JP3200201B2 - Nitride magnetic powder and method for producing the same - Google Patents

Description

DETAILED DESCRIPTION OF THE INVENTION

[0001]

BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a rare earth-iron-nitrogen based magnetic material having high magnetic properties and excellent oxidation resistance, and particularly to a magnetic material most suitable for use in small motors and actuators.

[0002]

2. Description of the Related Art Magnetic materials are used in a wide range of fields from home appliances, audio products, automobile parts and peripheral devices of computers, and their importance as electronic materials is increasing year by year. In particular, recently, there has been a demand for miniaturization and high efficiency of various electric and electronic devices, so that a magnetic material with higher performance is required.

[0003] In response to the demands of this era, Sm-Co based, N
The demand for rare earth magnetic materials such as d-Fe-B is rapidly increasing. However, the Sm-Co system has a problem that the supply of the material is unstable and the cost of the material is high, and the Nd-Fe-B system has a problem in that the heat resistance and the corrosion resistance are inferior. On the other hand, as a new rare earth magnetic material, a rare earth-iron-nitrogen magnetic material has been invented. This material has a high magnetization, an anisotropic magnetic field, and a high Curie point.
It is expected as a magnetic material that compensates for the drawbacks of the d-Fe-B system.

However, when a rare earth-iron-nitrogen-based material is used after being finely ground, its surface is oxidized and its coercive force is reduced, so that the material cannot exhibit its intrinsic high magnetic properties. . As a countermeasure, a method of improving the characteristics of the magnetic material by adding a metal component M to a rare earth-iron-nitrogen-based material can be considered. The material having the rare earth-iron-M-nitrogen composition is disclosed in JP-A-61-9551 (M = P
t, Pd, Rh, Re, Ru).

The material disclosed in Japanese Patent Application Laid-Open No. 61-9551 is a material containing a large amount of iron nitride, α-iron, rare earth nitride and M alone in production, and therefore has remarkable magnetic properties such as coercive force. Deteriorating, these materials do not become high performance magnet materials. For this reason, a rare earth-iron-M-nitrogen-based material having a rhombohedral or hexahedral crystal structure having high magnetic properties and excellent oxidation resistance is not known at present, and its appearance is strongly desired. ing.

[0006]

DISCLOSURE OF THE INVENTION The present invention relates to a rare-earth-iron-nitrogen-based material having a rhombohedral or hexagonal crystal structure in which a metal element M coexists to provide high magnetic properties and excellent oxidation resistance. The present invention provides a rare earth-iron-M-nitrogen composition magnetic material having the following characteristics:

[0007]

In order to obtain a rare earth-iron-nitrogen based magnetic material having high magnetic properties and oxidation resistance, the present inventors have conducted intensive studies on a system obtained by adding various elements (M) to a mother alloy. The present inventors have found a magnetic material having a composition of rare earth (R) -iron (Fe) -M-nitrogen (N) having a high magnetic property and excellent oxidation resistance and a crystal structure, and have accomplished the present invention.

That is, the present invention relates to (1) a compound represented by the general formula Rα (Fe
_{(1- γ) Mγ) (100-} α - β) is a magnetic material represented by N.beta, at least one kind of rare earth element R, including the Y, M is, Re, Ru, Os, Rh , Ir, Pd , P
At least one of the elements t and Au, α and β are atomic percentages 3 ≦ α ≦ 203 3 ≦ β ≦ 30 γ is an atomic ratio of 0.001 ≦ γ ≦ 0.5 and R, Fe , M and N are characterized in that the phase containing rhombohedral or hexagonal crystal structure is contained therein; and (2) 0.01 to 50% of Fe which is a component of the magnetic material described above. A magnetic material characterized by having a composition in which atomic% is replaced by Co, and (3) a general formula Rα _{/ (100-} β ₎ (Fe _(1- γ ₎ Mγ) _(100- α _- β)
_{) / (100-} β ₎ in an atmosphere containing at least one of nitrogen gas and ammonia gas,
The method for producing a magnetic material according to the above (1) or (2), wherein the heat treatment is performed at a temperature of 650 ° C.

Hereinafter, the present invention will be described in detail. As the rare earth (R), Y, La, Ce, Pr, Nd, P
m, Sm, Eu, Gd, Tb, Dy, Ho, Er, T
It is sufficient that at least one of m, Yb and Lu is included. Therefore, a mixture of two or more rare earth elements such as misch metal and dymium may be used. Preferred rare earths include Y, Ce, Pr, Nd, Sm, Gd, Dy, E
r. More preferably, Y, Ce, Pr, Nd,
Sm.

[0010] The R may have a purity that can be obtained by industrial production, and impurities unavoidable in production, such as O, H,
C, Al, Si, F, Na, Mg, Ca, Li and the like may be present. Iron (Fe) is the basic composition of the present magnetic material that is responsible for ferromagnetism, and
50 atomic% may be replaced by Co. In this case, a material having a high Curie point and high magnetization and high oxidation resistance is obtained. Hereinafter, a description of an iron component includes a case where Co is replaced by up to 50 atomic% with Co. Furthermore, Re, Ru, Os, which are essential components for exhibiting the effects of the present invention,
One of the elements (M) of Rh, Ir, Pd, Pt, and Au
Seed or two or more kinds with respect to the total amount of Fe and M
Coexist in the range of 50 atomic%.

The composition of the R-Fe-MN-based magnetic material in the present invention is such that the R component is 3 to 20 atomic%, the iron and M components together are 50 to 94 atomic%, and N is 3 to 30 atomic%. Must be in range. When the R component is less than 3 atomic%,
The soft magnetic phase containing a large amount of iron component is separated, and the coercive force of the nitride is reduced, so that a practical permanent magnet cannot be obtained. The R component is 2
If it exceeds 0 atomic%, the residual magnetic flux density is undesirably reduced. The composition of the R component is preferably 5 to 15 atomic%, and more preferably 7 to 12 atomic%.

The coexistence amount of M in iron must be in the range of 0.001 to 0.5 in atomic ratio to the total of iron and M components. If it exceeds 0.5, the saturation magnetization is lowered, which is not preferable. If it is less than 0.001, the effect of adding M on the oxidation resistance is hardly obtained. Further, since the metal radius of Au is significantly different from that of Fe, it is desirable that the M coexistence amount is 0.3 or less in order to obtain a stable rhombohedral or hexagonal system.

Considering the balance of magnetic properties such as magnetization and coercive force, the M substitution amount is preferably 0.01 to
0.2. Re, Ru, Os, R as M component
h, Ir, Pd, Pt, Au, Mn, Cr, N
i, Li, Na, K, Mg, Ca, Sr, Ba, Ti,
Zr, Hf, V, Nb, Ta, Mo, W, Cu, Ag,
Zn, B, Al, Ga, In, C, Si, Ge, Sn,
One or more of the elements Pb and Bi (M ′ component) may be added, but their contents are Re, R
u, Os, Rh, Ir, Pd, Pt, and Au without exceeding the total amount, and Re, Ru, Os, Rh, Ir, P
The total amount of d, Pt, and Au must be within the range of the γ value.

The crystal structure of the main phase of the R—Fe—M—N magnetic material must contain at least one of hexagonal and rhombohedral in a volume fraction of 50% or more of the whole. The main phase referred to herein is a phase containing at least R, Fe and N and having a rhombohedral or hexagonal crystal structure, and a phase having a composition and crystal structure other than that is called a subphase. .

For example, RFe _12-X M ′ _X N _{y is used} as a subphase.
It may contain a highly magnetic nitride phase that takes a tetragonal phase such as a phase, but in order to sufficiently exhibit the oxidation resistance effect of the present invention, the volume fraction of the magnetic material of the present invention must be Must not be exceeded. If the volume fraction exceeds 75%,
This is a very preferable material for practical use. R obtained by the present invention
-The main phase of the Fe-M-N-based material has a crystal structure that is substantially the same as the main raw material phase of the R-Fe-M alloy as the raw material, and nitrogen penetrates between lattices or the M component. The crystal lattice expands in many cases.

The term "main material phase" as used herein means a phase containing at least R and Fe and having a rhombohedral or hexagonal crystal structure. Is referred to as an auxiliary material phase. With the expansion of the crystal lattice, at least one of the items of the oxidation resistance and the magnetic properties is improved, and the magnetic material is suitable for practical use.

The magnetic characteristics referred to herein include the saturation magnetization (4πIs), residual magnetic flux density (Br), magnetic anisotropic magnetic field (Ha), magnetic anisotropic energy (Ea), magnetic anisotropy ratio, Curie point (Tc), intrinsic coercive force (iHc), squareness ratio (Br / 4πIs), maximum energy product [(BH) m
ax], the thermal demagnetization rate (α), and the temperature change rate (β) of the coercive force. However, the magnetic anisotropy ratio is
The ratio (a / b) of the magnetization (a) in the difficult magnetization direction and the magnetization (b) in the easy magnetization direction when an external magnetic field of 15 kOe is applied. Is evaluated as high.

[0018] For example, rare earth - as an iron -M master alloy, when choosing the _{Sm 10.5 (Fe 0. 95 Sn 0.05} ) 89.5 having a rhombohedral structure, by introducing nitrogen, crystal magnetic anisotropy in-plane It changes from anisotropic to uniaxial anisotropy suitable as a hard magnetic material, and the magnetic properties such as magnetic anisotropic energy and the oxidation resistance are improved. The amount of nitrogen (N) introduced is
It must be between 3 and 30 atomic%. If it exceeds 30 atomic%, the magnetization is low, and its practicality is small as a magnet material. If it is less than 3 atomic%, the performance of the raw material alloy cannot be improved much, which is not preferable. The nitrogen content is more preferably 5 to 25 atomic%, and particularly preferably 10 to 17 atomic%.
Atomic%.

Further, the optimum amount of nitrogen varies depending on the R-Fe-M composition ratio, the subphase amount ratio, and the crystal structure of the target R-Fe-MN-based magnetic material. If Nd _10.5 (Fe _0.9 Re _0.1 ) _89.5 is selected as a raw material alloy, the optimum amount of nitrogen is about 13 to 14 atomic%. The optimal amount of nitrogen at this time is different depending on the purpose, but is the amount of nitrogen at which at least one item among the oxidation resistance and the magnetic properties of the material is optimal. The absolute values of the temperature change rates of the demagnetization rate and the coercive force are minimum values, and the other values are maximum values. Of course, when adjusting a permanent magnet material having magnetic properties and oxidation resistance in practical use, the amount of nitrogen does not necessarily need to be optimal.

The R-Fe-MN-based magnetic material obtained by the present invention contains 0.01 to 10 atomic% of hydrogen (H) and 0.01 to 15 atomic% of oxygen (O). Is preferred. More preferred amounts of hydrogen and oxygen are 0.1 to
10 at% and 0.1 to 10 at%. Therefore, a particularly preferred composition of the R-Fe-MN-based material of the present invention is:
General formula Rα (Fe _(1- γ ₎ Mγ) _(100- α _- β _- δ _- ε
₎ When expressed as NβHδOε, α, β, δ, and ε are atomic%, and 2.4 ≦ α ≦ 20 2.4 ≦ β ≦ 30 0.1 ≦ δ ≦ 10 0.1 ≦ ε ≦ 10 γ is an atom The ratio is in the range of 0.001 ≦ γ ≦ 0.5.

The coexistence effect of the M component on the R—Fe—N magnetic material is mainly an improvement in oxidation resistance. In particular,
In the deterioration of the R-Fe-N-based magnetic material due to oxidation, a decrease in coercive force is more problematic than a decrease in magnetization. The composition of the present invention is characterized by having excellent stability of coercive force against oxidation. The source of the effect is due to the coexistence of the M component in the main phase of the R-Fe-N magnetic material, which is responsible for ferromagnetism.
The coexistence of the M component with the soft magnetic component mainly composed of the iron component precipitated near the grain surface due to slight oxidation also contributes to preventing a decrease in coercive force.

Although there are additional elements having the effect of the present invention in the M ′ component, since the M component of the present invention is an extremely stable element against oxidation of noble metal and Re, it is necessary to add these elements. Is considered to have a remarkable antioxidant effect. Further, apart from the object of the present invention, depending on the adjustment method and conditions of the master alloy, R near the grain boundary or RFe ₃ phase may be used.
In a material having an R-Fe-N composition such as a rich nitride phase and an α-Fe phase or a nitride phase thereof, the M component is condensed into a subphase exhibiting soft magnetism and is converted into a nonmagnetic phase. It also has the effect of improving the squareness ratio and coercive force of the nitride.

Hereinafter, the production method of the present invention will be exemplified. (1) Preparation of master alloy In the magnetic material of the present invention, R-Fe-
The main material phase of the M alloy has a structure in which the M component replaces the Fe site in the R-Fe alloy crystal, or the auxiliary material phase has a composition and structure different from that of the R-Fe two-component system due to the addition of M. The effect of the present invention is exhibited. Therefore, it is desirable to add M at the stage of master alloy adjustment.

As a method for producing an R—Fe—M alloy, R,
High frequency melting method in which Fe and M metals are melted by high frequency and cast into molds, etc., arc melting method in which metal components are charged into a boat such as copper and melted by arc discharge, on a copper roll which rotates molten metal with high frequency melting A super-quenching method for obtaining a ribbon-shaped alloy, a gas atomizing method for spraying a high-frequency molten metal with a gas to obtain an alloy powder, Fe and / or M powder or Fe-M alloy powder, R and / or M An R / D method in which the oxide powder and the reducing agent are reacted at a high temperature to reduce R or R and M while diffusing R or R and M into Fe and / or Fe-M alloy powder. A mechanical alloying method in which a metal component alone and / or an alloy is reacted while being finely pulverized by a ball mill or the like, an alloy obtained by any of the above methods is heated in a hydrogen atmosphere, and once reacted with R and / or M hydride. Decomposed into Fe and or M or Fe-M alloy, both the may be used in the HDDR method alloying are recombined while removing hydrogen as low at a high temperature after this.

When the high-frequency melting method or the arc melting method is used, a soft magnetic component mainly composed of Fe is likely to precipitate from the molten state when the alloy is solidified, and causes a decrease in coercive force even after the nitriding step. Therefore, in order to eliminate the soft magnetic component or to improve the crystallinity, the temperature is set to 800 ° C. or less in an inert gas such as argon or helium or in a vacuum.
It is effective to perform annealing in a temperature range of 1300 ° C.
The alloy produced by this method has a large crystal grain size and good crystallinity, and has a high residual magnetic flux density, as compared with the case where a super-quenching method or the like is used.

When the ultra-quenching method is used, fine crystal grains are obtained, and submicron particles can be prepared depending on the conditions. However, when the cooling rate is high, the alloy becomes amorphous, and magnetic properties such as magnetization are reduced even after nitriding. Also in this case, annealing after alloy preparation is effective.
The alloy obtained by the gas atomization method often takes a spherical form, and can be prepared from a fine powder to a coarse powder. Also in this case, depending on the conditions, it is necessary to perform annealing to improve the crystallinity. In addition to this method, R / D
The alloy prepared by the method, mechanical alloying method, or HDDR method can adjust fine crystal grains or have a distribution in the composition of the M component. It is possible to

Incidentally, the crystal phase of the alloy may be different depending on the annealing conditions. For example, depending on the R component,
A rhombohedral system and a hexagonal system may be used depending on the case of annealing and rapid cooling. Therefore, the conditions for annealing require careful attention, and the desired crystal phase can be selected by controlling the annealing conditions. (2) Coarse pulverization and classification It is possible to directly nitride the alloy ingot produced by the above method. However, if the crystal grain size is larger than 500 μm, the nitriding treatment time becomes longer. It is efficient.

Coarse pulverization is performed using a jaw crusher, a hammer,
This is performed using a stamp mill, a rotor mill, a pin mill, a coffee mill, or the like. Further, even if a pulverizer such as a ball mill or a jet mill is used, an alloy powder suitable for nitriding can be prepared depending on conditions. Also, after coarse grinding,
Adjusting the particle size using a sieve, a vibratory or sonic classifier, a cyclone, or the like is also effective for performing more uniform nitriding.

After the coarse pulverization and classification, annealing in an inert gas or hydrogen can remove structural defects, which is effective in some cases. Above, the method of preparing a powder material or an ingot material of a rare earth-iron alloy in the production method of the present invention has been exemplified.
There are differences in the following optimum conditions of nitriding depending on the microstructure, surface condition, and the like. (3) Nitriding / annealing Nitriding is a process in which a gas containing a nitrogen source, such as ammonia gas or nitrogen gas, is obtained by the above-mentioned method (1) or R-
This is a step of introducing nitrogen into the crystal structure by contacting with an Fe-M alloy powder or an ingot.

At this time, it is preferable to coexist hydrogen in the nitriding atmosphere gas since nitriding efficiency is high and nitriding can be performed with a stable crystal structure. Also argon, helium,
In some cases, an inert gas such as neon coexists.
The nitriding reaction can be controlled by gas composition, heating temperature, heat treatment time, and pressure. The heating temperature varies depending on the mother alloy composition and the nitriding atmosphere, but is selected in the range of 200 to 650 ° C. At a temperature of 200 ° C. or less, the rate of nitrogen penetration is low, and the reaction takes too much time. A more preferred temperature range is from 200C to 600C.

After nitriding, annealing in an inert gas and / or hydrogen gas is preferable from the viewpoint of improving magnetic properties. Examples of the nitriding / annealing apparatus include horizontal and vertical tubular furnaces, rotary reactors, and closed reactors. In any of the apparatuses, the magnetic material of the present invention can be adjusted. However, in order to obtain a powder having a uniform nitrogen composition distribution, it is preferable to use a rotary reactor.

The gas used for the reaction may be a gas flow system in which a gas stream of 1 atm or more is fed into the reaction furnace while keeping the gas composition constant, a gas sealing system in which the gas is sealed in a container at a pressure of 0.01 to 70 atm, or Supplied in combination. As a method for producing the magnetic material, (1) or
It is most preferable to use the step of adjusting the master alloy having the R-Fe-M composition by the method exemplified in (1) and (2) and then nitriding by the method shown in (3). This allows the M component having a high melting point to be contained in a desired portion of the mother alloy, which is particularly effective for improving oxidation resistance.

The above is the description of the method for producing the R—Fe—MN based magnetic material of the present invention. In particular, when the magnetic material of the present invention is applied as a practical hard magnetic material, (4)
Fine grinding, (5) magnetic field shaping, and (6) magnetization may be performed. Hereinafter, the example is shown simply. (4) Pulverization For example, among R-Fe-MN-based magnetic materials of a single magnetic domain type, particularly when a large crystal grain size is to be maintained and a large coercive force is desired to be developed after nitriding, Fine grinding is performed, for example, when the polycrystalline grains are kept after the treatment and anisotropic hard magnetic material is desired.

As a method of fine pulverization, a rotary ball mill,
A vibration ball mill, a planetary ball mill, a wet mill, a jet mill, a cutter mill, a pin mill, an automatic mortar and a combination thereof are used. The pulverization method is selected according to the adjustment of the amount of hydrogen or oxygen and the target pulverized particle size.

As a method for controlling the amounts of hydrogen and oxygen within the particularly preferred ranges of the present invention, for example, when a jet mill is used, the oxygen and water vapor concentrations in the pulverized gas are kept at a predetermined concentration, and an attritor or the like is used. When wet pulverization is used, a method of adjusting the amount of dissolved oxygen or water in the solvent may be used. (5) Magnetic field molding For example, when the magnetic powder obtained in (3) or (4) is applied to an anisotropic bonded magnet, compression molding is performed in a magnetic field after mixing with a thermosetting resin or a metal binder, After kneading with thermoplastic resin, injection molding is performed in a magnetic field,
Form a magnetic field.

The magnetic field shaping is preferably performed at 10 kOe in order to sufficiently orient the R-Fe-MN-based magnetic material in a magnetic field.
Above, more preferably in a magnetic field of 15 kOe or more. (6) Magnetization The anisotropic bonded magnet material and sintered magnet material obtained in (5) are usually magnetized to enhance magnet performance.

Magnetization is performed, for example, by an electromagnet that generates a static magnetic field,
This is performed by a condenser magnetizer that generates a pulse magnetic field. The magnetic field strength for sufficiently magnetizing is preferably 15 kOe or more, more preferably 30 kOe or more.

[0038]

The present invention will be described below in detail with reference to examples. The evaluation method is as follows. (1) Magnetic properties An R-Fe-MN-based magnetic material having an average particle size of about 3 μm was prepared by subjecting an external magnetic field of 15 kOe to 12 ton / cm ² at 5 mm × 1.
After shaping to about 0 mm × 2 mm and pulse magnetizing at room temperature with a magnetic field of 60 kOe, the intrinsic coercive force (iHc / kOe) was measured using a vibrating sample magnetometer (VSM). (2) Nitrogen amount, nitrogen amount and hydrogen amount Si ₃ N ₄ (including SiO ₂ quantified) as a standard sample,
The amounts of nitrogen and oxygen were determined by an inert gas melting method.
The amount of hydrogen was determined by an inert gas melting method using high-purity hydrogen gas (99.999%) as a standard gas. (3) Average particle size It was evaluated using a Lee Nurse specific surface area meter. (4) Oxidation resistance The powder molded product having an average particle size of 3 μm evaluated in (1) was
The sample was placed in a thermostat at 10 ° C., and after 200 hours, the intrinsic coercive force was measured in the same manner as in (1). The higher the retention, the higher the oxidation resistance. In particular, in the present test, evaluation was performed without adding various binders, so that a material having a retention of more than 70% can be determined to be a material that can be sufficiently used as, for example, practical physical properties when used as a bonded magnet. (5) Oxidation test 10 mg of a coarse powder sample adjusted to an average particle size of 15 μm was placed in a thermobalance, and heated in a 50 ml / min air stream at a heating rate of 1
The rate of weight change (% by weight) from 50 ° C. to 250 ° C. was measured at 0 ° C./min. The smaller the rate of weight change, the more difficult it is to oxidize.

[0039]

Example 1 Sm having a purity of 99.9% and a purity of 99.9%
Ar gas atmosphere using Fe and Pt having a purity of 99.9%
Melt and mix in an arc melting furnace under an atmosphere, and further in an argon atmosphere.
By annealing in air at 1050 ° C. for 50 hours, S
m_11.0(Fe_0.9Pt_0.1) _89.0Prepare alloy of composition
Was.

This alloy was pulverized by a jaw crusher and then further pulverized by a coffee mill in a nitrogen atmosphere, and the particle size was adjusted by a sieve to obtain a powder having an average particle diameter of about 50 μm. This Sm-Fe-Pt alloy powder was charged into a horizontal tubular furnace, and at 450 ° C, an ammonia partial pressure of 0.35.
Heat treatment was carried out in a mixed gas stream of atm and hydrogen gas of 0.75 atm, and then annealing in an argon gas stream was performed to adjust the average particle diameter to about 15 μm. Next, the powder was pulverized to a mean particle size of about 5 μm by a jet mill using a gas containing nitrogen and a part of oxygen and water vapor.

The composition, oxidation resistance and oxidation test results of the obtained Sm-Fe-Pt-N powder are shown in Table 1. Also,
The compact of the Sm-Fe-Pt-N-based powder compacted to 3 µm had a coercive force of 7.1 kOe and a residual magnetic flux density of 9.0 kG. As a result of analysis by the X-ray diffraction method, the crystal structure of this material was mainly rhombohedral, and no diffraction line corresponding to Pt alone was found.

[0042]

Examples 2 to 8 R-F by the same operation as in Example 1 except that the composition of the mother alloy was changed to the composition ratio shown in Table 1.
An eMN-based powder was obtained. Table 1 shows the results. As a result of analysis by the X-ray diffraction method, the crystal structures of these materials were mainly rhombohedral, and no diffraction line corresponding to M alone was found.

[0043]

Comparative Example 1 Sm-F was prepared in the same manner as in Example 1 except that Fe was added by the amount (atomic%) without adding Pt.
An eN powder was obtained. Table 1 shows the results.

[0044]

Comparative Example 2 Sm having a particle size of about 3 μm obtained in Example 1
_{9.2 (Fe 0.9 Pt 0.1) 74.6 N} 14.2 powder H _{0. 5} O _1.5 composition, After a magnetic field molding under the conditions of 2 ton / cm ^2, 15 kOe, under an argon atmosphere, 800 ° C., a heat treatment under conditions of 1 hour went. The intrinsic coercive force of the compact when quenched was 0.06 kOe. The inherent coercive force of the powder obtained by grinding this compact again to about 3 μm is 0.08 kO.
e. As a result of analyzing the crystal structure of this material by X-ray diffraction, diffraction lines corresponding to α-iron and iron nitride were mainly detected.

[0045]

[Table 1]

[0046]

As described above, according to the present invention, rare earth-iron-M- has excellent oxidation resistance and high magnetic properties.
A nitrogen-based magnetic material can be provided.

────────────────────────────────────────────────── ─── Continued on the front page (51) Int.Cl. ⁷ identification code FI C22C 38/00 303 C22C 38/00 303D (58) Fields investigated (Int.Cl. ⁷ , DB name) H01F 1/032-1 / 08 C22C 29 / 16,33 / 02,38 / 00

Claims (3)

(57) [Claims] (1) The general formula Rα (Fe _(1- γ ₎ Mγ) _(100- α
_{- beta)} is a magnetic material represented by N.beta, at least one kind of rare earth element R, including the Y, M is, Re, Ru, Os, Rh , Ir, Pd, Pt, A
at least one of the elements u, α and β are atomic percentages 3 ≦ α ≦ 203 3 ≦ β ≦ 30 γ is an atomic ratio of 0.001 ≦ γ ≦ 0.5 and R, Fe, M And a phase containing N has a rhombohedral or hexagonal crystal structure. 2. A magnetic material having a composition in which 0.01 to 50 atomic% of Fe which is a component of the magnetic material according to claim 1 is substituted with Co. 3. The method according to claim 1, wherein the formula Rα _{/ (100-} β ₎ (Fe _(1- γ ₎ M
γ) heat-treating the alloy represented by _(100- α _- β _{) / (100-} β ₎ at a temperature of 200 to 650 ° C. in an atmosphere containing at least one of nitrogen gas and ammonia gas. The method for producing a magnetic material according to claim 1 or 2, wherein