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

Abstract

To provide an Fe-based amorphous alloy and an Fe-based amorphous alloy ribbon having low iron loss, high magnetic flux density, and excellent processability.SOLUTION: An Fe-based amorphous alloy having excellent soft magnetic characteristics is adopted that contains, in atom%, Fe of 78.00% or more and 85.00% or less, B of 7.5% or more and 15.0% or less, Si of more than 6.0% to 10.0% or less, C of 0.5% or more and 5.0% or less, and Al of 0.005% or more and 1.50% or less, with the balance being impurities.SELECTED DRAWING: None

Description

Technical Field

[0001] The present invention relates to an Fe-based amorphous alloy having excellent soft magnetic properties and an Fe-based amorphous alloy ribbon having excellent soft magnetic properties.

Background Art

[0002] As methods for continuously producing ribbons and wires by rapidly cooling an alloy from a molten state, a centrifugal rapid cooling method, a single-roll method, a double-roll method, etc. are known. These methods produce ribbons and wires by rapidly solidifying the molten metal by ejecting the molten metal from an orifice or the like onto the inner peripheral surface or the outer peripheral surface of a rapidly rotating metal drum. Further, by appropriately selecting the alloy composition, an amorphous alloy similar to a liquid metal can be obtained, and a material excellent in magnetic properties or mechanical properties can be produced.

[0003] In particular, among amorphous alloys, Fe-based amorphous alloys are regarded as promising for applications such as cores of power transformers and high-frequency transformers. In order to improve the performance of these applications, there is a strong demand for reducing the iron loss and increasing the magnetic flux density of Fe-based amorphous alloys.

[0004] Patent Document 1 discloses an alloy represented by the composition TM a Si b B c C d M e (TM is at least one of Fe, Co, and Ni, M is at least one of Al, Ti, and Zr, a to e are atomic %, a: 70 to 85, b: 4 to 18, c: 7 to 18, d: 0 to 4, e: 0.01 to 0.3, and a + b + c + d + e = 100). The molten alloy is ejected onto a moving cooling substrate through a multi-slit nozzle having a plurality of openings and rapidly solidified to produce an amorphous alloy ribbon having at least one crystallization layer inside the plate thickness and excellent magnetic properties. As can be seen from FIG. 3 of Patent Document 1, the amorphous alloy ribbon described in Patent Document 1 has a saturation magnetic flux density of less than 1.5 T, which is somewhat low for use in applications such as cores of power transformers and high-frequency transformers.

[0005] Patent Document 2 describes an Fe-based amorphous alloy having excellent soft magnetic properties, which contains, in atomic percentages, 80.0% or more and 88.0% or less of Fe, 6.0% or more and 12.0% or less of B, 2.0% or more and 8.0% or less of C, 0.10% or more and 3.0% or less of Si, 0.10% or more and 2.0% or less of Al, further contains 0.10% or more and 6.0% or less of Mo, and the balance consists of inevitable impurities. However, the Fe-based amorphous alloy described in Patent Document 2 contains Mo, which is a high melting point element, and the manufacturing cost is somewhat high.

[0006] Patent Document 3 describes an amorphous alloy for an iron core having a high saturation magnetic flux density represented by the formula: Fe a B b P c Si d C e X f (where X is any one or two or more selected from Al, Sn, Ge, Ti, Zr, Nb, V, Mo, W, b is 1 to 5 atomic% of B, c is 1 to 10 atomic% of P, d is 4 to 14 atomic% of Si, e is 5 atomic% or less of C, f is 5 atomic% or less of X, and a is (100-(b + c + d + e + f)) atomic% of Fe). Judging from the examples of Patent Document 3, some of the amorphous alloys for an iron core described in Patent Document 3 have a saturation magnetic flux density exceeding 1.5 T, but low iron loss cannot be expected.

Prior Art Documents

Patent Documents

[0007]

Patent Document 1

Patent Document 2

Patent Document 3

Summary of the Invention

Problems to be Solved by the Invention

[0008] As described above, Fe-based amorphous alloys are regarded as promising for applications such as cores of power transformers and high-frequency transformers. In order to improve the performance of these applications, there is a strong demand for reducing the iron loss and increasing the magnetic flux density of Fe-based amorphous alloys. In addition, when applying Fe-based amorphous alloys to uses such as cores, in addition to having characteristics of low iron loss and high magnetic flux density, excellent workability is also required. Therefore, the present invention has been made in view of the above circumstances, and an object thereof 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 workability.

Means for Solving the Problems

[0009] In order to solve the above problems, the present invention adopts the following configuration. [1] An Fe-based amorphous alloy containing, in atomic%, 78.00% or more and 85.00% or less of Fe, 7.5% or more and 15.0% or less of B, more than 6.0% and 10.0% or less of Si, 0.5% or more and 5.0% or less of C, 0.005% or more and 1.50% or less of Al, and the balance being composed of impurities and the metal structure is an amorphous structure, the saturation magnetic flux density is 1.62 T or more, and the iron loss at a magnetic flux density of 1.3 T and a frequency of 50 Hz is 0.095 W / kg or less, Fe-based amorphous alloy. [2] An Fe-based amorphous alloy containing, in atomic%, 78.00% or more and 85.00% or less of Fe, 7.5% or more and 13.0% or less of B, more than 6.0% and 9.0% or less of Si, 1.0% or more and 4.0% or less of C, 0.005% or more and 1.50% or less of Al, and the balance being composed of impurities and the metal structure is an amorphous structure, the saturation magnetic flux density is 1.62 T or more, and the iron loss at a magnetic flux density of 1.3 T and a frequency of 50 Hz is 0.095 W / kg or less, Fe-based amorphous alloy. [3] At least one of Ni, Cr, and Co, and replacing Fe of the Fe-based amorphous alloy described in [1] or [2] in the range of 10.0 atomic% or less 、F e-based amorphous alloy. [4] An Fe-based amorphous alloy ribbon made of the Fe-based amorphous alloy according to any one of [1] to [3] 、F e-based amorphous alloy ribbon.

Effects of the Invention

[0010] 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, a high magnetic flux density, and excellent workability.

Embodiments for Carrying Out the Invention

[0011] Among various alloy components proposed so far, the present inventor focused on a component system mainly composed of Fe, B, C, and Si, and conducted studies and experiments to achieve low iron loss while maintaining a high magnetic flux density. Then, attention was paid to Al, which has conventionally been considered disadvantageous for amorphization. As is clear from the fact that Al is used as an element that forms a crystalline phase on the ribbon surface in Patent Document 1, Al has conventionally been known as an element that easily forms a crystalline phase. On the other hand, as described in Patent Document 2, there is also a finding that the thermal stability of the amorphous phase is improved by adding Al and Si.

[0012] Therefore, as a result of detailed experiments by the present inventors on a component system mainly composed of Fe with B, C, and Si as the main additive elements, it was found that low iron loss can be achieved by containing a small amount of Al. In addition, in order to compensate for the decrease in the amorphous layer forming ability due to the inclusion of Al, the optimal content ranges of Si, C, and B were found. As a result, without the need for the addition of Mo as described in Patent Document 2, the saturation magnetic flux density can be set to 1.62 T or more, and the iron loss (iron loss W 13 / 50 ) at a magnetic flux density of 1.3 T and a frequency of 50 Hz can be made 0.095 W / kg or less. Furthermore, it was found that excellent workability can be exhibited by optimizing the content of C within a range that does not reduce the amorphous layer forming ability. In this way, the inventors have completed an invention related to an Fe-based amorphous alloy that simultaneously exhibits a high saturation magnetic flux density, low iron loss, and excellent workability.

[0013] Hereinafter, the Fe-based amorphous alloy and the Fe-based amorphous alloy ribbon having excellent soft magnetic properties according to the present embodiment will be described. The Fe-based amorphous alloy of this embodiment contains, in atomic percentage, 78.00% or more and 85.00% or less of Fe, 7.5% or more and 15.0% or less of B, more than 6.0% and 10.0% or less of Si, 0.5% or more and 5.0% or less of C, 0.005% or more and 1.50% or less of Al, and the balance consists of impurities. Further, the Fe-based amorphous alloy of this embodiment may contain, in atomic percentage, 78.00% or more and 85.0% or less of Fe, 7.5% or more and 13.0% or less of B, more than 6.0% and 9.0% or less of Si, 1.0% or more and 4.0% or less of C, 0.005% or more and 1.50% or less of Al, and the balance consists of impurities. Further, the Fe-based amorphous alloy of this embodiment may be substituted with at least one of Ni, Cr, and Co in the range of 10.0 atomic% or less of Fe in the above Fe-based amorphous alloy. Further, the Fe-based amorphous alloy ribbon of this embodiment is made of the above Fe-based amorphous alloy.

[0014] First, the reasons for limiting the content of each element in the Fe-based amorphous alloy of this embodiment will be described.

[0015] Al is contained in the Fe-based amorphous alloy of this embodiment to achieve low iron loss. However, when the content of Al increases, the ability to form an amorphous phase decreases, and it becomes difficult to stably obtain an amorphous alloy, so it becomes difficult to stably set the saturation magnetic flux density to 1.62 T or more. Therefore, the Al content is in the range of 0.005 to 1.50%. The Al content may be 0.008% or more, 0.01% or more, 1.40% or less, or 1.30% or less.

[0016] B is contained in the Fe-based amorphous alloy of the present embodiment in order to improve the formation of the amorphous phase and the thermal stability of the amorphous phase. By optimizing the content of this element, it is possible to cancel out the decrease in the amorphous phase forming ability associated with the inclusion of Al and make the alloy structure stably an amorphous phase, and it becomes possible to further improve the soft magnetic properties. For example, the saturation magnetic flux density can be stably made 1.62 T or more. When B is less than 7.5 atomic%, improvement in the amorphous phase forming ability cannot be obtained, and an amorphous alloy cannot be stably obtained in the Fe-based amorphous alloy, and it becomes difficult to stably make the saturation magnetic flux density 1.62 T or more while maintaining the iron loss stably at 0.095 W / kg or less. On the other hand, even when B exceeds 15.0 atomic%, improvement in the amorphous phase forming ability cannot be obtained, and it becomes difficult to stably make the saturation magnetic flux density 1.62 T or more. Therefore, B is limited to the range of 7.5 atomic% or more and 15.0 atomic% or less. Preferably, B is 7.5 atomic% or more and 13.0 atomic% or less. More preferably, B is 8.0 atomic% or more and 12.5 atomic% or less.

[0017] Si and C, similar to B, are included in the Fe-based amorphous alloy of this embodiment to improve the formation of the amorphous phase and the thermal stability of the amorphous phase. Also, Si and C are elements effective for improving the workability of the Fe-based amorphous alloy. By optimizing the contents of Si and C, the decrease in the amorphous phase forming ability associated with the inclusion of Al can be offset, enabling the alloy structure to be stably formed as an amorphous phase and further improving the soft magnetic properties. Also, by improving the workability, the bending fracture diameter when forming a Fe-based amorphous alloy ribbon can be made 3.5 mm or less. If Si is 6.0 atomic % or less and C is less than 0.5 atomic %, the improvement in the amorphous phase forming ability cannot be obtained, and it becomes difficult to stably obtain an amorphous alloy in the Fe-based amorphous alloy and stably achieve a saturation magnetic flux density of 1.62 T or more. On the other hand, even if Si exceeds 10.0 atomic % and C exceeds 5.0 atomic %, the improvement in the amorphous phase forming ability cannot be obtained, and the workability deteriorates. Therefore, Si is limited to a range of more than 6.0 atomic % and 10.0 atomic % or less, and C is limited to a range of 0.5 atomic % or more and 5.0 atomic % or less. Preferably, Si is more than 6.0 atomic % and 9 atomic % or less, and C is 1.0 atomic % or more and 4.0 atomic % or less. More preferably, Si is more than 6.0 atomic % and 8.0 atomic % or less, and C is 1.0 atomic % or more and 3.5 atomic % or less.

[0018] In the Fe-based amorphous alloy, if the Fe content is usually 70 atomic % or more, a saturation magnetic flux density at a practical level as a general core can be obtained. However, in order to obtain a high saturation magnetic flux density of 1.62 T or more, it is necessary to set Fe to 78.00 atomic % or more. On the other hand, when the Fe content exceeds 85.00 atomic %, it becomes difficult to form the amorphous phase, and it becomes difficult to obtain good soft magnetic properties (stable iron loss W13 / 50 of 0.095 W / kg or less) peculiar to the amorphous alloy. Therefore, in the Fe-based amorphous alloy of this embodiment, the Fe content is limited to a range of 78.00 atomic % or more and 85.00 atomic % or less. A more preferable Fe content is 79.00 atomic % or more and 84.00 atomic % or less.

[0019] In the Fe-based amorphous alloy of this embodiment, by substituting a part of Fe with at least one of Ni, Cr, and Co in the 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. An upper limit is set for the substitution amount by these elements because when it exceeds 10.0 atomic%, the saturation magnetic flux density decreases and the raw material cost increases. When Fe is substituted with one or more of Ni, Cr, and Co, the total of the contents of Ni, Cr, and Co and the content of Fe may be in the range of 78.00 atomic% or more and 85.00 atomic% or less, and may also be in the range of 79.00 atomic% or more and 84.00 atomic% or less.

[0020] The remainder in the Fe-based amorphous alloy according to this embodiment is an impurity. The Fe-based amorphous alloy according to this embodiment may contain impurity elements contained in the steel material as impurities when, for example, a steel material is used as the Fe source. For example, N, P, S, O, etc. may be contained as impurities.

[0021] The Fe-based amorphous alloy of this embodiment can usually be obtained in the form of a thin strip. This Fe-based amorphous alloy thin strip is obtained by melting an alloy composed of the components described in the above embodiment, ejecting the molten metal onto a cooling plate that is moving at high speed through a slot nozzle or the like, and rapidly solidifying the molten metal. For example, it can be manufactured by a single-roll method or a twin-roll method. The rolls used in these roll methods are made of metal, and by rotating the rolls at high speed and causing the molten metal to collide with the roll surface or the inner surface of the roll, rapid solidification of the alloy is possible.

[0022] Single-roll devices include centrifugal rapid cooling devices that use the inner wall of a drum, devices that use an endless type belt, and improved versions thereof with auxiliary rolls and roll surface temperature control devices attached, as well as casting devices under reduced pressure, in a vacuum, or in an inert gas.

[0023] In this embodiment, the dimensions such as the thickness and width of the thin strip are not particularly limited, but the thickness of the thin strip is preferably, for example, 10 μm or more and 100 μm or less. Also, the width is preferably 10 mm or more. The Fe-based amorphous alloy ribbon obtained as described above can be used for applications such as cores in power transformers and high-frequency transformers.

[0024] In addition, the Fe-based amorphous alloy of this embodiment can also be in powder form in addition to the ribbon form. In that case, a method can be adopted in which the molten alloy or droplets of the molten alloy are ejected at high speed into a rotating roll or a liquid such as cooling water from a nozzle of a crucible filled with the molten alloy of the above-described composition, and rapidly solidified by rapid cooling.

[0025] By the above method, Fe-based amorphous alloy powder excellent in soft magnetic properties can be obtained.

[0026] The Fe-based soft magnetic alloy powder obtained as described above can be applied to applications such as cores of power transformers, high-frequency transformers, and coils by being consolidated by a mold or the like into a desired shape, and sintered and integrated as necessary.

[0027] Whether or not the Fe-based amorphous alloy of this embodiment has an amorphous structure can be confirmed, for example, by X-ray diffraction measurement using an X-ray diffractometer with a Co tube target. That is, when no distinct diffraction peak is obtained in the X-ray diffraction measurement, it can be confirmed that the Fe-based amorphous alloy has an amorphous structure.

[0028] As described above, according to the Fe-based amorphous alloy of this embodiment, by containing Al, optimizing the contents of B, Si, and C, and further making the content of Fe 78.00% or more, the iron loss (iron loss W 13 / 50 ) at a magnetic flux density of 1.3 T and a frequency of 50 Hz becomes 0.095 W / kg or less, the saturation magnetic flux density becomes 1.62 T or more, excellent soft magnetic properties can be exhibited, and it can be suitably used for cores of power transformers and high-frequency transformers. Also, the workability can be improved.

[0029] Also, according to the Fe-based amorphous alloy ribbon of the present embodiment, by containing Al, optimizing the contents of B, Si, and C, and further setting the Fe content to 78.00% or more, the iron loss (iron loss W 13 / 50 ) at a magnetic flux density of 1.3 T and a frequency of 50 Hz is 0.095 W / kg or less, the saturation magnetic flux density is 1.62 T or more, excellent soft magnetic properties can be exhibited, and it can be suitably used for cores of power transformers, high-frequency transformers, etc. Further, by improving the workability, the bending fracture diameter can be made 3.5 mm or less. As a result, when processing the Fe-based amorphous alloy ribbon into a core of a power transformer, a high-frequency transformer, etc., there is no risk of the alloy ribbon being damaged, and the productivity of the cores of the power transformer and the high-frequency transformer can be improved.

[0030] The bending fracture radius conforms to the metal material bending test method of JIS Z 2248:2006. A ribbon made of an Fe-based amorphous alloy is installed on a bending test machine, and both ends of the test piece are pressed against each other until they are in close contact, and the diameter of the test piece (bending fracture diameter) at the time of fracture is measured to obtain it.

Examples

[0031] Hereinafter, examples of the present invention will be described.

[0032] (Example 1) An alloy of various components shown in Table 1 was melted in an argon atmosphere and rapidly cooled and cast with a single-roll device to produce a ribbon of Fe-based amorphous alloy. The casting atmosphere was the atmosphere. The single-roll device used was composed of a copper alloy cooling roll with a diameter of 300 mm, a high-frequency power source for sample melting, a quartz crucible with a slot nozzle at the tip, etc. 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 about 20 μm, the width of the ribbon depended on the length of the slot nozzle and was 10 mm, and the length was approximately 100 m.

[0033] X-ray diffraction measurement was performed on the obtained Fe-based amorphous alloy ribbon to obtain an X-ray diffraction pattern. The X-ray source for the X-ray diffraction measurement was Co-Kα (wavelength λ = 1.7902 Å), and the scan range was 2θ = 10 deg or more and 120 deg or less. From the shape of the X-ray diffraction pattern, it was determined whether or not a crystalline phase was formed in the metal structure.

[0034] In addition, 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 kHz. Samples for iron loss measurement were all taken from 6 locations across the entire length of one lot of the 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 1 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 was a nitrogen atmosphere. On the other hand, the samples for the VSM apparatus were all thin flakes taken from the center of the width of the ribbon samples from the above 6 locations.

[0035] The measurement results of the saturation magnetic flux density and iron loss are shown in Table 1 as the average values of the data at 6 locations.

[0036] Furthermore, for the Fe-based amorphous alloy ribbon, the bending fracture diameter was measured. The bending fracture radius was measured in accordance with the bending test method for metallic materials in JIS Z 2248:2006. The Fe-based amorphous alloy ribbon was installed on a bending testing machine, and the bending fracture diameter at the time of fracture was measured. The results are shown in Table 1.

[0037]

Table 1

[0038] As shown in Table 1, in Examples 1 to 17 of the present invention, since the alloy compositions all satisfied the scope of the present invention, the saturation magnetic flux density was 1.62 T or more, and the iron loss (iron loss W 13 / 50) was 0.095 W / kg or less, and it was possible to simultaneously exhibit a high saturation magnetic flux density and low iron loss. Also, the bending fracture diameter was 3.5 mm or less, and the workability was good.

[0039] On the other hand, in Comparative Examples 1 to 10, since the alloy compositions did not satisfy the scope of the present invention, the iron loss (iron loss W 13 / 50 ) exceeded 0.095 W / kg or the saturation magnetic flux density became less than 1.62 T.

[0040] That is, in Comparative Example 1, since the Fe content was low, the saturation magnetic flux density became less than 1.62 T. In Comparative Example 2, since the Fe content was excessive, the iron loss (iron loss W 13 / 50 ) exceeded 0.095 W / kg. In Comparative Examples 3 and 4, since the B content deviated from the scope of the present invention, the iron loss (iron loss W 13 / 50 ) exceeded 0.095 W / kg. In Comparative Examples 5 and 6, since the Si content deviated from the scope of the present invention, the iron loss (iron loss W 13 / 50 ) exceeded 0.095 W / kg. In Comparative Examples 7 and 8, since the C content deviated from the scope of the present invention, the iron loss (iron loss W 13 / 50 ) exceeded 0.095 W / kg. In Comparative Examples 9 and 10, since the Al content deviated from the scope of the present invention, the iron loss (iron loss W 13 / 50 ) exceeded 0.095 W / kg. Also, in Comparative Example 10, the bending fracture diameter exceeded 3.5 mm, and the workability became inferior.

[0041] When X-ray diffraction measurement was performed on the Fe-based amorphous alloy ribbon, in Examples 1 to 17 and Comparative Examples 1 to 10 of the present invention, no distinct diffraction peak was observed, so it cannot be said that a crystalline phase was formed in the metal structure, and the whole was an amorphous phase.

[0042] (Example 2) Regarding the alloy shown as No. 1 in Table 1, using alloys of various components in which a part of Fe was replaced with at least one of Ni, Cr, and Co, a thin strip was cast under the same apparatus and conditions as in Example 1. The specific components of the alloys used are shown in Table 2. As a result, the thickness, width, and length of the obtained thin strip were approximately 20 μm, 10 mm, and approximately 100 m, respectively. The saturation magnetic flux density, iron loss, and bending fracture radius of the obtained thin strip were evaluated. The sampling method and measurement conditions of the samples used for these characteristic evaluations were the same as those in Example 1. The measurement results are shown in Table 2. The display format in Table 2 is the same as that in the case of Table 1.

[0043]

Table 2

[0044] As is clear from the results of Samples Nos. 18 to 24 in Table 2, even when a part of Fe was replaced with at least one of Ni, Cr, and Co in the range of 10.0 atomic% or less, the saturation magnetic flux density was 1.62 T or more, and the iron loss could be stably 0.095 W / kg or less in W. 13 / 50 Also, the bending fracture diameter was 3.5 mm or less, and the workability was good. Furthermore, for all samples, no distinct diffraction peak was observed in the X-ray diffraction measurement, and it was confirmed that they were amorphous.

[0045] As described above, according to the Fe-based amorphous alloy of the present invention, by containing Al, optimizing the contents of B, Si, and C, and further making the Fe content 78.00% or more, the iron loss (iron loss W 13 / 50 ) at a magnetic flux density of 1.3 T and a frequency of 50 Hz becomes 0.095 W / kg or less, the saturation magnetic flux density becomes 1.62 T or more, excellent soft magnetic properties can be exhibited, and it can be suitably used for cores of power transformers, high-frequency transformers, etc. Also, the workability can be improved. Also, according to the Fe-based amorphous alloy thin strip of the present invention, the iron loss (iron loss W 13 / 50) becomes 0.095 W / kg or less, the saturation magnetic flux density becomes 1.62 T or more, and further, the bending fracture diameter can be made 3.5 mm or less. As a result, when processing the Fe-based amorphous alloy ribbon into the core of a power transformer, a high-frequency transformer, etc., there is no risk of the alloy ribbon being damaged, and the productivity of the core of the power transformer or the high-frequency transformer can be improved.

Claims

1. In atomic percentage, it contains 78.00% or more and 85.00% or less of Fe, 7.5% or more and 15.0% or less of B, more than 6.0% and 10.0% or less of Si, 0.5% or more and 5.0% or less of C, 0.005% or more and 1.50% or less of Al, and the balance consists of impurities. The metallographic structure consists of an amorphous structure. An Fe-based amorphous alloy having a saturation magnetic flux density of 1.62 T or more and an iron loss of 0.095 W / kg or less at a magnetic flux density of 1.3 T and a frequency of 50 Hz.

2. In atomic percentage, it contains 78.00% or more and 85.00% or less of Fe, 7.5% or more and 13.0% or less of B, more than 6.0% and 9.0% or less of Si, 1.0% or more and 4.0% or less of C, 0.005% or more and 1.50% or less of Al, and the balance consists of impurities. The metallographic structure consists of an amorphous structure. An Fe-based amorphous alloy having a saturation magnetic flux density of 1.62 T or more and an iron loss of 0.095 W / kg or less at a magnetic flux density of 1.3 T and a frequency of 50 Hz.

3. An Fe-based amorphous alloy in which at least one of Ni, Cr, and Co substitutes Fe in the Fe-based amorphous alloy according to Claim 1 or 2 in the range of 10.0 atomic% or less.

4. An Fe-based amorphous alloy ribbon made of the Fe-based amorphous alloy according to any one of Claims 1 to 3.

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