JP2002294413A - Magnet material and manufacturing method therefor - Google Patents

Abstract

PROBLEM TO BE SOLVED: To solve such a problem that a conventional magnet material has an insufficient mean grain-size of crystal grains, a low magnetic flux density (Br), and an insufficient maximum magnetic energy product (BH) max. SOLUTION: The objective magnet material is characterized by including a R (Y or rare earth elements, for example) -T (Fe or Co) -M (one or more among Nb, Zr, Ti, Cr, Ta, V, W, Mn, Ni, Mo, and Hf) -A (N or B) base, and an added Cu element for introducing a Cu-rich phase of 0.2-10 vol.% into the base, and by having the mean grain size of 150 nm or less. Hereby, a magnet material of ultra fine crystals capable of realizing high magnetic characteristics, can be provided. The method for manufacturing the material includes hydrogenation and decomposition reaction treatment which keeps pulverized particles at 450-850 deg.C for 1-8 hours in hydrogen gas inert gas (except for nitrogen gas), after a pulverization step, and dehydrogenation and recombination reaction treatment which keeps them at 600 deg.C-950 deg.C for 0.1-2 hours in vacuum.

Description

DETAILED DESCRIPTION OF THE INVENTION

[0001]

The present invention relates to a magnet material and a method for manufacturing the same.

[0002]

2. Description of the Related Art Sm-Co magnets, Nd-Fe-B magnets and the like are known as high-performance rare earth magnets, and are currently mass-produced. Such high performance magnets are mainly motors,
Used for electrical equipment such as speakers and measuring instruments. In recent years, there has been a growing demand for smaller and lighter electrical appliances and lower power consumption of various electric appliances. ing. As a candidate for a new high-performance magnet material, Sm-Fe-N based material was
Announced by them and attracting attention. Sm-Fe-N
Shows high saturation magnetization comparable to Nd-Fe-B and Nd-Fe
Since it has a large magnetic anisotropy exceeding -B, it is expected to be applied as a high-performance magnet.

R-T-N permanent magnet materials (R is one or more rare earth elements, T is Fe or Fe and Co)
In order to realize high magnetic characteristics, it is necessary to optimize nitriding conditions and to make crystal grains finer. In addition to increasing the coercive force (iHc) due to the fineness of the crystal, an exchange coupling force acts between the fine particles, and the residual magnetic flux density (Br) and the maximum magnetic energy product (BH) max are improved.

[0004] As means for refining the crystal, there are a method of quenching a molten metal and a method of refining a crystal by a hydrogenation / decomposition reaction / dehydrogenation / recombination reaction treatment (HDDR method). The molten metal quenching method requires a very fast molten metal quenching speed (for example, the rotation peripheral speed of the cooling roll is about 30 m / sec or more), and equipment cost increases. Furthermore, in order to obtain a fine and uniform alloy structure, high-precision quenching control technology is required, leaving a problem in production. The HDDR method is a versatile manufacturing method.

[0005] Attempts to develop high-performance SmFeN by the HDDR method have been made by several research groups since the publication of Coey et al. Che
n and Z. Altunian converts a part of Fe in Sm2Fe17 into various elements (Ti, V, Cr, Zr, Nb,
Mo, Hf, Ta, W) and examined the HDDR reaction behavior in detail, and found that high magnetic properties can be obtained when substituted with Ti or Nb (Journal of Applied).
Physics, 75 (10) (1991) p6012). Tobiyo Sm2Fe1
7, Ti and B were added, and the average grain size of the crystal grains was 200 nm.
(Proceedings of 16
^th International Workshop on RE Magnetsand Their A
pplications (2000) p793).

However, the problem is that the crystal grains are still not sufficiently refined, the magnetic flux density (Br) is small, and the maximum magnetic energy product (BH) max is insufficient as compared with those obtained by the melt quenching method. Having.

Further, high performance NdFe
Development of B is also underway, and adjustment or treatment of alloy composition
It has been found that anisotropic alloy powder can be obtained by optimizing the process (Journal of Magnetic Society of J
apan, 23 (1999) p300), the average grain size of the crystal grains is 300 nm.
Therefore, a finer structure and higher characteristics are required.

[0008]

As described above, in the prior art, the crystal grains are not sufficiently refined yet, the magnetic flux density (Br) is small, and a sufficient maximum magnetic energy product (BH) max is obtained. There is a problem that has not been done.

SUMMARY OF THE INVENTION The present invention has been made to address such a problem, and an object of the present invention is to provide a magnet material of an ultrafine crystal and a method of manufacturing the same, which can realize high magnetic properties.

[0010]

The present inventors have SUMMARY OF THE INVENTION As a result of extensive studies to achieve the above object, the general formula _{R x (T 1-u-} v Cu u M v) 1-x-y A _y (where R is at least one element selected from rare earth elements including Y, T is at least one element selected from Fe or Co, M is Nb, Zr, Ti, Cr, Ta, V, W , Mn, N
at least one element selected from i, Mo, Hf; A is at least one element selected from N or B; x, y, u, and v each have an atomic ratio of 0.04 ≦ x ≦ 0.2; 001 ≦ y ≦ 0.2, 0.002 ≦ u ≦ 0.2, 0 ≦ v ≦ 0.2), TbCu ₇ type, Nd ₂ Fe ₁₄ B
_Type, Th 2 _{Ni 17 type,} a phase having any crystal structure of Th 2 _{Zn 17} type as the main phase, comprising a non-magnetic phase containing 20 atomic% or more of Cu 0.2 to 10 vol%, the main phase And a magnet material characterized in that the average crystal grain size of the non-magnetic phase is 150 nm or less.

That is, the magnetic material of the present invention is characterized by adding a Cu element and introducing a Cu-rich phase based on the RTA system. Until now, part of T was M,
It is reported that Cu was replaced, but Cu-ric
An h phase has not been formed. The above Cu-ric
The introduction of the h phase makes it possible to make crystal grains ultrafine compared to the case where no Cu-rich phase is present.

The HDDR treatment mainly includes a hydrogenation / decomposition reaction (HD reaction: coarse main phase-> T phase + R hydride) and a dehydrogenation / recombination reaction (DR reaction: T phase + R hydride-> fine main phase). In order to obtain ultra-fine and uniform crystal grains, control of the HD reaction and the DR reaction is extremely important. The point of control is to end the reaction while suppressing grain growth during the reaction. for that reason,
It is preferable to lower the hydrogen reaction temperature of the alloy. The introduction of another alloy phase as a pinning site for inhibiting grain growth is extremely effective in suppressing grain growth during the reaction, and is particularly preferable. However, it is extremely important for the magnetic properties that the introduced alloy phase is not soft magnetic. For example, since an M element such as Ti, V and Nb easily forms a soft magnetic phase such as Fe and MFe2 and MFe3, it is difficult to introduce a pinning phase only by adding the M element. The inventor has been studying the RTM-Cu alloy system for many years (Japanese Patent Application No. 11-375478),
High T concentration RT phase and non-magnetic Cu in RTM-Cu system
-I found a coexistence relationship with the rich phase. Non-magnetic phase Cu-
It was conceived to explore the possibility of ultra-miniaturization of the HDDR method by introducing the rich phase, and completed the present invention.

[0013]

Embodiments of the present invention will be described below.

[0014] magnet material of the present invention, as described above general formula _{R x (T 1-u-} v Cu u M v) 1-x-y A y ( wherein, R selected from rare earth elements including Y And T is at least one element selected from Fe or Co. M is Nb, Zr, Ti, Cr, Ta, V, W, Mn, N
at least one element selected from i, Mo, Hf; A is at least one element selected from N or B; x, y, u, and v each have an atomic ratio of 0.04 ≦ x ≦ 0.2; 001 ≦ y ≦ 0.2, 0.002 ≦ u ≦ 0.2, 0 ≦ v ≦ 0.2), TbCu ₇ type, Nd ₂ Fe ₁₄ B
_Type, Th 2 _{Ni 17 type,} a phase having any crystal structure of Th 2 _{Zn 17} type as the main phase, comprising a non-magnetic phase containing 20 atomic% or more of Cu 0.2 to 10 vol%, the main phase And the non-magnetic phase has an average crystal grain size of 150 nm or less. Hereinafter, each component constituting the magnet material of the present invention will be described in detail. (1) R element As R, at least one element selected from rare earth elements including Y is used. Each of the R elements brings a large magnetic anisotropy to the magnet material, and is added in the range of 4 to 20 atomic% in order to provide a high coercive force. If the total amount of the R element is less than 4 atomic%, a large amount of α-Fe precipitates and a large coercive force cannot be obtained, while if it exceeds 20 atomic%, the saturation magnetization is significantly reduced. A more preferable blending amount of the R element is 8 to
It is 12 at%, and more preferably 9 to 11 at%. It is preferable to use Sm, Nd, and Pr as the R element, and Sm and Nd are particularly preferable. 50 of the total amount of R
By setting Sm to at least atomic%, more preferably at least 70 atomic%, it is effective to enhance the performance of the magnetic material, especially the coercive force. (2) T element The T element is at least one element selected from Fe and Co, and mainly plays a role in magnetization of the magnet material. The saturation magnetization of the magnet material can be increased by blending a large amount of T, but if it is blended excessively, the coercive force may decrease due to the precipitation of the α-Fe phase. (3) Cu Cu is an element effective for refining the alloy structure. Addition of an appropriate amount of Cu forms a Cu-rich alloy phase (Cu content of 20 atomic% or more) in the mother alloy, and prevents pinning s for preventing grain growth.
The ite is extremely effective in suppressing grain growth and has the effect of making the structure ultrafine. In addition, the substitution of the element M may increase the HD reaction temperature of the alloy. However, by adding Cu and M in combination, the HD reaction and the DR reaction can be completed at a lower temperature and / or a shorter time, and the crystal grain size can be reduced. It is effective for miniaturization. If the compounding amount of Cu is less than 0.2 atomic% of the total amount of T, M, Cu, the effect of the compounding cannot be sufficiently achieved, while if it exceeds 20 atomic% of the total amount of T, M, Cu, the saturation magnetization decreases. Invite. A more preferred blending amount of the Cu element is 0.5 to 10 atomic% of the total amount of T, M, and Cu, and still more preferably 1.0 to 7 atomic%. Said C
50% by atom or less of Si, Ga, Zn, Al, La,
It is allowed to be substituted with at least one element selected from Ge. (4) M element The M element is Nb, Zr, Ti, Cr, Ta, V, Ta,
At least one selected from W, Mn, Ni, Mo, Hf
Although it is a kind of element, it can suppress the precipitation of the α-Fe phase in the mother alloy and is effective in refining the alloy structure. However, the substitution of the element M increases the HD reaction temperature of the alloy, and the effect of miniaturization of the element M alone is insufficient. M element is mainly T in the main phase.
The site occupied by the element is replaced.
If the total amount of M and Cu exceeds 20 atomic%, the saturation magnetization is significantly reduced. More preferred amounts of the M element are T, M, Cu
Is 1 to 10 atomic% of the total amount, more preferably 1.
5 to 8 atomic%. N elements such as Nb, Zr, and T
It is preferable to use i, V, and Hf, and Nb and Zr are particularly preferable. (5) A A is mainly present at the interstitial position of the main phase. By expanding the crystal lattice and changing the electronic structure as compared with the case where A is not contained, the Curie temperature,
It has the function of improving magnetic anisotropy and saturation magnetization. When A mainly uses B, the crystal structure of the main phase is Nd ₂ Fe ₁₄
The crystal structure of the main phase is any of TbCu ₇ type, Th ₂ Ni ₁₇ type, and Th ₂ Zn ₁₇ type when A mainly uses N. If the compounding amount of A is less than 0.1 atomic%, the effect of compounding cannot be sufficiently achieved.
Exceeding this causes a decrease in saturation magnetization. A more preferable compounding amount of A is 10 to 15 atomic%. 50% by atom or less of A is allowed to be replaced by at least one element selected from H, C, S, P and O. H, C, S, P, O
Alloy or HDD with composite addition of N and B
A fine hydride phase, B-ri
It has an effect of forming a ch phase, a C-rich phase, etc., and further refining the structure. It is preferable to use B even when A mainly uses N.

Depending on the amount of each element and the manufacturing process
Is TbCu₇Type, Nd₂Fe₁₄B type, Th₂Ni
₁₇Type, Th₂Zn₁₇Type, ThMn₁₂Phase, R₃Fe
₂₉Phase may be the main phase, but TbCu₇Type,
Nd₂Fe₁₄B type, Th₂Ni ₁₇Type, Th₂Zn
₁₇If one of the molds has
Property is obtained. Here, the main phase constitutes a magnet material.
Maximum volume occupancy among the crystalline and amorphous phases
Means a phase having The magnet material of the present invention is 5
The soft magnetic phase containing 0 atomic% or more of T is 0.5 to 4 by volume.
0% can be contained. In this case, the coercive force is
Although reduced, a high Br is obtained. Average grain size and
The volume ratio of the alloy phase can be observed with an electron microscope or an optical microscope.
It is judged comprehensively by using together with X-ray diffraction, etc.
Area analysis of transmission electron micrographs of material cross sections
Can be obtained by The magnet material of the present invention is an oxide
It is allowed to contain inevitable impurities such as.

Next, an example of a method for manufacturing a magnet material according to the present invention will be described.

First, an alloy coarse powder containing predetermined amounts of R, T, M, Cu and A elements is prepared. When A is mainly N, nitrogen is contained by gas treatment after HDDR treatment. The alloy coarse powder can be obtained by pulverizing a mother alloy obtained by arc melting, high frequency melting or the like into an average powder particle size of 3 to 500 μm. It can be obtained by pulverizing the alloy ribbon as it is produced by strip-casting melting or as it is afterwards.
The alloy powder thus obtained or the alloy before pulverization can be subjected to a heat treatment as necessary to be homogenized. It is also possible to control the type and volume occupancy of the main phase by adjusting the alloy powder and heat treatment conditions. A preferable structure of the mother alloy includes an RTM-Cu-A hard magnetic phase and a Cu-rich phase, and the volume ratio of the Cu-rich phase is 0.1 to 10%.

Next, HDDR conditions suitable for the present invention will be described. Hydrogenation / decomposition reaction treatment (HD treatment) is 0.1 to 1
In a hydrogen gas of 0 atm or an inert gas having a hydrogen gas partial pressure (excluding nitrogen gas),
Hold for 8 hours. In the HD process, the main phase in the mother alloy is converted to R hydride and T, T-M, T by a hydrogenation / decomposition reaction.
It is preferable to finish the HD treatment before decomposing into -M-Cu and Cu and the R hydride is coarsened in order to obtain a fine structure and good magnetic properties. HD process on lower temperature side and / or
Alternatively, on the short time side, no decomposition reaction occurs, or only a part of the mother alloy decomposes. In this case, since the crystal grains are not refined in the portion where the decomposition reaction did not occur, the post-treatment DR process and the nitriding treatment (A is mainly N
Br, iH of the magnet powder obtained through
c, (BH) max is low. On the other hand, when the HD process is at a higher temperature side and / or a longer time side, the structure after the HD treatment is coarsened, so that the hard magnetic phase after the DR treatment and the nitriding treatment (A is mainly N) is coarse. Magnetic properties are degraded. Preferred HD treatment conditions depend on the crystal structure of the main alloy phase, but in the case of the Nd ₂ Fe ₁₄ B
0-800 ° C, 2-4 hours, otherwise 500
-700 ° C, 2-4 hours. It should be noted that increasing the number of stages of HD processing is also effective for making the structure ultra-fine.

The dehydrogenation / recombination reaction treatment (DR treatment) is 1
600 ° C to 950 ° C in a vacuum of 3.333224 Pa or less
For 0.1 to 2 hours. In the DR process, R hydride disappears due to a dehydrogenation / recombination reaction, and TbCu ₇
Type, Nd ₂ Fe ₁₄ B type, Th ₂ Ni ₁₇ type, Th ₂ Z
Recrystallization to a phase having any of the _n17- type crystal structures is preferably performed before DR processing is completed before the recrystallized grains become coarse in order to obtain good magnetic properties. At a lower temperature and / or shorter time in the DR process, no recombination reaction occurs or only a part of the recombination reaction occurs. In this case, since the T phase, which is a soft magnetic phase, remains in the portion where the recombination reaction did not occur, the iHc of the magnet powder obtained through the nitriding treatment (A is mainly N) is obtained.
Is low. On the other hand, when the DR process is performed on a higher temperature side and / or a longer time side, the structure after the DR process is coarsened, so that the D
The hard magnetic phase after the R treatment and the nitriding treatment (A is mainly used only when N) is coarsened, so that the magnetic properties are deteriorated. Preferred HD treatment conditions depend on the crystal structure of the main alloy phase,
13.33224 PPa in the case of d ₂ Fe ₁₄ B structure
In the following vacuum, 700-850 ° C., 0.2-1 hour, otherwise, in a vacuum of 13.33224 Pa or less,
600-750 ° C, 0.2-1 hour.

If A is mainly N, then N is added to the alloy powder. In this case, 0.1 to 1
0.1-100 hours in a nitrogen gas atmosphere at 00 atm.
It is desirable to heat-treat at a temperature of 00 to 900 ° C.
As the atmosphere for the heat treatment, a nitrogen compound gas such as ammonia may be used instead of the nitrogen gas. The nitridation reaction can be controlled by using a mixture of a nitrogen gas or a nitrogen compound gas and a hydrogen gas. It is possible to partially replace N with H by using a nitrogen compound gas such as ammonia or by mixing hydrogen gas.

When a magnet body is manufactured from the magnet material of the present invention, an alloy powder containing a predetermined amount of R, T, M, Cu, N is subjected to hot pressing, hot isostatic pressing, discharge plasma sintering or the like. It can be manufactured by integrating as a high-density molded body.

The magnet material of the present invention can be used as a bonded magnet. As the binder, a resin such as an epoxy-based resin or a nylon-based resin may be used as before, but it is also possible to manufacture a metal-bonded magnet using a low-melting-point metal or a low-melting-point alloy as a binder.

[0023]

Next, specific examples of the present invention will be described. (Examples 1 to 10) First, high-purity raw materials were prepared at predetermined ratios shown in Table 1, and were subjected to high-frequency melting in an Ar atmosphere to prepare a mother alloy ingot, and the average powder particle size was determined using a mortar.
It was pulverized to not more than 06 μm. Continue to add this alloy powder to 1
A hydrogenation and decomposition reaction treatment is performed at 500 to 800 ° C. for 1 to 8 hours in hydrogen gas of atm, and then 13.3.
0.2 to 600 ° C. to 800 ° C. in a vacuum of 3224 Pa or less.
After performing the dehydrogenation and recombination reaction treatment for 1 to 2 hours, the mixture is heated at 450 ° C. in a nitrogen gas atmosphere of 1 atm.
Heat treatment was performed for a time to produce a magnet powder.

X-ray diffraction analysis and TEM / EDS analysis of the formed phase of each alloy powder at each processing stage showed that after HD treatment, it was mainly Sm hydrate and α-Fe phase, and after DR treatment and nitriding treatment, Mainly, it became a uniform and ultrafine main phase and a Cu-rich phase. The crystal structure of the main phase is TbCu ₇ type, Th ₂ Ni
_17-, it was confirmed that any of the Th 2 _{Zn 17} type. The composition of the Cu-rich phase in each alloy is mainly Cu
The amount was analyzed to be at least 20 atomic%. Next, an isotropic bonded magnet was prepared from each of the alloy powders to obtain a BH trace.
The er measurements were taken. In the case of the alloy of Example 6, Br
A high Br of 0.74 T was measured. Example 1
10 alloy composition, HDDR processing temperature, average grain size,
Table 1 shows the measurement results of the magnetic properties of the isotropic bonded magnet. (Comparative Examples 1 to 4) An alloy powder and an isotropic bonded magnet were prepared in the same manner as in Examples 1 to 10, and the same BH measurement was performed. Table 1 also shows the alloy compositions, HDDR processing temperatures, and BH measurement results of Comparative Examples 1 to 4. While the alloys of the examples include the Cu-rich phase, the alloys of the comparative examples are cases where Comparative Examples 1 to 3 do not include Cu, Comparative Example 4 includes Cu, and do not include the Cu-rich phase. . Cu-r
It was found that by including the ich phase, the crystal grain size of the alloy was finer than in the case where it was not present at all, and the magnetic properties were excellent. (Examples 11 to 15) First, high-purity raw materials were mixed at predetermined ratios shown in Table 2, and were subjected to high frequency melting in an Ar atmosphere to produce a mother alloy ingot, and the average powder particle diameter was 106 µm using a mortar. It was ground to the following. Subsequently, the alloy powder was subjected to a hydrogenation / decomposition reaction treatment in hydrogen gas of 1 atm at 600 to 850 ° C. for 1 to 8 hours, and then 13.3.
In a vacuum of 3224 Pa or less, at a temperature of 700 ° C. to 950 ° C.
A dehydrogenation / recombination reaction treatment for 1 to 2 hours was performed to produce a magnet powder.

X-ray diffraction analysis and TEM / EDS analysis of the formed phase of each alloy powder at each processing stage showed that after HD treatment, it was mainly Nd hydrate and α-Fe phase, and after DR treatment, it was mainly uniform. In addition, an ultrafine main phase and a Cu-rich phase were formed. The crystal structure of the main phase was confirmed to be _Nd 2 _{Fe 1 4} B type. The composition of the Cu-rich phase in each alloy is mainly Cu
The amount was analyzed to be at least 20 atomic%. Next, an isotropic bonded magnet was prepared from each of the alloy powders to obtain a BH trace.
The er measurements were taken. In the case of the alloy of Example 14, B
A high Br of r = 0.68T was measured. Example 1
Table 1 shows the alloy compositions of Nos. 1 to 15, the HDDR processing temperature, the average crystal grain size, and the results of measuring the magnetic properties of the isotropic bonded magnet.
Shown in (Comparative Examples 5 to 7) An alloy powder and an isotropic bonded magnet were produced in the same manner as in Example 1, and the same BH measurement was performed. Each alloy composition, HDDR processing temperature and B-
The results of the H measurement are also shown in Table 2. The alloy of the embodiment is Cu-r
While the alloy of Comparative Example contains the ich phase, Comparative Examples 5 to 6
Does not contain Cu, Comparative Example 7 contains Cu,
This is the case where no rich phase is included. The inclusion of the Cu-rich phase revealed that the alloy crystal grain size was finer than in the absence of this alloy.

[Table 1]

[Table 2] In Tables 1 and 2, TbCu ₇ type, Nd ₂ F
e ₁₄ B type and Th ₂ Zn ₁₇ type have been described.
The same results as those of the above three crystal structures were obtained for the h ₂ Ni ₁₇ type, and M was Zn other than Nb or Cr.
The same applies to Al, La, and Ge.
May be replaced by Si, Ga, Zn or the like.

[0026]

As described above, according to the magnet material of the present invention, it is possible to provide an ultrafine crystalline magnet material which can realize high magnetic properties.

──────────────────────────────────────────────────の Continued on the front page (51) Int.Cl. ⁷ Identification symbol FI Theme coat ゛ (Reference) C22C 1/04 C22C 1/04 H H01F 1/053 H01F 1/04 A F term (Reference) 4K017 AA01 BA03 BA06 BB04 BB05 BB08 BB09 BB12 CA06 DA02 EA03 FA02 FA03 4K018 AA11 AA27 BA05 BA18 BB04 BB06 BC01 BC02 BD01 KA46 5E040 AA04 AA06 NN01

Claims (5)

[Claims] 1. A compound represented by the general formula: R _x (T ₁ -uvCu _{u Mv} ) _{1 -xy} A _y (where R is at least one element selected from rare earth elements including Y, and T is At least one element M selected from Fe or Co is Nb, Zr, Ti, Cr, Ta, V, W, Mn, N
at least one element selected from i, Mo, Hf; A is at least one element selected from N or B; x, y, u, and v each have an atomic ratio of 0.04 ≦ x ≦ 0.2; 001 ≦ y ≦ 0.2, 0. 002 ≦ u ≦ 0.2, 0 ≦ v ≦ 0.2), TbCu ₇ type, Nd ₂ Fe ₁₄ B
_Type, Th 2 _{Ni 17 type,} a phase having any crystal structure of Th 2 _{Zn 17} type as the main phase, comprising a non-magnetic phase containing 20 atomic% or more of Cu 0.2 to 10 vol%, the main phase And a non-magnetic phase having an average crystal grain size of 150 nm or less. 2. The magnetic material according to claim 1, wherein M always includes at least one element selected from Nb and Zr. 3. The method according to claim 1, wherein 50% by atom or less of said Cu is Si, G
at least one selected from a, Zn, Al, La, and Ge
The magnetic material according to claim 1, wherein the magnetic material is replaced with a seed element. 4. The method according to claim 1, wherein 50% by atom or less of A is H, C, S,
4. The magnet material according to claim 1, wherein the magnet material is substituted with at least one element selected from P and O. 5. The method of producing a magnetic material according to claim 1, wherein the powder is pulverized to an average powder particle size of 3 to 500 μm, and then the hydrogen gas or the hydrogen gas partial pressure is reduced to 0.1 to 10 atm. 4 in inert gas (excluding nitrogen gas)
A hydrogenation and decomposition reaction treatment is performed at 50 to 850 ° C. for 1 to 8 hours, and then a dehydrogenation and recombination reaction is performed at 600 to 950 ° C. for 0.1 to 2 hours in a vacuum of 13.33224 Pa or less. A method for producing a magnet material, comprising performing a treatment.