Iron-based amorphous alloy and method for manufacturing the same

Abstract

The application provides an iron-based amorphous alloy and a preparation method thereof, and belongs to the technical field of metal functional material preparation. The preparation method of the iron-based amorphous alloy mainly uses the phenomenon that the atomic cluster structure in the iron-based alloy melt changes with temperature, simulates the characteristics that the types and quantity of high-symmetry atomic clusters in the iron-based alloy melt change with the temperature of the iron-based alloy melt, finds the temperature with the largest quantity of high-symmetry atomic clusters as the overheating treatment temperature of the alloy melt, uses the set overheating treatment temperature to increase the quantity of high-symmetry atomic clusters in the melt, and rapidly solidifies the high-symmetry atomic clusters into an amorphous solid alloy, so that the controllable preparation of the amorphous solid iron-based alloy with low coercivity, low hysteresis loss and high magnetic permeability is realized. The preparation method creates a new concept and method for the preparation of the amorphous iron-based alloy with low coercivity, low hysteresis loss and high magnetic permeability.

Description

Technical Field

[0001] This invention belongs to the field of metal functional materials preparation technology, and in particular relates to an iron-based amorphous alloy and its preparation method. Background Technology

[0002] As the external magnetic field changes, the magnetic flux density of iron-based amorphous alloys changes accordingly. The strength of the reverse magnetic field required to reduce the magnetic flux density of a saturated magnetized iron-based amorphous alloy to zero is called the coercivity. Changes in the magnetic flux density of iron-based amorphous alloys are always accompanied by the movement of magnetic domain walls. Energy loss, called hysteresis loss, is inevitable during this movement. The smaller the resistance to the movement of the domain walls, the smaller the coercivity, the less energy is lost, and the smaller the hysteresis loss. Simultaneously, the smaller the resistance to the movement of the domain walls, the faster the response to the external magnetic field, and the higher the permeability. In other words, low coercivity, low hysteresis loss, and high permeability mean that iron-based amorphous alloys lose less energy during changes in the (high-frequency) external magnetic field. Therefore, coercivity, hysteresis loss, and permeability are important parameters for evaluating the magnetic properties of iron-based amorphous alloys. Since the movement of magnetic domain walls is always accompanied by changes in the external magnetic field, and the ease with which the domain walls move is closely related to the microstructure of the iron-based amorphous alloy itself... Therefore, the microstructure of iron-based amorphous alloys is an important factor affecting coercivity, hysteresis loss, and permeability. To reduce the free energy of the system, the atoms in iron-based alloy melts exist in cluster structures. Iron-based amorphous alloys (iron-based amorphous solid alloys) retain the atomic cluster structure characteristics of iron-based alloy melts; that is, iron-based amorphous alloys are composed of a large number of interconnected atomic clusters. Therefore, atomic clusters are the basic structural units constituting the microstructure of iron-based amorphous alloys.

[0003] Only by basing the analysis on atomic cluster structures can the microstructure of amorphous alloys be controlled. Existing technologies have reported methods for controlling the microstructure of amorphous solid alloys based on atomic cluster structures. For example, Chinese patent CN109778084A discloses a method for controlling the microstructure of amorphous solid alloys using the configuration and quantity of atomic clusters in the melt. Specifically, it calculates the configuration and quantity of atomic clusters in the melt at different temperatures, obtains the calculation results of the changes in atomic cluster configuration and quantity with temperature, selects the desired atomic cluster configuration and quantity based on the calculation results, then heat-treats the melt at a temperature corresponding to the selected atomic cluster configuration and quantity, and finally rapidly solidifies the overheated amorphous alloy melt to obtain an amorphous solid alloy ribbon containing the selected atomic cluster configuration and quantity. This method only discloses how to control the microstructure of amorphous solid alloys based on a single atomic cluster structure, but it cannot directly establish a correlation between the atomic cluster structure and a specific macroscopic property of the amorphous solid alloy (such as coercivity, hysteresis loss, permeability, etc.). Furthermore, this method yields at most less than 10% of the total number of clusters of any single type, and it has no correlation with reducing the internal stress and free volume of amorphous alloys. Therefore, how to effectively control the coercivity, hysteresis loss, permeability, and other magnetic properties of iron-based amorphous alloys from the microstructure of atomic clusters has become one of the key and important scientific and technological problems that urgently need to be solved in the field of amorphous solid alloys.

[0004] In view of this, the present invention is hereby proposed. Summary of the Invention

[0005] The purpose of this invention is to overcome the shortcomings of existing technologies by providing an iron-based amorphous alloy and its preparation method. This invention can control the number of highly symmetric atomic clusters by changing the overheating temperature of the amorphous alloy melt, thereby controlling the coercivity, hysteresis loss, and permeability of the amorphous solid iron-based alloy.

[0006] The inventors discovered that, similar to the influence of multiple factors on domain wall movement in crystalline magnetic materials, such as microstructure (lattice defects, dislocations, grain boundaries, microcracks, and internal stress), the domain wall movement in iron-based amorphous magnetic alloys is primarily affected by the internal stress and free volume of the amorphous alloy itself, which pins the domain walls. The interconnections between numerous atomic clusters in amorphous alloys are the main source of the cumulative effect of internal stress and free volume. Clusters form extensive spatial structures mainly through point, line, and surface connections. Although the gaps between two interconnected clusters are small, the sheer number of clusters means that the total free volume in amorphous alloys can reach approximately 3% of the total volume of the material. This results in a slightly lower density for amorphous alloys compared to crystalline materials of the same composition and also acts as a microstructural defect hindering domain movement. Therefore, free volume is one of the most important factors affecting the microstructure of amorphous alloys. When two clusters are connected by sharing a single surface vertex, almost no interfacial stress is generated, but the largest void is formed between the two clusters, contributing the most to the free volume. When two clusters are connected collinearly, if the edge lengths of the cluster surfaces are the same, a coherent connection is formed, which also does not generate stress, and the void and free volume between the clusters are smaller than those generated by sharing a single vertex. When the edge lengths of the cluster surfaces are different, a non-coherent connection is formed, generating mismatch stress. When clusters are connected coplanarly, if there are equivalent planes on the cluster surfaces, the contact of these equivalent planes forms a coherent interface, and there is no interfacial mismatch stress. Two clusters sharing an equivalent plane also minimizes the void and free volume between the clusters. However, when unequal planes contact each other, a mismatched non-coherent interface is formed, generating interfacial stress. In other words, the interfacial stresses and voids existing between clusters constitute the main sources of internal stress and free volume in amorphous alloys. They generate additional magnetic anisotropy, resisting domain wall movement and influencing the microstructure of amorphous alloys, thereby directly affecting their macroscopic magnetic properties such as coercivity, hysteresis loss, and permeability. Therefore, reducing coercivity and hysteresis loss, and increasing permeability, requires reducing the internal stress and free volume of iron-based amorphous alloys.

[0007] To utilize atomic clusters to reduce internal stress and free volume in amorphous alloys, it is first necessary to identify which atomic clusters in the alloy melt are beneficial for reducing internal stress and free volume. Through further practical research, the inventors discovered that the structural differences in atomic clusters stem from the distribution of atoms within the cluster. These differences are controlled by cluster symmetry, particularly rotational symmetry, which has the greatest impact on cluster structure. For example, besides centrosymmetry and mirror reflection symmetry, six 5-fold rotational symmetries result in an icosahedral structure, with all surfaces covered by 20 equivalent planes and a solid angle interval of 36 degrees between adjacent equivalent planes. Conversely, 3-fold and 4-fold rotational symmetries result in cubic clusters with only 6 equivalent planes on their surface, and an angle of 90 degrees between adjacent equivalent planes. 5-fold rotational symmetry can also be combined with 6-fold rotational symmetry to further increase the number of coordinating atoms and equivalent planes, while reducing the angle between adjacent equivalent planes. Adding a sixth rotation to an icosahedron increases the number of equivalent planes to 24, adding two sixth rotations increases it to 26, and adding three sixth rotations increases it to 28, resulting in an increase in the number and density of equivalent planes. When high-symmetry clusters dominate in amorphous alloys, a large number of these clusters become neighboring clusters. Based on the principle of minimum interface energy, neighboring high-symmetry clusters preferentially form coherent interfaces without mismatch stress, reducing inter-cluster porosity. Therefore, increasing the number of high-symmetry clusters effectively reduces the internal stress and free volume of amorphous alloys, facilitating domain movement and reducing coercivity. When the direction of the external magnetic field changes, the domain walls experience less resistance and transition more easily as they move between these spatial equivalent planes, because the physical state of the material always changes along the lowest energy path when the external field changes. This improves the response speed of iron-based amorphous alloys to external magnetic fields and reduces energy loss during cyclic magnetization due to slow response speed. Changes in the external magnetic field cause energy loss in iron-based amorphous alloys, which is converted into heat, increasing the temperature and reducing the efficiency of electromagnetic devices. To improve the efficiency of electromagnetic devices, iron-based amorphous alloys with low coercivity, low hysteresis loss, and high permeability are required. Although high rotational symmetry atomic clusters are beneficial for reducing internal stress and free volume in amorphous alloys, a small number of high rotational symmetry atomic clusters cannot form a synergistic effect and cannot produce significant macroscopic effects in iron-based amorphous alloys. Only when the number of high rotational symmetry atomic clusters in the iron-based amorphous alloy is dominant can the resistance to domain wall movement and hysteresis loss be effectively reduced through synergistic effects. Therefore, increasing the number of high rotational symmetry atomic clusters is an important way to achieve low coercivity, low hysteresis loss, and high permeability in iron-based amorphous alloys. It can be seen that the macroscopic properties of amorphous alloys are highly dependent on and sensitive to the number of high rotational symmetry atomic clusters, and controlling the number of high rotational symmetry atomic clusters in amorphous alloys is one of the important ways to improve the properties of amorphous solid alloys (such as coercivity, hysteresis loss, and permeability).

[0008] To achieve the above objectives, the present invention adopts the following technical solution: The first objective of this invention is to provide a method for preparing iron-based amorphous alloys, comprising the following steps: Step 1: Based on the composition of the iron-based amorphous alloy to be prepared, simulate and calculate the relationship between the type and number of atomic clusters in the iron-based alloy melt and the temperature of the iron-based alloy melt, and obtain the calculation results of the change of the number of high symmetry atomic clusters with the temperature of the iron-based alloy melt. Step 2: Based on the calculation results, select the temperature of the iron-based alloy melt corresponding to the highest number of high-symmetry atomic clusters as the overheating treatment temperature of the iron-based alloy melt. Step 3: The iron-based alloy melt is subjected to heat treatment at the overheating temperature to obtain the overheated iron-based alloy melt. A temperature 8-12°C higher than the overheating temperature was selected as the pouring temperature of the iron-based alloy melt after overheating. Step 4: Heat the heat-treated iron-based alloy melt to the casting temperature, and then perform supercooling solidification to obtain an iron-based amorphous alloy with low coercivity, low hysteresis loss and high permeability.

[0009] Furthermore, based on the above-mentioned technical solution of the present invention, in step 1, the simulation calculation includes: without changing the composition of the iron-based alloy, using the molecular dynamics method to calculate the two-body function to simulate the types and quantities of atomic clusters in the iron-based alloy melt at different temperatures, obtaining the relationship between the types and quantities of atomic clusters in the iron-based alloy melt and the temperature of the iron-based alloy melt, and obtaining the calculation results of the quantity of highly symmetric atomic clusters changing with the temperature of the iron-based alloy melt; And / or, the melt temperature of the iron-based alloy is 1200-1600℃.

[0010] Furthermore, based on the above-mentioned technical solution of the present invention, in step 1, the structure of the atomic cluster is described by a Voronoi polyhedron with a rotational configuration. The selection of high-symmetry atomic clusters is based on the fact that the sum of the number of clusters N5 and N6 in the iron-based alloy melt exceeds 60% of the total number of vertices of the Voronoi polyhedron and the number of such atomic clusters with this characteristic exceeds 50% of the total number of all atomic clusters.

[0011] Furthermore, based on the above-mentioned technical solution of the present invention, in step 2, the melting temperature of the iron-based alloy corresponding to the largest number of high-symmetry atomic clusters is determined according to the calculation results, and the melting temperature of the iron-based alloy corresponding to the largest number of high-symmetry atomic clusters is selected as the overheating treatment temperature of the iron-based alloy melt.

[0012] Furthermore, based on the above technical solution of the present invention, in step 3, the heat preservation treatment time is 2-7 hours; And / or, the casting temperature of the heat-treated iron-based alloy melt is 10°C higher than the heat treatment temperature. o C.

[0013] Furthermore, based on the above-mentioned technical solution of the present invention, in step 3, the iron-based alloy melt is first heated to a preset temperature higher than the overheating treatment temperature, held at the preset temperature for a short time, and then cooled to the overheating treatment temperature and held at the overheating treatment temperature to obtain the overheated iron-based alloy melt.

[0014] Furthermore, based on the above technical solution of the present invention, in step 3, the preset temperature is 100-250°C higher than the overheating treatment temperature, the temperature is held at the preset temperature for 0.3-1 hour, and the heating rate to the preset temperature is 10-30°C / min. And / or, the cooling rate from the preset temperature to the overheating treatment temperature is 10-20℃ / min, and the temperature is maintained at the overheating treatment temperature for 2-7 hours.

[0015] Furthermore, based on the above-mentioned technical solution of the present invention, in step 4, the overheated iron-based alloy melt is heated to the pouring temperature, and then the iron-based amorphous alloy is prepared by high-speed planar continuous casting. The specific steps include: under the conditions of set cooling water temperature and cooling roller copper sleeve thickness, the overheated iron-based alloy melt is heated to the pouring temperature, and then continuously poured through a nozzle onto the surface of the high-speed rotating cooling roller copper sleeve, and rapidly supercooled and solidified to form an iron-based amorphous alloy with low coercivity, low hysteresis loss and high permeability.

[0016] Furthermore, based on the above technical solution of the present invention, in step 4, the linear velocity of the surface of the copper sleeve of the cooling roller is 20-25 m / s; And / or, the thickness of the copper sleeve of the cooling roller is 10-20 mm; And / or, the cooling water temperature is 20-40°C. o C; And / or, the heating rate of the heat-treated iron-based alloy melt to the casting temperature is 8-12°C / min.

[0017] Furthermore, based on the above technical solution of the present invention, in step 4, the iron-based alloy melt solidifies in the state with the largest number of highly symmetric atomic clusters. And / or, the iron-based amorphous alloy exists in the form of a thin strip, preferably, the thickness of the thin strip is 20-30 μm.

[0018] The second objective of this invention is to provide an iron-based amorphous alloy, which is prepared by the above-described method for preparing iron-based amorphous alloys.

[0019] Furthermore, based on the above-mentioned technical solution of the present invention, the iron-based amorphous alloy includes FeCr-based amorphous alloy and / or FeSiB-based amorphous alloy. And / or, the coercivity of the iron-based amorphous alloy is 0.5-3 A / m; And / or, the hysteresis loss of the iron-based amorphous alloy is 0.14-0.2 W / kg; And / or, the magnetic permeability of the iron-based amorphous alloy is 260-600 mH / m.

[0020] The technical solution of the present invention has at least the following advantages over the prior art: (1) This invention provides a method for preparing iron-based amorphous alloys. It mainly utilizes the phenomenon that the atomic cluster structure in the alloy melt changes with the temperature of the iron-based alloy melt. By simulating and calculating the characteristics of the changes in the types and quantities of high-symmetry atomic clusters in the iron-based alloy melt with temperature, it was found that the temperature containing the largest number of high-symmetry atomic clusters is used as the overheating temperature of the alloy melt. By using the set overheating temperature to increase the number of high-symmetry atomic clusters in the iron-based alloy melt, and rapidly solidifying them into an amorphous solid alloy, the controllable preparation of amorphous solid iron-based alloys with low coercivity, low hysteresis loss, and high permeability is achieved. This preparation method pioneers a new concept and method for preparing amorphous iron-based alloys with low coercivity, low hysteresis loss, and high permeability. The process method for controlling the number of high-symmetry atomic clusters in amorphous alloys established in this invention is not only a key technology for meeting the research and engineering production needs of important amorphous alloy thin strip materials, but also an important technology urgently needed for the development of high-performance amorphous solid iron-based alloy thin strip materials.

[0021] (2) The preparation method provided by the present invention is applicable to all amorphous iron-based alloy thin strips, especially to the preparation of amorphous iron-based alloy thin strips with low coercivity, low hysteresis loss and high permeability when the composition of the alloy melt fluctuates greatly.

[0022] (3) The method for preparing iron-based amorphous alloys provided by the present invention has the characteristics of simple implementation, high efficiency, low cost, strong controllability and repeatability, and high technical reliability, and is suitable for wide application in the field of metal functional material preparation technology. Attached Figure Description

[0023] To more clearly illustrate the specific embodiments of the present invention or the technical solutions in the prior art, the drawings used in the description of the specific embodiments or the prior art will be briefly introduced below. Obviously, the drawings described below are some embodiments of the present invention. For those skilled in the art, other drawings can be obtained from these drawings without creative effort.

[0024] Figure 1 This is a flowchart illustrating a method for preparing iron-based amorphous alloys with low coercivity, low hysteresis loss, and high permeability proposed in this invention. Figure 2 The calculation results of the two-body function of the Fe82Si8B8C1Cr1 alloy melt as a function of temperature in Example 1 of the present invention; Figure 3 This is a schematic diagram of a high-resolution image of an amorphous solid alloy thin strip obtained by rapid solidification technology from a Fe82Si8B8C1Cr1 alloy melt overheated at 1395℃ in Embodiment 1 of the present invention. Figure 4 The calculation results of the two-body function of Fe79Si10B11 alloy melt as a function of temperature in Example 2 of the present invention; Figure 5 This is a schematic diagram of high-resolution image measurement of amorphous solid alloy thin strip obtained by using rapid solidification technology on Fe79Si10B11 alloy melt overheated at 1380℃ in Embodiment 2 of the present invention. Detailed Implementation

[0025] To make the objectives, technical solutions, and advantages of this invention clearer, the technical solutions in the embodiments of this invention will be clearly and completely described below in conjunction with the embodiments of this invention. Those skilled in the art should understand that the embodiments described are merely illustrative of the invention and should not be considered as specific limitations thereof. All other embodiments obtained by those skilled in the art based on the embodiments of this invention without creative effort are within the scope of protection of this invention. Process parameters not specifically specified in the following embodiments are generally performed under conventional conditions.

[0026] The endpoints and any values ​​of the ranges disclosed in this invention are not limited to the precise ranges or values, and these ranges or values ​​should be understood to include values ​​close to these ranges or values. For numerical ranges, the endpoint values ​​of the various ranges, the endpoint values ​​of the various ranges and individual point values, and individual point values ​​can be combined with each other to obtain one or more new numerical ranges, which should be considered as specifically disclosed in this invention.

[0027] According to a first aspect of the present invention, a method for preparing an iron-based amorphous alloy is provided, comprising the following steps: Step 1: Based on the composition of the iron-based amorphous alloy to be prepared, simulate and calculate the relationship between the type and number of atomic clusters in the iron-based alloy melt and the temperature of the iron-based alloy melt, and obtain the calculation results of the change of the number of high symmetry atomic clusters with the temperature of the iron-based alloy melt. It should be noted that the "quantity" in step 1 above can refer to a specific numerical value or a quantity ratio. For example, the number of highly symmetric atomic clusters can refer to the total number of highly symmetric atomic clusters, or it can refer to the ratio of the number of highly symmetric atomic clusters to the total number of atomic clusters, similar to a quantity percentage (quantity proportion).

[0028] Step 2: Based on the calculation results, select the temperature of the iron-based alloy melt corresponding to the highest number of high-symmetry atomic clusters as the overheating treatment temperature of the iron-based alloy melt. Step 3: The iron-based alloy melt is subjected to heat treatment at the overheating temperature to obtain the overheated iron-based alloy melt. A temperature 8-12°C higher than the overheating temperature was selected as the pouring temperature of the iron-based alloy melt after overheating. Step 4: Heat the heat-treated iron-based alloy melt to the casting temperature, and then perform supercooling solidification to obtain an iron-based amorphous alloy with low coercivity, low hysteresis loss and high permeability.

[0029] The technical mechanism of this invention is as follows: Since it is impossible to measure atomic clusters in a melt experimentally, using computer simulations of the two-body distribution function of an alloy melt at different temperatures is undoubtedly an effective means of directly studying the atomic cluster structure of the melt at the atomic distribution level. Although this information is statistical, it can comprehensively reflect the atomic cluster structure information of the melt. Molecular dynamics is used to simulate the two-body distribution function of similar and dissimilar atoms in the melt. Based on the melt's composition and density, and the set interatomic interaction potentials (such as embedded atom potential EAM, Stillinger-Weber potential, etc.), atomic positions are randomly distributed to form an initial melt structure configuration. Molecular dynamics algorithms (such as the Verlet algorithm) are used to solve the atomic motion equations, simulating the dynamic behavior of the melt at certain temperatures and time scales. During the simulation, the position information of atoms is recorded at regular time steps, and the number of atoms at different distances r centered on each atom is counted. The atomic distribution is statistically analyzed to reveal the types of melt cluster structures and the percentage of each cluster structure type. To improve computational accuracy, the following steps were taken in the simulation: selecting appropriate numerical methods to reduce truncation error (such as higher-order Runge-Kutta methods); using adaptive algorithms to dynamically adjust the step size or grid density based on error estimates during the computation process, optimizing the step size or grid size to avoid increased truncation error caused by excessively large step sizes and accumulated rounding error caused by excessively small step sizes (balancing truncation error and rounding error); and using high-precision data types (such as double-precision floating-point numbers) provided by numerical computation libraries to reduce rounding error.

[0030] The structural characteristics of melt atomic clusters are primarily determined by the first peak of the two-body distribution function closest to the origin; the greater the peak intensity, the more atoms are distributed around the central atom. These clusters surrounding the central atom form Voronoi polyhedra with a certain rotational configuration, and are characterized by parametric...<N3, N4, N5, N6> The shape is defined by Nj, where Nj represents the number of vertices with j edges. All vertices of the icosahedral cluster are N5, and a total of 12 N5 vertices make the equivalent face cover the entire surface of the icosahedral cluster, classifying it as a high-symmetry cluster. In fact, the number of N5 vertices only needs to reach or approach half the total number of vertices for the equivalent face to form a channel along the cluster surface. Since N6 has a similar function to N5, and the number of N6 vertices in the Voronoi polyhedron is small, the sum of the number of N5 and N6 vertices is used as the basis for selecting high-symmetry rotational atomic clusters. At different iron-based alloy melting temperatures, the number of various clusters in the alloy melt is calculated, and the selection of high-symmetry atomic clusters is based on the sum of the number of N5 and N6 clusters exceeding half the total number of vertices. When the number of high-symmetry atomic clusters dominates the total number of clusters in the alloy melt, the corresponding temperature can be considered the temperature with the highest number of high-symmetry atomic clusters and is selected as the optimal overheating temperature for the iron-based alloy melt. By heating the alloy melt to a selected overheating temperature and rapidly solidifying it into an amorphous solid alloy ribbon, the preparation of the iron-based amorphous alloy with the highest number of highly symmetric atomic clusters is completed.

[0031] Furthermore, in existing technologies, a single overheating temperature is typically used during overheating and casting. The entire process involves calculation, heating to the target temperature, holding at that temperature, and casting, with the overheating temperature being the same as the casting temperature. Through extensive practical experience, the inventors discovered that although the time it takes for the molten iron-based alloy to travel from the crucible to the surface of the cooling roller during casting is very short, the temperature of the molten iron-based alloy still decreases. If casting is performed at a temperature equivalent to the overheating temperature (i.e., the casting temperature equals the overheating temperature), the actual temperature of the molten iron-based alloy at the instant of supercooling and solidification (in contact with the cooling roller) is not the calculated temperature corresponding to the highest number of highly symmetric atomic clusters. Therefore, this invention adopts a dynamic temperature control process logic of "pouring temperature = overheating treatment temperature (the temperature at which the number of high-symmetry atomic clusters in the iron-based alloy melt is the highest) + temperature compensation value". This effectively solves the technical problem of temperature drop during the pouring process causing deviation from the target state, ensuring that the atomic clusters in the iron-based alloy melt reach the same stable state as the calculated result during solidification. By separating the "overheating treatment temperature" and the "pouring temperature", it ensures that the amorphous solid alloy (thin strip) rapidly solidified at the instant the iron-based alloy melt (in contact with the cooling roller) undergoes overcooling solidification has the highest number of high-symmetry atomic clusters. The temperature compensation value mentioned above is the difference between the pouring temperature and the overheating treatment temperature in step 3, i.e., 8-12℃. This temperature compensation value should not be too large (e.g., exceeding 12℃) nor too small (e.g., below 8℃). Too large or too small a temperature compensation value can easily cause the number of clusters to deviate from the selected value (the calculated maximum number of high-symmetry atomic clusters) by at least 5%, and the greater the deviation beyond this compensation temperature, the greater the deviation. Therefore, typical but non-limiting temperatures are 8℃, 8.5℃, 9℃, 9.5℃, 10℃, 10.5℃, 11℃, 11.5℃, or 12℃, etc. Only by controlling the temperature compensation value within a specific range can the purpose of temperature compensation be achieved, thus solving the technical problem of deviation from the target state caused by temperature drop during casting (i.e., solidification is not at the temperature with the highest number of high-symmetry atomic clusters).

[0032] As an optional embodiment of the technical solution of the present invention, in step 1, the simulation calculation includes: without changing the composition of the iron-based alloy, using the molecular dynamics method to calculate the two-body function to simulate the types and quantities of atomic clusters in the iron-based alloy melt at different temperatures, obtaining the relationship between the types and quantities of atomic clusters in the iron-based alloy melt and the temperature of the iron-based alloy melt, and obtaining the calculation results of the quantity of highly symmetric atomic clusters changing with the temperature of the iron-based alloy melt.

[0033] As an optional embodiment of the technical solution of the present invention, in step 1, when simulating the relationship between the type and quantity of atomic clusters in the iron-based alloy melt and the temperature of the iron-based alloy melt, the temperature of the iron-based alloy melt is controlled between 1200-1600℃, for example, 1200℃, 1250℃, 1280℃, 1300℃, 1350℃, 1380℃, 1390℃, 1400℃, 1420℃, 1450℃, 1480℃, 1500℃, 1520℃, 1550℃, 1580℃, or 1600℃. If the temperature is outside the above temperature range, the iron-based alloy may be solid (or the melt contains some solid particles), or it exceeds the allowable temperature range of the manufacturing equipment. Therefore, the temperature of the iron-based alloy melt is controlled within the above numerical range.

[0034] As an optional embodiment of the technical solution of the present invention, in step 1, the atomic cluster structure is described using a Voronoi polyhedron with a rotational configuration. The selection of high-symmetry atomic clusters is based on the fact that the sum of the number of vertices of clusters N5 and N6 in the iron-based alloy melt exceeds 60% of the total number of vertices of the Voronoi polyhedron, and the number of such atomic clusters with this characteristic exceeds 50% of the total number of all atomic clusters.

[0035] As an optional embodiment of the technical solution of the present invention, in step 2, the temperature of the iron-based alloy melt corresponding to the largest number of high symmetry atomic clusters is determined according to the calculation results, and the temperature of the iron-based alloy melt corresponding to the largest number of high symmetry atomic clusters is selected as the overheating treatment temperature of the iron-based alloy melt.

[0036] As an optional embodiment of the technical solution of the present invention, in step 3, the heat preservation time is 2-7 hours, such as 2 hours, 4 hours, 5 hours, 6 hours and 7 hours, and any numerical range between two points.

[0037] In a preferred embodiment of the technical solution of the present invention, in step 3, the iron-based alloy melt is first heated to a preset temperature higher than the overheating treatment temperature, held at the preset temperature for a short time, and then cooled to the overheating treatment temperature and held at the overheating treatment temperature to obtain the overheated iron-based alloy melt.

[0038] The iron-based alloy melt is first heated to a preset temperature and then held at that temperature for a short time. This process ensures complete alloying of the various elements within the melt. Because the overheating temperature does not reach the melting point of iron, the melt still contains residual solid iron, existing in a solid-liquid two-phase state. Under these conditions, complete alloying of the elements takes a relatively long time. The preset temperature, being higher than the melting point of iron, allows for rapid and complete alloying, forming a fully liquid structure. Then, the melt is cooled to the overheating temperature. This process also prevents iron from solidifying. According to the alloy phase diagram, after alloying, the overheating temperature falls within the pure liquid temperature range.

[0039] In a preferred embodiment of the technical solution of the present invention, in step 3, the preset temperature is 100-200℃ higher than the overheating treatment temperature (e.g., 100℃, 120℃, 140℃, 150℃, 160℃, 180℃ or 200℃, etc.), and the temperature is maintained at the preset temperature for 0.5-1 hour (e.g., 0.5 hours, 0.6 hours, 0.8 hours or 1 hour, etc.), and the heating rate to the preset temperature is 10-30℃ / min (e.g., 10℃ / min, 12℃ / min, 15℃ / min, 18℃ / min, 20℃ / min, 25℃ / min, 28℃ / min or 30℃ / min, etc.).

[0040] And / or, the cooling rate from the preset temperature to the overheating treatment temperature is 10-20℃ / min (e.g., 10℃ / min, 12℃ / min, 15℃ / min, 18℃ / min or 20℃ / min, etc.), and the temperature is held at the overheating treatment temperature for 2-7 hours (e.g., 2 hours, 4 hours, 5 hours, 6 hours and 7 hours).

[0041] In a preferred embodiment of the technical solution of the present invention, in step 3, the casting temperature of the overheated iron-based alloy melt is 10°C higher than the overheating temperature. o C.

[0042] As an optional embodiment of the technical solution of the present invention, in step 4, the heat-treated iron-based alloy melt is heated to the pouring temperature, and then the iron-based amorphous alloy is prepared by high-speed planar continuous casting. The specific steps include: under the set cooling water temperature and cooling roller copper sleeve thickness conditions, the heat-treated iron-based alloy melt is heated to the pouring temperature, and then continuously poured into the surface of the high-speed rotating cooling roller copper sleeve through the nozzle, and quickly supercooled and solidified to form an iron-based amorphous alloy with low coercivity, low hysteresis loss and high permeability.

[0043] As an optional embodiment of the technical solution of the present invention, in step 4, the linear velocity of the surface of the copper sleeve of the cooling roller is 20-25 m / s (meters per second), for example, 20 m / s, 21 m / s, 22 m / s, 23 m / s, 24 m / s or 25 m / s, etc., and the numerical range between any two points. And / or, the thickness of the copper sleeve of the cooling roller is 10-20 mm, for example, 10 mm, 12 mm, 14 mm, 15 mm, 16 mm, 18 mm or 20 mm, etc., and the numerical range between any two points; And / or, the cooling water temperature is 20-40°C. o C, for example, is 20. o C, 25 o C, 30 o C, 35 o C or 40 o C and the numerical range between any two points; And / or, the heating rate of the heat-treated iron-based alloy melt to the casting temperature is 8-12℃ / min, for example, 8℃ / min, 10℃ / min or 12℃ / min.

[0044] As an optional embodiment of the technical solution of the present invention, in step 4, the iron-based alloy melt solidifies in the state with the largest number of highly symmetric atomic clusters. And / or, the iron-based amorphous alloy exists in the form of a thin strip, preferably, the thickness of the strip is 20-30 μm, for example, 20 μm, 22 μm, 24 μm, 25 μm, 28 μm or 30 μm, etc., and any numerical range between any two points; the width of the strip is 100-300 mm, for example, 100 mm, 120 mm, 144 mm, 170 mm, 180 mm, 213 mm, 240 mm, 260 mm, 282 mm or 300 mm, etc., and any numerical range between any two points; According to a second aspect of the present invention, an iron-based amorphous alloy is provided, which is prepared by the preparation method provided in the first aspect of the present invention.

[0045] As an optional embodiment of the technical solution of the present invention, the iron-based amorphous alloy includes FeCr-based amorphous alloy and / or FeSiB-based amorphous alloy.

[0046] As an optional embodiment of the technical solution of the present invention, the coercivity of the iron-based amorphous alloy is 0.5-3 A / m, such as 0.5 A / m, 1.0 A / m, 1.5 A / m, 2.0 A / m, 2.5 A / m, 2.7 A / m, 2.8 A / m or 3 A / m, etc., and the numerical range between any two points; And / or, the hysteresis loss of iron-based amorphous alloys is 0.14-0.2 W / kg, for example 0.14 W / kg, 0.15 W / kg, 0.16 W / kg, 0.18 W / kg or 0.2 W / kg, and the numerical range between any two points; And / or, the magnetic permeability of the iron-based amorphous alloy is 260-600 mH / m, for example, 260 mH / m, 280 mH / m, 300 mH / m, 400 mH / m, 500 mH / m, 600 mH / m, etc., and the numerical range between any two points.

[0047] As a preferred embodiment of the technical solution of the present invention, the method for preparing iron-based amorphous alloys with low coercivity, low hysteresis loss and high permeability includes the following steps: Step 1: Calculate the changes in the types and quantities of atomic clusters in the iron-based alloy melt with temperature. Without changing the composition of the iron-based alloy, the types and quantities of atomic clusters in the iron-based alloy melt at different temperatures are simulated using the molecular dynamics method to calculate the two-body function. Based on the calculated quantities of various clusters at different temperatures, and according to the listed criteria for identifying high-symmetry atomic clusters, the quantities of high-symmetry atomic clusters at each temperature can be obtained, thus revealing the characteristics of how the quantity of high-symmetry atomic clusters changes with the temperature of the iron-based alloy melt. It should be noted that the method of simulating the types and quantities of atomic clusters in the iron-based alloy melt at different temperatures using the molecular dynamics method to calculate the two-body function is existing technology, and the specific process will not be elaborated further.

[0048] Step 2, determine the temperature of the iron-based alloy melt with the most high symmetry atomic clusters: (1) Based on the calculation results, find the temperature of the iron-based alloy melt with the most high symmetry atomic clusters; (2) Set the calculated temperature with the most high symmetry atomic clusters as the overheating temperature of the iron-based alloy melt. Step 3, determine the overheating temperature and casting temperature of the amorphous alloy melt based on the calculation results: (1) Melt the selected iron-based alloy (i.e., heat the iron-based alloy to the preset temperature for a short time and then cool it down to the temperature with the most high symmetry atomic clusters (i.e., overheating temperature), and perform overheating treatment (heating treatment) on the iron-based alloy melt for 2-7 hours at the overheating temperature. (2) In order to enable the iron-based alloy melt to solidify rapidly at the temperature with the highest number of highly symmetric atomic clusters, the casting temperature of the iron-based alloy melt is set to be 8-12°C (e.g., about 10°C) higher than the overheating temperature. Step 4: Solidify the iron-based alloy melt at the temperature with the highest number of highly symmetric atomic clusters. The specific steps are as follows: Under the set cooling water temperature and cooling roller copper sleeve thickness conditions, heat the overheated iron-based alloy melt to the casting temperature, and then continuously pour it through the nozzle onto the surface of the high-speed rotating cooling roller copper sleeve (the linear velocity of the cooling roller copper sleeve surface is, for example, 20 m / s), and quickly solidify it into an amorphous solid alloy ribbon (iron-based amorphous alloy ribbon) with a thickness of about 28 μm.

[0049] The entire process of the technical solution of this invention is as follows: calculation - determining the temperature at which the number of high symmetry atomic clusters in the iron-based alloy melt is the highest as the overheating temperature - heating to the set temperature - holding - cooling to the overheating temperature - holding - heating to the casting temperature (increasing the temperature compensation value) - casting - supercooling and solidification (solidifying at the temperature at which the number of high symmetry atomic clusters is the highest).

[0050] To further illustrate the technical solution of the present invention, the following embodiments and comparative examples are provided. Unless otherwise specified, all raw materials used in the present invention are commercially available products.

[0051] Example 1 This embodiment provides a method for preparing iron-based amorphous alloys based on the synergistic effect of highly symmetric atomic clusters, for use in the preparation of amorphous solid alloy Fe82Si8B8C1Cr1 thin strips (the subscript numbers in the chemical formula are at%), wherein the amorphous solid alloy Fe82Si8B8C1Cr1 thin strips are prepared by the high-speed planar continuous casting method commonly used in the art.

[0052] The specific operating steps are as follows: Step 1: Calculate the changes in the types and numbers of atomic clusters in the Fe82Si8B8C1Cr1 iron-based alloy melt with temperature: First, according to the alloy composition, select a structural model containing 10,000 atoms, where the number of Fe, Si, B, C and Cr atoms are 8,200, 800, 800, 100 and 100 atoms respectively. Then, randomly distribute the atomic positions to form the initial melt structure configuration. Then, molecular dynamics was used to calculate the two-body function to simulate the types and quantities of atomic clusters in Fe82Si8B8C1Cr1 iron-based alloy melts at different temperatures (1200-1500℃). The atomic cluster structure was described by Voronoi polyhedra with rotational configurations, revealing the presence of <4,0,0,0>, <4,1,0,0>, <4,2,0,0>, <0,8,0,0>, <8,6,0,0>, <1,2,5,2>, <1,3,3,2>, <0,6,2,2>, <0,4,4,1>, <0,4,4,5>, <0,4,4,2>, <0,4,4,3>, <1,2,5,3>, and <1,3,3,1>. Dozens of atomic clusters with different configurations, such as <0,3,6,0>, <0,4,4,0>, <0,4,5,0>, <0,0,12,0>, <0,0,12,2>, <0,0,12,3>, <0,2,6,0>, <0,0,12,4>, <1,1,12,6>, <0,2,8,0>, <0,2,8,2>, <0,2,8,4>, <0,1,10,3>, <0,1,10,2>, <0,2,8,3>, <0,2,8,1>, <0,3,6,0>, <0,3,6,1>, <0,3,6,4>, <0,3,6,5>, <0,3,6,3>, and <0,4,4,6>. The criteria for selecting high-symmetry atomic clusters were: the sum of the numbers of clusters N5 and N6 in the iron-based alloy melt exceeding 60% of the total number of vertices of the Voronoi polyhedron; and the number of such clusters exceeding 50% of the total number of clusters. The following clusters were identified: <0,0,12,0>, <0,0,12,2>, <0,2,6,0>, <0,0,12,3>, <0,0,12,4>, <1,1,12,6>, <0,2,8,0>, <0,2,8,2>, <0,2,8,4>, and <0,1,10>. Atomic clusters with configurations such as <3>, <0,1,10,2>, <0,2,8,3>, <0,2,8,1>, <1,2,5,3>, <0,3,6,0>, <0,3,6,1>, <0,3,6,4>, <0,3,6,5>, <0,3,6,3>, and <0,4,4,6> are considered high-symmetry atomic clusters. They account for approximately 58% of all atomic clusters. The melting temperature of the iron-based alloy with the highest number of high-symmetry atomic clusters is 1395℃. Step 2, determine the overheating temperature at which the Fe82Si8B8C1Cr1 alloy melt contains the most high-symmetry atomic clusters: (1) Based on the calculation results of Step 1 (e.g. Figure 2 As shown), it was found that the melt temperature of the iron-based alloy with the most high symmetry atomic clusters was 1395℃; (2) The calculated melt temperature of the iron-based alloy with the most high symmetry atomic clusters, 1395℃, was set as the overheating temperature of the iron-based alloy melt. Step 3, determine the overheating temperature and casting temperature of the amorphous alloy melt: (1) Based on the calculation results, set the overheating temperature of the melt to 1395℃. After melting the Fe82Si8B8C1Cr1 alloy melt, heat it to the preset temperature of 1550℃ at a rate of 25℃ / min and hold it for 0.5 hours to ensure that the alloy melt is fully alloyed. Then, cool it down to the set overheating temperature of 1395℃ at a rate of 15℃ / min and hold it for 6 hours so that the atomic clusters in the iron-based alloy melt can reach the same stable state as the calculation results as much as possible; (2) In order to keep the number of highly symmetric atomic clusters in the iron-based alloy melt at the highest level when it solidifies rapidly, temperature compensation needs to be considered when determining the casting temperature. Add 10℃ to the overheating temperature as the casting temperature, that is, set the casting temperature of the alloy melt to 1405℃; Step 4: To ensure the iron-based alloy melt maintains the highest number of highly symmetric atomic clusters during solidification: Under the set cooling water temperature (35℃) and cooling copper sleeve thickness (18mm), the Fe82Si8B8C1Cr1 alloy melt, after being heated at 1395℃ for 6 hours, is heated to 1405℃ at a rate of 10℃ / min. Then, it is continuously poured through a nozzle onto a high-speed rotating rapid cooling copper roller (the linear velocity of the copper sleeve surface is 20 m / s), and is rapidly solidified into an amorphous solid Fe82Si8B8C1Cr1 alloy strip with a thickness of approximately 28μm and a width of 144mm, thereby controlling the number of cluster structures in the amorphous alloy strip.

[0053] High-resolution images of the amorphous solid Fe82Si8B8C1Cr1 alloy thin strip obtained through the above steps are shown below. Figure 3 The amorphous structural features shown are very obvious.

[0054] Example 2 This embodiment provides a method for preparing iron-based amorphous alloys based on the synergistic effect of highly symmetric atomic clusters, for use in the preparation of amorphous solid alloy Fe79Si10B11 thin strips (the subscript numbers in the chemical formula are at%), wherein the amorphous solid alloy Fe79Si10B11 thin strips are prepared by the high-speed planar continuous casting method commonly used in the art.

[0055] The specific steps are as follows: Step 1: Calculate the changes in the types and numbers of atomic clusters in the Fe79Si10B11 iron-based alloy melt with temperature: First, according to the alloy composition, select a structural model containing 10,000 atoms, in which the number of Fe, Si and B atoms are 7,900, 1,000 and 1,100 respectively. Then, randomly distribute the atomic positions to form the initial melt structure configuration. Then, molecular dynamics was used to calculate the two-body function to simulate the types and quantities of atomic clusters in Fe79Si10B11 iron-based alloy melts at different temperatures (1200-1600℃). The atomic cluster structure was described by Voronoi polyhedra with rotational configurations, revealing the existence of <4,0,0,0>, <4,1,0,0>, <0,8,0,0>, <8,6,0,0>, <1,2,5,2>, <1,3,3,3>, <0,4,4,5>, <0,4,4,2>, <0,4,4,3>, <1,2,5,3>, <0,4,4,1>, <0,3,6,0>, <0,4,4,0>, <0,0,12,0>, and <0,0,12,2>. Dozens of atomic clusters with different configurations, such as <0,2,6,0>, <0,0,12,3>, <0,0,12,4>, <1,1,12,6>, <0,2,8,0>, <0,2,8,2>, <0,2,8,4>, <0,1,10,3>, <0,1,10,2>, <0,2,8,3>, <0,2,8,1>, <0,3,6,5>, and <0,3,6,3>, were selected. The criteria for selecting high-symmetry atomic clusters were that the sum of the numbers of clusters N5 and N6 in the iron-based alloy melt exceeded 60% of the total number of vertices of the Voronoi polyhedron, and the number of such clusters exceeded 50% of the total number of clusters. This led to the identification of <0,0,12,0>, <0,0,12,2>, and <0,0,12,2>. Atomic clusters with configurations such as <0,2,6,0>, <0,0,12,3>, <0,0,12,4>, <1,1,12,6>, <0,2,8,0>, <0,2,8,2>, <0,2,8,4>, <0,1,10,3>, <0,1,10,2>, <0,2,8,3>, <0,2,8,1>, <1,2,5,3>, <0,3,6,5>, and <0,3,6,3> are considered as high-symmetry atomic clusters. The total number of high-symmetry atomic clusters accounts for approximately 54% of the total number of atomic clusters. The melting temperature of the iron-based alloy with the highest number of high-symmetry atomic clusters is 1380℃. Step 2, determine the overheating temperature at which the Fe79Si10B11 alloy melt contains the most high-symmetry atomic clusters: (1) Based on the calculation results in Step 1 (e.g. Figure 4As shown), it was found that the melt temperature of the iron-based alloy with the most high symmetry atomic clusters was 1380℃; (2) The calculated melt temperature of the iron-based alloy with the most high symmetry atomic clusters, 1380℃, was set as the overheating temperature of the iron-based alloy melt. Step 3, determine the overheating temperature and casting temperature of the amorphous alloy melt: (1) Based on the calculation results, set the overheating temperature of the melt to 1380℃. After melting the Fe79Si10B11 alloy melt, heat it to the preset temperature of 1500℃ at a rate of 10℃ / min and hold it for 0.5 hours to ensure that the alloy melt is fully alloyed. Then, cool it down to the set overheating temperature of 1380℃ at a rate of 10℃ / min and hold it for 2 hours so that the atomic clusters in the iron-based alloy melt can reach the same stable state as the calculation results as much as possible; (2) In order to keep the number of highly symmetric atomic clusters the most when the iron-based alloy melt solidifies rapidly, temperature compensation needs to be considered when determining the casting temperature. Add 10℃ to the overheating temperature as the casting temperature, that is, set the casting temperature of the alloy melt to 1390℃; Step 4: To ensure the iron-based alloy melt maintains the highest number of highly symmetric atomic clusters during solidification: Under the set cooling water temperature (35℃) and cooling copper sleeve thickness (18mm), the Fe79Si10B11 alloy melt, after being heated at 1380℃ for 2 hours, is heated to 1390℃ at a rate of 10℃ / min. Then, it is continuously poured through a nozzle onto a high-speed rotating rapid cooling copper roller (the linear velocity of the copper sleeve surface is 20 m / s), and is rapidly solidified into an amorphous solid Fe79Si10B11 alloy ribbon with a thickness of approximately 28μm and a width of 144mm, thereby controlling the number of cluster structures in the amorphous alloy ribbon.

[0056] High-resolution images of the amorphous solid Fe79Si10B11 alloy thin strip obtained through the above steps are shown below. Figure 5 The amorphous structural features shown are very obvious.

[0057] Comparative Example 1 This comparative example provides a method for preparing an iron-based amorphous alloy (amorphous Fe82Si8B8C1Cr1 alloy strip). Except for adjusting the overheating temperature in Example 1 from 1395℃ to 1500℃, the other steps are the same as in Example 1.

[0058] Comparative Example 2 This comparative example provides a method for preparing an iron-based amorphous alloy (amorphous Fe79Si10B11 alloy strip). Except that the casting temperature in Example 2 was determined without considering temperature compensation, i.e. the casting temperature and the overheating treatment temperature were kept the same at 1380°C, the other steps were the same as in Example 2.

[0059] Comparative Example 3 This comparative example provides a method for preparing an iron-based amorphous alloy (amorphous Fe79Si10B11 alloy thin strip). Except for steps 3 and 4 of Example 2, which are different from those of Example 2, the other steps are the same as those of Example 2.

[0060] Step 1 is the same as in Example 2; Step 2 is the same as in Example 2; Step 3, determine the overheating temperature and casting temperature of the amorphous alloy melt: (1) Based on the calculation results, the overheating temperature of the melt is set to 1380℃. After the Fe79Si10B11 alloy melt is melted, it is heated to the set overheating temperature of 1380℃ at a rate of 10℃ / min and held for 2 hours; (2) Temperature compensation is not considered when the casting temperature is determined, that is, the casting temperature and the overheating temperature are kept the same at 1380℃. Step 4: Under the set cooling water temperature (35℃) and cooling copper sleeve thickness (18mm), the Fe79Si10B11 alloy melt, which has been heated at 1380℃ for 2 hours (overheat treatment), is then continuously poured through a nozzle onto a high-speed rotating rapid cooling copper roller (the linear velocity of the copper sleeve surface is 20 m / s), and is rapidly solidified into an amorphous solid Fe79Si10B11 alloy strip with a thickness of about 28μm and a width of 144mm.

[0061] To compare the technical effects of the embodiments and comparative examples, the following experimental examples are provided.

[0062] Experimental Example 1 The coercivity, hysteresis loss, and permeability of the iron-based amorphous alloys prepared in each embodiment and the comparative example were tested using a power supply that could convert between DC and AC. The measured voltage was adjustable from 0 to ±50V, and the frequency was adjustable from 1Hz to 10kHz. The specific testing methods are as follows: Coercivity test: Using the MATS series BH hysteresis loop instrument of Hunan Lianzhong Technology Co., Ltd., the saturation hysteresis loop of the toroidal samples made of iron-based amorphous alloy in each embodiment and comparative example was measured in accordance with GB / T13888-2024 "Method for measuring the coercivity of magnetic materials in an open magnetic circuit (up to 160 kA / m)" to obtain the coercivity.

[0063] Hysteresis Loss Detection: Using the MATS magnetic performance measuring instrument from Hunan Lianzhong Technology Co., Ltd., the hysteresis loss of the toroidal samples made of iron-based amorphous alloys in each embodiment and comparative example was measured by the hysteresis loop integration method according to GB / T3655-2022 "Method for Measuring the Magnetic Properties of Electrical Steel Sheets (Strips) Using Epstein Squares". The magnitude of the hysteresis loss is proportional to the area enclosed by the loop. The hysteresis loss was obtained by numerical integration.

[0064] Permeability testing: Using the MATS series BH hysteresis loop tester of Hunan Lianzhong Technology Co., Ltd., the inductance of the winding coil of the toroidal sample made of iron-based amorphous alloy in each embodiment and comparative example was measured in accordance with GB / T13012-2008 "Method for Measurement of DC Magnetic Properties of Soft Magnetic Materials". The permeability was then calculated by substituting the inductance of the coil with the geometric parameters of the sample into the formula.

[0065] The specific test results for coercivity, hysteresis loss and permeability are shown in Table 1.

[0066] Table 1 Figure 2 This is the calculated result of the change in the number of highly symmetric atomic clusters with the temperature of the Fe82Si8B8C1Cr1 alloy melt in Example 1, obtained from simulation calculations. Figure 2 As can be seen, when the melting temperature of the iron-based alloy is 1500℃, the number (percentage) of high-symmetry atomic clusters is approximately 45%, while when the melting temperature is 1395℃, the number (percentage) of high-symmetry atomic clusters approaches 60%, approximately 58%. This indicates that the proportion of high-symmetry atomic clusters is highest at 1395℃. In other words, compared to a melting temperature of 1395℃, the number of high-symmetry atomic clusters decreases significantly at a melting temperature of 1500℃. Combining this with the data in Table 1, it can be seen that as the number of high-symmetry atomic clusters increases, when using the melting temperature of the alloy with the highest number of high-symmetry atomic clusters (1395℃) as the overheating temperature to prepare amorphous Fe82Si8B8C1Cr1 alloy strips (i.e., Example 1), the coercivity and hysteresis loss of the amorphous Fe82Si8B8C1Cr1 alloy strips significantly decrease, while the permeability significantly increases. This further demonstrates that coercivity, hysteresis loss, and permeability can be effectively controlled by adjusting the number of highly symmetric atomic clusters in amorphous alloys.

[0067] Comparative Example 2 is a comparative experiment with Example 2. Compared to Example 2, Comparative Example 2 did not consider temperature compensation when determining the casting temperature; that is, the casting temperature used in Comparative Example 2 was the same as the overheating temperature. As can be seen from the data in Table 1, the coercivity and hysteresis loss of Comparative Example 2 were both higher than those of Example 2, while the permeability was significantly lower. This fully demonstrates that by reasonably compensating for the casting temperature, the iron-based alloy melt can maintain the state with the highest number of highly symmetric atomic clusters during solidification, thereby obtaining an iron-based amorphous alloy with low coercivity, low hysteresis loss, and high permeability.

[0068] Comparative Example 3 is also a comparative experiment with Example 2. Compared with Example 2, Comparative Example 3 mainly differs in that no temperature compensation was performed and no short-term heating treatment at a preset temperature higher than the overheating treatment temperature was conducted before the overheating treatment. As can be seen from the data in Table 1, compared with Example 2, Comparative Example 3 shows a significant increase in coercivity and hysteresis loss, and a substantial decrease in permeability. This also demonstrates that by setting reasonable temperature compensation when determining the casting temperature and conducting a short-term heating treatment at a preset temperature higher than the overheating treatment temperature before the overheating treatment, it is beneficial to obtain lower coercivity and hysteresis loss, and higher permeability in iron-based amorphous alloys.

[0069] The present invention has also verified the above conclusions through multiple experiments. The experimental results were consistent and satisfactory trial results were achieved.

[0070] In summary, the iron-based amorphous alloy preparation method based on the synergistic effect of highly symmetric atomic clusters proposed in this invention can control the magnetic properties of amorphous iron-based alloys, obtaining amorphous solid iron-based alloy ribbons with low coercivity, low hysteresis loss, and high permeability. This method is applicable to various amorphous solid alloy ribbon systems. Therefore, the process method established in this invention for controlling the number of highly symmetric atomic clusters in amorphous alloys not only meets the key technical requirements for important amorphous alloy ribbon material research and engineering production, but is also an urgently needed technology for developing high-performance amorphous solid iron-based alloy ribbon materials.

[0071] The above description is merely a preferred embodiment of the present invention and is not intended to limit the invention. Various modifications and variations can be made to the present invention by those skilled in the art. Any modifications, equivalent substitutions, improvements, etc., made within the spirit and principles of the present invention should be included within the scope of protection of the present invention.

Claims

1. A method for preparing an iron-based amorphous alloy, characterized in that, Includes the following steps: Step 1: Based on the composition of the iron-based amorphous alloy to be prepared, simulate and calculate the relationship between the type and number of atomic clusters in the iron-based alloy melt and the temperature of the iron-based alloy melt, and obtain the calculation results of the change of the number of high symmetry atomic clusters with the temperature of the iron-based alloy melt. Step 2: Based on the calculation results, select the temperature of the iron-based alloy melt corresponding to the highest number of high-symmetry atomic clusters as the overheating treatment temperature of the iron-based alloy melt. Step 3: The iron-based alloy melt is subjected to heat treatment at the overheating temperature to obtain the overheated iron-based alloy melt. A temperature 8-12°C higher than the overheating temperature was selected as the pouring temperature of the iron-based alloy melt after overheating. Step 4: Heat the heat-treated iron-based alloy melt to the casting temperature, and then perform supercooling solidification to obtain an iron-based amorphous alloy with low coercivity, low hysteresis loss and high permeability.

2. The method for preparing the iron-based amorphous alloy according to claim 1, characterized in that, In step 1, the simulation calculation includes: without changing the composition of the iron-based alloy, using the molecular dynamics method to calculate the two-body function to simulate the types and quantities of atomic clusters in the iron-based alloy melt at different temperatures, obtaining the relationship between the types and quantities of atomic clusters in the iron-based alloy melt and the temperature of the iron-based alloy melt, and obtaining the calculation results of the quantity of highly symmetric atomic clusters changing with the temperature of the iron-based alloy melt. And / or, the melt temperature of the iron-based alloy is 1200-1600℃.

3. The method for preparing the iron-based amorphous alloy according to claim 1, characterized in that, In step 1, the structure of the atomic clusters is described by a Voronoi polyhedron with a rotational configuration. The selection of high-symmetry atomic clusters is based on the fact that the sum of the number of clusters N5 and N6 in the iron-based alloy melt exceeds 60% of the total number of vertices of the Voronoi polyhedron, and the number of such atomic clusters with this characteristic exceeds 50% of the total number of all atomic clusters.

4. The method for preparing the iron-based amorphous alloy according to claim 1, characterized in that, In step 2, based on the calculation results, the melt temperature of the iron-based alloy corresponding to the largest number of high-symmetry atomic clusters is determined, and the melt temperature of the iron-based alloy corresponding to the largest number of high-symmetry atomic clusters is selected as the overheating treatment temperature of the iron-based alloy melt.

5. The method for preparing the iron-based amorphous alloy according to claim 1, characterized in that, In step 3, the heat preservation treatment time is 2-7 hours; And / or, the casting temperature of the heat-treated iron-based alloy melt is 10°C higher than the heat treatment temperature. o C.

6. The method for preparing the iron-based amorphous alloy according to claim 1, characterized in that, In step 3, the iron-based alloy melt is first heated to a preset temperature higher than the overheating treatment temperature, held at the preset temperature for a short time, and then cooled to the overheating treatment temperature and held at the overheating treatment temperature to obtain the overheated iron-based alloy melt.

7. The method for preparing the iron-based amorphous alloy according to claim 6, characterized in that, In step 3, the preset temperature is 100-250°C higher than the overheating temperature, and the temperature is held at the preset temperature for 0.3-1 hour. The heating rate to the preset temperature is 10-30°C / min. And / or, the cooling rate from the preset temperature to the overheating treatment temperature is 10-20℃ / min, and the temperature is maintained at the overheating treatment temperature for 2-7 hours.

8. The method for preparing the iron-based amorphous alloy according to claim 1, characterized in that, In step 4, the heat-treated iron-based alloy melt is heated to the pouring temperature, and then the iron-based amorphous alloy is prepared by high-speed planar continuous casting. The specific steps include: under the set cooling water temperature and cooling roller copper sleeve thickness conditions, the heat-treated iron-based alloy melt is heated to the pouring temperature, and then continuously poured through the nozzle onto the surface of the high-speed rotating cooling roller copper sleeve, and rapidly supercooled and solidified to form an iron-based amorphous alloy with low coercivity, low hysteresis loss and high magnetic permeability.

9. The method for preparing the iron-based amorphous alloy according to claim 8, characterized in that, In step 4, the linear velocity of the surface of the copper sleeve of the cooling roller is 20-25 m / s; And / or, the thickness of the copper sleeve of the cooling roller is 10-20 mm; And / or, the cooling water temperature is 20-40°C. o C; And / or, the heating rate for heating the heat-treated iron-based alloy melt to the casting temperature is 8-12°C / min; And / or, the iron-based alloy melt solidifies in a state with the highest number of highly symmetric atomic clusters; And / or, the iron-based amorphous alloy exists in the form of a thin strip, preferably, the thickness of the thin strip is 20-30 μm.

10. An iron-based amorphous alloy, characterized in that, It is prepared by the method for preparing iron-based amorphous alloy according to any one of claims 1-9; Preferably, the iron-based amorphous alloy includes FeCr-based amorphous alloys and / or FeSiB-based amorphous alloys; Preferably, the coercivity of the iron-based amorphous alloy is 0.5-3 A / m; Preferably, the hysteresis loss of the iron-based amorphous alloy is 0.14-0.2 W / kg; Preferably, the magnetic permeability of the iron-based amorphous alloy is 260-600 mH / m.

Images