Patent Application
20210156011
The present invention relates to a soft magnetic alloy ribbon and a magnetic component.
As one form of a soft magnetic material, a soft magnetic alloy material is known. Further, a magnetic core using a soft magnetic alloy ribbon obtained by forming a soft magnetic alloy material into a ribbon shape is known. In order to reduce a size and improve properties of the magnetic core, it is required to improve magnetic properties (saturation magnetic flux density) of the soft magnetic alloy ribbon.
Patent Document 1 describes an invention related to an amorphous alloy ribbon, a nanocrystalline soft magnetic alloy, and the like. According to Patent Document 1, segregation of C generated on a surface of the ribbon can be controlled by controlling an amount of C in the ribbon and further controlling a gas atmosphere in a vicinity of a cooling roll.
Patent Document 2 describes an invention related to an amorphous alloy ribbon, a nanocrystalline soft magnetic alloy, and the like. According to Patent Document 2, segregation of Cu generated on a surface of the ribbon can be controlled by controlling a temperature of the ribbon on a roll during manufacturing the ribbon.
Patent Document 3 describes a soft magnetic alloy ribbon that has a base phase in which fine crystal grains having an average grain size of 60 nm or less are dispersed in an amorphous substance at a volume fraction of 50% or more, and that has an oxide film on a surface, in which a part of the oxide film has a B concentration lower than an average B concentration in the base phase.
[Patent Document 1] Japanese Patent Laid-Open No. 2007-182594
[Patent Document 2] Japanese Patent Laid-Open No. 2009-263775
[Patent Document 3] Japanese Patent Laid-Open No. 2011-149045
Generally, the soft magnetic alloy ribbon is manufactured by a super-rapid cooling method such as a single-roll method. In a case of mass production, the soft magnetic alloy ribbon is generally manufactured in an air atmosphere. Therefore, Fe in a vicinity of a surface of the soft magnetic alloy ribbon is oxidized, and a total amount of magnetic materials decreases. Patent Document 1 and Patent Document 2 do not describe the oxidation of Fe. Since the oxide film of the soft magnetic alloy ribbon in Patent Document 3 is thick, the total amount of magnetic materials is reduced.
An object of the present invention is to obtain a soft magnetic alloy ribbon having high corrosion resistance and good magnetic properties.
In order to achieve the above object, a soft magnetic alloy ribbon according to the present invention includes
Fe; and
M, in which
M is at least one selected from the group consisting of Nb, Ta, W, Zr, Hf, Mo, Cr, and Ti, and a part of M is included in oxides, and
a maximum point of a concentration of at least one of M included in the oxides is present in a region within 20 nm from the surface, when a concentration distribution of an element contained in the soft magnetic alloy ribbon is measured from a surface toward an interior of the soft magnetic alloy ribbon in a thickness direction.
The soft magnetic alloy ribbon according to the present invention has the above features, and thus becomes a soft magnetic alloy ribbon having high corrosion resistance and good magnetic properties.
The soft magnetic alloy ribbon according to the present invention may further include Si, in which
a part of Si may be included in oxides, and
The soft magnetic alloy ribbon according to the present invention, in which
[Si]/[M]≥1.50 is satisfied, when a concentration of M included in the oxides at the maximum point of the concentration of M is set as [M], and a concentration of Si included in the oxides at the maximum point of the concentration of Si is set as [Si].
The soft magnetic alloy ribbon according to the present invention may have a composition ratio of Si of 0.1 at % or more and 10 at % or less.
The soft magnetic alloy ribbon according to the present invention may have a composition ratio of M of more than 3 at % and 10 at % or less.
The soft magnetic alloy ribbon according to the present invention, in which amorphous may be observed in the ribbon.
The soft magnetic alloy ribbon according to the present invention, in which nanocrystals may be included in the ribbon.
A magnetic component according to the present invention includes the soft magnetic alloy ribbon described above.
Hereinafter, embodiments of the present invention are explained with the Figures.
A dimension of a soft magnetic alloy ribbon of the present embodiment is not particularly limited. For example, a thickness may be 5 μm to 30 μm and a width may be 5 mm to 250 mm.
The soft magnetic alloy ribbon of the present embodiment contains Fe and M. M is at least one selected from the group consisting of Nb, Ta, W, Zr, Hf, Mo, Ti, and Cr, and a part of M includes in oxides.
When concentration distributions of elements contained in the soft magnetic alloy ribbon are measured from a surface toward an interior of the soft magnetic alloy ribbon in a thickness direction, a maximum point of a concentration of at least one of M includes in oxides is present in a region within 20 nm from the surface.
When the maximum point of the concentration of at least one of M includes in oxides is present in the region within 20 nm from the surface, a layer including oxides of M segregates on the surface. As a result, oxidation of Fe can be prevented, and corrosion resistance of the soft magnetic alloy ribbon is improved. Further, magnetic properties are also improved.
The soft magnetic alloy ribbon of the present embodiment may further contain Si. When the concentration distributions of the elements contained in the soft magnetic alloy ribbon is measured from the surface toward the interior of the soft magnetic alloy ribbon in the thickness direction, a maximum point of a concentration of Si includes in oxides may be present in the region within 20 nm from the surface.
In fact,
As shown in
The concentration distribution is measured such that a distance between measurement points is 1.0 nm or more and 4.0 nm or less in terms of SiO2 in a region within 50 nm from the surface.
A method for confirming the maximum point of the concentration in the present embodiment will be described below. First, a concentration at each measurement point within a measurement range of the concentration distribution is confirmed. The measurement point having a concentration higher than that of any one of adjacent measurement points is the maximum point. When two or more adjacent measurement points have the same concentration, the two or more measurement points are regarded as a single measurement point group. When the concentration of the measurement point group is higher than the concentration of any measurement points adjacent to the measurement point group, the measurement point closest to the surface among the measurement point group is the maximum point.
When the concentration of M includes in oxides at the maximum point of the concentration of M includes in oxides is set as [M], and the concentration of Si includes in oxides at the maximum point of the concentration of Si includes in oxides is set as [Si], [Si]/[M]≥1.5 may be satisfied. When [Si]/[M]≥1.5 is satisfied, M and Si form a layer on the surface, thereby improving the corrosion resistance of the soft magnetic alloy ribbon. Further, magnetic properties are also improved. When there is a plurality of maximum points, the concentration of the maximum point closer to the surface among the plurality of maximum points is defined as [M] or [Si]. An upper limit of [Si]/[M] is not particularly limited, and for example, [Si]/[M]≤20 may be satisfied.
Specifically, a concentration of each element in the interior of the soft magnetic alloy ribbon is an average value of a concentration of each element in a portion 1.0 μm to 1.3 μm from the surface of the soft magnetic alloy ribbon. Generally, the concentration of each element in the interior of the soft magnetic alloy ribbon generally matches a composition ratio of each element in the entire soft magnetic alloy ribbon.
The composition ratio of Si in the soft magnetic alloy ribbon of the present embodiment is not particularly limited, and may be 0 at % or more and 18 at % or less, or 0 at % or more and 13.5 at % or less, or 0.1 at % or more and 10 at % or less. When the composition ratio of Si is 0.1 at % or more, the corrosion resistance is likely to be improved. When the composition ratio of Si is 0.1 at % or more and 10 at % or less, a saturation magnetic flux density is likely to be improved.
The composition ratio of M in the soft magnetic alloy ribbon of the present embodiment is not particularly limited, and the composition ratio of M may be 0.1 at % or more and 15 at % or less, or 3 at % or more and 12 at % or less, or more than 3 at % and 10 at % or less. In particular, when the composition ratio of M is more than 3 at % and 10 at % or less, the corrosion resistance is likely to be improved.
From the viewpoint of achieving both the saturation magnetic flux density and the corrosion resistance, the composition ratio of M may be 2 at % or more and 10 at % or less.
A microstructure of the soft magnetic alloy ribbon of the present embodiment is not particularly limited. For example, the soft magnetic alloy ribbon of the present embodiment may have a structure composed of only amorphous substances, and may have a nanohetero structure in which initial microcrystals are present in amorphous substances. An average grain size of the initial microcrystals may be 0.3 nm to 10 nm. In the present embodiment, it is assumed that when an amorphization ratio to be described later is 85% or more, the soft magnetic alloy ribbon has the structure formed of only amorphous substances or has the nanohetero structure.
The soft magnetic alloy ribbon of the present embodiment may have a structure formed of nanocrystals. In addition, among the structures formed of nanocrystals, a structure formed of Fe-based nanocrystals may be particularly provided.
The nanocrystal refers to a crystal in which a grain size is in a nano order. The Fe-based nanocrystal refers to a crystal in which a grain size is in a nano order and a crystal structure of Fe is bcc (body-centered cubic lattice structure). In the present embodiment, it is preferable to deposit Fe-based nanocrystals having an average grain size of 5 nm to 30 nm. A soft magnetic alloy ribbon 24 in which such Fe-based nanocrystals are deposited is likely to have a high saturation magnetic flux density and is likely to have a low coercive force. In the present embodiment, when the soft magnetic alloy ribbon has a structure containing nanocrystals and a structure containing Fe-based nanocrystals, the amorphization ratio to be described later is less than 85%.
Hereinafter, a method for confirming whether the soft magnetic alloy ribbon has a structure formed of amorphous substances (a structure composed of only amorphous substances or a nanohetero structure) or a structure formed of crystals is described. In the present embodiment, the soft magnetic alloy ribbon having an amorphization ratio X of 85% or more shown in the following Equation (1) has the structure formed of amorphous substances, and the soft magnetic alloy ribbon having an amorphization ratio X of less than 85% has the structure formed of crystals.
X=100−(Ic/(Ic+Ia)×100) (1)
Ic: crystalline scattering integrated intensity
Ia: amorphous scattering integrated intensity
The amorphization ratio X is calculated according to the above Equation (1) by performing crystal structure analysis for the soft magnetic alloy ribbon by using X-ray diffraction (XRD), identifying a phase, reading a peak (Ic: crystalline scattering integrated intensity, Ia: amorphous scattering integrated intensity) of crystallized Fe or a compound, and calculating the crystallization ratio based on a peak intensity. The calculation method will be described in more detail below.
The crystal structure analysis for the soft magnetic alloy ribbon of the present embodiment is performed by using XRD and a chart as shown in
The soft magnetic alloy ribbon of the present embodiment may contain a main component represented by a composition formula
(Fe(1−(α+β))X1αX2β)(1−(a+b+c+d))MaBbPcSid, in which
X1 is one or more selected from the group consisting of Co and Ni,
X2 is one or more selected from the group consisting of Al, Mn, Ag, Zn, Sn, As, Sb, Cu, Bi, S, N, O, and a rare earth element,
M is one or more selected from the group consisting of Nb, Ta, W, Zr, Hf, Mo, Cr, and Ti
0.001≤a≤0.150
0.020≤b≤0.200
0≤c≤0.150
0≤d≤0.180
α≥0,
β≥0, and
0≤α+β≤0.50 may be satisfied.
In the soft magnetic alloy ribbon having the above composition, amorphous substances are likely to be formed. Further, when the soft magnetic alloy ribbon having the above composition is subjected to a heat treatment, the Fe-based nanocrystals are likely to be deposited in the soft magnetic alloy ribbon.
Hereinafter, each component other than M and Si in the soft magnetic alloy ribbon 24 of the present embodiment will be described in detail.
The B content (b) may satisfy 0.020≤b≤0.200. In addition, 0.030≤b≤0.120 may be satisfied.
The P content (c) may satisfy 0≤c≤0.150. In addition, 0.010≤c≤0.050 may be satisfied.
The Fe content (1−(a+b+c+d)) is not particularly limited, and 0.70≤(1−(a+b+c+d))≤0.900 may be satisfied.
In the soft magnetic alloy ribbon of the present embodiment, a part of Fe may be substituted by X1 and/or X2.
X1 is one or more selected from the group consisting of Co and Ni. The X1 content may be α=0. That is, X1 may not be contained. The number of atoms of X1 is preferably 40 at % or less, with respect to a total number of atoms of 100 at % in the composition. That is, 0≤α {1−(a+b+c+d)}≤0.400 is preferably satisfied.
X2 is one or more selected from the group consisting of Al, Mn, Ag, Zn, Sn, As, Sb, Cu, Bi, S, N, O, and a rare earth element. The X2 content may be β=0. That is, X2 may not be contained. The number of atoms of X2 is preferably 3.0 at % or less, with respect to a total number of atoms of 100 at % in the composition. That is, 0≤β {1−(a+b+c+d)}≤0.030 is preferably satisfied. Oxygen, which is contained in a vicinity of the surface and includes in oxides with M and Si, is also contained in X2, but may be in a trace amount when viewed from the entire soft magnetic alloy ribbon and may be ignored.
The amount of substitution of Fe by X1 and/or X2 is a half of Fe based on the number of atoms. That is, 0≤α+β≤0.50 may be satisfied.
The soft magnetic alloy ribbon of the present embodiment may contain elements other than the above elements as inevitable impurities. For example, the soft magnetic alloy ribbon of the present embodiment may contain the inevitable impurities in an amount of 0.1 wt % or less with respect to 100 wt % of the soft magnetic alloy ribbon.
The composition for easily obtaining the soft magnetic alloy ribbon having Fe-based nanocrystals is described above, but the microstructure of the soft magnetic alloy ribbon is not particularly limited, and the composition of the soft magnetic alloy ribbon is not particularly limited except that the composition contains M. A soft magnetic alloy ribbon having a composition containing M may be used.
(Method for Manufacturing Soft Magnetic Alloy Ribbon)
A method for manufacturing the soft magnetic alloy ribbon of the present embodiment will be described below.
The method for manufacturing the soft magnetic alloy ribbon of the present embodiment is not particularly limited. For example, there is a method for manufacturing the soft magnetic alloy ribbon by a single-roll method. The ribbon may be a continuous ribbon.
In the single-roll method, first, pure raw materials of elements contained in the soft magnetic alloy ribbon to be finally obtained are prepared and weighed so as to have the composition same as that of the soft magnetic alloy ribbon to be finally obtained. Then, the pure raw materials of elements are melted and mixed to prepare a base alloy. A method for melting the pure raw materials is optionally, and, for example, there is a method for melting the pure raw materials by high-frequency heating after vacuum-evacuating the pure raw materials in a chamber. The base alloy and the soft magnetic alloy ribbon to be finally obtained have the same composition.
Next, the prepared base alloy is heated and melted to obtain a molten metal. A temperature of the molten metal is not particularly limited, and may be, for example, 1,200° C. to 1,500° C.
In the present embodiment, as shown in
The oxygen concentrations in release gas and spray gas are not particularly limited, and may be 0.5% to 100%, or 5% to 100%, or 30% to 100%. Injection pressures of the release gas and the spray gas are not particularly limited. For example, the injection pressure is 10 kPa or more and 300 kPa or less. The release gas and the spray gas may have the same oxygen concentration and/or injection pressure, and may have different oxygen concentrations and/or injection pressures.
The soft magnetic alloy ribbon 24 obtained by the above method may not contain crystals having a grain size larger than 30 nm. The soft magnetic alloy ribbon 24 may have the structure formed of only amorphous substances, and may have the nanohetero structure in which crystals having a grain size of 30 nm or less are present in amorphous substances.
A method for confirming whether crystals having a grain size larger than 30 nm are contained in the soft magnetic alloy ribbon 24 is not particularly limited. For example, a presence or absence of crystals having a grain size larger than 30 nm can be confirmed by normal X-ray diffraction measurement. The presence or absence of crystals having a grain size larger than 30 nm may be confirmed by direct observation using a transmission electron microscope.
A method for observing the presence or absence and the average grain size of the initial microcrystal is not particularly limited, and for example, the presence or absence and the average grain size of the initial microcrystal can be confirmed by using a transmission electron microscope to obtain a selected area electron diffraction image, a nano beam diffraction image, a bright field image or a high resolution image of a sample sliced by ion milling. In the case of using a selected area electron diffraction image or a nano beam diffraction image is used, ring-shaped diffraction is formed when a diffraction pattern is amorphous, whereas a diffraction spot due to a crystal structure is formed when the diffraction pattern is not amorphous. In the case of using a bright field image or a high resolution image, the presence or absence and the average grain size of the initial microcrystal can be observed by visual observation at a magnification of 1.00×105 times to 3.00×105 times.
By controlling the oxygen concentration of the gas injected from the release gas injection device 26 and the spray gas injection device 27, the soft magnetic alloy ribbon 24 in which the concentration distribution of the oxide of M of the present embodiment is formed is obtained.
Heat treatment conditions for manufacturing the soft magnetic alloy ribbon of the present embodiment are not particularly limited as long as oxidation of the surface of the soft magnetic alloy ribbon does not proceed. Preferred heat treatment conditions differ depending on the composition of the soft magnetic alloy ribbon. Generally, a preferred heat treatment temperature is about 400° C. to 700° C., and a preferred heat treatment time is about 0.5 hour to 10 hours. However, depending on the composition, there may be a preferred heat treatment temperature and a preferred heat treatment time outside the above ranges. In order to maintain a surface state of the soft magnetic alloy ribbon, a heat treatment is performed in an inert atmosphere such as Ar gas or in a vacuum atmosphere.
By performing the heat treatment in the inert atmosphere or in the vacuum atmosphere, while the surface state is maintained, diffusion of the elements constituting the soft magnetic alloy ribbon 24 can be promoted, a thermodynamic equilibrium state can be reached in a short time, and distortion and stress present in the soft magnetic alloy ribbon can be eliminated. As a result, a soft magnetic alloy having an improved saturation magnetic flux density can be easily obtained. When the heat treatment is performed at a temperature equal to or higher than a temperature at which the Fe-based nanocrystals are deposited, the Fe-based nanocrystals are deposited. Therefore, by performing the heat treatment at a temperature equal to or higher than the temperature at which the Fe-based nanocrystals are deposited in the inert atmosphere, the soft magnetic alloy ribbon having further improved saturation magnetic flux density can be easily obtained.
A method for calculating an average grain size of the Fe-based nanocrystals contained in the soft magnetic alloy ribbon obtained by the heat treatment is not particularly limited. For example, the average grain size can be calculated by observation using a transmission electron microscope. A method for confirming that the crystal structure is a bcc (body-centered cubic lattice structure) is also not particularly limited. For example, the crystal structure being a bcc can be confirmed by using X-ray diffraction measurement.
Hereinafter, a method for obtaining a core and an inductor of the present embodiment will be described, and the method for obtaining a core and an inductor from the soft magnetic alloy ribbon is not limited to the following method.
A method for obtaining a core from the soft magnetic alloy ribbon includes, for example, a method for winding the soft magnetic alloy ribbon and a method for laminating the soft magnetic alloy ribbon. When the soft magnetic alloy ribbon is laminated via an insulator, a core having improved properties can be obtained.
In addition, an inductor is obtained by applying a winding to the core. A method for applying the winding and a method for manufacturing the inductor are not particularly limited. For example, a method for winding at least one turn on the core manufactured by the above method can be used.
A magnetic component of the present embodiment, particularly the core and the inductor (coil) using the core, is obtained from the soft magnetic alloy ribbon of the present embodiment. A use of the core includes, for example, a transformer in addition to the inductor. The transformer and the inductor are used in a power device or the like.
The core of the present embodiment is particularly suitable for a small-sized power device. Generally, the transformer and inductor occupy a large volume in the power device. Here, even when the core of the present embodiment is miniaturized, a sufficiently high saturation magnetic flux density can be obtained. Therefore, even when the volume of the transformer and the inductor using the core of the present embodiment is reduced, a maximum magnetic flux density at a time of driving the power device is easily increased. Therefore, the core of the present embodiment is particularly suitable for a small-sized power device.
Although the embodiments of the present invention have been described above, the present invention is not limited to the above embodiments.
Even when the soft magnetic alloy ribbon of the present embodiment is prepared in an air atmosphere, the oxidation state of the surface of the soft magnetic alloy ribbon can be controlled by using the release gas and the spray gas. Therefore, the oxidation of Fe on the surface of the soft magnetic alloy ribbon can be controlled uniformly, and the corrosion resistance of the soft magnetic alloy ribbon can be controlled. Further, when Fe is locally oxidized on the surface of the soft magnetic alloy ribbon, the oxidation of Fe proceeds in an atmosphere and an oxide phase of Fe tends to increase. Then, a total amount of magnetic materials in the soft magnetic alloy ribbon tends to decrease. Therefore, as described above, the soft magnetic alloy ribbon of the present embodiment is suitably used for a magnetic component whose saturation magnetic flux density is required to improve. Therefore, the magnetic component in the present embodiment is particularly suitable for miniaturization of a power supply circuit of an electronic device, an information device, a communication device, or the like.
Hereinafter, the present invention will be described in detail based on Examples.
Raw materials were weighed to obtain an alloy composition shown in Table 1, and melted by high-frequency heating to prepare a base alloy.
Thereafter, the prepared base alloy was heated and melted to form a metal in a molten state at 1300° C., and then the metal was injected onto a roll by a single-roll method in which the roll was rotated at a rotation speed of 30 m/sec to prepare a ribbon. The material of the roll is Cu.
The roll was rotated in a direction shown in
Further, Table 1 and Table 2 show oxygen concentrations of the release gas and the spray gas in the case of performing the single-roll method. A sample in which the oxygen concentration of the release gas and the spray gas was 0% was sprayed with N2 gas, and a sample in which the oxygen concentration of the release gas and the spray gas was not 0% was sprayed with N2—O2 mixed gas.
Further, it was confirmed whether the ribbon before the heat treatment was formed of amorphous substances or crystals. The amorphization ratio X of each ribbon was measured by using XRD, and when X was 85% or more, it was considered that the ribbon was formed of amorphous substances.
Thereafter, the heat treatment was performed on ribbons of each Example and Comparative Example in Table 1 at 600° C. for 60 minutes in an N2 atmosphere (oxygen concentration: 10 ppm or less). The crystal grain size of each ribbon after the heat treatment was measured by a transmission electron microscope. It was confirmed that a nanocrystal having a crystal grain size of 5 nm to 30 nm was contained. Table 2 shows results.
A ribbon before the heat treatment was prepared at the same conditions except that the kind of M was changed for a sample No. 6 in Table 1, and the heat treatment was performed at the same conditions. Table 3 shows results.
The concentration distribution of elements contained in the soft magnetic alloy ribbon was measured from the surface (thickness 0 nm) toward the interior in the thickness direction by using XPS for each ribbon in Table 1 to Table 3. The concentration distribution was measured such that a distance between measurement points was 1.6 nm in terms of SiO2 in a region within 16 nm from the surface, and a distance between the measurement points was 3.2 nm in terms of SiO2 in a region having a depth of 16 nm or more from the surface. Table 1 to Table 3 show the presence or absence of the maximum point of the M element includes in oxides and the presence or absence of the maximum point of Si includes in oxides and maximum values thereof. In a case of having the maximum point, it is denoted as “Yes”, and in a case of not having the maximum point, it is denoted as “No”.
The saturation magnetic flux density of each ribbon after the heat treatment was measured. The saturation magnetic flux density was measured at a magnetic field of 1,500 kA/m using a vibrating sample magnetometer (VSM).
The obtained ribbon was subjected to a corrosion resistance test to confirm the corrosion resistance thereof. Specifically, each sample was inserted into a thermostatic chamber held at a temperature of 85° C. and a humidity of 85%, and the surface of each sample was visually observed every 30 minutes to confirm the presence or absence of a spot rust. Table 1 to Table 3 show a case where a time until the spot rust was observed for the first time was 2.0 times or more that of each Comparative Example (when N2 gas was sprayed) as A, a case where the time until the spot rust was observed for the first time was 1.2 times or more and less than 2.0 times that of each Comparative Example as B, a case where the time until the spot rust was observed for the first time was greater than 1.0 time and less than 1.2 times that of each Comparative Example as C and a case where the time until the spot rust was observed for the first time was 1.0 time or less that of each Comparative Example as D. A case where the evaluation was C or better was regarded as good. A sample No. 1 is taken as a reference in Table 1, and a sample No. 9 is taken as a reference in Table 2 and Table 3.
The microstructures of the soft magnetic alloy ribbons of Examples and Comparative Examples were confirmed by X-ray diffraction measurement and observation using a transmission electron microscope. Table 1 to Table 3 show results. An alloy composition being not change before and after the heat treatment was confirmed by ICP analysis.
indicates data missing or illegible when filed
As seen from Table 1 and Table 2, when the maximum point of the concentration of M (Nb) includes in oxides is present in a region within 20 nm from the surface, the corrosion resistance is excellent as compared with a case where the maximum point of the concentration of M includes in oxides is not present in the region within 20 nm from the surface. Further, when the maximum point of the concentration of M (Nb) includes in oxides after the heat treatment is present in the region within 20 nm from the surface, the saturation magnetic flux density is also good as compared with the case where the maximum point of the concentration of M includes in oxides is not present in the region within 20 nm from the surface.
In particular, when [Si]/[M]≥1.50 is satisfied, the corrosion resistance is particularly good.
As seen from Table 3, similar results are obtained even when the kind of M element is changed from Nb.
The same experiment as in each of Experimental Examples shown in Table 2 was conducted after changing the composition from Experimental Example 1. Table 4 to Table 6 show results. For the corrosion resistance test, a sample No. 22 is taken as a reference in Table 4, a sample No. 32 is taken as a reference in Table 5, and a sample No. 40 is taken as a reference in Table 6. The microstructure of each of soft magnetic alloy ribbons of Examples and Comparative Examples was nanocrystalline.
As seen from Table 4 to Table 6, when the maximum point of the concentration of M (Nb) includes in oxides is present in a region within 20 nm from the surface even when the composition is changed, the corrosion resistance is excellent as compared with a case where the maximum point of the concentration of M includes in oxides is not present in the region within 20 nm from the surface. Further, when the sample No. 22 and the sample No. 23 having the same composition are compared with each other, the sample No. 23 in which the maximum point of the concentration of M includes in oxides is present has a saturation magnetic flux density better than that of the sample No. 22 in which the maximum point of the concentration of M includes in oxides is not present in the region within 20 nm from the surface. When the sample No. 32 and a sample No. 33 having the same composition are compared with each other, the sample No. 33 in which the maximum point of the concentration of M includes in oxides is present has a saturation magnetic flux density better than that of the sample No. 32 in which the maximum point of the concentration of M includes in oxides is not present in the region within 20 nm from the surface. When the sample No. 40 and a sample No. 41 having the same composition are compared with each other, the sample No. 41 in which the maximum point of the concentration of M includes in oxides is present has a saturation magnetic flux density better than that of the sample No. 40 in which the maximum point of the concentration of M includes in oxides is not present in the region within 20 nm from the surface.
As seen from Table 4, the saturation magnetic flux density is higher when the composition ratio of Si is 0.1 at % or more and 10 at % or less, that is, 0.001≤d≤0.100. As seen from Table 5, the corrosion resistance is higher when the composition ratio of M is more than 3 at % and 10 at % or less, that is, 0.030<a≤0.100. As seen from Table 6, when the amount of P is 0.1 at % or more and 15 at % or less, that is, 0≤c≤0.150 was satisfied, the corrosion resistance is good.
The composition of the soft magnetic alloy ribbon was changed to a commonly used composition, and the same experiment as in each of Experimental Examples shown in Table 2 was conducted. Table 7 show results. For the corrosion resistance test, a sample No. 46 is taken as a reference for a sample No. 47, a sample No. 48 is taken as a reference for a sample No. 49, and a sample No. 50 is taken as a reference for a sample No. 51, and a sample No. 52 is taken as a reference for a sample No. 53. Table 7 also shows the microstructure of each of the soft magnetic alloy ribbons of Examples and Comparative Examples.
As seen from Table 7, when the maximum point of the concentration of M (Nb) includes in oxides is present in a region within 20 nm from the surface even when the composition is changed, the corrosion resistance and the saturation magnetic flux density are excellent as compared with a case where the maximum point of the concentration of M includes in oxides is not present in the region within 20 nm from the surface.
| Number | Date | Country | Kind |
|---|---|---|---|
| 2019-211335 | Nov 2019 | JP | national |
