Fe-sc-m bulk amorphous alloy with high glass forming ability, and preparation method and application thereof

Abstract

This invention discloses a Fe-Sc-M bulk amorphous alloy with high glass-forming ability, its preparation method, and its applications, relating to the field of metallic materials. The atomic percentage expression for the bulk amorphous alloy is: Fe 91 Sc7M2, where M is Ti or B, can be applied in the field of magnetic materials. This invention optimizes the glass-forming ability of the Fe-Sc bulk amorphous alloy system by adding Ti or B, obtaining a Fe-based amorphous alloy with high glass-forming ability and excellent soft magnetization properties. The magnetization of this amorphous alloy increases sharply with increasing magnetic field at low magnetic fields and then gradually reaches saturation, indicating that this alloy system exhibits typical soft magnetic properties. It can be used to fabricate magnetic devices with complex shapes, and the fabrication method is simple and easy to implement, giving it broad application potential in the field of magnetic materials.

Description

Technical Field

[0001] This invention relates to the field of metallic materials, and more particularly to a Fe-Sc-M bulk amorphous alloy with high glass-forming ability, its preparation method, and its applications. Background Technology

[0002] In recent years, iron-based amorphous alloys have attracted increasing attention from researchers due to their high strength, excellent corrosion resistance, and good soft magnetic properties. However, iron-based alloys have low amorphous forming ability and require very high cooling rates during the cooling process, resulting in samples that are typically filamentous or thin strips. As soft magnetic materials, iron-based amorphous alloy strips have been applied in the field of magnetic materials; however, compared with La-based, Zr-based, Pd-based, and Mg-based bulk amorphous alloys, the preparation of iron-based bulk amorphous alloys is more difficult.

[0003] In practical applications, the gaps between iron-based amorphous alloy strips reduce the saturation magnetization, thus lowering transformer efficiency. Furthermore, due to size limitations, it is difficult to fabricate complex-shaped magnetic devices using iron-based amorphous alloys, significantly restricting their applications. Therefore, there is an urgent need to find iron-based bulk amorphous alloys with greater glass-forming capabilities. Summary of the Invention

[0004] This invention provides a Fe-Sc-M bulk amorphous alloy with high glass-forming ability, its preparation method, and its application, to provide Fe-based bulk amorphous alloys with excellent glass-forming ability and thermal stability, and excellent soft magnetic properties.

[0005] To address the aforementioned technical problems, one objective of this invention is to provide a Fe-Sc-M bulk amorphous alloy with high glass-forming ability, wherein the atomic percentage expression of the bulk amorphous alloy is: Fe 91 Sc7M2, where M is Ti or B.

[0006] As a preferred embodiment, the atomic percentage expression of the bulk amorphous alloy is: Fe 91 Sc7Ti2.

[0007] As a preferred embodiment, the atomic percentage expression of the bulk amorphous alloy is: Fe 91 Sc7B2.

[0008] As a preferred embodiment, the thickness of the bulk amorphous alloy is less than or equal to 35 μm.

[0009] As a preferred embodiment, the bulk amorphous alloy has an amorphous structure.

[0010] To address the aforementioned technical problems, a second objective of this invention is to provide a method for preparing a Fe-Sc-M bulk amorphous alloy with high glass-forming ability, comprising the following steps:

[0011] (1) Weigh each metal element raw material according to the stoichiometric ratio of the block amorphous alloy, place them in the crucible in the order of lower melting point at the bottom and higher melting point at the top, evacuate the vacuum and introduce argon gas to reach -0.08-0.03 MPa, melt to form an alloy ingot, cool and flip the alloy ingot, repeat the melting 5-10 times to obtain the alloy ingot.

[0012] (2) Place the alloy ingot in the crucible of the gating system, evacuate the vacuum and introduce argon gas to 350-400 mbar, completely melt the alloy ingot and pour it into the mold, and cool and shape it.

[0013] As a preferred embodiment, in steps (1) and (2), the vacuum is evacuated to 3.5 × 10⁻⁶. -3 -5×10 -3 Pa.

[0014] As a preferred embodiment, in step (2), the alloy ingot is first melted at a current of 200-300A, and then completely melted at a current of 400-500A.

[0015] As a preferred option, in step (1), each elemental raw material is ultrasonically cleaned in petroleum ether and anhydrous ethanol in sequence before use.

[0016] To address the aforementioned technical problems, a third objective of this invention is to provide an application of a Fe-Sc-M bulk amorphous alloy with high glass-forming ability in the preparation of magnetic materials.

[0017] Compared with the prior art, the embodiments of the present invention have the following beneficial effects:

[0018] 1. This invention optimizes the glass-forming ability of Fe-Sc bulk amorphous alloys by adding Ti or B, thereby obtaining Fe-based amorphous alloys with high glass-forming ability and excellent soft magnetization performance. The magnetization of this amorphous alloy increases sharply with the increase of magnetic field under low magnetic field and then gradually reaches saturation, indicating that this alloy system exhibits typical soft magnetic properties. It can be used to fabricate magnetic devices with complex shapes. The fabrication method is simple and easy to implement, and it has broad application prospects in the field of magnetic materials.

[0019] 2. This application controls the appropriate content of Ti or B elements in amorphous materials. If the x value is too large or too small, it will cause the glass-forming ability of the amorphous alloy to change, making it difficult to form an amorphous structure. Attached Figure Description

[0020] Figure 1 : Fe in Embodiments 1-2 of the present invention91 Sc7Ti2 and Fe 91 X-ray diffraction image of Sc7B2 bulk amorphous alloy;

[0021] Figure 2 : Fe in Comparative Examples 1-3 of this invention 89 Sc 11 Fe 90 Sc 10 and Fe 91 X-ray diffraction image of Sc9 bulk amorphous alloy;

[0022] Figure 3 : Fe in Embodiment 1 of the present invention 91 Saturation magnetization curve of Sc7Ti2 bulk amorphous alloy;

[0023] Figure 4 : Fe in Embodiment 2 of the present invention 91 Saturation magnetization curve of Sc7B2 bulk amorphous alloy;

[0024] Figure 5 : Fe in Embodiment 1 of the present invention 91 DSC curves of Sc7Ti2 bulk amorphous alloy;

[0025] Figure 6 : Fe in Embodiment 2 of the present invention 91 DSC curves of Sc7B2 bulk amorphous alloy;

[0026] Figure 7 : Fe in Comparative Examples 1-3 of this invention 89 Sc 11 Fe 90 Sc 10 and Fe 91 DSC curves of Sc9 bulk amorphous alloy. Detailed Implementation

[0027] The technical solutions of the embodiments of the present invention will be clearly and completely described below with reference to the accompanying drawings. Obviously, the described embodiments are only some embodiments of the present invention, and not all embodiments. Based on the embodiments of the present invention, all other embodiments obtained by those skilled in the art without creative effort are within the scope of protection of the present invention.

[0028] Example 1

[0029] A Fe-Sc-M bulk amorphous alloy with high glass-forming ability, its atomic percentage expression is: Fe 91 The Sc7Ti2 material, with a thickness of 35 μm, was prepared using the following steps:

[0030] (1) Using Fe, Sc, and Ti metal elements with a purity of not less than 99.9% as raw materials, the raw materials are converted into mass percentages according to the atomic percentage expression of the alloy composition;

[0031] (2) Place the raw materials of each element in a copper crucible in the order of lowest melting point to highest melting point, and evacuate the vessel to a vacuum level of 3.5 × 10⁻⁶. -3 Pa, then introduce high-purity argon gas with a purity of 99.99wt% as a protective gas until the pressure inside the furnace reaches -0.08Mpa and stop the gas supply. The raw materials are then smelted at a smelting current of 450A. After all the materials are melted to form an alloy ingot, the ingot is cooled and flipped over. The ingot is then smelted again and the magnetic stirring is turned on. The smelting process is repeated 6 times to obtain an alloy ingot.

[0032] (3) Place the alloy ingot in the copper crucible of the gating system, and place a 2mm diameter copper mold below it. Evacuate the furnace cavity to 3.5×10⁻⁶. -3 After Pa, high-purity argon gas is introduced to 400 mbar. First, the ingot is melted at a current of 200 A, and then the alloy ingot is completely melted at a current of 500 A. The copper crucible is turned over so that it flows into a copper mold and is cooled and shaped to obtain Fe-Sc-M blocky amorphous alloy.

[0033] Example 2

[0034] A Fe-Sc-M bulk amorphous alloy with high glass-forming ability is prepared using the same steps, reagents, and process parameters as in Example 1, except that its atomic percentage expression is Fe. 91 Sc7B2, with a thickness of 35μm.

[0035] Comparative Example 1

[0036] A Fe-Sc bulk amorphous alloy with high glass-forming ability is prepared using the same steps, reagents, and process parameters as in Example 1, except that its atomic percentage expression is Fe. 89 Sc 11 The thickness is 35μm.

[0037] Comparative Example 2

[0038] A Fe-Sc bulk amorphous alloy with high glass-forming ability is prepared using the same steps, reagents, and process parameters as in Example 1, except that its atomic percentage expression is Fe. 90 Sc 10 The thickness is 35μm.

[0039] Comparative Example 3

[0040] A Fe-Sc bulk amorphous alloy with high glass-forming ability is prepared using the same steps, reagents, and process parameters as in Example 1, except that its atomic percentage expression is Fe. 91 Sc9, with a thickness of 35μm.

[0041] Performance testing

[0042] The coercivity and saturation magnetization of the 35 μm thick cast alloys from Examples 1-2 and Comparative Examples 1-3 were tested using a vibrating sample magnetometer (VSM). The vibration of the sample in the coil induces an alternating signal in the detection coil. This alternating voltage is proportional to the magnetic moment of the sample. The coercivity and saturation magnetization results were obtained by analyzing the hysteresis loop measured by the VSM. The test results are shown in Table 1. The saturation magnetization test results of Example 1 are as follows: Figure 3 As shown, the saturation magnetization detection results of Example 2 are as follows: Figure 4 As shown. Simultaneously, the glass transition temperature Tg and crystallization temperature Tx were obtained through DSC experiments. The DSC curve for Example 1 is shown below. Figure 5 As shown, the DSC curve of Example 2 is as follows: Figure 6 As shown, the DSC curves of Comparative Examples 1-3 are as follows: Figure 7 As shown.

[0043] Table 1 - Performance indicators of as-cast alloys in Examples 1-2 and Comparative Examples 1-3

[0044]

[0045] See Figure 1 As shown, the Fe-Sc-M as-cast alloys with a thickness of 35 μm prepared in Examples 1-2 of this application are amorphous structures.

[0046] As shown in Table 1, in Examples 1-2 of this application, the saturation magnetization of the samples showed a single change with different doping elements, exhibiting a decreasing trend. In Example 1, the addition of Ti to the Fe-Sc alloy system significantly altered the soft magnetic properties of the final alloy sample, with a marked increase in saturation magnetization, thus improving the soft magnetic properties. In Example 2, the addition of B to the Fe-Sc alloy system also significantly altered the soft magnetic properties of the final alloy sample, with an increase in saturation magnetization, further enhancing the soft magnetic properties. The saturation magnetization and permeability in Examples 1-2 were both higher than those in Comparative Examples 1-3, indicating that the examples exhibited superior soft magnetic properties compared to the comparative examples.

[0047] See Figure 5-6As shown in the DSC curves, the as-cast alloys of Examples 1-2 of the present invention have a wide supercooled liquid phase region, thus exhibiting high thermal stability and glass-forming ability.

[0048] See Figure 3-4 As shown, the magnetization of the amorphous alloys in Examples 1-2 increases sharply with the increase of the magnetic field under low magnetic field and then gradually reaches saturation, indicating that this alloy system exhibits typical soft magnetic properties.

[0049] The specific embodiments described above further illustrate the purpose, technical solution, and beneficial effects of the present invention. It should be understood that the above descriptions are merely specific embodiments of the present invention and are not intended to limit the scope of protection of the present invention. In particular, it should be noted that any modifications, equivalent substitutions, improvements, etc., made within the spirit and principles of the present invention should be included within the scope of protection of the present invention for those skilled in the art.

Claims

1. A Fe-Sc-M bulk amorphous alloy with high glass-forming ability, characterized in that, The atomic percentage expression for the bulk amorphous alloy is: Fe 91 Sc7Ti2.

2. The Fe-Sc-M bulk amorphous alloy with high glass-forming ability as described in claim 1, characterized in that, The thickness of the bulk amorphous alloy is less than or equal to 35 μm.

3. The Fe-Sc-M bulk amorphous alloy with high glass-forming ability as described in claim 1, characterized in that, The bulk amorphous alloy has an amorphous structure.

4. A method for preparing a Fe-Sc-M bulk amorphous alloy with high glass-forming ability as described in any one of claims 1-3, characterized in that, Includes the following steps: (1) Weigh each metal element raw material according to the stoichiometric ratio of the block amorphous alloy, place them in the crucible in the order of lower melting point at the bottom and higher melting point at the top, evacuate the vacuum and introduce argon gas to reach -0.08-0.03 MPa, melt to form an alloy ingot, cool and flip the alloy ingot, repeat the melting 5-10 times to obtain the alloy ingot. (2) Place the alloy ingot in the crucible of the gating system, evacuate the vacuum and introduce argon gas to 350-400 mbar, completely melt the alloy ingot and pour it into the mold, and cool and shape it.

5. The method for preparing a Fe-Sc-M bulk amorphous alloy with high glass-forming ability as described in claim 4, characterized in that, In steps (1) and (2), a vacuum is drawn to 3.5 × 10⁻⁶. -3 -5×10 -3 Pa.

6. The method for preparing a Fe-Sc-M bulk amorphous alloy with high glass-forming ability as described in claim 4, characterized in that, In step (2), the alloy ingot is first melted at a current of 200-300A, and then completely melted at a current of 400-500A.

7. The application of a Fe-Sc-M bulk amorphous alloy with high glass-forming ability as described in any one of claims 1-3 in the field of magnetic material preparation.

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