JPS59219452A - Permanent magnet material and its production - Google Patents

Abstract

PURPOSE:To produce an inexpensive permanent magnet material having an excellent magnetic characteristic by molding ultrafine alloy powder consisting of specifically composed light rare earth elements, additive elements such as B, Ti, etc. and Fe, etc. and sintering the molding in a reducing or non-oxidative atmosphere. CONSTITUTION:Alloy powder of 0.3-80mum average grain size having the compsn. contg., by atom ratio, 8-30% R (>=1 kind among rare earth elements including Y), 2-28% B, prescribed % of >=1 kind among additive elements M with the total of M below the max. value among the respective elements of the M incorporated therein (prescribed % of M; <=4.5% Ti, <=5.0% Bi, <=12.5% Nb, <=8.5% Cr, <=9.5 W, <=8.5% Al, <=7.0% Ge, <=5.5% Zr, <=5.5% Hf, <=8.0% Ni, <=9.5% V, <=10.5% Ta, <=9.5% Mo, <=8.0% Mn, <=2.5% Sb, <=3.5% Sn) and consists of the balance Fe and impurities unavoidable in production is molded and is sintered at 900-1,200 deg.C in a reducing or non-oxidative atmosphere, by which the FeBRM permanent magnet material is obtd.

Description

DETAILED DESCRIPTION OF THE INVENTION The present invention relates to a permanent magnet material based on FeBR system and a method for manufacturing the same.

Conventionally, magnets such as alnico and ferrite have been mainstream as one of the essential materials for permanent magnets, but with the recent development of electronics, the demand for smaller and lighter magnets has rapidly increased.

As a permanent magnet material that satisfies such requirements, rare earth (R) conort magnets having high residual magnetic flux density and high coercive force have been developed and put into practical use. In the following, in the present invention, R
indicates rare earth metal.

However, the delivered earth/held magnet is Sm, Y-
＼゛) 1R Flower - Because it contains a large amount of expensive rare earths such as Class V and expensive copal, the product price is very high, and this has become a major obstacle to replacing Alnico and Ferrai i.

B. In order for earth magnets to be used in a wider range of fields at low cost and in large quantities, they must be made mainly of light rare earths such as Nd and Pr, which do not contain expensive cobalt and are quantitatively abundant among rare earth elements. Various attempts have been made to obtain such a permanent magnet.

For example, Clark (A, E, C1ark) fabricated TbFe2 amorphous by sputtering and 4.
It has an energy product of 28.5 MGOe at 2° and 30
When heat treated at 0 to 500°C, coercive force Hc =
3.4KOe, maximum energy product (BH) mtax=
7HGOe. Similar research is 5I
It was also carried out for IFe2, and 9.28 GOe at 77°
It has been reported that

In addition, Kuhn (N, C, Koon) etc. are 0.9 (Fe
We found that when a ribbon of B)-0,05Tb-0,05La was prepared by an ultra-quenching method and then annealed to 875°", the lc exceeded 9 KOe. However, in this case, the square shape of the magnetization curve As a matter of course, the orientation is poor, and (BH) + oax is low (N, C, Koon
et al., Appl, Phys, Lett.

3s(xo), [381,840-842 FL, T
EEE Transactionon Magne
tics, Vol. MAG-18, No. 8. ! 982
．． Pages 1448-1450→.

Furthermore, Croat et al. (J, J., Croat) and Kabacoff et al. (L, 2003) fabricated ribbons using an ultra-quenching method for PrFe and NdFe compositions, and reported a value close to 8 KOe at room temperature (L).
, Kabacoff et al., J.

jlpp I. Phys, 53(3)1!381.2
pp. 255-2257, J.J.

Croat IEEE Vol. I8 No. 6144
2-1447).

Bulk permanent magnet bodies having arbitrary shapes and dimensions cannot be obtained from these FeBR-based ultra-quenched ribbons or RFe-based sputtered thin films, and it is difficult to use them as practical permanent magnet materials.

The magnetization curves of FeBR ribbons reported so far have poor squareness, and cannot be considered as practical permanent magnets that can compete with conventional magnets. Moreover, the spunter thin film and the ultra-quenched ribbon described in -1- are both essentially isotropic, and it is practically impossible to obtain a practical permanent magnet with magnetic anisotropy from them.

As described above, all of the methods conventionally attempted to obtain permanent magnets of rare earth iron alloys were unsuitable for obtaining practical permanent magnet materials.7 The present invention overcomes the difficulties of such conventional methods. As mentioned above, Fe,
In permanent magnet materials using R, a light rare earth element can be used as R, and conventional hard ferrite I.
The basic object of the present invention is to provide a new permanent magnet material and a method for producing the same, which have magnetic properties as good as or better than those of the present invention, and which do not require the use of scarce resources.

Furthermore, the present invention is based on Fe, which was previously developed and filed by the present inventor.
In a preferred embodiment of the present invention, it is also an object of the present invention to impart even more excellent coercive force to the BR three-element permanent magnet.

That is, according to the present invention, in terms of atomic percentage, 8 to 30% of R (where R is at least one kind of rare earth element including Y), B of 2 to 2H, and one or two of the predetermined two additive elements M. (Here, the specified additive elements M are Ti 4.5% or less, Ni 8.0% or less,
Bi 5.0% or less, ■ 8.5% or less, Nb
12.5% or less, Ta 10.5% or less, C
r”El, 5% or less, Mo 8.5% or less,
W 9.5X or less, Mn 8.0% or less, A
I 9.5% or less, Sb 2.5% or less, G
e7. O% or less, Sn 3.5% or less, Z
r 5.5% or less, and) If 5.5% or less) However, the content of M is less than the atomic percentage of the maximum value of each element of M contained, and the remainder is Fe and impurities unavoidable in manufacturing. (hereinafter referred to as FeBRM composition) and an average particle size of 0.3 to 80 pm, and
A FeBRM permanent magnet material is manufactured by sintering at 00 to 1200°C.

Regarding alloy compositions below, unless otherwise specified, % represents atomic percentage.

The present invention includes at least a primarily magnetically anisotropic/permanent magnetic material.

The present inventor has developed FeR in the production of rare earth iron alloy magnets.
When manufactured by powder metallurgy under certain conditions within the above FeBRM composition range containing B in addition to B, magnetic properties equivalent to or better than conventional alnico, ferrite, and rare earth magnets can be obtained. As a result of detailed research, we have discovered that it can be molded into any shape and practical size.

The following explanation will be based on the case of anisotropy.

That is, by using the manufacturing method of the present invention, this permanent magnet material becomes an industrially useful permanent magnet material that has magnetic properties equivalent to or better than hard ferrite in the FeBRM composition range described above according to the present invention.

Coercive force 1) In order to satisfy 1c IKOe or more, B should be 2z or more, and the residual magnetic flux density of hard ferrite Br should be about 4KG.
In order to achieve the above, B is set to 28% or less. R is coercive force I
In order to satisfy KOe or higher, it is required to be 8% or more, and because it is easily flammable and difficult to handle and manufacture industrially (and is expensive), it is set to 30% or less. Light rare earth is the main component of H (i.e. 50 atoms or more of light rare earth in all R)
L, 11~24XR13~27%B, balance (Fe+M
) is the maximum energy product (OH) max 7MGO
This is a preferable range for achieving a value of e or more.

Most preferably, the main component of H is a light rare earth, and 12 to 2
It has a composition of 0XR 14 to 24% B and the balance (Fe 10M), which enables a maximum energy product (BH) wax of 10 MGOe or more, and (BH) wax reaches a maximum of 33 MGOe or more.

Recently, permanent magnets have been subjected to increasingly harsh environments (for example, strong demagnetizing fields due to thinner magnets, strong reverse magnetic fields applied by coils and other magnets, and high temperature environments due to high-speed equipment and heavy metal loads). In many applications, even higher coercive force is required to stabilize the properties.

By containing one or more of the above specific additive elements M, this FeBRM permanent magnet can provide a higher iHc than the FeBR ternary permanent magnet (see FIG. 4). However, it has also become clear that the addition of these additive elements M causes a gradual decrease in the residual magnetization Br in each aspect. Therefore, the content of the additive element M should be such that at least the residual magnetization Br is equal to or higher than the residual magnetization Br of the conventional /\-doferrite and exhibits a high coercive force.

Next, in order to clarify the effect of each addition of the additive element M, changes in Br were measured by experiments by varying the amount added, and the results are shown in FIGS. 1 to 3. Bi, Mn, other additive elements M (Ti, V.

Nb, Ta, Cr, No, W, AI, Sb
, Ge, Sn, Zr, Hf), as shown in Figures 1 to 3.
It is defined as a range equivalent to or greater than approximately 4 kg. Furthermore, a preferable range is 8.5.8. The division into stages such as 10KG can be clearly read from FIGS. 1 to 3, respectively.

When adding a large amount of Mn and old, iHc decreases, but when Ni
is a ferromagnetic element, so Br does not decrease much (second
(see figure). Therefore, the upper limit of Ni is 8
z, and from the same viewpoint, 4.5z or less is preferable.

Although Mn addition has a greater effect on Br reduction than Ni, it is not drastic. Thus, the upper limit of the angle is preferably 8z from the point of view of IHc, and preferably 3.5z or more from the same point of view.

Regarding Bi, it is virtually impossible to manufacture an alloy in which the vapor pressure is extremely high and exceeds 5% Bi, so it is set at 5z or higher. In the case of alloys containing two or more additive elements, Br 4K
In order to satisfy the condition of G or higher, it is necessary that the amount of addition of each element be less than or equal to the maximum value (t) of the two upper limits of each element added.

As R, it is possible to use a resource-rich type 2 species, and since it does not necessarily require Srs or mainly Sm, the raw material is inexpensive and extremely useful. The rare earth element R used in the permanent magnet of the present invention is Y
It is a rare earth element that includes light rare earths and heavy rare earths, and one or more of them is used. That is, this R includes Nd, Pr, and La.

Ce, Tb+ Dy, Ho, Er, Eu, 5
ffl, Gd, Pm, Tm, Yb.

Lu, and Y are included. As R, a light rare earth element is sufficient, and Nd and Pr are particularly preferable. Further, one type of R is usually sufficient, but in practice, a mixture of two or more types (Mitsuhmetal, didymium, etc.) can be used for reasons such as convenience of availability. Note that R does not have to be a pure rare earth element, and may be one that is produced within an industrially available range and contains unavoidable impurities. S! Q, Y, La,
Ce, Gd, etc. can be used as a mixture with other light rare earths.

As B, pure poron or ferroboron can be used, and materials containing AI, Si, C, etc. as impurities can also be used.

In the permanent magnet material of the present invention, the presence of impurities that are unavoidable during manufacturing can be tolerated. It can also contain C, S, P, Gu, etc. within a predetermined limit, which contributes to convenience in manufacturing and cost reduction. C
may be contained from organic binders, and S, P, Gu, etc. may be contained from raw materials and manufacturing processes.

G 4.0% or less, P 3.5% or less, 52.5
% or less, Cu3.5% or less, but the total of these is practical if it is less than the maximum value of each component.

The manufacturing method of the permanent magnet material according to the present invention is essential for exhibiting high properties.The manufacturing method of the present invention will be explained in detail below.

In general, rare earth metals are chemically very active and easily combine with oxygen in the air and easily react with oxygen to create rare earth oxides. It is necessary to carry out in a non-oxidizing atmosphere.

First, an alloy powder having a predetermined alloy composition is prepared. - For example, raw wood '1 is weighed and blended to a predetermined composition within the above FeBRM composition range, then melted in a high frequency induction furnace or the like to form an ingot, and then crushed. Powder average particle size 0.
Coercive force (iHc) is l KOe in the range of 3 to 80 g, m
This becomes -1-. If the average particle size is smaller than 0.3 pm, oxidation will proceed rapidly and it will be difficult to obtain the desired alloy, which is not preferable for the stable production of high-performance permanent magnet materials of the present invention. Further, if the powder particle size exceeds 80 gm, the coercive force iHc becomes less than 1 KOe, which is not preferable in terms of maintaining the performance of the magnetic material. In the powder having a particle size within the above range, two types of similar powders having different compositions within the composition range of the present invention may be mixed and used in order to adjust the composition or promote densification during sintering.

The pulverization is preferably carried out in a wet manner, and alcohol solvents, hexane, trichloroethane, trichloroethylene, xylene, toluene, fluorine solvents, paraffin solvents, and the like can be used.

"Within the FeBRM composition range described in Section 2, for example, the raw material is Nd 1
After weighing to a composition of 5 atomic %, 8 B atoms, IVI atoms, and 2 balance Fe, melting was performed to obtain an ingot.

When crushing this ingot, the powder particle size is 0.3~
The grinding conditions were adjusted to fall within the range of 137 ILm. The powder particle size here refers to the average particle size measured using a Fischer subsieve sizer. In addition, the particle size is 40μ
For powders with a size of 2 m or more, a JIS standard sieve or microsieve was used.

The obtained powder was heated in a magnetic field of 10 KOe.
/crri', cl) Apply pressure to make a molded body, A
r 1080 °C and 11 in 200 Torr atmosphere
Sintering was performed at each temperature of 00°C for 1 hour.

Powder particle size after crushing and coercive force (i) of the obtained sintered body
The relationship of Ic) is shown in FIG.

The obtained alloy powder having a predetermined particle size is then molded. The pressure during molding is preferably in the range of 0.5 to F3 Ton/crn', 0.5 Ton/cr
If the pressure is less than n', the molded product will not have sufficient strength and will be extremely difficult to handle in practical use as a permanent magnet material. In addition, if it exceeds 8 Ton/crn', the strength of the molded product will greatly increase, which is preferable in terms of handling, but it will cause problems when continuously molding in terms of the strength of the press punch and die mold. Undesirable.

However, the molding pressure is not limited. Furthermore, when producing magnetically anisotropic magnet materials during pressure molding, pressure molding is performed in a magnetic field, and the magnetic field at that time is approximately 7.
Preferably, it is carried out in a magnetic field of ~13 KOe.

The obtained compact is sintered at a temperature of 800-1200°C, preferably 1000-1180°C.

If the sintering temperature is less than 800°C, sufficient density as a permanent magnet material cannot be obtained, and the required magnetic flux density cannot be obtained. If the temperature exceeds 1200°C, the sintered body will be deformed, the orientation will be lost, and the magnetic flux density and squareness will be lowered, which is not preferable.

Also, the sintering time should be at least 5 minutes, but if it is too long, there will be problems with mass production, so the preferred sintering time is 30 minutes or more.
It is 8 hours.

Sintering is performed in a reducing or non-oxidizing atmosphere. When an inert gas atmosphere is used as the sintering atmosphere, it may be a constant pressure or pressurized atmosphere, but it is also possible to perform the sintering in a reduced pressure atmosphere or a reduced pressure inert atmosphere as a method of densifying the sintered body.

Another method for increasing the sintering density is to conduct the sintering in an atmosphere of H2 gas, which is a reducing gas. Through each of the above steps, a magnetically anisotropic permanent magnet material with high magnetic flux density and excellent magnetic properties can be obtained.

The permanent magnet material of the present invention is obtained as a sintered body, and the density of the sintered body is preferably 81% or more of the theoretical density, more preferably 88 or more, and reaches a maximum of 89% or more.

Hereinafter, aspects and effects of the present invention will be explained according to examples. However, the present invention is not limited to the examples and described aspects.

(1) The starting material is Fe with a purity of 89.9% C weight 2,
The same applies to raw material purity below) electrolytic iron, B and “C7x”
Ropo CI7 alloy (19.38%B, 5.32%AI
.

0.74$Si, 0.03XG, balance Fe), R to L
Te purity H% or more ('Impurities are mainly other rare earth metals)
use.

As Go, electrolytic CO with a purity of 89.9% was used.

M is Ti, Mo, Bi, Mn with a purity of 99X.
, Sb.

Ni, Ta, Ge, 88% W, 99.9% C
7) AI, Sn, 85%)If, also V as 81.
Ferrovanadium with 2% V, 87.8 as Nb
Ferroniobium with % Nb, Eil as Cr, 9%
75.5% as ferrochrome and Zr containing Cr
Ferrozirconium containing Zr was used.

(2) Magnet raw materials were melted using high frequency induction. At that time, an alumina crucible was used as the crucible, and an ingot cast into a water-cooled copper mold was used.

(3) Crush the ingot obtained by melting to 35 mes
h, then further milled by ball mill to 0.3 to 80IL.
Grinding was carried out to obtain m.

(4) Powder is 0.5-8To in a magnetic field of 7-13KOe.
Molding was performed at a pressure of n/ctn'. (However, when producing an isotropic magnet, it was molded without applying a magnetic field.) (5) The molded body was sintered at a temperature of 800°C to 1200°C. The atmosphere at that time was a reducing gas, an inert gas, or a vacuum. The sintering time was in the range of 15 minutes to 8 hours.

Example 1 Atomic percentage composition (same below): 76Fe, 8B, 15N
The alloy d#ITi was ground into a powder with an average particle size of 37 Lm, and a compact was made by applying pressure of 37 on/cm'c)) in a magnetic field of 10 KOe, and the powder was heated at various temperatures of 2 in an Ar atmospheric pressure atmosphere.
The sintered density and properties when time-sintered were as shown in the table below.

Example 2 An alloy having a composition of 73Fe1110BΦ15Nd.2v was ground into a powder with an average particle size of 5 gm, and a molded body was made by applying a pressure of 1.5 Tons/crrf in a magnetic field of 1 OKOe and in a vacuum of 1 x 10'-''torr. The sintered density and properties when sintered at each temperature for 1 hour are as shown in the table below.

Example 3 An alloy with a composition of 78Fe, 8B, and 15Nd-INb was ground into powder with an average particle size of 2p and ra, and a molded body was made by applying a pressure of 2 Ton/crrf in a magnetic field of 10 KOe, and at various temperatures in an Ar atmosphere of 200 Torr. The sintered density and properties after sintering for 1 hour were as shown in the table below.

Example 4 An alloy having the composition 74Fe, 8B, 17Ndl+lTa was ground into powder with an average particle size of 37 tm, and pulverized in a magnetic field of 10 KOe. A molded body was made by applying a pressure of 5 Ton/cm' and sintered at each temperature for 3 hours in an Ar atmospheric pressure atmosphere.The sintered density and properties were as shown in the table below.

Example 5 Composition? 5.5Fe ・10B-14Nd eO,5Cr
The alloy was ground into powder with an average particle size of 2.8 μm,
A compact was made by applying a pressure of 27 on/cm' in a magnetic field of 0 KOe, and sintered at the nominal temperature for 4 hours in a vacuum of 1X10 Torr. The sintered density and properties were as shown in the table below.

Example 6 Composition? Grind the alloy called eFe No. 8B Fist 15Nde1Mo to powder with an average particle size of 3.5p, ra, 1OK
A compact was made by applying a pressure of 37 on/crrf in a magnetic field of Oe, and sintered in Ar at 60 Torr for 2 hours at each temperature. The sintered density and properties were as shown in Table F.

Example 7 An alloy with a composition of 75.5Fe and 7B 17Ndl10.5W was ground into powder with an average particle size of 3.8#L11.
．． A compact was made by applying a pressure of 37 on/crn' in a magnetic field of 0 KOe, and sintered in an Ar atmospheric pressure atmosphere at each temperature for 1 hour. The sintered density and properties were as shown in the table below.

Example 8 An alloy having a composition of 7BFe, 8B, 14Nd, and IMn was ground to obtain an average particle size of 4. The sintered density and properties of the sintered powder when it was made into a powder of Ogra, applied a pressure of 1.57 on/crn' in a magnetic field of 10 KOe, and sintered for 2 hours at each temperature in an Ar200 Torr atmosphere are as shown in the table below. Became.

Example 9 Composition 7ft, 5Fe・7B・1BNd・0.5N
An alloy with an average particle size of 4. The sintered density was obtained by applying a pressure of 27 on/crn' in a magnetic field of 10 KOe to a molded body of OILm powder, and sintering it for 1 hour at each temperature in a vacuum of 1. The characteristics are as shown in the table below.

Example 10 An alloy called Jflu8Fe @8B φ15Nd ・IAI was ground into powder with an average particle size of 2.57Lm, and 1O
A compact was made by applying a pressure of 1.5 Ton/cm'' in a KOe magnetic field, and sintered in Ar 40 O Torr at each temperature for 2 hours. The sintered density and properties were as shown in the table below.

Example 11 Composition? 4.5Fe ・13B ・11Jd 110.5
An alloy of Ge was ground into a powder with an average particle size of 3.5 JLm, a molded body was made by applying a pressure of 7.57 on/cm' in a magnetic field of 10 KOe, and sintering was performed at each temperature for 2 hours in an atmospheric pressure atmosphere. The sintered density and properties are as shown in the table below.

Example 12 An alloy with a composition of 78Fe, 8B, 14Nd, ISn was ground into powder with an average particle size of 4.0 lm, and a compact was made by applying a pressure of 2.57 on/crn' in a magnetic field of 10 KOe at Ar80 Torr. The sintered density and properties when sintered at each temperature for 1 hour are as shown in the table below.

Example 13 An alloy with a composition of 75Fe ψ9B Q15Nd @ISb was ground and the average particle size was 3. Lpm powder, 10KOe
A molded body was made by applying a pressure of 1.57 on/crn' in a magnetic field of , and then heated at each temperature of 1.
The sintered density and properties after sintering for 5 hours are as shown in the table below.

Example 14 An alloy with a composition of 75Fe, 7B, 17Nd, and IBi was ground to obtain an average particle size of 2. The sintered density and properties of IILm powder were made into compacts by applying a pressure of 2.57 on/crn in the magnetic field of LOKOe, and sintered in ArTorr for 0.5 hours at each temperature, as shown in the table below. Became.

Example 15 Composition? An alloy of 6Fe, 8B, 15Pr, and IAI is crushed to have an average particle size of 4. OJ7. IJj powder and 1OKO
A compact was made by applying a pressure of 1.5 Ton/am' in a magnetic field of 1.5 m, and sintered in Ar20 O Torr at each temperature for 2 hours. The sintered density and properties were as shown in the table below.

Example 16 An alloy having a composition of 73Fe, 88-15Nd, 2Dy, and 1v was ground to obtain an average particle size of 3. IJj, 11 powder, 10
2. In the magnetic field of KOe. A molded body was made by applying a pressure of Oton/cm' and sintered at each temperature for 1 hour in Ar 100 Torr.The sintered density and properties were as shown in the table below.

Example 17 An alloy with a composition of 7θFee8B・15Nd-IAI was ground to obtain an average particle size of 3. Q4m powder and 3 without applying a magnetic field.
A molded body was made at a pressure of Ton/ctn' and sintered at each temperature for 1 hour in Ar atmospheric pressure, and the sintered density and properties were as shown in the table below.

Furthermore, Fig. 6 shows 78.5Fe, 8B@15Nd, 0.
5AI (produced in the same manner as the present invention, anisotropic example 1O)
The demagnetization curve of the present invention is shown in comparison with that of a known amorphous ribbon. Amorphous ribbon? 0.5Fe@15.5
Be7Tb・7La is 660″c after being made into an ultra-quenched ribbon.
It was heat-treated for 15 minutes (Source: J, J.Be
IEEE Transaction on
Magnetics Vol.

MAG-18No, J In2. P1451-145
3).

As seen in the above examples, FeBRM-based permanent magnet phase nails can be manufactured into high-performance products of any size by the powder metallurgical sintering method of the present invention, and can be stably and inexpensively manufactured into industrial products. It is very useful industrially.

Note that it is not possible to create high properties and arbitrary shapes using conventional manufacturing methods such as sputtering and ultra-quenching.

[Brief explanation of the drawing]

1 to 3 show residual magnetization Br(
Figure 4 is a graph showing the relationship between KG) and additive element M (horizontal axis, , In yet another example, the average particle size of the alloy powder (horizontal axis log scale gm) and coercive force 1Hc (KO
Fig. 6 is a graph showing a comparison between the demagnetization characteristic curves of a representative example of the present invention and a conventional FeBR-based amorphous ribbon, and Fig. 7 is a graph showing the relationship between sintering temperature, magnetic properties, and density. Graphs showing the relationship between are shown, respectively. Applicant Sumitomo Special Metals Co., Ltd. Agent Patent Attorney Asami Kato Procedural Amendment (spontaneous) February 28, 1980 Mr. Kazuo Wakasugi, Commissioner of the Patent Office 7, -,, = H1 Case Indication 1988 Patent Application No. No. 90038 (filed on May 24, 1982) 2 Name of the invention Permanent magnet material and its manufacturing method 3 Relationship with the case of the person making the amendment Name of applicant Sumitomo Special Metals Co., Ltd. 5 Date of supplementary order Voluntary 6 Amendment Column 7 for detailed explanation of the invention in the subject specification Content 1 of the amendment: The column for detailed explanation of the invention in the specification is amended as follows. (1) On page 8, line 20, "11" is corrected to "12". (2) On page 12, line 6, add “(other rare earth elements, Ca, Mg, Fe, Ti, C, 0, etc.)” after “impurities”. (3) Page 12, lines 13 and 15, r before “etc.”
Ca, Mg, O, Si” are added. (4) On the same page, line 18, before “However,” rCa, Mg84%
Hereinafter, 02% or less, St 5% or less" will be added. that's all

Claims (2)

[Claims] (1) In terms of atomic percentage, 8 to 30% R (where R is at least a species of rare earth element including Y), 2 to 28%
B, one or more kinds of additive elements M in a predetermined percentage (herein, the additive elements M in a predetermined percentage include Ti 4.5% or less, Ni 8.0% or less,
Bi 5.0X or less, V 9.5% or less, N
b 12.5% or less, Ta 10.5% or less, 1; r 8.5% or less, Mo 9.5X or less, W 9.5% or less, Mn 8. (1% or less, AI L5% or less, Sb 2.5% or less, Ge 7.0% or less, Sn 3.5% or less, Zr 5.5% or less, and Hf 5.5% or less) However, M The content of M is less than the atomic percentage of the element having the maximum value among the M elements, and the remainder is Fe and impurities unavoidable during manufacturing, and the composition is 0.3 to 80 ILm.
The alloy powder with an average particle size of 900-120
FeBRM permanent magnet material made by sintering at 0°C. (2) In terms of atomic percentage, 8 to 30% of R (where R is at least one kind of rare earth element including Y), 2 to 28 parts of B, and one or more kinds of additive elements M of a predetermined percentage; ( Here, the predetermined percentage of additive elements M are Ti: 4.5% or less, Ni: 8.02% or less, Bi: 5.0% or less, V L: 5% or less, Nb: 12.5% or less, Ta: 10.5%
Below, Cr, 8.5% or less, No. 9.
5% or less, W 9.5X or less, Mn 8.0
% or less, AI Ia, 5% or less, Sb 2.
5% or less, Ge 7.9% or less, Sn 3.
5% or less, Zr 5.5% or less, and Hf 5.5% or less) However, the content of M is not more than the atomic percentage of the element having the maximum value among the M contained elements, and the balance is Fe and manufacturing.
0.3~80wl with a composition consisting of unavoidable impurities
The alloy powder with an average particle size of 11 was compacted, reduced, 1.
Or non-oxidizing, SOO ~ 120 in constant atmosphere
A method for producing a FeBRM permanent magnet material, characterized by sintering at 0°C.