Fe-based amorphous alloys, Fe-based amorphous alloy strips, and iron cores

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

[Technical Field]

[0001] The present invention relates to Fe-based amorphous alloys, Fe-based amorphous alloy strips, and iron cores, and more particularly to Fe-based amorphous alloys, Fe-based amorphous alloy strips, and iron cores that exhibit excellent soft magnetic properties. This application claims priority based on Japanese Patent Application No. 2024-098236, filed in Japan on June 18, 2024, and the contents of that application are incorporated herein by reference. [Background technology]

[0002] Methods for continuously producing thin strips and wires by rapidly cooling alloys from a molten state include centrifugal quenching, single-roll method, and double-roll method. These methods involve rapidly solidifying molten metal by ejecting it from an orifice or the like onto the inner or outer surface of a rapidly rotating metal drum, thereby producing thin strips and wires. Furthermore, by appropriately selecting the alloy composition, amorphous alloys similar to liquid metals can be obtained, enabling the production of materials with excellent magnetic or mechanical properties.

[0003] In particular, among amorphous alloys, Fe-based amorphous alloys are considered promising materials for the cores of power transformers and high-frequency transformers. To improve the performance of these materials, there is a strong demand for further reduction of iron loss and further improvement of saturation magnetic flux density in Fe-based amorphous alloys. For example, Fe-based amorphous alloys are described in Patent Documents 1-4. [Prior art documents] [Patent Documents]

[0004] [Patent Document 1] Japanese Patent Publication No. 5-140703 [Patent Document 2] Japanese Patent Publication No. 5-98402 [Patent Document 3] Japanese Patent Application Publication No. 2012-21190 [Patent Document 4] International Publication No. 2015 / 016161

Summary of the Invention

Problems to be Solved by the Invention

[0005] The present invention has been made in view of the above circumstances, and an object thereof is to provide an Fe-based amorphous alloy, an Fe-based amorphous alloy ribbon, and a core having low iron loss and a high magnetic flux density.

Means for Solving the Problems

[0006] The Fe-based amorphous alloy of the present invention contains, in atomic%, B: 8.0% or more and 18.0% or less, Si: 0.1% or more and 9.0% or less, [[ID=​​​​​​​​​​​​​​​​​​​​​​​​​​​​​​​​​​​​​​​

[0009] The inventors have found that by adjusting the content 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 including Mn in a range of 0.05% to 0.60% and Sn in a range of 0.010 to 0.40%, excellent soft magnetic properties can be obtained while further improving amorphous-forming ability. Specifically, iron loss W 13 / 50 We found that it is 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] The following describes embodiments of the present invention, namely Fe-based amorphous alloys and Fe-based amorphous alloy strips.

[0011] In this embodiment, excellent soft magnetic properties refer to iron loss W 13 / 50 This refers to a characteristic where the magnetic field density is low and the saturation magnetic flux density is high.

[0012] The Fe-based amorphous alloy of this embodiment contains, in atomic percent, 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] Furthermore, the Fe-based amorphous alloy of this embodiment may have a Mn content in the range of 0.10% to 0.40%. Furthermore, the Fe-based amorphous alloy of this embodiment may have a Sn content in the range of 0.010% to 0.20%. Furthermore, the Fe-based amorphous alloy of this embodiment may have a Si content in the range of 0.10% or more and less than 6.0%. Furthermore, the Fe-based amorphous alloy of this embodiment may be modified by substituting Fe with at least one element from Ni, Cr, and Co in an amount of 10,000 atomic percent or less.

[0014] The Fe-based amorphous alloy thin strip of this embodiment may be made of the above-mentioned Fe-based amorphous alloy. The core of this embodiment may be composed of the above-mentioned Fe-based amorphous alloy, Fe-based amorphous alloy strip, Fe-based amorphous alloy powder, or Fe-based amorphous alloy wire.

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

[0016] In this embodiment, element B is included in the Fe-based amorphous alloy to improve amorphous phase formation and the thermal stability of the amorphous phase. Assuming that other elements are included within the above-mentioned composition range, optimizing the content of this element makes it possible to stably form an amorphous phase in the alloy structure and further improve the soft magnetic properties. For example, iron loss W 13 / 50 The iron loss can be stably reduced to 0.100 W / kg or less. If B is less than 8.0 atomic%, improvement in amorphous phase formation ability cannot be obtained, and amorphous alloys cannot be stably obtained in Fe-based amorphous alloys, and the iron loss W cannot be stably reduced while maintaining a saturation magnetic flux density of 1.60 T or more. 13 / 50 It becomes difficult to stably maintain the iron loss W below 0.100 W / kg. On the other hand, even if B exceeds 18.0 atomic%, no improvement in amorphous phase formation ability is obtained, and iron loss W is difficult to maintain while stably maintaining the saturation magnetic flux density above 1.60 T. 13 / 50 It becomes difficult to stably maintain the concentration at 0.100 W / kg or less. Therefore, B is set to 8.0 atomic% or more and 18.0 atomic% or less. Preferably, B is set to 10.0 atomic% or more or 11.0 atomic% or more. Also preferably, B is set to 15.0 atomic% or less or 14.0 atomic% or less.

[0017] Si and C are also 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. On the premise that other elements are included in the above composition ranges, by optimizing the contents of Si and C, 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 0.10 atomic % and C is less than 0.10 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. As a result, while maintaining the saturation magnetic flux density stably at 1.60 T or more, it becomes difficult to maintain the iron loss W 13 / 50 stably at 0.100 W / kg or less. On the other hand, even when Si exceeds 9.0 atomic % and C exceeds 5.0 atomic %, the ability to form an amorphous phase cannot be improved, and it becomes difficult to make the iron loss W 13 / 50 stably 0.100 W / kg or less. Therefore, Si is set to 0.10 atomic % or more and 9.0 atomic % or less, and C is set to 0.10 atomic % or more and 5.0 atomic % or less. Preferably, Si is 0.40 atomic % or more, 1.0 atomic % or more, or 3.0 atomic % or more. Also preferably, Si is 8.6 atomic % or less, 7.5 atomic % or less, less than 6.0 atomic %, or 5.5 atomic % or less. Also preferably, C is 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 preferably, C is 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 the present embodiment in order to improve the soft magnetic properties. On the premise that other elements are included in the above composition ranges, by optimizing the content of Mn, it becomes possible to stably make the iron loss W 13 / 50 0.100 W / kg or less. When Mn is less than 0.05 atomic %, while maintaining the saturation magnetic flux density stably at 1.60 T or more, it becomes difficult to maintain the iron loss W 13 / 50 stably at 0.100 W / kg or less. On the other hand, when Mn exceeds 0.60 atomic %, the iron loss W 13 / 50It becomes difficult to stably maintain the concentration 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 0.10 atomic% or more or 0.15 atomic% or more. Also, the Mn content is set to 0.50 atomic% or less, 0.40 atomic% or less, or 0.30 atomic% or less.

[0019] In this embodiment, Sn is included in the Fe-based amorphous alloy to improve amorphous phase formation and the thermal stability of the amorphous phase. Assuming that other elements are included within the above-mentioned composition range, optimizing the content of this element makes it possible to stably form an amorphous phase in the alloy structure and further improve the soft magnetic properties. Specifically, for example, when manufacturing a thin strip made of Fe-based amorphous alloy by the single-roll method, there is a slight concern that a crystalline phase may form on the free surface of the strip, which is the surface that does not come into contact with the roll, because the cooling rate is slightly lower than on the surface that comes into contact with the roll. However, by including Sn, the ability to form an amorphous phase can be further enhanced, thereby making the entire thin strip stably amorphous and suppressing the deterioration of soft magnetic properties. Specifically, it is possible to stably maintain the saturation magnetic flux density at 1.60 T or higher while stably reducing the iron loss to 0.100 W / kg or less. When the Sn content is less than 0.010 atomic%, improvement in amorphous phase formation ability cannot be obtained, and amorphous alloys cannot be stably obtained in Fe-based amorphous alloys. As a result, iron loss W cannot be maintained while stably maintaining the saturation magnetic flux density at 1.60 T or higher. 13 / 50 It becomes difficult to stably maintain the iron loss below 0.100 W / kg. On the other hand, even if Sn exceeds 0.40 atomic%, no improvement in amorphous phase formation ability is obtained, and iron loss W is not maintained while stably maintaining the saturation magnetic flux density above 1.60 T. 13 / 50 It is difficult to maintain a stable level of 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 0.050 atomic% or more, 0.070 atomic% or more, or 0.10 atomic% or more. Also preferably, the Sn content is 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, a Fe content of 70,000 atomic percent or more is usually sufficient to obtain a practical saturation magnetic flux density for a typical iron core. However, to obtain a high saturation magnetic flux density of 1.60 T or more, assuming that other elements are included within the aforementioned composition range, the Fe content needs to be 78,000 atomic percent or more. On the other hand, if the Fe content exceeds 86,000 atomic percent, the formation of the amorphous phase becomes difficult, and the good soft magnetic properties (iron loss W) characteristic of amorphous alloys are lost. 13 / 50 It becomes difficult to stably obtain a strength of 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. A more preferable Fe content is 79.000 atomic% or more or 80.000 atomic% or more. A more preferable Fe content is 84.000 atomic% or less or 83.000 atomic% or less.

[0021] In the Fe-based amorphous alloy of this embodiment, iron loss W is reduced while maintaining a high saturation magnetic flux density by substituting a portion of Fe with at least one of Ni, Cr, and Co in a range of 10,000 atomic percent or less. 13 / 50 Improvements in soft magnetic properties such as these can also be achieved. An upper limit has been set on the amount of substitution by these elements because exceeding 10,000 atomic percent results in a lower saturation magnetic flux density and increased raw material costs. When Fe is substituted with one or more of Ni, Cr, and Co, the total content of Ni, Cr, Co and Fe must be between 78,000 atomic percent and 86,000 atomic percent, or it may be between 79,000 atomic percent and 80,000 atomic percent, or it may be between 84,000 atomic percent and 83,000 atomic percent.

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

[0023] The remainder of the Fe-based amorphous alloy according to this embodiment is impurities. 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 percent, for example, when a steel material is used as the Fe source. For example, it may contain S, N, O, Al, Ti, etc., in a total amount of less than 0.150 atomic percent, 0.100 atomic percent or less, 0.050 atomic percent or less, or 0.010 atomic percent or less as impurities. In addition, it may contain P as an impurity in a range of less than 0.070 atomic percent, 0.050 atomic percent or less, or 0.010 atomic percent or less.

[0024] The chemical composition of the Fe-based amorphous alloy in this embodiment can be measured by general analytical methods. For example, the chemical composition can be measured using ICP-AES (Inductively Coupled Plasma-Atomic Emission Spectrometry). Specifically, the chemical composition is determined by measuring a test specimen taken from the Fe-based amorphous alloy using a predetermined measuring device under conditions based on a calibration curve prepared in advance. C and S can be measured using the combustion-infrared absorption method, N can be measured using the inert gas fusion-thermal conductivity method, and O can be measured using the inert gas fusion-nondispersive infrared absorption method.

[0025] The Fe-based amorphous alloy of this embodiment has an amorphous structure. This provides excellent soft magnetic properties. Whether or not it has an amorphous structure 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 peaks are 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 peaks are obtained in the X-ray diffraction measurement" means that there are no peaks with a full width at half maximum (FMAX) of 4° or less for the (110) diffraction peak of α-Fe.

[0026] In this embodiment, the measurement conditions for X-ray diffraction are as follows: the X-ray source is Cu-Kα (wavelength λ = 1.5406 Å), the longitudinal limiting slit is 2 mm, the scan speed is 2 deg / min, the step size is 0.02 deg, the 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 Fe-based amorphous alloy thin strip of this embodiment are subjected to the following methods to achieve saturation magnetic flux density and iron loss W 13 / 50 When measured, the saturation magnetic flux density is 1.60T or higher, the magnetic flux density is 1.3T, and the iron loss (W) at a frequency of 50Hz is 13 / 50 The power-to-weight ratio becomes 0.100 W / kg or less, resulting in excellent soft magnetic properties.

[0028] Iron loss W 13 / 50 The measurement is performed using an SST (Single Sheet Tester). The iron loss measurement conditions are set to a magnetic flux density of 1.3T and a frequency of 50Hz. Samples for iron loss measurement are taken from six locations along the entire length of one thin strip coil. Thin strip samples cut to a length of 120mm are used for iron loss measurement. The width of the thin strip sample is the same as the width of the thin strip. These thin strip samples for iron loss measurement are subjected to measurement by aneury in a magnetic field (magnetic field: 800A / m, applied in the casting direction) for 1 hour at a predetermined temperature selected from the range of 320 to 380°C. The atmosphere during aneury is a nitrogen atmosphere. The arithmetic mean of the measured values ​​of the iron loss samples taken from the six locations is used as the iron loss (W) of the Fe-based amorphous alloy and Fe-based amorphous alloy thin strip. 13 / 50 )

[0029] On the other hand, the saturation magnetic flux density is measured using a VSM (vibrating sample magnetometer). For the VSM device, thin strips taken from the center of the width of each of the six thin strip samples are used. The VSM sample size is 5 mm square, and it is taken from the center of the width of the thin strip sample. The measurement conditions are to excite the positive side to a maximum magnetization force of 10 kOe, and then to a maximum magnetization force of 10 kOe on the negative side, and the arithmetic mean of the maximum magnetic polarization values ​​on the positive and negative sides is taken as the saturation magnetic flux density. The arithmetic mean 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 thin strip.

[0030] The following describes the manufacturing method of the Fe-based amorphous alloy and Fe-based amorphous alloy strip according to this embodiment. The Fe-based amorphous alloy according to this embodiment can usually be obtained in the form of a strip. This Fe-based amorphous alloy strip can be manufactured by a method in which an alloy consisting of the components described in the above embodiment is melted, the molten metal is ejected from a slot nozzle or the like onto a cooling plate moving at high speed, and the molten metal is rapidly cooled and solidified, for example, by the single-roll method or the double-roll method. The rolls used in these roll methods are made of metal, and rapid cooling and solidification of the alloy is possible by rotating the rolls at high speed and causing the molten metal to collide with the roll surface or inner surface of the roll.

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

[0032] In this embodiment, the dimensions of the thin strip, such as its thickness and width, are not particularly limited, but the thickness of the thin strip is preferably, for example, 10 μm or more and 100 μm or less. The width is preferably 10 mm or more. As described above, the Fe-based amorphous alloy thin strip obtained can be used as a material for the iron core in power transformers and high-frequency transformers.

[0033] Furthermore, the Fe-based amorphous alloy of this embodiment can be obtained not only in the form of a thin strip, but also in the form of a powder or wire. To obtain a powdered Fe-based amorphous alloy, a method can be employed in which the molten alloy of the above composition is dropped in droplet form from a nozzle of a crucible filled with the molten alloy, and a gas stream or water stream is blown onto the droplets to rapidly cool and solidify them. To obtain a wire-shaped Fe-based amorphous alloy, a method can be employed in which the molten alloy or droplets of the molten alloy are ejected at high speed from a nozzle of a crucible filled with the molten alloy of the above composition into a rotating roll or a liquid such as cooling water, and then rapidly cooled and solidified.

[0034] By the method described above, Fe-based amorphous alloy powder or Fe-based amorphous alloy wire with excellent soft magnetic properties can be obtained.

[0035] As described above, the Fe-based soft magnetic alloy powder and Fe-based amorphous alloy wire obtained can be compacted into the desired shape using a mold or the like, and then sintered and integrated as needed, making them suitable for applications such as power transformers, high-frequency transformers, and coil cores.

[0036] As described above, the Fe-based amorphous alloy and Fe-based amorphous alloy thin strip of this embodiment optimize the content of B, Si, and C, incorporating 0.05-0.60% Mn and 0.010-0.40% Sn, and further increasing the Fe content to 78.00-86.00%, thereby reducing iron loss (W) at a magnetic flux density of 1.3T and a frequency of 50Hz. 13 / 50 The magnetic flux density (W / kg) becomes 0.100 W / kg or less, and the saturation magnetic flux density becomes 1.60 T or more, exhibiting excellent soft magnetic properties, making it suitable for use in the cores of power transformers and high-frequency transformers.

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

[0038] As described above, the Fe-based amorphous alloy of this embodiment has iron loss W 13 / 50 It has a low magnetic flux density and a high saturation magnetic flux density. These characteristics make it suitable as a material for various iron cores.

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

[0040] The wound core 61 shown in Figure 1A is formed by winding a thin strip of Fe-based amorphous alloy, either as is or after slitting to adjust its width, in a spiral pattern to create a toroidal core. The wound core 61 shown in Figure 1A has an outer shape that is approximately circular when viewed from above. A cavity 62 is provided in the center. The stacking direction of the Fe-based amorphous alloy strips is from the inner circumference side where the cavity 62 of the toroidal core is located towards the outer circumference side.

[0041] The wound core 71 shown in Figure 1B, similar to the case in Figure 1A, is formed by winding a thin strip of Fe-based amorphous alloy, either as is or after slitting to adjust its width, in a spiral pattern to create a toroidal core. The wound core 71 shown in Figure 1B has a roughly fan-shaped outer form when viewed from above. A cavity 72 is provided in the center. The stacking direction of the Fe-based amorphous alloy strips is from the inner circumference side where the cavity 72 of the toroidal core is located towards the outer circumference side.

[0042] The laminated core 81 shown in Figure 2 is formed by cutting or punching out thin strips of Fe-based amorphous alloy in a predetermined shape to create thin strip pieces 83 of a predetermined shape, and then stacking multiple thin strip pieces 83 to form a laminated core. The laminated core 81 shown in Figure 2 has an outer shape that is approximately rectangular when viewed from above. A cavity 82 is provided in the center. The stacking direction of the thin strip pieces 83 is the vertical direction in the figure of the laminated core.

[0043] The wound cores 61, 71 and stacked core 81 shown in Figures 1A, 1B, and 2 may all have an adhesive layer interposed between the Fe-based amorphous alloy strips or between the strip pieces. By providing the adhesive layer, the shape of the wound cores 61, 71 and stacked core 81 is maintained, and the strength of each core 61, 71, and 81 is improved. In addition, by providing the adhesive layer, insulation between the Fe-based amorphous alloy strips or strip pieces is ensured, and the iron loss W of the cores 61, 71, and 81 is reduced.13 / 50 This can improve performance. There are no particular restrictions on the material of the adhesive layer; acrylic resins, epoxy resins, compositions containing acrylic and epoxy resins, natural varnishes, or synthetic varnishes are all applicable.

[0044] Furthermore, the wound cores 61, 71 and stacked core 81 according to this embodiment may be subjected to stress-relieving annealing. The wound cores 61, 71 and stacked core 81 that have undergone stress-relieving annealing have iron loss W 13 / 50 This is significantly improved. Furthermore, strain relief annealing may be performed while applying a magnetic field. Note that when strain relief annealing is performed on wound cores 61, 71 and laminated core 81, the surface of the Fe-based amorphous alloy thin strip or thin strip 83 will change color, so whether or not strain 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 power transformers, high-frequency transformers, and the like.

[0046] Furthermore, the iron core according to this embodiment is not limited to one made from a thin strip of Fe-based amorphous alloy as described above, but may also be made from powder of Fe-based amorphous alloy or from wire of Fe-based amorphous alloy. [Examples]

[0047] The following describes embodiments of the present invention.

[0048] (Example 1) Thin strips of Fe-based amorphous alloy were fabricated by melting alloys, adjusted to the components shown in Tables 1A and 1B, in an argon atmosphere and rapidly cooling them in a single-roll apparatus for casting. The casting atmosphere was air. The single-roll apparatus used consisted of a 300 mm diameter copper alloy cooling roll, a high-frequency power supply for sample melting, and a quartz crucible with a slot nozzle at 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 set to 24 m / sec. As a result, the thickness of the obtained thin strip 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 composition of the obtained Fe-based amorphous alloy thin strips was measured by the method described above. The results are shown in Tables 1A and 1B. The "Fe (atomic %)" in Tables 1A and 1B includes the impurity content. The impurity content in Invention Examples 1-20 and Comparative Examples 1-12 was so small that it could not be expressed as a significant figure.

[0050] X-ray diffraction measurements were performed on the obtained Fe-based amorphous alloy thin strips to obtain X-ray diffraction patterns. The X-ray source for the X-ray diffraction measurements was Cu-Kα (wavelength λ = 1.5406 Å), the longitudinal limiting slit was 2 mm, the scan speed was 2 deg / min, the step size was 0.02 deg, the scan range was 2θ = 5 deg to 100 deg, and the measurement method was the θ-2θ method. Regarding the X-ray source, the X-ray diffraction peaks from the CuKα line were separated into Kα1 and Kα2 lines, and the intensity data after removing the Kα2 line was evaluated. From the shape of the X-ray diffraction pattern, it was determined whether or not a crystalline phase was formed in the metal structure. Specifically, it was confirmed that there were no peaks with a full width at half maximum (FMAX) of 4° or less for the (110) diffraction peak of α-Fe.

[0051] Furthermore, iron loss W of Fe-based amorphous alloy thin strips 13 / 50The iron loss was measured using an SST (Single Sheet Tester). The measurement conditions for iron loss were set to a magnetic flux density of 1.3T and a frequency of 50Hz. Samples for iron loss measurement were taken from six locations along the entire length of one thin strip coil. Thin strip samples cut to a length of 120mm were used for iron loss measurement. The width of the thin strip sample was the same as the width of the thin strip. These thin strip samples for iron loss measurement were subjected to aneury in a magnetic field (magnetic field: 800A / m, applied in the casting direction) for 1 hour at a predetermined temperature selected from the range of 320 to 380°C for measurement. The atmosphere during aneury was a nitrogen atmosphere.

[0052] On the other hand, the saturation magnetic flux density was measured using a VSM (vibrating sample magnetometer). For the VSM, thin strips were taken from the center of the width of each of the thin strip samples from the six locations mentioned above. The VSM sample size was 5 mm square, and it was taken from the center of the width of the thin strip sample. The measurement conditions were to excite the positive side to a maximum magnetization force of 10 kOe, and then excite the negative side to a maximum magnetization force of 10 kOe, and the arithmetic mean of the maximum magnetic polarization values ​​on the positive and negative sides was taken as the saturation magnetic flux density.

[0053] Saturated magnetic flux density and iron loss W 13 / 50 The measurement results were calculated as the arithmetic mean of the data from the six locations and are shown in Tables 1A and 1B.

[0054] [Table 1A]

[0055] [Table 1B]

[0056] As shown in Table 1A, in all of the Examples 1 to 20 of the present invention, the alloy composition met the range of the present invention, resulting in a saturation magnetic flux density of 1.60 T or higher, and an iron loss (W) at a magnetic flux density of 1.3 T and a frequency of 50 Hz. 13 / 50 The saturation magnetic flux density (SMF) was reduced to 0.100 W / kg or less, allowing for both high SMF and low iron loss to be achieved simultaneously.

[0057] On the other hand, as shown in Table 1B, Comparative Examples 1 to 12 all failed to satisfy the range of the present invention in terms of alloy composition, resulting in iron loss (W 13 / 50 The power output exceeds 0.100 W / kg, or the saturation magnetic flux density falls below 1.60 T.

[0058] In other words, in Comparative Example 1, the Fe content was less than 78.00%, and the saturation magnetic flux density was less than 1.60 T. Comparative Example 2 had an Fe content of over 86.00%, and iron loss (W 13 / 50 The power consumption exceeded 0.100 W / kg. Comparative Example 3 shows that the amount of B exceeds 18.0%, and iron loss (W 13 / 50 The power consumption exceeded 0.100 W / kg. Comparative Example 4 had a B content of less than 8.0%, and iron loss (W 13 / 50 The power consumption exceeded 0.100 W / kg. Comparative Example 5 has a Si content of less than 0.10%, and iron loss (W 13 / 50 The power consumption exceeded 0.100 W / kg. Comparative Example 6 had a Si content exceeding 9.0%, and iron loss (W 13 / 50 The power consumption exceeded 0.100 W / kg. Comparative Example 7 has a C content of less than 0.10%, and iron loss (W 13 / 50 The power consumption exceeded 0.100 W / kg. Comparative Example 8 shows that the amount of C exceeds 5.0%, and iron loss (W 13 / 50 The power consumption exceeded 0.100 W / kg. Comparative Example 9 has a Mn content of less than 0.05%, and iron loss (W 13 / 50 The power consumption exceeded 0.100 W / kg. Comparative Example 10 had a Mn content exceeding 0.60%, and iron loss (W 13 / 50 The power consumption exceeded 0.100 W / kg. Comparative Example 11 had a Sn content of less than 0.010%, and iron loss (W 13 / 50 The power consumption exceeded 0.100 W / kg. Comparative Example 12 had a Sn content exceeding 0.40%, and iron loss (W 13 / 50 The power consumption exceeded 0.100 W / kg.

[0059] Furthermore, when X-ray diffraction measurements were performed on Fe-based amorphous alloy thin strips, no clear diffraction peaks were observed in Examples 1-20 of the present invention and Comparative Examples 1-12. Therefore, it cannot be said that a crystalline phase was formed in the metal structure, and the entire structure was amorphous.

[0060] (Example 2) Thin strips were cast using the same apparatus and conditions as in Example 1, with respect to the alloys shown in Example 19 of the present invention in Table 1A, in which a portion of Fe was replaced with at least one of Ni, Cr, or Co. The specific components of the alloys used are shown in Table 2. As a result, the thickness, width, and length of the obtained thin strips were approximately 25 μm, 10 mm, and approximately 100 m, respectively. The saturation magnetic flux density and iron loss W of the obtained thin strips were determined. 13 / 50 The following was evaluated. The sampling method and measurement conditions used for these characteristic evaluations were the same as in Example 1. The measurement results are shown in Table 2. The display procedure in Table 2 is the same as in Tables 1A and 1B.

[0061] [Table 2]

[0062] As is clear from the results of Examples 21-27 in Table 2, even if a portion of Fe is replaced with at least one of Ni, Cr, or Co in a range of 10.00 atomic% or less, the saturation magnetic flux density is 1.60 T or higher, and the iron loss W 13 / 50 It was found that the concentration could be stably maintained at 0.100 W / kg or less. Furthermore, no clear diffraction peaks were observed in any of the samples during X-ray diffraction measurements, confirming that they were amorphous.

[0063] As is clear from the above examples, the Fe-based amorphous alloy and Fe-based amorphous alloy thin strip of the present invention optimize the content of B, Si, and C, incorporating 0.05-0.60% Mn and 0.010-0.40% Sn, and further increasing the Fe content to 78.00-86.00%, thereby reducing iron loss (W) at a magnetic flux density of 1.3T and a frequency of 50Hz. 13 / 50The magnetic flux density (W / kg) becomes 0.100 W / kg or less, and the saturation magnetic flux density becomes 1.60 T or higher, exhibiting excellent soft magnetic properties, and it was found to be suitable for use in the cores of power transformers and high-frequency transformers. [Industrial applicability]

[0064] The present invention provides an Fe-based amorphous alloy, a Fe-based amorphous alloy strip, and an iron core that have low iron loss and high magnetic flux density, and therefore has industrial applicability. [Explanation of symbols]

[0065] 61, 71... Rolled Iron Core (Iron Core) 81... Sekitetsushin (Tetsushin)

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. The tissue is amorphous, The surface is smooth, An Fe-based amorphous alloy having an iron loss W 13 / 50 of 0.100 W / kg or less and a saturation magnetic flux density of 1.60 T or more when magnetized at a frequency of 50 Hz and a magnetic flux density of 1.3 T.

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. A thin strip of Fe-based amorphous alloy, comprising the Fe-based amorphous alloy described in any one of claims 1 to 4.

6. An iron core made of an Fe-based amorphous alloy as described in any one of claims 1 to 4.

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