Fe-BASED AMORPHOUS ALLOY AND THIN Fe-BASED AMORPHOUS ALLOY STRIP

Abstract

This Fe-based amorphous alloy has an amorphous structure and contains, in terms of at%, 8.0-18.0% B, 2.0-9.0% Si, 0.10-5.00% C, 0.05-0.60% Mn, 78.00-86.00% Fe, not less than 0.010 but less than 1.000% P, 0.001-0.020% S, and 0.0010-0.2000% N, with the remainder being impurities.

Description

Fe-based amorphous alloy and Fe-based amorphous alloy ribbon

[0001] The present invention relates to an Fe-based amorphous alloy and an Fe-based amorphous alloy ribbon, and more particularly to an Fe-based amorphous alloy and an Fe-based amorphous alloy ribbon that are excellent in soft magnetic properties and processability.

[0002] Known methods for continuously producing ribbons or wires by rapidly cooling an alloy from a molten state include the centrifugal quenching method, the single-roll method, and the twin-roll method. These methods produce ribbons or wires by ejecting molten metal from an orifice or other opening onto the inner or outer peripheral surface of a metal drum rotating at high speed, causing the molten metal to rapidly solidify. Furthermore, by appropriately selecting the alloy composition, it is possible to obtain amorphous alloys similar to liquid metals, and to produce materials with excellent magnetic or mechanical properties.

[0003] In particular, among amorphous alloys, Fe-based amorphous alloys are considered promising as materials for the iron cores of power transformers and high-frequency transformers. To improve the performance of these materials, there is a strong demand for further reduction in iron loss and further improvement in saturation magnetic flux density of Fe-based amorphous alloys. However, the iron loss W at a magnetic flux density of 1.3 T and a frequency of 50 Hz is １３／５０ It has been extremely difficult to obtain an Fe-based amorphous alloy having a magnetic flux density of 0.100 W / kg or less and a saturation magnetic flux density of 1.60 T or more.

[0004] Furthermore, Fe-based amorphous alloys are sometimes obtained as ribbons having a thickness of 0.1 mm or less. In order to use Fe-based amorphous alloy ribbons for iron cores of power transformers, high-frequency transformers, and the like, the ribbons may be bent. However, when Fe-based amorphous alloy ribbons having poor workability are bent, cracks may occur at the bent portion. Therefore, in order to improve the yield when the ribbons are processed into iron cores, etc., the Fe-based amorphous alloy ribbons are required to have excellent workability.

[0005] In Patent Document 1, the composition of the main elements is Fe ａ M ｂ Si ｃ B ｄ(80<a≦82, 0.05≦b≦1, 2≦c≦7, 12≦d≦16, a+b+c+d=100, M is at least one of Co and Ni) and containing, by mass %, as impurities, P: 0.008 to 0.1%, Mn: 0.15 to 0.5%, and S: 0.004 to 0.05%. The document describes an Fe-based amorphous alloy ribbon that has excellent soft magnetic properties in AC.

[0006] Patent Document 2 describes an Fe-based amorphous alloy ribbon containing, in atomic %, B: 5 to 25%, Si: 1 to 30%, N: 0.001 to 0.2%, with the balance being Fe and unavoidable impurities.

[0007] Patent Document 3 describes an amorphous alloy ribbon containing Fe, Si, B, C, Mn, S, and inevitable impurities, and having a composition in which, when the total amount of Fe, Si, B, and C is taken as 100.0 atomic %, Si is 3.0 atomic % or more and 10.0 atomic % or less, B is 10.0 atomic % or more and 15.0 atomic % or less, and C is 0.2 atomic % or more and 0.4 atomic % or less, the Mn content is more than 0.12 mass % and less than 0.15 mass %, the S content is more than 0.0034 mass % and less than 0.0045 mass %, and the thickness is 10 μm or more and 40 μm or less and the width is 100 mm or more and 300 mm or less.

[0008] Patent Document 4 describes Fe １００－ｘ－ｙ－ｚ Si ｘ B ｙ P ｚ (atomic %) as the main component, where x, y, and z satisfy 0.5≦x≦15, 5≦y≦25, z≦15, and 18≦x+y+z≦30, respectively, and the alloy contains, with respect to the main component, 0.01% by mass to 0.3% by mass of Mn, 0.0001% by mass to 0.01% by mass of Al, 0.001% by mass to 0.03% by mass of Ti, 0.005% by mass to 0.2% by mass of Cu, and 0.001% by mass to 0.05% by mass of S.

[0009] In Patent Document 1, in a component system containing trace amounts of P, Mn, and S, the amounts of Fe, Si, B, and C are limited to a narrow range, thereby improving iron loss and reducing iron loss W １３／５０It is said that the bending strength can be stably reduced to 0.100 W / kg or less, but no consideration is given to improving the workability (bending fracture diameter).

[0010] Patent Document 2 describes that by adding N to Fe-B-Si and Fe-B-Si-C amorphous alloys, impurity elements (such as Al) that are said to promote crystallization are concentrated in the surface oxide layer, thereby preventing crack propagation in the amorphous alloy ribbon and significantly improving workability, and also describes that the effect of adding N reduces the bending fracture diameter by about 40% in both cases, improving brittleness. However, iron loss W １３／５０ There has been no consideration whatsoever about stably reducing the power consumption to 0.100 W / kg or less.

[0011] Patent Document 3 describes that by adjusting the Mn and S contents in an Fe-B-Si-C amorphous alloy ribbon, molten metal can be continuously discharged from a discharge nozzle for a long period of time. However, no consideration is given to improving both the saturation magnetic flux density and iron loss and the workability (bending fracture diameter).

[0012] Patent Document 4 describes that by using Fe-Si-B-P as the main component and specifying the contents of Mn, Al, Ti, Cu, and S, it is difficult for a crystalline phase to form and excellent soft magnetic properties are exhibited, but no consideration is given to improving processability (bending fracture diameter).

[0013] JP 2006-312777 A JP 2006-316348 A WO 2016 / 084741 A JP 2009-174034 A

[0014] The present invention has been made in view of the above circumstances, and an object of the present invention is to provide an Fe-based amorphous alloy and an Fe-based amorphous alloy ribbon that have low iron loss, high magnetic flux density, and excellent processability.

[0015] In order to solve the above problems, the present invention employs the following configuration: [1] An Fe-based amorphous alloy containing, in atomic percent, B: 8.0% to 18.0%, Si: 2.0% to 9.0%, C: 0.10% to 5.00%, Mn: 0.05% to 0.60%, Fe: 78.00% to 86.00%, P: 0.010% to less than 1.000%, S: 0.006% to 0.020%, and N: 0.0010% to 0.2000%, with the balance being impurities, and having an amorphous structure. [2] An Fe-based amorphous alloy containing, in atomic percent, B: 13.0% to 18.0% inclusive, Si: 2.0% to 6.0% inclusive, C: 0.10% to 3.00% inclusive, Mn: 0.05% to 0.60% inclusive, Fe: 78.00% to 86.00% inclusive, P: 0.010% to less than 1.000%, S: 0.006% to 0.020% inclusive, N: 0.0010% to 0.2000% inclusive, the balance consisting of impurities, and having an amorphous structure. [3] The Fe-based amorphous alloy according to [1], containing, in atomic percent, Si: 2.0% to 5.0% inclusive, and N: 0.0030% to 0.2000% inclusive. [4] The Fe-based amorphous alloy according to [2], containing, in atomic percent, Si: 2.0% to 5.0% and N: 0.0030% to 0.2000%. [5] The Fe-based amorphous alloy according to [1], in which Fe is substituted with at least one element selected from Ni, Cr, and Co in a range of 10.0 atomic percent or less. [6] The Fe-based amorphous alloy according to [2], in which Fe is substituted with at least one element selected from Ni, Cr, and Co in a range of 10.0 atomic percent or less. [7] Core loss W when magnetized at a frequency of 50 Hz and a magnetic flux density of 1.3 T. １3／５０ The Fe-based amorphous alloy according to [1], wherein the iron loss W when magnetized at a frequency of 50 Hz and a magnetic flux density of 1.3 T is 0.100 W / kg or less and the saturation magnetic flux density is 1.60 T or more. １3／５０

[10] The Fe-based amorphous alloy ribbon according to

[10] , having a bending fracture diameter of 4 mm or less.

[0016] According to the present invention, it is possible to provide an Fe-based amorphous alloy and an Fe-based amorphous alloy ribbon that have low iron loss, high magnetic flux density, and excellent workability.

[0017] The inventors have found that by controlling the content of S, an element that deteriorates brittleness, and adjusting the contents of amorphous-forming elements such as B, C, Si, P, and N, it is possible to obtain an Fe-based amorphous alloy with excellent workability, such as a bending fracture diameter of 4 mm or less, while improving amorphous-forming ability. It has also been found that optimizing the N content can provide excellent workability, such as a bending fracture diameter of 4 mm or less. Furthermore, by adding Mn in the range of 0.05% to 0.60%, it is possible to achieve both excellent soft magnetic properties and workability, specifically, iron loss W １３／５０ It was found that it was possible to achieve a magnetic flux density of 0.100 W / kg or less, a saturation magnetic flux density of 1.60 T or more, and a bending fracture diameter of 4 mm or less.

[0018] Hereinafter, an Fe-based amorphous alloy and an Fe-based amorphous alloy ribbon according to embodiments of the present invention will be described.

[0019] In this embodiment, "excellent soft magnetic properties" refers to low iron loss and high saturation magnetic flux density, and "excellent processability" refers to a ribbon made of an Fe-based amorphous alloy having a small bending fracture diameter.

[0020] The Fe-based amorphous alloy of this embodiment contains, in atomic %, B: 8.0% to 18.0%, Si: 2.0% to 9.0%, C: 0.10% to 5.00%, Mn: 0.05% to 0.60%, Fe: 78.00% to 86.00%, P: 0.010% to less than 1.000%, S: 0.006% to 0.020%, N: 0.0010% to 0.2000%, with the remainder being impurities, and is an Fe-based amorphous alloy having an amorphous structure.

[0021] Furthermore, the Fe-based amorphous alloy of this embodiment contains, in atomic %, B: 13.0% or more and 18.0% or less, Si: 2.0% or more and 6.0% or less, C: 0.10% or more and 3.00% or less, Mn: 0.05% or more and 0.60% or less, Fe: 78.00% or more and 86.00% or less, P: 0.010% or more and less than 1.000%, S: 0.006% or more and 0.020% or less, N: 0.0010% or more and 0.2000% or less, with the remainder being impurities, and is an Fe-based amorphous alloy having an amorphous structure.

[0022] In the Fe-based amorphous alloy of the present embodiment, Fe may be substituted with at least one element selected from Ni, Cr, and Co in an amount of 10.0 atomic % or less. The Fe-based amorphous alloy ribbon of the present embodiment is made of the above-mentioned Fe-based amorphous alloy.

[0023] First, the reasons for limiting the content of each element in the Fe-based amorphous alloy of this embodiment will be described.

[0024] B is included in the Fe-based amorphous alloy of this embodiment to improve the formation of an amorphous phase and the thermal stability of the amorphous phase. By optimizing the content of this element, the alloy structure can be stably amorphous, further improving soft magnetic properties. For example, the saturation magnetic flux density can be stably 1.60 T or higher. If the B content is less than 8.0 atomic %, the amorphous phase formation ability is not improved, and the amorphous alloy cannot be stably obtained in the Fe-based amorphous alloy. This makes it difficult to stably achieve a saturation magnetic flux density of 1.60 T or higher while maintaining a stable iron loss of 0.100 W / kg or lower. On the other hand, if the B content exceeds 18.0 atomic %, the amorphous phase formation ability is not improved, and it becomes difficult to stably achieve a saturation magnetic flux density of 1.60 T or higher. Therefore, the B content is set to 8.0 atomic % or higher and 18.0 atomic % or lower. The lower limit of B is preferably 10.0 atomic %, more preferably 13.0 atomic %. The upper limit of B is preferably 16.0 atomic %, and more preferably 15.0 atomic %.

[0025] Like B, Si and C are added to the Fe-based amorphous alloy of this embodiment to improve amorphous phase formation and thermal stability of the amorphous phase. By optimizing the Si and C contents, the alloy structure can be stably amorphous, further improving soft magnetic properties. If the Si content is less than 2.0 atomic % and the C content is less than 0.10 atomic %, the amorphous phase formation ability is not improved, and the amorphous alloy cannot be stably obtained in the Fe-based amorphous alloy. It becomes difficult to stably maintain the saturation magnetic flux density at 1.60 T or more while maintaining the iron loss at 0.100 W / kg or less. On the other hand, if the Si content exceeds 9.0 atomic % and the C content exceeds 5.00 atomic %, the amorphous phase formation ability is not improved, and it becomes difficult to stably maintain the iron loss at 0.100 W / kg or less. Therefore, the Si content is set to 2.0 atomic % to 9.0 atomic % and the C content is set to 0.10 atomic % to 5.00 atomic %. The lower limit of Si is preferably 3.0 atomic %, more preferably 4.0 atomic %. The upper limit of Si is preferably 8.0 atomic %, more preferably 7.0 atomic %. The lower limit of C is preferably 0.50 atomic %, more preferably 1.00 atomic %. The upper limit of C is preferably 4.00 atomic %, more preferably 3.00 atomic %.

[0026] Mn is added to the Fe-based amorphous alloy of this embodiment to improve its soft magnetic properties. By optimizing the Mn content, for example, it becomes possible to stably maintain the saturation magnetic flux density at 1.60 T or more while stably maintaining the core loss at 0.100 W / kg or less. If the Mn content is less than 0.05 atomic %, it becomes difficult to stably maintain the saturation magnetic flux density at 1.60 T or more while stably maintaining the core loss at 0.100 W / kg or less. On the other hand, if the Mn content exceeds 0.60 atomic %, it becomes difficult to stably maintain the core loss at 0.100 W / kg or less. Therefore, the Mn content is set to 0.05 atomic % or more and 0.60 atomic % or less. The lower limit of Mn is preferably 0.10 atomic %, more preferably 0.20 atomic %. The upper limit of Mn is preferably 0.50 atomic %, more preferably 0.40 atomic %.

[0027] In Fe-based amorphous alloys, if the Fe content is 70 atomic % or more, a saturation magnetic flux density at a level sufficient for practical use as a general iron core can be obtained. However, in order to obtain a high saturation magnetic flux density of 1.60 T or more, the Fe content must be 78.00 atomic % or more. On the other hand, if the Fe content exceeds 86.00 atomic %, it becomes difficult to form an amorphous phase, and the good soft magnetic properties (iron loss W) specific to amorphous alloys are lost. １３／５０ It becomes difficult to stably obtain a tensile strength (a value of 0.100 W / kg or less). Therefore, in the Fe-based amorphous alloy of this embodiment, the Fe content is set to 78.00 atomic % or more and 86.00 atomic % or less. The lower limit of Fe is preferably 79.00 atomic %, more preferably 80.00 atomic %. The upper limit of Fe is preferably 85.00 atomic %, more preferably 84.00 atomic %.

[0028] In the Fe-based amorphous alloy of this embodiment, by replacing a portion of Fe with at least one of Ni, Cr, and Co in a range of 10.0 atomic % or less, it is possible to improve soft magnetic properties such as iron loss while maintaining a high saturation magnetic flux density. The reason for setting an upper limit on the amount of substitution by these elements is that if the amount exceeds 10.0 atomic %, the saturation magnetic flux density will decrease and the raw material cost will increase. When Fe is replaced by one or more of Ni, Cr, and Co, the total content of Ni, Cr, and Co and the Fe content may be 78.00 atomic % or more and 86.00 atomic % or less, or may be 79.00 atomic % or more and 84.00 atomic % or less.

[0029] Furthermore, the Fe-based amorphous alloy of this embodiment must contain, in atomic percent, P: 0.010% or more and less than 1.000%, S: 0.006% or more and 0.020% or less, and N: 0.0010% or more and 0.2000% or less.

[0030] Like B, Si, and C, P is added to improve the formation of an amorphous phase and the thermal stability of the amorphous phase. By optimizing the P content, the alloy structure can be stably amorphous, further improving soft magnetic properties. If the P content is less than 0.010 atomic %, the amorphous phase formation ability is not improved, and the amorphous alloy cannot be stably obtained in the Fe-based amorphous alloy, making it difficult to stably maintain the iron loss at 0.100 W / kg or less. On the other hand, even if the P content is 1.000 atomic % or more, the amorphous phase formation ability is not improved, making it difficult to stably maintain the iron loss at 0.100 W / kg or less. Therefore, the P content is set to 0.010 atomic % or more and less than 1.000 atomic %. The lower limit of P is preferably 0.050 atomic %, more preferably 0.010 atomic %. The upper limit of P is preferably 0.900 atomic %, more preferably 0.800 atomic %.

[0031] S is an element that deteriorates the brittleness of the Fe-based amorphous alloy of this embodiment. By optimizing the S content, it is possible to make the bending fracture diameter of the Fe-based amorphous alloy ribbon 4 mm or less. Therefore, the S content is set to 0.006 atomic % or more and 0.020 atomic % or less. The upper limit of S is preferably 0.016 atomic %, more preferably 0.014 atomic %, and even more preferably 0.010 atomic %.

[0032] N is contained in the Fe-based amorphous alloy of this embodiment to improve amorphous-forming ability and workability. By optimizing the N content, it is possible to reduce the bending fracture diameter of the Fe-based amorphous alloy ribbon to 4 mm or less. If the N content is less than 0.0010 atomic %, the effect of improving workability cannot be obtained. On the other hand, if the N content exceeds 0.20 atomic %, the effect of amorphous-forming ability saturates, and iron loss may increase. Therefore, the N content is set to 0.0010 atomic % or more and 0.2000 atomic % or less. The lower limit of N is preferably 0.0020 atomic %, more preferably 0.0030 atomic %. The upper limit of N is preferably 0.1500 atomic %, more preferably 0.1000 atomic %.

[0033] The balance in the Fe-based amorphous alloy according to this embodiment is impurities. For example, when a steel material is used as the Fe source, the Fe-based amorphous alloy according to this embodiment may contain impurity elements contained in the steel material as impurities in a total amount of less than 0.100 atomic %. For example, the Fe-based amorphous alloy may contain impurities such as O, Al, Ti, etc. in a total amount of less than 0.100 atomic %.

[0034] The Fe-based amorphous alloy of this embodiment has an amorphous structure. This allows for excellent soft magnetic properties to be obtained. Whether or not the alloy has an amorphous structure can be confirmed, for example, by X-ray diffraction measurement using an X-ray diffractometer with a Co tube. That is, if no clear diffraction peak is obtained in the X-ray diffraction measurement, it can be confirmed that the Fe-based amorphous alloy has an amorphous structure. Here, "no clear diffraction peak is obtained in the X-ray diffraction measurement" means that the α-Fe(110) diffraction peak does not have a half-width of 4° or less.

[0035] When the saturation magnetic flux density and iron loss of the Fe-based amorphous alloy and Fe-based amorphous alloy ribbon of this embodiment are measured by the method described below, the saturation magnetic flux density is 1.60 T or more, the magnetic flux density is 1.3 T, and the iron loss (iron loss W １３／５０ ) becomes 0.100 W / kg or less, and the soft magnetic properties become excellent.

[0036] Iron loss is measured using an SST (Single Strip Tester). The iron loss measurement conditions are set to a magnetic flux density of 1.3 T and a frequency of 50 Hz. Samples for iron loss measurement are collected from six locations along the entire length of one lot of ribbon. Ribbon samples cut to a length of 120 mm are used for the iron loss measurement samples. These ribbon samples for iron loss measurement are annealed at 360°C for one hour in a magnetic field (magnetic field: 800 A / m, magnetic field applied in the casting direction) and then used for measurement. The atmosphere during annealing is a nitrogen atmosphere. Meanwhile, saturation magnetic flux density is measured using a VSM (Vibrating Sample Magnetometer) device. The samples for the VSM device are thin pieces collected from the width center of each of the ribbon samples from the six locations.

[0037] Furthermore, the Fe-based amorphous alloy ribbon of this embodiment can have a bending fracture diameter of 4 mm or less. The bending fracture diameter can be obtained in accordance with the bending test method for metallic materials of JIS Z 2248: 2006, by placing a ribbon made of an Fe-based amorphous alloy in a bending tester, pressing both ends of the test piece together until they come into close contact, and measuring the diameter of the test piece at fracture (bending fracture diameter).

[0038] The Fe-based amorphous alloy and the method for producing the Fe-based amorphous alloy ribbon according to this embodiment will be described below. The Fe-based amorphous alloy according to this embodiment can usually be obtained in the form of a ribbon. This Fe-based amorphous alloy ribbon can be produced by melting an alloy consisting of the components described in the above embodiment, ejecting the molten metal through a slot nozzle or the like onto a cooling plate moving at high speed, and rapidly solidifying the molten metal, for example, by a single-roll method or a twin-roll method. The rolls used in these roll methods are made of metal, and the alloy can be rapidly solidified by rotating the rolls at high speed and causing the molten metal to collide with the surface or inner surface of the roll.

[0039] Single-roll equipment includes centrifugal quenching equipment that uses the inner wall of a drum, equipment that uses an endless belt, and improved versions of these, such as auxiliary rolls and equipment equipped with roll surface temperature control devices, as well as casting equipment that operates under reduced pressure, in a vacuum, or in an inert gas.

[0040] In this embodiment, the dimensions of the ribbon, such as the thickness and width, are not particularly limited, but the ribbon thickness is preferably, for example, 10 μm or more and 100 μm or less. The ribbon width is preferably 10 mm or more. The Fe-based amorphous alloy ribbon obtained as described above can be used as a material for iron cores in power transformers and high-frequency transformers.

[0041] The Fe-based amorphous alloy of this embodiment can also be obtained in the form of a powder, in addition to a ribbon. To obtain a powdered Fe-based amorphous alloy, a method can be employed in which the molten alloy or droplets of the molten alloy are ejected at high speed from the nozzle of a crucible filled with the molten alloy of the above composition into a rotating roll or a liquid such as cooling water, thereby causing rapid solidification.

[0042] By the above-mentioned method, it is possible to obtain an Fe-based amorphous alloy powder having excellent soft magnetic properties.

[0043] The Fe-based soft magnetic alloy powder obtained as described above can be compacted in a mold or the like to form a desired shape, and if necessary, sintered to form an integrated body, and can be used for applications such as power transformers, high-frequency transformers, and coil cores.

[0044] As described above, according to the Fe-based amorphous alloy and Fe-based amorphous alloy ribbon of this embodiment, the contents of B, Si, and C are optimized, P, S, and N are contained, and the Fe content is set to 78.00% or more, whereby the iron loss (iron loss W １３／５０ ) is 0.100 W / kg or less, the saturation magnetic flux density is 1.60 T or more, and excellent soft magnetic properties can be exhibited, making it suitable for use in the iron cores of power transformers and high-frequency transformers.

[0045] Furthermore, the Fe-based amorphous alloy ribbon of the present embodiment can have a bending fracture diameter of 4 mm or less. As a result, when the Fe-based amorphous alloy ribbon is processed into iron cores of power transformers, high-frequency transformers, or the like, there is no risk of the alloy ribbon being broken, and the productivity of iron cores of power transformers and high-frequency transformers can be improved.

[0046] Examples of the present invention will be described below.

[0047] Example 1: An Fe-based amorphous alloy ribbon was produced by melting alloys of the various compositions shown in Tables 1A and 1B in an argon atmosphere, quenching them in a single-roll apparatus, and casting them. The casting atmosphere was air. The single-roll apparatus used consisted of a copper alloy cooling roll with a diameter of 300 mm, a high-frequency power source for melting the sample, and a quartz crucible with a slot nozzle attached to its tip. In this experiment, a slot nozzle with a length of 10 mm and a width of 0.6 mm was used. The peripheral speed of the cooling roll was 24 m / s. As a result, the thickness of the obtained ribbon was approximately 20 μm, the width was 10 mm (depending on the length of the slot nozzle), and the length was approximately 100 m.

[0048] The obtained Fe-based amorphous alloy ribbon was subjected to X-ray diffraction measurement to obtain an X-ray diffraction pattern. The X-ray source for the X-ray diffraction measurement was set to Co-Kα (wavelength λ=0.17902 nm), and the scan range was set to 2θ=10° or more and 120° or less. Whether a crystalline phase was formed in the metal structure was determined from the shape of the X-ray diffraction pattern.

[0049] The saturation magnetic flux density and iron loss of the Fe-based amorphous alloy ribbon were measured using an SST (Single Strip Tester). The iron loss measurement conditions were a magnetic flux density of 1.3 T and a frequency of 50 Hz. The samples for iron loss measurement were collected from six locations along the entire length of one lot of ribbon. The samples for iron loss measurement were ribbon samples cut to a length of 120 mm. These ribbon samples for iron loss measurement were annealed at 360°C for one hour in a magnetic field (magnetic field: 800 A / m, applied in the casting direction) and then used for measurement. The atmosphere during annealing was a nitrogen atmosphere. Meanwhile, the samples for the VSM device were thin pieces collected from the width center of the ribbon samples from the six locations.

[0050] The results of the measurements of saturation magnetic flux density and iron loss are shown in Table 1 as the average values ​​of data at six points.

[0051] Furthermore, the bending fracture diameter of the Fe-based amorphous alloy ribbon was measured. The bending fracture diameter was measured in accordance with JIS Z 2248:2006, a bending test method for metal materials, in which the Fe-based amorphous alloy ribbon was placed in a bending tester, and the bending fracture diameter at break was measured. The results are shown in Table 1.

[0052]

[0053] As shown in Table 1, in all of Inventive Examples 1 to 26, the alloy composition satisfied the range of the present invention, and therefore the saturation magnetic flux density was 1.60 T or more, and the iron loss (iron loss W １３／５０ ) was 0.100 W / kg or less, and it was possible to simultaneously exhibit high saturation magnetic flux density and low iron loss. In addition, the bending fracture diameter was 4 mm or less, and workability was also good.

[0054] On the other hand, in Comparative Examples 1 to 15, the alloy composition did not satisfy the range of the present invention, and therefore the iron loss (iron loss W１３／５０ ) exceeded 0.100 W / kg, the saturation magnetic flux density was less than 1.60 T, or the bending fracture diameter exceeded 4 mm.

[0055] That is, in Comparative Example 1, the Fe content was low, and the saturation magnetic flux density was less than 1.60 T. In Comparative Example 2, the Fe content was excessive, and the iron loss (iron loss W １３／５０ ) exceeded 0.100 W / kg.

[0056] In Comparative Example 3, the B content was low, and the iron loss (iron loss W １３／５０ ) exceeded 0.100 W / kg. In Comparative Example 4, the B content was excessive, and the saturation magnetic flux density was less than 1.60 T.

[0057] In Comparative Example 5, the Si content was low and the iron loss (iron loss W １３／５０ In Comparative Example 6, the Si content was excessive, and the iron loss (iron loss W １３／５０ ) exceeded 0.100 W / kg.

[0058] In Comparative Example 7, the C content was low, and the iron loss (iron loss W １３／５０ In Comparative Example 8, the C content was excessive, and the iron loss (iron loss W １３／５０ ) exceeded 0.100 W / kg.

[0059] In Comparative Example 9, the Mn content was low, and the iron loss (iron loss W １３／５０ ) exceeded 0.100 W / kg. In Comparative Example 10, the Mn content was excessive, and the iron loss (iron loss W １３／５０ ) exceeded 0.100 W / kg.

[0060] In Comparative Example 11, the P content was low, and the iron loss (iron loss W １３／５０ In Comparative Example 12, the P content was excessive, and the iron loss (iron loss W １３／５０ ) exceeded 0.100 W / kg.

[0061] In Comparative Example 13, the S content was excessive, and the bending fracture diameter exceeded 4 mm.

[0062] In Comparative Example 14, the N content was low and the bending fracture diameter exceeded 4 mm. In Comparative Example 15, the N content was excessive and the iron loss (iron loss W １３／５０) exceeded 0.100 W / kg.

[0063] In addition, when X-ray diffraction measurement was performed on the Fe-based amorphous alloy ribbon, no clear diffraction peak was observed in any of Inventive Examples 1 to 26 and Comparative Examples 1 to 15, so it cannot be said that a crystalline phase was generated in the metal structure, and the entire structure was an amorphous phase.

[0064] Example 2 For the alloy No. 1 in Table 1, alloys of various compositions in which part of the Fe was replaced with at least one of Ni, Cr, and Co were used to cast ribbons using the same equipment and conditions as in Example 1. The specific compositions of the alloys used are shown in Table 2. As a result, the thickness, width, and length of the obtained ribbons were approximately 20 μm, 10 mm, and approximately 100 m, respectively. The saturation magnetic flux density, core loss, and bending fracture diameter of the obtained ribbons were evaluated. The sample collection method and measurement conditions used for evaluating these properties were the same as in Example 1. The measurement results are shown in Table 2. The notation in Table 2 is the same as in Table 1.

[0065]

[0066] As is clear from the results of Samples No. 27 to 33 in Table 2, even if a part of Fe is replaced with at least one of Ni, Cr, and Co in the range of 10.0 atomic % or less, the saturation magnetic flux density is 1.60 T or more, and the iron loss is W. １３／５０ It was found that the bending fracture diameter was 4 mm or less, and the workability was also good. Furthermore, no clear diffraction peaks were observed in X-ray diffraction measurements of any of the samples, confirming that they were amorphous.

[0067] As is clear from the above examples, according to the Fe-based amorphous alloy of the present invention, by optimizing the contents of B, Si, and C, adding P, S, and N, and further increasing the Fe content to 78.00% or more, the iron loss (iron loss W １３／５０) was 0.100 W / kg or less, and the saturation magnetic flux density was 1.60 T or more, demonstrating excellent soft magnetic properties, making it suitable for use in the iron cores of power transformers and high-frequency transformers. Furthermore, workability was also improved.

[0068] Furthermore, according to the Fe-based amorphous alloy ribbon of the present invention, the iron loss (iron loss W １３／５０ It was found that the magnetic flux density was 0.100 W / kg or less, the saturation magnetic flux density was 1.60 T or more, and the bending fracture diameter was 4 mm or less. This means that when the Fe-based amorphous alloy ribbon is processed into iron cores of power transformers, high-frequency transformers, etc., there is no risk of the alloy ribbon being damaged, and it was found that the productivity of iron cores of power transformers and high-frequency transformers can be improved.

[0069] The Fe-based amorphous alloy ribbon of the present disclosure has low core loss, high magnetic flux density, and excellent processability, and therefore has high industrial applicability.

Claims

1. An Fe-based amorphous alloy containing, in atomic percent, B: 8.0% or more and 18.0% or less, Si: 2.0% or more and 9.0% or less, C: 0.10% or more and 5.00% or less, Mn: 0.05% or more and 0.60% or less, Fe: 78.00% or more and less than 86.00%, P: 0.010% or more and less than 1.000%, S: 0.006% or more and 0.020% or less, N: 0.0010% or more and 0.2000% or less, the remainder being impurities, and having an amorphous structure.

2. An Fe-based amorphous alloy containing, in atomic percent, B: 13.0% or more and 18.0% or less, Si: 2.0% or more and 6.0% or less, C: 0.10% or more and 3.00% or less, Mn: 0.05% or more and 0.60% or less, Fe: 78.00% or more and less than 86.00%, P: 0.010% or more and less than 1.000%, S: 0.006% or more and 0.020% or less, N: 0.0010% or more and 0.2000% or less, the remainder being impurities, and having an amorphous structure.

3. An Fe-based amorphous alloy according to claim 1, containing, in atomic percent, Si: 2.0% or more and 5.0% or less, and N: 0.0030% or more and 0.2000% or less.

4. An Fe-based amorphous alloy according to claim 2, containing, in atomic percent, Si: 2.0% or more and 5.0% or less, and N: 0.0030% or more and 0.2000% or less.

5. An Fe-based amorphous alloy according to claim 1, wherein Fe is substituted with at least one element selected from the group consisting of Ni, Cr and Co in an amount of 10.0 atomic % or less.

6. An Fe-based amorphous alloy according to claim 2, wherein Fe is substituted with at least one element selected from the group consisting of Ni, Cr and Co in an amount of 10.0 atomic % or less.

7. Iron loss W when magnetized at a frequency of 50 Hz and a magnetic flux density of 1.3 T １3／５０ 2. The Fe-based amorphous alloy according to claim 1, wherein the magnetic flux density is 0.100 W / kg or less and the saturation magnetic flux density is 1.60 T or more.

8. Iron loss W when magnetized at a frequency of 50 Hz and a magnetic flux density of 1.3 T １3／５０ 3. The Fe-based amorphous alloy according to claim 2, wherein the magnetic flux density is 0.100 W / kg or less and the saturation magnetic flux density is 1.60 T or more.

9. An Fe-based amorphous alloy ribbon comprising the Fe-based amorphous alloy according to any one of claims 1 to 8.

10. The Fe-based amorphous alloy ribbon according to claim 9, having a bending fracture diameter of 4 mm or less.

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