KR20160030366A - Magnetic compound and method of producing the same - Google Patents

Magnetic compound and method of producing the same Download PDF

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KR20160030366A
KR20160030366A KR1020150125243A KR20150125243A KR20160030366A KR 20160030366 A KR20160030366 A KR 20160030366A KR 1020150125243 A KR1020150125243 A KR 1020150125243A KR 20150125243 A KR20150125243 A KR 20150125243A KR 20160030366 A KR20160030366 A KR 20160030366A
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group
hexagon
element selected
crystal structure
thmn
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KR101733296B1 (en
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노리츠구 사쿠마
아키라 가토
고타 와시오
히데후미 기시모토
마사오 야노
아키라 마나베
마사아키 이토
슌지 스즈키
?지 스즈키
구리마 고바야시
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도요타 지도샤（주）
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    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
    • H01F1/00—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties
    • H01F1/01—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials
    • H01F1/03—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity
    • H01F1/032—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of hard-magnetic materials
    • H01F1/09—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of hard-magnetic materials mixtures of metallic and non-metallic particles; metallic particles having oxide skin
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C30/00—Alloys containing less than 50% by weight of each constituent
    • C22C30/02—Alloys containing less than 50% by weight of each constituent containing copper
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C1/00—Making non-ferrous alloys
    • C22C1/02—Making non-ferrous alloys by melting
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C30/00—Alloys containing less than 50% by weight of each constituent
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
    • H01F1/00—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties
    • H01F1/01—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials
    • H01F1/03—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity
    • H01F1/032—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of hard-magnetic materials
    • H01F1/04—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of hard-magnetic materials metals or alloys
    • H01F1/047—Alloys characterised by their composition
    • H01F1/053—Alloys characterised by their composition containing rare earth metals
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
    • H01F1/00—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties
    • H01F1/01—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials
    • H01F1/03—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity
    • H01F1/032—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of hard-magnetic materials
    • H01F1/04—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of hard-magnetic materials metals or alloys
    • H01F1/047—Alloys characterised by their composition
    • H01F1/053—Alloys characterised by their composition containing rare earth metals
    • H01F1/055—Alloys characterised by their composition containing rare earth metals and magnetic transition metals, e.g. SmCo5
    • H01F1/059—Alloys characterised by their composition containing rare earth metals and magnetic transition metals, e.g. SmCo5 and Va elements, e.g. Sm2Fe17N2
    • H01F1/0593—Alloys characterised by their composition containing rare earth metals and magnetic transition metals, e.g. SmCo5 and Va elements, e.g. Sm2Fe17N2 of tetragonal ThMn12-structure

Abstract

A magnetic compound is expressed by an equation (R_(1-x)Zr_x)_a(Fe_(1-y)Co_y)_bT_cM_dA_e (in the same equation, R is a rare earth element of one type or more, and T is an element of one type or more selected in a group comprising Ti, V, Mo and W, and M is an inevitable impurity element and is an element of one type or more selected in a group comprising Al, Cr, Cu, Ga, Ag and Au; and A is an element of one type or more selected in a group comprising N, C, H and P, and 0 <= x <= 0.5, 0 <= y <= 0.6, 4 <= a <= 20, b = 100-a-c-d, 0 < c < 7, 0 <= d <= 1, 1 <= e <= 18). A main phase of the magnetic compound has a ThMn_12 type crystalline structure, and a volume fraction of α-(Fe,Co) phase is 20% or less.

Description

MAGNETIC COMPOUND AND METHOD OF PRODUCING THE SAME [0002]

The present invention relates to a magnetic compound having a ThMn 12 type crystal structure having a high anisotropic magnetic field and a high saturation magnetization, and a method for producing the same.

The application of permanent magnets has reached a wide range of fields such as electronics, information and communications, medical equipment, machine tools, industrial and automobile motors, and the demand for suppression of carbon dioxide emissions is increasing. In addition, the spread of hybrid cars, In recent years, the development of high-performance permanent magnets has been increasingly expected in terms of improvement of power generation efficiency and the like.

Currently, Nd-Fe-B type magnets that dominate the market as high-performance magnets are also used in magnets for drive motors for HV / EHV. In recent years, development of a new permanent magnet material has been progressed in response to further miniaturization of motors and increase in output (increase in residual magnetization of magnets).

Research on rare earth-iron-based magnetic compounds having a ThMn 12 type crystal structure has been under way as one of development of materials having performance exceeding Nd-Fe-B type magnet. For example, Japanese Laid-Open Patent Publication No. 2004-265907, R (Fe 100-yw Co w Ti y) x Si z A v ( where, R 50 is that with one kind or two kinds of rare earth elements containing Y yisangim X = 10 to 12.5, y = (8.3-1.7 x z) to 12, z = 0.2 to 2.3, v = 0.1 to 3, w = 0 to 30), and is composed of a single-phase structure having a ThMn 12- type crystal structure.

The compound having the composition of the presently proposed NdFe 11 TiN x having the ThMn 12 type crystal structure has a high anisotropic magnetic field but is low in saturation magnetization as compared with the Nd-Fe-B type magnet, .

The present invention provides a magnetic compound having a high anisotropic magnetic field and a high saturation magnetization.

According to the present invention, the following are provided. Equation (1) (R (1-x) Zr x) a (Fe (1-y) Co y) b T c M d A e (In the formula, R is a rare earth element at least one a, T is Ti, V, Mo and W, M is at least one element selected from the group consisting of Al, Cr, Cu, Ga, Ag and Au, A is at least one element selected from the group consisting of N, 0? X? 0.5, 0? Y? 0.6, 4? A? 20, b = 100-a-c-d, 0 <c <7 , 0? D? 1, 1? E? 18) having a ThMn 12 type crystal structure and a volume fraction of? - (Fe, Co) phase of 20% or less.

(2) The magnetic compound according to (1), wherein 0? X? 0.3 and 7? E?

(1) or (2), wherein the relationship between x and c satisfies the range of the region (0 <c <7, x? 0) surrounded by c> -38x + 3.8 and c> (2).

4 formula (R (1-x) Zr x) a (Fe (1-y) Co y) b T c M d (and the above formula, R is a rare earth element at least one, T is Ti, V, Mo and W, M is at least one element selected from the group consisting of inevitable impurity elements and Al, Cr, Cu, Ga, Ag and Au, and 0? X? 0.5, 0 &lt; y &lt; = 0.6, 4 &lt; = a &lt; = 20, and b = 100-a-c-d, 0 &lt; c & At a rate of 1 × 10 2 to 1 × 10 7 K / sec; and a step of pulverizing the solidified alloy obtained by quenching, wherein A is an element selected from the group consisting of N, C, H and P And at least one element selected from the group consisting of iron and iron.

(5) The method of (4), further comprising a step of performing a heat treatment at 800 to 1300 ° C for 2 to 120 hours after the quenching step.

(6) A rare earth element-containing magnetic compound having a ThMn 12 -type crystal structure, wherein the lattice constant (a) of the crystal structure is in the range of 0.850 nm to 0.875 nm and the lattice constant (c) is in the range of 0.480 nm to 0.505 nm , the range of the lattice volume is 3 0.351 ㎚ 3 ~ 0.387 ㎚, wherein Hexagon a, B, to C, respectively Hexagon a: 6-membered ring consisting of Fe with a focus on the rare earth atoms (8i) and Fe (8j) site,

Hexagon B: Fe (8i) -Fe (8i) The dumbbell is composed of two opposing sides and a six-membered ring composed of Fe (8i) and Fe (8j)

Hexagon C: When the center of the hexagon is defined as a six-atom ring composed of Fe (8j) and Fe (8f) sites located on a straight line connecting Fe (8i)

Hexagon A length in the a axis direction: Hex (A) is smaller than 0.611 nm,

The average distance of Fe (8i) -Fe (8i) in hexagonal A is 0.254 nm to 0.288 nm, the average distance of Fe (8j) -Fe (8j) in hexagonal B is 0.242 nm to 0.276 nm, And the average distance of Fe (8f) -Fe (8f) facing the hexagonal C in the hexagonal C with the center of the hexagonal C therebetween is 0.234 nm to 0.268 nm.

Expression (7) (R (1-x) Zr x) a (Fe (1-y) Co y) b T c M d A e (In the formula, R is a rare earth element at least one a, T is Ti, V, Mo and W, M is at least one element selected from the group consisting of Al, Cr, Cu, Ga, Ag and Au, A is at least one element selected from the group consisting of N, C, H and P, and 0? X? 0.5, 0? Y? 0.7, 4? A? 20, b = 100-a-c-d, 0 <c? , 0? D? 1, 1? E? 18) having a ThMn 12 type crystal structure and a volume fraction of? - (Fe, Co) phase of not more than 20%.

According to the present invention, in a compound represented by the formula (R (1-x) Zr x ) a (Fe (1-y) Co y ) b T c M d A e having a ThMn 12 type crystal structure, T The proportion of the magnetic elements of Fe and Co is increased and the magnetization is improved. Further, by adjusting the cooling rate of the molten metal in the manufacturing process, the magnetization can be improved by decreasing the α- (Fe, Co) phase precipitated during cooling and precipitating a large amount of ThMn 12 type crystals. Further, by making the size specified in the above (6), the size balance of each hexagon is improved, and the ThMn 12 type crystal structure can be knitted stably.

The features, advantages, and technical and industrial significance of exemplary embodiments of the present invention will be described below with reference to the accompanying drawings, in which like numerals represent like elements.
1 is a graph showing the stable region of the T component in the RFe 12-x T x compound.
2 is a schematic view of a device used in the strip casting method.
3 is a perspective view schematically showing a ThMn 12 type crystal structure.
4A to 4C are perspective views schematically showing hexagons A, B and C in the ThMn 12 type crystal structure.
5A and 5B are perspective views schematically showing hexagons A, B, and C in the ThMn 12 type crystal structure.
6 is a perspective view schematically showing a change in hexagon size.
Fig. 7 shows the composition and characteristics of the magnets of Examples 1 to 5 and Comparative Examples 1 to 5.
8 is a graph showing the measurement results of saturation magnetization (room temperature) and anisotropic magnetic field in Examples 1 to 5 and Comparative Examples 1 to 5.
Fig. 9 is a graph showing the results of measurement of saturation magnetization (180 deg. C) and anisotropic magnetic field in Examples 1 to 5 and Comparative Examples 1 to 5. Fig.
10 is a graph showing the measurement results of saturation magnetization (room temperature) and anisotropic magnetic field in Examples 6 and 7 and Comparative Examples 6 to 12.
11 is a graph showing the results of measurement of saturation magnetization (180 DEG C) and anisotropic magnetic field in Examples 6 and 7 and Comparative Examples 6 to 12. Fig.
12 shows the compositions of the magnets of Examples 6 and 7 and Comparative Examples 6 to 12, the production method thereof, and the properties thereof.
13 is a reflection electron image of the particles obtained in Examples 6 and 7 and Comparative Example 8. Fig.
14 is a graph showing XRD results of the particles obtained in Examples 6 and 7 and Comparative Example 8. Fig.
15 is a graph showing the relationship between the size of the? - (Fe, Co) phase in the sample before nitriding measured from the SEM image and the volume fraction of? - (Fe, Co) phase in the sample after nitridation.
16 shows the composition of the magnets, the Co substitution ratio, and the characteristics of the magnets of Examples 8 to 15 and Comparative Example 13.
17 is a graph showing the relationship between Co substitution ratio and magnetic properties in Examples 8 to 15 and Comparative Example 13. Fig.
18 is a graph showing the relationship between Co substitution ratio and magnetic properties in Examples 8 to 15 and Comparative Example 13;
19 is a graph showing the relationship between the Co substitution ratio and the Curie temperature in Examples 8 to 15 and Comparative Example 13. Fig.
20 is a graph showing the relationship between the Co substitution ratio and the lattice constant (a) of the crystal structure in Examples 8 to 15 and Comparative Example 13;
21 is a graph showing the relationship between the Co substitution ratio and the lattice constant (c) of the crystal structure in Examples 8 to 15 and Comparative Example 13;
22 is a graph showing the relationship between the Co substitution ratio and the lattice volume (V) in Examples 8 to 15 and Comparative Example 13. Fig.
23 is a graph showing measurement results of saturation magnetization (room temperature) and anisotropic magnetic field in Examples 8 to 15 and Comparative Example 13;
24 is a graph showing the measurement results of saturation magnetization (180 DEG C) and anisotropic magnetic field in Examples 8 to 15 and Comparative Example 13;
Fig. 25 shows the composition and characteristics of the magnets of Example 16 and Comparative Examples 14 to 17. Fig.
26 shows the amounts of Ti of the magnets of Example 16 and Comparative Examples 14 to 17. FIG.
FIG. 27 is a graph showing XRD results in Example 16 and Comparative Examples 14 to 17. FIG.
28 shows the composition and characteristics of the magnets of Examples 17 to 23 and Comparative Examples 18 to 25.
29 shows the composition and characteristics of the magnets of Examples 24 to 27 and Comparative Examples 26 to 31. Fig.
30 is a graph showing the correlation between Ti amount and Zr change in Examples 17 to 27 and Comparative Examples 18 to 31;
31 shows the composition and characteristics of the magnets of Examples 28 to 33 and Comparative Examples 32 and 33. Fig.
32 is a graph showing the relationship between the amount of N and the lattice constant (a) of the crystal structure in Examples 28 to 33 and Comparative Examples 32 to 33;
33 is a graph showing the relationship between the amount of N and the lattice constant (c) of the crystal structure in Examples 28 to 33 and Comparative Examples 32 to 33;
34 is a graph showing the relationship between the N amount and the lattice volume (V) in Examples 28 to 33 and Comparative Examples 32 to 33;

Hereinafter, the magnetic compound according to the present invention will be described in detail. The magnetic compound of the present invention is represented by the following formula (R (1-x) Zr x ) a (Fe (1-y) Co y ) b T c M d A e , do.

(R) R is a rare earth element and is an essential component in the magnetic compound of the present invention because it exhibits permanent magnet properties. Specifically, R is at least one element selected from among Y, La, Ce, Pr, Nd, Sm and Eu, and it is preferable to use Pr, Nd and Sm. The compounding amount a of R is 4 atomic% or more and 20 atomic% or less. When the content is less than 4 atomic%, precipitation of the Fe phase becomes remarkable and the volume fraction of the Fe phase after the heat treatment can not be lowered. When the content is more than 20 atomic%, the grain boundary phase is excessively large.

(Zr) Zr is effective for stabilizing the ThMn 12 type crystal phase by replacing a part of the rare earth element. That is, the Zr element is substituted with an R element in the ThMn 12 type crystal, and shrinkage of the crystal lattice occurs. As a result, when the alloy is heated to a high temperature or a nitrogen atom or the like is introduced into the crystal lattice, it has an effect of stably maintaining the ThMn 12 type crystal phase. On the other hand, in terms of magnetic properties, since the strong magnetic anisotropy derived from the R element is diluted by Zr substitution, it is necessary to determine the amount of Zr in terms of crystal stability and magnetic properties. However, in the present invention, the addition of Zr is not essential. When the amount of Zr is 0, the ThMn 12 type crystal phase can be stabilized by adjustment of the composition of the alloy and heat treatment or the like, and the anisotropic magnetic field becomes high. However, if the substitution amount of Zr exceeds 0.5, the anisotropic magnetic field is significantly lowered. The amount of Zr (x) is preferably 0? X? 0.3.

(T) T is at least one element selected from the group consisting of Ti, V, Mo and W. 1 shows the stabilization region of the T element in the RFe 12-x T x compound (KHJ Buschow, Rep.Prog.Phys. 54, 1123 (1991)), It is known that the addition of Ti, V, Mo and W as the three elements stabilizes the ThMn 12 type crystal structure and exhibits excellent magnetic properties.

Conventionally, in order to obtain the stabilizing effect of the T component, since the ThMn 12 type crystal structure is formed by adding to the alloy in a larger amount than the necessary amount, the content of the Fe component constituting the compound in the alloy is lowered, The occupying sites of the Fe atoms are replaced with, for example, Ti atoms, and the overall magnetization is lowered. In order to improve the magnetization, the amount of Ti to be added is reduced. In this case, the stabilization of the ThMn 12 type crystal structure is inhibited. Although RFe 11 Ti has been reported as a conventional RFe 12-x Ti x compound, no compounds have been reported wherein x is less than 1, i.e., Ti is less than 7 atomic%.

Stabilization of the ThMn 12 -type crystal structure is inhibited when Ti which stabilizes the ThMn 12 -type crystal structure is reduced, and α- (Fe, Co) which is an obstacle to the anisotropic magnetic field or coercive force is precipitated. The present invention suppresses precipitation amount of? - (Fe, Co) by controlling the cooling rate of the molten alloy and makes the volume fraction of? - (Fe, Co) , It is possible to stably produce the ThMn 12 phase having high magnetic properties.

The compounding amount of the T component is such that x is less than 1, that is, less than 7 atomic% in the RFe 12-x Ti x compound. If it is 7 atomic% or more, the content of the Fe component constituting the compound is lowered and the overall magnetization is lowered.

In the compound represented by the formula (R (1-x) Zr x ) a (Fe (1-y) Co y ) b T c M d A e of the present invention, the Zr amount (x) and the T amount (c) (0 <c <7, x? 0) surrounded by c> -38x + 3.8 and c> 6.3x + 0.65.

(M) M is an inevitable impurity element and at least one element selected from the group consisting of Al, Cr, Cu, Ga, Ag and Au. This inevitable impurity element means a element that enters the raw material or an element that is mixed in the manufacturing process, and specifically includes Si and Mn. M is a contribution to the viscosity, the melting point of the phase other than the particles, or suppressed ThMn 12-form crystal of the growth of ThMn 12 type crystals (for example, the grain boundary), however, in the present invention is not essential. The amount (d) of M is less than 1 atomic%. If the content is more than 1 atomic%, the content of the Fe component constituting the compound in the alloy is lowered and the overall magnetization is lowered.

(A) A is at least one element selected from the group consisting of N, C, H and P. A can be expanded by the grating on the ThMn 12 by breaking the crystal lattice on the ThMn 12, improving the amount of characteristics of anisotropic magnetic field, saturation magnetization. The blend amount (e) of A is 1 at% or more and 18 at% or less. If the content is less than 1 atomic%, the effect can not be exhibited. If the content exceeds 18 atomic%, the content of the Fe component constituting the compound in the alloy is lowered, and the stability of the ThMn 12 phase is impaired and partly decomposed to lower the overall magnetization . The amount (e) of A is preferably 7? E? 14.

(Fe and Co) The compound of the present invention is Fe other than the above elements, and a part of Fe may be substituted with Co. By replacing Co with Fe, an increase in spontaneous magnetization can be caused by the slater magnetic poling rule, so that both characteristics of anisotropic magnetic field and saturation magnetization can be improved. However, when the substitution amount of Co exceeds 0.6, the effect can not be exerted. Further, substitution of Fe with Co increases the Curie point of the compound, and therefore has an effect of suppressing the decrease in magnetization at high temperature.

The magnetic compound of the present invention is represented by the above formula and is characterized by having a ThMn 12 type crystal structure. The ThMn 12 -type crystal structure is tetragonal and the values of 2? In the XRD measurement result are 29.801 °, 36.554 °, 42.082 °, 42.368 ° and 43.219 ° (± 0.5 °), respectively. The magnetic compound of the present invention is characterized in that the volume fraction of the? - (Fe, Co) phase is 20% or less. This volume fraction was calculated by the area ratio of? - (Fe, Co) phase in the cross section by image analysis by observing the sample with OM or SEM-EDX by resin burial polishing. Assuming that the tissue is not randomly oriented, the following relationship is established between the average area ratio (A) and the volume ratio (V). A? V Therefore, in the present invention, the area ratio of the? - (Fe, Co) phase measured in this way is defined as a volume fraction.

As described above, the magnetic compound of the present invention can improve the magnetization by reducing the T component as compared with the conventional RFe 11 Ti-type compound, and by reducing the volume fraction of the? - (Fe, Co) , It is possible to remarkably improve both characteristics of the saturation magnetization.

(Manufacturing Method) The magnetic compound of the present invention can be basically produced by a conventional manufacturing method such as a mold casting method or an arc melting method. However, in the conventional method, the magnetic compound other than the ThMn 12 phase (α- (Fe, Co ) Phase is precipitated, and the anisotropic magnetic field and the saturation magnetization are lowered. It is noted that the temperature <? - (Fe, Co) at which the ThMn 12- type crystal is precipitated is precipitated, and in the present invention, the molten alloy is quenched at a rate of 1 × 10 2 to 1 × 10 7 K / sec , and precipitation of α- (Fe, Co) is suppressed so that the FeMnO 3 crystal does not stay in the vicinity of the temperature at which α- (Fe, Co) is precipitated.

As the cooling method, for example, the apparatus 10 as shown in Fig. 2 can be used to cool it at a predetermined speed by a strip casting method. In this apparatus 10, the alloy raw material is dissolved in the melting furnace 11 to have a composition represented by the formula (R (1-x) Zr x ) a (Fe (1-y) Co y ) b T c M d The molten metal 12 of the alloy is prepared. T is at least one element selected from the group consisting of Ti, V, Mo and W, M is an inevitable impurity element, and Al, Cr, Cu, Ga, Ag and Au 0? X? 0.5, 0? Y? 0.6, 4? A? 20, b = 100-a-c-d, 0 <c <7, 0? D? This molten metal 12 is supplied to the tundish 13 at a constant supply amount. The molten metal 12 supplied to the tundish 13 is supplied to the cooling roll 14 by its own weight from the end of the tundish 13.

The tundish 13 is made of ceramics or the like and temporarily stores the molten metal 12 continuously supplied from the melting furnace 11 at a predetermined flow rate and stores the molten metal 12 into the cooling roll 14, (Rectified). The tundish 13 also has a function of adjusting the temperature of the molten metal 12 immediately before reaching the cooling roll 14. [

The cooling roll 14 is made of a material having a high thermal conductivity such as copper or chromium. The surface of the roll is subjected to chromium plating or the like in order to prevent erosion with the hot molten metal. This roll can be rotated in the direction of the arrow at a predetermined rotational speed by a driving device not shown. By controlling the rotation speed, the cooling rate of the molten metal can be controlled at a rate of 1 x 10 2 to 1 x 10 7 K / sec.

The solidified alloy melt 12 is cooled on the outer periphery of the cooling roll 14 and becomes a solidified alloy 15 in the form of a flake, peeled off from the cooling roll 14, crushed, and recovered in the recovery device.

In the present invention, the particles obtained in the above step may be subjected to a heat treatment at 800 to 1300 占 폚 for 2 to 120 hours. By this heat treatment, the ThMn 12 phase is homogenized, and both characteristics of the anisotropic magnetic field and the saturation magnetization are further improved.

After grinding, the recovered alloy is infiltrated with element A (A is at least one element selected from the group consisting of N, C, H and P). Specifically, when nitrogen is used as the element A, nitrogen gas, ammonia gas, or the like is used as a nitrogen source, and the substrate is subjected to heat treatment at a temperature of 200 to 600 DEG C for 1 to 24 hours to nitride the substrate. When carbon is used as the element A, heat treatment is performed at 300 to 600 ° C. for 1 to 24 hours using a C 2 H 2 (CH 4 , C 3 H 8 , CO) gas or a heat decomposition gas of methanol as a carbon source And carbonize it. In addition, solid carburization using carbon powder or molten salt carburization using KCN or NaCN may be performed. H and P can be subjected to ordinary hydrogenation and printing.

(Crystal Structure) The magnetic compound of the present invention is a rare earth element-containing magnetic compound having a ThMn 12 type tetragonal crystal structure as shown in Fig. The lattice constant (a) of the crystal structure is in the range of 0.850 nm to 0.875 nm, the lattice constant (c) is in the range of 0.480 nm to 0.505 nm, and the lattice volume is in the range of 0.351 nm 3 to 0.387 nm 3 . 4A to 4C and FIGS. 5A and 5B, hexagonal A, B and C are referred to as hexagonal A, and a hexagonal ring (also referred to as a hexagonal ring) consisting of Fe (8i) and Fe (Fig. 4B and Fig. 5A) composed of Fe (8i) and Fe (8j) sites, with hexagonal B: Fe (8i) , Hexagon C: a hexagon ring (Fig. 4C and Fig. 5B) composed of Fe (8j) and Fe (8f) sites located on the straight line connecting the center of Fe (8i) (8i) -Fe (8i) in hexagon A is 0.254 nm to 0.288 nm, and the hexagonal B has Fe (8j) (8f) -Fe (8f) having an average distance of 0.242 nm to 0.276 nm and having an average distance of Fe (8f) -Fe (8f) facing the center of the hexagonal C in the hexagonal C between 0.234 nm and 0.268 nm The compounds.

As shown in FIG. 6, the magnetic compound of the present invention has a small amount of stabilizing element T (for example, Ti) and substitutes for Fe with a large atomic radius from Fe to a conventional magnetic compound, The balance is poor, but it is adjusted by supplementing Zr with a smaller atomic radius than Nd.

The magnetic powder of the present invention is represented by the following formula (R (1-x) Zr x ) a (Fe (1-y) Co y ) b T c M d A e , T is at least one element selected from the group consisting of Ti, V, Mo and W, M is at least one element selected from the group consisting of inevitable impurity elements and elements selected from the group consisting of Al, Cr, Cu, Ga, Ag and Au Wherein A is at least one element selected from the group consisting of N, C, H and P and 0? X? 0.5, 0? Y? 0.7, 4? A? 20, b = 100- c-d, 0 &lt; c? 7, 0? d? 1 and 1? e? 18, and has a ThMn 12 type crystal structure and a volume fraction? - (Fe, Co) of 20% or less.

Examples 1 to 5 and Comparative Examples 2 to 5

A molten alloy for the purpose of producing a compound having the composition shown in Fig. 7 below was prepared and rapidly quenched at a rate of 10 4 K / sec by a strip cast method to prepare rapidly quenched flakes. Followed by heat treatment for 4 hours. Subsequently, the flakes were pulverized in an Ar atmosphere using a cutter mill to recover particles having a particle diameter of 30 to 75 mu m. The size and area ratio of? - (Fe, Co) phase were measured from the SEM image (reflected electron image) of the obtained particles, and the volume ratio was calculated using the area ratio = the volume ratio. Subsequently, the obtained particles were nitrided in a nitrogen gas having a purity of 99.99% for 4 hours at 450 占 폚. (VSM) and crystal structure analysis (XRD) of the obtained particles were carried out and the size of the α- (Fe, Co) phase in the sample before nitriding measured from the SEM image based on the graph of FIG. The volume fraction of the? - (Fe, Co) phase after nitridation was calculated from the graph showing the relationship of the volume fraction of? - (Fe, Co) phase in the sample. The results are shown in Figs. 7 and 8 and Fig.

Comparative Example 1

A molten alloy for the purpose of producing a compound having the composition shown in Fig. 7 below was prepared and rapidly quenched at a rate of 10 4 K / sec by a strip cast method to prepare a quenched flake, By using a cutter mill to recover particles having a particle diameter of 30 mu m or less. The obtained particles were molded in a magnetic field, sintered at 1050 占 폚 for 3 hours, and then heat-treated at 900 占 폚 for 1 hour and further at 600 占 폚 for 1 hour. The magnetic properties evaluation (VSM) and the crystal structure analysis (XRD) of the obtained magnets were carried out. The results are shown in Figs. 7, 8 and 9. Fig.

As can be seen from the results shown in Fig. 7 and Fig. 8 and Fig. 9, when the amount of Ti is less than 7 at%, the saturation magnetization is improved (especially at a high temperature), and the anisotropic magnetic field above the NdFeB magnet and the saturation magnetization (Examples 1 to 5). Also, the addition of Co showed an increase in saturation magnetization, particularly at a high temperature (comparison between Examples 1 and 2).

Examples 6 and 7

A molten alloy of the composition shown in Fig. 12 for the purpose of producing a compound was prepared and rapidly quenched at a rate of 10 4 K / sec by a strip cast method to prepare a quenched flake. In Example 7, heat treatment was then performed in an Ar atmosphere at 1200 DEG C for 4 hours. Subsequently, the flakes were pulverized in an Ar atmosphere using a cutter mill to recover particles having a particle diameter of 30 to 75 mu m. The size and area ratio of? - (Fe, Co) phase were measured for the obtained particles in the same manner as in Example 1, and the volume ratio was calculated. Subsequently, the obtained particles were nitrided in a nitrogen gas having a purity of 99.99% for 4 hours at 450 占 폚. (VSM) and crystal structure analysis (XRD) of the obtained particles were carried out, and the volume fraction of the? - (Fe, Co) phase after nitridation was calculated in the same manner as in Example 1. The results are shown in Fig. 12, Fig. 10, and Fig.

Comparative Examples 6 to 10

An alloy for the purpose of producing a compound having the composition shown in Fig. 12 below was arc-dissolved and cooled at a rate of 50 K / sec to prepare a flake. In Comparative Examples 7, 8 and 10, heat treatment was then performed in an Ar atmosphere at 1100 DEG C for 4 hours. Subsequently, the flakes were pulverized in an Ar atmosphere using a cutter mill to recover particles having a particle diameter of 30 to 75 mu m. The obtained particles were nitrided in a nitrogen gas having a purity of 99.99% for 4 hours at 450 占 폚. (VSM) and crystal structure analysis (XRD) of the obtained particles were carried out, and the results of measurement of the size and volume fraction of the? - (Fe, Co) phase measured in the same manner as in Example 1 were also shown. 12 and Fig. 10 and Fig.

Comparative Examples 11 and 12

A molten alloy for the purpose of producing a compound having the composition shown in FIG. 12 was prepared and quenched at a rate of 10 4 K / sec by a strip cast method to prepare a quenched flake. In Comparative Example 12, heat treatment was then performed in an Ar atmosphere at 1100 DEG C for 4 hours. Subsequently, the flakes were pulverized in an Ar atmosphere using a cutter mill to recover particles having a particle diameter of 30 to 75 mu m. The obtained particles were nitrided in a nitrogen gas having a purity of 99.99% for 4 hours at 450 占 폚. (VSM) and crystal structure analysis (XRD) of the obtained particles were carried out, and the results of measurement of the size and volume fraction of the? - (Fe, Co) phase measured in the same manner as in Example 1 were also shown. 12 and Fig. 10 and Fig.

Fig. 13 shows reflected electron images of the particles obtained in Examples 6 and 7 and Comparative Example 8. In Comparative Example 8 in which arc melting was performed, Fe was largely precipitated and the structure was heterogeneous. On the other hand, In EPMA, segregation of tissue was not confirmed. 14 shows the XRD results of the particles obtained in Examples 6 and 7 and Comparative Example 8. The results of XRD of Comparative Example 8 (arc dissolution)? Example 6 (quench)? Example 7 (quenching + homogenization heat treatment) The peak strength of? -Fe is lowered.

From the above results, it is considered that the quenching leads to the refinement of the? - (Fe, Co) phase and the decrease in the amount of precipitation, and further the fineness and homogeneity of the entire structure. Further, it is considered that the microstructure homogenization proceeds and the α- (Fe, Co) phase is also reduced by further performing the heat treatment after cooling, thereby further improving the characteristics. As described above, even when the amount of Ti is reduced from 7 at% to 4 at%, precipitation of the? - (Fe, Co) phase is suppressed by the quenching treatment and the homogenization heat treatment and the anisotropic magnetic field of the conventional one is expressed, It is possible to produce a magnetic compound having a TnMn 12 type crystal structure that is highly compatible with the characteristics of the TnMn 12 type crystal structure.

Examples 8 to 15 and Comparative Example 13

A molten alloy for the purpose of producing a compound having the composition shown in Fig. 16 below was prepared and rapidly quenched at a rate of 10 4 K / sec by a strip casting method to prepare a quenched flake, And the cobalt amount (y) was changed in Nd 7.7 (Fe (1-y) Co y ) 86.1 Ti 6.2 N 7.7 ) for 4 hours. Subsequently, the flakes were pulverized in an Ar atmosphere using a cutter mill to recover particles having a particle diameter of 30 μm or less. The obtained particles were nitrided at 450 DEG C for 4 to 24 hours in a nitrogen gas having a purity of 99.99%. Evaluation of magnetic properties (VSM) and crystal structure analysis (XRD) of the obtained particles were carried out. The results are shown in Fig. 16 and Fig. 17 to Fig.

As can be seen from the experimental results, the anisotropic magnetic field showed a high value without being influenced by the Co substitution rate. On the other hand, the saturation magnetization exhibited the maximum saturation magnetization with a Co substitution ratio of about 0.3, and showed a tendency to decrease at y = 0.7 or more. With respect to the Curie point, it increased with the increase of the amount of Co (the measurement was impossible due to limitations on the apparatus for y = 0.5 or more). Therefore, it can be seen that the range of 0? Y? 0.7 is preferable for Co.

20 to 22 show the relationship between the Co substitution ratio and the lattice constant (a), the lattice constant (c) and the lattice volume (V) of the crystal structure. From this result, it can be seen that the range of the lattice constant (a) is 0.850 nm to 0.875 nm, the range of the lattice constant (c) is 0.480 nm to 0.505 nm, and the range of the lattice volume (V) is 0.351 nm 3 to 0.387 nm 3 .

23 and 24 show the relationship between anisotropic magnetic field and saturation magnetization. Sufficiently high magnetic properties were obtained in the samples of the examples of the present invention.

(8i) -Fe (8i) -Fe (8i) site consisting of Fe (8i) and Fe (8j) sites centering on rare earth atom R, hexagon A, B and C in the crystal structure, 8i) dumbbell is located on opposite sides and a six-atom ring consisting of Fe (8i) and Fe (8j) sites, hexagon C: the center of which is located on the straight line of Fe (8i) ) and when defined as the 6-membered ring consisting of Fe (8f) site, Hexagon a of length Hex (a in the a-axis direction), from the FIG. 7 NdFe 11 TiN (Nd 7.7 Fe 92.3 Ti 7.7 N 7.7) of the following composition Which is smaller than 0.611 nm.

Example 16 and Comparative Examples 14 to 17

A molten alloy for the purpose of producing a compound having the composition shown in Fig. 25 below was prepared and rapidly quenched at a rate of 10 4 K / sec by a strip cast method to prepare rapidly quenched flakes. The titanium amount (c) was changed in Nd 7.7 (Fe 0.75 Co 0.25 ) 92.30-c Ti c N 7.7 ). Subsequently, the flakes were pulverized in an Ar atmosphere using a cutter mill to recover particles having a particle diameter of 30 μm or less. The obtained particles were nitrided in a nitrogen gas having a purity of 99.99% for 4 hours at 450 占 폚. Evaluation of magnetic properties (VSM) and crystal structure analysis (XRD) of the obtained particles were carried out. The results are shown in Fig. 25 and Fig.

From the results of crystal structure analysis by XRD shown in Fig. 27, it was found that 1-12 phases were formed when Ti amount was 5.8 at% or more. On the other hand, 3-29 phase was generated when Ti amount was 3.8 at%, and 2-17 phase was generated when Ti amount was 1.9 at% or less. 26 shows the relationship between Ti amount change and crystal structure change.

Examples 17 to 27 and Comparative Examples 18 to 31

A molten alloy for the purpose of producing a compound having the composition shown in Fig. 28 and Fig. 29 below was prepared and rapidly quenched at a rate of 10 4 K / sec by a strip casting method to prepare a quenched flake, The Zr substitution ratio (x) and titanium amount (c) were changed in the Nd ( 7.7-x ) Zr x Fe 0.75 Co 0.25 92.30-c Ti c N 7.7 subjected to the heat treatment at 1200 ° C for 4 hours. Subsequently, the flakes were pulverized in an Ar atmosphere using a cutter mill to recover particles having a particle diameter of 30 μm or less. The obtained particles were nitrided at 450 DEG C for 4 to 16 hours in a nitrogen gas having a purity of 99.99%. Evaluation of magnetic properties (VSM) and crystal structure analysis (XRD) of the obtained particles were carried out. The results are shown in Fig. 28, Fig. 29 and Fig.

From the results shown in FIG. 28 and FIG. 29, it was found that the forming ability of 1-12 phase was lowered with decreasing Ti amount, but increased with the increase of Zr addition amount. From the results shown in Fig. 30, it can be seen that in the region where the 1-12 phase can be formed, c> -38x + 3.8 and c> 6.3x + 0.65 are satisfied between the Zr substitution ratio (x) (0 &lt; c &lt; 7, x &gt; 0). This is because, as shown in FIG. 6, when the amount of Ti is lowered, the 8i site of hexagon A is substituted with an Fe atom having a smaller atomic radius from the Ti atom, so that the size balance of hexagon A is lowered. However, it is considered that 1-12 phase could be produced irrespective of lowering of Ti amount by replenishing the size balance by substituting Zr having smaller atomic radius than Nd atom.

Examples 28 to 33 and Comparative Examples 32 to 33

A molten alloy for the purpose of producing a compound having the composition shown in Fig. 31 below was prepared and rapidly quenched at a rate of 10 4 K / sec by a strip cast method to prepare rapidly quenched flakes. Followed by heat treatment for 4 hours. Subsequently, the flakes were pulverized in an Ar atmosphere using a cutter mill to recover particles having a particle diameter of 30 μm or less. The obtained particles were nitrided at 450 DEG C for 4 hours in a nitrogen gas having a purity of 99.99% (Nd 7.7 (Fe 0.75 Co 0.25 ) 86.5 Ti 5.8 N e , and the nitrogen content in Nd 7.7 Fe 86.5 Ti 5.8 N e e). Evaluation of magnetic properties (VSM) and crystal structure analysis (XRD) of the obtained particles were carried out. The results are shown in Figs.

It was confirmed that the lattice constant increases together with the increase in the amount of N in both the a-axis direction and the c-axis direction. It was also found that nitrogen penetrated to about 15.4 at% without destroying the crystal structure. In addition, the increase in the saturation magnetization and the anisotropic magnetic field accompanied with the increase in the amount of N was also confirmed in the same manner as described above.

Claims (7)

(R (1-x) Zr x ) a (Fe (1-y) Co y ) b T c M d A e ,
A magnetic compound having a ThMn 12 type crystal structure and having a volume fraction of? - (Fe, Co) phase of not more than 20%.
Here, R is at least one rare earth element,
T is at least one element selected from the group consisting of Ti, V, Mo and W,
M is at least one element selected from the group consisting of inevitable impurity elements and Al, Cr, Cu, Ga, Ag and Au,
A is at least one element selected from the group consisting of N, C, H and P,
0? X? 0.5,
0? Y? 0.6,
4? A? 20,
b = 100-a-c-d,
0 &lt; c &lt; 7,
0? D? 1,
1? E? 18. The method according to claim 1,
0? X? 0.3 and 7? E? 14. 3. The method according to claim 1 or 2,
Satisfies the range of 0 <c <7, x? 0, c> -38x + 3.8 and c> 6.3x + 0.65. A method for producing a magnetic compound according to claim 1,
Preparing a molten metal alloy having a composition represented by the following formula (R (1-x) Zr x ) a (Fe (1-y) Co y ) b T c M d ;
A step of quenching the molten metal at a rate of 1 × 10 2 to 1 × 10 7 K / sec,
And a step of crushing the solidified alloy obtained by quenching and then causing the element A to enter.
Here, R is at least one rare earth element,
T is at least one element selected from the group consisting of Ti, V, Mo and W,
M is at least one element selected from the group consisting of inevitable impurity elements and Al, Cr, Cu, Ga, Ag and Au,
0? X? 0.5,
0? Y? 0.6,
4? A? 20,
b = 100-a-c-d,
0 &lt; c &lt; 7,
0? D? 1,
A is at least one element selected from the group consisting of N, C, H and P. 5. The method of claim 4,
Further comprising the step of subjecting the quenching step to a heat treatment at 800 to 1300 ° C for 2 to 120 hours. As the rare earth element-containing magnetic compound having a ThMn 12- type crystal structure,
The range of the lattice constant (a) of the crystal structure is 0.850 nm to 0.875 nm,
The lattice constant (c) ranges from 0.480 nm to 0.505 nm,
The range of the lattice volume is 0.351 nm 3 to 0.387 nm 3 ,
Here, hexagon A, B, and C are
Hexagon A: a six-membered ring consisting of Fe (8i) and Fe (8j) sites centered on rare earth atoms,
Hexagon B: Fe (8i) -Fe (8i) The dumbbell is composed of two opposing sides and a six-membered ring composed of Fe (8i) and Fe (8j)
Hexagon C: When the center of the hexagon is defined as a six-atom ring composed of Fe (8j) and Fe (8f) sites located on a straight line connecting Fe (8i)
The length in the a-axis direction of hexagon A is smaller than 0.611 nm,
In hexagon A, the average distance between Fe (8i) -Fe (8i) is 0.254 nm to 0.288 nm,
The average distance between Fe (8j) -Fe (8j) in hexagonal B is 0.242 nm to 0.276 nm,
Wherein an average distance between Fe (8f) -Fe (8f) facing the center of hexagon C in hexagonal C is 0.234 nm to 0.268 nm. (R (1-x) Zr x ) a (Fe (1-y) Co y ) b T c M d A e ,
A magnetic powder having a ThMn 12 type crystal structure and having a volume fraction of? - (Fe, Co) phase of not more than 20%.
Here, R is at least one rare earth element,
T is at least one element selected from the group consisting of Ti, V, Mo and W,
M is at least one element selected from the group consisting of inevitable impurity elements and Al, Cr, Cu, Ga, Ag and Au,
A is at least one element selected from the group consisting of N, C, H and P,
0? X? 0.5,
0? Y? 0.7,
4? A? 20,
b = 100-a-c-d,
0 &lt; c &lt; 7,
0? D? 1,
1? E? 18.
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WO2020032547A1 (en) * 2018-08-10 2020-02-13 주식회사 엘지화학 Magnetic powder and method for producing magnetic powder
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Family Cites Families (6)

* Cited by examiner, † Cited by third party
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