Fe-BASED AMORPHOUS ALLOY, Fe-BASED AMORPHOUS ALLOY RIBBON, AND IRON CORE

Abstract

This Fe-based amorphous alloy has an amorphous structure and contains, in terms of at%, 8.0-18.0% B, 0.10-9.0% Si, 0.10-5.0% C, 0.05-0.60% Mn, 0.010-0.40% Sn, and 78.000-86.000% Fe, with the remainder comprising impurities.

Description

Fe-based amorphous alloy, Fe-based amorphous alloy ribbon and iron core

[0001] The present invention relates to an Fe-based amorphous alloy, an Fe-based amorphous alloy ribbon, and an iron core, and more particularly to an Fe-based amorphous alloy, an Fe-based amorphous alloy ribbon, and an iron core having excellent soft magnetic properties. This application claims priority based on Japanese Patent Application No. 2024-098236, filed on June 18, 2024, the contents of which are incorporated herein by reference.

[0002] Known methods for continuously producing ribbons or wires by rapidly cooling alloys 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 the like 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] Among amorphous alloys, Fe-based amorphous alloys are particularly 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. For example, Patent Documents 1 to 4 describe Fe-based amorphous alloys.

[0004] Japanese Unexamined Patent Publication No. 5-140703 Japanese Unexamined Patent Publication No. 5-98402 Japanese Unexamined Patent Publication No. 2012-21190 International Publication No. 2015 / 016161

[0005] 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, an Fe-based amorphous alloy ribbon, and an iron core that have low iron loss and high magnetic flux density.

[0006] The Fe-based amorphous alloy of the present invention contains, in atomic %, B: 8.0% to 18.0%, Si: 0.10% to 9.0%, C: 0.10% to 5.0%, Mn: 0.05% to 0.60%, Sn: 0.010% to 0.40%, and Fe: 78.000% to 86.000%, with the balance being impurities, and has an amorphous structure. The Fe-based amorphous alloy ribbon of the present invention may be made of an Fe-based amorphous alloy. The iron core of the present invention may be made of an Fe-based amorphous alloy ribbon.

[0007] According to the present invention, it is possible to provide an Fe-based amorphous alloy, an Fe-based amorphous alloy ribbon, and an iron core that have low core loss and high magnetic flux density.

[0008] 1A and 1B are schematic diagrams showing an example of a wound core according to an embodiment of the present invention, and FIG. 2A and FIG. 2B are schematic diagrams showing an example of a stacked core according to an embodiment of the present invention.

[0009] The present inventors have found that by adjusting the contents of amorphous-forming elements such as B, C, and Si, an Fe-based amorphous alloy with improved amorphous-forming ability can be obtained. Furthermore, they have found that by adding Mn in the range of 0.05% to 0.60% and Sn in the range of 0.010 to 0.40%, the amorphous-forming ability can be further improved and excellent soft magnetic properties can be obtained. Specifically, the 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 and a saturation magnetic flux density of 1.60 T or more.

[0010] Hereinafter, an Fe-based amorphous alloy and an Fe-based amorphous alloy ribbon according to embodiments of the present invention will be described.

[0011] In this embodiment, excellent soft magnetic properties are defined as iron loss W １３／５０ This means that the magnetic flux density is low and the saturation magnetic flux density is high.

[0012] The Fe-based amorphous alloy of this embodiment contains, in atomic %, B: 8.0% to 18.0%, Si: 0.10% to 9.0%, C: 0.10% to 5.0%, Mn: 0.05% to 0.60%, Sn: 0.010% to 0.40%, and Fe: 78.000% to 86.000%, with the remainder being impurities, and has an amorphous structure.

[0013] The Fe-based amorphous alloy of this embodiment may also have a Mn content in the range of 0.10% to 0.40%. Furthermore, the Fe-based amorphous alloy of this embodiment may also have a Sn content in the range of 0.010% to 0.20%. Furthermore, the Fe-based amorphous alloy of this embodiment may also have a Si content in the range of 0.10% to less than 6.0%. Furthermore, the Fe-based amorphous alloy of this embodiment may have Fe substituted with at least one element selected from Ni, Cr, and Co in a range of 10.000 atomic % or less.

[0014] The Fe-based amorphous alloy ribbon of the present embodiment may be made of the above-mentioned Fe-based amorphous alloy. The iron core of the present embodiment may be made of the above-mentioned Fe-based amorphous alloy, Fe-based amorphous alloy ribbon, Fe-based amorphous alloy powder, or Fe-based amorphous alloy wire.

[0015] First, the reasons for limiting the content of each element in the Fe-based amorphous alloy of this embodiment will be described.

[0016] B is contained 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, provided that the other elements are included in the above-mentioned composition ranges, the alloy structure can be made into a stable amorphous phase, and the soft magnetic properties can be further improved. For example, iron loss W １３／５０ If the B content is less than 8.0 atomic %, the amorphous phase forming ability is not improved, and the amorphous alloy cannot be stably obtained in the Fe-based amorphous alloy. １３／５０On the other hand, even if the B content exceeds 18.0 atomic %, the amorphous phase forming ability is not improved, and the iron loss W １３／５０ It becomes difficult to stably maintain the B content at 0.100 W / kg or less. Therefore, the B content is set to 8.0 atomic % or more and 18.0 atomic % or less. Preferably, the B content is set to 10.0 atomic % or more or 11.0 atomic % or more. Also, the B content is preferably set to 15.0 atomic % or less or 14.0 atomic % or less.

[0017] Like B, Si and C are contained 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 contents of Si and C, provided that the other elements are included in the above-mentioned composition ranges, the alloy structure can be stably made into an amorphous phase, and the soft magnetic properties can be further improved. If Si is less than 0.10 atomic % and C is less than 0.10 atomic %, the amorphous phase forming ability cannot be improved, and an amorphous alloy cannot be stably obtained in the Fe-based amorphous alloy. This allows the iron loss W to be reduced while the saturation magnetic flux density is stably maintained at 1.60 T or more. １３／５０ On the other hand, even if Si exceeds 9.0 atomic % and C exceeds 5.0 atomic %, the amorphous phase forming ability is not improved, and the iron loss W １３／５０ It becomes difficult to stably maintain the Si content at 0.100 W / kg or less. Therefore, the Si content is set to 0.10 atomic % or more and 9.0 atomic % or less, and the C content is set to 0.10 atomic % or more and 5.0 atomic % or less. Preferably, the Si content is set to 0.40 atomic % or more, 1.0 atomic % or more, or 3.0 atomic % or more. Also, the Si content is preferably set to 8.6 atomic % or less, 7.5 atomic % or less, less than 6.0 atomic %, or 5.5 atomic % or less. Also, the C content is preferably set to more than 0.20 atomic %, 0.30 atomic % or more, 0.50 atomic % or more, 0.80 atomic % or more, or 1.0 atomic % or more. Also, the C content is preferably set to 4.0 atomic % or less, 3.0 atomic % or less, 2.0 atomic % or less, or 1.8 atomic % or less.

[0018] Mn is contained in the Fe-based amorphous alloy of this embodiment to improve the soft magnetic properties. Assuming that the other elements are contained in the above-mentioned composition ranges, the Mn content can be optimized to reduce the iron loss W １３／５０ When the Mn content is less than 0.05 atomic %, the iron loss W １３／５０ On the other hand, if the Mn content exceeds 0.60 atomic %, it becomes difficult to stably maintain the iron loss W １３／５０ It becomes difficult to stably maintain the Mn content 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. Preferably, the Mn content is set to 0.10 atomic % or more or 0.15 atomic % or more. Furthermore, the Mn content is set to 0.50 atomic % or less, 0.40 atomic % or less, or 0.30 atomic % or less.

[0019] Sn 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, assuming that the other elements are included in the above-mentioned composition ranges, the alloy structure can be stably made amorphous, thereby further improving the soft magnetic properties. Specifically, for example, when a ribbon made of an Fe-based amorphous alloy is produced by the single-roll method, the cooling rate on the free surface of the ribbon that does not contact the roll is slightly slower than that on the surface that contacts the roll, which raises a slight concern about the possibility of crystalline phase formation. However, by adding Sn, the amorphous phase forming ability can be further improved, thereby stably making the entire ribbon amorphous and suppressing deterioration of the soft magnetic properties. Specifically, the iron loss can be stably maintained at 0.100 W / kg or less while maintaining a saturation magnetic flux density of 1.60 T or more. If the Sn content is less than 0.010 atomic %, the amorphous phase forming ability is not improved, and the amorphous alloy cannot be stably obtained in the Fe-based amorphous alloy. As a result, the iron loss W １３／５０On the other hand, even if the Sn content exceeds 0.40 atomic %, the amorphous phase forming ability is not improved, and the iron loss W １３／５０ It is difficult to stably maintain the Sn content at 0.100 W / kg or less. Therefore, the Sn content is set to 0.010 atomic % or more and 0.40 atomic % or less. Preferably, the Sn content is set to 0.050 atomic % or more, 0.070 atomic % or more, or 0.10 atomic % or more. Also preferably, the Sn content is set to 0.30 atomic % or less, 0.20 atomic % or less, less than 0.20 atomic %, or 0.18 atomic % or less.

[0020] In Fe-based amorphous alloys, if the Fe content is 70.000 atomic % or more, a saturation magnetic flux density at a practical level for a general iron core can be obtained. However, in order to obtain a high saturation magnetic flux density of 1.60 T or more, it is necessary to make the Fe content 78.000 atomic % or more, provided that the other elements are contained in the above-mentioned composition ranges. On the other hand, if the Fe content exceeds 86.000 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 (0.100 W / kg or less). Therefore, in the Fe-based amorphous alloy of this embodiment, the Fe content is set to 78.000 atomic % or more and 86.000 atomic % or less. More preferably, the Fe content is 79.000 atomic % or more or 80.000 atomic % or more. Furthermore, more preferably, the Fe content is 84.000 atomic % or less or 83.000 atomic % or less.

[0021] In the Fe-based amorphous alloy of this embodiment, a portion of Fe is replaced with at least one of Ni, Cr, and Co in a range of 10.000 atomic % or less, thereby reducing iron loss W while maintaining a high saturation magnetic flux density. １３／５０Improvements in soft magnetic properties such as the above can also be achieved. The reason for setting an upper limit on the substitution amount with these elements is that if the amount exceeds 10.000 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 content of Ni, Cr, and Co and the Fe content may be 78.000 atomic % or more and 86.000 atomic % or less, or may be 79.000 atomic % or more, or 80.000 atomic % or more, or 84.000 atomic % or less, or 83.000 atomic % or less.

[0022] When a portion of Fe is substituted with at least one of Ni, Cr, and Co, the amount of substitution may be 0.100 atomic % or more, 0.500 atomic % or more, or 1.000 atomic % or more, and may be 8.000 atomic % or less, or 6.000 atomic % or less.

[0023] The remainder in the Fe-based amorphous alloy according to this embodiment is impurities. When, for example, 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 in a total amount of less than 0.150 atomic %. For example, the Fe-based amorphous alloy may contain impurities such as S, N, O, Al, Ti, etc. in a total amount of less than 0.150 atomic %, 0.100 atomic % or less, 0.050 atomic % or less, or 0.010 atomic % or less. Furthermore, the alloy may contain P as an impurity in a range of less than 0.070 atomic %, 0.050 atomic % or less, or 0.010 atomic % or less.

[0024] The chemical composition of the Fe-based amorphous alloy of this embodiment may be measured by a general analytical method. For example, the chemical composition may be measured using ICP-AES (Inductively Coupled Plasma-Atomic Emission Spectrometry). Specifically, the chemical composition is identified by measuring a test piece taken from the Fe-based amorphous alloy using a predetermined measuring device under conditions based on a pre-created calibration curve. C and S may be measured using a combustion-infrared absorption method, and N may be measured using an inert gas fusion-thermal conductivity method. O may be measured using an inert gas fusion-non-dispersive infrared absorption method.

[0025] The structure of the Fe-based amorphous alloy of this embodiment is an amorphous structure. This allows for excellent soft magnetic properties to be obtained. Whether or not the structure is amorphous can be confirmed, for example, by X-ray diffraction measurement using an X-ray diffractometer with a Cu 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 there is no peak with a half-width (full width at half maximum) of 4° or less of the diffraction peak of α-Fe (110).

[0026] In this embodiment, the measurement conditions for the X-ray diffraction measurement are as follows: an X-ray source is Cu-Kα (wavelength λ=1.5406 Å), a length limiting slit is 2 mm, a scan speed is 2 deg / min, a step width is 0.02 deg, a scan range is 2θ=5 deg or more and 100 deg or less, and the measurement method is the θ-2θ method.

[0027] The Fe-based amorphous alloy and the Fe-based amorphous alloy ribbon of this embodiment can be measured for saturation magnetic flux density and iron loss W by the method described below. １３／５０ When measuring the saturation magnetic flux density of 1.60 T or more, the iron loss (W １３／５０ ) becomes 0.100 W / kg or less, and the soft magnetic properties become excellent.

[0028] Iron loss W １３／５０ is measured using an SST (Single Sheet 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 ribbon coil. Ribbon samples cut to a length of 120 mm are used as samples for iron loss measurement. The width of the ribbon sample is the same as that of the ribbon. These ribbon samples for iron loss measurement are annealed in a magnetic field (magnetic field: 800 A / m, applied in the casting direction) for one hour at a predetermined temperature selected from the range of 320 to 380°C before being used for measurement. The atmosphere during annealing is a nitrogen atmosphere. The arithmetic mean value of the measured values ​​of the samples for iron loss measurement collected from the six locations is used as the iron loss (W １３／５０ )

[0029] On the other hand, the saturation magnetic flux density is measured using a VSM (vibrating sample magnetometer). The samples for the VSM device are thin pieces taken from the width center of each of the ribbon samples from the six locations. The VSM sample size is 5 mm square and is taken from the width center of the ribbon sample. The measurement conditions are to magnetize the ribbon sample to a maximum magnetizing force of 10 kOe in the positive direction and then to a maximum magnetizing force of 10 kOe in the negative direction, and the arithmetic mean value of the maximum magnetic polarization values ​​in the positive and negative directions is taken as the saturation magnetic flux density. The arithmetic mean value of the measured values ​​of the VSM samples taken from the six locations is taken as the saturation magnetic flux density of the Fe-based amorphous alloy and the Fe-based amorphous alloy ribbon.

[0030] 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 from 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.

[0031] Single-roll devices to which the single-roll method is applied include centrifugal quenching devices that use the inner wall of a drum, devices that use an endless type belt, and improved versions of these devices that are equipped with auxiliary rolls or roll surface temperature control devices, as well as casting devices that can cast under reduced pressure, in vacuum, or in an inert gas.

[0032] 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.

[0033] Furthermore, the Fe-based amorphous alloy of this embodiment can be obtained in the form of a powder or wire, in addition to a ribbon. To obtain a powdered Fe-based amorphous alloy, a method can be used in which the molten alloy having the above-mentioned composition is dropped in droplets from a nozzle of a crucible filled with the molten alloy, and a gas or water flow is sprayed onto the droplets to rapidly solidify them. To obtain a wire-shaped Fe-based amorphous alloy, a method can be used in which the molten alloy or droplets of the molten alloy are sprayed at high speed from a nozzle of a crucible filled with the molten alloy having the above-mentioned composition onto a rotating roll or a liquid such as cooling water to rapidly solidify them.

[0034] By the above-mentioned method, it is possible to obtain an Fe-based amorphous alloy powder or an Fe-based amorphous alloy wire having excellent soft magnetic properties.

[0035] The Fe-based soft magnetic alloy powder and Fe-based amorphous alloy wire obtained as described above can be compacted using a mold or the like to form into 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.

[0036] 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, 0.05 to 0.60% of Mn and 0.010 to 0.40% of Sn are contained, and the Fe content is set to 78.00 to 86.00%, whereby the 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.

[0037] Next, an iron core made of an Fe-based amorphous alloy according to an embodiment of the present invention will be described.

[0038] As described above, the Fe-based amorphous alloy of this embodiment has iron loss W １３／５０ These properties make it suitable as a material for various iron cores.

[0039] 1A and 1B show a wound core, which is an example of the core of this embodiment, and FIG. 2 shows a stacked core, which is another example of the core of this embodiment.

[0040] The wound core 61 shown in Fig. 1A is formed into a toroidal core shape by spirally winding the Fe-based amorphous alloy ribbon according to this embodiment as is, or by slitting the Fe-based amorphous alloy ribbon to adjust its width. The wound core 61 shown in Fig. 1A has a substantially circular outer shape in a plan view. A hollow portion 62 is provided in the center. The stacking direction of the Fe-based amorphous alloy ribbon is from the inner periphery side, where the hollow portion 62 of the toroidal core is located, toward the outer periphery side.

[0041] 1A , the wound core 71 shown in FIG. 1B is formed by spirally winding the Fe-based amorphous alloy ribbon according to this embodiment, either directly or after slitting the Fe-based amorphous alloy ribbon to adjust its width, into a toroidal core shape. The wound core 71 shown in FIG. 1B has a substantially fan-shaped outer shape in a plan view. A hollow portion 72 is provided in the center. The stacking direction of the Fe-based amorphous alloy ribbon is from the inner periphery, where the hollow portion 72 of the toroidal core is located, toward the outer periphery.

[0042] The stacked core 81 shown in Fig. 2 is obtained by cutting or punching the Fe-based amorphous alloy ribbon according to this embodiment into a predetermined shape to form thin strips 83, and then stacking a plurality of the thin strips 83 to form a laminated core. The stacked core 81 shown in Fig. 2 has a substantially rectangular outer shape in a plan view. A hollow portion 82 is provided in the center. The stacking direction of the thin strips 83 is the vertical direction in the drawing of the laminated core.

[0043] 1A, 1B, and 2, an adhesive layer may be interposed between the Fe-based amorphous alloy ribbons or between the thin ribbon pieces. By providing an adhesive layer, the shape of the wound cores 61, 71 and the stacked core 81 is maintained, and the strength of each core 61, 71, and 81 itself is improved. Furthermore, by providing an adhesive layer, insulation between the Fe-based amorphous alloy ribbons or thin ribbon pieces is ensured, and the iron loss W of the cores 61, 71, and 81 is reduced. １３／５０There are no particular limitations on the material of the adhesive layer, and acrylic resins, epoxy resins, compositions containing acrylic resins and epoxy resins, natural varnishes, synthetic varnishes, etc. may be used.

[0044] Furthermore, the wound cores 61, 71 and stacked core 81 according to this embodiment may be subjected to stress relief annealing. The wound cores 61, 71 and stacked core 81 that have been subjected to stress relief annealing have iron loss W １３／５０ The stress relief annealing may be performed while applying a magnetic field. In the wound cores 61, 71 and stacked core 81 that have been subjected to stress relief annealing, the surfaces of the Fe-based amorphous alloy ribbons or ribbon pieces 83 are discolored, so whether or not stress relief annealing has been performed can be determined by the presence or absence of discoloration.

[0045] The iron core according to this embodiment can be suitably used as an iron core for a power transformer or a high-frequency transformer.

[0046] The iron core according to this embodiment is not limited to one made from the Fe-based amorphous alloy ribbon as described above, but may be one made from Fe-based amorphous alloy powder or Fe-based amorphous alloy wire.

[0047] Examples of the present invention will be described below.

[0048] Example 1 An alloy prepared to have the compositions shown in Tables 1A and 1B was melted in an argon atmosphere, quenched in a single-roll apparatus, and cast to produce a ribbon of an Fe-based amorphous alloy. 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 sample melting, 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 resulting ribbon was 25 μm, the width was 10 mm (depending on the length of the slot nozzle), and the length was approximately 100 m.

[0049] The chemical compositions of the obtained Fe-based amorphous alloy ribbons were measured by the above-mentioned method. The results are shown in Tables 1A and 1B. The "Fe (atomic %)" in Tables 1A and 1B includes the content of impurities. The content of impurities in Inventive Examples 1 to 20 and Comparative Examples 1 to 12 was so small that it was not possible to express it as a significant digit.

[0050] 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 Cu-Kα (wavelength λ = 1.5406 Å), the length limiting slit was 2 mm, the scan speed was 2 deg / min, the step width was 0.02 deg, the scan range was 2θ = 5 deg or more and 100 deg or less, and the measurement method was the θ-2θ method. Regarding the X-ray source, the X-ray diffraction peak from CuKα ray was separated into Kα1 ray and Kα2 ray, and the intensity data after removing the Kα2 ray was evaluated. From the shape of the X-ray diffraction pattern, it was determined whether or not a crystalline phase had formed in the metal structure. Specifically, it was confirmed that there was no peak with a half-width (full width at half maximum) of 4° or less of the (110) diffraction peak of α-Fe.

[0051] In addition, the iron loss W of the Fe-based amorphous alloy ribbon １３／５０ was measured using a single sheet tester (SST). The iron loss measurement conditions were set to 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 ribbon coil. The samples for iron loss measurement were ribbon samples cut to a length of 120 mm. The width of the ribbon sample was the same as the width of the ribbon. These ribbon samples for iron loss measurement were annealed in a magnetic field (magnetic field: 800 A / m, applied in the casting direction) for 1 hour at a predetermined temperature selected from the range of 320 to 380°C, and then used for measurement. The atmosphere during annealing was a nitrogen atmosphere.

[0052] On the other hand, the saturation magnetic flux density was measured using a VSM (vibrating sample magnetometer). The samples for the VSM were thin pieces taken from the width center of each of the six ribbon samples. The VSM sample size was 5 mm square and was taken from the width center of the ribbon sample. The measurement conditions were as follows: the ribbon was excited to a maximum magnetizing force of 10 kOe in the positive direction, and then excited to a maximum magnetizing force of 10 kOe in the negative direction, and the arithmetic average of the maximum magnetic polarization values ​​in the positive and negative directions was taken as the saturation magnetic flux density.

[0053] Saturation magnetic flux density and iron loss W １３／５０ The measurement results are shown in Tables 1A and 1B as the arithmetic mean values ​​of the data at six points.

[0054]

[0055]

[0056] As shown in Table 1A, in all of Inventive Examples 1 to 20, 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 (W １３／５０ ) was 0.100 W / kg or less, and high saturation magnetic flux density and low core loss could be achieved simultaneously.

[0057] On the other hand, as shown in Table 1B, in Comparative Examples 1 to 12, the alloy compositions did not satisfy the range of the present invention, and therefore the iron loss (W １３／５０ ) exceeded 0.100 W / kg or the saturation magnetic flux density became less than 1.60 T.

[0058] That is, in Comparative Example 1, the Fe content was less than 78.00%, and the saturation magnetic flux density was less than 1.60 T. In Comparative Example 2, the Fe content was more than 86.00%, and the iron loss (W １３／５０ In Comparative Example 3, the B content exceeded 18.0%, and the iron loss (W １３／５０ In Comparative Example 4, the B content was less than 8.0%, and the iron loss (W １３／５０ In Comparative Example 5, the Si content was less than 0.10%, and the iron loss (W １３／５０ In Comparative Example 6, the Si content exceeded 9.0%, and the iron loss (W １３／５０In Comparative Example 7, the C content was less than 0.10%, and the iron loss (W １３／５０ In Comparative Example 8, the C content was more than 5.0%, and the iron loss (W １３／５０ In Comparative Example 9, the Mn content was less than 0.05%, and the iron loss (W １３／５０ In Comparative Example 10, the Mn content exceeded 0.60%, and the iron loss (W １３／５０ In Comparative Example 11, the Sn content was less than 0.010%, and the iron loss (W １３／５０ In Comparative Example 12, the Sn content exceeded 0.40%, and the iron loss (W １３／５０ ) exceeded 0.100 W / kg.

[0059] 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 20 and Comparative Examples 1 to 12, so it cannot be said that a crystalline phase was generated in the metal structure, and the entire structure was an amorphous phase.

[0060] (Example 2) For the alloy shown in Example 19 of the present invention in Table 1A, alloys of various compositions in which part of the Fe was replaced with at least one of Ni, Cr, and Co were used, and ribbons were cast 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 ribbon were about 25 μm, 10 mm, and approximately 100 m, respectively. The saturation magnetic flux density and iron loss W of the obtained ribbon were １３／５０ The sample collection method and measurement conditions used for these characteristic evaluations were the same as those in Example 1. The measurement results are shown in Table 2. The indications in Table 2 are the same as those in Tables 1A and 1B.

[0061]

[0062] As is clear from the results of Examples 21 to 27 of the present invention in Table 2, even when a part of Fe is replaced with at least one of Ni, Cr, and Co in the range of 10.00 atomic % or less, the saturation magnetic flux density is 1.60 T or more, and the iron loss W １３／５０Furthermore, no clear diffraction peaks were observed in the X-ray diffraction measurements of any of the samples, confirming that they were amorphous.

[0063] As is clear from the above examples, according to the Fe-based amorphous alloy and Fe-based amorphous alloy ribbon of the present invention, by optimizing the contents of B, Si, and C, containing 0.05 to 0.60% of Mn and 0.010 to 0.40% of Sn, and further setting the Fe content to 78.00 to 86.00%, it is possible to obtain an iron loss (W １３／５０ ) was 0.100 W / kg or less, the saturation magnetic flux density was 1.60 T or more, and it was found that excellent soft magnetic properties could be exhibited, making it suitable for use in the iron cores of power transformers and high-frequency transformers.

[0064] INDUSTRIAL APPLICABILITY The present invention provides an Fe-based amorphous alloy, an Fe-based amorphous alloy ribbon, and an iron core that have low iron loss and high magnetic flux density, and therefore has industrial applicability.

[0065] 61, 71... Wound core (iron core) 81... Stacked core (iron core)

Claims

1. In atomic percent, B: 8.0% or more and 18.0% or less, Si: 0.10% or more and 9.0% or less, C: 0.10% or more and 5.0% or less, Mn: 0.05% or more and 0.60% or less, Sn: 0.010% or more and less than 0.20% Fe: Contains 78.000% to 86.000% The remainder consists of impurities. An amorphous Fe alloy with an amorphous structure.

2. In atomic percent, Mn: 0.10% or more and 0.40% or less. The Fe-based amorphous alloy according to claim 1.

3. In atomic percent, Si: 0.10% or more and less than 6.0% The Fe-based amorphous alloy according to claim 1.

4. The Fe-based amorphous alloy according to claim 1, wherein Fe is substituted with at least one element from Ni, Cr, and Co in an amount of 10,000 atomic percent or less.

5. Iron 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 claim 1, wherein the power is 0.100 W / kg or less and the saturation magnetic flux density is 1.60 T or more.

6. A thin strip of Fe-based amorphous alloy, comprising the Fe-based amorphous alloy described in any one of claims 1 to 5.

7. An iron core made of an Fe-based amorphous alloy as described in any one of claims 1 to 5.