CN110670001A - Silicon-rich and P-type iron-based amorphous nanocrystalline alloy and preparation method of iron-based amorphous alloy nanocrystalline magnetic core - Google Patents

Abstract

The invention provides a compound shown as formula Fe_xSi_yB_zCu_eNb_mP_nThe application also provides a preparation method of the iron-based amorphous nanocrystalline alloy; according to the application, by adding a proper amount of P element, the coercive force of the iron-based amorphous nanocrystalline alloy is effectively reduced, the effective magnetic permeability of 1-20 kHz is improved, and the iron-based amorphous nanocrystalline alloy is good in amorphous forming capability and excellent in thermal stability by being matched with other elements.

Description

Silicon-rich and P-type iron-based amorphous nanocrystalline alloy and iron-based amorphous alloy nanocrystalline magnetic core the preparation method of

technical field

The invention relates to the technical field of magnetic materials, in particular to an iron-based amorphous nanocrystalline alloy and a preparation method of an iron-based amorphous alloy nanocrystalline magnetic core.

Background technique

Soft magnetic materials and their associated devices (inductors, transformers, and motors) play a key role in energy conversion throughout the world. The conversion of electrical energy involves bidirectional energy flow between energy sources, storage, and the grid, and is widely used in power electronics. The introduction of wide band gap (WBG) semiconductors has enabled power conversion, electronics and motor controllers to operate at higher frequencies. This can further reduce the size requirements of components (inductors and capacitors) in power electronics and enable them to have higher efficiencies and higher rotational speeds. At the same time, the market has increasingly higher performance requirements for soft magnetic materials.

Since the 19th century, when pure iron was the only soft magnetic material available, metallurgists, materials scientists and related people have been coming up with improved materials. The invention of silicon steel in 1900 was a noteworthy event for soft magnetic materials. At present, silicon steel and pure iron, which occupy nearly 80% of the market share of metal soft magnetic materials, still dominate the global soft magnetic market and are the materials of choice for large transformers and motors. However, the low resistance of silicon steel and pure iron makes it seriously affected by the eddy current effect, especially when the operating frequency increases, the magnetic core has more serious eddy current loss, causing serious energy and environmental problems. It is inconsistent with the development direction of high frequency, high current, miniaturization, and high efficiency and energy saving. After decades of development and research, a new generation of soft magnetic materials amorphous/nanocrystalline soft magnetic alloys have excellent soft magnetic properties, that is, high saturation magnetization _BS and permeability μ and low iron It has _attracted many domestic and foreign researchers to conduct a large number of scientific researches and some research results have been successfully industrialized.

Fe-based amorphous/nanocrystalline soft magnetic alloys are gradually replacing silicon steel, permalloy and ferrite due to their outstanding soft magnetic properties and relatively low cost, and are widely used in high-frequency electronic transformers, inductors and other power electronics In the device, it can improve the efficiency of the transformer, reduce the volume, reduce the weight, and reduce the loss. It is known as a new type of green energy-saving material in the 21st century, and is currently widely used in the field of power electronics.

Although the newly developed thermal soft magnetic composite material is suitable for obtaining extremely high resistivity due to insulating cladding design and can adapt to higher operating frequencies, its conductivity is not high. In view of the current state of soft magnetic materials, further development of iron-based amorphous nanocrystalline soft magnetic alloys with high saturation magnetic induction, high permeability and low loss is the key to meeting the requirements of power electronics for soft magnetic materials.

SUMMARY OF THE INVENTION

The technical problem solved by the present invention is to provide an iron-based amorphous nanocrystalline alloy with good amorphous forming ability, excellent thermal stability and excellent soft magnetic properties.

In view of this, the present application provides an iron-based amorphous nanocrystalline alloy represented by formula (I),

Fe _x Si _y B _z Cu _e Nb _m P _n (I);

Among them, x, y, z, e, m and n respectively represent the atomic percentage of the corresponding components; 71.5≤x≤73.5, 12.5≤y≤15.5, 1.0≤z≤7.0, 0.5≤e≤2.0, 1.0≤ m≤3.0, 0<n≤3; and x+y+z+e+m+n=100.

Preferably, the atomic percentage of Fe is 72-73.5, and the atomic percentage of Si is 13-15.5.

Preferably, the atomic percentage of B is 4-6, the atomic percentage of P is 0.5-2, the atomic percentage of Cu is 0.5-1.2, and the atomic percentage of Nb is 0.5-1.2. is 1.5 to 3.0.

Preferably, in the iron-based amorphous nanocrystalline alloy, n+z=7.

Preferably, in the iron-based amorphous nanocrystalline alloy, n+y=15.5.

Preferably, in the iron-based amorphous nanocrystalline alloy, n+x=73.5.

Preferably, the iron-based amorphous nanocrystalline alloy is Fe _73.5 Si _15.5 B ₆ Cu ₁ Nb ₃ P ₁ , Fe _73.5 Si _15.5 B ₅ Cu ₁ Nb ₃ P ₂ , Fe _73.5 Si _15.5 B ₄ Cu ₁ Nb ₃ P ₃ , Fe _73.5 Si _14.5 B ₇ Cu ₁ Nb ₃ P ₁ , Fe _73.5 Si _13.5 B ₆ Cu ₁ Nb ₃ P ₂ , Fe _73.5 Si _12.5 B ₅ Cu ₁ Nb ₃ P ₃ , Fe ₇₃ Si _15.5 B ₇ Cu ₁ Nb ₃ P _0.5 , Fe _72.5 Si _15.5 B ₆ Cu ₁ Nb ₃ P ₁ , Fe ₇₂ Si _15.5 B ₅ Cu ₁ Nb ₃ P _1.5 or Fe _71.5 Si _15.5 B ₄ Cu ₁ Nb ₃ P ₂ .

The present application also provides a method for preparing an iron-based amorphous nanocrystalline magnetic core, comprising the following steps:

Smelting after the composition of the iron-based amorphous alloy nanocrystalline alloy according to claim 1, obtains the iron-based amorphous nanocrystalline mother alloy;

Quickly quenching the iron-based amorphous nanocrystalline mother alloy with a copper roll to obtain an iron-based amorphous alloy ribbon;

The iron-based amorphous alloy thin strip is heat-treated to obtain an iron-based amorphous nanocrystalline magnetic core.

Preferably, in the rapid quenching of the copper roll, the line speed of the copper roll is 50 m/s to 55 m/s.

Preferably, the initial temperature of the heat treatment is 200°C, the primary heating rate is 10°C/min, the first-stage holding temperature is 460-510°C, and the holding time is 15min; the secondary heating rate is 1°C/min, and the second heating rate is 1°C/min. The holding temperature in the stage is 500-520 °C, and the holding time is 60 minutes; it is cooled to 300 °C with the furnace and air-cooled.

The present application provides an iron-based amorphous nanocrystalline alloy, which has an iron-based amorphous nanocrystalline alloy represented by the formula F _x Si _y B _z Cu _e Nb _m P _n . The coercivity of the iron-based amorphous nanocrystalline alloy is effectively reduced, the effective magnetic permeability of 1kHz to 20kHz is improved, and by cooperating with other elements, the amorphous forming ability of the iron-based amorphous nanocrystalline alloy is good. Excellent stability; further, through heat treatment, the α-Fe nano-magnetic particles with nanoparticles of about 15 nm in the iron-based amorphous nanocrystalline alloy also make the iron-based amorphous nanocrystalline alloy have excellent soft magnetic properties.

Description of drawings

Fig. 1 is the process flow schematic diagram of iron-based amorphous nanocrystalline alloy of the present invention;

Fig. 2 is the XRD spectrum under the quenched state of the first group of embodiment series alloy strips;

Fig. 3 is the XRD spectrum under the quenched state of the second group of embodiment series alloy strips;

FIG. 4 is the XRD spectrum of the third group of embodiment series alloy strips in the quenched state.

Detailed ways

In order to further understand the present invention, the preferred embodiments of the present invention are described below in conjunction with the examples, but it should be understood that these descriptions are only for further illustrating the features and advantages of the present invention, rather than limiting the claims of the present invention.

In response to the demand for iron-based amorphous nanocrystalline alloys in the prior art, the present application improves magnetic properties through alloy composition design and alloying, in order to improve the magnetic properties of iron-based amorphous nanocrystalline magnetics at high frequencies. Specifically, the embodiment of the present invention discloses an iron-based amorphous nanocrystalline alloy represented by formula (I),

Fe _x Si _y B _z Cu _e Nb _m P _n (I);

Among them, x, y, z, e, m and n respectively represent the atomic percentage of the corresponding components; 71.5≤x≤73.5, 12.5≤y≤15.5, 1.0≤z≤7.0, 0.5≤e≤2.0, 1.0≤ m≤3.0, 0<n≤3; and x+y+z+e+m+n=100.

In the iron-based amorphous nanocrystalline alloy of the present application, Fe is a ferromagnetic material, which provides magnetism for the iron-based amorphous nanocrystalline alloy; the atomic percentage of Fe is 71.5-73.5; in a specific embodiment, The atomic percentage of Fe is 72-73.5.

Si and B are amorphous forming elements, wherein the content of Si has a great influence on the magnetic permeability performance of the iron-based amorphous nanocrystalline alloy. The atomic percent content of Si is 12.5-15.5, and in a specific embodiment, the atomic percent content of Si is 13-15.5. The atomic percent content of B is 1.0-7.0, and in a specific embodiment, the atomic percent content of B is 4-6.

Cu and Nb act as nanocrystal forming elements, and size-controllable nanocrystalline particles can be obtained during the annealing process. The atomic percent content of Cu is 0.5-2.0; in a specific embodiment, the atomic percent content of Cu is 0.5-1.2. The atomic percent content of Nb is 1.0-3.0, and in a specific embodiment, the atomic percent content of Nb is 1.5-3.0.

P can promote the ability to form amorphous, reduce the coercivity, and improve the permeability in the 1kHz ~ 20kHz frequency band. The atomic percent content of P is greater than 0 and less than or equal to 3; in a specific embodiment, the atomic percent content of P is 0.5-2. Too much content of P will deteriorate the toughness of the quenched alloy strip and weaken the thermal stability of the alloy strip.

In a specific embodiment, the n+z=7; the n+y=15.5; the n+x=73.5.

In a specific embodiment, the iron-based amorphous nanocrystalline alloys described in this application are Fe _73.5 Si _15.5 B ₆ Cu ₁ Nb ₃ P ₁ , Fe _73.5 Si _15.5 B ₅ Cu ₁ Nb ₃ P ₂ , Fe _73.5 Si _15.5 B ₄ Cu ₁ Nb ₃ P ₃ , Fe _73.5 Si _14.5 B ₇ Cu ₁ Nb ₃ P ₁ , Fe _73.5 Si _13.5 B ₆ Cu ₁ Nb ₃ P ₂ , Fe _73.5 Si _12.5 B ₅ Cu ₁ Nb ₃ P ₃ , Fe ₇₃ Si _15.5 B ₇ Cu ₁ Nb ₃ P _0.5 , Fe _72.5 Si _15.5 B ₆ Cu ₁ Nb ₃ P ₁ , Fe ₇₂ Si _15.5 B ₅ Cu ₁ Nb ₃ P _1.5 or Fe _71.5 Si _15.5 B ₄ Cu ₁ Nb ₃ P ₂ .

The present application also provides a method for preparing the iron-based amorphous nanocrystalline magnetic core, comprising the following steps:

According to the ingredients of the iron-based amorphous alloy nanocrystalline alloy, the alloy is smelted and then smelted to obtain the iron-based amorphous nanocrystalline mother alloy;

Quickly quenching the iron-based amorphous nanocrystalline mother alloy with a copper roll to obtain an iron-based amorphous alloy ribbon;

The iron-based amorphous alloy thin strip is heat-treated to obtain an iron-based amorphous nanocrystalline magnetic core.

In the preparation process of the iron-based amorphous alloy, the present application firstly batches according to the composition of the iron-based amorphous nanocrystalline alloy, and then smelts to obtain the iron-based amorphous nanocrystalline master alloy; in order to ensure the quality of the master alloy, the smelting Before vacuuming, the vacuum degree is within 1×10 ^-3 Pa; then high-purity argon gas is introduced, which can be used as protective gas, arc ignition and heat source. During the smelting process, the titanium ingot can be pre-melted to absorb the residual oxygen in the smelting furnace, and then start smelting. The relevant operations of the specific smelting are not particularly limited in this application, and are technical means well known to those skilled in the art.

In the present application, the iron-based amorphous nanocrystalline master alloy is then subjected to copper roll rapid quenching to obtain an iron-based amorphous alloy thin strip; during this process, the line speed of the copper roll is 50m/s～55m/s .

According to the present invention, the iron-based amorphous alloy thin strip is finally heat-treated to obtain an iron-based amorphous nanocrystalline magnetic core. In this application, the initial temperature of the heat treatment is 200°C, the primary heating rate is 10°C/min, the first-stage holding temperature is 460-510°C, and the holding time is 15min; the secondary heating rate is 1°C/min, In the second stage, the holding temperature is 500 to 520°C, and the holding time is 60 minutes; the furnace is cooled to 300°C for air cooling. Heat treatment according to the above system. During the crystallization and annealing process, α-Fe uniformly nucleates and grows into nanocrystalline particles, which are uniformly distributed in the amorphous alloy matrix to form an amorphous/nanocrystalline dual-phase composite structure and obtain excellent soft magnetic properties. can.

The invention improves the magnetic properties of the iron-based amorphous nanocrystalline alloy strip by adding suitable P element, and uses XRD to analyze the structure of the alloy strip after annealing in each group of examples, and only α-Fe with nanoparticles of about 15 nm is detected. (Si) nano-magnetic particles, which is also the reason for the excellent soft magnetic properties of the alloy ribbon.

In order to further understand the present invention, the iron-based amorphous nanocrystalline alloy provided by the present invention and its preparation method are described in detail below with reference to the examples, and the protection scope of the present invention is not limited by the following examples.

Example

(1) Melting of master alloy

The general chemical formula of the composition of the alloy designed by the invention is F _x Si _y B _z Cu _e Nb _m P _n (#), wherein 71.5≤x≤73.5, 12.5≤y≤15.5, 1.0≤z≤7.0, 0.5≤e ≤2.0, 1.0≤m≤3.0, 0<n≤3, and let x+y+z+e+m+n=100, unless otherwise specified, the letters x, y, z, e, m and n are all expressed as atomic percent.

The industrial raw materials required for the master alloy are elemental elements Fe, Cu, Nb, Mo, Si and FeB and FeP alloys. The purity of the raw materials is shown in Table 1;

Table 1 Raw materials and their purity

These raw materials are weighed according to the formula, and then smelted using a WK-II A type non-consumable vacuum arc melting furnace. In order to ensure the quality of the master alloy, the furnace body is evacuated before smelting, so that the vacuum degree is within 1×10 ^-3 Pa, and then high-purity argon gas (purity 99.99%) is introduced. Here, argon gas is not only used for protection , also act as arc ignition and heat source. When each batch of samples is smelted, a smelting pot is reserved to hold the titanium ingots, and the titanium ingots are first smelted during smelting to absorb the residual oxygen in the smelting furnace, and then the experimental samples are smelted. Each sample must be turned and smelted repeatedly 4 Second, in order to ensure the uniformity of alloy composition, reduce the segregation of elements, and obtain high-quality master alloy.

(2) Preparation of amorphous alloy thin strip by copper roll rapid quenching method

The preparation of the amorphous alloy strip of the present invention uses the NMS-II induction type solution rapid quenching and stripping machine. The oxide layer on the surface of the copper roller is slightly polished with sandpaper, and then the dirt on the surface is wiped with gauze dipped in acetone, so that the surface of the copper roller is clean and free of oxide layer to ensure its cooling effect.

The above-mentioned smelted master alloy is ground off the oxide layer on the surface layer by a grinding machine, and it is broken into alloy blocks with a diameter of about 5-8mm, which are put into a quartz tube, and then the quartz tube is fixed on the copper roller. , the hole diameter of the quartz tube is 0.4~0.6mm, and the height from the orifice to the surface of the copper roller is controlled at 0.25mm; after the test tube is installed, close the furnace door, and vacuum the furnace body to less than 6×10 ^-3 Pa, At this time, close the vacuum valve, fill the furnace chamber with high-purity argon as a protective gas, and also inflate the air pressure chamber connected to the test tube, and pay attention to adjusting the air pressure of the air pressure chamber to be greater than the air pressure of the furnace chamber, and the pressure difference is 0.03～ 0.04MPa. Use the intermediate frequency induction coil to heat the master alloy. After the alloy is melted, pay attention to observe that when the color of the melt suddenly changes from orange to yellow-white, you can press the switch to turn on the pressure chamber, and use the pressure difference to spray the melt to the line speed of On a rapidly rotating copper roll of 50m/s to 55m/s, an alloy strip with a thickness of about 25mm and a width of about 1.2mm is prepared;

(3) X-ray diffraction analysis (XRD) and differential scanning calorimetry (DSC) analysis

石墨单色器滤波，管电压为40kV，管电流为30mA，测试范围为20～90°，步长0.02°，扫描速度8°/min；本申请中非晶态合金带材可通过XRD谱来确定，若其特征谱呈现为宽泛的衍射峰(又称“馒头峰”)，方可断定带材为完全非晶态结构；X-ray diffraction analysis (XRD) was used to verify whether the prepared alloy strips had a complete amorphous structure. In order to ensure that the alloy strips had a complete amorphous structure, the XRD spectra of all quenched alloy samples were obtained from the alloy strips. The free surface (relative to the other side of the copper roller surface); the relevant test conditions and parameters are: X-ray wavelength

Graphite monochromator filtering, the tube voltage is 40kV, the tube current is 30mA, the test range is 20-90°, the step size is 0.02°, and the scanning speed is 8°/min; the amorphous alloy strip in this application can be obtained by XRD spectrum. It is determined that if its characteristic spectrum presents a broad diffraction peak (also known as "steamed bread peak"), it can be concluded that the strip is a completely amorphous structure;

The alloy strip was thermally analyzed by differential scanning calorimetry (DSC) method to investigate the crystallization behavior and thermal stability of the alloy strip. Measure the DSC curve of the amorphous ribbon in DSC-TGA mode;

Before the test, the strip was cut into small pieces with an area of less than 1mm × 1mm, weighed about 20mg and put into the sample table in the alumina crucible, and heated the sample under the protection of _N2 atmosphere. 20°C/min, the heating range is 300-800°C; by analyzing the DSC curve of the sample, the phase transition of each sample during the heating process can be obtained, and the thermal characteristic temperature parameters such as Curie temperature T _c , glass transition temperature can be obtained. T _g and the crystallization initiation temperature T _x and crystallization peak temperature T _p of the alloy strip; according to the characteristic temperature value of the DSC curve of the alloy strip, the thermal stability of the alloy strip can be reflected, which is the heat treatment of the amorphous strip The determination of the process provides a reference to determine the approximate annealing temperature range.

(4) Preparation and heat treatment of toroidal core

The alloy strip in the quenched state is wound into a ring magnetic core with a specification of D×d×H=16×12×1.2mm, and the core is controlled by weighing the weight and the inner and outer diameters to have a consistent lamination factor ; Then heat treatment, crystallization and annealing treatment of the ring magnetic core. The heat treatment equipment is a programmable control single vacuum tube high temperature sintering furnace produced by Nobadi Material Technology Co., Ltd. The model of the furnace is NBD-O1200-60IT; during heat treatment, The magnetic core sample was placed in a tube furnace for crystallization and annealing treatment, and the ɑ-Fe(Si) nanocrystalline phase was precipitated; during the heat treatment process, the furnace temperature was 200 °C, the heating rate was 10 °C/min once, and the first-stage holding temperature was 460～510 ℃, the holding time is 15min; the secondary heating rate is 1 ℃/min, heated to the second-stage holding temperature Ta ₍ preferably 520 ℃) and kept for 60 minutes, then open the furnace cover and cool to 300 ℃ with the furnace air cooling, In order to prevent the oxidation of the alloy strip core, the core is protected by _N2 during the annealing process.

(5) Magnetic performance test and results

The invention uses the MATS-2010SD soft magnetic DC equipment produced by Hunan Lianzhong Science and Technology to measure the static magnetic hysteresis loop of the alloy strip magnetic core sample to obtain the intrinsic coercive force Hc of the magnetic core.

The saturation magnetization Ms of the annealed alloy strip was measured using a vibrating sample magnetometer (VSM) developed by Beijing Wuke Optoelectronics Technology Co. The range of the magnetic field is: -12500 to 12500Oe; before the test, use the prepared Ni standard to calibrate the equipment, then crush the magnetic sample to be tested, weigh about 0.032g, wrap it tightly with tin foil, and put it into a copper mold measured in.

Use the 1J3260B precision magnetic component analyzer produced by British Wayne Kerr Electronics to measure the single-smashed inductance of the magnetic core sample in the range of 1kHz-200kHz; the test conditions are: voltage 50mV, switching power supply frequency 1kHz, enameled package with a diameter of 0.50mm Copper wire; then converted to effective permeability by formula.

The preparation and testing method of iron-based amorphous nanocrystalline alloys (the process is shown in Figure 1) After the above description, the specific implementation of iron-based amorphous nanocrystalline alloys with specific components is carried out:

A) First group of examples

On the premise of satisfying the formula (#) and its conditions, let n+z=7, and the variation range of n is 0≤n≤6, according to this composition ratio, the alloy is weighed and sampled, and according to the above steps (1 ) method to smelt the series alloy to obtain the master alloy for stripping, then prepare the amorphous alloy thin strip by the method of the above-mentioned step (2), the XRD spectrum of the alloy strip sample is shown in Figure 2, from Figure 2 It can be seen that from n≥4, the alloy strip begins to crystallize. In the range of 0<n≤3, the XRD diffraction spectrum of all alloy strip samples only has a broadened diffuse scattering peak around 2θ of about 45°. , indicating that the alloy sample has a completely amorphous structure. The DSC analysis shows that there are two distinct exothermic peaks in the DSC curves of all samples, corresponding to the precipitation of ɑ-Fe(Si) and Fe-(B,P) compounds, respectively. The crystallization temperature is marked as T _x1 (that is, the point at which ɑ-Fe(Si) begins to precipitate), and the second-level initial crystallization temperature is marked as T _x2 (that is, the point at which the Fe-(B, P) compound starts to precipitate) , the difference between the two-stage initial crystallization temperatures is marked as ΔT _x (definition: ΔT _x =T _x2 -T _x1 ). According to steps (3) and (4), heat treatment and magnetic property tests are performed on the completely amorphous alloy strip. The comparison of thermal characteristic temperature and magnetic properties of alloy strips of this group of examples is summarized in Table 2.

Table 2 Characteristic temperature and annealed magnetic properties data table of the first group of embodiment alloy strips

*In Table 2, the structure of the quenched alloy strip: a represents the completely amorphous structure; b represents the amorphous + partially crystalline state. × indicates that the data is not given.

B) Second group of examples

On the premise of satisfying the formula (#) and its conditions, let n+y=15.5, and the variation range of n is 1≤n≤4, according to this composition ratio, the alloy is weighed and sampled, according to the above steps (1 ) method to smelt the series alloy to obtain the master alloy for stripping, then prepare the amorphous alloy thin strip by the method of the above-mentioned step (2), the XRD spectrum of the alloy strip sample is shown in Figure 3, all alloy strips The XRD spectra of the alloy samples only have a broadened diffuse scattering peak around 2θ of about 45°, indicating that the alloy samples are completely amorphous structures. The DSC analysis showed that two distinct exothermic peaks appeared in the DSC curves of all samples, corresponding to the precipitation of ɑ-Fe(Si) and Fe-(B,P) compounds, respectively. According to steps (3) and (4), heat treatment and magnetic property tests are performed on the completely amorphous alloy strip. The comparison of thermal characteristic temperature and magnetic properties of the alloy strips of this group of examples is summarized in Table 3.

Table 3 Characteristic temperature and annealed magnetic properties data table of the second group of embodiment alloy strips

*In Table 3, the structure of the quenched alloy strip: a represents a completely amorphous structure.

C) The third group of embodiments

On the premise of satisfying the formula (#) and its conditions, let n+x=73.5, and the variation range of n is 0.5≤n≤2.0, according to this composition ratio, the alloy is weighed and sampled, according to the above steps (1 ) method to smelt the series alloy to obtain the master alloy for stripping, then prepare the amorphous alloy thin strip by the method of the above-mentioned step (2), the XRD spectrum of the alloy strip sample is shown in Figure 4, all alloy strips The XRD spectra of the alloy samples only have a broadened diffuse scattering peak around 2θ of about 45°, indicating that the alloy samples are completely amorphous structures. The DSC analysis showed that two distinct exothermic peaks appeared in the DSC curves of all samples, corresponding to the precipitation of ɑ-Fe(Si) and Fe-(B,P) compounds, respectively. According to steps (3) and (4), heat treatment and magnetic property tests are performed on the completely amorphous alloy strip. The thermal characteristic temperature and magnetic properties of the alloy strips of this group of examples are summarized in Table 4.

Table 4 Characteristic temperature and annealed magnetic properties data table of the third group of example alloy strips

*In Table 4, the structure of the quenched alloy strip: a represents a completely amorphous structure.

According to the above three sets of examples, it can be seen that the coercive force of the iron-based amorphous nanocrystalline alloy strip can be effectively reduced by the addition of suitable P element, and the effective magnetic permeability of 1kHz to 20kHz can be improved; as in the first set of examples The Fe _73.5 Si _15.5 B ₆ Cu ₁ Nb ₃ P ₁ alloy strip core has a coercivity of 1.2 A/m after annealing, and an effective permeability of 120 k at 1 kHz; Fe _72.5 in the third group of examples The coercivity of the Si _15.5 B ₆ Cu ₁ Nb ₃ P ₁ alloy strip core after annealing is 0.6 A/m, and the effective permeability at 1 kHz is 87 k.

The descriptions of the above embodiments are only used to help understand the method and the core idea of the present invention. It should be pointed out that for those skilled in the art, without departing from the principle of the present invention, several improvements and modifications can also be made to the present invention, and these improvements and modifications also fall within the protection scope of the claims of the present invention.

The above description of the disclosed embodiments enables any person skilled in the art to make or use the present invention. Various modifications to these embodiments will be readily apparent to those skilled in the art, and the generic principles defined herein may be implemented in other embodiments without departing from the spirit or scope of the invention. Thus, the present invention is not intended to be limited to the embodiments shown herein, but is to be accorded the widest scope consistent with the principles and novel features disclosed herein.

Claims (10)

1. An iron-based amorphous nanocrystalline alloy as shown in formula (I), Fe _x Si _y B _z Cu _e Nb _m P _n (I); Among them, x, y, z, e, m and n respectively represent the atomic percentage of the corresponding components; 71.5≤x≤73.5, 12.5≤y≤15.5, 1.0≤z≤7.0, 0.5≤e≤2.0, 1.0≤ m≤3.0, 0<n≤3; and x+y+z+e+m+n=100. 2 . The iron-based amorphous nanocrystalline alloy according to claim 1 , wherein the atomic percentage of Fe is 72-73.5, and the atomic percentage of Si is 13-15.5. 3 . 3 . The iron-based amorphous nanocrystalline alloy according to claim 1 , wherein the atomic percentage of the B is 4-6, the atomic percentage of the P is 0.5-2, and the Cu The atomic percentage of Nb is 0.5-1.2, and the atomic percentage of Nb is 1.5-3.0. 4 . The iron-based amorphous nanocrystalline alloy according to claim 1 , wherein, in the iron-based amorphous nanocrystalline alloy, n+z=7. 5 . 5 . The iron-based amorphous nanocrystalline alloy according to claim 1 , wherein, in the iron-based amorphous nanocrystalline alloy, n+y=15.5. 6 . 6 . The iron-based amorphous nanocrystalline alloy according to claim 1 , wherein, in the iron-based amorphous nanocrystalline alloy, n+x=73.5. 7 . 7 . The iron-based amorphous nanocrystalline alloy according to claim 1 , wherein the iron-based amorphous nanocrystalline alloy is Fe _73.5 Si _15.5 B ₆ Cu ₁ Nb ₃ P ₁ , Fe _73.5 Si _15.5 B ₅ . Cu ₁ Nb ₃ P ₂ , Fe _73.5 Si _15.5 B ₄ Cu ₁ Nb ₃ P ₃ , Fe _73.5 Si _14.5 B ₇ Cu ₁ Nb ₃ P ₁ , Fe _73.5 Si _13.5 B ₆ Cu ₁ Nb ₃ P ₂ , Fe _73.5 Si _12.5 B ₅ Cu ₁ Nb ₃ P ₃ , Fe ₇₃ Si _15.5 B ₇ Cu ₁ Nb ₃ P _0.5 , Fe _72.5 Si _15.5 B ₆ Cu ₁ Nb ₃ P ₁ , Fe ₇₂ Si _15.5 B ₅ Cu ₁ Nb ₃ P _1.5 or Fe _71.5 Si _15.5 B ₄ Cu ₁ Nb ₃ P ₂ . 8. A preparation method of an iron-based amorphous nanocrystalline magnetic core, comprising the following steps: Smelting after the composition of the iron-based amorphous alloy nanocrystalline alloy according to claim 1, obtains the iron-based amorphous nanocrystalline mother alloy; Quickly quenching the iron-based amorphous nanocrystalline mother alloy with a copper roll to obtain an iron-based amorphous alloy ribbon; The iron-based amorphous alloy thin strip is heat-treated to obtain an iron-based amorphous nanocrystalline magnetic core. 9 . The preparation method according to claim 8 , wherein, in the rapid quenching of the copper roll, the linear speed of the copper roll is 50 m/s˜55 m/s. 10 . 10. The preparation method according to claim 8, wherein the initial temperature of the heat treatment is 200°C, the primary heating rate is 10°C/min, the first-stage holding temperature is 460-510°C, and the holding time is 15min ; The secondary heating rate is 1°C/min, the second-stage holding temperature is 500-520°C, and the holding time is 60min; the furnace is cooled to 300°C for air cooling.

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