Fe-based amorphous alloys and Fe-based amorphous alloy thin tapes

Abstract

The Fe-based amorphous alloy contains, by atomic percent: B: 8.0% or more and 18.0% or less, Si: 2.0% or more and 9.0% or less, Mn: 0.05% or more and 0.60% or less, Fe: 78.00% or more and 86.00% or less, S: 0.006% or more and 0.020% or less, and N: 0.0010% or more and 0.2000% or less, with the remainder consisting of impurities. Furthermore, the microstructure of the Fe-based amorphous alloy is amorphous.

Description

[Technical Field]

[0001] Field of the Invention This invention relates to an Fe-based amorphous alloy and a Fe-based amorphous alloy strip, and more particularly to an Fe-based amorphous alloy and a Fe-based amorphous alloy strip with excellent processability. [Previous Technology]

[0002] Background of the Invention Methods for continuously manufacturing thin strips or wires by rapidly cooling an alloy from its molten state include centrifugal quenching, single-roller methods, and double-roller methods. These methods manufacture thin strips or wires by rapidly solidifying the molten metal by spraying it from an orifice onto the inner or outer circumferential surface of a high-speed rotating metal cylinder. Furthermore, by rationally selecting the alloy composition, it is possible to obtain amorphous alloys similar to liquid metals, enabling the manufacture of materials with excellent magnetic or mechanical properties.

[0003] In particular, compared with non-Fe amorphous alloys, Fe-based amorphous alloys have relatively low iron loss and relatively high saturation magnetic flux density, and therefore are expected to be used as cores of power transformers or high-frequency transformers.

[0004] Furthermore, Fe-based amorphous alloys are sometimes obtained in the form of thin strips with a thickness of 0.1 mm or less. To use these Fe-based amorphous alloy strips in the cores of power transformers or high-frequency transformers, bending is sometimes performed on the strips. However, if Fe-based amorphous alloy strips with poor machinability are bent, cracks may occur at the bend. Therefore, to improve the yield when processing the strips into cores, excellent machinability is required for the Fe-based amorphous alloy strips.

[0005] Patent document 1 describes an Fe-B-Si-C amorphous alloy thin strip, the basic element of which is Fe, and B, Si and C are used as alloy constituent elements. Furthermore, the contents of impurities P, Mn and S elements are respectively P: 0.008% or more and 0.1% or less, Mn: 0.15% or more and 0.5% or less, and S: 0.004% or more and 0.05% or less, by weight%.

[0006] Patent document 2 describes an Fe-based amorphous alloy thin strip, which contains, in atomic percent: B: 5-25%, Si: 1-30%, and N: 0.001-0.2%, and the remainder is composed of Fe and unavoidable impurities.

[0007] Patent Document 3 discloses an amorphous alloy strip containing Fe, Si, B, C, Mn, S and unavoidable impurities, and having the following composition: when the total mass of Fe, Si, B, and C is 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; and the content of Mn is greater than 0.12 mass% and less than 0.15 mass%, and the content of S is greater than 0.0034 mass% and less than 0.0045 mass; the thickness of the amorphous alloy strip is 10 μm or more and 40 μm or less, and the width is 100 mm or more and 300 mm or less.

[0008] In Patent Document 1, by using B, Si, and C as alloying elements and specifying the content of P, Mn, and S elements, it is possible to use low-grade materials, thereby reducing the alloy cost when manufacturing the thin strip. However, no research has been conducted on the improvement of processability (bending failure diameter).

[0009] Patent Document 2 describes how, by including nitrogen (N) in Fe-B-Si and Fe-B-Si-C amorphous alloys, impurity elements (such as Al), known as crystallization-promoting elements, are concentrated in the surface oxide layer, thereby preventing the propagation of cracks in the amorphous alloy strips and significantly improving processability. Furthermore, it describes how, based on the effect of containing N, the bending failure diameter is reduced by approximately 40%, thus improving brittleness. However, it does not describe the inclusion of sulfur (S) in the amorphous alloy.

[0010] Although Patent Document 3 describes a method for continuously ejecting molten metal from a nozzle for an extended period by adjusting the Mn and S content in an Fe-B-Si-C amorphous alloy strip, no research has been conducted on improving workability (bending failure diameter). [Prior Art Documents] [Patent Documents]

[0011] [Patent Document 1] Japanese Patent Application Publication No. Hei 9-95760 [Patent Document 2] Japanese Patent Application Publication No. 2006-316348 [Patent Document 3] International Publication No. 2016 / 084741 [Summary of the Invention]

[0012] Summary of the Invention [Problem to be Solved by the Invention] The present invention was made in view of the above circumstances, and its object is to provide an Fe-based amorphous alloy and a Fe-based amorphous alloy strip with excellent processability.

[0013] [Means for Solving the Problem] In order to solve the above-mentioned problem, the present invention adopts the following structure. [1] An Fe-based amorphous alloy, comprising, in atomic percent: B: 8.0% or more and 18.0% or less, Si: 2.0% or more and 9.0% or less, Mn: 0.05% or more and 0.60% or less, Fe: 78.00% or more and 86.00% or less, S: 0.006% or more and 0.020% or less, and N: 0.0010% or more and 0.2000% or less, the remainder being composed of impurities, and the microstructure of the Fe-based amorphous alloy is amorphous. [2] The Fe-based amorphous alloy as described in [1], wherein B: 13.0 atomic percent or more and 18.0 atomic percent or less. [3] The Fe-based amorphous alloy as described in [1], wherein Si: 2.0 atomic percent or more and 6.0 atomic percent or less. [4] The Fe-based amorphous alloy described in [2], wherein Si is 2.0 atomic% or more and 6.0 atomic% or less. [5] The Fe-based amorphous alloy described in [1], wherein N is 0.0030 atomic% or more and 0.2000 atomic% or less. [6] The Fe-based amorphous alloy described in [2], wherein N is 0.0030 atomic% or more and 0.2000 atomic% or less. [7] The Fe-based amorphous alloy described in [3], wherein N is 0.0030 atomic% or more and 0.2000 atomic% or less. [8] The Fe-based amorphous alloy described in [4], wherein N is 0.0030 atomic% or more and 0.2000 atomic% or less. [9] The Fe-based amorphous alloy described in [1], wherein the ratio of N to S (N / S) is 0.20 or more and 15 or less.

[10] The Fe-based amorphous alloy described in [2], wherein the ratio of N to S (N / S) is 0.20 or more and 15 or less.

[11] The Fe-based amorphous alloy described in [3], wherein the ratio of N to S (N / S) is 0.20 or more and 15 or less.

[12] The Fe-based amorphous alloy described in [4], wherein the ratio of N to S (N / S) is 0.20 or more and 15 or less.

[13] The Fe-based amorphous alloy described in any one of [1] to

[12] , wherein at least one element selected from Ni, Cr, and Co is used to replace Fe in the range of 10.0 atomic percent or less.

[14] The Fe-based amorphous alloy described in any of [1] to

[12] has an iron loss W 13 / 50 of less than 0.100 W / kg and a saturation magnetic flux density of more than 1.60 T when magnetized at a frequency of 50 Hz and a magnetic flux density of 1.3 T.

[15] The Fe-based amorphous alloy described in

[13] has an iron loss W 13 / 50 of less than 0.100 W / kg and a saturation magnetic flux density of more than 1.60 T when magnetized at a frequency of 50 Hz and a magnetic flux density of 1.3 T.

[16] An Fe-based amorphous alloy thin strip is composed of an Fe-based amorphous alloy as described in any one of [1] to

[12] .

[17] The Fe-based amorphous alloy thin strip as described in

[16] is wherein at least one element selected from Ni, Cr, and Co is used to replace Fe in the range of 10.0 atomic% or less.

[18] The Fe-based amorphous alloy thin strip as described in

[16] has an iron loss W13 / 50 of 0.100 W / kg or less when magnetized at a frequency of 50 Hz and a magnetic flux density of 1.3 T, and a saturation magnetic flux density of 1.60 T or more.

[19] The Fe-based amorphous alloy thin strip as described in

[16] has a bending failure diameter of 4 mm or less.

[0014] [Effects of the Invention] According to the present invention, an Fe-based amorphous alloy and a Fe-based amorphous alloy strip with excellent processability can be provided.

Implementation Method

[0015] In order to implement the invention, the inventors discovered that by limiting the content of S, an element that worsens brittleness, and by adjusting the content of amorphous forming elements such as B, Si, and N, not only can the amorphous forming ability be improved, but also an Fe-based amorphous alloy with excellent workability and a bending fracture diameter of less than 4 mm can be obtained. Furthermore, it was discovered that by containing Mn in the range of 0.05 atomic% to 0.60 atomic%, excellent soft magnetic properties and workability can be simultaneously achieved.

[0016] Hereinafter, Fe-based amorphous alloys and Fe-based amorphous alloy strips, which are embodiments of the present invention, will be described.

[0017] In this embodiment, excellent processability means that when the Fe-based amorphous alloy is made into a thin strip, its bending failure diameter is small. Furthermore, excellent soft magnetic properties mean that it has low iron loss and high saturation magnetic flux density.

[0018] The Fe-based amorphous alloy of this embodiment contains, in atomic percent: B: 8.0% or more and 18.0% or less, Si: 2.0% or more and 9.0% or less, Mn: 0.05% or more and 0.60% or less, Fe: 78.00% or more and 86.00% or less, S: 0.006% or more and 0.020% or less, and N: 0.0010% or more and 0.2000% or less, with the remainder consisting of impurities, and the microstructure of the Fe-based amorphous alloy is amorphous.

[0019] Furthermore, the B content of the Fe-based amorphous alloy in this embodiment may be 13.0 atomic% or more and 18.0 atomic% or less. Furthermore, the Si content of the Fe-based amorphous alloy in this embodiment may be 2.0 atomic% or more and 6.0 atomic% or less.

[0020] Furthermore, when the Fe-based amorphous alloy of this embodiment contains S and N, the ratio of N to S (N / S) can be 0.20 or more and 15 or less. Furthermore, the Fe-based amorphous alloy of this embodiment can replace Fe with at least one element selected from Ni, Cr, and Co within a range of 10.0 atomic percent or less. Furthermore, the Fe-based amorphous alloy strip of this embodiment is composed of the aforementioned Fe-based amorphous alloy.

[0021] First, the reasons for limiting the content of each element in the Fe-based amorphous alloy of this embodiment will be explained.

[0022] In the Fe-based amorphous alloy of this embodiment, B is included to form an amorphous phase and improve the thermal stability of the amorphous phase. By optimizing the content of this element, the alloy structure can be stably made into an amorphous phase, and the soft magnetic properties can be further improved. For example, the saturation magnetic flux density can be stably made to be 1.60 T or more. When B is less than 8.0 atomic%, the improvement in the ability to form an amorphous phase cannot be obtained, and an amorphous alloy cannot be stably obtained in the Fe-based amorphous alloy. It is difficult to stably maintain the iron loss at 0.100 W / kg or less while maintaining the saturation magnetic flux density at 1.60 T or more. On the other hand, even if B is greater than 18.0 atomic%, the improvement in the ability to form an amorphous phase cannot be obtained, and it is difficult to stably maintain the saturation magnetic flux density at 1.60 T or more. Therefore, B is made to be 8.0 atomic% or more and 18.0 atomic% or less. The lower limit of B is preferably 10.0 atomic%, and more preferably 13.0 atomic%. The upper limit of B should be 16.0 atoms, and further preferably 15.0 atoms.

[0023] Similar to B, in the Fe-based amorphous alloy of this embodiment, Si is included to form an amorphous phase and improve the thermal stability of the amorphous phase. By optimizing the Si content, the alloy structure can be stably made into an amorphous phase, and the soft magnetic properties can be further improved. When Si is less than 2.0 atomic%, the ability to form an amorphous phase cannot be improved, and an amorphous alloy cannot be stably obtained in the Fe-based amorphous alloy. It is difficult to stably maintain the saturation magnetic flux density at 1.60 T or more while keeping the iron loss stably below 0.100 W / kg. On the other hand, even if Si is greater than 9.0 atomic%, the ability to form an amorphous phase cannot be improved, and it is difficult to stably keep the iron loss below 0.100 W / kg. Therefore, Si is 2.0 atomic% or more and 9.0 atomic% or less. The lower limit of Si is preferably 3.0 atomic%, and more preferably 4.0 atomic%. The upper limit of Si should preferably be 6.0 atoms, further preferably 5.0 atoms, and especially preferably less than 5.0 atoms.

[0024] In the Fe-based amorphous alloy of this embodiment, Mn is included to improve soft magnetic properties. By optimizing the Mn content, for example, it is possible to stably maintain the iron loss at 0.100 W / kg or less while maintaining the saturation magnetic flux density at 1.60 T or more. When Mn is less than 0.05 atomic%, it is difficult to stably maintain the iron loss at 0.100 W / kg or less while maintaining the saturation magnetic flux density at 1.60 T or more. On the other hand, if Mn is greater than 0.60 atomic%, it is difficult to stably maintain the iron loss at 0.100 W / kg or less. Therefore, Mn is set at 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%, and the upper limit of Mn is preferably 0.50 atomic%, more preferably 0.40 atomic%.

[0025] In Fe-based amorphous alloys, a Fe content of 70 atomic% or more is generally sufficient to obtain a saturation magnetic flux density that is practical for common iron cores. However, to obtain a high saturation magnetic flux density of 1.60T or more, the Fe content needs to be 78.00 atomic% or more. On the other hand, if the Fe content is greater than 86.00 atomic%, it is difficult to form an amorphous phase and difficult to obtain the good soft magnetic properties characteristic of amorphous alloys (to stably keep the iron loss W13 / 50 below 0.100 W / kg). Therefore, in the Fe-based amorphous alloy of this embodiment, the Fe content is 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%, and the upper limit of Fe is preferably 85.00 atomic%, more preferably 84.00 atomic%.

[0026] In the Fe-based amorphous alloy of this embodiment, by replacing a portion of Fe with at least one of Ni, Cr, and Co within a range of 10.0 atomic% or less, soft magnetic properties such as iron loss can be improved while maintaining a high saturation magnetic flux density. The reason for setting an upper limit on the substitution amount of these elements is that if it exceeds 10.0 atomic%, the saturation magnetic flux density will decrease or the raw material cost will increase. When replacing Fe with one or more of Ni, Cr, and Co, the total content of Ni, Cr, Co and Fe is sufficient to be 78.00 atomic% or more and 86.00 atomic% or less, or it can be 79.00 atomic% or more and 84.00 atomic% or less.

[0027] Further, the Fe-based amorphous alloy of this embodiment needs to contain, in atomic percent: S: more than 0.006% and less than 0.020%, and N: more than 0.0010% and less than 0.2000%.

[0028] In the Fe-based amorphous alloy of this embodiment, sulfur (S) is an element that worsens brittleness. By optimizing the content of S, when producing Fe-based amorphous alloy strips, the bending failure diameter can be 4 mm or less. Therefore, the content of S is 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 more preferably 0.010 atomic% or less.

[0029] In the Fe-based amorphous alloy of this embodiment, N is included to improve amorphous formation capability and workability. By optimizing the N content, when producing Fe-based amorphous alloy strips, the bending failure diameter can be 4 mm or less. When N is less than 0.0010 atomic%, the improvement in workability cannot be obtained. On the other hand, if N is greater than 0.2000 atomic%, the amorphous formation capability becomes saturated, raising concerns about increased iron loss. Therefore, N is 0.0010 atomic% or more and 0.2000 atomic% or less. It is preferable that N is 0.0020 atomic% or more. It is further preferable that N is 0.0030 atomic% or more. It is preferable that N is 0.1500 atomic% or less. It is further preferable that N is 0.1000 atomic% or less.

[0030] When the Fe-based amorphous alloy of this embodiment contains S and N, the ratio (atomic ratio) of N to S (N / S) can be 0.20 or more and 15 or less. By making the ratio of N to S (N / S) 0.20 or more and 15 or less, the processability can be further improved. Furthermore, the soft magnetic properties can also be improved. The lower limit of (N / S) can be 0.40, and further can be 0.60. The upper limit of (N / S) can be 13, and further can be 11.

[0031] The remaining portion in the Fe-based amorphous alloy of this embodiment is an impurity. In the Fe-based amorphous alloy of this embodiment, for example, when steel is used as the Fe source, it may contain impurity elements found in steel as impurities. For example, it may contain C, P, Al, Ti, O, etc., totaling less than 0.10 atomic percent as impurities. The standard for the amount of each element contained as an impurity is: C less than 0.03 atomic percent, P less than 0.01 atomic percent, Al less than 0.01 atomic percent, Ti less than 0.005 atomic percent, and O less than 0.04 atomic percent.

[0032] The Fe-based amorphous alloy of this embodiment has an amorphous structure. This allows for the acquisition of excellent soft magnetic properties. Whether or not it has an amorphous structure can be confirmed, for example, by X-ray diffraction measurement using a Co-tube X-ray diffraction apparatus. That is, if a distinct diffraction peak cannot be obtained in the X-ray diffraction measurement, it can be confirmed that the Fe-based amorphous alloy has an amorphous structure. Here, "no distinct diffraction peak can be obtained in the X-ray diffraction measurement" means that there is no peak with a full width at half maximum (FWHM) of 4° or less for the α-Fe(110) diffraction peak.

[0033] When measuring the saturation magnetic flux density and iron loss of the Fe-based amorphous alloy and Fe-based amorphous alloy thin strip of this embodiment using the method described below, the saturation magnetic flux density should preferably be 1.60 T or higher, and the iron loss (iron loss W 13 / 50) at a magnetic flux density of 1.3 T and a frequency of 50 Hz should preferably be 0.100 W / kg or lower. Therefore, the Fe-based amorphous alloy and Fe-based amorphous alloy thin strip of this embodiment exhibit excellent soft magnetic properties.

[0034] Iron loss was measured using an SST (Single Strip Tester). The iron loss measurement conditions were set to a magnetic flux density of 1.3T and a frequency of 50Hz. The iron loss test samples were collected from six locations along the entire length of a batch of strips. The iron loss test samples were cut into 120mm long strip samples. These iron loss test strip samples were annealed at 360°C in a magnetic field (magnetic field: 800A / m, applied in the casting direction) for 1 hour before measurement. The gas environment during annealing was set to a nitrogen gas environment. On the other hand, saturation magnetic flux density was measured using a VSM (Vibrating Sample Magnetometer). The VSM sample was a thin strip obtained from the central portion of the width of the strip samples collected from the aforementioned six locations.

[0035] Furthermore, the Fe-based amorphous alloy strip of this embodiment can achieve a bending failure diameter of 4 mm or less. The bending failure diameter is obtained by placing the Fe-based amorphous alloy strip in a bending test machine according to the bending test method of JIS Z 2248:2006, pressing the two ends of the specimen together until they are in close contact, and measuring the diameter of the specimen at the time of fracture (bending failure diameter).

[0036] Hereinafter, the manufacturing method of the Fe-based amorphous alloy and the Fe-based amorphous alloy strip of this embodiment will be described. The Fe-based amorphous alloy of this embodiment can generally be obtained in the form of a strip. The Fe-based amorphous alloy strip can be manufactured by, for example, a single-roll method or a double-roll method, in which an alloy composed of the components described in the above embodiment is melted, and the molten liquid is ejected through a slit nozzle or the like onto a high-speed moving cooling plate, thereby rapidly cooling and solidifying the molten liquid. The rollers used in such roller methods are made of metal, and by rotating the rollers at high speed and causing the molten liquid to collide with the surface or inner surface of the rollers, the alloy can be rapidly cooled and solidified.

[0037] The single-roller device also includes a centrifugal quenching device using the inner wall of a cylinder, a device using an annular belt, and a casting device with an auxiliary roller or roller surface temperature control device as an improvement of such devices, in a reduced pressure or vacuum or in an inactive gas.

[0038] In this embodiment, there are no particular limitations on the thickness, width, and other dimensions of the strip. The thickness of the strip is preferably 10 μm or more and 100 μm or less. Furthermore, the width is preferably 10 mm or more. The Fe-based amorphous alloy strip obtained as described above can be used for applications such as the core of power transformers or high-frequency transformers.

[0039] Furthermore, in addition to being made into thin strips, the Fe-based amorphous alloy of this embodiment can also be made into powder. In order to obtain the powdered Fe-based amorphous alloy, the following method can be used: the alloy melt or droplets of the alloy melt are sprayed at high speed from the nozzle of a crucible filled with the alloy melt of the above composition into a rotating roller or a liquid such as cooling water, so as to rapidly cool and solidify it.

[0040] Using the above method, Fe-based amorphous alloy powder with excellent soft magnetic properties can be obtained.

[0041] The Fe-based soft magnetic alloy powder obtained as described above is compacted into the target shape by using a mold or the like, and then sintered as needed to become a whole, so that it can be used for applications such as the core of power transformers or high-frequency transformers and coils.

[0042] As described above, the Fe-based amorphous alloy and Fe-based amorphous alloy strip according to this embodiment can improve processability by optimizing the content of B and Si, containing an appropriate amount of Mn, and further containing S and N, and further making the Fe content 78.00% or more.

[0043] Furthermore, the iron loss (iron loss W 13 / 50) of the Fe-based amorphous alloy and Fe-based amorphous alloy thin strip of this embodiment at a magnetic flux density of 1.3T and a frequency of 50Hz should preferably be 0.100W / kg or less, and the saturation magnetic flux density should preferably be 1.60T or more. Therefore, the Fe-based amorphous alloy and Fe-based amorphous alloy thin strip of this embodiment can exhibit excellent soft magnetic properties. This makes them suitable for use in the cores of power transformers or high-frequency transformers.

[0044] Furthermore, the Fe-based amorphous alloy strip of this embodiment can achieve a bending failure diameter of 4 mm or less. Therefore, when the Fe-based amorphous alloy strip is processed into the core of a power transformer or high-frequency transformer, there is no concern about strip breakage, thus improving the productivity of the core of the power transformer or high-frequency transformer. The bending failure diameter of the Fe-based amorphous alloy strip of this embodiment is preferably 2 mm or less. [Example]

[0045] Hereinafter, embodiments of the present invention will be described.

[0046] (Example 1) Fe-based amorphous alloy strips were obtained by melting alloys of various compositions shown in Tables 1A and 1B in an argon gas environment, rapidly cooling them using a single-roller apparatus, and then casting them. The casting gas environment was atmospheric. Furthermore, the single-roller apparatus used consisted of a 300mm diameter copper alloy cooling roller, a high-frequency power supply for sample melting, and a quartz crucible with a slit nozzle attached to its front end. In this experiment, a slit nozzle with a length of 10mm and a width of 0.6mm was used. The circumferential speed of the cooling roller was set to 24m / s. As a result, the thickness of the obtained strip was approximately 20μm, and since the width depended on the length of the slit nozzle, the width was 10mm, and the length was approximately 100m.

[0047] X-ray diffraction was performed on the obtained Fe-based amorphous alloy thin strip to obtain an X-ray diffraction pattern. The X-ray source for the X-ray diffraction was set to Co-Kα (wavelength λ = 0.17902 nm), and the scanning range was set to 2θ = 10° or higher and 120° or lower. Based on the shape of the X-ray diffraction pattern, it was determined whether a crystalline phase was formed in the metal structure.

[0048] Furthermore, the saturation magnetic flux density and iron loss of Fe-based amorphous alloy strips 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 iron loss test samples were collected from six locations along the entire length of a batch of strips. The iron loss test samples were cut into 120 mm long strip samples. These iron loss test strip samples were annealed at 360°C in a magnetic field (magnetic field: 800 A / m, applied in the casting direction) for 1 hour before measurement. The gas environment during annealing was set to a nitrogen gas environment. On the other hand, the VSM apparatus used strips obtained from the central portion of the width of the strip samples collected from the aforementioned six locations.

[0049] Regarding the measurement results of saturation magnetic flux density and iron loss, the average values ​​of data from 6 locations are shown in Tables 1A and 1B.

[0050] Further, the bending failure diameter of the Fe-based amorphous alloy thin strip was determined. The bending failure diameter was determined according to the bending test method for metallic materials in JIS Z 2248:2006. The Fe-based amorphous alloy thin strip was placed in a bending test machine, and the bending failure diameter at fracture was measured. The results are shown in Tables 1A and 1B.

[0051] [Table 1A] No. Remaining chemical components: impurities Saturation magnetic flux density Bs(T) Iron loss W 13 / 50 (W / kg) Bending failure diameter (mm) Fe (atom%) B (atom%) Si (atom%) Mn (atom%) S (atom%) N (atom%) N / S Example of the present invention 1 79.06 17.8 3.0 0.10 0.006 0.0300 5.00 1.61 0.097 3 Example of the present invention 2 80.21 13.6 5.6 0.57 0.008 0.0100 1.25 1.61 0.097 2 Example of the present invention 3 81.02 14.3 4.6 0.06 0.010 0.0140 1.40 1.62 0.097 2 Example of the present invention 4 81.15 14.2 4.3 0.30 0.020 0.0300 1.50 1.63 0.098 3 Example of the present invention 5 80.26 17.1 2.4 0.21 0.008 0.0190 2.38 1.62 0.096 2 Example of the present invention 6 80.15 14.6 5.1 0.13 0.012 0.0040 0.33 1.62 0.099 3 Example of the present invention 7 85.28 11.6 2.6 0.50 0.010 0.0150 1.50 1.66 0.096 3 Example of the present invention 8 81.20 11.3 7.4 0.07 0.010 0.0200 2.0 1.62 0.098 3 Example of the present invention 9 81.19 9.4 8.8 0.58 0.010 0.0200 2.00 1.62 0.097 3 Example of the present invention 10 81.84 11.4 6.6 0.08 0.018 0.0600 3.33 1.63 0.098 4 Example of the present invention 11 79.13 13.4 7.0 0.45 0.010 0.0060 0.60 1.61 0.098 4 Example of the present invention 12 80.05 11.4 8.3 0.10 0.010 0.1400 14.00 1.62 0.097 2 Example of the present invention 13 80.67 15.4 3.6 0.30 0.008 0.0200 2.50 1.62 0.095 2 Example of the present invention 14 82.05 15.5 2.3 0.14 0.009 0.0040 0.44 1.64 0.097 2 Example of the present invention 15 81.07 13.4 5.4 0.12 0.007 0.0080 1.14 1.62 0.096 2 Example of the present invention 16 83.15 13.6 3.0 0.24 0.007 0.0050 0.71 1.65 0.095 1 Example of the present invention 17 79.21 16.2 4.1 0.48 0.008 0.0020 0.25 1.61 0.098 4 Example of the present invention 18 84.06 13.3 2.5 0.07 0.010 0.0580 5.80 1.66 0.096 1 Example of the present invention 19 83.14 8.5 8.2 0.14 0.012 0.0100 0.83 1.65 0.098 3 Example of the present invention 20 79.21 12.0 8.6 0.16 0.011 0.0200 1.82 1.61 0.097 3 Example of the present invention twenty one 80.26 13.2 6.3 0.23 0.010 0.0020 0.20 1.62 0.098 4 Example of the present invention twenty two 80.10 13.6 6.2 0.07 0.012 0.0180 1.50 1.61 0.097 3

[0052] [Table 1B] No. Remaining chemical components: impurities Saturation magnetic flux density Bs(T) Iron loss W 13 / 50 (W / kg) Bending failure diameter (mm) Fe (atom%) B (atom%) Si (atom%) Mn (atom%) S (atom%) N (atom%) N / S Comparative example 101 77.72 15.8 6.3 0.15 0.010 0.0200 2.00 1.59 0.098 3 Comparative example 102 86.11 9.7 4.1 0.07 0.007 0.0150 2.14 1.66 0.104 3 Comparative Example 103 83.46 7.6 8.6 0.32 0.006 0.0100 1.67 1.64 0.105 3 Comparative Example 104 78.37 18.3 2.8 0.52 0.008 0.0080 1.00 1.60 0.102 2 Comparative Example 105 81.32 16.6 1.8 0.26 0.007 0.0120 1.71 1.63 0.104 2 Comparative Example 106 79.36 11.2 9.3 0.11 0.008 0.0180 2.25 1.61 0.103 2 Comparative Example 107 80.84 13.3 5.8 0.04 0.010 0.0150 1.50 1.62 0.102 2 Comparative Example 108 79.24 13.8 6.3 0.63 0.012 0.0200 1.67 1.60 0.103 3 Comparative Example 109 81.33 14.2 4.1 0.23 0.024 0.1200 5.00 1.62 0.104 5 Comparative Example 110 81.54 13.2 4.8 0.46 0.008 0.0008 0.10 1.63 0.103 5 Comparative Example 111 81.58 12.0 6.0 0.18 0.018 0.2200 12.22 1.63 0.103 3 Comparative Example 112 80.82 14.3 4.6 0.25 0.022 0.0040 0.18 1.62 0.101 5 Comparative example 113 80.14 15.1 4.2 0.34 0.012 0.2100 17.50 1.62 0.101 3 The underlined part indicates that it is outside the scope of this invention.

[0053] As shown in Table 1A, the alloy compositions of Examples 1 to 22 of the present invention all satisfy the scope of the present invention. Therefore, the saturation magnetic flux density is 1.60T or higher, and the iron loss (iron loss W 13 / 50) at a magnetic flux density of 1.3T and a frequency of 50Hz is 0.100W / kg or lower, thus simultaneously exhibiting high saturation magnetic flux density and low iron loss. Furthermore, the bending failure diameter is 4mm or lower, and the machinability is also good.

[0054] On the other hand, as shown in Table 1B, the alloy compositions of Comparative Examples 101 to 113 do not meet the scope of the present invention, therefore the iron loss (iron loss W 13 / 50) is greater than 0.100 W / kg, or the saturation magnetic flux density is less than 1.60 T.

[0055] That is, in Comparative Example 101, the Fe content is low and the saturation magnetic flux density is less than 1.60T. In Comparative Example 102, the Fe content is excessive and the iron loss (iron loss W 13 / 50) is greater than 0.100W / kg.

[0056] In Comparative Example 103, the B content was low, and the iron loss (iron loss W 13 / 50) was greater than 0.100 W / kg. In Comparative Example 104, the B content was excessive, and the iron loss (iron loss W 13 / 50) was greater than 0.100 W / kg.

[0057] In Comparative Example 105, the Si content was low, and the iron loss (iron loss W 13 / 50) was greater than 0.100 W / kg. In Comparative Example 106, the Si content was excessive, and the iron loss (iron loss W 13 / 50) was greater than 0.100 W / kg.

[0058] In Comparative Example 107, the Mn content was low, and the iron loss (iron loss W 13 / 50) was greater than 0.100 W / kg. In Comparative Example 108, the Mn content was excessive, and the iron loss (iron loss W 13 / 50) was greater than 0.100 W / kg.

[0059] In Comparative Example 109, the sulfur content was excessive, and the bending failure diameter was greater than 4 mm. Furthermore, the iron loss (iron loss W 13 / 50) was greater than 0.100 W / kg.

[0060] In Comparative Example 110, the N content was low, and the bending failure diameter was greater than 4 mm. Furthermore, the iron loss (iron loss W 13 / 50) was greater than 0.100 W / kg. In Comparative Example 111, the N content was excessive, and the iron loss (iron loss W 13 / 50) was greater than 0.100 W / kg.

[0061] In Comparative Example 112, the sulfur content was excessive, and the bending failure diameter was greater than 4 mm. Furthermore, the iron loss (iron loss W 13 / 50) was greater than 0.100 W / kg. In Comparative Example 113, the nitrogen content was excessive, and the iron loss (iron loss W 13 / 50) was greater than 0.100 W / kg.

[0062] Furthermore, X-ray diffraction measurements were performed on the Fe-based amorphous alloy thin strips. The results showed that no clear diffraction peaks were observed in Examples 1 to 22 of the present invention and Comparative Examples 101 to 113. Therefore, it cannot be said that a crystalline phase was generated in the metal structure, and the whole system is an amorphous phase.

[0063] (Example 2) Using alloys with various compositions obtained by replacing a portion of Fe with at least one of Ni, Cr, and Co for each alloy shown in No. 1 of Table 1A, thin strips were cast using the same apparatus and conditions as in Example 1. Furthermore, the specific compositions of the alloys used are shown in Table 2. As a result, the thickness, width, and length of the obtained thin strips were approximately 20 μm, 10 mm, and approximately 100 m, respectively. The saturation magnetic flux density, iron loss, and bending failure diameter of the obtained thin strips 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. Furthermore, the display method in Table 2 is the same as in Tables 1A and 1B.

[0064] [Table 2] No. Remaining chemical components: impurities Fe (atom%) Ni (atom%) Cr (atom%) Co (atom%) B (atom%) Si (atom%) Mn (atom%) S (atom%) N (atom%) N / S Example of the present invention twenty three 79.67 1.00 15.4 3.6 0.30 0.006 0.0200 3.3 Example of the present invention twenty four 77.67 3.00 15.4 3.6 0.30 0.006 0.0200 3.3 Example of the present invention 25 78.67 2.00 15.4 3.6 0.30 0.006 0.0200 3.3 Example of the present invention 26 75.67 3.00 2.00 15.4 3.6 0.30 0.006 0.0200 3.3 Example of the present invention 27 74.67 3.00 3.00 15.4 3.6 0.30 0.006 0.0200 3.3 Example of the present invention 28 73.67 3.00 4.00 15.4 3.6 0.30 0.006 0.0200 3.3 Example of the present invention 29 71.67 2.00 4.00 3.00 15.4 3.6 0.30 0.006 0.0200 3.3

[0065] Based on the results of samples No. 23-29 in Table 2, it can be seen that even when replacing a portion of Fe with at least one of Ni, Cr, or Co within the range of less than 10.0 atomic percent, the saturation magnetic flux density is above 1.60 T, and the iron loss W13 / 50 can be stably kept below 0.100 W / kg. Furthermore, the bending failure diameter is less than 4 mm, and the workability is also good. Moreover, no clear diffraction peaks were observed in X-ray diffraction measurements of any of the samples, confirming them as amorphous.

[0066] According to the above embodiments, it can be seen that the Fe-based amorphous alloy of the present invention, by optimizing the content of B and Si, containing an appropriate amount of Mn, further containing S and N, and further making the Fe content 78.00% or more, improves its machinability. Furthermore, at a magnetic flux density of 1.3T and a frequency of 50Hz, the iron loss (iron loss W 13 / 50) is 0.100W / kg or less, and the saturation magnetic flux density is 1.60T or more, exhibiting excellent soft magnetic properties, making it suitable for use in the cores of power transformers or high-frequency transformers.

[0067] Furthermore, according to the Fe-based amorphous alloy strip of the present invention, the bending failure diameter is 4 mm or less. Also, the iron loss (iron loss W 13 / 50) is 0.100 W / kg or less, and the saturation magnetic flux density is 1.60 T or more. Therefore, it is clear that when the Fe-based amorphous alloy strip is processed into the core of a power transformer or high-frequency transformer, there is no concern about the alloy strip breaking, thus improving the productivity of the core of the power transformer or high-frequency transformer. [Industrial Applicability]

[0068] The Fe-based amorphous alloys and Fe-based amorphous alloy strips disclosed herein have excellent machinability, and therefore have high industrial applicability.

Claims

1. An Fe-based amorphous alloy, comprising, in atomic percent: B: 8.0% or more and 18.0% or less, Si: 2.0% or more and 9.0% or less, Mn: 0.05% or more and 0.60% or less, Fe: 78.00% or more and 86.00% or less, S: 0.006% or more and 0.020% or less, and N: 0.0010% or more and 0.2000% or less, the remainder being composed of impurities, wherein the C content of the aforementioned impurities is less than 0.03 atomic percent; and the microstructure of the Fe-based amorphous alloy is amorphous; the atomic ratio of N to S (N / S) is 0.20 or more and 15 or less.

2. The Fe-based amorphous alloy as claimed in Item 1, wherein B: 13.0 atomic% or more and 18.0 atomic% or less.

3. The Fe-based amorphous alloy as claimed in Item 1, wherein Si comprises 2.0 atomic% or more and 6.0 atomic% or less.

4. The Fe-based amorphous alloy as claimed in Item 2, wherein Si comprises 2.0 atomic% or more and 6.0 atomic% or less.

5. The Fe-based amorphous alloy as claimed in Item 1, wherein N: ≥0.0030 atomic% and ≤0.2000 atomic% 6. The Fe-based amorphous alloy as claimed in claim 2, wherein N: ≥0.0030 atomic% and ≤0.2000 atomic% 7. The Fe-based amorphous alloy as claimed in claim 3, wherein N: ≥0.0030 atomic% and ≤0.2000 atomic% 8. The Fe-based amorphous alloy as claimed in claim 4, wherein N: ≥0.0030 atomic% and ≤0.2000 atomic% 9. For any of the Fe-based amorphous alloys in claims 1 to 8, wherein at least one of the elements Ni, Cr, and Co is used to replace Fe in the range of less than 10.0 atomic percent.

10. For any of the Fe-based amorphous alloys in claims 1 to 8, the iron loss W13 / 50 when magnetized at a frequency of 50 Hz and a magnetic flux density of 1.3 T is less than 0.100 W / kg, and the saturation magnetic flux density is more than 1.60 T.

11. For the Fe-based amorphous alloy as claimed in Item 9, the iron loss W13 / 50 when magnetized at a frequency of 50Hz and a magnetic flux density of 1.3T is less than 0.100W / kg, and the saturation magnetic flux density is more than 1.60T.

12. The Fe-based amorphous alloy as claimed in Item 1, wherein the Fe content is 82.05 atomic% or more.

13. The Fe-based amorphous alloy as claimed in Item 1, wherein the Fe content is 79.21 atomic% or less.

14. The Fe-based amorphous alloy as claimed in Item 1, wherein the Mn content is 0.45 atomic% or more.

15. An Fe-based amorphous alloy strip, comprising any one of the Fe-based amorphous alloys as claimed in claims 1 to 14.

16. The Fe-based amorphous alloy ribbon of claim 15, wherein at least one of the elements Ni, Cr, and Co is used to replace Fe in the range of less than 10.0 atomic percent.

17. The Fe-based amorphous alloy thin strip of claim 15 has an iron loss W13 / 50 of less than 0.100 W / kg and a saturation magnetic flux density of more than 1.60 T when magnetized at a frequency of 50 Hz and a magnetic flux density of 1.3 T.

18. The Fe-based amorphous alloy strip of claim 15 has a bending failure diameter of less than 4 mm.

19. The Fe-based amorphous alloy thin strip of claim 18 has a bending failure diameter of less than 2 mm.