CN117286430A - Low-permeability amorphous alloy and preparation method and application thereof - Google Patents
Low-permeability amorphous alloy and preparation method and application thereof Download PDFInfo
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- 229910000808 amorphous metal alloy Inorganic materials 0.000 title claims abstract description 56
- 238000002360 preparation method Methods 0.000 title abstract description 8
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims abstract description 105
- 230000005291 magnetic effect Effects 0.000 claims abstract description 94
- 239000000956 alloy Substances 0.000 claims abstract description 85
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 84
- 229910052742 iron Inorganic materials 0.000 claims abstract description 48
- 238000010438 heat treatment Methods 0.000 claims abstract description 40
- 238000001816 cooling Methods 0.000 claims abstract description 14
- 238000009826 distribution Methods 0.000 claims abstract description 9
- 229910052759 nickel Inorganic materials 0.000 claims abstract description 8
- 230000035699 permeability Effects 0.000 claims description 41
- 238000004321 preservation Methods 0.000 claims description 18
- 238000010791 quenching Methods 0.000 claims description 12
- 230000000171 quenching effect Effects 0.000 claims description 11
- 238000003723 Smelting Methods 0.000 claims description 6
- 238000000034 method Methods 0.000 claims description 5
- 238000010079 rubber tapping Methods 0.000 claims description 4
- 230000008569 process Effects 0.000 claims description 3
- 238000004519 manufacturing process Methods 0.000 claims description 2
- 239000000203 mixture Substances 0.000 claims 1
- 238000005516 engineering process Methods 0.000 abstract description 11
- 239000010949 copper Substances 0.000 description 9
- 239000000463 material Substances 0.000 description 7
- 230000000052 comparative effect Effects 0.000 description 6
- 229910052802 copper Inorganic materials 0.000 description 6
- 229910001004 magnetic alloy Inorganic materials 0.000 description 6
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 5
- 229910000976 Electrical steel Inorganic materials 0.000 description 5
- 238000007599 discharging Methods 0.000 description 5
- 230000005294 ferromagnetic effect Effects 0.000 description 5
- 238000012360 testing method Methods 0.000 description 4
- 238000007792 addition Methods 0.000 description 3
- 230000006698 induction Effects 0.000 description 3
- 239000000696 magnetic material Substances 0.000 description 3
- 239000002184 metal Substances 0.000 description 3
- 229910052751 metal Inorganic materials 0.000 description 3
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 2
- 230000001808 coupling effect Effects 0.000 description 2
- 239000013078 crystal Substances 0.000 description 2
- 238000011161 development Methods 0.000 description 2
- 238000004134 energy conservation Methods 0.000 description 2
- 238000011534 incubation Methods 0.000 description 2
- 230000005389 magnetism Effects 0.000 description 2
- 230000005298 paramagnetic effect Effects 0.000 description 2
- 238000007711 solidification Methods 0.000 description 2
- 230000008023 solidification Effects 0.000 description 2
- 229910008423 Si—B Inorganic materials 0.000 description 1
- 238000002441 X-ray diffraction Methods 0.000 description 1
- 238000004458 analytical method Methods 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 238000006243 chemical reaction Methods 0.000 description 1
- 238000001514 detection method Methods 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- 230000002349 favourable effect Effects 0.000 description 1
- 239000012535 impurity Substances 0.000 description 1
- 229910000697 metglas Inorganic materials 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 229910052757 nitrogen Inorganic materials 0.000 description 1
- 238000011056 performance test Methods 0.000 description 1
- 239000002243 precursor Substances 0.000 description 1
- 229920006395 saturated elastomer Polymers 0.000 description 1
- 239000007787 solid Substances 0.000 description 1
- 238000006467 substitution reaction Methods 0.000 description 1
- 230000009466 transformation Effects 0.000 description 1
- 229910052727 yttrium Inorganic materials 0.000 description 1
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C45/00—Amorphous alloys
- C22C45/02—Amorphous alloys with iron as the major constituent
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/04—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering with simultaneous application of supersonic waves, magnetic or electric fields
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/52—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C33/00—Making ferrous alloys
- C22C33/003—Making ferrous alloys making amorphous alloys
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- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
- H01F1/00—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties
- H01F1/01—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials
- H01F1/03—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity
- H01F1/12—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials
- H01F1/14—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials metals or alloys
- H01F1/147—Alloys characterised by their composition
- H01F1/153—Amorphous metallic alloys, e.g. glassy metals
- H01F1/15308—Amorphous metallic alloys, e.g. glassy metals based on Fe/Ni
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- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
- H01F1/00—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties
- H01F1/01—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials
- H01F1/03—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity
- H01F1/12—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials
- H01F1/14—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials metals or alloys
- H01F1/147—Alloys characterised by their composition
- H01F1/153—Amorphous metallic alloys, e.g. glassy metals
- H01F1/15341—Preparation processes therefor
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2201/00—Treatment for obtaining particular effects
- C21D2201/03—Amorphous or microcrystalline structure
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Abstract
The invention discloses a low-permeability amorphous alloy which is characterized by being formed by heat treatment of an iron-based alloy disordered structure strip through a segmented magnetic field, wherein the alloy component of the iron-based alloy disordered structure strip is Fe-Si-B-M, and M is one or more of C, co, nb, mn, cu and Ni. The invention reduces the quasi dislocation dipole density of the alloy through the combination technologies of alloy components, sectional magnetic field adding, sectional temperature reducing, rapid cooling and the like, improves the structural disorder, effectively releases the internal stress, and combines the uniform magnetic anisotropy induced by the sectional magnetic field, thereby realizing the low magnetic conductivity and low loss of the amorphous alloy. The invention also discloses a preparation method of the low-permeability amorphous alloy and application of the low-permeability amorphous alloy to a hybrid magnetic circuit distribution transformer.
Description
Technical Field
The invention belongs to the technical field of soft magnetic alloy materials, and particularly relates to a low-permeability amorphous alloy, a preparation method and application thereof.
Background
Compared with the traditional soft magnetic material, the amorphous soft magnetic alloy is prepared by adopting a super quenching solidification technology with the cooling speed of about one million degrees per second. Because of super-quenching solidification, atoms are not ordered and crystallized when the alloy is solidified, the obtained solid alloy has a long-range disordered structure, and crystal grains and crystal boundaries of crystalline alloy are not present, so that the amorphous soft magnetic alloy has excellent performances of higher saturated magnetic induction intensity, low coercivity and the like, and has the characteristics of energy conservation in the manufacturing process and energy conservation in the using process. The amorphous soft magnetic alloy can provide an effective solution for improving the conversion efficiency of the transformer and reducing the loss. Therefore, the development and application of the amorphous soft magnetic material have important significance in developing novel power electronic equipment such as environment-friendly, energy-saving and efficient transformers, sensors and the like.
The outstanding soft magnetic performance of the amorphous alloy brings remarkable energy-saving effect to the transformer, and the no-load loss of the amorphous energy-saving transformer is about 70-80% lower than that of silicon steel. The American Allied company (Metglas corporation precursor) developed Fe-Si-B alloy in the 60 s, which was the earliest industrialized amorphous alloy with a saturation magnetic density of 1.56T, which was significantly lower than the Fe-Si-B-C (HB 1M) amorphous alloy with a saturation magnetic density of 1.64T proposed by Japanese Hitachi Metal (Hatchi Metal) in 2006. The noise and loss of devices made with the HB1M New alloy developed by Hitachi Metal Co were reduced and the device volume was reduced by 10%. However, the magnetic permeability of the common amorphous alloy is about 5 times that of oriented silicon steel at the magnetic saturation point, and the two materials cannot be matched when combined in the application of the hybrid magnetic circuit core transformer, so that development and application of the low-loss and low-magnetic permeability amorphous alloy for realizing the distribution transformer with the advantages of both the magnetic properties of the amorphous alloy and the silicon steel are needed.
CN201910772826.2 discloses an iron-based amorphous alloy with high saturation induction density and a preparation method, wherein the critical thickness of the strip of the amorphous alloy is more than or equal to 40 μm; the saturation induction intensity of the alloy strip sample is more than or equal to 1.65T; the coercive force of the alloy strip sample is less than or equal to 5A/m. However, the magnetic permeability of the amorphous alloy is high.
CN201910061888.2 discloses a high Bs amorphous material and a preparation method thereof, wherein the typical component of the amorphous strip is Fe x Si y B z Wherein x=75-80%Y=10-15%, z=7-10%; and sequentially carrying out first heat treatment and second heat treatment on the amorphous strip under the condition of nitrogen protection, wherein the first heat treatment specifically comprises the following steps: heating the amorphous strip from room temperature to 300-330 ℃ according to the heating rate of 5-20 ℃/min, and preserving heat for 20-40min; the second heat treatment specifically comprises the following steps: heating the amorphous strip subjected to the first heat treatment from 300-330 ℃ to 380-430 ℃ according to the heating rate of 5-20 ℃/min, and preserving heat for 90-120min; and cooling the amorphous strip after the second heat treatment to obtain the high-Bs amorphous material. However, the coercive force of the amorphous alloy is as high as 42A/m, which is not favorable for energy saving of the transformer.
Therefore, there is a need to develop an amorphous alloy having low loss, low magnetic permeability, good amorphous forming ability and manufacturability.
Disclosure of Invention
The invention provides a low-permeability amorphous alloy with lower permeability and lower loss.
The invention provides a low-permeability amorphous alloy which is formed by heat treatment of an iron-based alloy disordered structure strip through a segmented magnetic field, wherein the alloy component of the iron-based alloy disordered structure strip is one or more of Fe-Si-B-M, and M is C, co, nb, mn, cu and Ni.
Further, the alloy component of the strip with the disordered iron-based alloy structure is Fe a Si b B c C d Co e A is 78-82,4-b is 11-c is 13-d is 0-d is 1-e 2-a+b+c+d+e=100.
Further, the alloy component of the iron-based alloy amorphous strip is Fe x Si 13 B 8 Nb 2 Mn 2 Cu 1 R y And x is 64-72,2-y is 10, R is Co or Ni.
Further, the process of the segmented magnetic field heat treatment comprises the following steps: first stage magnetic field heat treatment temperature T 1 Is T c -50℃≤T 1 ＜T c ，T c Is amorphous Curie temperature, and the heat preservation time is t 1 At t 1 Vertical within timeApplying a magnetic field F1 in the direction of the strip with the disordered structure of the iron-based alloy; second stage magnetic field heat treatment temperature T 2 Is T c ≤T 2 ≤T c The temperature is +120 ℃, the heat preservation time is t 2 At t 2 The magnetic field F2 is applied in a direction perpendicular to the strip of the disordered structure of the iron-based alloy in time, and then the strip is rapidly cooled to the tapping temperature.
The Fe, co and Ni provided by the invention are ferromagnetic elements, the addition of Co and Ni can increase the ferromagnetic coupling effect of the alloy, improve the magnetic moment and magnetocrystalline anisotropy, and the addition of atoms C, nb, mn and Cu can improve the atomic mismatching ratio and the mixed entropy of the alloy and increase the disorder of an alloy system. The reason for applying a magnetic field perpendicular to the direction of the unordered structural strip at a temperature lower than the amorphous curie temperature is that the amorphous phase is ferromagnetic, the magnetic moment direction is ordered, and the ferromagnetic coupling action of ferromagnetic elements Fe, co and Ni is combined to induce uniform magnetic anisotropy perpendicular to the direction of the unordered structural strip and promote stress relaxation and stress release. However, too large a uniform magnetic anisotropy reduces permeability but increases loss. The magnetic field heat treatment is carried out at a temperature higher than the amorphous Curie temperature, at this time, the amorphous phase of the strip with the disordered structure of the iron-based alloy is paramagnetic phase, the magnetic moment direction is disordered and disordered, and the application of the magnetic field F2 in the direction perpendicular to the strip with the disordered structure of the iron-based alloy can induce relatively weak uniform magnetic anisotropy, so that low loss and low magnetic permeability are cooperatively realized.
Further, the amorphous Curie temperature T c Is 290-340 ℃.
Further, the heat preservation time t 1 The magnetic field strength of the magnetic field F1 is 80Oe-800Oe within 10min-180 min.
At t 1 The amorphous alloy provided by the invention has lower magnetism and lower loss, and if the magnetic field strength is too high or the magnetic field is applied for too long, the uniform magnetic anisotropy is too high, so that the loss is too high.
Further, the method comprises the steps of,time t of incubation 2 The magnetic field strength of the magnetic field F2 is 160Oe-4500Oe within 10min-80 min.
At t 2 And applying proper magnetic field intensity in a direction perpendicular to the disordered structure strip in time, so that under the condition that the amorphous phase of the disordered structure strip of the iron-based alloy is paramagnetic phase, relatively weak uniform magnetic anisotropy is induced by externally applying a magnetic field with proper magnetic field intensity, and the amorphous alloy provided by the invention has lower magnetism and lower loss.
Further, the rapid cooling rate is 100 ℃/min to 1500 ℃/min. The transformation of the amorphous structure formed with uniform magnetic anisotropy is limited by rapid cooling, so that the amorphous structure upon application of the magnetic field F2 is maintained.
Further, the low permeability amorphous alloy has a loss of less than 0.14W/kg, preferably less than 0.1W/kg, at 1.3T,50 Hz.
Furthermore, the magnetic permeability of the low-magnetic-permeability amorphous alloy is kept constant under the condition of 50Hz-100kHz, and is smaller than 8000. Further preferably, the low permeability amorphous alloy has a permeability of 6000 to 7500 at 50Hz to 100 kHz.
Further, the low permeability amorphous alloy also includes unavoidable impurities.
The invention also provides a preparation method of the low-permeability amorphous alloy, which comprises the following steps:
(1) Preparing materials and smelting according to alloy components of the iron-based alloy strip with the disordered structure to obtain a master alloy, and rapidly quenching the master alloy with a single roller to obtain the iron-based alloy strip with the disordered structure;
(2) Heating the strip with the disordered iron-based alloy structure to the first-stage magnetic field heat treatment temperature T 1 Lower heat preservation t 1 Wherein T is c -50℃≤T 1 ＜T c ，T c Is amorphous Curie temperature, at t 1 Applying a magnetic field F1 in a direction perpendicular to the strip with a disordered structure in time, and then heating to a second-stage magnetic field heat treatment temperature T 2 Lower heat preservation t 2 Wherein T is c ≤T 2 ≤T c +120℃, at t 2 Time-lapse saggingAnd (3) applying a magnetic field F2 in the direction of the strip with the disordered structure of the iron-based alloy, and then rapidly cooling to the tapping temperature to obtain the low-permeability amorphous alloy.
The invention also provides application of the low-permeability amorphous alloy to a hybrid magnetic circuit distribution transformer. The low-permeability amorphous alloy provided by the invention is applied to a hybrid magnetic circuit distribution transformer, and the uniformity of the hybrid magnetic circuit structure can be improved due to the fact that the permeability of the low-permeability amorphous alloy is similar to that of silicon steel, so that the overall performance loss of the hybrid magnetic circuit distribution transformer is reduced, and the energy efficiency of the hybrid magnetic circuit distribution transformer is improved.
Compared with the prior art, the invention has the beneficial effects that:
(1) The invention reduces the quasi dislocation dipole density of the alloy through the combination technologies of alloy components, sectional magnetic field adding, sectional temperature reducing, rapid cooling and the like, improves the structural disorder, effectively releases the internal stress, and combines the uniform magnetic anisotropy induced by the sectional magnetic field, thereby realizing the low magnetic conductivity and low loss of the amorphous alloy.
(2) The preparation method can reduce the loss and the magnetic permeability of the amorphous alloy, and the loss is less than 0.14W/kg, even less than 0.1W/kg under the conditions of 1.3T and 50 Hz. The magnetic permeability is less than 8000 under the condition of 50 Hz. The magnetic permeability is kept constant at 50Hz-100kHz and is smaller than 8000. Meanwhile, the amorphous soft magnetic alloy has good toughness, so that the prepared amorphous soft magnetic alloy has excellent comprehensive performance, and can widen the product market and application prospect of amorphous soft magnetic materials.
Drawings
FIG. 1 is an XRD pattern of disordered structured strips prepared in examples 1, 2, 3, and 4 of the present invention;
fig. 2 is a graph showing the magnetic permeability of the low magnetic permeability amorphous alloy according to example 1 of the present invention.
Detailed Description
The present invention will be described in further detail with reference to the following examples and drawings, and it should be noted that the following examples are intended to facilitate the understanding of the present invention and are not to be construed as limiting in any way.
Example 1
(1) This example is according to formula Fe 70 Si 13 B 8 Nb 2 Mn 2 Cu 1 Co 4 And (3) preparing materials, smelting the alloy to obtain master alloy, and preparing the master alloy into the strip with the disordered iron-based alloy structure by a single-roller rapid quenching technology, wherein the rotating speed of a copper roller is 35m/s. The microstructure of the strip prepared by the rapid quenching technology is detected by adopting a D8 advanced type polycrystalline X-ray diffractometer (XRD), the result is shown in figure 1, and the strip with the disordered structure of the iron-based alloy is shown in figure 1 to be of an amorphous structure.
(2) Placing the strip with the disordered iron-based alloy structure in a furnace, heating to 290 ℃, preserving heat for 30min, and applying a magnetic field of 800Oe in the direction perpendicular to the strip with the disordered iron-based alloy structure during the heat preservation; then heating to 460 ℃ and preserving heat for 30min, and applying a magnetic field of 800Oe in the direction vertical to the strip of the disordered iron-based alloy structure during the heat preservation; and then rapidly cooling to 120 ℃ and discharging.
Example 2
(1) This example is according to formula Fe 72 Si 13 B 8 Nb 2 Mn 2 Cu 1 Ni 2 And (3) burdening and smelting to obtain a master alloy, and preparing the master alloy into the strip with the disordered iron-based alloy structure by a single-roller rapid quenching technology, wherein the rotating speed of a copper roller is 35m/s. The microstructure of the strip with the disordered iron-based alloy structure prepared by adopting the D8 advanced polycrystalline X-ray diffractometer (XRD) detection and rapid quenching technology is shown in the figure 1, and the result is shown in the figure 1, wherein the strip with the disordered iron-based alloy structure is in an amorphous structure.
(2) Placing the strip with the disordered iron-based alloy structure in a furnace, heating to 280 ℃, preserving heat for 30min, and applying a magnetic field of 80Oe in the direction perpendicular to the strip with the disordered iron-based alloy structure during the heat preservation; then heating to 440 ℃ and preserving heat for 40min, and applying a magnetic field of 800Oe in the direction vertical to the strip of the disordered iron-based alloy structure during the heat preservation; and then rapidly cooling to 120 ℃ and discharging.
Example 3
(1) This example is according to formula Fe 81 Si 4 B 13 C 1 Co 1 And (3) burdening and smelting to obtain a master alloy, and preparing the master alloy into the strip with the disordered iron-based alloy structure by a single-roller rapid quenching technology, wherein the rotating speed of a copper roller is 35m/s. By usingD8 The microstructure of the strip prepared by the rapid quenching technology is detected by an advanced type polycrystalline X-ray diffractometer (XRD), and the result is shown in figure 1, wherein the strip with the disordered structure of the iron-based alloy is shown in figure 1 to be in an amorphous structure.
(2) Placing the strip with the disordered iron-based alloy structure in a furnace, heating to 270 ℃, preserving heat for 30min, and applying a magnetic field of 100Oe in the direction perpendicular to the strip with the disordered iron-based alloy structure during the heat preservation; then heating to 390 ℃ and preserving heat for 30min, and applying a magnetic field of 1000Oe in the direction perpendicular to the strip during the heat preservation; and then rapidly cooling to 120 ℃ and discharging.
Example 4
(1) This example is according to formula Fe 82 Si 4 B 13 C 1 And (3) burdening and smelting to obtain a master alloy, and preparing the master alloy into the strip with the disordered iron-based alloy structure by a single-roller rapid quenching technology, wherein the rotating speed of a copper roller is 35m/s. The microstructure of the strip prepared by the rapid quenching technology is detected by adopting a D8 advanced type polycrystalline X-ray diffractometer (XRD), the result is shown in figure 1, and the strip with the disordered structure of the iron-based alloy is shown in figure 1 to be of an amorphous structure.
(2) Placing the strip with the disordered iron-based alloy structure in a furnace, heating to 260 ℃, preserving heat for 30min, and applying a magnetic field of 80Oe in the direction perpendicular to the strip with the disordered iron-based alloy structure during the heat preservation; then heating to 380 ℃ and preserving heat for 30min, and applying a magnetic field of 800Oe in the direction perpendicular to the strip material during the heat preservation; and then rapidly cooling to 120 ℃ and discharging.
Example 5
Unlike example 4, in step (2), the unordered structural strip of iron-based alloy was placed in a furnace, heated to 260 ℃ and held for 120min, during which a magnetic field of 80Oe was applied perpendicular to the direction of the unordered structural strip; then heating to 380 ℃ and preserving heat for 30min, and applying a magnetic field of 800Oe in the direction perpendicular to the strip material during the heat preservation; and then rapidly cooling to 120 ℃ and discharging.
Comparative example 1
The difference compared to example 1 is that no magnetic field is applied during the incubation. The amorphous alloy samples prepared in example 1 and comparative example 1 above were subjected to the following test:
the loss test using an AC B-H meter showed that the loss of the sample after heat treatment of example 1 was 1.18W/kg at 1.3T and 50Hz, which was far lower than the loss of the alloy sample after heat treatment of comparative example 1 by 2W/kg.
The loss test was performed by using an impedance analyzer, and the test result is shown in fig. 2, which shows that the permeability of the sample after the heat treatment of the above-mentioned example 1 is relatively stable.
Application example
The iron core of the hybrid magnetic circuit distribution transformer is prepared by combining and superposing the low-permeability amorphous alloy strip and the silicon steel sheet prepared in the embodiment 1, and then the iron core is wound by copper wires to obtain the hybrid magnetic circuit distribution transformer.
Performance analysis:
it can be seen from Table 1 that the amorphous alloys prepared in examples 1 to 5 had permeability of 6700 to 7350 at 100kHz, the permeability was lower and stable, the amorphous alloy prepared in comparative example 1 had permeability of 143000 at 50Hz, the permeability was less stable, the amorphous alloy prepared in examples 1 to 5 had losses of 1.18 to 1.35 at 1.3T and 50Hz, which were lower than the loss 2 of the amorphous alloy prepared in comparative example 1, and thus the amorphous alloys prepared in examples 1 to 5 had lower permeability and lower magnetic loss.
TABLE 1 Performance test results for examples 1-5 and comparative example 1
While the foregoing embodiments have been described in detail in connection with the embodiments of the invention, it should be understood that the foregoing embodiments are merely illustrative of the invention and are not intended to limit the invention, and any modifications, additions, substitutions and the like made within the principles of the invention are intended to be included within the scope of the invention.
Claims (13)
1. The low-permeability amorphous alloy is characterized by being formed by heat treatment of an iron-based alloy disordered structure strip through a segmented magnetic field, wherein the alloy component of the iron-based alloy disordered structure strip is one or more of Fe-Si-B-M, and M is C, co, nb, mn, cu and Ni.
2. The low permeability amorphous alloy according to claim 1, wherein the alloy composition of the iron-based alloy disordered structural strip is Fe a Si b B c C d Co e A is 78-82,4-b is 11-c is 13-d is 0-d is 1-e 2-a+b+c+d+e=100.
3. The low permeability amorphous alloy according to claim 1, wherein the alloy component of the iron-based alloy amorphous strip is Fe x Si 13 B 8 Nb 2 Mn 2 Cu 1 R y And x is 64-72,2-y is 10, R is Co or Ni.
4. A low permeability amorphous alloy according to any one of claims 1 to 3, wherein the segmented magnetic field heat treatment process is: first stage magnetic field heat treatment temperature T 1 Is T c -50℃≤T 1 ＜T c ，T c Is amorphous Curie temperature, and the heat preservation time is t 1 At t 1 Applying a magnetic field F1 in a direction perpendicular to the strip with the disordered iron-based alloy structure in time; second stage magnetic field heat treatment temperature T 1 Is T c ≤T 1 ≤T c The temperature is +120 ℃, the heat preservation time is t 2 At t 2 The magnetic field F2 is applied in a direction perpendicular to the strip of the disordered structure of the iron-based alloy in time, and then the strip is rapidly cooled to the tapping temperature.
5. The low permeability amorphous alloy according to claim 4, wherein the amorphous curie temperature T c Is 290-340 ℃.
6. The low permeability amorphous alloy according to claim 4, wherein the holding time t 1 The magnetic field strength of the magnetic field F1 is 80Oe-800Oe within 10min-180 min.
7. According toThe low permeability amorphous alloy according to claim 4, wherein the holding time t 2 The magnetic field strength of the magnetic field F2 is 160Oe-4500Oe within 10min-80 min.
8. The low permeability amorphous alloy according to claim 4, wherein the rapid cooling rate is 100 ℃/min-1500 ℃/min.
9. The low permeability amorphous alloy according to claim 1, wherein the low permeability amorphous alloy has a loss of less than 0.14W/kg at 1.3T,50 Hz; the magnetic permeability is kept constant at 50Hz-100kHz and is less than 8000.
10. The low permeability amorphous alloy according to claim 1, wherein the low permeability amorphous alloy has a loss of less than 0.1W/kg at 1.3T,50 Hz.
11. The low permeability amorphous alloy according to claim 1, wherein the low permeability amorphous alloy has a permeability of 6000 to 7500 at 50Hz to 100 kHz.
12. A method for producing the low permeability amorphous alloy according to any one of claims 1 to 11, comprising:
(1) The method comprises the steps of preparing and smelting alloy components of the iron-based alloy strip with the disordered structure according to any one of claims 1-11 to obtain a master alloy, and carrying out single-roll rapid quenching on the master alloy to obtain the iron-based alloy strip with the disordered structure;
(2) Heating the strip with the disordered iron-based alloy structure to the first-stage magnetic field heat treatment temperature T 1 Lower heat preservation t 1 Wherein T is c -50℃≤T 1 ＜T c ，T c Is amorphous Curie temperature, at t 1 Applying a magnetic field F1 in a direction perpendicular to the strip with a disordered structure in time, and then heating to a second-stage magnetic field heat treatment temperature T 2 Lower heat preservation t 2 Wherein T is c ≤T 2 ≤T c +120℃At t 2 And (3) applying a magnetic field F2 in a direction perpendicular to the strip with the disordered structure of the iron-based alloy in time, and then rapidly cooling to the tapping temperature to obtain the low-permeability amorphous alloy.
13. Use of a low permeability amorphous alloy according to any one of claims 1 to 11 in a hybrid magnetic circuit distribution transformer.
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