Under argon protection, heat the melting temperature to 1500°C - 1600°C, and the melting duration is 5 min - 10 min to form a primary melt. Second-stage melting: After reducing the melting temperature to 1300°C - 1400°C, add the boromagnesium compound to the primary melt and stir for a duration of 5 min - 10 min to obtain a secondary melt; Solidification and cooling: Under argon protection, when the secondary melt stands still to the semi-solid state, use high-pressure water quenching or gas cooling to form the amorphous soft magnetic alloy material, and the cooling rate is 10 4 K / s - 10 5 K / s.

[0008] Preferably, the boromagnesium compound is Mg2B2O5, and the boromagnesium compound is added as a reaction substance in the second-stage melting.

[0009] Preferably, the addition amount of the boromagnesium compound is 0.1% - 0.3% of the total mass of the raw materials.

[0010] Preferably, the nitride is AlN; the oxide is at least one of B2O3 and Al2O3.

[0011] Based on the same inventive concept, the present invention also provides a method for preparing an amorphous soft magnetic alloy iron core. The preparation method includes the following steps: Grinding treatment: Take the alloy block of the amorphous soft magnetic alloy material and mechanically grind it into amorphous particles in a cooling environment, and use deionized water to wash the amorphous particles to remove surface impurities and oxides; Pre-pressing and forming: Put the washed amorphous particles into a mold and perform pre-pressing under heating conditions to obtain a pre-pressed alloy sheet; Densification treatment: Subject the pre-pressed alloy sheet to hot isostatic pressing to form a dense alloy sheet; Rolling and stacking treatment: Fine-roll the dense alloy sheet in a rolling mill to obtain a rolled alloy sheet, cut the rolled alloy sheet and stack and fix it to form a laminated sheet; Annealing treatment: Perform spray annealing on the laminated sheet in a high-frequency magnetic field; Surface treatment and assembly: After ultrasonic polishing the surface of the annealed laminated sheet, coat an insulating layer on the surface of the laminated sheet, and then assemble the laminated sheet into an amorphous soft magnetic alloy iron core.

[0012] Preferably, in the grinding treatment, the particle size of the amorphous particles is less than 20 μm.

[0013] Preferably, in the grinding process, the temperature of the cooling environment does not exceed -40°C.

[0014] Preferably, in the pre-pressing and forming process, the hot pressing temperature of the pre-pressing and forming is 400°C - 600°C, and the hot pressing pressure is 3000 MPa - 5000 MPa.

[0015] Preferably, in the pre-pressing and forming process, the thickness of the pre-pressed alloy sheet is 0.03 mm - 0.04 mm.

[0016] Preferably, in the densification process, the temperature of the hot isostatic pressing is 500°C - 600°C, the pressure of the hot isostatic pressing is 80 MPa - 120 MPa, and the holding time of the hot isostatic pressing is 20 min - 30 min.

[0017] Preferably, in the rolling and stacking process, the thickness of the rolled alloy sheet is 0.01 mm - 0.014 mm, and the thickness of the stacked sheets is 1 cm - 20 cm.

[0018] Preferably, in the annealing process, the magnetic field strength is 50 mT - 200 mT, the annealing temperature is 250°C - 450°C, and the annealing time is 1 h - 2 h.

[0019] Preferably, in the surface treatment and assembly, the ultrasonic frequency is 20 kHz - 40 kHz, and the polishing time is 10 min - 20 min.

[0020] Based on the same inventive concept, the present invention also provides an amorphous soft magnetic alloy iron core, which is made by using the preparation method of the amorphous soft magnetic alloy iron core described above.

[0021] Compared with the prior art, the beneficial effects of the present invention are as follows: The amorphous soft magnetic alloy material provided by the present invention, the chemical expression of the component atoms of the alloy material is: Fe a Si b Al c V d Mn e Cr f B x Mg y N h O i; wherein, 80 ≤ a ≤ 85, 3 ≤ b ≤ 5, 1 ≤ c ≤ 3, 0.5 ≤ d ≤ 1.5, 1 ≤ e ≤ 2, 1 ≤ f ≤ 2, 3 ≤ x ≤ 5, 0.5 ≤ y ≤ 1.5, 0.5 ≤ h ≤ 1.0, 0.1 ≤ i ≤ 0.3, and a + b + c + d + e + f + x + y + h + i = 100. This amorphous soft magnetic alloy material has a high saturation magnetic induction intensity and magnetic permeability, and can significantly reduce eddy current losses at high frequencies, and it has good mechanical properties and corrosion resistance. Detailed implementation manner

[0022] The following embodiments are provided to better further understand the present invention, which is not limited to the described optimal implementation manner, and does not constitute a limitation on the content and protection scope of the present invention. Any product that is the same as or similar to the present invention obtained by anyone under the inspiration of the present invention or by combining the features of the present invention with those of other prior arts falls within the protection scope of the present invention.

[0023] For those steps or conditions of specific experiments not specified in the present invention, the operations or conditions of the conventional experimental steps described in the literature in this field can be followed.

[0024] The present invention provides an amorphous soft magnetic alloy material, and the chemical expression of the component atoms of the alloy material is: Fe a Si b Al c V d Mn e Cr f B x Mg y N h O i ; wherein, 80 ≤ a ≤ 85, 3 ≤ b ≤ 5, 1 ≤ c ≤ 3, 0.5 ≤ d ≤ 1.5, 1 ≤ e ≤ 2, 1 ≤ f ≤ 2, 3 ≤ x ≤ 5, 0.5 ≤ y ≤ 1.5, 0.5 ≤ h ≤ 1.0, 0.1 ≤ i ≤ 0.3, and a + b + c + d + e + f + x + y + h + i = 100. a, b, c, d, e, f, x, y, h, i are respectively the atomic percentage values of the corresponding elements.

[0025] In the alloy material of the invention, iron is the matrix element of the soft magnetic alloy, providing high magnetic permeability and high saturation magnetic induction intensity for the alloy material. Iron forms a favorable magnetic flux path in the amorphous structure, reducing the coercive force and magnetic loss, and especially helping to improve the magnetic permeability of the alloy in high-frequency applications. In the range of its atomic percentage value 80 ≤ a ≤ 85, a higher iron content helps to maintain the amorphous structure, while improving the mechanical strength and ductility of the material. If the iron content is lower than this range, the saturation magnetic induction intensity will decrease. If it is higher than this range, the soft magnetic properties will deteriorate, greatly increasing the loss and coercive force of the alloy.

[0026] In the invented alloy material, the addition of silicon significantly increases the resistivity and high-frequency performance of the alloy, effectively reducing eddy current loss. In the range of its atomic percentage value 3 ≤ b ≤ 5, as an amorphous forming element, silicon can more effectively inhibit grain growth, promote the formation of amorphous structure, improve the soft magnetic properties of the alloy, and at the same time enhance the antioxidant and corrosion resistance of the material, making it more stable in harsh environments. If the silicon content > 5, it will cause the saturation magnetic induction intensity of the alloy to decrease; if the silicon content < 3, it will cause the amorphous forming ability of the alloy to decline and deteriorate the magnetic properties.

[0027] In the invented alloy material, aluminum reacts with magnesium during melting to form magnesium-aluminum compounds (such as MgAl2O4), which can effectively refine grains and promote the formation of nanocrystals. In the range of its atomic percentage value 1 ≤ c ≤ 3, it helps to improve the ductility and workability of the alloy, facilitating the forming and lamination of the alloy in subsequent processes. In addition, adding aluminum in this range can also improve the oxidation resistance of the alloy and extend the service life of the iron core. If the aluminum content > 3, it will cause the saturation magnetic induction intensity of the alloy to decrease.

[0028] In the invented alloy material, vanadium can effectively improve the magnetic permeability in the alloy and maintain good magnetic properties under high-temperature conditions. In the range of its atomic percentage value 0.5 ≤ d ≤ 1.5, adding vanadium can improve the high-temperature stability of the alloy, making it show higher performance stability in heat treatment and high-temperature applications. If the vanadium content > 1.5, it will cause the saturation magnetic induction intensity of the alloy to decrease and the heat treatment window to narrow.

[0029] In the invented alloy material, manganese can enhance the ductility of the alloy, improve the mechanical properties and workability of the material. In the range of its atomic percentage value 1 ≤ e ≤ 2, manganese helps to refine grains in the amorphous alloy, improve the soft magnetic properties and saturation magnetic induction intensity, and at the same time helps to improve the corrosion resistance of the alloy, making it suitable for high-humidity or corrosive environments. If the manganese content > 2, it will cause the grain size of the alloy to increase, deteriorating the performance and making the material more brittle.

[0030] In the invented alloy material, chromium, as an anti-corrosion element, can significantly improve the stability of the alloy in humid or oxidative environments. In the range of its atomic percentage value 1 ≤ f ≤ 2, chromium helps to reduce the hysteresis loss, and at the same time improve the high-frequency magnetic properties of the iron core. It can also play a role in refining grains in the amorphous structure and improving the soft magnetic properties. If the chromium content > 2, it will cause the saturation magnetic induction intensity of the alloy to decrease.

[0031] In the invented alloy material, oxygen is introduced in the form of oxides (such as B2O3, Al2O3), which can form nano-scale oxide composite phases in the alloy. When the atomic percentage value is in the range of 0.1 ≤ i ≤ 0.3, it is more capable of stabilizing the amorphous structure and refining the grains. At the same time, in this range, the presence of the oxide composite phase can enhance the antioxidant performance of the material, improve the durability and high-temperature stability of the alloy. If the oxygen content > 0.3, it will cause the alloy to be more prone to oxidation and embrittlement.

[0032] In the invented alloy material, by adding nitrides (such as AlN), nitrogen can react with other elements in the alloy during the melting process to form nano-crystalline nitride composite phases. When the atomic percentage value is in the range of 0.5 ≤ h ≤ 1.0, it can further refine the grains and optimize the microstructure of the alloy, reduce magnetic loss, and improve the magnetic permeability and saturation magnetic induction intensity of the alloy.

[0033] In the invented alloy material, boron is a key element to promote the formation of the amorphous structure and can significantly improve the soft magnetic properties of the alloy. In the range of 3 ≤ x ≤ 5, the composite phases (such as MgB2) formed by boron reacting with magnesium and aluminum can further refine the grains, enhance the high saturation magnetic induction intensity of the alloy, and at the same time reduce the movement energy of the magnetic domain walls and improve the magnetic conductivity of the alloy. If the boron content > 5, it will cause the soft magnetic properties of the alloy to decline.

[0034] In the invented alloy material, magnesium reacts with boron and aluminum to form magnesium boride (MgB2) and magnesium aluminate (MgAl2O4). When the atomic percentage value is in the range of 0.5 ≤ y ≤ 1.5, these two composite phases can refine the grains and improve the saturation magnetic induction intensity. At the same time, in this range, the magnesium element also has high ductility, which helps to enhance the mechanical strength and workability of the iron core in the alloy. If the magnesium content > 1.5, it will cause the saturation magnetic induction intensity of the alloy to decline and the grains to be difficult to refine.

[0035] Based on the same inventive concept, the present invention also provides a preparation method of an amorphous soft magnetic alloy material, including: Ⅰ. Configure raw materials: Weigh the raw materials of each element according to the component ratio of the above-mentioned amorphous soft magnetic alloy material. The elements iron, silicon, aluminum, vanadium, manganese, and chromium in the raw materials are introduced in the form of single substances, and the remaining elements are introduced in the form of boron-magnesium compounds, nitrides, and oxides. The purity of the raw materials is greater than 99.9%. The nitride is AlN; the oxide is at least one of B2O3 and Al2O3.

[0036] Ⅱ. First-stage melting: Put the raw materials except the boron-magnesium compound into a high-frequency induction melting furnace. Under the protection of argon, heat the melting temperature to 1500°C - 1600°C, and the melting duration is 5 min - 10 min to form a primary melt; Ⅲ. Second-stage smelting: After reducing the smelting temperature to 1300°C - 1400°C, add magnesium borate compound to the primary melt and stir for 5 min - 10 min to obtain the secondary melt. Among them, the magnesium borate compound is Mg2B2O5, and the magnesium borate compound is added as a reactant in the second-stage smelting. The addition amount of the magnesium borate compound is 0.1% - 0.3% of the total mass of the raw materials. The second-stage smelting should ensure the full reaction of magnesium, boron, and aluminum to generate nanoscale magnesium boride and magnesium aluminate.

[0037] Ⅳ. Solidification and cooling: Under argon protection, when the secondary melt stands still to the semi-solid state, use high-pressure water quenching or gas cooling to form the amorphous soft magnetic alloy material, and the cooling rate is 10 4 K / s - 10 5 K / s.

[0038] Based on the same inventive concept, the present invention also provides a preparation method for an amorphous soft magnetic alloy core. The preparation method includes the following steps: 1) Grinding treatment: Take the alloy block of the amorphous soft magnetic alloy material and mechanically grind it into amorphous particles in a cooling environment, and use deionized water to wash the amorphous particles to remove surface impurities and oxides.

[0039] In this step, the particle size of the amorphous particles is less than 20 μm, and liquid nitrogen or dry ice is used to make the temperature of the cooling environment not exceed -40°C.

[0040] 2) Pre-pressing and forming: Load the washed amorphous particles into a mold and perform pre-pressing under heating conditions to obtain a pre-pressed alloy sheet.

[0041] In this step, the hot pressing temperature for pre-pressing and forming is 400°C - 600°C, the hot pressing pressure is 3000 MPa - 5000 MPa, ensure that the amorphous particles are tightly combined and formed after pressing, and the thickness of the pre-pressed alloy sheet is 0.03 mm - 0.04 mm.

[0042] 3) Densification treatment: Subject the pre-pressed alloy sheet to hot isostatic pressing to form a dense alloy sheet.

[0043] In this step, use a hot isostatic press to further improve the density and uniformity of the pre-pressed alloy sheet. The temperature of the hot isostatic pressing is 500°C - 600°C, the pressure of the hot isostatic pressing is 80 MPa - 120 MPa, and the holding time of the hot isostatic pressing is 20 min - 30 min.

[0044] 4) Rolling and stacking treatment: Fine-roll the dense alloy sheet in a rolling mill to obtain a rolled alloy sheet, and cut and stack the rolled alloy sheet to form a laminated sheet.

[0045] In this step, the thickness of the rolled alloy sheet is 0.01 mm - 0.014 mm, and the thickness of the laminated sheet is 1 cm - 20 cm.

[0046] 5) Annealing treatment: The laminated sheet is subjected to spray annealing treatment in a high-frequency magnetic field to promote the formation and homogenization of the nanocrystalline phase, and improve the magnetic permeability and soft magnetic properties. Among them, the magnetic field strength is 50 mT - 200 mT, the annealing temperature is 250 °C - 450 °C, and the annealing time is 1 h - 2 h.

[0047] 6) Surface treatment and assembly: The surface of the annealed laminated sheet is subjected to ultrasonic polishing treatment to improve the surface finish and low-loss characteristics of the laminated sheet; an insulating layer is coated on the surface of the laminated sheet to avoid eddy current loss between layers and improve the high-frequency performance of the iron core, and then the laminated sheets are assembled into an amorphous soft magnetic alloy iron core according to the design requirements.

[0048] In this step, the ultrasonic frequency is 20 kHz - 40 kHz, and the polishing time is 10 min - 20 min.

[0049] Based on the same inventive concept, the present invention also provides an amorphous soft magnetic alloy iron core, which is made by using the preparation method of the above amorphous soft magnetic alloy iron core.

[0050] Examples 1 - 10 and Comparative Examples 1 - 3 The samples of Examples 1 - 10 of the present invention respectively select the element ratios and alloy materials of the amorphous soft magnetic alloy materials in the above different ranges and the preparation process parameters of the iron core, and the samples of Comparative Examples 1 - 3 respectively select the alloy materials available on the market.

[0051] Among them, Table 1 is a comparison table of the alloy element composition contents of the samples of Examples 1 - 10 and Comparative Examples 1 - 3 of the present invention.

[0052] Table 1

[0053] Among them, Table 2 is a comparison table of the preparation process parameters of the samples of Examples 1 - 10 of the present invention.

[0054] Table 2

[0055] Test results Test environment: All the samples of the examples and the comparative examples are tested at room temperature (about 25 °C).

[0056] Test equipment: Standard magnetic testing devices and mechanical property testing devices are used.

[0057] Test sample size: The thickness of the sample is 1 cm - 20 cm.

[0058] Among them, the magnetic test parameters are measured as follows: Saturation magnetic induction intensity (Bs): Measured by a soft magnetic DC measuring device under a magnetic field of 1000 A / m, with the unit of tesla (T).

[0059] Initial permeability (μ): The permeability at 0.8 A / m is tested by a soft magnetic DC measuring device, and the unit is dimensionless.

[0060] Coercivity (Hc): Measured by a soft magnetic DC measuring device under a magnetic field of 1000 A / m to test the resistance of the material during demagnetization, with the unit of ampere per meter (A / m).

[0061] Loss (P): The hysteresis loss measured by a soft magnetic AC measuring device at different frequencies, with the unit of watt per kilogram (W / kg). The losses at 1 kHz / 1.7 T, 10 kHz / 1.7 T, and 100 kHz / 1.7 T are tested respectively.

[0062] The mechanical property test parameters are measured as follows: Hardness (HV): Tested by Vickers hardness test, with the unit of HV.

[0063] Tensile strength (σ): The tensile strength of the material is tested, with the unit of megapascal (MPa).

[0064] Ductility (δ): The ductility of the material, with the unit of %.

[0065] Density (ρ): The density of the material, with the unit of gram per cubic centimeter (g / cm³).

[0066] Table 3

[0067] Relevant performance tests were carried out on 10 samples of Examples 1 - 10 and 3 samples of Comparative Examples 1 - 3 (three existing products on the market), a total of 13 samples. The test comparison results of the 13 samples are shown in Table 3.

[0068] Table 3 is a summary comparison table of the magnetic properties and mechanical properties test results of the samples of Examples 1 - 10 and the samples of Comparative Examples 1 - 3.

[0069] Result analysis 1. Saturation magnetic induction intensity (Bs) As can be seen from Table 3, the saturation magnetic induction intensity of the samples in Examples 1-10 of the present invention is between 1.92 T and 1.98 T, which is significantly higher than that of the existing products, 1.85 T to 1.87 T (Samples 11-13 of Comparative Examples 1-3). This is because by adding magnesium boride compounds to the alloy and optimizing the melting process, the saturation magnetic induction intensity of the alloy material has been effectively improved. The obtained alloy material has higher magnetic properties under high magnetic field conditions, which enables the amorphous soft magnetic alloy core prepared by the present invention to perform better in high-power motors and transformer applications.

[0070] 2. Initial permeability (μ) As can be seen from Table 3, the initial permeability of the samples in Examples 1-10 of the present invention is between 75,500 and 78,500, which is significantly higher than that of the existing product samples 11-13. This is because the uniform distribution of the nanocrystalline phase and the improved stability of the composite phase obtained in the alloy material of the present invention have increased the permeability, enabling the alloy material to have good magnetic conductance performance under low magnetic fields, which helps the core to be quickly magnetized and efficiently transfer energy in low-frequency and high-frequency applications.

[0071] 3. Coercive force (Hc) As can be seen from Table 3, the coercive force of the samples in Examples 1-10 of the present invention is between 2.7 A / m and 3.0 A / m, which is significantly lower than that of the existing product samples 11-13, which is 3.4 A / m to 3.6 A / m.

[0072] Those skilled in the art know that a lower coercive force means less energy is consumed during the magnetization and demagnetization processes of the alloy material, which is crucial for improving the efficiency of the soft magnetic alloy. Therefore, the low coercive force of the alloy material of the present invention indicates higher sensitivity and controllability in magnetic properties, enabling it to be better applied to corresponding magnetic products.

[0073] 4. Loss (P) As can be seen from Table 3, the losses of the samples in Examples 1-10 of the present invention at 1 kHz / 1.7 T, 10 kHz / 1.7 T, and 100 kHz / 1.7 T are below 14 W / kg, below 27 W / kg, and below 50 W / kg respectively, all lower than those of the existing products 1-3.

[0074] This is because the low loss of the alloy material of the present invention benefits from the refined grains and nanocrystalline composite phase, which helps to reduce the hysteresis loss and eddy current loss at high frequencies. Thus, the lower high-frequency loss enables the alloy material of the present invention to perform more excellently in high-frequency transformers and inductors.

[0075] 5. Mechanical properties Hardness (HV): As can be seen from Table 3, the hardness of the samples tested in Examples 1-10 of the present invention is between 650 HV and 670 HV, which is higher than that of the existing product samples 11-13 (615 HV - 625 HV).

[0076] Tensile strength (σ): The tensile strength of the samples tested in Examples 1-10 of the present invention is between 585 MPa and 605 MPa, which is higher than that of the existing product samples 11-13 (555 MPa - 565 MPa).

[0077] Ductility (δ): The ductility of the samples tested in Examples 1-10 of the present invention is between 2.9% and 3.3%, which is higher than that of the existing product samples 11-13 (2.6% - 2.8%).

[0078] From the above data comparison, it can be seen that the higher hardness and tensile strength indicate an improvement in the wear resistance and strength of the alloy, while the ductility improves the formability of the alloy material.

[0079] Therefore, the improvement in mechanical properties makes the alloy material more advantageous in high-strength applications and the forming of iron cores with complex structures.

[0080] In summary, the alloy material and iron core prepared by the present invention are significantly superior to the existing products in terms of magnetic properties and mechanical properties, especially in terms of high saturation magnetic induction intensity, low coercivity, low high-frequency loss, high hardness and tensile strength. Therefore, these performance improvements make the amorphous soft magnetic alloy iron core of the present invention more suitable for application scenarios such as high-efficiency motors, transformers and inductors.

[0081] The above are only examples of the present invention and are not used to limit the present invention. Any modifications, equivalent replacements, improvements, etc. made within the spirit and principles of the present invention are included in the scope of the claims of the present invention pending approval.

Claims

1. An amorphous soft magnetic alloy material, characterized in that, The chemical expression of the component atoms of the alloy material is as follows: Fe a Si b Al c V d Mn e Cr f B x Mg y N h O i ; In the formula, 80 ≤ a ≤ 85, 3 ≤ b ≤ 5, 1 ≤ c ≤ 3, 0.5 ≤ d ≤ 1.5, 1 ≤ e ≤ 2, 1 ≤ f ≤ 2, 3 ≤ x ≤ 5, 0.5 ≤ y ≤ 1.5, 0.5 ≤ h ≤ 1.0, 0.1 ≤ i ≤ 0.3, and a + b + c + d + e + f + x + y + h + i = 100.

2. A method for preparing an amorphous soft magnetic alloy material, characterized in that, It includes: Configuring raw materials: Weigh the raw materials of each element according to the component ratio of the amorphous soft magnetic alloy material described in Claim 1. The elements of iron, silicon, aluminum, vanadium, manganese, and chromium in the raw materials are introduced in the form of single substances, and the remaining elements are introduced in the form of boron-magnesium compounds, nitrides, and oxides; The first-stage melting: Put the raw materials except the boron-magnesium compound into a high-frequency induction melting furnace. Under the protection of argon, heat the melting temperature to 1500°C - 1600°C, and the melting duration is 5 min - 10 min to form a primary melt; The second-stage melting: After reducing the melting temperature to 1300°C - 1400°C, add the boron-magnesium compound to the primary melt and stir for 5 min - 10 min to obtain a secondary melt; Solidification and cooling: Under argon protection, when the secondary melt stands still until it reaches a semi-solid state, the amorphous soft magnetic alloy material is formed by high-pressure water quenching or gas cooling, and the cooling rate is 10 4 K / s - 10 5 K / s.

3. The preparation method of the amorphous soft magnetic alloy material according to claim 2, characterized in that, The boron-magnesium compound is Mg2B2O5, and the boron-magnesium compound is added as a reaction substance in the second-stage melting.

4. The preparation method of the amorphous soft magnetic alloy material according to claim 2, characterized in that, The addition amount of the boron-magnesium compound is 0.1% - 0.3% of the total mass of the raw materials.

5. The preparation method of the amorphous soft magnetic alloy material according to claim 2, characterized in that, The nitride is AlN; the oxide is at least one of B2O3 and Al2O3.

6. A method for preparing an amorphous soft magnetic alloy core, characterized in that, The preparation method includes the following steps: Grinding treatment: Take the alloy block of the amorphous soft magnetic alloy material described in Claim 1 and mechanically grind it into amorphous particles in a cooling environment, and use deionized water to wash the amorphous particles to remove surface impurities and oxides; Pre-pressing and forming: Load the washed amorphous particles into a mold and perform pre-pressing under heating conditions to obtain a pre-pressed alloy sheet; Densification treatment: Subject the pre-pressed alloy sheet to hot isostatic pressing to form a dense alloy sheet; Rolling and stacking treatment: Fine-roll the dense alloy sheet in a rolling mill to obtain a rolled alloy sheet, cut the rolled alloy sheet and stack and fix it to form a laminated sheet; Annealing treatment: Spray-anneal the laminated sheet in a high-frequency magnetic field; Surface treatment and assembly: After ultrasonic polishing the surface of the annealed laminated sheet, coat an insulating layer on the surface of the laminated sheet, and then assemble the laminated sheet into an amorphous soft magnetic alloy iron core.

7. The preparation method of the amorphous soft magnetic alloy iron core according to claim 6, characterized in that, In the grinding treatment, the particle size of the amorphous particles is less than 20 μm.

8. The preparation method of the amorphous soft magnetic alloy iron core according to claim 6, characterized in that, In the grinding treatment, the temperature of the cooling environment does not exceed -40°C.

9. The method for preparing the amorphous soft magnetic alloy iron core according to claim 6, wherein, In the pre-pressing and forming, the hot pressing temperature of the pre-pressing and forming is 400°C - 600°C, and the hot pressing pressure is 3000 MPa - 5000 MPa.

10. The preparation method of the amorphous soft magnetic alloy iron core according to claim 6, characterized in that, In the pre-pressing and forming, the thickness of the pre-pressed alloy sheet is 0.03 mm - 0.04 mm.

11. The preparation method of the amorphous soft magnetic alloy iron core according to claim 6, characterized in that, In the densification treatment, the temperature of the hot isostatic pressing is 500°C - 600°C, the pressure of the hot isostatic pressing is 80 MPa - 120 MPa, and the holding time of the hot isostatic pressing is 20 min - 30 min.

12. The preparation method of the amorphous soft magnetic alloy iron core according to claim 6, wherein, In the rolling and stacking process, the thickness of the rolled alloy sheet is 0.01 mm - 0.014 mm, and the thickness of the stacked sheet is 1 cm - 20 cm.

13. The preparation method of the amorphous soft magnetic alloy iron core according to claim 6, characterized in that, In the annealing process, the magnetic field strength is 50 mT - 200 mT, the annealing temperature is 250 °C - 450 °C, and the annealing time is 1 h - 2 h.

14. The preparation method of the amorphous soft magnetic alloy iron core according to claim 6, characterized in that, In the surface treatment and assembly, the ultrasonic frequency is 20 kHz - 40 kHz, and the polishing time is 10 min - 20 min.

15. An amorphous soft magnetic alloy core, characterized in that, The iron core is made by the preparation method of the amorphous soft magnetic alloy iron core according to any one of claims 6 - 14.

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