WO2018227792A1 - 一种具有低应力敏感性的铁基非晶合金及其制备方法 - Google Patents

一种具有低应力敏感性的铁基非晶合金及其制备方法 Download PDF

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WO2018227792A1
WO2018227792A1 PCT/CN2017/100862 CN2017100862W WO2018227792A1 WO 2018227792 A1 WO2018227792 A1 WO 2018227792A1 CN 2017100862 W CN2017100862 W CN 2017100862W WO 2018227792 A1 WO2018227792 A1 WO 2018227792A1
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iron
amorphous alloy
based amorphous
strip
stress
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PCT/CN2017/100862
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French (fr)
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李晓雨
庞靖
李庆华
杨东
刘红玉
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青岛云路先进材料技术有限公司
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Priority to JP2020519164A priority Critical patent/JP2020524222A/ja
Priority to US16/335,257 priority patent/US20190256944A1/en
Publication of WO2018227792A1 publication Critical patent/WO2018227792A1/zh

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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
    • 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
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C33/00—Making ferrous alloys
    • C22C33/04—Making ferrous alloys by melting
    • 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
    • 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
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C2200/00—Crystalline structure
    • C22C2200/02—Amorphous

Definitions

  • the invention relates to the technical field of iron-based amorphous alloys, in particular to an iron-based amorphous alloy with low stress sensitivity and a preparation method thereof.
  • Fe-based amorphous alloy ribbons such as Fe-Si-B amorphous alloy ribbons are widely used as cores for power transformers and high frequency transformers. Based on the above characteristics, amorphous iron-based materials have dominated the field of transformers for a long time.
  • amorphous materials With the continuous renewal of silicon steel materials, the advantages of amorphous materials are relatively weak. For example, the saturation magnetic density of amorphous materials is obviously low, the magnetic induction is low, and the stress sensitivity is poor. In order to improve the saturation magnetic induction and reduce the loss of amorphous materials, amorphous materials have done a lot of work in recent years, but the research on the sensitivity of amorphous materials to stress is not significant. Stress removal is the fundamental guarantee for the low loss characteristics of amorphous materials. In addition, as the main material of the magnetic circuit of the transformer, the thickness of the strip is 20-30 ⁇ m. Because it is hard and brittle, it is difficult to shear.
  • the cross section of the amorphous alloy transformer core is rectangular, and the corresponding high and low voltage windings can only Use a rectangle.
  • the rectangular winding has poor short-circuit resistance with respect to the circular winding, so it is necessary to improve the short-circuit resistance of the amorphous alloy transformer.
  • the stress of the amorphous transformer core is mainly composed of two parts of stress.
  • One is the internal stress generated by the amorphous material during the preparation process, that is, the quenched internal stress of the amorphous material.
  • the iron core manufacturing process is caused by the iron core structure. Inevitable assembly external stress. A large number of studies have mainly reduced stress from the annealing process and the optimization of the transformer core structure.
  • the quenching internal stress of amorphous materials is mainly related to the formation of amorphous materials. Rapid cooling is a necessary condition for the formation of amorphous materials.
  • the high temperature melt is poured onto the cooling substrate to form a short-range order at a cooling rate of 10 6 °C/s.
  • the short-range disordered structure of the liquid state is "frozen", and internal stress is generated inside these "frozen” structures.
  • the amorphous material can effectively remove the internal stress of the amorphous material through the annealing process, and the amorphous industry has done a lot of work in removing the internal stress. Annealing Removes the internal stress in the quenched state and also causes the thermal stress generated by the large difference in core temperature, that is, the internal stress cannot be completely removed.
  • the external stress of the assembly is mainly caused by the process of making the core of the amorphous strip during the assembly process of the core and the external stress caused by the structural characteristics of the core itself.
  • the generation of such stress is inevitable, and the research on this part of the stress is relatively small, mainly by the optimization of the transformer core structure and the operation specification.
  • the amorphous alloy transformer winding is a rectangular structure, and the electric power received is far less uniform than the circular winding of the ordinary transformer, and it is more easily deformed when subjected to sudden short-circuit electric power. Since the core material of the amorphous alloy transformer is very sensitive to mechanical stress, both tensile stress and bending stress will affect its performance.
  • the amorphous alloy transformer body adopts an axial load-bearing structure.
  • the amorphous alloy core and the rectangular winding are not interfered by each other, and the rectangular winding is pressed by the upper and lower clamps and the pressing plate, and the compacted structure is self-contained. Therefore, the test of the short-circuit electric power of the rectangular winding in the axial direction and the radial direction is more severe than that of the circular winding.
  • JP-A-63-45318 proposes measures for improving the annealing process, mainly by reducing the temperature difference in the core. That is, a method of installing a heat insulating material on the inner and outer surfaces of the core to minimize the temperature difference in the core during cooling, and the like, it is desired to improve the thin strip itself to improve the weight and bulk of the core, and to be heated in the heat treatment furnace, and the core is heated. The more likely each part is to generate temperature unevenness.
  • the method of annealing and de-stressing does not cause crystallization due to excessive temperature of the iron core in the furnace and incomplete stress removal due to too low temperature.
  • the specific embodiment of the method is not specifically described herein, and the iron core annealing process and the annealing cost are increased, and the practical annealing process is not practical.
  • Chinese Patent Publication No. CN1281777C mentions that by adding a specific range of P in a limited composition range of Fe, Si, B, and C, it is found that temperature unevenness occurs in various portions of the core during annealing. Annealing at lower temperatures also shows excellent soft magnetic properties. The inventors only considered the effect of P on reducing the temperature unevenness of the amorphous iron core, and did not consider the problem of oxidation of the phosphorus-containing amorphous ribbon and surface crystallization. The anti-oxidation ability of the P element is extremely poor, and annealing in an aerobic environment is highly susceptible to deterioration of performance due to oxidation and deterioration of apparent quality.
  • the phosphorus-containing amorphous material is annealed, and the surface of the strip is blue due to oxidation, and the performance is deteriorated.
  • This has extremely high requirements on the oxygen content of the annealing atmosphere; in addition, there is no preparation of the amorphous ribbon ferrophosphorus at this stage, so that the introduction of the ferrophosphorus will produce unavoidable impurities, which easily causes the problem of surface crystallization of the strip.
  • the above method avoids the defect of large temperature difference of iron core At the same time, the problems of annealing and oxidation of amorphous ribbon and crystallization of the ribbon are introduced.
  • U.S. Patent No. US20160172087 discloses a study of the stress release of different compositions, points out the effect of B and C on the degree of stress release, and demonstrates the amount of stress release after strip annealing through an experimental model. This characterization method can explain the stress release of different components to a certain extent, but the inventor only removes the internal stress angle after annealing of the single strip to explain the stress release degree, and does not consider the final soft magnetic properties of the material and the assembly of the transformer core. Deterioration of performance after stress.
  • the embodiment of the above invention example optimizes the annealing process or the amorphous transformer core assembly process
  • the amorphous ribbon stress can be removed to a greater extent to some extent, but these optimizations are not specifically considered for the strip.
  • the feasibility of preparation and implementation is comprehensively considered, and there is a lack of comprehensive understanding of the destressing (evasion stress) of amorphous ribbons, and the results are relatively one-sided.
  • the technical problem solved by the present invention is to provide an iron-based amorphous alloy strip, and the iron-based amorphous alloy strip provided by the present application has low stress sensitivity.
  • the present application provides an iron-based amorphous alloy as shown in formula (I).
  • the iron-based amorphous alloy has a saturation magnetic induction of ⁇ 1.60T.
  • the atomic percentage of the Fe is 80.0 ⁇ a ⁇ 81.5.
  • the atomic percentage of the B is 11.0 ⁇ b ⁇ 12.5.
  • the atomic percentage of the Si is 7.0 ⁇ c ⁇ 8.0.
  • a 80.0, 12.0 ⁇ b ⁇ 13.0, and 7.0 ⁇ c ⁇ 8.0.
  • a 80.5, 11.5 ⁇ b ⁇ 12.5, and 7.0 ⁇ c ⁇ 8.0.
  • the iron-based amorphous alloy 81.0 ⁇ a ⁇ 81.5, 11.0 ⁇ b ⁇ 13.0, 7.0 ⁇ c ⁇ 8.0.
  • the application also provides a method for preparing an iron-based amorphous alloy strip as shown in formula (I), comprising:
  • the element is compounded according to the atomic percentage of the formula (I), and the raw material after the compounding is melted, and the melted molten metal is heated and kept warm, and then subjected to single-roll quenching to obtain an iron-based amorphous alloy strip;
  • the method further comprises:
  • the iron-based amorphous alloy after the single roll quenching is heat-treated.
  • the method further comprises: winding a single-roll quenched iron-based amorphous alloy into a sample ring having an inner diameter of 50.5 mm and an outer diameter of 53.5 to 54 mm, and a strain coefficient allowed by loss of the sample ring after heat treatment.
  • the excitation power allows a strain factor of 6%.
  • the heat-treated iron-based amorphous alloy strip has a coercive force of ⁇ 3.5 A/m; at 50 Hz, 1.35 T, the heat-affected iron-based amorphous alloy strip has a magnetizing power of ⁇ 0.1450 VA/kg, core loss ⁇ 0.1100W/kg; at 50Hz, 1.40T, the thermal power of the iron-based amorphous alloy strip after heat treatment is ⁇ 0.1700VA/kg, core loss ⁇ 0.1500W/kg .
  • the iron-based amorphous alloy strip is in a completely amorphous state, has a critical thickness of at least 75 ⁇ m, and a shear limit strip thickness of at least 29 ⁇ m.
  • FIG. 1 is a schematic view showing a simulation experiment device for an unstressed state of an iron-based amorphous alloy sample ring prepared by the present invention
  • FIG. 2 is a schematic view of a simulation test apparatus for applying a stress state to an iron-based amorphous alloy sample ring prepared by the present invention.
  • an embodiment of the invention discloses an iron-based amorphous alloy as shown in formula (I),
  • the iron-based amorphous alloy provided by the present application contains Fe, Si and B, and has good amorphous forming ability, saturation magnetic induction strength and soft magnetic property by controlling the content of the above elements; further, the present application provides The strip prepared from the iron-based amorphous alloy has low stress sensitivity after heat treatment.
  • Fe is a basic element, and its content is 79.5 ⁇ a ⁇ 82.5 in terms of atomic percentage. If the atomic percentage of Fe is too low, the saturation magnetic induction density of the iron-based amorphous alloy is too low. The defect of improving the low magnetic density of amorphous can not be obtained, and sufficient magnetic flux density and structurally dense core design cannot be obtained; if the content is too high, the thermal stability of the iron-based amorphous alloy and the formability of the strip are lowered. It is difficult to straighten the strip and a good magnetic product cannot be obtained. In a specific embodiment, the atomic percentage of Fe is 79.5 ⁇ a ⁇ 81.5, and more specifically, the atomic percentage of Fe is 80.0 ⁇ a ⁇ 81.5.
  • the atomic percentage of the Si is 6.5 ⁇ c ⁇ 8.5, and if the content is too low, the formability of the iron-based amorphous alloy strip and the thermal stability of the amorphous alloy strip are lowered, so that the amorphous material is stably formed. It becomes difficult; when the content is too high, the brittleness of the iron-based amorphous alloy is increased, and the ductility of the strip after annealing is deteriorated.
  • the Si content is 7.0 ⁇ c ⁇ 8.0.
  • the atomic percentage of B is 11.0 ⁇ b ⁇ 13.5, and if the content of B is too low, it becomes difficult to form an amorphous material stably, and if the content is too high, the ability to form an amorphous state is not further advanced.
  • the increase, that is, the B content in the above range allows the iron-based amorphous alloy of the present invention to have excellent soft magnetic properties.
  • the content of B is 11.0 ⁇ b ⁇ 13.0, and more specifically, the content of B is 11.0 ⁇ b ⁇ 12.5.
  • composition and content of the iron-based amorphous alloy provided by the present application are reasonably combined from the improvement of the magnetic induction intensity and the improvement of the amorphous forming ability, respectively, forming an iron-based amorphous alloy with high saturation magnetic induction strength, and further, having a high
  • the iron-based amorphous alloy of the present application also has low stress sensitivity; that is, the iron-based amorphous alloy provided by the present application has high saturation magnetic induction and low stress sensitivity due to the iron-based amorphous alloy. Adjustment of composition and content.
  • the application also provides a method for preparing an iron-based amorphous alloy strip as shown in formula (I), comprising:
  • the element is compounded according to the atomic percentage of the formula (I), and the raw material after the compounding is melted, and the melted molten metal is heated and kept warm, and then subjected to single-roll quenching to obtain an iron-based amorphous alloy strip;
  • the present application employs a conventional technical means in the art to prepare an iron-based amorphous alloy ribbon of the specific composition of the present application.
  • the process of the ingredients and the smelting in the above preparation method is a process well known to those skilled in the art, and the specific operation means are not specifically described in the present application.
  • the metal raw material is smelted using an intermediate frequency smelting furnace, the smelting temperature is 1300 to 1500 ° C, and the time is 80 to 120 min.
  • the melted molten metal is heated and maintained, and then subjected to single-roll quenching to obtain an iron-based amorphous alloy strip.
  • the temperature for the temperature rise is preferably from 1350 to 1470 ° C, and the time of the heat retention is preferably from 20 to 50 min.
  • the present application obtains a completely amorphous iron-based amorphous alloy strip having an amorphous limit band thickness of at least 75 ⁇ m, and the strip toughness is good, and the sheet is folded 180 degrees continuously.
  • the shear limit band thickness is at least 29 ⁇ m, and the industrial production of the product has a considerable preparation margin, which reduces the requirements for the cooling equipment in the industrialization process.
  • the present application heat treats the amorphous iron-based alloy strip for ease of application.
  • the iron-based amorphous alloy provided by the present application can realize a wide retreat
  • the heat treatment is performed in the fire interval, and the obtained iron-based amorphous alloy strip has a low excitation power and loss.
  • the temperature of the heat treatment described herein is 325 to 395 ° C; in a specific embodiment, the temperature of the heat treatment is 335 to 385 ° C.
  • the prepared iron-based amorphous alloy strip is preferably wound into a sample ring having an inner diameter of 50.5 mm and an outer diameter of 53.5 to 54 mm, and the sample ring is subjected to heat treatment.
  • the deterioration of the loss and the excitation power of the sample ring under heat treatment is detected by the simulation experiment, so as to explain the transformation of the properties of the iron-based amorphous alloy strip under stress state; if the strain coefficient is large Under the condition that the loss coefficient of the iron-based amorphous alloy strip and the deterioration coefficient of the excitation power are still within the acceptable range, it can be explained that the iron-based amorphous alloy strip has lower stress sensitivity, if the strain coefficient is even smaller. The loss coefficient of the iron-based amorphous alloy strip and the deterioration coefficient of the excitation power are still unacceptable, which indicates that the stress sensitivity of the iron-based amorphous alloy strip is poor.
  • the experimental results show that the iron-based amorphous alloy ribbon of the present invention has low stress sensitivity.
  • the present invention reduces the stress sensitivity of the iron-based amorphous alloy strip by adjusting the content of the added component and the component, that is, the content of the component and the component synergistically to improve the magnetic properties of the iron-based amorphous alloy.
  • the alloy composition represented by Fe a B b Si c is prepared using industrial pure iron, silicon or boron iron; the alloy component has inevitable impurity elements such as C in addition to the main element. , Mn, S, etc.
  • the materials of different components are sequentially added to the intermediate frequency induction smelting furnace with a furnace capacity of 100kg in the order of boron iron, silicon and pure iron (the melting temperature is 1300-1500 ° C, the time is 80-120 min); the molten steel is calmed. At the end, it is poured into the spray bag, and an amorphous ribbon with an amorphous bandwidth of 20 mm is prepared by a single roll planar casting method.
  • alloy strips with different thicknesses are prepared by adjusting parameters such as roll speed and liquid level (The roller speed during the belt making process is 1000 to 1400 r/min, and the belt speed is controlled to be 20 to 30 m/s, and the liquid level is 200 to 300 mm.
  • the roller speed during the belt making process is 1000 to 1400 r/min, and the belt speed is controlled to be 20 to 30 m/s, and the liquid level is 200 to 300 mm.
  • Table 1 shows the amorphous limit band thickness of each alloy component.
  • the saturation magnetization values of each amorphous alloy strip were tested using VSM.
  • the alloy composition was comprehensively evaluated by the strip amorphous forming ability and the saturation magnetic induction value.
  • the maximum thickness of the strip can be determined according to the number of brittle points of the strip. The brittle point is evaluated by taking the length of the strip as the circumference of the crystallizer and cutting the strip along the length of the strip. The number of brittle points is not more than 2
  • the material can be sheared, and equal to 2 is considered to be the limit of the strip of the alloy component.
  • Table 1 presents the different alloy compositions with corresponding amorphous limit band thickness, tape toughness limit band thickness, and saturation magnetic induction.
  • Amorphous limit band thickness and tape toughness limit thickness are the alloy component tape making process sexual considerations, the thicker the above-mentioned belt, the more stringent the requirements for the belt making equipment.
  • the amorphous limit band thickness of the alloy composition is thicker, and the amorphous degree of the strip is higher.
  • Comparative Examples 1 to 4 have a relatively high amorphous limit band thickness, the maximum shearable thickness is 27 ⁇ m or less, which not only imposes more stringent requirements on the cooling strength of the belt making equipment, but also on the assembly efficiency of the core, and at the same time on the transformer. During assembly and operation, easy debris has buried the foreshadowing, which has increased the safety hazard of transformer operation. In addition, its saturation magnetic density is less than 1.57T, which makes the design of amorphous transformer narrow and narrow, which can not meet the design trend of high magnetic density of transformer. Comparing Comparative Example 6 with Examples 4 to 6, it can be seen that the same Fe content, the higher the Si content, the smaller the shear thickness.
  • Comparative Example 8 ⁇ 9 alloy amorphous saturation magnetic density is obviously high. This is expected by transformer design.
  • the maximum shearable thickness is between 36 and 38 ⁇ m. It has absolute advantage in iron core forming efficiency, but its amorphous limit band It can be seen from the thickness value that the amorphous forming ability is obviously insufficient, and the process conditions of the slanting line are not obtained, and the excitation power and loss are also affected.
  • the strips having a thickness of 26 to 28 ⁇ m and a width of 30 mm in Table 1 were wound into a sample ring having an inner diameter of 50.5 mm and an outer diameter of 53.5 to 54 mm, and the sample ring was subjected to stress relief annealing using a box annealing furnace. Annealing was carried out in an argon-protected atmosphere from 325 to 395 ° C with a 10 ° C interval and 1 h of incubation. The heat treatment process adds a magnetic field along the strip preparation direction with a magnetic field strength of 1200 A/m.
  • the silicon steel tester was used to test the excitation and loss of the strip after heat treatment. The test conditions were 1.35T/50Hz and 1.40T/50Hz, respectively.
  • the performance test results are shown in Table 2:
  • An amorphous material with a large saturation magnetic induction strength has a lower saturation magnetic induction material, which allows a larger working magnetic density, that is, operation at a 1.4T magnetic density exhibits relatively low excitation power and loss.
  • Comparative Examples 8-9 are tested at 1.4T, and the performance will be better.
  • the 1.4T loss and excitation increase, resulting in a large performance at 1.4T.
  • Examples 1 to 11 exhibited excellent soft magnetic properties at 1.35/50 Hz and 1.450/5 Hz; the 1.35/50 Hz loss was within 0.11 W/kg, and the 1.4 T/50 Hz loss was within 0.15 W/kg.
  • the amorphous material has a relatively low unavoidable loss value, and the amorphous material is deteriorated by the external stress after being assembled into an iron core.
  • a stress model of amorphous ring was established to characterize the deterioration of the properties of amorphous products with different compositions after stress deformation, and the simulation of amorphous ribbons was assembled into a transformer.
  • the iron core is subject to changes in stress properties.
  • Sample treatment Select the amorphous ribbon as the composition of Table 3, and make a sample ring with an inner diameter of 50.5 mm and an outer diameter of 53.5 to 54 mm.
  • the sample ring is subjected to stress relief annealing using a box annealing furnace, and annealing is selected in argon. Conducted in a protective atmosphere.
  • the sample tape prepared by different components is selected, and the sample ring is prepared according to the above requirements for heat treatment.
  • the heat treatment temperature is 325-395 ° C, and the heat treatment is performed as a gradient every 5 degrees, the heat preservation time is 60-120 min; the magnetic field strength is 800-1400 A/ m.
  • the optimum heat treatment performance of each component in the above heat treatment process was selected to test the performance deterioration of the strip after stress.
  • Fig. 1 is a schematic diagram of the simulation test device without stress state of the sample loop, and Fig. 2 is applied by the sample loop. Schematic diagram of the simulation test device of the stress state; when the sample ring is applied with stress, the A plate is fixed, and the feed amount of the sample ring is given under the push of the push plate B, the sample ring is deformed by the stress, and the plate B is fixedly pressed to test the deformation condition.
  • the loss P 1 of the material and the excitation power Pe 1 were measured using a silicon steel tester at 1.35 T/50 Hz.
  • the initial sample ring (under the condition of non-deformation) has an inner diameter of D 0 , the properties are P 0 and Pe 0 respectively , and the inner diameter after deformation is D 1 .
  • this experiment stipulates that the performance deterioration is within 50%, and the corresponding ring-shaped variable corresponding to the performance value is the maximum allowable deformation coefficient value of the corresponding component material.

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Abstract

一种铁基非晶合金，其组分为Fe aB bSi c，其中，a、b与c分别表示原子百分含量：79.5≤a≤82.5，11.0≤b≤13.5，6.5≤c≤8.5，a+b+c＝100。通过单辊快淬的方法获得该铁基非晶合金带材。该铁基非晶合金具有较高的饱和磁感应强度、较高的非晶形成能力与较低的抗应力敏感性，可用于制作电力变压器、发电机、发动机的铁芯材料；同时由于其低应力敏感性，在制作电力变压器时可提高非晶变压器的抗突发短路能力。

Description

一种具有低应力敏感性的铁基非晶合金及其制备方法
本申请要求于2017年06月14日提交中国专利局、申请号为201710447487.1、发明名称为“一种具有低应力敏感性的铁基非晶合金及其制备方法”的中国专利申请的优先权，其全部内容通过引用结合在本申请中。
技术领域
本发明涉及铁基非晶合金技术领域，尤其涉及一种具有低应力敏感性的铁基非晶合金及其制备方法。
背景技术
由于具有低铁损、高饱和磁通量密度、高磁导率及其它优点，Fe基无定形合金薄带如Fe-Si-B无定形合金薄带被广泛用作电源变压器与高频变压器的铁心。基于以上特点，非晶铁基材料在面世很长一段时间内，在变压器领域独领风骚。
随着硅钢材料的持续更新，非晶材料的优势相对弱化。比如，非晶材料饱和磁密明显偏低、磁感应强度低、抗应力敏感度差等。针对非晶材料提高饱和磁感应强度和降低损耗等的改进，近年来非晶材料做了大量的工作，但是针对非晶材料抗应力敏感度差的研究未有显著的结果。而应力去除是非晶材料的低损耗特征的根本保障。另外，作为变压器磁路的主要材料非晶合金，其带材厚度为20-30μm，因其硬而脆，难以剪切，因此非晶合金变压器铁心截面均采用矩形，相应高低压绕组也只能采用矩形。矩形绕组相对圆形绕组而言抗短路能力较差，所以提高非晶合金变压器抗短路能力很有必要。
非晶变压器铁芯的应力主要由两部分应力组成，一是非晶材料在制备过程中产生的内应力即非晶材料淬态内应力，另一方面是铁芯制作过程由于铁芯结构特点产生的不可避免的装配外应力。大量的研究主要从退火工艺以及变压器铁芯结构优化降低应力。
非晶材料的淬态内应力产生主要跟非晶材料形成有关，快速冷却是非晶材料形成的必要条件，高温的熔体浇注到冷却基体上，在106℃/s的冷却速度形成短程有序长程无序结构的非晶带材。液态这种短程无序结构被“冻结”，这些被“冻结”的结构内部会有内应力产生。非晶材料通过退火工艺可以有效的去除非晶材料的内应力，非晶行业退火工艺去除内应力方面做过大量的工作。退火 去除淬态内应力的同时也会由于铁芯温度差异较大而产生的热应力，即内应力无法完全去除。
装配外应力的产生主要是铁芯装配过程中非晶带材制作铁芯过程以及铁芯本身结构特征带来的外应力。这种应力的产生不可避免，这部分去应力的研究相对较少，主要是通过变压器铁芯结构的优化和操作的规范来去除。非晶合金变压器绕组是矩形结构，所受电动力远不如普通变压器圆形绕组均匀，承受突发短路电动力时更容易变形。由于非晶合金变压器的铁心材料对机械应力非常敏感，无论是张应力还是弯曲应力都会影响其性能，所以在结构设计时加以充分考虑，以减少铁心受力；一般需采取特殊的紧固措施，将非晶合金变压器器身采用轴向承重结构。非晶合金铁心和矩形绕组受力互不干扰，矩形绕组通过上下夹件及压板压紧，压紧结构自成体系。因此矩形绕组的轴向和径向所承受短路电动力的考验要比圆形绕组严酷。为了降低变压器的装配和设计难度，降低非晶合金的应力敏感性是非常重要的。
例如，特开昭63-45318号公报提出了退火工艺改善的措施，主要是通过降低铁芯内温差的方法实现。即在铁心内外周面安装绝热材料，极力降低冷却时的铁心内的温度差的方法等，希望改善薄带本身，以改善铁心重量重与体积大的问题，装入到热处理炉后加热，铁心的各部位越容易产生温度不均的情况。该方法退火去应力不会因为炉内有铁芯温度过高产生晶化以及温度过低去应力不完全的现象。但是文中未具体表述这种方法的具体实施方式，并且会增加铁芯退火的工序以及退火成本，实际退火过程中实用性不强。
公开号为CN1281777C的中国专利中提到，在Fe、Si、B、C的受限的组成范围中通过添加特定范围的P，由此发现了在退火中的铁心各部位产生温度不均的场合，在更低的温度下退火，也能显现优异软磁性。发明人仅考虑P对降低非晶铁芯温度不均的作用，未考虑含磷非晶带材氧化以及表面晶化的问题。P元素的抗氧化能力极差，在有氧的环境中退火极易因受氧化而使性能严重恶化以及表观质量变差。比如在Fe、Si、B、C退火环境中进行含磷非晶材料退火，带面因为氧化而变蓝色，性能会恶化。这对退火气氛的氧含量有极高的要求；另外现阶段尚无制备非晶带材磷铁，致使磷铁引入会产生不可避免的杂质，容易产生带材表面晶化问题。综上，上述方法在规避铁芯温差大的缺陷 的同时，又引入了非晶带材退火氧化和制带晶化等问题。
公开号为US20160172087的美国专利提到了针对不同成分应力释放度的研究，指出B、C对应力释放度的作用，并通过实验模型说明带材退火后应力释放量。这种表征方法一定程度上可以说明不同成分应力释放情况，但是发明人仅从单片带材退火后去除内应力角度以应力释放度来说明，未考虑材料最终软磁性能以及变压器铁芯受装配应力后性能的恶化情况。
如上所述，上述发明例的实施方案虽然对退火工艺或者非晶变压器铁芯装配工艺做了优化，一定程度上可以更大程度的去除非晶带材应力，但是未具体考虑这些优化对于带材制备以及实施的可行度综合考量，并且缺乏对非晶带材去应力(规避应力)更为全面的认识，其结果相对片面。
发明内容
本发明解决的技术问题在于提供一种铁基非晶合金带材，本申请提供的铁基非晶合金带材具有较低的应力敏感性。
有鉴于此，本申请提供了一种如式(Ⅰ)所示的铁基非晶合金，
FeaBbSic(Ⅰ)；
其中，a、b与c分别表示对应组分的原子百分含量；79.5≤a≤82.5，11.0≤b≤13.5，6.5≤c≤8.5，a+b+c＝100。
优选的，所述铁基非晶合金的饱和磁感应强度≥1.60T。
优选的，所述Fe的原子百分含量为80.0≤a≤81.5。
优选的，所述B的原子百分含量为11.0≤b≤12.5。
优选的，所述Si的原子百分含量为7.0≤c≤8.0。
优选的，所述铁基非晶合金中，a＝80.0，12.0≤b≤13.0，7.0≤c≤8.0。
优选的，所述铁基非晶合金中，a＝80.5，11.5≤b≤12.5，7.0≤c≤8.0。
优选的，所述铁基非晶合金中，81.0≤a≤81.5，11.0≤b≤13.0，7.0≤c≤8.0。
本申请还提供了一种如式(Ⅰ)所示的铁基非晶合金带材的制备方法，包括：
按照式(Ⅰ)的原子百分比进行元素的配料，将配料后的原料进行熔炼，将熔炼后的熔液升温保温后进行单辊快淬，得到铁基非晶合金带材；
FeaBbSic(Ⅰ)；
其中，a、b与c分别表示对应组分的原子百分含量；79.5≤a≤82.5，11.0≤b≤13.5，6.5≤c≤8.5，a+b+c＝100。
优选的，所述单辊快淬之后还包括：
将单辊快淬后的铁基非晶合金进行热处理。
优选的，所述热处理之前还包括：将单辊快淬后的铁基非晶合金绕制成内径为50.5mm，外径为53.5～54mm的样环，热处理后样环的损耗允许的应变系数为10.0％，激磁功率允许的应变系数为6％。
优选的，所述热处理后的铁基非晶合金带材的矫顽力≤3.5A/m；在50Hz，1.35T条件下，所述热处理后的铁基非晶合金带材的激磁功率＜0.1450VA/kg，铁芯损耗＜0.1100W/kg；在50Hz，1.40T条件下，所述热处理后的铁基非晶合金带材的激磁功率＜0.1700VA/kg，铁芯损耗＜0.1500W/kg。
优选的，所述铁基非晶合金带材为完全非晶状态，临界厚度至少为75μm，可剪极限带厚至少为29μm。
本申请提供了一种铁基非晶合金带材，其具有如式FeaBbSic的原子组成，其中a、b与c分别表示对应组分的原子百子含量；79.5≤a≤82.5，11.0≤b≤13.5，6.5≤c≤8.5，a+b+c＝100；本申请提供的铁基非晶合金中的Fe可保证得到稳定的制备性能更低、成带率更高的非晶铁基合金；Si元素有利于稳定地形成无定形材料；B是对合金非晶态化贡献最大的元素；因此，本申请通过调整Fe、Si和B的含量，使铁基非晶合金具有高饱和磁感应强度与高延展性；同时还具有低应力敏感度，使用本合金制备的铁芯装配成变压器具有较强的抗突发短路能力。
附图说明
图1为本发明制备的铁基非晶合金样环无应力状态的模拟实验装置示意图；
图2为本发明制备的铁基非晶合金样环施加应力状态的模拟试验装置示意图。
具体实施方式
为了进一步理解本发明，下面结合实施例对本发明优选实施方案进行描述，但是应当理解，这些描述只是为进一步说明本发明的特征和优点，而不是 对本发明权利要求的限制。
无论内应力还是外应力的产生是不可避免的，通过退火工艺优化、变压器铁芯结构优化以及规范操作其应力依然存在。如何通过成分调整并完成针对不同成分带材对应力(内应力、外应力)敏感度的评估，确立应力敏感度小的非晶成分范围，进而有效的呈现非晶制品优异的软磁性能，制备抗突发短路能力较强的非晶变压器是本申请研究的主要目的。由此，本发明实施例公开了一种如式(Ⅰ)所示的铁基非晶合金，
FeaBbSic(Ⅰ)；
其中，a、b与c分别表示对应组分的原子百分含量；79.5≤a≤82.5，11.0≤b≤13.5，6.5≤c≤8.5，a+b+c＝100。
本申请提供的铁基非晶合金由于含有Fe、Si与B，并通过控制上述元素的含量，使其具有较好的非晶形成能力、饱和磁感应强度和软磁性能；进一步的，本申请提供的铁基非晶合金制备得到的带材在热处理后具有较低的抗应力敏感性。
在铁基非晶合金中，Fe作为基础元素，以原子百分比计，其含量为79.5≤a≤82.5，所述Fe的原子百分含量过低则铁基非晶合金的饱和磁感应密度过低，起不到改善非晶低磁密的缺陷，不能得到足够的磁通量密度和结构密实的铁芯设计；含量过高则降低了铁基非晶合金的热稳定性和带材的可成形性，会使带材顺行变得困难，且不能得到好的磁性产品。在具体实施例中，所述Fe的原子百分含量为79.5≤a≤81.5，更具体的，所述Fe的原子百分含量为80.0≤a≤81.5。
所述Si的原子百分含量为6.5≤c≤8.5，其含量过低，则降低铁基非晶合金带材可成形性以及非晶合金带材的热稳定性，使稳定的形成无定形材料变得困难；含量过高则使铁基非晶合金的脆性变大，退火后带材的延展性变差。在具体实施例中，所述Si的含量为7.0≤c≤8.0。
所述B的原子百分含量为11.0≤b≤13.5，所述B的含量过低，则使稳定的形成无定形材料变得困难，而含量过高则不会使形成无定形状态的能力进一步增加，即上述范围的B含量可使本发明的铁基非晶合金具有优良的软磁性能。在具体实施例中，所述B的含量为11.0≤b≤13.0，更具体的，所述B的含量为 11.0≤b≤12.5。
在本申请中，所述铁基非晶合金的较佳的组合方式为：a＝80.0，12.0≤b≤13.0，7.0≤c≤8.0；或a＝80.5，11.5≤b≤12.5，7.0≤c≤8.0；或81.0≤a≤81.5，11.0≤b≤13.0，7.0≤c≤8.0。
本申请提供的铁基非晶合金的组分及含量分别从提高磁感应强度与提高非晶形成能力进行合理组合，形成了一种高饱和磁感应强度的铁基非晶合金，进一步的，在具有高饱和磁感应强度的基础上，本申请的铁基非晶合金还具有低应力敏感性；即本申请提供的铁基非晶合金具有高饱和磁感应强度与低应力敏感性是由于铁基非晶合金的组分与含量的调整。
本申请还提供了一种如式(Ⅰ)所示的铁基非晶合金带材的制备方法，包括：
按照式(Ⅰ)的原子百分比进行元素的配料，将配料后的原料进行熔炼，将熔炼后的熔液升温保温后进行单辊快淬，得到铁基非晶合金带材；
FeaBbSic(Ⅰ)；
其中，a、b与c分别表示对应组分的原子百分含量；79.5≤a≤82.5，11.0≤b≤13.5，6.5≤c≤8.5，a+b+c＝100。
在制备铁基非晶合金带材的过程中，本申请采用了本领域常规的技术手段，制备了本申请具体成分的铁基非晶合金带材。上述制备方法中的配料与熔炼的过程为本领域技术人员熟知的过程，本申请对其具体操作手段不进行特别的说明。在熔炼过程中，使用中频冶炼炉将金属原材料熔炼，所述熔炼的温度为1300～1500℃，时间为80～120min。在熔炼之后，本申请将熔炼后的熔液升温保温后采用单辊快淬，而得到了铁基非晶合金带材。所述升温的温度优选为1350～1470℃，所述保温的时间优选为20～50min。经过单辊快淬之后，本申请得到了完全非晶状态的铁基非晶合金带材，其形成非晶极限带厚至少为75μm，且带材韧性较好，对折180度不断。对本发明而言，其可剪极限带厚至少29μm，则本产品的工业化生产有相当大的制备余量，降低了在其工业化过程中对冷却设备的要求。
在初步制备非晶铁基合金带材之后，为了便于应用，本申请将所述非晶铁基合金带材进行热处理。本申请提供的铁基非晶合金可使其实现在较宽泛的退 火区间内进行热处理，且使得到的铁基非晶合金带材具有较低的励磁功率与损耗。本申请所述热处理的温度为325～395℃；在具体实施例中，所述热处理的温度为335～385℃。
按照本发明，在上述热处理之前，优选将制备得到的铁基非晶合金带材绕制成内径为50.5mm，外径为53.5～54mm的样环，再将上述样环进行热处理。通过模拟实验检测热处理后样环在受应力的状态下，损耗与激磁功率的恶化情况，以此说明铁基非晶合金带材的性能在应力状态下的转变情况；若应变系数较大的情况下，铁基非晶合金带材的损耗与激磁功率的恶化系数仍在可接受的范围之内，则可说明铁基非晶合金带材具有较低的应力敏感性，若应变系数即使较小，铁基非晶合金带材的损耗与激磁功率的恶化系数仍不可接受，则可说明铁基非晶合金带材的应力敏感性较差。通过本申请的模拟实验，实验结果表明，本发明的铁基非晶合金带材具有较低的应力敏感性。
本申请通过调整添加组分与组分的含量，即组分与组分的含量协同作用在提高铁基非晶合金磁性能的同时降低了铁基非晶合金带材的应力敏感性。
为了进一步理解本发明，下面结合实施例对本发明提供的铁基非晶合金进行详细说明，本发明的保护范围不受以下实施例的限制。
实施例
1)制备铁基非晶合金带材
按照FeaBbSic表示的合金成分进行配料，使用工业用纯铁、硅、硼铁配制如表1所示的合金成分；合金成分除主元素外，具有不可避免的杂质元素，如C、Mn、S等。将不同成分所配物料依次按照硼铁、硅、纯铁的顺序顺次加入炉容为100kg的中频感应冶炼炉重熔(熔炼的温度为1300～1500℃，时间为80～120min)；钢水镇静结束，浇筑到喷包中，通过单辊平面流铸法制备非晶带宽为20mm非晶带材，制带过程中通过调整辊速、液位等参数制备出不同带厚的合金成分带材(制带过程中的辊速1000～1400r/min，控制出带线速度为20～30m/s，液位高度为200～300mm)。
2)铁基非晶合金带材非晶形成能力及饱和磁感应强度测试
采用XRD测试不同成分带材自由面，直至带厚到非晶态为止，表1显示各合金成分非晶极限带厚，使用VSM测试各非晶合金带材的饱和磁化强度值。 通过带材非晶形成能力以及饱和磁感应强度值综合评价合金成分。根据带材脆点数量评估带材可剪最大厚度，脆点评估是取带材长度为结晶器周长相等，沿着带材长度方向剪切带材，脆点个数不超过2个认为带材可剪切，等于2个则认为是该合金成分带材的极限可剪带厚。
表1不同成分的非晶铁基合金及其性能数据表
Figure PCTCN2017100862-appb-000001
表1呈现了不同合金成分随对应的非晶极限带厚、制带韧性极限带厚以及饱和磁感应强度。非晶极限带厚以及制带韧性极限厚度是对合金成分制带工艺 性的考量，上述带厚越厚，则对制带设备的要求度更加宽松。
相同的制带条件，合金成分非晶极限带厚愈厚，带材非晶度越高。对比例1～4虽然具有相对高的非晶极限带厚，可剪最大厚度在27μm以下，这不仅对制带设备的冷却强度提出更严苛的要求，也对铁芯组装效率，同时对变压器组装以及运行过程中易碎片埋下了伏笔，造成变压器运行的安全隐患增加；另外其饱和磁密不足1.57T，这使得非晶变压器设计宽泛性变窄，无法满足变压器高磁密的设计趋势；比较例6与实施例4～6对比可以看出，相同的Fe含量，Si含量越高，其可剪厚度变小。
对比例8～9合金非晶饱和磁密明显偏高这是变压器设计所期待的，最大可剪厚度介于36～38μm，在铁芯成型方面效率方面具有绝对优势，但是由其非晶极限带厚厚度值可以看出，其非晶形成能力明显不足，不具备制带顺行的工艺条件，同时也会影响其励磁功率和损耗。
从表1可以看出，从制带顺行和变压器设计综合考量，实施例1～11的合金成分具有较好的工艺顺行度和宽泛的变压器设计区间。
将表1中的选取带厚为26～28μm带宽为30mm的带材，卷绕成内径为50.5mm，外径为53.5～54mm的样环，使用箱式退火炉将样环进行去应力退火，退火选择在氩气保护的气氛中进行，由325～395℃之间，每个间隔为10℃，保温1h。热处理过程加沿着带材制备方向的磁场，磁场强度为1200A/m。使用硅钢测试仪测试热处理后带材激磁和损耗，测试条件分别在1.35T/50Hz与1.40T/50Hz，性能测试结果如表2所示：
表2实施例与对比例热处理后的性能数据表
Figure PCTCN2017100862-appb-000002
Figure PCTCN2017100862-appb-000003
由表2可以看出，在1.35T/50Hz条件下，比较例1～3与比较例8～9损耗值偏大，性能在0.12W/kg以上；而1.4T/50Hz条件下，比较例1～4及6励磁与损耗较1.35T/50Hz明显增加，且较其他样品在1.4T/50Hz明显偏大，这主要跟上述样品的饱和磁密低有关。非晶材料励磁和损耗随着磁密的增加而增加，特别是励磁功率表现的尤为突出。饱和磁感应强度大的非晶材料较低饱和磁感应强度材料，允许工作磁密更大，即在1.4T磁密下工作会显示相对低的励磁功率和损耗。正常来讲，比较例8～9在1.4T下测试，性能会更优，但因为其1.35T下性能偏大，所以在1.4T损耗及励磁有所增加，导致在1.4T下性能偏大。
实施例1～11在1.35/50Hz与1.40/50Hz表现出优异的软磁性能；1.35/50Hz损耗在0.11W/kg以内，1.4T/50Hz损耗在0.15W/kg以内。
3)应力敏感度测试
上述研究提到非晶材料具有相对低的不可避免的损耗值，非晶材料在装配成铁芯后受外应力影响性能会恶化。本研究建立非晶样环受应力模型，表征不同成分非晶制品受应力产生形变后的性能恶化情况，模拟非晶带材装配成变压 器铁芯受应力性能变化。
样品处理：选取如表3成分的非晶带材，绕制成内径为50.5mm，外径为53.5～54mm的样环，使用箱式退火炉将样环进行去应力退火，退火选择在氩气保护的气氛中进行。选取不同成分制备的样带，按照上述要求制作成样环进行热处理，热处理保温温度为325～395℃，每5度作为一个梯度进行热处理，保温时间为60～120min；磁场强度为800～1400A/m。选取上述热处理过程中各成分最佳热处理性能进行带材受应力后性能恶化情况实验。
应力的施加通过计算圆形带材缩进距离考量，样环进给量根据形变系数公式计算，如图1所示，图1为样环无应力状态的模拟试验装置示意图，图2样环施加应力状态的模拟试验装置示意图；样环在施加应力时，A板固定，在推动板B推动作用下给定样环进给量，样环受应力发生形变，固定推动板B，测试形变条件下材料的损耗P1和励磁功率Pe1，使用硅钢测试仪测试样品在1.35T/50Hz下的性能。
初始样环(无形变条件下)内径为D0，性能分别为P0、Pe0，形变后内径为D1，性能分别为P1、Pe1，定义应变系数＝(D1-D0)*100％/D0，损耗恶化系数＝(P1-P0)*100％/P0，激磁功率恶化系数＝(Pe1-Pe0)/Pe0。
综合考虑选取性能的差异和形变后性能恶化的允许度，本次实验规定性能恶化在50％以内的为可接受范围，该性能值对应的样环形变量为对应成分材料的最大允许形变系数值。
如表3可见，由于成分本身的差异其最佳性能略有差异，比较例9性能相对偏大，其他性能值基本在同一范畴。热处理温度优于成分差异在345～385℃不等。应力实验均选取各成分退火后最佳性能样品进行应力敏感性实验。
表3不同成分最佳热处理性能数据表
Figure PCTCN2017100862-appb-000004
Figure PCTCN2017100862-appb-000005
表4不同应变系数下损耗值及恶化系数数据表
Figure PCTCN2017100862-appb-000006
表4不同应变系数下损耗值及恶化系数数据表(续表)
Figure PCTCN2017100862-appb-000007
表5不同应变系数下励磁功率及恶化系数数据表
Figure PCTCN2017100862-appb-000008
Figure PCTCN2017100862-appb-000009
表5不同应变系数下励磁功率及恶化系数数据表(续表)
Figure PCTCN2017100862-appb-000010
表4、表5可以清楚看出，铁基非晶合金受应力影响而发生一定程度的性能恶化，且性能恶化系数随着形变系数的增加而增大。对比各成分损耗和励磁功率发现，励磁功率的恶化情况明显超过其损耗。励磁功率允许的恶化系数为6％，而损耗允许的恶化系数为10％。也就是说，对非晶带材施加外应力对励磁功率的影响更大。
对比实施例和比较例发现，不同成分受应力后性能恶化系数有较大差异，实施例4-6、12～13的非晶合金带材的损耗允许10.0％的应变系数，实施例4-6、12～13的励磁功率允许6％的恶化系数，综合考虑性能短板效应，实施例允许的恶化系数为6％；而比较例损耗和激磁功率的允许的应变系数分别是8％和2％，比较例允许的恶化系数为2％；由此可见，退火的后非晶带材实施例抗应 力敏感性有明显优势，允许更大的形变而保证材料性能在可接受范围内。
以上实施例的说明只是用于帮助理解本发明的方法及其核心思想。应当指出，对于本技术领域的普通技术人员来说，在不脱离本发明原理的前提下，还可以对本发明进行若干改进和修饰，这些改进和修饰也落入本发明权利要求的保护范围内。
对所公开的实施例的上述说明，使本领域专业技术人员能够实现或使用本发明。对这些实施例的多种修改对本领域的专业技术人员来说将是显而易见的，本文中所定义的一般原理可以在不脱离本发明的精神或范围的情况下，在其它实施例中实现。因此，本发明将不会被限制于本文所示的这些实施例，而是要符合与本文所公开的原理和新颖特点相一致的最宽的范围。

Claims (13)

  1. 一种如式(Ⅰ)所示的铁基非晶合金，
    FeaBbSic (Ⅰ)；
    其中，a、b与c分别表示对应组分的原子百分含量；79.5≤a≤82.5，11.0≤b≤13.5，6.5≤c≤8.5，a+b+c＝100。
  2. 根据权利要求1所述的铁基非晶合金，其特征在于，所述铁基非晶合金的饱和磁感应强度≥1.60T。
  3. 根据权利要求1所述的铁基非晶合金，其特征在于，所述Fe的原子百分含量为80.0≤a≤81.5。
  4. 根据权利要求1所述的铁基非晶合金，其特征在于，所述B的原子百分含量为11.0≤b≤12.5。
  5. 根据权利要求1所述的铁基非晶合金，其特征在于，所述Si的原子百分含量为7.0≤c≤8.0。
  6. 根据权利要求1所述的铁基非晶合金，其特征在于，所述铁基非晶合金中，a＝80.0，12.0≤b≤13.0，7.0≤c≤8.0。
  7. 根据权利要求1所述的铁基非晶合金，其特征在于，所述铁基非晶合金中，a＝80.5，11.5≤b≤12.5，7.0≤c≤8.0。
  8. 根据权利要求1所述的铁基非晶合金，其特征在于，所述铁基非晶合金中，81.0≤a≤81.5，11.0≤b≤13.0，7.0≤c≤8.0。
  9. 一种如式(Ⅰ)所示的铁基非晶合金带材的制备方法，包括：
    按照式(Ⅰ)的原子百分比进行元素的配料，将配料后的原料进行熔炼，将熔炼后的熔液升温保温后进行单辊快淬，得到铁基非晶合金带材；
    FeaBbSic (Ⅰ)；
    其中，a、b与c分别表示对应组分的原子百分含量；79.5≤a≤82.5，11.0≤b≤13.5，6.5≤c≤8.5，a+b+c＝100。
  10. 根据权利要求9所述的制备方法，其特征在于，所述单辊快淬之后还包括：
    将单辊快淬后的铁基非晶合金进行热处理。
  11. 根据权利要求10所述的制备方法，其特征在于，所述热处理之前还包括：将单辊快淬后的铁基非晶合金绕制成内径为50.5mm，外径为53.5～54mm的样环，热处理后样环的损耗允许的应变系数为10.0％，激磁功率允许的应变系数为6％。
  12. 根据权利要求10所述的制备方法，其特征在于，所述热处理后的铁基非晶合金带材的矫顽力≤3.5A/m；在50Hz，1.35T条件下，所述热处理后的铁基非晶合金带材的激磁功率＜0.1450VA/kg，铁芯损耗＜0.1100W/kg；在50Hz，1.40T条件下，所述热处理后的铁基非晶合金带材的激磁功率＜0.1700VA/kg，铁芯损耗＜0.1500W/kg。
  13. 根据权利要求10或11所述的制备方法，其特征在于，所述铁基非晶合金带材为完全非晶状态，临界厚度至少为75μm，可剪极限带厚至少为29μm。
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