JPH10154610A - Manufacturing method of anisotropic magnet powder, anisotropic magnet powder and anisotropic bond magnet - Google Patents

Abstract

PROBLEM TO BE SOLVED: To make feasible of manufacturing anisotropic magnet powders having excellent magnetic characteristics and reliability by a method wherein quenched alloy powders in a specific composition filled in a metallic capsule is hot processed to align the readily magnetizable axial direction of a main phase crystalline particles for providing the anisotropy. SOLUTION: The anisotropic magnet powders represented by a formula, after filling up an SS 41 made box type capsule with quenched alloy powders 1 containing impurities indispensable for manufacture, are hot processed to be aligned in the readily magnetizable axial direction of TbCu 7 type structure in the constitutional structure for the manufacture. Provided that in the formula, R1 represents an element out of rare earth elements including Y, R2 represents an element selected from a group of Zr, Hf, Sc, M represents an element selected from a group of Ti, Si, V, Cr, Mo, Mn, W, Ni, Ca, Cu, Al, Nb, Sn, Ag, Ta while x, y, z, u respectively satisfies the inequalities mentioned as follows, i.e., 2<=x, 0.01<=y, 4<=x+y<=20, 0<=z<=40, 0<=u<=20 in atomic %.

Description

DETAILED DESCRIPTION OF THE INVENTION

[0001]

BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to an anisotropic rare earth bonded magnet material having a high performance and a high degree of freedom in shape, and more particularly to a method for producing an anisotropic magnet powder, an anisotropic magnet powder, and an anisotropic magnet powder. Related to an isotropic bonded magnet.

[0002]

2. Description of the Related Art Rare earth magnets, such as Nd-Fe-B based sintered magnets, are magnets that offer unprecedented high performance.
It has greatly contributed to the miniaturization and low power consumption of electronic devices such as devices. Above all, resin-bonded magnets in which magnet powder is bonded with a resin as a binder, so-called bond magnets, are extremely excellent in shape flexibility, such as making ring magnets that are difficult to manufacture with bulk magnets such as sintering. Taking advantage of the advantages, the market is growing significantly, mainly for applications such as various spindle motors for OA and stepping motors.

[0003] Rare earth bonded magnet materials include an anisotropic bonded magnet in which hard magnetic phase crystal grains in the constitutional structure have an easy axis of magnetization in almost one direction, and an easy axis of crystal grains in a random direction. And isotropic bonded magnets.

As an isotropic bonded magnet material, a bonded magnet using an Nd-Fe-B-based magnet powder produced by a liquid quenching method as a raw material and using an epoxy resin or a nylon resin as a binder is mainly used. The constituent structure of the magnet powder is a structure composed of a substantially single phase of the Nd2Fe14B phase.

Further, a magnet material called a spring magnet or a nanocomposite magnet has recently attracted attention as an isotropic bonded magnet material other than the above-mentioned conventional Nd-Fe-B magnet powder. This is in addition to the hard magnetic phase, which makes permanent magnet properties appear as a constituent tissue,
It has a soft magnetic phase such as α-Fe having high magnetization, and furthermore, has a structure in which the crystal grain size is on the order of 10 nm. In general, since a soft magnetic phase undergoes magnetization reversal with a very small coercive force, it has been considered that its coercive force is degraded when present as a permanent magnet material structure, adversely affecting magnet properties. However, in the case of a crystal grain size of the order of 10 nm and having an interface with the hard magnetic phase, since the exchange interaction acts between the crystal grains of the hard magnetic phase and the soft magnetic phase, the magnetization reversal of the soft magnetic phase occurs. Is suppressed by the exchange interaction at the interface with the hard magnetic phase, and the coercive force can be secured. Such materials include Nd2Fe1 as a hard magnetic phase.
4B phase, Nd-Fe-B based material having α-Fe phase and Fe3B phase as soft magnetic phase, Sm2Fe1 as hard magnetic phase
Sm-F having 7Nx phase and α-Fe phase as soft magnetic phase
e-N-based material and SmZr (F
e, Co) 7Nx phase and Sm-Zr- (Fe, Co) -N-based material having an α-Fe phase as a soft magnetic phase.

As an anisotropic bonded magnet, Sm 2 Co 17 is used.
The system is currently accepted by the market. In this method, a heat treatment is applied to an alloy ingot having a specific composition, and then the powder is ground to obtain a powder. By such a manufacturing method,
It is a bonded magnet having a high performance of about 20 MGOe.

Other anisotropic bonded magnet materials include Sd produced by nitriding Nd-Fe-B-based powder or Sm-Fe-based alloy anisotropically formed by the HDDR method.
m-Fe-N powders and the like have been developed.

[0008]

The prior art described above is
It has the following problems.

First, isotropic bonded magnet materials have lower performance than anisotropic bonded magnet materials. Nd-Fe- actually put on the market
The magnetic property (maximum energy product) of the B-based isotropic bonded magnet is at most about 10 to 12 MGOe.

[0010] In the above-described spring magnet having a composite structure of a hard magnetic phase and a soft magnetic phase, a relatively high magnetization can be obtained, but the coercive force is low. As a result, the maximum energy product as a bond magnet is 10 MGOe. It stays at a lower value than below. Further, since the coercive force is low, it is not suitable for use at high temperatures.

On the other hand, an anisotropic bonded magnet can obtain a high energy product. However, the various anisotropic bonded magnets described above have the following problems.

First, the Sm2Co17-based bonded magnet has a high content of Sm, a rare earth element, which is more expensive than Nd, and also contains expensive Co as a main element, making it a very expensive magnet. Although the bonded magnet has the potential to obtain a performance of about 20 MGOe, the price / performance ratio is high and the cost performance is inferior.

Nd-Fe- produced by the HDDR method
The B-based magnet powder is inferior in oxidation resistance because active Nd is used as a rare earth element, and requires a surface coating for actual use. In addition, since the anisotropic method is realized by the method of HDDR, stable manufacturing is difficult, and there is a large variation in characteristics. In particular, it is difficult to stably obtain a sufficient degree of orientation. It is about 15 to 17 MGOe. Furthermore, the temperature coefficient of the coercive force is larger than that of the Sm-Co system, and the coercive force is inferior in magnetization due to the low coercive force and the poor degree of orientation. Therefore, it has not yet been accepted in the market. is there.

The Sm—Fe—N powder is Sm 2 Co 17
Unlike the system and HDDR, the coercive force mechanism is a so-called nucleation type. Therefore, in order to obtain a coercive force, it is necessary to pulverize the magnet powder.
It is required to make fine powder of about μm. However, if such a uniform fine powder is formed into a bond magnet, it is difficult to increase the density as a bond magnet, and the resulting magnet properties remain low in view of their potential, and the properties at the mass production level are low. It is about 15 to 17 MGOe. In addition, since the powder is made into a fine powder, characteristic deterioration due to oxidation is severe in the manufacturing process, and it is difficult to obtain satisfactory magnetic characteristics.

In Example 1 described in JP-A-8-191006, there is a description of an Sm-Zr-Fe-N based anisotropic bonded magnet, which is also obtained by pulverizing an alloy ingot. It is necessary to make the magnet powder into a fine powder of about 3 μm as in the case of the above-mentioned Sm—Fe—N material, and it is difficult to increase the density and the effect of oxidation is large. It has a problem of poor stability.

The present invention solves the above-mentioned problems of the prior art, and among them, the invention according to claim 1 orients a hard magnetic phase which is a main phase having a fine crystal grain size by hot working. It is another object of the present invention to provide a method for producing anisotropic magnet powder having excellent magnetic properties and reliability.

It is an object of the present invention to provide a method for producing a magnet powder which further improves magnetic properties, particularly squareness, by performing heat treatment, and has less variation in properties.

According to an eleventh aspect of the present invention, by performing nitriding, nitrogen atoms are interstitially dissolved in the anisotropic main phase crystal to substantially improve saturation magnetization and anisotropic magnetic field. It is intended to obtain an anisotropic magnet powder having higher characteristics.

The invention according to the second, third, seventh, eighth, twelfth and thirteenth inventions is based on a rapidly quenched thin strip prepared by liquid quenching of an alloy powder before being processed, and has a fine uniform shape. Easily produce anisotropic magnet powder having a structure consisting of crystal grains,
Another object of the present invention is to provide a manufacturing method for manufacturing with high productivity.

The invention according to claims 4, 5, 9, 10, 14 and 15 provides anisotropic magnet powder having a high degree of orientation and excellent magnetic properties by defining working conditions in the hot working step. The purpose of the present invention is to provide a manufacturing method.

[0021] According to a sixteenth aspect of the present invention, the N in the magnet powder is reduced.
It is an object of the present invention to provide an anisotropic magnet powder capable of stabilizing a main phase crystal structure and stably obtaining high magnetic properties by regulating the amount.

It is another object of the present invention to provide an anisotropic bonded magnet having high magnetic properties and high reliability by combining the anisotropic magnet powder of the present invention with a resin.

[0023]

Means for Solving the Problems To achieve the above object, the invention according to claim 1 is characterized in that R1xR2y (Fe100-uM
u) It is represented by a composition formula of 100-xy-zCoz (provided that R1
Is one or more of the rare earth elements containing Y, R2 is one or more elements selected from the group of Zr, Hf, Sc, and M is Ti, Si, V, Cr, Mo,
Mn, W, Ni, Ga, Cu, Al, Nb, Sn, A
one or more elements selected from the group consisting of g and Ta, wherein x, y, z, and u are 2 ≦ x and 0.0
1 ≦ y, 4 ≦ x + y ≦ 20, 0 ≦ z ≦ 40, 0 ≦ u ≦ 2
0) Further, after filling a quenched alloy powder containing impurities unavoidable in production into a metal capsule, hot working is performed to change the direction of the axis of easy magnetization of the main phase crystal grains having the TbCu7 type structure in the constitutional structure. It is characterized in that it is oriented to give anisotropy, and after hot working, a work inside is taken out of the metal capsule and the work is crushed.

According to a second aspect of the present invention, in the first aspect, the quenched alloy powder is obtained by pulverizing a quenched ribbon obtained by solidifying a molten alloy by a liquid quenching method or the quenched ribbon. It is characterized by something.

According to a third aspect of the present invention, in the first aspect, the quenched alloy powder is obtained by pulverizing a quenched ribbon obtained by solidifying a molten alloy by a liquid quenching method or the quenched ribbon. It is characterized by being heat-treated at 400 to 700 ° C.

According to a fourth aspect of the present invention, in the first aspect, the strain rate during the working in the hot working step is 0.1 to 10 s ^-1 .

According to a fifth aspect of the present invention, in the first aspect, the temperature during processing in the hot working step is 400
~ 800 ° C.

The invention according to claim 6 is characterized in that R1xR2y (Fe
(100-uMu) 100-xy-zCoz (where R1 is one or more of the rare earth elements including Y, R2 is one selected from the group consisting of Zr, Hf and Sc)
Species or more, M is Ti, Si, V, Cr,
Mo, Mn, W, Ni, Ga, Cu, Al, Nb, S
one or more elements selected from the group consisting of n, Ag, and Ta, wherein x, y, z, and u are each in atomic% and 2 ≦ x;
0.01 ≦ y, 4 ≦ x + y ≦ 20, 0 ≦ z ≦ 40, 0 ≦
u ≦ 20), and after filling a quenched alloy powder containing impurities unavoidable in production into a metal capsule and subjecting it to hot working, the axis of easy magnetization of the main phase crystal grains having a TbCu7 type structure in the constitutional structure is formed. Orienting the direction to impart anisotropy, and after taking out a processed product inside the metal capsule from the metal capsule after hot working, from 400 to
The heat treatment is performed in a temperature range of 800 ° C., and the processed product after the heat treatment is pulverized.

The invention according to claim 7 is the invention according to claim 6, wherein the quenched alloy powder is obtained by pulverizing a quenched ribbon or a quenched ribbon obtained by solidifying a molten alloy by a liquid quenching method. It is characterized by something.

According to an eighth aspect of the present invention, in the sixth aspect, the quenched alloy powder is obtained by pulverizing a quenched ribbon or a quenched ribbon obtained by solidifying a molten alloy by a liquid quenching method. It is characterized by being heat-treated at 400 to 700 ° C.

According to a ninth aspect of the present invention, in the sixth aspect, the strain rate at the time of working in the hot working step is 0.1 to 10 s ^-1 .

According to a tenth aspect of the present invention, in the sixth aspect, the temperature during processing in the hot working step is 400 ° C.
~ 800 ° C.

[0033] The eleventh aspect of the present invention is directed to the case where R1xR2y (F
e100-uMu) 100-xy-zCoz (where R1 is one or more rare earth elements including Y, and R2 is one selected from the group consisting of Zr, Hf, and Sc).
Species or more, M is Ti, Si, V, Cr,
Mo, Mn, W, Ni, Ga, Cu, Al, Nb, S
one or more elements selected from the group consisting of n, Ag, and Ta, wherein x, y, z, and u are each in atomic% and 2 ≦ x;
0.01 ≦ y, 4 ≦ x + y ≦ 20, 0 ≦ z ≦ 40, 0 ≦
u ≦ 20) and a quenched alloy powder containing impurities inevitable in production, filled in a metal capsule, and then hot worked to form an easy axis of magnetization of a main phase crystal grain having a TbCu7 type structure in a constitutional structure. Orienting the direction to impart anisotropy, taking out a work inside from the metal capsule after hot working, taking out the work from the metal capsule, and using a nitrogen gas or ammonia gas or a mixed gas atmosphere thereof. Heat treatment in a temperature range of 300 to 700 ° C., and then pulverization.

According to a twelfth aspect of the present invention, in the eleventh aspect, the quenched alloy powder is obtained by pulverizing a quenched ribbon obtained by solidifying a molten alloy by a liquid quenching method or the quenched ribbon. It is characterized by something.

According to a thirteenth aspect of the present invention, in the eleventh aspect, the quenched alloy powder is obtained by pulverizing a quenched ribbon obtained by solidifying a molten alloy by a liquid quenching method or the quenched ribbon. It is characterized by being heat-treated at 400 to 700 ° C.

According to a fourteenth aspect, in the eleventh aspect, in the hot working step, a strain rate at the time of working is 0.1 to 10 s ^-1 .

According to a fifteenth aspect of the present invention, in the eleventh aspect, the temperature during processing in the hot working step is 40 or less.
The temperature is 0 to 800 ° C.

According to a sixteenth aspect of the present invention, (R1xR2yF
e100-xy-zCoz) 1-vNv (where R1 is one or more rare earth elements including Y, and R2 is one selected from the group consisting of Zr, Hf and Sc).
Species or more, M is Ti, Si, V, Cr,
Mo, Mn, W, Ni, Ga, Cu, Al, Nb, S
one or more elements selected from the group consisting of n, Ag, and Ta, wherein x, y, and z are each 2% x, 0.0
1 ≦ y, 4 ≦ x + y ≦ 20, 0 ≦ z ≦ 40, 0 ≦ z ≦ 2
0 and v are atomic ratios of 0 ≦ v ≦ 0.2), and the direction of the easy axis of magnetization of the main phase crystal grains having a TbCu7 type structure in the constitutional structure is composed of a quenched alloy powder containing impurities inevitable in production. It is characterized by being oriented to give anisotropy.

The invention according to claim 17 is characterized in that the anisotropic magnet powder produced by the production method according to claim 1 is bonded with a resin.

The invention according to claim 18 is characterized in that the anisotropic magnet powder produced by the production method according to claim 6 is bonded with a resin.

According to the nineteenth aspect of the present invention, the above-mentioned eleventh aspect is provided.
An anisotropic bonded magnet, wherein an anisotropic magnet powder produced by the production method described in 1) is bonded with a resin.

According to a twentieth aspect of the present invention, there is provided the above-mentioned sixteenth aspect.
Wherein the anisotropic magnet powder described in (1) is bonded with a resin.

[0043]

BEST MODE FOR CARRYING OUT THE INVENTION Hereinafter, the present invention will be described in detail.

First, the alloying elements constituting the anisotropic magnet powder of the present invention and their constituent requirements will be described.

R1 is at least one of the rare earth elements containing Y
It is an element composed of a seed, and is a main element constituting a hexagonal phase having a TbCu7 type structure exhibiting hard magnetic properties, which is a main phase in a constitutional structure. Here, the main phase refers to a phase having the largest volume ratio in the constituent structure of the magnet. Further, it is preferable that at least one of Sm, Nd, and Pr is included. The composition range is desirably 2% or more in atomic ratio. This is because, if the composition is less than 2%, a large amount of a soft magnetic phase such as an α-Fe phase precipitates in the constitutional structure, thereby deteriorating the magnet properties, particularly the coercive force.

R2 is an element capable of substituting a site occupied by a rare earth in the TbCu7 type intermetallic compound phase, which is the main phase, and preferably has an atomic radius relatively close to that of the rare earth element. , Hf, and Sc. By adding such an element, the crystal structure of the main phase is stabilized, and the saturation magnetization of the main phase is increased. In order to obtain such an effect, it is desirable that R2 be at least 0.1% in atomic ratio.

It is desirable that the sum of the added amounts of the R1 element and the R2 element is 4 to 20% in atomic%. This is because if the content is less than 4 atomic%, a sufficient coercive force cannot be obtained as a permanent magnet, while if it exceeds 20%, the magnetization is significantly reduced.

Fe is a main constituent element of an intermetallic compound phase having a TbCu7 type structure, which is a main phase. Most of the magnetization of this compound phase is due to the magnetic moment of Fe atoms. Part of Fe is an element represented by M (M is T
i, Si, V, Cr, Mo, Mn, W, Ni, Ga, C
or one or more elements selected from u, Al, Nb, Sn, Ag, and Ta). M
Substitution by means of fine particles makes it possible to improve the coercive force and squareness by making the crystal grain size fine and homogenous, and to increase the volume ratio of the main phase. However, if the substitution amount of M exceeds 20%, the decrease in magnetization due to the decrease in Fe is remarkable, which is not preferable.

By substituting a part of Fe sites in the main phase, Co has an effect of improving the thermal stability because the Curie point of the main phase is improved. The Co composition range is desirably 40% or less. This is because the coercive force is remarkably reduced when it exceeds 40%. Further, an increase in the use amount of Co, which is relatively expensive, causes an increase in cost and lowers cost performance. A more preferred range is 4 to 30%. By setting the composition in such a range, the stability of the crystal structure of the main phase is improved.

N forms an interstitial solid solution in the TbCu7 type phase as the main phase. As a result, the interatomic distance between the transition metal elements is increased, and as a result, the saturation magnetization of the main phase is increased and the Curie point is improved. The composition range of N is desirably 20% or less in atomic%. This is because when it exceeds 20%, the main phase becomes TbCu.
This is because the type 7 phase undergoes phase decomposition and cannot maintain the crystal structure, resulting in deterioration of magnetic properties.
In addition to N, C or P forms an interstitial solid solution similarly to N and has an effect of improving magnetic properties.

Next, the method for producing the anisotropic magnet powder of the present invention will be described in detail step by step, including the reasons for limiting each item.

1) Production process of quenched alloy powder First, raw materials are weighed so as to have a predetermined alloy composition, and a quenched alloy powder is produced by any of the following methods. The quenched alloy powder according to the present invention has a constituent structure of 10 nm.
It is desirable that the average grain size be of the order or a composite structure of such a crystal structure and an amorphous structure. In order to produce such a quenched alloy powder, the following production method can be used.

A) A so-called liquid quenching method in which a molten alloy melted by high-frequency heating or the like in an inert atmosphere is sprayed onto the rolls by a quenching ribbon manufacturing apparatus having a single roll or twin rolls. Manufactures quenched ribbons.

B) An alloy powder is produced by rapidly solidifying a molten alloy melted by high-frequency heating or the like in an inert atmosphere by injecting an inert gas and solidifying the molten alloy by a so-called gas atomizing method.

C) A molten alloy melted by high frequency heating or the like in an inert atmosphere is sprayed onto a rotating disk to obtain a rapidly solidified powder.

In particular, according to the liquid quenching method a), a very high cooling rate can be easily realized.
A quenched ribbon having an m-order crystal structure or a composite structure of such a crystal structure and an amorphous structure can be manufactured with high productivity, and it can be said that this is a production method most suitable for the present invention. Specifically, when a quenched ribbon is manufactured by a single roll method, such a structure can be obtained if the roll speed is set to a rotation speed of 10 to 60 m / s. 10m / s
At a rotation speed of less than 1, the presence of coarse crystal grains of the order of 100 nm becomes remarkable, and the final magnet properties are reduced. On the other hand, if the rotation speed exceeds 60 m / s, the molten metal is scattered so much that the yield is undesirably reduced. Here, the crystal grain size is preferably on the order of 10 nm as described above.

The quenched alloy powder is produced by the above-described method, but in some cases, it is effective to perform heat treatment on the obtained powder. In particular, by effecting crystallization by heat treatment after the constituent structure is converted to a completely amorphous structure, there is an effect that a crystal structure having a uniform crystal grain size of the order of 10 nm can be obtained. The heat treatment temperature in this case is desirably 400 to 700 ° C. This is because if the temperature is lower than 400 ° C., the above-mentioned crystallization effect cannot be sufficiently obtained, and even if it is obtained, a very long heat treatment is required, and mass productivity is lacking. If the heat treatment is performed at a temperature exceeding 700 ° C., the crystal grains after hot working are remarkably coarsened and the final magnet properties are deteriorated.

2) Hot working step The quenched alloy powder produced in the above-described step is first encapsulated in a metal capsule. Having the alloy powder once encapsulated in a metal capsule and performing hot working has the following effects.

A) The alloy powder can be processed without being oxidized even in the normal atmosphere.

B) Since atmosphere control is unnecessary, a relatively large amount of material can be processed at one time, and the mass productivity is excellent.

C) High strain rate processing such as rolling and forging can be performed.

On the other hand, as a conventional technique, description of processing of a magnetic material having an alloy composition as in the present invention is described in JP-A-6-172936, page 4, column 5, lines 21 to 29.
There is a description on the line. However, the manufacturing method described there,
First, a bulk compact is produced by compression-molding an alloy powder by hot pressing or HIP, and thereafter, it is produced through a complicated process of plastically deforming further by hot working. However, this method has the following problems. First, a high-density green compact must be produced and then subjected to a complicated process of further plastic deformation. Also, in order to produce a high-density green compact, cracks and cracks must not occur, so hot pressing or HIP with a low strain rate must be applied, resulting in a large cycle time and a long time. And mass production is hardly expected. Further, when performing the hot pressing or HIP, atmosphere control is required, which also greatly reduces mass productivity.

On the other hand, in the hot working step in the manufacturing method of the present invention, there is no step of forming a compact as in the prior art, and the quenched alloy powder is hot worked as it is. Further, it is preferable to generate cracks and cracks more actively during the processing in order to finally obtain the powder. Therefore, as seen in the effects b) and c), the strain rate of rolling or the like is reduced. A method that is quick and excellent in mass productivity can be adopted. When expressed as the strain rate during processing, the strain rate during hot working is 0.1 to 10 s.
It is desirable to set it to ^-1 . Here, the strain rate is the thickness T1 before processing and the final thickness T2, and the time required for processing is t
If (s) is set, it can be expressed by (1-T2 / T1) / t. If the strain rate is less than 0.1 s ⁻¹ , the time required for processing becomes too long, resulting in poor mass productivity. In addition, a solid-state reaction occurs due to diffusion at the interface between the metal capsule and the quenched alloy powder inside, resulting in a magnetic field. There is a problem that characteristics are deteriorated. Furthermore, it is difficult for cracks and cracks to enter the magnet material,
It becomes a bulk, and before moving on to a pulverization step for making a powder in a later step, an extra step such as cutting and crushing of the bulk material must be performed, resulting in an increase in process cost. On the other hand, if the strain rate is 0.1 to 10 s ^-1, the hot working is completed in a short time, and no reaction occurs with the capsule interface. In addition, cracks and cracks are likely to occur, and after hot working, a moderately sized lump or powdered material is obtained, and it is easy to produce pulverized powder in the subsequent process. It can be applied as a powder. However, when the strain rate exceeds 10 s ⁻¹ , it is necessary to increase the size of the processing machine, which causes a significant increase in process cost.

As the metal capsule material used in the present invention, a material having a melting point of 900 ° C. or more is desirable. Particularly preferably, general-purpose low-carbon steels such as inexpensive SS materials (JIS standards) and iron-based materials such as stainless steels are desirable. As a method for filling the metal capsule, for example, a box-shaped metal capsule having one open side is produced by welding a plate material of a predetermined size, and the quenched alloy powder is filled therein. When filling the quenched alloy powder, the powder may be filled as it is,
In the case of a relatively long ribbon, the powder may be slightly pulverized before filling, if necessary, in order to increase the filling rate.
After the box-shaped capsule is filled with the quenched alloy powder, the opened one side is welded around the periphery with a plate material and sealed. At this time, the internal alloy powder slightly oxidizes during hot working due to oxygen remaining in the capsule. For this reason, a deaeration port that can be evacuated is provided in a part of the metal capsule, and after filling the alloy powder into the capsule, the inside of the capsule is evacuated from the deaeration port and then the deaeration port is sealed and sealed. Is more preferable.

The working temperature during hot working is 400 to 800
It is desirable to be set to ° C. When processed in such a temperature range, the c-axis direction, which is the direction of easy magnetization of the main phase crystal grains of the TbCu7 type structure, which is the constitutional structure in the alloy powder encapsulated in the capsule, is aligned with the direction of the maximum compressive stress. The crystal grows preferentially and becomes a crystal grain having a crystal grain size of about several tens to 300 nm. When the hot working is performed at a temperature lower than 400 ° C., the crystal growth as described above does not sufficiently occur, and at a temperature higher than 800 ° C., the crystal grain size becomes coarse and the magnetic properties deteriorate.

3) Heat treatment step After the hot working, the work inside is taken out of the metal capsule. This processed product is obtained by processing quenched alloy powder. After hot working, the work can be directly crushed to obtain magnet powder. However, it is more preferable to perform a heat treatment on the workpiece. The heat treatment is desirably performed in an atmosphere of an inert gas such as Ar gas to prevent oxidation. The optimal heat treatment temperature range is 400-800
° C. This is because if the temperature is lower than 400 ° C., there is no effect of the heat treatment, and if the temperature is higher than 800 ° C., on the contrary, the crystal grain size becomes coarse and the magnetic properties deteriorate. Such heat treatment promotes anisotropy due to preferential growth of the main phase crystal grains and also has an effect of removing residual strain, thereby improving magnetic properties, particularly squareness.

4) Nitriding Treatment Nitriding is performed by heat treatment in a nitrogen gas, an ammonia gas, or a mixed atmosphere thereof. The heat treatment is preferably performed in a temperature range of 300 to 700 ° C. This is because nitriding does not proceed below 300 ° C.
If the temperature exceeds 0 ° C., phase decomposition occurs, the crystal structure of the main phase cannot be maintained, and magnet characteristics cannot be obtained.

5) Pulverizing Step After the hot working step, or after performing the heat treatment or nitriding treatment as described above, a magnet powder having a desired particle size is obtained through a pulverizing step. JP-A-8-1910 which is the above-mentioned prior art
In Example 1 described in Japanese Patent Publication No. 06, it was necessary to obtain a fine powder having a particle size of about 3 μm in order to obtain a coercive force.
Considering the formability as a bonded magnet, the average particle size is 100
It may be set to μm or less.

Next, the anisotropic bonded magnet of the present invention will be described.

The anisotropic magnet powder obtained by the above-described manufacturing method is mixed with either a thermosetting resin such as an epoxy resin or a thermoplastic resin such as a nylon resin,
After bonding in a magnetic field, bonding is performed to obtain a bonded magnet. When a thermosetting resin such as an epoxy resin is used, the resin is mixed with the resin, kneaded, molded while being oriented in a magnetic field, and then subjected to a curing treatment to form an anisotropic bonded magnet. When using a thermoplastic resin such as nylon resin, after mixing and kneading with the resin, it is heated, molded while orienting in a magnetic field while the resin is almost molten, and then cooled to form an anisotropic bonded magnet. .

The anisotropic bonded magnet manufactured as described above has the following characteristics as compared with the above-described conventional technology.

1) Magnetic properties higher than anisotropic bonded magnets using Nd-Fe-B-based powder or Sm-Fe-N-based powder by the HDDR method, specifically, a magnet having a maximum energy product of 18 MGOe or more. Characteristics can be obtained with good mass productivity.

2) Since it is not necessary to make the powder into a fine powder having a size of about several μm, it is necessary to use an Sm—Fe—N based or
In Example 1 described in JP-A-191006, Sm-
Compared with an anisotropic bonded magnet using a Zr—Fe—N-based powder, the density can be increased by increasing the volume ratio of the magnetic powder, and high magnetic characteristics can be obtained. Further, since the (surface area / volume) ratio of the powder is small, the powder is not easily affected by oxidation, handling during the process is easy, and high thermal stability can be secured.

3) Since Sm is used as the main rare earth element, Nd is superior in corrosion resistance and thermal stability as compared with the main element Nd-Fe-B system.

2) By performing nitriding, magnetic properties of 20 MGOe or more, which is equal to or more than that of the Sm 2 Co 17 based bonded magnet, can be obtained with good mass productivity. Further, since the content of expensive Co is lower than that of the Sm2Co17-based material, there is also an effect of cost reduction.

Hereinafter, the present invention will be described more specifically based on examples.

(Example 1) Sm, Z having a purity of 99.9%
The raw metal of r, Fe, Co is Sm9Zr3Fe81Co7
Was weighed so as to have a composition represented by the following formula, was melted in a high-frequency induction furnace in an Ar gas atmosphere, and was cast in a copper mold to produce an alloy ingot having a weight of about 1 kg. Cut out a sample piece from the ingot and place it on the bottom at 0.6 mm
The tube was placed in a transparent quartz tube provided with an orifice of φ, and then this quartz tube was attached to a quenching ribbon manufacturing apparatus having a single roll of copper having a diameter of 300 mm. Thereafter, the sample piece was melted in a quartz tube by high-frequency heating in an Ar atmosphere, and a molten alloy was sprayed onto the rotating copper roll to obtain a ribbon-shaped quenched ribbon. The roll rotation speed at this time is 40 m /
s. Further, in a similar manner, a quenched ribbon of about 250 g in total having the same composition was obtained. This was pulverized into flakes so as to be easily filled into capsules described later, to obtain an alloy powder.

The quenched alloy powder produced in this way was
Fill into a box-shaped capsule made of S41 (JIS standard),
The outer periphery of the cover material of SS41 provided with the deaeration port is welded. FIG. 1 shows a schematic sectional view of the capsule. Then this SS41
The capsule was placed in an electron beam welding chamber, and the inside of the chamber was evacuated. The degree of vacuum in the chamber is 10 ^-2
The evacuation port was sealed by electron beam welding.

The SS4 containing the alloy powder as described above
1 capsule was heated to 750 ° C. in an air furnace, taken out of the furnace, and immediately rolled by a rolling mill so as to have a total workability of 75%. After the completion of the rolling, the outside of the rolled material was cooled by water cooling, and after sufficiently cooling, the internal workpiece was taken out from the SS41 capsule. The removed workpiece was not in the form of an integral bulk, but was in the form of powder or lump. This processed product was directly pulverized with a raikai machine to obtain a powder having an average particle size of about 50 μm. 1.6 wt% of an epoxy resin was added to the obtained powder, mixed, and compression-molded at a molding pressure of 7 ton / cm2 while orienting in a magnetic field of 15 kOe, followed by a 1.5-hour cure treatment in a nitrogen gas atmosphere. Do
An anisotropic bonded magnet was produced. For the obtained anisotropic bonded magnet, the maximum applied magnetic field was 25 kO
The magnetic properties were measured in e. The obtained magnetic properties were Br = 9.
1 kG, iHc = 10.2 kOe, (BH) max = 18.6 MGOe,
High magnetic properties were obtained. Further, X-ray diffraction was performed on the magnet powder before forming the bond magnet. X-ray is Cu-Kα
And the diffraction angle 2θ was measured in the range of 20 ° to 60 °. As a result, peaks of the hexagonal phase of the TbCu7 type structure, which is the main phase, were observed, and among those peaks, the reflection intensity of the peak considered to be the (002) diffraction peak of the main phase was different from that of the other peaks of the main phase. Compared to the above, it was confirmed that anisotropy was achieved. As a result of TEM observation, the main phase crystal grain size was 20 to 100 nm.

Example 2 For the alloys having the respective compositions shown in Table 1, under the same conditions as in Example 1, from ingot production to rolling and pulverization, a powder having an average particle size of about 50 μm was obtained. 1.6 wt% of an epoxy resin is added to the obtained powder, mixed, compression-molded at a molding pressure of 7 ton / cm2 while orienting in a magnetic field of 15 kOe, and then cured in a nitrogen gas atmosphere for 1.5 hours. Was performed to produce an anisotropic bonded magnet. The magnetic properties of the obtained anisotropic bonded magnet were measured by a direct current magnetic flux meter at a maximum applied magnetic field of 25 kOe. Table 1 also shows the measurement results.

[0081]

[Table 1]

As is evident from Table 1, high magnetic properties can be obtained with the anisotropic bonded magnet using the powder in the composition range of the present invention, but low magnetic properties can be obtained with the comparative example.

(Example 3) Sm, P having a purity of 99.9%
The raw metal of r, Zr, Fe, Co, Ti is Sm7Pr4
It was weighed to have a composition represented by Zr3Fe76Co8Ti2, melted in a high-frequency induction furnace in an Ar gas atmosphere, and cast in a copper mold to produce an alloy ingot having a weight of about 1 kg. Next, a ribbon-shaped quenched ribbon was manufactured using the same quenched ribbon manufacturing apparatus as in Example 1 at a roll rotation speed of 35 m / s. Next, hot rolling was performed under the same conditions as in Example 1. After rolling, the work is taken out of the capsule, and the work is 300 to 9 in an Ar atmosphere.
Heat treatment was performed at each temperature of 00 ° C. After the heat treatment, the powder was pulverized to obtain a powder having an average particle size of about 50 μm, which was combined with a resin in the same manner as in Example 1 to obtain an anisotropic bonded magnet.
Table 2 shows the measurement results of the heat treatment temperature after rolling and the obtained magnetic properties.

[0084]

[Table 2]

As is clear from the table, after hot working,
When heat treatment is performed in a temperature range of 0 to 800 ° C., higher magnetic properties can be obtained.

(Example 4) Sm, N having a purity of 99.9%
The raw material metal of d, Zr, Fe, Co is Sm5Nd3Zr4
It was weighed to have a composition represented by Fe83Co5, melted in a high-frequency induction furnace in an Ar gas atmosphere, and cast in a copper mold to produce an alloy ingot having a weight of about 1 kg. Next, from the production of the quenched ribbon to the hot rolling, the same conditions as in Example 1 were used. After rolling, the processed product was taken out of the capsule, and the processed product was subjected to a heat treatment at each temperature shown in Table 3 for 2 hours in a nitrogen atmosphere at 1 atm, thereby performing a nitriding treatment. Table 3 also shows the magnetic properties of anisotropic bonded magnets prepared from the powder after nitriding in the same manner as in the above examples.

[0087]

[Table 3]

As is clear from the table, by performing the nitriding treatment in the temperature range of 300 to 700 ° C. after the hot working, it is possible to obtain high magnetic properties, particularly a maximum energy product exceeding 20 MGOe.

Example 5 Raw metal was weighed, and nitrided magnet powders having the respective compositions shown in Table 4 were obtained in the same manner as in Example 4. However, the temperature of the nitriding treatment was 500 ° C. An anisotropic bonded magnet was prepared from these powders under the same conditions as in Example 1, and the magnetic properties were measured. Table 4 also shows the measurement results.

[0090]

[Table 4]

As is clear from the table, high magnetic characteristics can be obtained in the composition range defined by the present invention.

(Example 6) Sm, N having a purity of 99.9%
The raw material metal of d, Zr, Fe, Co is Sm6Pr2Zr2
Weighed to a composition represented by Fe83Si2Co5,
This was melted in a high-frequency induction furnace in an Ar gas atmosphere and cast in a copper mold to produce an alloy ingot having a weight of about 1 kg. Next, a ribbon-shaped quenched ribbon was produced using a quenched ribbon production apparatus at a roll rotation speed of 55 m / s.
From the result of TEM observation and X-ray diffraction, it was confirmed that the quenched ribbon obtained at this time was almost in an amorphous phase. After heat-treating these quenched ribbons at each temperature of 300 to 800 ° C. for 20 minutes, they are encapsulated in capsules as in Example 1, and heated to 700 ° C. in an atmospheric furnace to reach a total workability of 75%. Hot rolling was performed as described above. After the completion of the rolling, the outside of the rolled material was cooled by water cooling, and the processed product was taken out from the capsule. The taken-out workpiece was treated in the same manner as in Example 1 to obtain a powder having an average particle size of about 50 μm. Using the obtained powder, a bonded magnet was obtained in the same manner as in Example 1, and the magnetic properties were measured. Table 5 shows the heat treatment temperature applied to the quenched ribbon and the magnetic properties of the finally obtained bonded magnet.

[0093]

[Table 5]

As is clear from the table, 400 quenched ribbons
Good magnetic properties can be obtained in a bonded magnet obtained by performing a heat treatment at a temperature of about 700 ° C. and then performing a hot rolling.

(Embodiment 7) Sm, Nd, Zr, Fe, C
A quenched ribbon was produced from an alloy ingot composed of u and Co under the same conditions as in Example 1, and the resulting quenched ribbon was hot-worked by each of the processing methods described below.

A) The obtained quenched ribbon was first subjected to hot isostatic pressing at 650 ° C. by an HIP apparatus in an argon atmosphere to obtain a high-density bulk. After cooling, it was taken out of the HIP device, and hot-pressed with a total workability of 75% and a strain rate of 0.03 s ^-1 using a hot press device in an argon atmosphere.

B) After filling the obtained quenched ribbon into a cylindrical capsule made of SS41, degassed and sealed, and placed in an air furnace for 5 minutes.
Immediately after heating to 00 ° C, a total forging degree of 75
%, And hot forging was performed at a strain rate of 0.1 s ^-1 .

C) The obtained quenched ribbon was SUS304 (J
After filling into a rectangular capsule made of IS standard), degassing and sealing, and then heating to 600 ° C. in an atmospheric furnace, immediately using a rolling mill, a total workability of 80% and a strain rate of 0.8 s ^-1 was hot rolled.

D) After filling the obtained quenched ribbon into capsules made of SS41, degassing and sealing, heating at 700 ° C. in an atmospheric furnace, and immediately, using a rolling mill, a total workability of 80%, strain rate Rolling of 3 s ^-1 was performed.

E) The obtained quenched ribbon was sealed in a rectangular capsule made of SS41, and then 750 ° C. in an atmospheric furnace.
, And immediately hot-rolled by a rolling mill at a total working ratio of 80% and a strain rate of 10 s ^-1 .

F) After filling the obtained quenched ribbon into capsules made of SS41, degassing and sealing, heating to 780 ° C. in an atmospheric furnace, and immediately, using a rolling mill, a total work degree of 75% and a strain rate Hot rolling of 15 s ^-1 was performed.

After performing each of the above-mentioned hot working, the processed product was taken out of the capsule, and then heat-treated at 450 ° C. for 2 hours in a nitrogen atmosphere at 1 atm. Thereafter, it was pulverized to obtain a powder having an average particle size of about 50 μm. The composition of each of the obtained powders was (Sm6.5Nd1.5Zr3Fe83).
Cu2 Co4) 88N12. 1.6 wt% of epoxy resin is added to each powder, mixed, compression-molded at a molding pressure of 7 ton / cm2 while orienting in a magnetic field of 15 kOe, and then cured in a nitrogen gas atmosphere for 1.5 hours. ,
An anisotropic bonded magnet was produced.

Table 6 also shows the strain rates at the time of each of the hot workings A) to F) and the magnetic properties of the finally obtained anisotropic bonded magnet.

[0104]

[Table 6]

As is clear from the table, high magnetic properties can be obtained when processing is performed at the strain rate of the present invention.

Example 8 Sm, P having a purity of 99.9%
The raw metal of r, Zr, Fe, Ag, Co is Sm4Pr5
After weighing to obtain a composition represented by Zr3Fe79Ag2Co7 and preparing an alloy ingot in the same manner as in Example 1,
A quenched ribbon was produced at a roll speed of 35 m / s by a quenched ribbon manufacturing apparatus. After the obtained quenched ribbon was sealed in a metal capsule in the same manner as in Example 1, hot rolling was performed at each temperature shown in Table 7. The strain rate during rolling varied depending on the rolling temperature, but was in the range of 0.5 to 5 s ^-1 . After such rolling, the work was taken out from the inside and heat-treated at 450 ° C. for 2 hours in a nitrogen atmosphere at 1 atm. After the heat treatment, the processed product was pulverized to obtain a powder having an average particle size of about 40 μm. Table 7 also shows the hot rolling temperature and the properties of the finally obtained anisotropic bonded magnet.

[0107]

[Table 7]

As is clear from the table, it is understood that high magnetic properties can be obtained by rolling at a temperature of 400 to 800 ° C.

(Example 9) Sm, Z having a purity of 99.9%
The raw metal of r, Fe, Ni, Co is Sm5Nd3Zr4
It was weighed to have a composition represented by Fe83Co5, melted in a high-frequency induction furnace in an Ar gas atmosphere, and cast in a copper mold to produce an alloy ingot having a weight of about 1 kg. Next, from the production of the quenched ribbon to the hot rolling, the same conditions as in Example 1 were used. After rolling, the processed product was taken out of the capsule, and the processed product was subjected to a heat treatment at each temperature shown in Table 3 for 2 hours in a nitrogen atmosphere at 1 atm for nitriding treatment, followed by grinding to obtain a magnet powder. . The composition of the powder was (Sm9Zr4Fe80Ni2Co5) 0.88N0.12. An anisotropic bonded magnet was produced from this powder in the same manner as in Example 1. The demagnetization curves of the sample at room temperature and 100 ° C. were measured by a direct current magnetic flux meter having a temperature variable unit for high temperature measurement attached to a local area.
From the results, the temperature coefficient (α) of Br and the temperature coefficient (β) of iHc in the range from room temperature to 100 ° C. were calculated,
(Α, β) = (− 0.04, −0.30) (however, the unit of both α and β is% / ° C.).

Nd12.6Fe8 produced by the HDDR method
A magnet powder having a composition represented by 1.3B6.0Ga0.1;
The same measurement was performed on a bonded magnet using a magnetic powder having a composition represented by Fe-N-based Sm9.0Fe77.4N13.6. As a result, in the former case, (α, β) = (− 0.10, −0.
53), for the latter, (α, β) = (-0.06, -0.49).

As is clear from these results, the anisotropic bonded magnet according to the present invention can obtain good thermal stability.

[0112]

According to the first aspect of the present invention, a hard magnetic phase which is a main phase having a fine crystal grain size is oriented by hot working to provide an anisotropic material having excellent magnetic properties and reliability. Magnetic powder can be obtained.

According to the sixth aspect of the present invention, by performing heat treatment after hot working, it is possible to further improve magnetic properties and to obtain a magnet powder with little property variation.

According to the eleventh aspect of the present invention, by performing nitriding, nitrogen atoms are interstitially dissolved in the anisotropic main phase crystal to substantially improve the saturation magnetization and the anisotropic magnetic field. Further, anisotropic magnet powder having higher characteristics can be obtained.

The invention according to claims 2, 3, 7, 8, 12 and 13 is based on a quenched ribbon prepared by liquid quenching of an alloy powder before processing, and is characterized by fine uniform crystal grains. High-performance anisotropic magnet powder having a structure having a diameter can be obtained with high productivity.

The invention according to claims 4, 5, 9, 10, 14 and 15 is an anisotropic magnet having a high degree of orientation and excellent magnetic properties by defining working conditions in the hot working step. A method for producing a powder can be provided.

According to the present invention, the crystal structure of the main phase is stabilized by defining the amount of N in the magnet powder.
An anisotropic magnet powder capable of stably obtaining high magnetic properties is obtained.

The invention according to claims 17 to 20 is
By bonding the anisotropic magnet powder of the present invention to a resin, an anisotropic bonded magnet having high magnetic properties and reliability can be obtained.

[Brief description of the drawings]

FIG. 1 is a schematic cross-sectional view of a metal capsule filled with a quenched alloy powder.

[Explanation of symbols]

 DESCRIPTION OF SYMBOLS 1 ... Quenched alloy powder 2 ... SS41 box-shaped capsule 3 ... SS41 lid material 4 ... Deaeration port 5 ... Weld part

Claims (20)

[Claims] 1. R1xR2y (Fe100-uMu) 100-xyz
Coz is represented by a composition formula (where R1 is one or more of the rare earth elements including Y, R2 is Z
one or more elements selected from the group consisting of r, Hf, Sc, and M is Ti, Si, V, Cr, Mo, Mn, W, N
one or more elements selected from the group consisting of i, Ga, Cu, Al, Nb, Sn, Ag, Ta, and x, y, z,
u is atomic%, 2 ≦ x, 0.01 ≦ y, 4 ≦ x +
y ≦ 20, 0 ≦ z ≦ 40, 0 ≦ u ≦ 20) Further, after quenching alloy powder containing impurities inevitable in manufacturing is filled in a metal capsule, TbCu7 in the structural structure is subjected to hot working. It is characterized by orienting the direction of easy axis of magnetization of the main phase crystal grains having a mold structure to impart anisotropy, taking out a work inside from the metal capsule after hot working, and pulverizing the work. Method for producing anisotropic magnet powder. 2. The quenched alloy powder according to claim 1, wherein the quenched alloy powder is a quenched ribbon obtained by solidifying a melt of the alloy by a liquid quenching method or the quenched ribbon. A method for producing anisotropic magnet powder. 3. The quenched alloy powder is obtained by heat-treating a quenched ribbon obtained by solidifying a molten alloy by a liquid quenching method or a crushed ribbon thereof at 400 to 700 ° C. The method for producing anisotropic magnet powder according to claim 1, wherein: 4. The method for producing anisotropic magnet powder according to claim ¹ , wherein a strain rate during the working in the hot working step is 0.1 to 10 s ⁻¹ . 5. The hot working step, wherein the working temperature is 400 to 800 ° C.
A method for producing the anisotropic magnet powder described in the above. 6. R1xR2y (Fe100-uMu) 100-xyz
Coz is represented by a composition formula (where R1 is one or more of the rare earth elements including Y, R2 is Z
one or more elements selected from the group consisting of r, Hf, Sc, and M is Ti, Si, V, Cr, Mo, Mn, W, N
one or more elements selected from the group consisting of i, Ga, Cu, Al, Nb, Sn, Ag, Ta, and x, y, z,
u is atomic%, 2 ≦ x, 0.01 ≦ y, 4 ≦ x +
y ≦ 20, 0 ≦ z ≦ 40, 0 ≦ u ≦ 20) Further, after quenching alloy powder containing impurities inevitable in manufacturing is filled in a metal capsule, TbCu7 in the structural structure is subjected to hot working. Orientation of the axis of easy magnetization of the main phase crystal grains having the mold structure is performed to impart anisotropy, and after hot working, after taking out a work inside from the metal capsule from the metal capsule, 400 A method for producing anisotropic magnet powder, characterized by heat-treating in a temperature range of -800 ° C, and further pulverizing the processed product after the heat treatment. 7. The quenched alloy powder according to claim 6, wherein the quenched alloy powder is a quenched ribbon obtained by solidifying a melt of the alloy by a liquid quenching method or a quenched ribbon thereof. A method for producing anisotropic magnet powder. 8. The quenched alloy powder is a quenched ribbon obtained by solidifying a melt of the alloy by a liquid quenching method or a crushed ribbon obtained by heat treatment at 400 to 700 ° C. The method for producing anisotropic magnet powder according to claim 6, characterized in that: 9. The method for producing anisotropic magnet powder according to claim 6, wherein a strain rate during the working in the hot working step is 0.1 to 10 s ⁻¹ . 10. The method for producing anisotropic magnet powder according to claim 6, wherein a temperature during the hot working step is 400 to 800 ° C. 11. R1xR2y (Fe100-uMu) 100-xy-
where R1 is one or more of the rare earth elements containing Y, and R2 is Z
one or more elements selected from the group consisting of r, Hf, Sc, and M is Ti, Si, V, Cr, Mo, Mn, W, N
one or more elements selected from the group consisting of i, Ga, Cu, Al, Nb, Sn, Ag, Ta, and x, y, z,
u is atomic%, 2 ≦ x, 0.01 ≦ y, 4 ≦ x +
y ≦ 20, 0 ≦ z ≦ 40, 0 ≦ u ≦ 20) Further, a quenched alloy powder containing impurities inevitable in production is filled in a metal capsule, and then hot worked to form TbCu7 in the structural structure. Orientation of the axis of easy magnetization of the main phase crystal grains having a mold structure to impart anisotropy, take out a work inside from the metal capsule after hot working, and take out the work from the metal capsule 300 to 7 in an atmosphere of nitrogen gas or ammonia gas or a mixed gas thereof.
A method for producing anisotropic magnet powder, which comprises heat-treating in a temperature range of 00 ° C. and then pulverizing. 12. The quenched alloy powder obtained by solidifying a melt of the alloy by a liquid quenching method or a quenched ribbon obtained by pulverizing the quenched ribbon.
A method for producing the anisotropic magnet powder described in the above. 13. The quenched alloy powder is obtained by heat-treating a quenched ribbon obtained by solidifying a molten alloy by a liquid quenching method or a crushed ribbon thereof at 400 to 700 ° C. The method for producing anisotropic magnet powder according to claim 11, wherein: 14. The method for producing anisotropic magnet powder according to claim 11, wherein a strain rate during the working in the hot working step is 0.1 to 10 s ⁻¹ . 15. The method for producing anisotropic magnet powder according to claim 11, wherein a temperature during the hot working step is 400 to 800 ° C. 16. (R1xR2yFe100-xy-zCoz) 1-
vNv (where R1 is one or more of the rare earth elements including Y, R2 is Zr,
One or more elements selected from the group consisting of Hf and Sc, M is Ti, Si, V, Cr, Mo, Mn, W, N
i, Ga, Cu, Al, Nb, Sn, Ag, Ta, or one or more elements selected from the group consisting of ≦ x + y ≦
20, 0 ≦ z ≦ 40, 0 ≦ z ≦ 20, and v is an atomic ratio of 0 ≦ v ≦ 0.2) and a quenched alloy powder containing impurities inevitable in production, and a TbCu7 type structure in a constitutional structure. Anisotropic magnet powder characterized by imparting anisotropy by orienting the direction of easy axis of main phase crystal grains having the following. 17. An anisotropic bonded magnet, wherein the anisotropic magnet powder produced by the production method according to claim 1 is bonded with a resin. 18. An anisotropic bonded magnet, wherein the anisotropic magnet powder produced by the production method according to claim 6 is bonded with a resin. 19. An anisotropic bonded magnet, wherein the anisotropic magnet powder produced by the production method according to claim 11 is bonded with a resin. 20. An anisotropic bonded magnet, wherein the anisotropic magnet powder according to claim 16 is bonded with a resin.