JP2003017307A - Solid material for magnet and method of fabricating the magnet - Google Patents

Abstract

PROBLEM TO BE SOLVED: To obtain a solid material for magnet which is given the density of 6.15 to 7.45 g/cm<3> and assures excellent higher magnetic characteristics and thermal stability. SOLUTION: Magnetic powder of the rare-earth-iron-nitrogen-hydrogen system is pressed and molded in the magnetic field and thereafter it is compressed within the water using the impulse wave having pressure of 3 to 22 GPa.

Description

Detailed Description of the Invention

[0001]

BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention utilizes a solid material for a rare earth-iron-nitrogen-hydrogen-based magnet, which has a high magnetic property while being lightweight, and is excellent in thermal stability, and a magnet using the same. Device and parts. This invention also
The present invention relates to a manufacturing method for obtaining a solid material for a magnet having high magnetic properties while preventing compaction and denitrification by impact compression after compacting in a magnetic field.

[0002] The solid material referred to here is a lump-shaped material. Furthermore, the solid material for a magnet referred to here means a lump-shaped magnetic material, and the powders of the magnetic material forming the solid material for a magnet are directly bonded to each other or continuously through a metal phase or an inorganic phase. However, it is a magnetic material in a state of forming a lump as a whole.

[0003]

2. Description of the Related Art As a high-performance rare earth magnet, for example, Sm
-Co type magnets and Nd-Fe-B type magnets are known.
The former is widely used due to its high thermal stability and corrosion resistance, while the latter is widely used due to its extremely high magnetic properties, low cost, and stable supply of raw materials. Nowadays, a rare earth magnet which has both higher thermal stability and higher magnetic properties and which is light in weight and low in raw material cost is demanded as an actuator for electric equipment or various FA, or a magnet for a rotating machine.

On the other hand, when a rare earth-iron compound having a rhombohedral or hexagonal crystal structure is reacted in a mixed gas of NH ₃ and H ₂ at a relatively low temperature of 400 ° C. to 600 ° C., N
It has been reported that atoms and H atoms penetrate into interstitial sites of the above-mentioned crystal, for example, Th ₂ Zn ₁₇ type compound, resulting in a remarkable increase in Curie temperature and magnetic anisotropy (US Pat. No. 5,186,766). . In recent years, high-performance solid magnets using such rare earth-iron-nitrogen based magnetic materials are expected to be put into practical use as new magnet materials meeting the above-mentioned demand.

[0005]

A rare earth-iron-nitrogen-hydrogen material (hereinafter R-F) containing nitrogen and hydrogen in the intermetallic compound lattice and having a rhombohedral or hexagonal crystal structure.
(e-N-H magnetic material) is generally obtained in a powder state, but α-Fe at a temperature of about 600 ° C or higher under normal pressure.
Since it is easy to decompose into a decomposed phase and a rare earth nitride phase, it is very difficult to sinter by self-sintering to obtain a solid material for a magnet by an ordinary industrial method.

Therefore, as the magnet using the R—Fe—N—H magnetic material, a bond magnet using a resin as a binder is manufactured and used. However, a magnet made of this material has a Curie temperature of 400 ° C. or higher, and although it uses magnetic powder that does not lose its magnetization even at a temperature of 200 ° C. or higher, 12-nylon The low heat resistance temperature of the binder such as resin and the temperature coefficient of coercive force
0.5% / ° C, but coercive force 0.6MA /
The irreversible demagnetization rate becomes large mainly due to the small m (see Technical Report No. 729 of the Institute of Electrical Engineers of Japan, edited by The Institute of Electrical Engineers, p. 41), and it is used only at a temperature of less than about 100 ° C. That is, recently, due to the requirement of heavy duty, there has been a problem that this bond magnet cannot be used when making a brushless motor or the like as a power source used in a high temperature environment of 150 ° C. or higher.

Further, in the case of producing a compression-molded bonded magnet using a resin as a binder, a molding pressure of 10 weight ton / cm ² or more, which is industrially difficult, is required in order to improve the filling rate and improve the performance. Considering the mold life, etc., the mixing ratio is often less than 80% by volume,
There is a problem that the excellent basic magnetic characteristics of the R—Fe—N—H magnetic material cannot be sufficiently exhibited depending on the compression-molded bonded magnet.

In order to solve the above problems, Japanese Patent No. 3108232 proposes a method for manufacturing a rare earth-iron-nitrogen permanent magnet which does not use a resin binder. However, according to the method, in order to suppress the residual temperature after impact compression to a temperature not higher than the decomposition temperature of the Th ₂ Zn ₁₇ type rare earth-iron-nitrogen based magnetic material, the pressure during impact compression is set to a certain narrow range. There was a drawback that it had to be limited. Further, according to this method, the decomposition of the rare earth-iron-nitrogen based magnetic material could not be sufficiently suppressed, so the coercive force remained at a low value of 0.21 MA / m at maximum.

Further, in Japanese Patent Laid-Open No. 2001-6959, for the purpose of obtaining a large-sized molded body without cracks or chips, a Th ₂ Zn ₁₇ type rare earth-iron-nitrogen based magnetic material is compressed and solidified by using a cylindrical converging shock wave. Although a method is disclosed, the maximum value of coercive force of the magnet obtained by the method is 0.62.
MA / m was still unsatisfactory.

Besides, Th ₂ Z formed by shock wave compression
Examples of the n ₁₇ type rare earth-iron-nitrogen based magnetic material are described in J.
Appl. Phys. There is one reported in Volume 80, No. 1, 356, but at 10 GPa, the filling rate is low and 2
At 0 GPa, the decomposition into α-Fe decomposition phase and SmN phase proceeds, so the maximum values of magnetic characteristics under each shock compression condition are coercive force 0.57 MA / m, (BH) _max = 134 kJ / m ³ ,
Were those not be said with respect to Th ₂ Zn ₁₇ type R-Fe-N-H-based bonded magnet has a sufficiently high magnetic properties.

Further, in applications for home electric appliances, office automation equipment and electric vehicles, light weight and high performance are required.
Density of -Co-based magnet 8.4 g / cm ³ approximately, Nd-F
When the density of the e-B magnet is about 7.5 g / cm ³ , the weight tends to increase when these magnets are mounted. Further, even if the magnet can be made smaller and lighter due to the margin of magnetic characteristics depending on the application, it is not necessarily advantageous in terms of cost considering the yield due to processing. For example, since the cutting waste is proportional to the cutting area, the smaller the volume, the worse the yield per unit volume of the product.

Since various bonded magnets that make up the drawbacks are inferior in thermal stability as described above, a magnet which is lightweight yet has high magnetic characteristics, excellent thermal stability and high cost performance has not yet been developed. .

[0013]

DISCLOSURE OF THE INVENTION The present invention contains 80 to 97% by volume of an R—Fe—N—H magnetic material having a rhombohedral or hexagonal crystal structure, and 6.15 to 7. 45 g
An object of the present invention is to provide a solid material for a magnet, which has a small density of / cm ³ and excellent magnetic characteristics and stability. Another object of the present invention is to provide a method for producing the solid material for a magnet. Still another object of the present invention is to provide a device and a part using the solid material for a magnet.

[0014]

The inventors of the present invention contain an R—Fe—N—H magnetic material having a rhombohedral or hexagonal crystal structure, are lightweight, and have high magnetic properties and stability. In order to obtain a solid material for a magnet, the raw material composition, the content rate, and the manufacturing method thereof have been studied earnestly. As a result, a magnetic material powder containing not only nitrogen but also hydrogen is used, and the volume fraction thereof is 80 to
97% by volume, after compacting into a compact in a magnetic field, the compact is shock-compressed with an underwater shock wave having a constant shock wave pressure, and the ultra-high-pressure shear property of shock compression, activation action, and short-time action Taking advantage of the characteristics such as the phenomenon, the residual temperature after impact compression is determined by the decomposition temperature of the R-Fe-NH magnetic material (about 6 at normal pressure).
(00 ° C) or less, while preventing decomposition, it can be used even at 100 ° C or higher at a density of 6.15 to 7.45 g / cm ³ , and is solidified by a metal bond to R-Fe-N.
The present invention has been completed based on the finding that a solid material for -H magnets can be easily obtained.

That is, the aspects of the present invention are as follows. (1) Rare earth having a rhombohedral or hexagonal crystal structure-
A solid material for a magnet, comprising 80 to 97% by volume of an iron-nitrogen-hydrogen based magnetic material. (2) A rare earth-iron-nitrogen-hydrogen-based solid material for magnets having a rhombohedral or hexagonal crystal structure, which has a density of 6.15 to 7.45 g / cm ³ . (3) (1) or (2) a solid material for a magnet according, room temperature remanence B _r, room temperature coercivity H _cJ, permeance coefficient P _c and the maximum use temperature when used as a magnet The relation of T _max is _{Br r} ≤ μ ₀ H _cJ (P _c +1) (11000-50T _max ) /, where μ ₀ is the magnetic permeability of vacuum
Solid material for a magnet, which is a (10000-6T _max). (4) The solid material for a magnet according to any one of (1) to (3) above, which has a coercive force H _cJ of 0.76 MA / m or more and a squareness ratio B _r / J _s of 95% or more. A solid material for a magnet, which is (5) The solid material for a magnet according to any one of (1) to (4) above, wherein a component other than the rare earth-iron-nitrogen-hydrogen based magnetic material has an element density of 6.5 g / cm ³ or less, A solid material for a magnet, which is a compound or a mixture thereof. (6) The solid material for a magnet according to any one of (1) to (5), wherein at least one of the atmosphere and an inert gas is provided in a portion other than the rare earth-iron-nitrogen-hydrogen based magnetic material. A solid material for a magnet, characterized by containing. (7) The solid material for a magnet as set forth in any one of (1) to (6) above, wherein an oxide, a fluoride, a carbide, a nitride are added to a portion other than the rare earth-iron-nitrogen-hydrogen magnetic material. A solid material for a magnet, comprising at least one selected from a hydride, a carbonate, a sulfate, a silicate, a chloride and a nitrate. (8) The solid material for a magnet according to any one of (1) to (7), wherein the organic material is contained in a portion other than the rare earth-iron-nitrogen-hydrogen based magnetic material. Solid material. (9) The solid material for a magnet as set forth in any one of (1) to (8), wherein the rare earth-iron-nitrogen-hydrogen magnetic material or a mixture of the magnetic material and other constituents has a shock wave pressure of 3 or less. ~ 2
The solid material for magnets according to any one of claims 1 to 8, wherein the solid material is compressed and solidified by using an underwater shock wave of 2 GPa. (10) A method for producing the solid material for a magnet according to any one of (1) to (9) above, which comprises rare earth-iron-nitrogen-
A method for producing a solid material for a magnet, comprising compacting hydrogen-based magnetic powder in a magnetic field and then compressing and solidifying it using an underwater shock wave. (11) A component for use in a device that utilizes a static magnetic field of a magnet, characterized by using the solid material for a magnet according to any one of the above (1 to 9). (12) An apparatus having a maximum operating temperature T _max of 100 ° C. or higher, which utilizes the static magnetic field of a magnet, and which has the above-mentioned (1
An apparatus using the component described in 1).

[0016]

BEST MODE FOR CARRYING OUT THE INVENTION The R—Fe—N—H based magnetic material used in the solid material for a magnet of the present invention includes the following (1).
At least one magnetic material selected from (7) to (7). (1) A magnetic material represented by the general formula R _α Fe _100-α-β-γ N _β H _γ , having a rhombohedral or hexagonal crystal structure, and R is selected from rare earth elements including Y. At least one element, and α, β and γ are atomic percentages, 3 ≦ α ≦ 20, 5 ≦ β ≦ 30, 0.01 ≦ γ ≦ 10
A magnetic material characterized by: (2) A magnetic material represented by the general formula R _α Fe _{100-α-β-γ-δ} N _β H _γ O _δ , having a rhombohedral or hexagonal crystal structure, and R contains Y. It is at least one element selected from rare earth elements, and α, β, γ, δ are atomic percentages, 5 ≦ α ≦ 20, 10 ≦ β ≦ 25, 0.01 ≦
A magnetic material having γ ≦ 5 and 1 ≦ δ ≦ 10. (3) Ni, Ti, and 20 atomic% or less of R and / or Fe
V, Cr, Mn, Zn, Zr, Nb, Mo, Ta,
The above (1) substituted with at least one element selected from W, Ru, Rh, Pd, Hf, Re, Os, Ir and B
Alternatively, the magnetic material according to (2). (4) 10 atomic% or less of N and / or H is C, P, Si,
The magnetic material according to any one of (1) to (3) above, which is substituted with at least one element selected from S and Al. (5) Among the components of the magnetic material according to any of (1) to (4) above, 50 atom% or more of R is Sm. (6) A magnetic material, characterized in that, of the components of the magnetic material according to any one of (1) to (5), 0.01 to 50 atomic% of Fe is replaced with Co. (7) A magnetic material obtained by reacting Zn with the grain boundaries or the surface of the magnetic material according to any one of (1) to (6) above.

These magnetic materials can be obtained by known methods (for example, US Pat. No. 5,186,766 and US Pat. No. 5,164).
No. 104, Japanese Patent No. 2703281, Japanese Patent No. 270
No. 5,985, No. 2,708,568, No. 2,739,860, No. 2,857,476, etc.)
Is prepared by.

These R-Fe-N-H magnetic materials are
It is obtained in the form of powder having an average particle size of 0.1 to 100 μm, and is supplied as a raw material of a solid material for magnets. If the average particle size is less than 0.1 μm, the magnetic field orientation becomes poor and the residual magnetic flux density becomes low. On the other hand, if the average particle size exceeds 100 μm, the coercive force becomes low and the practicality becomes poor. In order to impart excellent magnetic field orientation, the range of the more preferable average particle diameter is 1 to 100 μm, and the most preferable range is 2 to 80 μm. Further, the R-Fe-N-H-based material is
It is characterized by high saturation magnetization, high Curie point, and large magnetic anisotropy. Therefore, if a single crystal powder having a particle size of 2 μm or more is used, the magnetic field can be easily oriented by an external magnetic field, and an anisotropic magnet having high magnetic characteristics can be obtained.

One of the major characteristics of the R-Fe-N-H type magnetic material is that it has high oxidation resistance and does not easily generate rust. Nd-Fe-B based sintered magnets have extremely high magnetic properties and are widely used in actuators such as VCMs and various motors, but their surface easily oxidizes even in the atmosphere at room temperature, and therefore prevents rust removal. For the purpose, surface treatment by nickel plating or epoxy resin coating is essential.

On the other hand, in the case of the magnet using the R—Fe—N—H type magnetic material, the above-mentioned surface treatment is not necessary or can be simplified. This is a cost effective, yet, because it can make the most of the magnetic force of the magnet when used as a partial actuator or motor is no magnetic low surface layer, for example, (BH) _max value Nd Even if it is inferior to the -Fe-B system sintered magnet, similar cost performance can be exhibited.

By the way, Th ₂ Zn ₁₇ containing no hydrogen
In the R-Fe-N-based magnetic material, the amount of nitrogen is less than 3 per R ₂ Fe ₁₇ when attempting to optimize the magnetic properties, and thermodynamically unstable R ₂ Fe ₁₇ N _{3- Δ} phase occurs. This phase is easily decomposed into an α-Fe decomposition phase and a rare earth nitride by thermal and mechanical energy, and as a result, conventional shock wave compression cannot provide a high-performance solid material for magnets.

On the other hand, in the R—Fe—N—H type magnetic material, if hydrogen is controlled within the range defined above, the main phase thereof is usually thermodynamically stable R ₂ Fe. ₁₇ N ₃
The H _x phase or the R ₂ Fe ₁₇ N _{3 + Δ} H _x phase containing excess nitrogen (usually x is in the range of about 0.01 to 2) becomes an α-Fe decomposition phase by thermal and mechanical energy, and Decomposition into a rare earth nitride phase is significantly suppressed as compared with the Th ₂ Zn ₁₇ type R—Fe—N based magnetic material containing no H. This is nothing but an important finding for obtaining a magnetic solid material having high magnetic properties and excellent thermal stability and oxidation resistance.

The solid material for magnets of the present invention is R-Fe-N.
A material containing 80 to 97% by volume of an H-based magnetic material. A portion of 3 to 20% by volume other than the R—Fe—N—H-based material may be vacuum, or may be an element, a compound, or a mixture thereof having a density of 6.5 g / cm ³ or less.

The density of the solid material for magnets of the present invention is 6.15.
It is preferably set to be about 7.45 g / cm ³ . 6.15
Even if it is less than g / cm ³ , it may be preferable if the component of the R—Fe—N—H magnetic material is 80% by volume or more. Further, even if the R-Fe-N-H based magnetic material is 97% by volume or less, it may exceed 7.45 g / cm ^{3, and} thus the characteristics of the solid magnetic material of the present invention which are lighter than existing solid magnets are characterized. Sometimes it can not be used. For example, Sm ₂ F
e ₁₇ N ₃ H _0.1 true density of magnetic material is 7.69 g / cm
³ (IEEE Trans. Magn., MAG-2
8, pages 2326, and Powder D by ICDD
However, if the content of the magnetic material is 80 to 97% by volume, the density is 6.15 to 100% by volume, assuming that the gas other than the magnetic material has a sufficiently low density such that it can be ignored. 7.4
It becomes 6.

The true density referred to here is the density w / v obtained from the volume v of the R—Fe—N—H unit cell obtained from X-rays and the total w of the atomic weights of the atoms constituting the unit cell. And is generally called X-ray density D _x . Also, the density D of the solid material for magnets
_m can be obtained by a macro method such as the Archimedes method or the volume method.

Although the relationship between the volume fraction and the density of the R—Fe—N—H-based material changes depending on the composition of the R—Fe—N—H-based material and the type of portion other than the magnetic material, it has good thermal stability. A magnetic material content of 80% by volume or more is required to obtain a solid material for magnets, and a density of 7.45 g / cm ³ or less is required to obtain a lightweight solid material for magnets. The solid material contains R-Fe-N-H based magnetic material in an amount of 80 to 97% by volume and has a density of 6.15 to.
It is in the range of 7.45 g / cm ³ .

The more preferable range of the volume fraction of the R—Fe—N—H magnetic material or the density of the solid material for magnets is 83 to 97% by volume for the use where heat stability is required. A density of 6.35 to 7.45 g / cm ³ is selected, and in order to obtain a lightweight magnet having excellent mechanical strength, magnetic properties and thermal stability, the density is 85 to 96% by volume. A range of 6.50 to 7.40 g / cm ³ is selected.

In the solid material for a magnet of the present invention, the relationship between the residual magnetic flux density B _r at room temperature, the coercive force H _{cJ at} room temperature, the permeance coefficient P _c when used as a magnet and the maximum operating temperature T _max is μ ₀ . _Assuming that the magnetic permeability is in vacuum, B _r ≤ μ ₀ H _cJ (P _c +1) (11000-50T _max ) /
(10000-6T _max ) is more desirable. The above relational expression is an expression that defines the condition under which the magnet does not significantly demagnetize, and its meaning will be supplemented below. Here, the remarkable demagnetization refers to irreversible and large demagnetization, for example, demagnetization such that the irreversible demagnetization rate exceeds −20% within 1000 hours.

B representing the change in magnetization with respect to the reverse magnetic field of the magnet
-The H coordinate of the bending point on the -H curve has a squareness ratio of about 1
When it is 00%, the value is almost H _cJ . When the operating point of the magnet is on the higher magnetic field side than the bending point, it is demagnetized rapidly and the performance of the magnet cannot be effectively exhibited.
The operating point should be on the lower magnetic field side than the inflection point. Therefore, the ratio of the magnetic flux density to the demagnetizing field determined by the shape of the magnet is the internal permeance coefficient P _c0 , and the permeance at each operating point, which is determined by the magnitude of the reverse magnetic field applied to the magnet during operation, after being incorporated as a magnet in a magnetic circuit or device. When the smallest permeance coefficient among the coefficients is P _c , P _c0 and P _c
If the smaller one of them is set to P _cmin , significant demagnetization will occur unless it is at least the following expression (1).

[0030]

[Equation 1]

Equation (1) is a conditional equation at room temperature, and at temperature T ° C., the temperature coefficient of residual magnetic flux density [α
(B _r )] and the temperature coefficient of coercive force [α (H _cJ )], it is rewritten as the following equation (2) to determine the condition under which significant demagnetization does not occur.

[0032]

[Equation 2]

If P _c0 is smaller than P _c and demagnetized immediately after the magnetic field is removed even if magnetized, it is possible to remarkably demagnetize the magnet by previously incorporating it in a yoke or the like. However, if the condition defined by the equation (2) is not satisfied at least, the demagnetization due to the use of the magnet cannot be avoided.

[0034] by R-Fe-N-H-based composition and temperature range of the material _{α (B r), α (} H cJ) is the value varies substantially alpha (B _r) is -0.06% / ° C., α (H _cJ ) is -0.5
% / ° C. Since the absolute value of α (H _cJ ) is larger than the value of α (B _r ) and both are negative values, the higher T is, the combination of positive values (B _r , H
The area of _cJ ) becomes small. Accordingly, magnet made using a magnet for solid materials of the present invention, when used under the condition of permeance coefficient P _c, B in a range that is determined in (2) below the temperature T _{m ax} ° C. which is greatest during operation By controlling _r and H _cJ , demagnetization of the magnet can be alleviated. In the equation (2), T = T _max , α (B _r ) = − 0.0
Substituting 6 and α (H _cJ ) = − 0.5 and rearranging gives the following formula (3).

[0035]

[Equation 3]

That is, when a magnet is used, B _r , H _cJ , P _c ,
If T _max satisfies the expression (3), it can be said that the magnet does not cause significant demagnetization. According to the equation (3), the larger the value of H _cJ , the larger the value that B _r can take. In order to obtain a magnet having high thermal stability and high magnetic properties, it is preferable to use a solid material for magnet having H _cJ exceeding 0.62 MA / m.

By the way, even if B _r is increased by increasing the volume fraction of the magnetic material to obtain a solid material for magnet having a high maximum energy product (BH) _{max at} room temperature, T
_{When the} temperature is high such that _max is, for example, 100 ° C. or more and deviates from the range of the equation (3), demagnetization becomes remarkable, the volume fraction of the magnetic material is low, and the solid material for magnet with small B _r and performance are May not change.
That is, the combination of P _c and T _max and H of the solid material for magnets
_{Depending on cJ} , there is no point in increasing the volume fraction of the R—Fe—N—H magnetic material and increasing B _r . Rather, lowering the volume fraction of the magnetic material results in a solid material for magnets that is lightweight and has high cost performance.

A specific example will be described. H _cJ = 0.
If R-Fe-N-H based magnetic powder of 62 MA / m is used as a raw material and shock wave compression is used, it is almost 1 under certain conditions.
It can be a solid material for magnets having a volume fraction of 00%. At this time, B _r exceeds 1.2T. But,
In the case of applications where P _c = 1 and T _max = 100 ° C., it is not necessary to set B _r to 0.99 T or more from the equation (3). That is,
In this case, even if the solid material for magnet has B _r higher than 0.99 T, it will be demagnetized by the operation or use of the magnet, and the performance will be the same as that of the magnet having B _r of 0.99 T. . Therefore, by lowering the volume fraction of the magnetic substance to about 83% to 85%, B _r = 0.99
It is preferable to use a magnet having a size of about T, which is lightweight and inexpensive.

The above is the minimum permeance coefficient determined by the shape or magnetic circuit of the magnet, the operation, and B _r , H.
_The thermal stability is determined by the magnetic characteristics of the magnetic material such as _cJ , α (B _r ), and α (H _cJ ), which is a property generally called the temperature characteristic of the magnet.

In addition to the above, a major cause of the decrease in thermal stability is that the magnetic powders are not sufficiently solidified by being bonded by a metal bond. Originally, permanent magnets have the easy magnetization directions of the crystals aligned in order to create a magnetostatic potential in the external world, but because they are in a magnetically non-equilibrium state, magnetic powders are not sufficiently bonded and fixed. Then, each magnetic powder rotates in the matrix to change the direction of the easy magnetization direction, and the stored magnetostatic energy gradually decreases.

For a material having a magnetic powder filling rate of less than 80%, for example, a bonded magnet, when the resin is softened or deteriorated at a high temperature of 100 ° C. or higher, the above-mentioned relaxation occurs relatively easily and remarkable demagnetization occurs. It will be. As its name implies, a bonded magnet is a magnet that is bonded with a binder, not a magnet that is solidified by metal bonding. It can be said that the lack of thermal stability is a problem resulting from that.

On the other hand, in the case of the material of the present invention, since the volume fraction is 80% or more or 83% or more, the magnetic powders are solidified by the metal bond and such relaxation does not occur. As described above, in order to achieve satisfactory thermal stability at 100 ° C. or higher, it is necessary to control the lower limit and the upper limit of the volume fraction of the magnetic material within a specific range.

The solid material for a magnet according to the present invention has a coercive force H _cJ of 0.76 when formed into a magnet without using a special method.
A solid material for magnets having a MA / m or more and a squareness ratio B _r / J _s of 95% or more can also be used. However, J _s is a saturation magnetization at room temperature, and is a magnetization value in the present invention when the external magnetic field is 1.2 MA / m.

For example, the Sm ₂ Fe ₁₇ N ₃ H _0.1 material has a nucleation-type magnetic field reversal mechanism, so that the grain size and the coercive force H _cJ have a relationship that is substantially inversely proportional. 2 μm
When it is less than 1.0, the coercive force exceeds 0.76 MA / m, but in this region, the magnetic powder tends to aggregate as the particle size of the magnetic powder becomes smaller. Falls sharply and the squareness ratio decreases.

FIG. 1 shows a ball mill using Sm ₂ Fe ₁₇ N ₃ H
Magnetic powders of various particle sizes obtained by pulverizing _0.1 powders were compression-molded under an external magnetic field of 1.2 MA / m and a molding pressure of 14 ton / cm ² , and their coercive force H _cJ and squareness ratio B _{r were obtained.} The relationship between / J _s (● in the figure) is shown. H _cJ is 0.73 MA /
When it exceeds m, the squareness ratio drops sharply and H _cJ is 0.76M.
It becomes 95% or less at A / m or more.

The solid material for a magnet of the present invention can make the structure fine when shock-wave-compressed and solidified. Therefore, a magnetic powder having a coercive force of less than 0.76 MA / m is used to obtain a squareness ratio It is possible to prepare a high green compact, compress and solidify it by shock waves, and at the same time improve the coercive force to obtain a solid magnet material having both a high squareness ratio and a high coercive force. When the coercive force is in the range of 0.8 to 1.2 MA / m, the squareness ratio is 95
%, It is possible to adjust in a range of almost 100% by adding a method such as a magnetic field orientation method and a component of a magnetic material.

In the solid material for magnet of the present invention, R-F
Components other than the e-N-H magnetic material have a density of 6.5 g / cm.
It is preferably an element, a compound or a mixture of ³ or less. Even if the volume fraction of the magnetic material is limited to 80% if the density of the element exceeds 6.5 g / cm ³ ,
In many cases, the total density of the solid material for magnets exceeds 7.45 g / cm ³ , which is not preferable because the lightweight feature of the present invention cannot be utilized.

Elements having a density of 6.5 g / cm ³ or less include Al, Ar, B, Be, Br, C, Ca, Cl,
F, Ga, Ge, H, He, Kr, Mg, N, Ne,
Examples thereof include O, P, S, Se, Si, Te, Ti, V, Y and Zr. Even if these compounds or alloys or elements having a density of 6.5 g / cm ³ or more are contained, Mn-
A compound or alloy having a density of 6.5 g / cm ³ or less such as Al-C or Al-Cu-Mg alloy, or a mixture having a volume ratio of 1: 1 such as Bi-Al has a density of 6.5 g. It is also preferable that it is less than / cm ³ .

At least one kind of gas having a density of 6.5 g / cm ³ or less in the portion other than the R—Fe—N—H magnetic material, for example, inert gas such as air, nitrogen gas, He, Ar and Ne. May be These solid materials for magnetic material-gas composite magnets are characterized by being lightweight.

Further, the portions other than the R—Fe—N—H magnetic material are MgO, Al ₂ O ₃ , and the density of 6.5 g / cm ³ or less.
ZrO ₂ , SiO ₂ , oxides such as ferrite, Ca
Fluorides such as F ₂ and AlF ₃ , TiC, SiC, ZrC
And the like, and nitrides such as Si ₃ N ₄ , ZnN, and AlN are preferable, and also hydrides, carbonates, sulfates, silicates, chlorides, nitrates, and mixtures thereof. good. Among these, especially BaO ・ 6Fe
₂ O ₃ series, SrO · 6Fe ₂ O ₃ series, hard magnetic ferrite such as La-added ferrite series, and in some cases Mn-Zn
Incorporation of Ni-Zn system soft magnetic ferrite and the like can improve magnetic characteristics and stability thereof. These solid materials for magnetic material-inorganic composite magnet have high mechanical strength and excellent thermal stability and magnetic properties.

Further, the portion other than the R—Fe—N—H magnetic material may be an organic substance having a density of 6.5 g / cm ³ or less. For example, resins called engineering resins such as polyamide, polyimide, polyphenylene oxide, and wholly aromatic polyester, liquid crystal polymers, epoxy resins, phenol-modified epoxy resins, unsaturated polyester resins, alkyd resins, fluororesins, and other heat-resistant thermoplastics. Alternatively, thermosetting resins, organosilicon compounds such as silicone rubber, organometallic compounds such as coupling agents and lubricants, and the like have glass transition points, softening points, melting points, and decomposition points of 10 or less.
Any organic substance having a temperature of 0 ° C. or higher can be used as a component of the magnet solid material of the present invention. However, the volume fraction thereof is 20% or less, preferably 17% or less, and R-Fe
It should not interfere with the solidification of the —N—H magnetic material due to the metal bond. This magnetic material-organic compound magnet solid material is excellent in impact resistance in spite of being lightweight. However, in a severe environment of high temperature and high humidity, it may be better not to use the solid material for magnetic material-organic compound magnet.

R-Fe-N- of the magnet solid material of the present invention
Two or more kinds of the above-mentioned gas, inorganic substance, and organic substance can be contained at the same time in the portion other than the H-based magnetic material. For example, it is a solid material for R-Fe-NH magnetic material-gas-inorganic-organic compound magnet having voids which are air and containing silicone rubber in which silica is dispersed. It is desirable to make the most of it and use it properly according to the purpose.

Next, the method for producing the solid material for a magnet of the present invention will be described. However, the production method of the present invention is not limited to this. In the solidification step by the shock compression method of the present invention using shock waves in water, the ultrahigh-pressure shearing property and the activation effect of the shock waves induce the solidification effect due to the metallic bond of the powder and the micronization effect of the structure, and the solidification occurs. Along with this, high coercive force is possible. At this time, the duration of the shock pressure itself is longer than in the case of using the conventional shock wave, but the temperature rise due to the volume compression and the increase in entropy due to the non-linear phenomenon of the shock wave disappears in a very short time (several μs or less). And as a result,
Almost no decomposition or denitrification occurs.

The residual temperature is present even after compression with underwater shock waves. This residual temperature is the decomposition temperature (about 600 at normal pressure).
(° C.) or higher, decomposition of the R—Fe—N—H-based compound or the like will start and the magnetic characteristics will deteriorate, which is not preferable. However, it is much easier to keep the residual temperature lower when using the underwater shock wave than when using the conventional shock wave.

Further, by carrying out the powder compacting in a stationary magnetic field of 80 kA / m or more, preferably 800 kA / m or more, or a pulsed magnetic field, the easy axis of magnetization of the powder can be aligned in one direction, and thus obtained. Even if the green compact is impact-compressed and solidified, the orientation is not impaired, and a solid magnetic material body having magnetic uniaxial anisotropy can be obtained.

In the present invention, the shock wave pressure is set to 3 in order to suppress the temperature rise of the green compact during shock compression.
It is necessary to use an underwater shock wave of ~ 22 GPa. If the shock wave pressure is lower than 3 GPa, the density is not always 6.15 g /
A solid material for a magnet having a size of cm ³ or more cannot be obtained. If the shock wave pressure is higher than 40 GPa, decomposition products such as α-Fe decomposition phase may occur, which is not preferable. Furthermore, the density is 6.
In the range of 35 to 7.45 g / cm ³ , further 6.50 to
In order to obtain a solid material for magnet in the range of 7.40 g / cm ³ with good reproducibility, the shock wave pressure of the underwater shock wave is 3 to 20 GPa,
Further, it is achieved by setting the shock wave pressure to 4 to 15 GPa. However, in the magnetic material-gas composite magnet solid material, if the impact pressure is too high, the density easily becomes 7.45 g / c.
It is preferable to use an underwater shock wave having a shock wave pressure of 3 to 15 GPa because it becomes a solid material for a magnet exceeding m ³ .

As a shock compression method using an underwater shock wave,
By powder compacting the powder inside the double tube, putting water in the middle part, placing explosives on the outer periphery, and detonating the explosives,
Introducing a shock wave into the water in the middle part, a method of compressing the powder in the innermost part, compacting the powder into a closed container, putting it into water, and detonating the explosive in water, A method of compressing the powder by the shock wave, and Japanese Patent No. 29513
The method according to Japanese Patent Laid-Open No. 49 or Japanese Patent Application Laid-Open No. 6-198496 can be selected, and in any method, the following advantages of shock compression by an underwater shock wave can be obtained.

That is, (1) The pressure of the underwater shock wave is determined by the Yugonio relationship between the explosive and the water, and the pressure P is roughly expressed by the following equation. P = 288 (MPa) {(ρ / ρ ₀ ) ^7.25 −1} From the above equation, when the underwater shock wave is used, the increase amount of the pressure P is extremely large with respect to the change of the water density ρ with respect to the reference time density ρ ₀ . Because of its large size, it is possible to easily obtain an ultrahigh pressure by adjusting the amount of explosive, and the temperature of the magnetic material at that time is easily kept at a low temperature as compared with the case of using a conventional shock wave. (2) The duration of the impact pressure itself is longer than that when the conventional shock wave is used. (3) The temperature rise of the magnetic material due to the volume compression and the increase in entropy due to the nonlinear phenomenon of the shock wave disappears in an extremely short time. (4) The temperature of the magnetic material is rarely kept high thereafter, and is rarely kept long. (5) Impact pressure is evenly applied to the object to be compressed. Due to these excellent characteristics of underwater shock waves, R-
The Fe-N-H-based material does not cause thermal decomposition and is easily compressed and solidified by the metal bond.

As described above, R-Fe-N, which is thermally stable as a magnetic powder and is hard to precipitate an α-Fe decomposition phase.
The volume fraction of the magnetic material is 80 to 80 for the first time by selecting the -H magnetic material and molding it by the shock wave compression method.
It is possible to produce a solid material for magnets having a density of 97% and a density of 6.15 to 7.45 g / cm ^{3. Since the} solid material for magnets has a high magnetic property and is solidified by metal bonding. In addition, it has excellent heat stability.

Next, the apparatus or parts of the present invention will be described.
It Maximum operating temperature T_maxFor applications where the temperature is 100 ° C or higher
Is a conventional R-Fe-N-H based bonded magnet.
It contains a fat component and the magnetic powders are solidified by metal bonding.
Therefore, it has poor thermal stability and is difficult to use.
It was If the solid material for a magnet of the present invention is a yoshinba resin
R-Fe-N-H magnetic powders are metallic even if they contain
Has excellent thermal stability because it is solidified by bonding. Further magnet
Solid material B _r, H_cJIs P when magnet is used_cAnd T
_maxAnd if it is in the area defined by equation (3), it will be greatly reduced.
Non-magnetism, light weight, high cost performance and heat stability
It is possible to obtain a magnet having excellent properties.

[0061] The upper limit of T _max is the vicinity of the Curie point of the R-Fe-N-H-based materials, but exceeding 400 ° C., the composition and components of the solid material magnet for a magnet, T _{ma x} by people used as a magnet The upper limit takes various values of 400 ° C. or lower. For example,
Zn coated _Rc -Fe- with _HcJ = 1.6 MA / m
Even if the N—H-based material is used, it cannot be used as the magnet of the present invention when T _max is 220 ° C. or higher.

The P _c0 of the magnet obtained by the solid material for a magnet of the present invention is 0.01 to 100, more preferably 0.
1 to 10, and when the combination of the values of P _c0 , B _r , and H _cJ deviates from the range of the formula (1), the yoke is mounted and then P _c0 is increased, and then the magnetization is performed. Is preferred.

Various actuators, voice coil motors, linear motors, motors for rotating machines as rotors or stators using the static magnetic field of magnets obtained from the solid material for magnets of the present invention, among them, especially for industrial machines and automobiles In addition to magnetic field sources for motors, medical equipment and metal sorters, VSM
Generator, ESR device, magnetic field generator for analyzer such as accelerator,
Devices and parts such as magnetron traveling wave tube, OA equipment such as printer heads and optical pickups, undulators, wigglers, retarders, magnet rolls, magnet chucks, and various magnet sheets, except for special applications such as stepping motors with extremely small P _c. 1
Even in an environment of 00 ° C. or higher, it can be used stably without significant demagnetization.

Depending on the application, it can be used at a temperature of 125 ° C. or higher. For example, H _cJ > 0.7 (MA / m) and P _c > 1.
There is a case where Furthermore, use at 150 ° C. or higher is also possible, and for example, there is a case where H _cJ > 0.8 (MA / m) and P _c > 2. When used in these devices or parts, after subjecting the solid material for magnets of the present invention to various processes, the yokes and hole pieces of various shapes and various magnetic shunting materials are bonded, adhered, and joined together before use. May be.

The present invention will be described below based on examples. The degree of decomposition of the R-Fe-N-H magnetic material is determined by the X-ray diffraction diagram (Cu-Kα) of the molded solid material for magnet.
Line), the diffraction angle 2θ is 4 with respect to the height a of the strongest line in the diffraction lines derived from the rhombohedral or hexagonal crystal structure.
Ratio b of heights b of diffraction lines derived from α-Fe decomposition phase near 4 degrees
Judged by / a. If this value is 0.2 or less, it can be said that the degree of decomposition is small. It is preferably 0.1 or less. More preferably, it is 0.05 or less, and in this case, it can be said that there is almost no decomposition.

[0066]

[Embodiment 1] FIG. 2 is an explanatory view showing an example of means for carrying out an impact compression method using an underwater shock wave. A Sm ₂ Fe ₁₇ mother alloy having an average particle size of 60 μm was applied to NH ₃ partial pressure of 0.35a.
After performing hydrogen nitridation at 450 ° C. for 9 ks in an ammonia-hydrogen mixed gas stream having a tm and H ₂ partial pressure of 0.65 atm,
It was annealed for 3.6 ks in an argon stream and then pulverized to 2 μm by a jet mill. 1.2 of this powder
As shown in FIG. 2, the compact obtained by performing the powder compacting while orienting the magnetic field in the magnetic field of MA / m was put in the copper pipe 1 and fixed to the copper plug 2. Further, the copper pipe 3 is fixed to the copper plug 2, and further, the gap is filled with water, a uniform gap is provided in the outer peripheral portion, the paper cylinder 4 is arranged, and 200 g of the ammonium nitrate-based explosive 5 is placed in the gap. It was loaded and the above explosive was detonated from the detonator 6 to detonate the explosive. The shock wave pressure at this time was 14 GPa. Sm _9.0 Fe _76.1 N _13.4 solidified from pipe 1 after impact compression
Take out the magnet solid material of composition H _1.5 , 4.0M
It was magnetized with a pulsed magnetic field of A / m and the magnetic characteristics at room temperature were measured. As a result, the saturation magnetization J _s = 1.21T and the residual magnetic flux density B _r
= 1.19 T, coercive force H _cJ = 0.73 MA / m, and maximum energy product (BH) _max = 243 kJ / m ³ .
Moreover, as a result of measuring the density by the Archimedes method, 7.4
It was 0 g / cm ³ . At this time, the volume fraction of the R—Fe—N—H magnetic material was 96.2%. Further, as a result of analysis by X-ray diffraction, it is found that the solidified solid material for magnet has almost no precipitation of α-Fe decomposition phase and has a crystal structure of Th ₂ Zn ₁₇ type rhombohedral crystal. confirmed.

The same experiment was repeated many times by adjusting the amount of explosive. It has been confirmed that when the shock wave pressure is higher than 15 GPa, the density often exceeds 7.45 g / cm ^3, and when the shock wave pressure is higher than 40 GPa, decomposition products such as α-Fe decomposition phase are generated. In order to obtain a magnet solid material having a density of 6.15 to 7.45 g / cm ³ with good reproducibility, the shock wave pressure is set to 3 to 15%.
It has also been found that it is preferable to use GPa.

[0068]

EXAMPLE 2 A ball mill was used as the crushing method for the R—Fe—N—H magnetic material, and the components other than the R—Fe—N—H magnetic material and the shock wave pressure were as shown in Table 1. Except for the above, a solid material for a magnet was prepared in the same manner as in Example 1,
After magnetized with a pulse magnetic field of 4.0MA / m, B _r, H
_{The cJ} , squareness ratio B _r / J _s , and (BH) _max were measured. The results are shown in Table 1. The squareness ratio was 96%, even though H _cJ was a large value of 0.81 MA / m. The results are shown by ◯ in FIG. 1 and compared with the case of a normal compression molded body.

[0069]

[Examples 3 to 5] Solid materials for magnets were prepared in the same manner as in Example 1 except that the components other than the R-Fe-NH magnetic material and the shock wave pressure were as shown in Table 1. Example 2
The various magnetic properties were measured in the same manner as in. The results are shown in Table 1.

[0070]

[Table 1]

[0071]

Comparative Example 1 A Sm _9.1 Fe _77.9 N _13.0 magnetic material was obtained by the same operation as in Example 1 except that Sm ₂ Fe ₁₇ mother alloy having an average particle diameter of 20 μm was nitrided in N ₂ gas stream at 495 ° C. for 72 ks. It was This powder was pulverized to 2 μm, and a solid material for magnet was produced by the same method as in Example 1. The magnet was magnetized with a pulse magnetic field of 4.0 MA / m and the magnetic characteristics at room temperature were measured. As a result, the saturation magnetization J _s = 1.22T, the residual magnetic flux density B _r = 0.93T, and the coercive force H _cJ = 0. .34 MA /
m, maximum energy product (BH) _max = 113 kJ / m ³ . The density was measured by Archimedes' method and found to be 7.23 g / cm ³ . In the X-ray diffraction pattern of this material, in addition to the crystal structure of Th ₂ Zn ₁₇ type rhombohedral crystal, α-
A diffraction line derived from the Fe decomposition phase was also observed. Diffraction angle 2θ is 4
Diffraction line of α-Fe decomposition phase and Th ₂ Zn around 4 degrees
The intensity ratio b / a to the (303) strongest line showing the crystal structure of the _17- type rhombohedral crystal was 0.22.

[0072]

COMPARATIVE EXAMPLE 2 As shown in FIG. 3, a copper pipe 1 was prepared by using the R—Fe—N—H magnetic powder having an average particle diameter of 2 μm in Example 1 as an example.
And then fixed to a copper plug 2 with a uniform gap provided on the outer periphery, a paper cylinder 4 is placed, and the same amount of ammonium nitrate-based explosive 5 as in Example 1 is loaded into the gap, and the initiator 6 is used to I detonated explosives and detonated them. After impact compression, the solidified sample was taken out of the pipe 1 and analyzed by X-ray diffraction. As a result, it was confirmed that an SmN phase and a large amount of α-Fe decomposition phase were produced after impact compression, and the starting material Sm -F
It was found that the e-N-H compound was decomposed. The strength ratio b / a at this time was 3.2.

[0073]

Example 6 and Comparative Examples 3 and 4 Using magnetic powder of Sm _9.0 Fe _76.4 N _13.5 H _1.1 having an average particle size of 2.5 μm and shock wave pressure of 3 GPa (Example 6) and 23 G
A solid material for a magnet was produced in the same manner as in Example 1 except that Pa (Comparative Example 3) was used. The magnetic characteristics of these solid materials for magnets were measured in the same manner as in Example 1. The results are shown in Table 2.

Further, these solid materials for magnets were processed into discs of exactly the same shape and magnetized with a pulse magnetic field of 4.8 MA / m to obtain magnets with P _c0 of 2. 12 these magnets
It was left for 3.6 Ms in a thermostat bath at 5 ° C, taking care not to apply a reverse magnetic field as much as possible. Using a sample pull-out type magnetic flux measuring device, the value of the magnetic flux before and after being left in a constant temperature bath was measured, and the change rate of the magnetic flux, that is, the irreversible demagnetization rate (%) was obtained. The results are shown in Table 2. It can be judged that the smaller the absolute value of the irreversible demagnetization rate, the better the thermal stability. Further, the irreversible demagnetization ratio was determined in the same manner as above for the injection-molded bonded magnet (Comparative Example 4) using a binder of 12-nylon having a magnetic powder volume ratio of 60% and a P _c0 of 2 by a known method. The results are shown in Table 2.

[0075]

[Table 2]

The result obtained by the above evaluation is P _c
Is equal to P _c0 and T _max = 125 ° C., it is appropriate to examine the degree of demagnetization before and after operation or use.

As shown in Table 2, as in Comparative Example 4, R
When the volume fraction of the —Fe—N—H-based magnetic material was less than 80%, the magnetic powders did not solidify with each other due to metal bonds, and thus showed extremely low thermal stability. Further, even though the magnetic powders are solidified by the metal bond, P _c , T _max , B _r ,
It was also found that the thermal stability of Comparative Example 3 in which H _cJ did not satisfy the expression (3) was considerably worse than that of Example 6 in which the expression [3] was satisfied.

[0078]

Example 7 and Comparative Example 5 A DC motor with a brush was assembled by fixing two magnets of Example 6 without using a yoke and using a stator, and applying a certain amount of electric power to the coil at 100 ° C. Was operated for 36 ks under the environment (Example 7). In addition, a motor was assembled using the magnet of Comparative Example 3 in the same manner as above and operated in the same manner (Comparative Example 5). The rotation speed after 36 ks changed by about 2% in the motor of Example 7 and about 10% in the motor of Comparative Example 5 as compared with immediately after the initial rotation speed stabilized, and the rotation speed after 36 ks was almost 510 rpm in both cases.
Was the same. The magnet of Comparative Example 3 used in the motor of Comparative Example 5 has a density 17% higher than that of the magnet of Example 6 used in the motor of Example 7, and the volume fraction of the R—Fe—N—H magnet is higher. Despite the high price, the performance with the above motor was the same.

[0079]

[Embodiment 8] In Embodiment 6, the components other than the R—Fe—N—H magnetic material are ZrO ₂ , and the shock wave pressure is 14 G.
A magnet having a density of 7.38 g / cm ³ was prepared in the same manner except that the pressure was changed to Pa, and a motor was assembled in the same manner as in Example 7 and operated in an environment of 100 ° C. As a result, Example 7
The result was equivalent to.

[0080]

INDUSTRIAL APPLICABILITY According to the present invention, rare earth-iron-nitrogen-hydrogen system magnetic powder having a specific composition and crystal structure is compacted by compaction and shock-compressed by an underwater shock wave, so that self-sintering can be performed. It is possible to obtain a solid material for a rare earth-iron-nitrogen-hydrogen-based magnet, which prevents decomposition and denitrification, is lightweight, has high performance, and particularly has high thermal stability.

[Brief description of drawings]

FIG. 1 is a magnetic solid material (●) obtained by magnetic field compression molding magnetic powders of various particle sizes obtained by ball-milling an Sm ₂ Fe ₁₇ N ₃ H _0.1 magnetic material, and a solid magnetic material of Example 2. It is a figure showing the relation between coercive force of (○) and squareness ratio.

FIG. 2 is an explanatory view showing an example of means for carrying out an impact compression method using an underwater shock wave.

FIG. 3 is an explanatory view showing a means for carrying out an impact compression method directly using a detonation wave of explosive used in a comparative example.

[Explanation of symbols]

1 Copper pipe (used to hold powder) 2 Copper plug 3 Copper pipe (used to hold water) 4 paper cylinders (used to hold explosives) 5 explosives 6 detonator

   ─────────────────────────────────────────────────── ─── Continued front page    (72) Inventor Ichiro Shibasaki             Asahi Kasei Co., Ltd. 1 No. 2 Samejima, Fuji City, Shizuoka Prefecture             In the company (72) Inventor Nobuyoshi Imaoka             Asahi Kasei Co., Ltd. 1 No. 2 Samejima, Fuji City, Shizuoka Prefecture             In the company (72) Inventor Akira Chiba             2-29-605, Suizenji 2-chome, Kumamoto City, Kumamoto Prefecture F term (reference) 5E040 AA03 AA19 BB01 CA01 HB06                       NN04 NN12 NN13

Claims (12)

[Claims] 1. A rare earth-iron-nitrogen-hydrogen based magnetic material having a rhombohedral or hexagonal crystal structure in an amount of 80 to 97% by volume.
A solid material for a magnet, characterized by containing. 2. A rare earth-iron-nitrogen-hydrogen based solid material for magnets having a rhombohedral or hexagonal crystal structure, which has a density of 6.15 to 7.45 g / cm ³ . 3. A residual magnetic flux density B _r at room temperature, a coercive force H _{cJ at} room temperature, and a permeance coefficient P _c when used as a magnet.
And the maximum operating temperature T _max , where μ ₀ is the magnetic permeability of vacuum, B _r ≦ μ ₀ H _cJ (P _c +1) (11000-50T _max ) /
(10000-6T _max) solid material for a magnet according to claim 1 or 2, characterized in that a. 4. A coercive force H _cJ of 0.76 MA / m or more,
Moreover, the solid material for magnet according to any one of claims 1 to 3, wherein the squareness ratio B _r / J _s is 95% or more. 5. The element other than the rare earth-iron-nitrogen-hydrogen based magnetic material is an element or compound having a density of 6.5 g / cm ³ or less, or a mixture thereof.
The solid material for a magnet according to any one of 1. 6. The magnet according to claim 1, wherein at least one of the atmosphere and an inert gas is contained in a portion other than the rare earth-iron-nitrogen-hydrogen based magnetic material. Solid material. 7. An oxide, a fluoride, a carbide, a nitride, a hydride, a carbonate, a sulfate, a silicate, a chloride and a nitrate of at least a portion other than the rare earth-iron-nitrogen-hydrogen based magnetic material. It contains 1 type, Claim 1 characterized by the above-mentioned.
7. The solid material for magnets according to any one of to 6. 8. The organic material is contained in a portion other than the rare earth-iron-nitrogen-hydrogen based magnetic material.
7. The solid material for magnets according to any of 7. 9. A rare earth-iron-nitrogen-hydrogen based magnetic material or a mixture of the magnetic material and other constituents having a shock wave pressure of 3 to 22.
The solid material for magnets according to any one of claims 1 to 8, wherein the solid material is compressed and solidified using an underwater shock wave of GPa. 10. The rare earth-iron-nitrogen-hydrogen based magnetic powder is compacted in a magnetic field and then compressed and solidified using an underwater shock wave. A method for manufacturing a solid material for a magnet. 11. A component for use in an apparatus utilizing a static magnetic field of a magnet, which component uses the solid material for a magnet according to any one of claims 1 to 9. 12. An apparatus having a maximum operating temperature T _max of 100 ° C. or higher utilizing a static magnetic field of a magnet, characterized by using the component according to claim 11 as a component thereof.