Iron-based amorphous alloy, powdery / granular material thereof, and compacted powder material thereof

Abstract

To achieve both a high saturation magnetization Ms and a low coercivity Hc in an iron-based amorphous alloy.SOLUTION: An iron-based amorphous alloy is represented by a composition formula FeaSibBcPdCe, where the composition ratio a satisfies 76.0≤a≤80.0, the composition ratio b satisfies 3.0≤b≤6.9, the composition ratio c satisfies 9.9≤c≤14.0, the composition ratio d satisfies 0.8≤d≤4.6, and the composition ratio e satisfies 1.0≤e≤4.1.SELECTED DRAWING: None

Description

[Technical Field]

[0001] The present invention relates to an iron-based amorphous alloy, a powder or granule thereof, and a compacted powder material thereof. [Background technology]

[0002] Powders of soft magnetic iron-based amorphous alloys are highly processable, and in addition to being used as bulk materials, they are processed into various shapes and sizes, such as ribbons, wires, and powders, and are widely used. For example, among the compacted powder materials obtained by compacting iron-based amorphous alloy powders, many exhibit excellent magnetic properties. Therefore, compacted powder materials made from iron-based amorphous alloys can be said to be powerful magnetic materials.

[0003] Patent Document 1 describes an iron-based amorphous alloy that can be produced relatively inexpensively without using very expensive materials such as Ga, Pd, and Zr, and that is composed of Fe, Si, B, P, and C and a supercooling improving element M. Here, the supercooling improving element M is an element that has the function of facilitating the amorphization of the iron-based amorphous alloy. Patent Document 1 lists Nb and Mo as the supercooling improving element M. [Prior art documents] [Patent documents]

[0004] [Patent Document 1] Japanese Patent Application Laid-Open No. 2005-290468 Summary of the Invention [Problem to be solved by the invention]

[0005] Incidentally, when an iron-based amorphous alloy is used as a soft magnetic material, there is a tendency for the iron-based amorphous alloy to be required to have a high saturation magnetization Ms (or saturation magnetic flux density Bs) and a low coercive force Hc. In Patent Document 1, the saturation magnetic flux density Bs is used instead of the saturation magnetization Ms. Since the saturation magnetic flux density Bs can be converted from the saturation magnetization Ms, the saturation magnetic flux density Bs will be used when describing the iron-based amorphous alloy described in Patent Document 1.

[0006] To obtain a high saturation magnetization Ms, simply increase the amount of Fe contained in the iron-based amorphous alloy. However, the higher the Fe composition ratio in the iron-based amorphous alloy, the more likely it is that a crystalline phase will precipitate in addition to the amorphous phase. Manufacturers of iron-based amorphous alloys often design the composition ratio of each element to facilitate the amorphization of the iron-based amorphous alloy and suppress the precipitation of a crystalline phase. In other words, manufacturers often design the composition ratio of each element to achieve the desired saturation magnetization Ms and coercive force Hc.

[0007] In fact, referring to Tables 3 and 4 of Patent Document 1, the degree of supercooling ΔTx and saturation magnetic flux density Bs are listed for each example of an iron-based amorphous alloy. Although Patent Document 1 does not list the coercive force Hc, it uses the degree of supercooling ΔTx as an alternative index. The degree of supercooling ΔTx is used as an index representing the ease of amorphization in an iron-based amorphous alloy. The greater the value of the degree of supercooling ΔTx, the easier it tends to be to amorphize.

[0008] Among these examples, the iron-based amorphous alloy exhibiting the highest saturation magnetic flux density Bs is Example 4-1, and the iron-based amorphous alloy exhibiting the largest degree of supercooling ΔTx is Example 3-6. Example 4-1 exhibits a degree of supercooling ΔTx of 40.2 and a saturation magnetic flux density Bs of 1.53 T. Example 3-6 exhibits a degree of supercooling ΔTx of 52.8 and a saturation magnetic flux density Bs of 1.13 T.

[0009] Thus, in an iron-based amorphous alloy, when an attempt is made to increase either the saturation magnetization Ms or the coercive force Hc, the other magnetic property tends to decrease. In other words, it is difficult for an iron-based amorphous alloy to achieve both a high saturation magnetization Ms and a low coercive force Hc (or a large degree of supercooling ΔTx).

[0010] One aspect of the present invention has been made in consideration of the above-mentioned problems, and its object is to provide a composition of Fe a Si b B c P d C e The object of the present invention is to provide an iron-based amorphous alloy having a coercive force Hc of Hc≦300 A / m and a saturation magnetization Ms of Ms≧155 emu / g. [Means for solving the problem]

[0011] In order to solve the above problems, an iron-based amorphous alloy according to one aspect of the present invention is an iron-based amorphous alloy having the composition formula Fe a Si b B c P d C e In this iron-based amorphous alloy, when the composition ratios a, b, c, d, and e of each element are expressed as percentages, the sum of a, b, c, d, and e is 97.0≦a+b+c+d+e≦100, the composition ratio a of Fe satisfies 76.0≦a≦80.0, the composition ratio b of Si satisfies 3.0≦b≦6.9, the composition ratio c of B satisfies 9.9≦c≦14.0, the composition ratio d of P satisfies 0.8≦d≦4.6, and the composition ratio e of C satisfies 1.0≦e≦4.1.

[0012] In order to solve the above-mentioned problems, a powder or granular material according to one aspect of the present invention is made of the above-mentioned iron-based amorphous alloy.

[0013] In order to solve the above-mentioned problems, a compacted powder material according to one aspect of the present invention is made of the above-mentioned powder and granular material. [Effects of the Invention]

[0014] According to one aspect of the present invention, a compound having the composition formula Fe a Si b B c P d C e In the iron-based amorphous alloy represented by the formula (1), it is possible to achieve both a high saturation magnetization Ms and a low coercive force Hc. [Brief explanation of the drawings]

[0015] [Figure 1] 1 is a graph showing a DSC curve of an iron-based amorphous alloy according to an embodiment of the present invention. [Figure 2] (a) is a scatter plot in which the coercive force of each iron-based amorphous alloy representing an example of the present invention and a comparative example is plotted in the space spanned by the composition ratio a of Si and the composition ratio c of B. (b) is a scatter plot in which the coercive force of each iron-based amorphous alloy is plotted in the space spanned by the composition ratio a of Si and the composition ratio d of P. (c) is a scatter plot in which the coercive force of each iron-based amorphous alloy is plotted in the space spanned by the composition ratio a of Si and the composition ratio e of C. (d) is a scatter plot in which the coercive force of each iron-based amorphous alloy is plotted in the space spanned by the composition ratio c of B and the composition ratio d of P. (e) is a scatter plot in which the coercive force of each iron-based amorphous alloy is plotted in the space spanned by the composition ratio c of B and the composition ratio e of C. 1(f) is a scatter diagram in which the coercive force of each iron-based amorphous alloy is plotted in the space spanned by the P composition ratio d and the C composition ratio e. [Figure 3] This is a scatter plot in which the coercive force of each iron-based amorphous alloy is plotted in the space spanned by the sum of the Si composition ratio b and the B composition ratio c, and the sum of the P composition ratio d and the C composition ratio e. DETAILED DESCRIPTION OF THE INVENTION

[0016] [Embodiment 1] An iron-based amorphous alloy according to a first embodiment of the present invention will be described. The iron-based amorphous alloy of this embodiment has the composition formula Fe a Si b B c P d C e In this embodiment, the composition ratios a, b, c, d, and e of the elements Fe, Si, B, P, and C are expressed as percentages. The sum of a, b, c, d, and e is 97.0≦a+b+c+d+e≦100. That is, when elements other than Fe, Si, B, P, and C are referred to as impurity elements, the iron-based amorphous alloy of this embodiment may contain impurity elements as long as the composition ratio is less than 2.0. Furthermore, in the iron-based amorphous alloy of this embodiment, the composition ratio a of Fe satisfies 76.0≦a≦80.0, the composition ratio b of Si satisfies 3.0≦b≦6.9, the composition ratio c of B satisfies 9.9≦c≦14.0, the composition ratio d of P satisfies 0.8≦d≦4.6, and the composition ratio e of C satisfies 1.0≦e≦4.1. In the following, at% is used as the unit of composition ratios typified by composition ratios a, b, c, d, and e. When expressing composition ratios typified by composition ratios a, b, c, d, and e, the first decimal place is used after rounding to the nearest whole number.

[0017] A typical example of an impurity is oxygen (O). In the iron-based amorphous alloy of this embodiment, the composition ratio of Fe is the highest. Therefore, an oxide film is likely to form on the surface of the iron-based amorphous alloy, mainly due to the oxidation of Fe by oxygen contained in the atmosphere. Furthermore, the influence of the surface of a solid becomes more pronounced as the size of the solid decreases. This is because the ratio of surface area to volume increases as the size decreases. As will be described later in the second embodiment, when the iron-based amorphous alloy is in the form of a powder or granular material, the O composition ratio may exceed 1.0 and approach 3.0. However, an iron-based amorphous alloy having an O composition ratio of less than 3.0 can achieve both a high saturation magnetization Ms and a low coercive force Hc. Therefore, impurity elements having a composition ratio of less than 3.0 may be contained in the iron-based amorphous alloy. The composition ratio of the impurity elements is preferably low, and may be less than 2.0 or even less than 1.0.

[0018] In the iron-based amorphous alloy of this embodiment, it is preferable that the composition ratios b and c satisfy 15.0≦b+c≦18.0, and the composition ratios d and e satisfy 4.0≦d+e≦6.0.

[0019] An example of the composition ratios a, b, c, d, and e is a:b:c:d:e=78.45:4.15:13:0.95:3.45.

[0020] The alloy of this embodiment contains more B than the alloys of the examples of Patent Document 1. That is, a larger value is adopted for the composition ratio c. This configuration increases the density of the alloy, thereby improving the saturation magnetization Ms. Furthermore, by adjusting the composition ratios of elements other than Fe and B (i.e., Si, P, and C), an alloy is realized that can achieve both a high saturation magnetization Ms and a low coercive force Hc.

[0021] Furthermore, in the iron-based amorphous alloy of this embodiment, it is preferable that the coercive force Hc satisfies Hc≦300 A / m and the saturation magnetization Ms satisfies Ms≧155 emu / g. The magnetic properties of the iron-based amorphous alloy (in this embodiment, the coercive force Hc and the saturation magnetization Ms) can be measured using a magnetic measurement device typified by a vibrating sample magnetometer (VSM) and a superconducting quantum interference device (SQUID) magnetometer.

[0022] The iron-based amorphous alloy of this embodiment may have a supercooling degree ΔTx, which is the difference between the crystallization temperature Tx and the glass transition temperature Tg, satisfying ΔTx≧100K, and a saturation magnetization Ms satisfying Ms≧155 emu / g. The crystallization temperature is also called the recrystallization onset temperature. The method for measuring the saturation magnetization Ms is as described above. Meanwhile, the supercooling degree ΔTx can be determined from the DSC curve obtained by measuring the differential scanning calorimetry (DSC) of the iron-based amorphous alloy. For example, the supercooling degree ΔTx can be determined by performing DSC measurement using the method described in Japanese Industrial Standards (JIS) H 7151-1991, "Method for measuring the crystallization temperature of amorphous metals."

[0023] According to JIS H 7151-1991, it is preferable to increase the temperature at a heating rate of 10°C / min, and it is preferable to adjust the measuring device so that the baseline of the DSC curve is always as straight as possible parallel to the temperature axis. This adjustment may be performed automatically by the DSC measuring device.

[0024] Furthermore, JIS H 7151-1991 states that when a DSC curve has multiple exothermic peaks, the intersection of the baseline BLx and the tangent TLx is defined as the crystallization temperature Tx. Here, the baseline BLx is an extension of the baseline on the low-temperature side of the lowest-temperature exothermic peak among peaks at which sufficient heat is released due to crystallization, and the tangent TLx is a tangent to the curve on the low-temperature side of the exothermic peak at which the slope is maximum. JIS H 7151-1991 does not describe how to determine the glass transition temperature Tg. However, if the method for determining the crystallization temperature Tx is also applied to the glass transition temperature Tg, the result is as follows. That is, when a DSC curve has multiple endothermic peaks, the intersection of the baseline BLg and the tangent TLg can be defined as the glass transition temperature Tg. Here, the baseline BLg is an extension of the baseline on the low-temperature side of the highest endothermic peak among the peaks at which sufficient heat absorption associated with glass transition is observed, and the tangent TLg is a tangent at the point where the gradient of the curve on the low-temperature side of the endothermic peak is maximum.

[0025] Fig. 1(a) is a graph of a DSC curve obtained from one example of an iron-based amorphous alloy according to this embodiment. Fig. 1(b) is an enlarged view of the graph shown in Fig. 1(a), showing an enlarged view of a heat generation region RG where the iron-based amorphous alloy generates heat as the temperature rises. Fig. 1(b) also shows a baseline BLx and a tangent line TLx. Fig. 1(c) is an enlarged view of the graph shown in Fig. 1(a), showing an enlarged view of an endothermic region RA where the iron-based amorphous alloy absorbs heat as the temperature rises.

[0026] The DSC curve shown in Figure 1(a) has three peaks PG1, PG2, and PG3 in the exothermic region RG and one peak PA1 in the endothermic region RA. Of the three peaks PG1, PG2, and PG3, peak PG1 is located at the lowest temperature. Therefore, the crystallization temperature Tx is determined as the intersection of the baseline BLx and the tangent line TLx to peak PG1. According to Figure 1, the crystallization temperature Tx is approximately 510°C. Similarly, the glass transition temperature Tg, determined using the above-mentioned method, was approximately 290°C. Therefore, the degree of supercooling ΔTx, defined as ΔTx = Tx - Tg, is approximately 220°C.

[0027] The iron-based amorphous alloy configured as above can be suitably used as a raw material for the powder or granular material described later in the second embodiment.

[0028] The method for producing the iron-based amorphous alloy of this embodiment is not particularly limited, and can be appropriately selected from existing alloy production methods, so a description of the production method will be omitted here.

[0029] [Embodiment 2] A powder or granular material according to a second embodiment of the present invention will now be described. The powder or granular material according to this embodiment is a powder or granular material produced using the iron-based amorphous alloy according to the first embodiment as a material. That is, the powder or granular material according to this embodiment is made of the alloy described in the first embodiment.

[0030] In this embodiment, water atomization is used as a manufacturing method for producing powder and granular materials using the iron-based amorphous alloy according to embodiment 1. Water atomization is a manufacturing method suitable for producing powder and granular materials with a relatively small average particle size D50. By using water atomization, powder and granular materials with an average particle size D50 of 50 μm or less can be produced. Note that the lower limit of powder and granular materials that can be produced by water atomization is currently 0.5 μm. Therefore, the powder and granular materials according to this embodiment can satisfy the average particle size D50 of 0.5 μm≦D50≦50 μm. Furthermore, the powder and granular materials according to this embodiment can satisfy the average particle size D50 of 0.5 μm≦D50≦20 μm. By reducing the average particle size D50 of the powder and granular materials, the compacted powder material described in embodiment 3, which is used for electronic components, can be made even smaller.

[0031] The water atomization method is described in JP 2003-034849 A, JP 2021-055182 A, etc. Therefore, a description of the water atomization method will be omitted here.

[0032] Furthermore, the method for producing the powder or granular material of this embodiment is not limited to the water atomization method, but may be a SWAP method, a gas atomization method, or the like.

[0033] [Embodiment 3] The compacted powder material according to the third embodiment of the present invention is obtained by compacting the powder or granular material according to the second embodiment as a raw material. Therefore, the compacted powder material according to the present embodiment is made of the powder or granular material according to the second embodiment. In the compacted powder material according to this embodiment, the average particle diameter D50 of the powder particles used as raw materials can be reduced as described above, so the compacted powder material according to this embodiment can be made smaller than conventional compacted powder materials. [Example]

[0034] A group of embodiments of the present invention will be described with reference to Tables 1 and 2.

[0035] Table 1 summarizes the composition ratio, iron content, alloy density, saturation magnetization Ms, saturation magnetic flux density Bs, and coercive force Hc for each alloy. In Table 1, the number of decimal points used for each of the composition ratios a to e, alloy density, saturation magnetization Ms, and coercive force Hc varies depending on the magnitude of the value. Specifically, the composition ratio a and saturation magnetization Ms are expressed with one decimal point, the composition ratios b to e and alloy density are expressed with two decimal points, and the coercive force Hc is expressed as an integer. Note that each composition ratio listed in Table 1 is a so-called pre-mixed value composition ratio calculated based on the target composition of the iron-based amorphous alloy and the composition ratio of each element contained in the starting materials. As will be described later with reference to Table 2, it is believed that there is no significant difference between the pre-mixed value composition ratio of each element and the actual composition ratio of each element in the resulting alloy. Therefore, in Table 1, the composition ratio of the alloy is defined using the composition ratio of each element, which is the charge value of each element. However, the composition ratio of the alloy may also be defined using the actual composition ratio of each element in the obtained alloy. [Table 1]

[0036] Table 2 summarizes the actual composition ratios a to e, saturation magnetization Ms, and coercive force Hc for Examples 13 to 20 of iron-based amorphous alloys obtained when the composition ratio of the charged values ​​was a:b:c:d:e=78.45:4.15:13:0.95:3.45. Referring to Table 2, it can be seen that in each of Examples 13 to 20, the saturation magnetization Ms and coercive force Hc satisfy Ms≧155 emu / g and Hc≦300 A / m, respectively. Furthermore, it can be seen that the variation in each of the composition ratios a to e falls within a ±1% range. Therefore, in the iron-based amorphous alloy according to one embodiment of the present invention, it can be assumed that there is no significant difference between the composition ratios, which are the charged values ​​of each element, and the actual composition ratios of each element in the resulting alloy. [Table 2]

[0037] Furthermore, powders of iron-based amorphous alloys were produced using each of the obtained alloys by water atomization. In Table 1, the composition ratios a, b, c, d, and e of each element are listed as composition ranges within the scope of the present invention. For each of the composition ratios a, b, c, d, and e of each alloy, if they fall within the composition range, T (True) is added, and if they do not fall within the composition range, F (False) is added. If all of a, b, c, d, and e are T, the alloy is designated as an example, and if any one of them is F, the alloy is designated as a comparative example. Table 1 is arranged from top to bottom in descending order of Fe composition ratio a.

[0038] It was found that the iron-based amorphous alloys of the respective examples had a supercooling ΔTx that satisfied ΔTx≧100K and a saturation magnetization Ms that satisfied Ms≧155 emu / g.

[0039] A graph of the DSC curve measured for the iron-based amorphous alloy of the example is shown in Figure 1. Referring to Figure 1, it was found that the iron-based amorphous alloy of the example had a crystallization temperature Tx of about 510°C, a glass transition temperature Tg of about 290°C, and a degree of supercooling ΔTx of about 220°C.

[0040] FIG. 2(a) is a scatter plot in which the coercive force of each iron-based amorphous alloy representing an example of the present invention and a comparative example is plotted in the space spanned by the composition ratio a of Si and the composition ratio c of B. FIG. 2(b) is a scatter plot in which the coercive force of each iron-based amorphous alloy is plotted in the space spanned by the composition ratio a of Si and the composition ratio d of P. FIG. 2(c) is a scatter plot in which the coercive force of each iron-based amorphous alloy is plotted in the space spanned by the composition ratio a of Si and the composition ratio e of C. FIG. 2(d) is a scatter plot in which the coercive force of each iron-based amorphous alloy is plotted in the space spanned by the composition ratio c of B and the composition ratio d of P. FIG. 2(e) is a scatter plot in which the coercive force of each iron-based amorphous alloy is plotted in the space spanned by the composition ratio c of B and the composition ratio e of C. FIG. 2(f) is a scatter diagram in which the coercive force of each iron-based amorphous alloy is plotted in the space spanned by the P composition ratio d and the C composition ratio e.

[0041] FIG. 3 is a scatter plot in which the coercive force of each iron-based amorphous alloy is plotted in the space spanned by the sum of the Si composition ratio b and the B composition ratio c, and the sum of the P composition ratio d and the C composition ratio e.

[0042] In each diagram in Figure 2 and Figure 3, iron-based amorphous alloys whose coercive force Hc satisfies Hc≦300 A / m are plotted with open circles, and iron-based amorphous alloys that do not satisfy this condition (i.e., satisfy Hc>300 A / m) are plotted with crosses (or x).

[0043] Each diagram in FIG. 2 is a correlation diagram obtained by focusing on two of the composition ratios a to e. Therefore, even within the composition range (the composition range shown in Table 1) of one embodiment of the present invention shown in each diagram in FIG. 2, there are iron-based amorphous alloys plotted with an "x" mark. For example, referring to FIG. 2(a), it was found that, even among iron-based amorphous alloys in which the Si composition ratio b satisfies 3.0≦b≦6.9, there are five iron-based amorphous alloys (i.e., comparative examples) that do not satisfy Hc≦300 A / m. These five comparative examples are iron-based amorphous alloys in which at least one of the composition ratios a, c, d, and e other than composition ratio b does not fall within the composition range of one embodiment of the present invention.

[0044] 3, it was found that the sum b+c of the Si composition ratio b and the B composition ratio c satisfies Hc≦300 A / m when 15.0≦b+c≦18.0 is satisfied. It was also found that the sum d+e of the P composition ratio d and the C composition ratio e satisfies Hc≦300 A / m when 4.0≦d+e≦6.0 is satisfied. The reason why there are iron-based amorphous alloys plotted with × even among those satisfying 15.0≦b+c≦18.0 or those satisfying 4.0≦d+e≦6.0 is the same as that described above.

[0045] 〔summary〕 An object of one aspect of the present invention is to provide a compound having the composition formula Fe a Si b B c P d C e The object of the present invention is to provide an iron-based amorphous alloy having a coercive force Hc of Hc≦300 A / m and a saturation magnetization Ms of Ms≧155 emu / g.

[0046] In order to achieve the above object, the iron-based amorphous alloy according to the first aspect of the present invention is an iron-based amorphous alloy having a composition formula of Fe a Si b B c Pd C e In this iron-based amorphous alloy, when the composition ratios a, b, c, d, and e of each element are expressed as percentages, the sum of a, b, c, d, and e is 97.0≦a+b+c+d+e≦100, the composition ratio a of Fe satisfies 76.0≦a≦80.0, the composition ratio b of Si satisfies 3.0≦b≦6.9, the composition ratio c of B satisfies 9.9≦c≦14.0, the composition ratio d of P satisfies 0.8≦d≦4.6, and the composition ratio e of C satisfies 1.0≦e≦4.1.

[0047] The iron-based amorphous alloy according to the first embodiment exhibits a coercive force Hc that satisfies Hc≦300 A / m and a saturation magnetization Ms that satisfies Ms≧155 emu / g. Therefore, the iron-based amorphous alloy can achieve both a high saturation magnetization Ms and a low coercive force Hc.

[0048] In the iron-based amorphous alloy according to the second aspect of the present invention, in addition to the configuration of the iron-based amorphous alloy according to the first aspect described above, a configuration is adopted in which the composition ratios b and c satisfy 15.0≦b+c≦18.0, and the composition ratios d and e satisfy 4.0≦d+e≦6.0.

[0049] According to the above configuration, it is possible to reliably achieve both a high saturation magnetization Ms and a low coercive force Hc.

[0050] In the iron-based amorphous alloy according to the third aspect of the present invention, in addition to the configuration of the iron-based amorphous alloy according to the first or second aspect described above, a configuration is adopted in which the coercive force Hc satisfies Hc≦300 A / m and the saturation magnetization Ms satisfies Ms≧155 emu / g.

[0051] The coercive force Hc and saturation magnetization Ms of a magnetic material can be easily measured using a magnetic measurement device such as a VSM or a SQUID, so it can be easily confirmed whether or not an iron-based amorphous alloy falls within the scope of the present invention.

[0052] In the iron-based amorphous alloy according to the fourth aspect of the present invention, in addition to the configuration of the iron-based amorphous alloy according to the first or second aspect described above, a configuration is adopted in which the degree of supercooling ΔTx, which is the difference between the crystallization temperature Tx and the glass transition temperature Tg, satisfies ΔTx≧100K, and the saturation magnetization Ms satisfies Ms≧155 emu / g.

[0053] The degree of supercooling ΔTx, defined as Tx - Tg, is used as an index of the ease of amorphization, and in the iron-based amorphous alloy given as an example in Patent Document 1, the maximum value was ΔTx = 52.8 K. The iron-based amorphous alloy according to the fourth aspect satisfies ΔTx ≧ 100 K, and can be said to be an iron-based amorphous alloy that is much easier to amorphize than conventional iron-based amorphous alloys. Therefore, this iron-based amorphous alloy can achieve both high saturation magnetization Ms and low coercive force Hc not only by the SWAP method but also by the water atomization method, making it suitable as a raw material for powder or granular materials.

[0054] In order to solve the above problems, a powder or granular material according to a fifth aspect of the present invention is made of the iron-based amorphous alloy according to the first or second aspect described above.

[0055] The powder material according to the fifth aspect can achieve both high saturation magnetization Ms and low coercive force Hc, similar to the iron-based amorphous alloy according to the first aspect.

[0056] In the powder or granular material according to the sixth aspect of the present invention, in addition to the configuration of the powder or granular material according to the fifth aspect described above, a configuration is adopted in which the average particle size D50 satisfies 0.5 μm≦D50≦50 μm.

[0057] As described above, the iron-based amorphous alloy according to one embodiment of the present invention can be produced as powder having both a high saturation magnetization Ms and a low coercive force Hc, even when the water atomization method is used. Therefore, powder of the iron-based amorphous alloy having an average particle size D50 that satisfies the relationship 0.5 μm≦D50≦50 μm can be easily produced.

[0058] In order to solve the above problems, a compacted powder material according to a seventh aspect of the present invention comprises the powder or granular material according to the fifth or sixth aspect described above.

[0059] The compacted powder material according to the seventh aspect can achieve both high saturation magnetization Ms and low coercive force Hc, similar to the powder and granular material according to the fifth and sixth aspects.

[0060] [Additional Notes] The present invention is not limited to the above-described embodiments, and various modifications are possible within the scope of the claims. Embodiments obtained by appropriately combining the technical means disclosed in different embodiments are also included in the technical scope of the present invention.

Claims

1. Composition formula Fe ａ Si ｂ B ｃ P ｄ C ｅ An iron-based amorphous alloy represented by When the composition ratios a, b, c, d, and e of each element are expressed as percentages, the sum of a, b, c, d, and e is 97.0≦a+b+c+d+e≦100; The composition ratio a of Fe satisfies 76.0≦a≦80.0, The composition ratio b of Si satisfies 3.0≦b≦6.9, the composition ratio c of B satisfies 9.9≦c≦14.0, the P composition ratio d satisfies 0.8≦d≦4.6; An iron-based amorphous alloy in which the composition ratio e of C satisfies 1.0≦e≦4.

1.

2. The composition ratio b and the composition ratio c satisfy 15.0≦b+c≦18.0, 2. The iron-based amorphous alloy according to claim 1, wherein the composition ratio d and the composition ratio e satisfy the relationship 4.0≦d+e≦6.

0.

3. The coercive force Hc satisfies Hc≦300 A / m, and 3. The iron-based amorphous alloy according to claim 1, wherein the saturation magnetization Ms satisfies Ms ≥ 155 emu / g.

4. The degree of supercooling ΔTx, which is the difference between the crystallization temperature Tx and the glass transition temperature Tg, satisfies ΔTx≧100K, and 3. The iron-based amorphous alloy according to claim 1, wherein the saturation magnetization Ms satisfies Ms ≥ 155 emu / g.

5. A powder or granular material made of the iron-based amorphous alloy according to claim 1 or 2.

6. The powder or granular material according to claim 5, wherein the average particle diameter D50 satisfies 0.5 μm≦D50≦50 μm.

7. A compacted powder material comprising the powder or granular material according to claim 5.

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