JP2007119909A - Rare-earth-iron-nitrogen-base magnet powder and method for manufacturing the same - Google Patents

Abstract

<P>PROBLEM TO BE SOLVED: To provide a method for inexpensively manufacturing magnet powder having excellent magnetic characteristics at a yield enhanced by a reduction diffusion method by reducing the non-magnetic phase which lowers the magnetic characteristics of the rare-earth-iron-nitrogen-base magnet powder and reducing the distortion of the crystal which is the nucleus for magnetization inversion and the remaining of a-Fe. <P>SOLUTION: The method includes steps of; mixing rare earth oxide powder, iron powder and reducing agent powder, such as an alkaline metal, at prescribed ratios: heating the mixture at 90 to 1,180°C in an inert gaseous atmosphere; subsequently cooling the mixture down to ≤500°C, then supplying gaseous nitrogen to cause the decay of the mixture after discharging the inert gas; then supplying a gaseous mixture containing ammonia and hydrogen while keeping the mixture at ≤300°C to elevate the temperature thereof; charging the mixture into water to perform wet process treatment; removing the hydrogen having invaded the magnet alloy by the wet process treatment; and thereafter, subjecting the magnet alloy to pulverization. <P>COPYRIGHT: (C)2007,JPO&INPIT

Description

  The present invention relates to a rare earth-iron-nitrogen based magnet powder and a method for producing the same, and more specifically, by uniformly nitriding using a reduction diffusion method, not only a non-magnetic phase but also a core of magnetization reversal (nucleation). Manufacturing method capable of producing a rare earth-iron-nitrogen based magnet powder having excellent magnetic properties with high yield and low cost, and distortion of crystals and residual α-Fe greatly The present invention relates to a rare earth-iron-nitrogen based magnet powder obtained by the method.

Rare earth-iron-nitrogen based magnets represented by Sm-Fe-N are known as high performance and inexpensive rare earth-transition metal-nitrogen based magnets. This Sm-Fe-N magnet powder is said to exhibit the maximum saturation magnetization by being composed of Sm ₂ Fe ₁₇ N _x (x = 3) (see Non-Patent Document 1).
This rare earth-iron-nitrogen based magnet has been conventionally used in a melting method in which a rare earth-iron alloy is produced using a high frequency furnace, an arc furnace or the like using Fe and Sm metal, Fe, Fe ₂ O ₃ , Sm ₂ O _3, etc. It is obtained by nitriding a mother alloy obtained by a reduction diffusion method in which a rare earth-iron alloy is produced by mixing heat treatment of Ca. The powdered rare earth-iron-nitrogen based magnet obtained in this way has a coercive force generation mechanism that is a nucleation type, so that in the next step, the average particle size is reduced to several μm to about 5 μm. It has been crushed.

On the other hand, there is a method (refer to Patent Documents 1 and 2) in which a fine magnetic powder is obtained without pulverizing the master alloy by reducing the particle size of the powder used as the starting material, but the raw material becomes expensive. Industrially, it is impractical because of cost limitations.
In addition, the melting method requires heat treatment for melting, pulverizing, and homogenizing the raw material powder at 1500 ° C. or higher (see Patent Document 3), and the process is extremely complicated. Impurities are generated by oxidation due to exposure to the inside, and nitriding is performed after wet processing. However, since the surface is oxidized during wet processing, nitriding cannot proceed uniformly, so that saturation magnetization and coercive force among magnetic properties. , The squareness is lowered, and as a result, the maximum energy product is lowered. In addition, because the rare earth metal required as a raw material is expensive, the method for producing a rare earth-iron-nitrogen based magnet is more cost-effective than the reduction diffusion method in which an inexpensive rare earth oxide powder can be used as a raw material. It is considered inferior.

From the above situation, conventionally, a mixture containing at least an iron powder having an average particle diameter of about 50 μm, a rare earth oxide, and a reducing agent for reducing the rare earth oxide is mixed in a non-oxidizing atmosphere. The reduction diffusion method by heating and firing is advantageous. First, a reduction product containing a rare earth-iron alloy is obtained, and then this reduction product is wet-processed to form in the reduction product. The oxide of the reducing agent is removed, and then the obtained rare earth-iron-based alloy is nitrided in a mixed gas stream containing ammonia and hydrogen, and then pulverized and dried to obtain a desired rare earth-iron-nitrogen system. Manufactures magnet powder.
As described above, in the conventional method for producing a rare earth-iron-nitrogen based magnet powder using the reduction diffusion method, generally, the reduction product obtained in the reduction diffusion step is wet-treated, and then the obtained rare earth-iron alloy is used. Nitriding is performed (see Patent Document 4). In the reduced product, the Sm ₂ Fe ₁₇ phase that is the main phase and the SmFe ₃ phase, the SmFe ₂ phase, and the CaO that are non-magnetic phases are mixed together. Or removed by acidic solution. In addition, before the wet treatment, hydrogen is absorbed into the reduced product to cause collapse (see Patent Documents 5 and 6). As a result, the particle size of the reduced product is reduced, and wet processing can be performed more efficiently.

In order to uniformly distribute nitrogen to the rare earth-iron alloy in the nitriding step after the wet process, the particle size is adjusted after the wet process. This particle size adjustment eliminates the sieve having a mesh size of 106 μm, which shows a decrease in magnetic properties after nitriding.
If there is a large amount of nonmagnetic phase remaining after wet processing, the ratio of the main phase is lowered, and the saturation magnetization 4πIm is lowered. However, if these nonmagnetic phases are removed too much, the iron oxyhydroxide adhering to the Sm ₂ Fe ₁₇ phase, which is the main phase in the wet processing liquid, is reduced to α-Fe in the subsequent nitriding step, Since it becomes a new creation site, the coercive force iHc and the squareness Hk are significantly reduced. Therefore, in the conventional method, wet processing is performed by selecting conditions such that SmFe ₃ phase and the like existing so as to cover the main phase particles remain to some extent. However, in the subsequent nitriding, most of the SmFe ₃ phase is peeled off from the main phase particles, but it is not complete, and if there is too much SmFe ₃ phase, it cannot be completely removed, and finally obtained rare earth-iron-nitrogen based magnet powder The saturation magnetization of 4πIm was reduced. In addition, non-uniform nitridation and α-Fe generation occur due to oxidation of the particle surface during wet processing and drying, and further, hydrogen is dissolved in the magnet powder by acid cleaning, and the magnetic properties tend to be reduced. there were.

The powdered rare earth-iron-nitrogen based magnet obtained as described above has a coercive force generation mechanism that is a nucleation type, so that the average particle size in the next step is from several μm to 5 μm. It needs to be crushed. Therefore, the non-magnetic phase that lowers the magnetic properties is reduced, and furthermore, rare earth-iron-nitrogen based magnet powder free from the distortion of crystals serving as the core of magnetization reversal and free of α-Fe can be obtained. The establishment of a method was strongly desired.
Japanese Patent Laid-Open No. 11-189811 Japanese Patent Laid-Open No. 2003-29766 Japanese Patent Laid-Open No. 3-141608 JP-A 61-295308 JP-A-9-241708 Japanese Patent Laid-Open No. 11-124605 T.A. Iriyama IEEE TRANSACTIONS ON MAGNETICS, VOL. 28, NO. 5 (1992)

  In view of such a situation, the present invention uniformly nitrides using the reduction diffusion method, so that not only the nonmagnetic phase but also the crystal distortion or α-Fe residual that becomes the nucleus of magnetization reversal (nucleation). Method for producing rare earth-iron-nitrogen based magnet powders with excellent yield and low cost, and a rare earth-iron-nitrogen system obtained by the method It is to provide magnet powder.

  As a result of intensive studies to solve such conventional problems, the present inventors have found that the surface of the particles obtained by reduction diffusion treatment is required in order to improve the performance of rare earth-iron-nitrogen based magnet powder. Nitride nitriding in a state that is not covered with oxide film and does not interfere with nitriding, and then clarified that wet processing (pickling) should be strengthened to eliminate non-magnetic phase and reduce the degree of processing by grinding. In addition, the reduction temperature is set to a lower region than before, and the reduction diffusion treatment is performed, and the hydrogen is absorbed and collapsed, and after cooling to a specific temperature or less, the atmosphere and temperature during the nitriding treatment are controlled. After nitriding uniformly, the obtained nitriding product is wet-processed, the Ca content is washed and separated, and further, hydrogen dissolved in the magnet powder is removed by heat treatment at the time of pickling in the wet process. Can reduce nonmagnetic phase, high saturation Reduction is obtained, crystals of the strain to be nuclear magnetization reversal, found that the squareness of the a demagnetization curve reduction can high coercive force of the alpha-Fe is improved, and accomplished the present invention.

  That is, the first invention of the present invention is a mixture of rare earth oxide powder, iron powder, and at least one reducing agent powder selected from alkali metals, alkaline earth metals or hydrides thereof at a predetermined ratio. A step of heating the obtained mixture in an inert gas atmosphere at 900 to 1180 ° C., and subsequently cooling the obtained reaction product to 500 ° C. or less in an inert gas atmosphere, A process of supplying a gas containing hydrogen after having partly discharged, and absorbing and decomposing hydrogen in the obtained reaction product, and then maintaining the collapsed reaction product at a temperature of 300 ° C. or lower and ammonia and Supplying a mixed gas containing hydrogen, raising the temperature in this air stream, nitriding the reaction product at 350 to 500 ° C., then throwing the obtained nitriding product into water Wet treatment A step of heat-treating the wet-processed coarse magnet powder at 120 to 480 ° C. to remove hydrogen that has penetrated into the magnet alloy by the wet-treatment; There is provided a method for producing a uniformly nitrided rare earth-iron-nitrogen based magnet powder characterized by comprising a pulverizing step.

The second invention of the present invention provides the method for producing a rare earth-iron-nitrogen based magnet powder according to the first invention, wherein the cooling temperature of the reaction product is 250 ° C. or lower. .
According to a third aspect of the present invention, there is provided a rare earth-iron-nitrogen based magnet powder according to the first aspect, wherein the wet-processed magnet coarse powder is heat-treated in a vacuum or an inert gas atmosphere. A manufacturing method is provided.

In addition, according to a fourth aspect of the present invention, in any one of the first to third aspects, the mixing amount of the rare earth oxide powder is 1.1 times to 1.4 times the stoichiometric composition of R ₂ Fe _17. A method for producing a rare earth-iron-nitrogen based magnet powder is provided.
Further, in a fifth invention according to the first invention, the coarse magnet powder has a form of secondary particles in which primary particles are gathered and sintered in the shape of grapes. There is provided a method for producing a rare earth-iron-nitrogen based magnet powder characterized in that the cumulative number percentage having a particle size of 20 μm or more is less than 10%.
Further, the sixth invention of the present invention is the production of a rare earth-iron-nitrogen based magnet powder according to the first invention, wherein the ammonia partial pressure in the mixed gas is 0.2 to 0.6 atm. A method is provided.

On the other hand, the seventh invention of the present invention provides a rare earth-iron-nitrogen based magnet powder obtained by the method of any one of the first to sixth inventions.
According to an eighth aspect of the present invention, there is provided the rare earth-iron-nitrogen based magnet powder according to the seventh aspect, wherein the rare earth element is Sm.
The ninth invention of the present invention provides the rare earth-iron-nitrogen based magnet powder according to the sixth or seventh invention, wherein the Sm content is 23.2 to 23.6% by weight. Is done.
According to a tenth aspect of the present invention, there is provided a rare earth-iron-nitrogen based magnet powder according to the seventh aspect, wherein the amount of hydrogen contained in the magnet powder is 0.06 wt% or less. The

The eleventh invention of the present invention is the rare earth-iron according to any one of the seventh to tenth inventions, wherein the α-Fe ratio represented by the following general formula (1) is 5% or less. -A nitrogen-based magnet powder is provided.
α-Fe ratio = α-Fe (110) peak intensity / rare earth-Fe-nitrogen (300) peak intensity in X-ray diffraction (1)

Furthermore, the twelfth invention of the present invention is the seventh or eighth invention, wherein the integral width represented by the following general formula (2) is 0.2 deg. A rare earth-iron-nitrogen based magnet powder is provided which is characterized by:
Integration width = Sm ₂ Fe ₁₇ N ₃ in X-ray diffraction (113) Area of diffraction peak / peak intensity height (2)

According to the present invention, when performing the reduction diffusion treatment on the raw material mixture, and subsequently performing the nitriding treatment and then performing the wet treatment, the reduction product absorbs hydrogen and collapses after the reduction diffusion treatment is completed. The surface of the active alloy powder particles can be uniformly nitrided and the yield can be improved. After that, maintaining the good state so that the particle surface of the collapsed reduced product is not oxidized and lowering the nitriding efficiency, lowering the reduction diffusion temperature than in the conventional method to 900-1180 ° C., the primary particles are small A rare earth-iron-nitrogen based magnet powder is produced. As a result, the stress applied during grinding can be reduced by reducing the grinding load, and the distortion of the magnet powder crystal can be reduced.
In addition, non-magnetic phase can be reduced by performing wet treatment after nitriding treatment instead of nitriding after wet processing, and iron oxyhydroxide adheres around the main phase during wet processing, and the iron oxyhydroxide during nitriding Is not precipitated as α-Fe, and the Ca component is washed and separated after the wet treatment, and further, the hydrogen dissolved in the magnet powder at the time of pickling in the wet treatment is removed by heat treatment, Squareness can be improved. Therefore, it is possible to obtain a rare earth-iron-nitrogen based magnet powder having a small α-Fe ratio with a high saturation magnetization and a coercive force and a good squareness of the demagnetization curve, and a low manufacturing cost. The value is extremely great.

  Hereinafter, the uniformly nitrided rare earth-iron-nitrogen based magnet powder of the present invention and the manufacturing method thereof will be described in detail with reference to the drawings.

  The present invention includes a step of mixing a rare earth oxide powder, an iron powder, and at least one reducing agent powder selected from an alkali metal, an alkaline earth metal, or a hydride thereof at a predetermined ratio, and an obtained mixture A step of heating at 900 to 1180 ° C. in an inert gas atmosphere, and subsequently cooling the obtained reaction product to 500 ° C. or less in an inert gas atmosphere, and then discharging at least a part of the inert gas. A step of supplying a gas containing hydrogen and allowing the resulting reaction product to absorb and disintegrate hydrogen, and then a mixed gas containing ammonia and hydrogen while maintaining the disintegrated reaction product at a temperature of 300 ° C. or lower. The step of nitriding the reaction product at 350 to 500 ° C., then adding the obtained nitriding product into water and performing a wet treatment, Wash The separated magnetic crude powder was heat treated at 120 ° C. or higher, removing the hydrogen which has entered into the magnet alloy by the wet process, then includes the step of finely pulverizing the magnet crude powder obtained.

1. Production Method of Rare Earth-Iron Master Alloy (1) Mixing of Raw Material Powder First, rare earth oxide powder and iron powder are prepared and mixed as magnet raw material powder.
The rare earth oxide powder is not particularly limited, but at least one element selected from Sm, Gd, Tb, and Ce, or at least selected from Pr, Nd, Dy, Ho, Er, Tm, and Yb. Those containing one kind of element are preferred. Among these, those containing Sm are particularly preferable because the effects of the present invention can be remarkably exhibited. When Sm is contained, in order to obtain a high coercive force, it is preferable to obtain Sm of 60% by weight or more, preferably 90% by weight or more of the entire rare earth in order to obtain a high coercive force.

As the iron powder, for example, reduced iron powder, gas atomized powder, water atomized powder, electrolytic iron powder, and the like can be used, and classification is performed so as to obtain an optimum particle size as necessary.
Here, up to 30% by weight of the iron powder can be added as iron oxide powder to adjust the calorific value of the reduction diffusion reaction. When a rare earth-iron-cobalt-nitrogen based magnet powder having a composition in which 20% by weight or less of Fe is replaced with Co is produced, cobalt powder and / or cobalt oxide powder and / or iron-cobalt are used as a Co source. Use alloy powder. As the cobalt oxide, for example, cobaltous oxide, cobalt tetroxide, or a mixture thereof having the above particle size can be used.

Here, each magnet raw material powder is composed of iron powder in which powder having a particle size of 10 to 70 μm accounts for 80% or more of the whole, rare earth oxide powder in which powder having a particle size of 10 μm or less accounts for 80% or more of the total, cobalt When adding, it is preferable to use cobalt powder and / or cobalt oxide powder.
When the number of iron powders exceeding 70 μm increases, the iron part in which rare earth elements are not diffused increases in the rare earth-iron mother alloy powder, the particle diameter of the mother alloy powder increases, and the nitrogen distribution is uneven. Thus, the squareness of the obtained rare earth-iron-nitrogen based magnet powder tends to be lowered.
On the other hand, the rare earth oxide powder and the cobalt oxide powder have a composition of less than 30% by weight even in the rare earth oxide powder, which is the most abundant of these. It is desirable that there be a uniform distribution around. Therefore, it is preferable that the powder having a particle size of 0.1 to 10 μm occupies 80% or more of the whole.
When the powder having a particle size of less than 0.1 μm increases, the powder rises during manufacture and becomes difficult to handle. Further, when the number of particles exceeding 10 μm increases, the iron part in which the rare earth element in the rare earth-iron-mother alloy powder obtained by the reduction diffusion method has not diffused increases.
Here, for iron (-cobalt) -alloy powder, powder having a particle size of 10 to 80 μm accounts for 80% or more of the whole, and for rare earth oxide powder, powder having a particle size of 0.1 to 10 μm is used. What occupies 80% or more of the whole is preferable. When the particle size exceeds 80 μm, the iron part in which the rare earth element is not diffused increases in the rare earth-iron master alloy, the particle size of the master alloy powder increases, and the nitrogen distribution becomes nonuniform. The squareness of the obtained rare earth-iron-nitrogen based magnet powder tends to be lowered.

(2) Reduction Diffusion Next, the above raw material powders are mixed, heat-treated at a predetermined temperature in an inert gas atmosphere, and a rare earth-iron-based master alloy having a Th ₂ Zn ₁₇ type crystal structure by a reduction diffusion method. To manufacture.

As described above, the reduction diffusion method involves heating a mixture of a rare earth oxide powder, another metal powder, and a reducing agent such as Ca in an inert gas atmosphere at, for example, 900 to 1300 ° C. This is a method of directly obtaining alloy powder by removing the reducing agent components such as CaO and residual Ca as a by-product by wet-treating the product.
In the present invention, a rare earth oxide and other oxide raw materials are reduced and reduced by putting a magnetic raw material powder made of iron and, if necessary, cobalt and a reducing agent into a reaction vessel and subjecting to heat treatment. A rare earth element such as a rare earth element is diffused into the iron powder to produce a rare earth-iron mother alloy having a Th ₂ Zn ₁₇ type crystal structure.
The rare earth oxide powder is preferably added in a range of 1.1 to 1.4 times the stoichiometric composition of R ₂ Fe ₁₇ . If it is less than 1.1 times, the diffusion of rare earth elements with respect to iron powder becomes non-uniform. Further, in order to perform uniform nitriding, it is necessary to hydrogen decay the reduced product before nitriding. However, when the Sm rich phase is reduced, the particles are easily sintered and the hydrogen decay property of the reduced product is deteriorated, and the resulting rare earth-iron-nitrogen is obtained. This is not preferable because the coercive force and squareness of the system magnet powder are lowered. If it exceeds 1.4 times, the number of Sm-rich phases that lower the magnetization other than the main phase increases, and it is necessary to remove the Sm-rich phases, resulting in a decrease in yield and cost for removal.
Here, it is important that the raw material powders are uniformly mixed so as not to be separated due to a difference in powder characteristics. As a mixing method, for example, a ribbon blender, a tumbler, an S-shaped blender, a V-shaped blender, a Nauter mixer, a Henschel mixer, a super mixer, a high speed mixer, a ball mill, a vibration mill, an attritor, a jet mill and the like can be used.

As the reducing agent, alkali metals, alkaline earth metals, hydrides thereof, and the like can be used. From the viewpoint of safety in handling and cost, granular metallic calcium sieved to a mesh size of 4.00 mm or less is preferable. The reducing agent is mixed with the raw material powder or separated so that calcium vapor can come into contact with the raw material powder, but if mixed and reduced and diffused, the reaction product becomes porous, and the subsequent nitriding treatment is performed. Can be done efficiently.
It is also effective to mix an additive that promotes the decay of the reaction product in the subsequent wet processing step together with the raw material powder and the reducing agent. As the disintegration accelerator, alkaline earth metal salts such as calcium chloride, calcium oxide, and the like can be used, and they are uniformly mixed simultaneously with the raw material powder and the like. Here, the inert gas is at least one selected from argon gas and helium gas.

  In the present invention, the heat treatment temperature needs to be in the range of 900 to 1180 ° C. When the temperature is less than 900 ° C., the rare earth element diffuses unevenly with respect to the iron powder, and the coercive force and squareness of the obtained rare earth-iron-nitrogen based magnet powder are lowered. Further, if the heat treatment temperature is less than 900 ° C., it takes time for diffusion, which is not desirable. On the other hand, if it exceeds 1180 ° C, the generated rare earth-iron mother alloy causes grain growth, so that uniform nitriding becomes difficult, and the saturation magnetization and squareness of the magnet powder may be reduced.

Here, the relationship between the heat treatment temperature and the particle size distribution (accumulated number percentage) is shown in FIG. 1, and the SEM image is shown in FIG. FIG. 1 shows that the particle size of the obtained nitriding product increases as the heat treatment temperature increases. From the SEM image of FIG. 2, when the heat treatment temperature is high (1190 ° C.), the surface of the rare earth-iron-nitrogen alloy particles is smooth, whereas the primary particles become smaller as the heat treatment temperature is lowered. When temperature is 1050 degreeC, it turns out that the secondary particle sintered in the shape of a grape is formed.
That is, in the present invention, the rare earth-iron-nitrogen-based powder (magnet coarse powder) in the nitriding product is a large number of primary particles including those having a small particle size, and is sintered into a grape shape. The next particle is formed. In this case, it is desirable that the primary particles have a small proportion of particles having a particle size of 20 μm or more, and the cumulative number percentage is less than 10%. Such a powder is not only easy to grind, but also has excellent magnetic properties.
The heat treatment temperature is preferably 930 to 1080 ° C., and a reaction product containing rare earth-iron mother alloy particles having a small primary particle diameter is used, so that nitrogen easily diffuses from the rare earth-iron mother alloy grain boundary during nitriding. This is the reason why the nitriding distance becomes shorter. Further, at the time of pulverization, since the strength of the grain boundary between the sintered particles is low, the degree of processing can be small, so that the crystal distortion can be reduced. Furthermore, it is preferable that the heat treatment temperature is lower because the evaporation of Sm is less and the input amount can be reduced.

Here, the product obtained by the reduction diffusion reaction, for example, when metallic calcium is used as the reducing agent, rare earth-iron mother alloy having a Th ₂ Zn ₁₇ type crystal structure and calcium oxide, unreacted surplus It is a massive mixture composed of metallic calcium and the like. Furthermore, when granular metal calcium is mixed with the raw material powder and subjected to a reduction diffusion reaction, a porous massive mixture is obtained.
On the other hand, the melting method employed in Patent Document 3 uses a rare earth metal as the rare earth material, which is more expensive than the rare earth oxide material used in the reduction diffusion method. In particular, when the rare earth element is Sm that provides excellent magnetic properties, the difference is significant. Moreover, the unnecessary powder generated by the particle size adjustment reduces the product yield and further increases the powder cost. In addition, the melting method requires a homogenization heat treatment step for eliminating the α-Fe phase in the obtained alloy, and further includes a step of coarsely pulverizing the alloy subjected to the homogenization heat treatment before introducing nitrogen, and a coarse pulverization step. This is not preferable because it requires a step of adjusting the particle size of the powder.

In the present invention, the reaction product after the reduction-diffusion reaction is then cooled from the heat treatment temperature to 500 ° C. or lower, preferably 250 ° C. or lower without changing the atmospheric gas as an inert gas. . Here, the inert gas is at least one selected from argon gas and helium gas as described above. At this time, if the temperature after cooling exceeds 500 ° C., the risk of explosion or the like increases when supplying the gas containing hydrogen, which is not preferable.
For example, when a reduction diffusion reaction is performed using calcium as a reducing agent, the obtained reaction product is a lump made of rare earth-iron (-cobalt) mother alloy powder, calcium oxide, unreacted excess metallic calcium, and the like. It becomes a mixture aggregate.

A rare earth-iron-nitrogen based magnet, for example, an Sm—Fe—N based magnet powder is said to exhibit the maximum saturation magnetization by being composed of Sm ₂ Fe ₁₇ N _x (x = 3). That is, it is known that the magnetic properties are deteriorated when the amount of nitrogen is too small or too large. Under such circumstances, when nitrogen is diffused into Sm—Fe in a subsequent step, nitriding must be performed uniformly so that the above composition is obtained.
When the aggregate of the reaction product obtained by the reduction diffusion treatment is a lump exceeding an outer diameter of 10 mm, the amount of nitrogen after nitriding tends to be low. The reason for this is that excess metal Ca that does not contribute to the reaction in the reduction diffusion treatment does not form a solid solution in the produced Sm-Fe alloy but exists at the grain boundaries of the Sm-Fe alloy powder, This seems to be due to hindering the diffusion of nitrogen into the Sm-Fe alloy. Therefore, in order to perform nitridation uniformly, it is desirable that nitrogen can reach the generated Sm—Fe alloy surface evenly, and the average outer diameter of the aggregate of the reaction product is 10 mm or less before the nitriding treatment. Is preferred.

(3) Hydrogen treatment The present invention is characterized in that a hydrogen treatment is performed on the reaction product. The cooling is performed so that the temperature of the atmosphere containing at least hydrogen is 500 ° C. or lower. When the temperature exceeds 500 ° C., the energy consumption increases, and the target rare earth-iron mother alloy can be decomposed or a side reaction product can be generated. Occlusion of hydrogen in the reaction product can be performed sufficiently even at room temperature. When the reaction product occludes hydrogen, self-heating occurs and the material temperature rises, so care must be taken not to exceed 500 ° C.

In the hydrogen treatment, after the reduction diffusion treatment is performed, the inert gas used in the reduction diffusion treatment is replaced with a hydrogen atmosphere gas while the cooled reaction product is put in the furnace, and the atmosphere gas containing hydrogen is added. It is carried out by compressing or flowing for a certain period of time while flowing. At this time, heating may be performed within a range that does not adversely affect the nitriding treatment in the next step.
The replacement of the hydrogen gas is preferably performed by degassing the inert gas in the furnace and introducing the hydrogen gas after evacuation, because the hydrogen gas can be completely replaced in a short time. The degree of vacuum at this time is preferably −30 kPa or less, more preferably −100 kPa or less with respect to atmospheric pressure. Since argon gas has a higher specific gravity than hydrogen gas, hydrogen treatment cannot be effectively performed if hydrogen gas cannot be completely replaced to the bottom of the reaction product, and may remain in a large mass after hydrogen treatment. Therefore, attention is required. Next, it is preferable to pressurize the pressure in the furnace to +5 kPa or more with respect to atmospheric pressure in order to promote the occlusion of hydrogen after replacement with an atmospheric gas containing hydrogen. The pressurization is more preferably +10 to 50 kPa with respect to atmospheric pressure. When the reaction product occludes hydrogen in a pressurized state, it can be confirmed that the hydrogen occlusion proceeds by gradually decreasing from the initial pressurization pressure.

In the reaction product, the Sm ₂ Fe ₁₇ phase, which is the main phase, is usually covered with an Sm rich phase. By performing the above hydrogen treatment, hydrogen enters the crystal lattice of the Sm-rich phase, etc., and the Sm-rich phase has a larger expansion coefficient than the main phase, so it breaks from the grain boundary between the Sm-rich phase and the main phase. To do. In addition, unreacted reducing agent, calcium oxide, and the like around the strongly agglomerated reaction product react with hydrogen, and the agglomeration is loosened and collapses.
It is preferable to set the reaction temperature and time so that the particle size of the taken-out disintegrant is 10 mm or less, preferably 1 mm or less. In the state where the particle size of the collapsed material exceeds 10 mm, uniform nitriding becomes difficult in the nitriding treatment process, and the square shape of the magnetic characteristics is lowered, and there is no effect of hydrogen treatment.

As shown in Patent Document 5 (Japanese Patent Laid-Open No. 9-241708) and Patent Document 6 (Japanese Patent Laid-Open No. 11-124605), when the reaction product is cooled by a conventional reduction diffusion method, the reaction product is cooled after being cooled. It will naturally collapse by taking it out and exposing it to the atmosphere.
However, the reaction product that has been subjected to hydrogen treatment according to the present invention and occluded with hydrogen has already collapsed when taken out of the container after the hydrogen treatment, and the disintegration property in the subsequent nitriding step is also improved. Therefore, the agglomeration of the produced Sm ₂ Fe ₁₇ phase magnetic powder, which is the main phase, collapses small, and the surface of the magnetic powder becomes active, and the distribution of nitrogen in the magnetic powder alloy is uniform in the subsequent nitriding treatment. As a result, the squareness of the demagnetization curve of the rare earth-iron-nitrogen based magnet powder obtained by fine pulverization is improved. Further, the rare earth-iron-nitrogen based coarse magnet powder obtained by nitriding after being disintegrated by hydrogen treatment as in the present invention has a uniform nitrogen distribution, so that the rare earth-iron-nitrogen based system reduces the magnetic properties. Since the magnet powder decreases, the yield increases.

(4) Cooling of collapsed material After the hydrogen treatment, if the temperature of the collapsed product exceeds 300 ° C, the nitridation reaction with the reaction product proceeds rapidly during nitriding, increasing the α-Fe phase. Therefore, it is desirable to cool to a temperature lower than 300 ° C. This is because, at temperatures exceeding 300 ° C., the reaction product is active, so the alloy is rapidly nitrided, and the intermetallic compound having a Th ₂ Zn ₁₇ type crystal structure is decomposed into an Fe-rich phase and SmN. Because it is presumed. However, no improvement in magnetic properties can be expected even when cooled to a temperature lower than 20 ° C.

Many reduction diffusion methods have been proposed so far, but the reaction product after the reduction diffusion reaction is absorbed and collapsed before nitriding, and nitriding is rarely performed thereafter. This is because cooling is once performed before supplying hydrogen, which leads to loss of heat energy.
In addition, in most cases, a step of cooling the reduced product is employed prior to nitriding, but the temperature after cooling is within the nitriding temperature range. That is, it was not cooled to a temperature lower than 300 ° C., which is the minimum temperature for nitriding. The main reason is that the lower the temperature, the more heat energy is required to raise the temperature in the next nitriding step. Therefore, the mechanism by which the mother alloy is nitrided by continuously cooling the reaction product to 300 ° C. or lower without changing the atmospheric gas as an inert gas has been completely studied. There wasn't.

2. Method for Producing Rare Earth-Iron-Nitrogen Magnet Powder After cooling, the atmosphere gas is changed to a nitriding gas without moving the porous collapsed reaction product to the next nitriding step. If the reaction product is exposed to the atmosphere at this time, the active rare earth-iron mother alloy powder in the reaction product is oxidized and the reactivity is deactivated, resulting in a variation in the degree of nitriding. It is necessary to bring it into the nitriding process so as not to be exposed to the atmosphere (oxygen).

(1) Nitriding treatment In the nitriding process, after the inert gas of the atmospheric gas is discharged, the temperature is raised by supplying a mixed gas containing at least ammonia and hydrogen while maintaining the temperature at 300 ° C. or lower. The object is heated to a specific temperature.

  In the conventional method, the magnet raw material powder is reduced and diffused, the reaction product is taken out after cooling, the rare earth-iron master alloy obtained by wet processing is nitrided and finely pulverized to obtain the rare earth-iron-nitrogen based magnet powder. I am making it. However, when the rare earth-iron-nitrogen based magnet powder thus obtained is analyzed, the amount of Sm is high and the nonmagnetic phase is increased. In addition, the X-ray diffraction of the pulverized powder has larger crystal distortion and α-Fe ratio, which are the cores of magnetization reversal, compared to the rare earth-iron-nitrogen based magnet powder before pulverization. A large lump of about mm is included in about 60% by weight. When the magnetic properties are measured by pulverizing the rare earth-iron-nitrogen based magnet powder obtained by nitriding the rare earth-iron master alloy containing this lump with an aperture of 106 μm and measuring the magnetic properties, the demagnetization curve The squareness (HK) of the steel becomes low, and a preferable magnet powder cannot be obtained.

On the other hand, in the present invention, as described above, after absorbing and collapsing hydrogen into the mother alloy, the atmospheric gas is changed, and the temperature is raised in a mixed gas stream containing ammonia and hydrogen, and 350 to The reaction product is subjected to nitriding treatment at 500 ° C., and then the obtained nitriding treatment product is put into water and wet-treated. The nitriding gas needs to contain at least ammonia and hydrogen, and argon, nitrogen, helium, etc. can be mixed to control the reaction. The amount of the nitriding gas is preferably an amount sufficient for the amount of nitrogen in the magnet powder to be 3.3 to 3.7% by weight.
The ratio of ammonia to the total airflow pressure (ammonia partial pressure) is 0.2 to 0.6, preferably 0.3 to 0.5. If the ammonia partial pressure is less than 0.2, the nitridation of the master alloy does not proceed over a long period of time, and the amount of nitrogen cannot be reduced to 3.3 to 3.7% by weight. The coercive force decreases.

It is necessary to perform a nitriding heat treatment of the master alloy by supplying a mixed gas stream containing ammonia and hydrogen at a nitriding temperature of 350 to 500 ° C., preferably 400 to 480 ° C. When the temperature is less than 350 ° C., it takes a long time to introduce 3.3 to 3.7% by weight of nitrogen into the rare earth-iron master alloy in the reaction product, so that the industrial advantage is lost. On the other hand, when the temperature exceeds 500 ° C., the Sm ₂ Fe ₁₇ phase, which is the main phase, is decomposed to produce α-Fe, and thus the squareness of the demagnetization curve of the finally obtained rare earth-iron-nitrogen based magnet powder. Is unfavorable because it decreases. From the cooling temperature to the nitriding temperature, it is desirable for increasing the production efficiency to raise the temperature relatively rapidly at a rate of 3 to 10 ° C. per minute. Further, the holding time at the cooling temperature is not particularly limited.
The retention time for the nitriding treatment is 100 to 300 minutes, preferably 140 to 250 minutes, although it depends on the nitriding temperature. If it is less than 100 minutes, nitriding becomes insufficient, while if it exceeds 300 minutes, nitriding proceeds excessively, which is not preferable.

In the present invention, following the nitriding treatment, it is desirable to further heat-treat the alloy powder in an inert gas such as hydrogen gas, nitrogen gas, argon gas or helium gas. Particularly preferred is a heat treatment with nitrogen gas and / or argon gas after heat treatment with hydrogen gas.
Thereby, the nitrogen distribution in the individual crystal cells constituting the magnet powder can be made more uniform, and the squareness can be improved. The holding time of the heat treatment is 30 to 200 minutes, preferably 60 to 250 minutes.

(2) Wet treatment In the present invention, the treated product after nitriding is wet treated, and the by-products (calcium oxide, calcium nitride, etc.) of the reducing agent component contained therein are rare earth-iron-nitrogen based magnet powder. Separate and remove from.

As described above, the wet treatment is performed on the magnet powder after the nitridation. When the reaction product is wet-treated before nitriding, the surface of the mother alloy is oxidized during this wet treatment process, thereby varying the degree of nitridation. Because it can be used.
In addition, if the treatment product is left in the atmosphere for a long time after nitriding, an oxide of a reducing agent component such as calcium is generated and difficult to remove, or the surface of the magnet powder is oxidized, resulting in non-uniform nitriding. The squareness decreases due to the decrease in the ratio of nuclei and the formation of nuclei of new creation. Therefore, the nitriding product left in the atmosphere is preferably wet-treated within two weeks after being taken out from the reactor.

In the wet treatment, first, the disintegrated product is put into water, and decantation-water injection-decantation is repeated to remove much of the produced Ca (OH) ₂ . Further, if necessary, in order to remove residual Ca (OH) ₂ , acid washing is performed using acetic acid and / or hydrochloric acid. It is good to implement in the range whose hydrogen ion concentration pH of the aqueous solution at this time is 4-7. There may be a non-magnetic phase around the main phase that lowers the saturation magnetization of the magnetic properties due to the influence of Sm added excessively during reduction diffusion, and the Sm amount is 23.2 to 23.6% by weight. Thus, it is preferable to perform pickling.
After the completion of the acid cleaning treatment, for example, washing with water, dehydrating with an organic solvent such as alcohol or acetone, and drying in an inert gas atmosphere or vacuum can obtain a rare earth-iron-nitrogen based magnet coarse powder. it can.

(3) Dehydrogenation treatment During pickling in this wet treatment, hydrogen reacts with the rare earth-iron (-cobalt) -nitrogen magnet or the rare earth-iron-cobalt-nitrogen magnet coarse powder and enters the alloy. When hydrogen is dissolved in the magnet powder, iHc is greatly reduced. For this reason, it is necessary to remove hydrogen dissolved in the magnet powder by heat treatment.

  The atmosphere for the heat treatment is not particularly limited, but it may be performed in a vacuum or in an inert gas. Preference is given to a vacuum. FIG. 3 shows the relationship between the heating temperature, iHc, and Hk when the magnet coarse powder after the wet treatment is heated in vacuum. The processing time was 30 minutes. The iHc and Hk have good characteristics in the heating temperature range of 120 to 480 ° C. FIG. 4 shows the relationship between the amount of hydrogen in the magnet powder after heat treatment and iHc, Hk when the magnet coarse powder after the wet treatment is heat-treated at 250 ° C. in vacuum. It can be seen that good magnetic properties are exhibited when the amount of hydrogen in the magnet coarse powder is 0.06 wt% or less. Considering the above results, it can be said that the treatment temperature is 120 to 480 ° C., and at this time, the amount of hydrogen in the magnet powder is preferably 0.06% by weight or less.

If the heating temperature is lower than 120 ° C., a long treatment time is required and the efficiency is poor, and if it exceeds 480 ° C., the magnet powder is decomposed to produce α-Fe, so that iHc and Hk are lowered.
The obtained rare earth-iron-nitrogen based magnet coarse powder has a shape in which the particle surface is not smooth and a large number of particles having different particle diameters are aggregated as a whole.
More specifically, a large number of particles having a smaller particle diameter gather around the primary particles having a relatively large particle diameter, and are sintered into grapes to form secondary particles. The proportion of primary particles having a particle size of 20 μm or more is small, and the cumulative number percentage is less than 10%.

(4) Fine grinding and drying Next, the obtained magnet coarse powder is put together with a solvent in a grinding machine such as a bead mill or a medium stirring mill so that the rare earth-iron-nitrogen based magnet powder has an average particle diameter of 1 to 5 μm. Finely pulverize, then filter and dry.

The fine pulverization of the magnet coarse powder in the present invention is not particularly limited as long as it is a pulverizer that is widely used in various chemical industries handling solids and pulverizes various materials to a desired degree. . Among these, it is preferable to use a wet pulverization method using a medium stirring mill or a bead mill, which is excellent in that the composition and particle size of the powder can be made uniform easily.
As a solvent used for pulverization, isopropyl alcohol, ethanol, toluene, methanol, hexane, or the like can be used, and isopropyl alcohol is particularly preferable. After pulverization, a rare earth-iron-nitrogen based magnet fine powder is obtained by filtering and drying using a filter having a predetermined opening.

3. Rare earth-iron-nitrogen based magnet powder In the present invention, the rare earth-iron-nitrogen based magnet powder obtained by the above method is not limited by the kind of rare earth, but Sm-Fe-N is preferred. In particular, the Sm content is more preferably 23.2 to 23.6% by weight with respect to the whole magnet powder.

The rare earth-iron-nitrogen based magnet powder of the present invention is characterized in that the α-Fe ratio represented by the following general formula (1) is 5% or less.
α-Fe ratio = α-Fe (110) peak intensity / rare earth-Fe-nitrogen (300) peak intensity in X-ray diffraction (1)
This α-Fe ratio is obtained by removing the background of the wide-area measurement result and then the position of the (110) plane of α-Fe (JCPDS No. 6-696) and the (300) plane of Sm ₂ Fe ₁₇ N _3. It is calculated by the following formula using the corresponding peak intensities I _Fe and I _SFN . In the original X-ray diffraction quantitative analysis, it is necessary to correct the peak intensity ratio between the compounds. However, if the rare earth-iron-nitrogen magnet according to the present invention is used, such correction may be omitted. . Further, it is assumed that there is no compound other than α-Fe, Sm ₂ Fe ₁₇ (Sm ₂ Fe ₁₇ N ₃ : main phase).
When the ratio of α-Fe deposited on the surface of the main phase of the rare earth-iron-nitrogen based magnet powder becomes larger than 5%, the magnet powder main phase becomes a nucleation site, and therefore the coercive force iHc and the squareness Hk are reduced. It will drop significantly.

The rare earth-iron-nitrogen magnet powder of the present invention is obtained as a rare earth-iron-nitrogen magnet powder having small primary particles by lowering the reduction diffusion temperature. Therefore, since the stress during pulverization is small, the distortion of the crystal is small. This is confirmed by X-ray diffraction measurement of the obtained rare earth-iron-nitrogen based magnet powder. In the present invention, the integral width represented by the following general formula (2) is 0.2 deg. It is characterized by the following.
Integration width = Sm ₂ Fe ₁₇ N ₃ in X-ray diffraction (113) Area of diffraction peak / peak intensity height (2)

Furthermore, the rare earth-iron-nitrogen based magnet powder of the present invention controls the atmosphere and temperature during nitriding after finishing the reduction diffusion treatment so that the particle surface does not interfere with nitriding due to oxidation or the like. Nitriding is uniformly performed while maintaining a good state. And since it wet-processes after nitriding rather than nitriding after a wet process, the nonmagnetic phase is reducing. Further, since iron oxyhydroxide adheres around the main phase during wet processing and precipitates as α-Fe during nitridation and does not deteriorate the magnetic properties, the α- of the rare earth-iron-nitrogen based magnet powder Fe is reduced, and the ratio is 5% or less. Furthermore, hydrogen dissolved in the magnet powder during the wet treatment is removed by heat treatment thereafter, so that the amount of hydrogen is 0.06% by weight or less. As a result, a rare earth-iron-nitrogen based magnet powder having high saturation magnetization and coercive force and good demagnetization curve squareness is obtained.
That is, the magnetic properties of the rare earth-iron-nitrogen based magnet powder are such that the saturation magnetization is 1.4 T (14 kG), the coercive force is 800 kA / m (10 kOe), and the squareness: Hk is 400 kA / m (5 kOe) or higher Have excellent performance.

  EXAMPLES Hereinafter, although an Example demonstrates this invention, this invention is not limited to these Examples. The obtained nitride powder was measured by the following method.

(1) Magnetic properties The magnetic properties of the alloy powder are rare earths in stearic acid by applying an orientation magnetic field of 1600 A / m according to Japan Bond Magnet Industry Association, Bond Magnet Test Method Guidebook, BM-2002, BM-2005. A sample was prepared by orienting iron-nitrogen based magnet powder, and measurement was performed by magnetizing with a magnetic field of 4000 kA / m. The specific gravity of the magnet alloy powder is 7.67 g / cm 3, and a vibration sample type magnetometer with a maximum magnetic field of 1200 kA / m without demagnetizing correction is used. m), squareness: Hk (kA / m) was measured.
The rare earth-iron-nitrogen magnet has sufficient performance as long as the saturation magnetization is 1.4T (14 kG), the coercive force is 800 kA / m (10 kOe), and the squareness is Hk 400 kA / m (5 kOe) or more. I can say that. Hk represents the squareness of the demagnetization curve, and is the magnitude of the demagnetizing field when the magnetization 4πI takes 90% of the residual magnetization 4πIr in the second quadrant.
(2) Crystal distortion Sm ₂ Fe ₁₇ N ₃ (113) diffraction peak using powder X-ray diffractometer (Cu-Kα, Rotaflex RAD-rVB manufactured by Rigaku Corporation, SUN SP / IPX manufactured by Mac Science Co., Ltd.) The integral width of was obtained. The integral width was calculated as a value obtained by dividing the area of the Sm ₂ Fe ₁₇ N ₃ (113) diffraction peak by the peak intensity height. Since the crystal strain is expressed by 2θ (deg.), Deg. The larger the is, the larger the strain becomes, which is a measure of the amount of strain remaining in the magnet powder after grinding.
The measurement was performed with an optical system using a gonion radius of 185 mm, a divergence slit of 1.0 °, a scattering slit of 1.0 °, a light receiving slit of 0.3 mm, and a curved graphite monometer.
(3) α-Fe ratio The α-Fe ratio was determined using the powder X-ray diffractometer used in the crystal strain measurement. The α-Fe ratio corresponds to the position of the (110) plane of α-Fe (JCPDS No. 6-696) and the (300) plane of Sm ₂ Fe ₁₇ N ₃ after removing the background of the wide-area measurement result. The ratio calculated from the following formula using the peak intensities IFe and ISFN.

Originally, in the X-ray diffraction quantitative analysis, it is necessary to correct the peak intensity ratio between compounds, but the ratio calculation is not performed here. Further, it is assumed that there is no compound other than α-Fe, Sm ₂ Fe ₁₇ (Sm ₂ Fe ₁₇ N ₃ : main phase).
When the ratio of α-Fe deposited on the surface of the main phase of the rare earth-iron-nitrogen based magnet powder increases, it becomes a nucleation site of the main phase of the rare earth-iron-nitrogen based magnet powder, and therefore the coercive force iHc and the squareness Hk. Therefore, the influence on the magnetic properties and squareness can be easily determined by the α-Fe ratio.

(4) Particle shape The particle surface and shape of the rare earth-iron-nitrogen magnet powder before pulverization were observed with a scanning electron microscope (SEM: manufactured by Hitachi, Ltd., S-800).
(5) Particle size distribution From the SEM image, the photograph of the particle size of the primary particle was magnified 1000 times, the longest length of each particle was measured with a ruler with a minimum memory of 1 mm, and the cumulative number percentage Asked.

Example 1
As the magnet raw material powder, 24.3 g of iron powder (Fe purity 99% or more) produced by the atomizing method and having a particle size of 10 to 70 μm accounted for 94% of the total, and a particle size of 0.1 to 10 μm. Weigh 11.4 g of samarium oxide powder (Sm ₂ O ₃ purity 99.5% or higher), which accounts for 96% of the total, and measure metallic calcium particles (Ca purity 99% or higher) 4 or less in particle size (Tyler mesh) 4 .6 g was mixed with a conditioning mixer (MX-201: manufactured by Sinky) for 30 seconds. Samarium oxide powder is 1.27 times the Sm ₂ Fe ₁₇ stoichiometric composition.
This was inserted into a stainless steel reaction vessel, and the inside of the vessel was evacuated with a rotary pump and replaced with Ar gas. Then, the temperature was raised to 900 ° C. while flowing Ar gas, held for 4 hours, and kept at 250 ° C. in the furnace. It was cooled while circulating Ar gas. Next, the temperature of the reaction vessel was lowered to 20 ° C., the inside of the vessel was reduced to −100 kPa, and hydrogen gas was introduced. The hydrogen gas pressure was kept at 20 kPa. Hydrogen absorption began after about 5 minutes. The reaction was performed for about 15 minutes while adjusting the hydrogen gas pressure in the reaction vessel to 10 to 20 kPa. After the treatment, it is cooled to 20 ° C., and the temperature is switched to an ammonia-hydrogen mixed gas having an ammonia partial pressure of 0.33 atm. The temperature is maintained at 450 ° C. for 200 minutes. Hold for minutes and cool.
The taken porous mass reaction product was immediately poured into pure water, and collapsed to obtain a slurry. From this slurry, the Ca (OH) ₂ suspension was separated by decantation. The operation of stirring pure water for 1 minute after pouring and then decanting was repeated 5 times to obtain an alloy powder slurry.
While stirring the obtained alloy powder slurry, dilute acetic acid was added dropwise, and the pH was maintained at pH 5.0 for 7 minutes. The alloy powder was filtered, washed with water several times with ethanol, and vacuum dried at 35 ° C. to obtain 27.0 g of Sm—Fe—N magnet powder. The yield of the obtained powder was (recovered amount / raw material input amount) 67.5% by weight. Subsequently, the obtained Sm—Fe—N magnet powder was classified with a sieve having an aperture of 106 μm. The sieve was 95% by weight of the obtained Sm-Fe-N magnet powder, and the ratio was high.
In the obtained coarse powder, the cumulative percentage of primary particles of 20 μm was 0.2%, and primary particles and sintered grape-like secondary particles were observed. The obtained Sm—Fe—N magnet powder was heat-treated in an electric furnace (turboback: manufactured by Tokyo Vacuum) at 250 ° C. for 30 minutes in a vacuum.
The powder composition was Sm 23.2 wt%, N 3.32 wt%, O 0.15 wt%, H 0.042 wt%, and the balance Fe.
This alloy powder was finely pulverized in ethanol using a vibration mill (multi-mill: manufactured by Narumi Giken) in ethanol at a SUJ2 ball of 5/32 inches and a vibration frequency of 30 Hz for 120 minutes and then vacuum dried at room temperature.
The magnetic properties of the obtained magnet powder and the magnetic properties of the alloy powder were applied with an orientation magnetic field of 1600 A / m in accordance with Japan Bond Magnet Industry Association, Bond Magnet Test Method Guidebook, BM-2002, BM-2005. A sample was prepared by orienting rare earth-iron-nitrogen magnet powder in stearic acid, and magnetized with a magnetic field of 4000 kA / m. The specific gravity of the magnet alloy powder was 7.67 g / cm ^3, and a saturation sample: 4πIm (T) and coercive force: iHc (kA) using a vibrating sample magnetometer with a maximum magnetic field of 1200 kA / m without correcting the demagnetizing field. / M), squareness: Hk (kA / m) was measured.
The X-ray density of the powder calculated from the analytical composition and the lattice constant of the Th ₂ Zn ₁₇ type crystal structure was 7.67 g / cm ³ , and the saturation magnetic flux density 4πIm was converted with this value. iHc is the coercive force. Hk represents the squareness of the demagnetization curve, and is the magnitude of the demagnetizing field when the magnetization 4πI takes 90% of the residual magnetization 4πIr in the second quadrant. The results are shown in Tables 2 and 3.
4πIm 1.41T, iHc 996 kA / m, Hk 528 kA / m, and high characteristics were obtained. Crystal strain (integral width) is 0.04 deg. The α-Fe ratio was 0.8%.

(Example 2)
The reducing diffusion temperature under the conditions of Example 1 was changed to 1180 ° C., and the other conditions were reduced diffusion, hydrogen treatment, nitriding treatment, and wet treatment as in Example 1, and 27.2 g of Sm—Fe—N coarse powder. Got. The yield of the obtained powder was (recovered amount / raw material input amount) 68.0% by weight. The obtained Sm—Fe—N crude powder was classified with a sieve having an opening of 106 μm. The sieve was 96% by weight of the obtained Sm-Fe-N magnet powder, and the ratio was high.
In the obtained powder, the cumulative percentage of primary particles of 20 μm was 9.7%, and primary particles and sintered grape-like secondary particles were observed. The obtained Sm—Fe—N magnet powder was heat-treated in vacuum at 250 ° C. for 30 minutes.
The powder composition was Sm 23.5 wt%, N 3.35 wt%, O 0.16 wt%, H 0.031 wt%, and the balance Fe.
In the same manner as in Example 1, the obtained Sm—Fe—N magnet powder was sampled after being finely pulverized, and magnetic properties, crystal distortion (integral width), and α-Fe ratio were obtained. The results are shown in Tables 2 and 3. It was 4πIm 1.41T, iHc 1000 kA / m, Hk 558 kA / m, and high characteristics were obtained. Crystal strain (integral width) is 0.18 deg. The α-Fe ratio was 5.1%.

(Example 3)
The reduction diffusion temperature under the conditions of Example 1 was changed to 1050 ° C., the nitridation was changed to 350 ° C., 300 minutes, and the ammonia partial pressure was changed to 0.2 atm. Nitriding treatment and wet treatment were performed to obtain 26.8 g of Sm—Fe—N crude powder. The yield of the obtained powder was (recovered amount / raw material input amount) 67.0% by weight. Got. The obtained Sm—Fe—N crude powder was classified with a sieve having an opening of 106 μm. The sieve was 95% by weight of the obtained Sm-Fe-N magnet powder, and the ratio was high.
In the obtained powder, the cumulative percentage of primary particles of 20 μm was 3.0%, and primary particles and sintered grape-like secondary particles were observed. The obtained Sm—Fe—N magnet powder was heat-treated in vacuum at 250 ° C. for 30 minutes.
The powder composition was Sm 23.3% by weight, N 3.39% by weight, O 0.14% by weight, H 0.045% by weight and the balance Fe.
In the same manner as in Example 1, the sample was pulverized and then sampled to determine the magnetic properties, crystal distortion (integral width), and α-Fe ratio. The results are shown in Tables 2 and 3. 4πIm 1.45T, iHc 990 kA / m, Hk 547 kA / m, and high characteristics were obtained. Crystal strain (integral width) is 0.09 deg. The α-Fe ratio was 0.9%.

Example 4
The reduction diffusion temperature under the conditions of Example 1 was changed to 1050 ° C., nitridation was changed to 500 ° C., 100 minutes, and the partial pressure of ammonia was changed to 0.6 atm. Processing and wet processing were performed to obtain 27.0 g of Sm—Fe—N crude powder. The yield of the obtained powder was (recovered amount / raw material input amount) 67.5% by weight. The obtained Sm—Fe—N crude powder was classified with a sieve having an opening of 106 μm. The sieve was 96% by weight of the obtained Sm-Fe-N magnet powder, and the ratio was high.
In the obtained powder, the cumulative percentage of primary particles of 20 μm was 4.0%, and primary particles and sintered grape-like secondary particles were observed. The obtained Sm—Fe—N magnet powder was heat-treated in vacuum at 250 ° C. for 30 minutes.
The powder composition was Sm 23.3 wt%, N 3.35 wt%, O 0.14 wt%, H 0.035 wt%, balance Fe.
In the same manner as in Example 1, the sample was pulverized and then sampled to determine the magnetic properties, crystal distortion (integral width), and α-Fe ratio. The results are shown in Tables 2 and 3. 4πIm 1.44T, iHc 982 kA / m, Hk 502 kA / m, and high characteristics were obtained. Crystal strain (integral width) is 0.08 deg. The α-Fe ratio was 0.7%.

(Example 5)
The reduction diffusion temperature under the conditions of Example 1 was reduced to 1050 ° C., followed by reduction diffusion, and then the temperature of the reaction vessel was lowered to 250 ° C. and hydrogen gas was introduced. Hydrogen treatment was performed at the same hydrogen gas pressure as in Example 1. After the treatment, nitriding was performed at 500 ° C. for 100 minutes and the ammonia partial pressure was changed to 0.60 atm. The other conditions were wet treatment in the same manner as in Example 1, and 27.1 g of Sm—Fe—N crude powder was obtained. Got. The yield of the obtained powder was (recovered amount / raw material input amount) 67.5% by weight. Got. The obtained Sm—Fe—N crude powder was classified with a sieve having an opening of 106 μm. The sieve was 96% by weight of the obtained Sm-Fe-N magnet powder, and the ratio was high.
In the obtained powder, the cumulative percentage of primary particles of 20 μm was 4.0%, and primary particles and sintered grape-like secondary particles were observed. The obtained Sm—Fe—N magnet powder was heat-treated in vacuum at 250 ° C. for 30 minutes.
The powder composition was Sm 23.3 wt%, N 3.35 wt%, O 0.18 wt%, H 0.040 wt% and the balance Fe.
In the same manner as in Example 1, the sample was pulverized and then sampled to determine the magnetic properties, crystal distortion (integral width), and α-Fe ratio. The results are shown in Tables 2 and 3. 4πIm 1.42T, iHc 950 kA / m, and Hk 512 kA / m. Crystal strain (integral width) is 0.07 deg. The α-Fe ratio was 0.8%.

(Example 6)
The raw material blending amount was 24.3 g of iron powder, 10.2 g of samarium oxide powder, and 4.2 g of calcium. Samarium oxide powder is 1.15 times the Sm ₂ Fe ₁₇ stoichiometric composition. The reduction diffusion temperature under the conditions of Example 1 was reduced to 1050 ° C., and reduction diffusion was performed. The other conditions were the same as in Example 1 to obtain 27.5 g of Sm—Fe—N coarse powder. The yield of the obtained powder was (recovered amount / raw material input amount) 71.0% by weight. Subsequently, it was classified with a sieve having an aperture of 106 μm. The sieving amount was 95% by weight of the obtained Sm—Fe—N magnet powder, which was a high proportion of the whole powder.
In the obtained powder, the cumulative percentage of primary particles of 20 μm or more was 2.0%, and primary particles and sintered secondary particles were observed. The obtained Sm—Fe—N magnet powder was treated in vacuum at 250 ° C. for 30 minutes.
The powder composition was Sm 23.3 wt%, N 3.4 wt%, O 0.15 wt%, H 0.037 wt%, and the balance Fe.
In the same manner as in Example 1, the sample was pulverized and then sampled to determine the magnetic properties, crystal distortion (integral width), and α-Fe ratio. The results are shown in Table 2. 4πIm 1.40T, iHc 1020 kA / m, Hk 558 kA / m, and high characteristics were obtained. Crystal strain (integral width) is 0.10 deg. The α-Fe ratio was 1.0%.

(Example 7)
The raw material blending amount was 24.3 g of iron powder, 12.5 g of samarium oxide powder, and 5.1 g of calcium. Samarium oxide powder is 1.40 times the Sm2Fe17 stoichiometric composition. The treatment after mixing was performed in the same manner as in Example 3 to obtain 26.8 g of Sm—Fe—N coarse powder. The yield of the obtained powder was (recovered amount / raw material input amount) 64.0% by weight. Subsequently, it was classified with a sieve having an aperture of 106 μm. The under-sieving amount was 96% by weight of the obtained Sm—Fe—N magnet powder, which was a high ratio to the whole powder.
In the obtained powder, the cumulative percentage of primary particles of 20 μm or more was 4.0%, and primary particles and sintered secondary particles were observed. The obtained Sm—Fe—N magnet powder was treated in vacuum at 250 ° C. for 30 minutes.
The powder composition was Sm 23.3 wt%, N 3.5 wt%, O 0.17 wt%, H 0.035 wt% and the balance Fe.
In the same manner as in Example 1, the sample was pulverized and then sampled to determine the magnetic properties, crystal distortion (integral width), and α-Fe ratio. The results are shown in Table 2. It was 4πIm 1.42T, iHc 1035 kA / m, Hk 555 kA / m, and high characteristics were obtained. Crystal strain (integral width) is 0.07 deg. The α-Fe ratio was 0.7%.

(Comparative Example 1)
In Example 1, wet treatment was performed after reduction diffusion and nitridation, but in Comparative Example 1, nitridation was performed after hydrogen treatment and then wet treatment after reduction diffusion. 27.0 g of Sm—Fe—N crude powder was obtained at a reduction diffusion temperature of 1100 ° C., nitridation at 450 ° C. for 200 minutes, and an ammonia partial pressure of 0.33 atm. The yield of the obtained powder was (recovered amount / raw material input amount) 67.5% by weight. No dehydrogenation treatment was performed after nitriding. The obtained Sm—Fe—N crude powder was classified with a sieve having an opening of 106 μm. The sieve was 92% by weight of the obtained Sm—Fe—N magnet powder, and the ratio was high.
In the obtained powder, the cumulative percentage of primary particles of 20 μm was 3.0%, and primary particles and sintered grape-like secondary particles were observed.
The powder composition was Sm 23.9 wt%, N 3.31 wt%, O 0.14 wt%, H 0.028 wt%, and the balance Fe.
In the same manner as in Example 1, the sample was pulverized and then sampled to determine the magnetic properties, crystal distortion (integral width), and α-Fe ratio. The results are shown in Tables 2 and 3. 4πIm 1.32T, iHc 700 kA / m, Hk 360 kA / m, and magnetic properties were low. Crystal strain (integral width) is 0.07 deg. The α-Fe ratio was 6%.

(Comparative Example 2)
The reduction diffusion temperature is 1100 ° C., nitridation is 450 ° C., 200 minutes, and the ammonia partial pressure is 0.33 atm. Other than that, the reduction diffusion, nitriding treatment, and wet treatment are performed under the same conditions as in Example 1, and Sm—Fe—N 26.9 g of coarse powder was obtained. The yield of the obtained powder was (recovered amount / raw material input amount) 67.3% by weight. No hydrogen treatment was performed after the reduction diffusion. The obtained Sm—Fe—N crude powder was classified with a sieve having an opening of 106 μm. The sieve was 68% by weight of the obtained Sm—Fe—N magnet powder, and the ratio was low.
In the obtained powder, the cumulative percentage of primary particles of 20 μm was 5.0%, and primary particles and sintered grape-like secondary particles were observed. The obtained Sm—Fe—N magnet powder was heat-treated in vacuum at 250 ° C. for 30 minutes.
The powder composition was Sm 23.3 wt%, N 3.32 wt%, O 0.14 wt%, H 0.050 wt% and the balance Fe.
In the same manner as in Example 1, the sample was pulverized and then sampled to determine the magnetic properties, crystal distortion (integral width), and α-Fe ratio. The results are shown in Tables 2 and 3. They were 4πIm 1.42T, iHc 930 kA / m, and Hk 436 kA / m, and the magnetic properties were low. Crystal strain (integral width) is 0.08 deg. The α-Fe ratio was 0.8%.

(Comparative Example 3)
The reduction diffusion temperature is 1100 ° C., the nitridation is 450 ° C., 200 minutes, and the ammonia partial pressure is 0.33 atm. Other than that, the reduction diffusion, nitriding treatment, and wet treatment are performed, and the heat treatment is performed after the wet treatment. 27.0 g of Sm—Fe—N crude powder was obtained without performing the above step. The yield of the obtained powder was (recovered amount / raw material input amount) 67.5% by weight. The obtained Sm—Fe—N crude powder was classified with a sieve having an opening of 106 μm. The sieve was 95% by weight of the obtained Sm-Fe-N magnet powder, and the ratio was high.
The cumulative percentage of primary particles 20 μm in the obtained powder was 4.0%, and primary particles and sintered grape-like secondary particles were observed.
The powder composition was Sm 23.4% by weight, N 3.38% by weight, O 0.16% by weight, H 0.078% by weight and the balance Fe.
In the same manner as in Example 1, the sample was pulverized and then sampled to determine the magnetic properties, crystal distortion (integral width), and α-Fe ratio. The results are shown in Tables 2 and 3. 4πIm 1.42T, iHc 900 kA / m, Hk 430 kA / m, and the magnetic properties were low. Crystal strain (integral width) is 0.17 deg. The α-Fe ratio was 5%.

(Comparative Example 4)
Among the conditions of Example 1, the reduction diffusion temperature was changed to 850 ° C., nitridation was 450 ° C., 200 minutes, and the ammonia partial pressure was changed to 0.33 atmospheres. The treatment, nitriding treatment, and wet treatment were performed to obtain 27.2 g of Sm—Fe—N coarse powder. The yield of the obtained powder was (recovered amount / raw material input amount) 68.0% by weight. Got. The obtained Sm—Fe—N crude powder was classified with a sieve having an opening of 106 μm. The sieve was 95% by weight of the obtained Sm-Fe-N magnet powder, and the ratio was high.
The obtained powder had no primary particles of 20 μm or more, and primary particles and sintered grape-like secondary particles were observed. The obtained Sm—Fe—N magnet powder was heat-treated in vacuum at 250 ° C. for 30 minutes.
This powder composition was Sm 23.2 wt%, N 3.39 wt%, O 0.14 wt%, H 0.052 wt%, and the balance Fe.
In the same manner as in Example 1, the sample was pulverized and then sampled to determine the magnetic properties, crystal distortion (integral width), and α-Fe ratio. The results are shown in Tables 2 and 3. 4πIm 1.41T, iHc 860 kA / m, and Hk 400 kA / m, which were low. Crystal strain (integral width) is 0.04 deg. The α-Fe ratio was 11%.

(Comparative Example 5)
Among the conditions of Example 1, the reduction diffusion temperature was changed to 1190 ° C., the nitridation was changed to 450 ° C., 200 minutes, and the ammonia partial pressure was 0.33 atm. Treatment, nitriding treatment, and wet treatment were performed to obtain 27.3 g of Sm—Fe—N coarse powder. The yield of the obtained powder was 68.3% by weight (recovered amount / raw material input amount). The obtained Sm—Fe—N crude powder was classified with a sieve having an opening of 106 μm. The sieve was 94% by weight of the obtained Sm—Fe—N magnet powder, and the ratio was high.
In the obtained powder, the cumulative percentage of primary particles of 20 μm was 47%, and primary particles and secondary particles having a smooth surface after sintering were observed. The obtained Sm—Fe—N magnet powder was heat-treated in vacuum at 250 ° C. for 30 minutes.
The powder composition was Sm 23.4 wt%, N 3.31 wt%, O 0.17 wt%, H 0.040 wt%, and the balance Fe.
In the same manner as in Example 1, the sample was pulverized and then sampled to determine the magnetic properties, crystal distortion (integral width), and α-Fe ratio. The results are shown in Tables 2 and 3. 4πIm 1.40T, iHc 875 kA / m, and Hk 410 kA / m. Crystal strain (integral width) is 0.22 deg. The α-Fe ratio was 1.2%.

(Comparative Example 6)
Among the conditions of Example 1, the reduction diffusion temperature was changed to 1050 ° C., the nitridation was changed to 450 ° C., 200 minutes, and the ammonia partial pressure was changed to 0.1 atm. Treatment, nitriding treatment, and wet treatment were performed to obtain 26.9 g of Sm—Fe—N coarse powder. The yield of the obtained powder was (recovered amount / raw material input amount) 67.3% by weight. The obtained Sm—Fe—N crude powder was classified with a sieve having an opening of 106 μm. The sieve was 96% by weight of the obtained Sm-Fe-N magnet powder, and the ratio was high.
In the obtained powder, the cumulative percentage of primary particles of 20 μm was 3%, and primary particles and sintered grape-like secondary particles were observed. The obtained Sm—Fe—N magnet powder was heat-treated in vacuum at 250 ° C. for 30 minutes.
The powder composition was Sm 23.3 wt%, N 3.19 wt%, O 0.16 wt%, H 0.033 wt% and the balance Fe.
In the same manner as in Example 1, the sample was pulverized and then sampled to determine the magnetic properties, crystal distortion (integral width), and α-Fe ratio. The results are shown in Tables 2 and 3. 4πIm 1.35T, iHc 683 kA / m, and Hk 330 kA / m, which were low. Crystal strain (integral width) is 0.08 deg. The α-Fe ratio was 6.1%.

(Comparative Example 7)
Of the conditions of Example 1, the reduction diffusion temperature was changed to 1050 ° C., the nitridation was changed to 450 ° C., 200 minutes, and the ammonia partial pressure was changed to 0.7 atm. Treatment, nitriding treatment, and wet treatment were performed to obtain 26.8 g of Sm—Fe—N coarse powder. The yield of the obtained powder was (recovered amount / raw material input amount) 67.0% by weight. The obtained Sm—Fe—N crude powder was classified with a sieve having an opening of 106 μm. The sieve was 95% by weight of the obtained Sm-Fe-N magnet powder, and the ratio was high.
In the obtained powder, the cumulative percentage of primary particles of 20 μm was 2%, and primary particles and sintered grape-like secondary particles were observed. The obtained Sm—Fe—N magnet powder was heat-treated in vacuum at 250 ° C. for 30 minutes.
The powder composition was Sm 23.3 wt%, N 3.41 wt%, O 0.17 wt%, H 0.042 wt% and the balance Fe.
In the same manner as in Example 1, the sample was pulverized and then sampled to determine the magnetic properties, crystal distortion (integral width), and α-Fe ratio. The results are shown in Tables 2 and 3. 4πIm 1.37T, iHc 735 kA / m, and Hk 355 kA / m, which were low. Crystal strain (integral width) is 0.07 deg. The α-Fe ratio was 6.2%.

(Comparative Example 8)
Among the conditions of Example 1, the reduction diffusion temperature was changed to 1050 ° C., nitridation was changed to 340 ° C., 300 minutes, and the ammonia partial pressure was 0.6 atm. Treatment, nitriding treatment, and wet treatment were performed to obtain 26.8 g of Sm—Fe—N coarse powder. The yield of the obtained powder was (recovered amount / raw material input amount) 67.0% by weight. The obtained Sm—Fe—N crude powder was classified with a sieve having an opening of 106 μm. The sieve was 95% by weight of the obtained Sm-Fe-N magnet powder, and the ratio was high.
In the obtained powder, the cumulative percentage of primary particles of 20 μm was 2%, and primary particles and sintered grape-like secondary particles were observed. The obtained Sm—Fe—N magnet powder was heat-treated in vacuum at 250 ° C. for 30 minutes.
The powder composition was Sm 23.2 wt%, N 3.35 wt%, O 0.16 wt%, H 0.050 wt% and the balance Fe.
In the same manner as in Example 1, the sample was pulverized and then sampled to determine the magnetic properties, crystal distortion (integral width), and α-Fe ratio. The results are shown in Tables 2 and 3. 4πIm 1.38T, iHc 800 kA / m, and Hk 430 kA / m, which were low. Crystal strain (integral width) is 0.08 deg. The α-Fe ratio was 10.3%.

(Comparative Example 9)
Among the conditions of Example 1, the reduction diffusion temperature was changed to 1050 ° C., the nitridation was changed to 520 ° C., 100 minutes, and the ammonia partial pressure was 0.33 atmospheres. Treatment, nitriding treatment, and wet treatment were performed to obtain 26.8 g of Sm—Fe—N coarse powder. The yield of the obtained powder was (recovered amount / raw material input amount) 67.0% by weight. The obtained Sm—Fe—N crude powder was classified with a sieve having an opening of 106 μm. The sieve was 96% by weight of the obtained Sm-Fe-N magnet powder, and the ratio was high.
In the obtained powder, the cumulative percentage of primary particles of 20 μm was 3%, and primary particles and sintered grape-like secondary particles were observed. The obtained Sm—Fe—N magnet powder was heat-treated in vacuum at 250 ° C. for 30 minutes.
The powder composition was Sm 23.3 wt%, N 3.00 wt%, O 0.16 wt%, H 0.046 wt%, and the balance Fe.
In the same manner as in Example 1, the sample was pulverized and then sampled to determine the magnetic properties, crystal distortion (integral width), and α-Fe ratio. The results are shown in Tables 2 and 3. 4πIm 1.39T, iHc 750 kA / m, and Hk 435 kA / m, which were low. Crystal strain (integral width) is 0.09 deg. The α-Fe ratio was 9.2%.

(Comparative Example 10)
Among the conditions of Example 1, the reduction diffusion temperature was changed to 1050 ° C., nitridation was 450 ° C., 300 minutes, and the ammonia partial pressure was changed to 0.33 atm. Hydrogen treatment, nitriding treatment, and wet treatment were performed to obtain 27.0 g of Sm—Fe—N crude powder. The yield of the obtained powder was (recovered amount / raw material input amount) 67.5% by weight. The heat treatment after the wet treatment was not performed. The obtained Sm—Fe—N crude powder was classified with a sieve having an opening of 106 μm. The sieve was 96% by weight of the obtained Sm-Fe-N magnet powder, and the ratio was high.
In the obtained powder, the cumulative percentage of primary particles of 20 μm was 3.0%, and primary particles and sintered grape-like secondary particles were observed. No dehydrogenation treatment was performed on the Sm—Fe—N magnet powder obtained after the wet treatment.
The powder composition was Sm 23.3 wt%, N 3.35 wt%, O 0.14 wt%, H 0.090 wt%, and the balance Fe.
In the same manner as in Example 1, the sample was pulverized and then sampled to determine the magnetic properties, crystal distortion (integral width), and α-Fe ratio. The results are shown in Tables 2 and 3. 4πIm 1.42T, iHc 640 kA / m, and Hk 352 kA / m, which were low. Crystal strain (integral width) is 0.09 deg. The α-Fe ratio was 0.9%.

(Comparative Example 11)
Among the conditions of Example 1, the reduction diffusion temperature was changed to 1050 ° C., nitridation was 450 ° C., 300 minutes, and the ammonia partial pressure was changed to 0.33 atm. Hydrogen treatment, nitriding treatment, and wet treatment were performed to obtain 27.1 g of Sm—Fe—N crude powder. The yield of the obtained powder was (recovered amount / raw material input amount) 67.8% by weight. The obtained Sm—Fe—N crude powder was classified with a sieve having an opening of 106 μm. The sieve was 96% by weight of the obtained Sm-Fe-N magnet powder, and the ratio was high.
In the obtained powder, the cumulative percentage of primary particles of 20 μm was 4.0%, and primary particles and sintered grape-like secondary particles were observed. The obtained Sm—Fe—N magnet powder was heat-treated in vacuum at 100 ° C. for 30 minutes.
The powder composition was Sm 23.2 wt%, N 3.35 wt%, O 0.14 wt%, H 0.075 wt%, balance Fe.
In the same manner as in Example 1, the sample was pulverized and then sampled to determine the magnetic properties, crystal distortion (integral width), and α-Fe ratio. The results are shown in Tables 2 and 3. 4πIm 1.42T, iHc 700 kA / m, and Hk 400 kA / m. Crystal strain (integral width) is 0.09 deg. The α-Fe ratio was 0.9%.

(Comparative Example 12)
Among the conditions of Example 1, the reduction diffusion temperature was changed to 1050 ° C., nitridation was 450 ° C., 300 minutes, and the ammonia partial pressure was changed to 0.33 atm. Hydrogen treatment, nitriding treatment, and wet treatment were performed to obtain 27.0 g of Sm—Fe—N crude powder. The yield of the obtained powder was (recovered amount / raw material input amount) 67.5% by weight. The obtained Sm—Fe—N crude powder was classified with a sieve having an opening of 106 μm. The sieve was 96% by weight of the obtained Sm-Fe-N magnet powder, and the ratio was high.
In the obtained powder, the cumulative percentage of primary particles of 20 μm was 3.0%, and primary particles and sintered grape-like secondary particles were observed. The obtained Sm—Fe—N magnet powder was treated in vacuum at 520 ° C. for 30 minutes.
The powder composition was Sm 23.3 wt%, N 3.35 wt%, O 0.14 wt%, H 0.028 wt%, balance Fe.
In the same manner as in Example 1, the sample was pulverized and then sampled to determine the magnetic properties, crystal distortion (integral width), and α-Fe ratio. The results are shown in Tables 2 and 3. 4πIm 1.45T, iHc 300 kA / m, and Hk 210 kA / m, which were low. Crystal strain (integral width) is 0.09 deg. The α-Fe ratio was 15.0%.

(Comparative Example 13)
The reduction diffusion temperature under the conditions of Example 1 was 1050 ° C., and reduction diffusion was performed. Thereafter, the temperature of the reaction vessel was lowered to 350 ° C. and hydrogen gas was introduced. Hydrogen treatment was performed at the same hydrogen gas pressure as in Example 1. After the treatment, nitriding is performed at 450 ° C. for 300 minutes, and the ammonia partial pressure is 0.33 atm. The other conditions are wet treatment in the same manner as in Example 1, and 26.9 g of Sm—Fe—N crude powder is obtained. Obtained. The yield of the obtained powder was (recovered amount / raw material input amount) 67.3% by weight. The obtained Sm—Fe—N crude powder was classified with a sieve having an opening of 106 μm. The sieve was 96% by weight of the obtained Sm-Fe-N magnet powder, and the ratio was high.
In the obtained powder, the cumulative percentage of primary particles of 20 μm was 3.0%, and primary particles and sintered grape-like secondary particles were observed. The obtained Sm—Fe—N magnet powder was treated in vacuum at 250 ° C. for 30 minutes.
This powder composition was Sm 23.4% by weight, N 3.36% by weight, O 0.15% by weight, H 0.045% by weight and the balance Fe.
In the same manner as in Example 1, the sample was pulverized and then sampled to determine the magnetic properties, crystal distortion (integral width), and α-Fe ratio. The results are shown in Tables 2 and 3. 4πIm 1.39T, iHc 690 kA / m, and Hk 410 kA / m, which were low. Crystal strain (integral width) is 0.09 deg. The α-Fe ratio was 10.5%.

(Comparative Example 14)
The raw material blending amount was 24.3 g of iron powder, 9.4 g of samarium oxide powder, and 3.8 g of calcium. Samarium oxide powder is 1.05 times the Sm2Fe17 stoichiometric composition. The processing after mixing was performed in the same manner as in Example 3 to obtain 28.9 g of Sm—Fe—N coarse powder. The yield of the obtained powder was (recovered amount / raw material input amount) 77.1% by weight. Subsequently, it was classified with a sieve having an aperture of 106 μm. The sieve was 72.3% by weight of the obtained Sm—Fe—N magnet powder, which was a low ratio to the whole powder.
The obtained powder had a cumulative percentage of primary particles of 20 μm or more of 7.0%, and primary particles and sintered secondary particles were observed. The obtained Sm—Fe—N magnet powder was treated in vacuum at 250 ° C. for 30 minutes.
The powder composition was Sm 23.3 wt%, N 3.4 wt%, O 0.17 wt%, H 0.036 wt% and the balance Fe.
In the same manner as in Example 1, the sample was pulverized and then sampled to determine the magnetic properties, crystal distortion (integral width), and α-Fe ratio. The results are shown in Table 2. It was 4πIm 1.37T, iHc 700 kA / m, Hk 370 kA / m, and high characteristics were obtained. Crystal strain (integral width) is 0.05 deg. The α-Fe ratio was 7.0%.

(Comparative Example 15)
The raw material blending amount was 24.3 g of iron powder, 14.3 g of samarium oxide powder, and 5.8 g of calcium. Samarium oxide powder is 1.60 times the Sm ₂ Fe ₁₇ stoichiometric composition. The treatment after mixing was performed in the same manner as in Example 1 to obtain 25.2 g of Sm—Fe—N coarse powder. The yield of the powder (recovered amount / raw material input amount) was 56.7% by weight and was low. Subsequently, the powder was classified with a sieve having an opening of 106 μm. The sieve was 96% by weight of the obtained Sm-Fe-N magnet powder.
In the obtained powder, the cumulative percentage of primary particles of 20 μm or more was 3.0%, and primary particles and sintered secondary particles were observed. The obtained Sm—Fe—N magnet powder was treated in vacuum at 250 ° C. for 30 minutes.
The powder composition was Sm 23.3 wt%, N 3.5 wt%, O 0.15 wt%, H 0.034 wt%, and the balance Fe.
In the same manner as in Example 1, the sample was pulverized and then sampled to determine the magnetic properties, crystal distortion (integral width), and α-Fe ratio. The results are shown in Table 2. It was 4πIm 1.37T, iHc 1020 kA / m, Hk 550 kA / m, and 4πIm was low. Crystal strain (integral width) is 0.07 deg. The α-Fe ratio was 0.8%.

"Evaluation"
As a result of the above, according to the examples, a rare earth-iron (-cobalt) master alloy manufactured by a reduction diffusion method using a specific raw material powder, nitrided under specific conditions, and dehydrogenated after wet processing It can be seen that all of the iron (-cobalt) -nitrogen based magnet powders have preferable magnetic properties (saturation magnetization, coercive force, squareness).
On the other hand, since Comparative Example 1 was wet-treated before nitriding, the nitrogen distribution in the alloy became non-uniform and the squareness was reduced. In addition, about 8% by weight of particles on the sieve having an aperture of 106 μm or more that deteriorate the magnetic properties was present. Further, the amount of Sm and the α-Fe ratio deviated from the preferred range, Sm was 23.9% by weight, the nonmagnetic phase was excessive, and 4πIm was reduced. In addition, iron oxyhydroxide adhering to the surface of the magnet powder due to nitriding after the wet treatment is deposited on the surface of the magnet by nitriding, and the α-Fe ratio is 6%, and iHc and Hk are reduced.
In Comparative Example 2, unlike in Example 1, the reduction diffusion reaction product was not subjected to hydrogen treatment and was nitrided with coarse particles, so that the nitrogen distribution in the alloy became non-uniform and the squareness was reduced. In addition, about 30% by weight of particles on the sieve having an aperture of 106 μm or more that deteriorate the magnetic properties was present. In Comparative Example 3, since the dehydrogenation treatment was not performed after the wet treatment, the magnetic characteristics were deteriorated.
In Comparative Examples 4 and 5, the reduction diffusion temperature deviated from the preferred range, and when the reduction diffusion temperature was 850 ° C., the reduction time was insufficient, and therefore the effect of undiffused Fe in the Sm ₂ Fe ₁₇ alloy was not achieved. The Fe ratio was 11%, and the number of particles (single crystal) with a smooth particle surface increased at 1190 ° C., so that the strain applied to the particle surface during pulverization was 0.22 deg. IHc and Hk are reduced.
In Comparative Examples 6 and 7, the ammonia partial pressure in the nitriding atmosphere deviates from the preferred range, and in Comparative Examples 8 and 9, the nitriding temperature deviates from the preferred range, but the reduction diffusion temperature is within the preferred range. Even so, α-Fe exceeds 5% due to insufficient nitridation, pernitridation, and decomposition of the main phase, and 4πIm, iHc, and Hk are reduced.
In Comparative Example 10, finely pulverized without removing hydrogen dissolved in the magnet powder after the wet treatment, and in Comparative Examples 11 and 12, the dehydrogenation temperature and the amount of hydrogen deviated from the preferred ranges. IHc and Hk are reduced.
In Comparative Example 13, the hydrogen treatment temperature deviated from the preferred range, and α-Fe exceeded 10% due to decomposition of the main phase, and 4πIm, iHc, and Hk were reduced. Since the reaction product is active at a hydrogen treatment temperature of 350 ° C., when nitriding is performed thereafter, the alloy is abruptly nitrided, and the Sm—Fe intermetallic compound having a Th ₂ Zn ₁₇ type crystal structure becomes Fe. It is estimated that it decomposed into a rich phase and SmN.
In Comparative Examples 14 and 15, the blending amount of samarium oxide deviates from the preferable range, and in Comparative Example 14, the diffusion of the rare earth element is not uniform with respect to the iron powder. Further, in order to perform uniform nitridation, it is necessary to hydrogen decay the reduced product before nitriding, but since the Sm-rich phase is reduced, the particles are easily sintered and the hydrogen decay property of the reduced product is deteriorated, and α-Fe is 7%. And 4πIm, iHc, and Hk are reduced.
In Comparative Example 15, there is no problem with the amount of α-Fe and the integral width, but since the amount of samarium oxide is large, the Sm-rich phase other than the main phase increases in the magnet powder, and the SmFeN powder after the Sm-rich phase is removed The yield was greatly reduced. In terms of magnetic properties, the Sm-rich phase could not be completely removed, and 4πIm was lowered.

It is a graph which shows the reductive diffusion process temperature dependence with respect to the particle size distribution (cumulative number percentage) before the grinding | pulverization of rare earth-iron- nitrogen system magnet powder. It is a photograph which shows the SEM image of the rare earth-iron- nitrogen-type magnet powder before the grinding | pulverization obtained by performing a reduction | restoration diffusion process by heat-treatment temperature 1050 degreeC and 1190 degreeC, and nitriding after that. It is a graph which shows the relationship between heating temperature, iHc, and Hk when the magnet coarse powder after a wet process is heat-processed in vacuum for 30 minutes. It is a graph which shows the relationship between the amount of hydrogen of magnet powder after heat-processing the magnet coarse powder after wet processing at 250 degreeC in vacuum, and iHc and Hk.

Claims (12)

  A step of mixing a rare earth oxide powder, an iron powder, and at least one reducing agent powder selected from an alkali metal, an alkaline earth metal or a hydride thereof at a predetermined ratio, and the resulting mixture is treated with an inert gas; A step of heating at 900 to 1180 ° C. in an atmosphere, and subsequently cooling the obtained reaction product to 500 ° C. or less in an inert gas atmosphere, and after discharging at least a part of the inert gas, hydrogen is contained. A step of supplying a gas and absorbing the hydrogen into the obtained reaction product and causing the reaction product to decay, and then supplying a mixed gas containing ammonia and hydrogen while maintaining the collapsed reaction product at a temperature of 300 ° C. or lower. The step of nitriding the reaction product at 350 to 500 ° C. by heating in this air stream, the step of adding the obtained nitriding product into water and performing the wet processing, and the wet processing It includes a step of heat-treating the magnet coarse powder at 120 to 480 ° C., removing hydrogen that has entered the magnet alloy by wet treatment, and finally pulverizing the obtained magnet coarse powder. A method for producing uniformly nitrided rare earth-iron-nitrogen based magnet powder.   The method for producing a rare earth-iron-nitrogen based magnet powder according to claim 1, wherein the cooling temperature of the reaction product is 250 ° C. or less.   2. The process for producing a rare earth-iron-nitrogen based magnet powder according to claim 1, wherein the wet magnet crude powder is heat-treated in a vacuum or in an inert gas atmosphere. Rare earth according to the mixing amount of the rare earth oxide powder, any one of the preceding claims, characterized in that a 1.1-fold to 1.4-fold stoichiometric composition of R ₂ Fe ₁₇ - Iron - A method for producing nitrogen-based magnet powder.   The coarse magnet powder has a form of secondary particles in which primary particles are gathered and sintered into a grape shape, and the primary particles have a cumulative percentage of particles having a particle size of 20 μm or more of less than 10%. The method for producing a rare earth-iron-nitrogen based magnet powder according to claim 1.   The method for producing a rare earth-iron-nitrogen based magnet powder according to claim 1, wherein the partial pressure of ammonia in the mixed gas is 0.2 to 0.6 atm.   Rare earth-iron-nitrogen based magnet powder obtained by the method according to claim 1.   The rare earth-iron-nitrogen based magnet powder according to claim 7, wherein the rare earth element is Sm.   The rare earth-iron-nitrogen based magnet powder according to claim 8, wherein the Sm content is 23.2 to 23.6% by weight.   The rare earth-iron-nitrogen based magnet powder according to claim 7, wherein the amount of hydrogen contained in the magnet powder is 0.06% by weight or less. The rare earth-iron-nitrogen based magnet powder according to claim 7, wherein an α-Fe ratio represented by the following general formula (1) is 5% or less.
α-Fe ratio = α-Fe (110) peak intensity / rare earth-Fe-nitrogen (300) peak intensity in X-ray diffraction (1) The integral width represented by the following general formula (2) is 0.2 deg. The rare earth-iron-nitrogen based magnet powder according to claim 7 or 8, wherein:
Integration width = Sm ₂ Fe ₁₇ N ₃ in X-ray diffraction (113) Area of diffraction peak / peak intensity height (2)

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