JPS59211558A - Permanent magnet material - Google Patents

Abstract

PURPOSE:To obtain an anisotropic sintered permanent magnet material having superior magnetic characteristics by sintering Fe alloy powder contg. a rare earth element including Y, B and a specified element. CONSTITUTION:Fe alloy powder contg. 8-30atomic% at least one kind of rare earth element including Y, 2-28atomic% B and a specified amount of one or more among Ti, Bi, Nb, Cr, W, Al, Ge, Ni, V, Ta, Mo, Mn, Sb, Sn, Zr and Hf is molded and sintered to obtain an anisotropic sintered permanent magnet material. The grain size of the sintered body is 1-90mum. A sintered permanent magnet comparable or superior to hard ferrite in magnetic characteristics is obtd. without using scarce elements such as Co.

Description

DETAILED DESCRIPTION OF THE INVENTION The present invention relates to a FeBRM-based sintered permanent material, and particularly to one having a specific crystal grain size that can realize favorable magnetic properties. In the present invention, R represents a rare earth element containing Y.

With the recent advancements in electronics technology, permanent magnets have been used in speakers, motors, magnetic disk drive.

It is widely used in devices such as seismometers, generators, and magnetrons, and is an industrially important material.

In addition, alnico, hard ferrite, aluminum, samarium cobalt (SmCo), and the like are well known as permanent magnet materials and are in practical use. Among these, alnico has a high residual magnetic flux density (hereinafter abbreviated as Br) but has a low coercive force (hereinafter abbreviated as Hc), and hard ferrite has a large He but low Br.

With advances in electronics technology, electrical components are becoming more highly integrated and smaller, but magnetic circuits using alnico and hard ferrite have to be larger in both quantity and volume than other components. ! There is no. On the other hand, Sm
Co-based magnets have high Br and large He content, so they meet the demands for miniaturization and high performance of magnetic circuits, but samarium, which is used as a raw material, is a rare resource, and Conoheld is a magnet that is unevenly distributed in specific regions. As a result, supply is unstable. Therefore, a new j that does not have these problems
It has been desired to develop a K-magnetic material.

1. In order for rare earth magnets to be used cheaply and in large quantities in a wider range of fields, it is necessary to use light rare earths, which do not contain expensive cobalt and are contained in large amounts in ores, as rare earth metals. It is necessary to make it the main component. As one attempt at such a permanent magnet material, an RFe2-based compound (where R is at least one kind of rare earth metal) was investigated. Clark (A, E, C1ark) spuntered amorphous TbFe2 at 4.2° and 29.5
M, GOec7: + Energy product, 300-50
When heat treated at 0°C, retention force at room temperature) 1c = 3.4K
It was found that the maximum energy product (B) max = 7 MGOe. Similar studies have been conducted on SmFe2, and it has been reported that 9.2 MGOe can be obtained at 77°. However, all of these materials are thin films made by sputtering, and are not magnets used in general speakers or motors. It was also reported that an ultra-quenched ribbon of a PrFe-based alloy exhibits a high coercive force (Hc=2.8KOe).

Furthermore, Kuhn et al.
It was found that when an ultra-quenched amorphous ribbon of 'l Tbo, o5 Ldo, o5 is annealed at 627°C, Hc reaches as much as 9KOe (Br2' 5KG). However, in this case, the squareness of the magnet curve is poor (B)I)
max is low (N, C, Koon et al., Appl, Ph
yS.

Lett, 39(10), 1981.840-842
page).

Also, Kabacotu (L, Kabacof f) etc. are (F
eO, 11B o, , )1-xPrx (X=0~0.
3 atomic ratio) was prepared, and Fe-Pr
It has been reported that there is a two-component system with He at KOe level at room temperature.

These ultra-quenched ribbons or sputtered thin films are not practical permanent magnets (bodies) that can be used as such, and practical permanent magnets cannot be obtained from these ribbons or thin films.

That is, it is not possible to obtain a bulk permanent magnet body having an arbitrary shape from a conventional ultra-quenched Fe-B-R ribbon or RFe-based sputtered film.

The magnetization curves of the FeψBeR ribbons reported so far have poor squareness, and cannot be considered practical permanent magnet materials that can compete with conventional magnets. In addition, both the 1° sputtered thin film and the ultra-quenched ribbon are isotropic in terms of wood, and it is possible to obtain magnetically anisotropic practical water magnet E1 from them.
It is virtually incompetent.

Therefore, the basic purpose of the present invention is to eliminate the drawbacks of the conventional methods described above, and to create a new practical permanent magnet body that has magnetic properties equivalent to or better than conventional hard ferrite, without using resource-poor substances such as CO. It's about getting. More specifically, the present invention has good magnetic properties above room temperature, can be molded into any shape and practical size, has a highly square magnetization curve,
Furthermore, it is an object of the present invention to obtain a practical permanent magnet having magnetic anisotropy, which can effectively use resource-rich minor elements as R.

The present inventors previously discovered that Nd, which does not necessarily require samarium, has no resource wealth, and has almost no known uses to date, and Fe, which has Fe as its main component.
A BR compound permanent magnet was developed and filed by the same applicant as the present application (Japanese Patent Application No. 57-145072).

This FeBR-based magnet material has high Br and high energy product (
It is a new industrial permanent magnet material v1 that replaces conventional alnico, hard ferrite, and SmCo magnets.

The present invention basically aims at providing a range of sintered crystal grain size in order to obtain even better magnetic properties in this FeBR-based sintered unsintered permanent magnet material, and furthermore, the coercive force is increased. The purpose is also to make improvements as necessary.

That is, the permanent magnet material of the present invention is a FeBR-based sintered permanent magnet material with an atomic percentage of 8 to 30 R (where R is at least one rare earth element including Y), 2
~28% B, one or two or more of the following specified 2 additive elements M (excluding MOX, when M includes two or more of the above additive elements, the total amount of M is the Magnetic anisotropic sintered permanent magnet material 2 consisting of atomic percentage of the maximum value (at most), and the balance Fe, and the average crystal grain size of the sintered body is 1 to 90 pm Ti: 4.5% or less, Ni: 8.0 %below,
Bi 5.0% or less, ■ 9.5% or less, Nb
12.5% or more, Ta 10.5% or less, O
r 8.5% or less, Mo 9.5X or less, W
9.5% or less, Mn 8.0% 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.

The present invention will be explained in detail below.

As disclosed in Japanese Patent Application No. 57-145072, FeBR alloy exhibits high magnetic properties as a sintered body and has a Curie point 3.
It is a novel crystalline alloy with a temperature of 00°C to about 370°C. The inventors of the present invention have discovered that by making this FeBR alloy into a sintered body through the processes of melting, casting, pulverizing, orientation forming in a magnetic field, and sintering, a permanent magnet with magnetic properties that could not be confirmed with this system in the past. Furthermore, in the present invention, it has been found that excellent magnetic properties as a permanent magnet can be exhibited when the average crystal grain size of the sintered body is within a certain range. Through extensive experiments, it has been clarified that high-performance FeBRM-based sintered permanent magnets can be stably manufactured industrially.

The FeBRM alloy has been found by measurements by the present inventors to have a high magnetocrystalline anisotropy constant Ku and an anisotropic magnetic field Ha comparable to that of conventional SmCo magnets.

According to the theory of single-domain particles, magnetic materials with high Ha have the potential to become high-performance fine particle magnets, such as hard ferrite and SmCo magnets.

Generally, in a single-domain fine-grain magnet, if the particles are large, the particles will have a domain wall, so reversal of magnetization easily occurs due to movement of the domain wall, and He is small. - On the other hand, when the particle size becomes smaller than a certain size, the particle no longer has a domain wall and the reversal of magnetization proceeds only by rotation, so Hc increases. The critical dimension of this single magnetic domain differs depending on each material, and in the case of iron it is 0.01
It is said that JLrrr, hard ferrite is about 1JLm, and SmGo type is about 4JLm.

Further, high values of Hc for each of these materials are obtained near this critical dimension. In the FeBRM permanent magnet of the present invention, Hel.
KOe or more can be obtained, preferably He4KOe or more can be obtained in the range of 1.5 to 70 p-m. The permanent magnet of the present invention is obtained as a sintered body. Therefore, the size of crystal grains after sintering the sintered body is a problem. The Hc of the sintered body is l K
In order to make it more than Oe, the 11 uniform crystal grain size after this sintering is l
It was experimentally confirmed that #L11 or higher is required.

In order to obtain an even finer sintered body crystal grain size, it is necessary to create a fine powder before sintering. However, the fine powder of FeBRM alloy is easily oxidized, the effect of strain applied to the fine particles becomes large, and when the particle size becomes extremely small, it becomes a superparamagnetic material instead of a ferromagnetic material. is expected to decrease significantly. Furthermore, when the crystal grain size becomes larger than 99p-tn, the grains are no longer single-domain fine grains, but have domain walls inside the grains, so that reversal of magnetization occurs easily and Hc becomes small.

In order for Ha to be 1 KOe or more, it must be 9Q) ha or less. Particularly preferably, it is 1.5 to 7Q#Lm, and a high characteristic with Hc of 4 KOe or more can be obtained (see Table 1 below). The rare earth element R used in the permanent magnet of the present invention includes Y,
It is a rare earth element including light rare earths and heavy rare earths, and one or more of them is used. That is, this R is Nd,
Pr, La, Ce, Tb, Dy, Ha.

Er, Eu, Sm, Gd, Pi, Tm, Y
b, Lu and Y are included. As R, a light rare earth element is sufficient, and Nd and Pr are particularly preferable. Also usually H
One of them is sufficient, but in practice, a mixture of two or more (Mitushmetal, didymium, etc.) can be used for reasons such as convenience of manpower, Sm, Y, La, G.
E, Gd, etc. can be used as a mixture with other R1, especially Nd, Pr, etc. Note that this R does not have to be a pure rare earth element, and may contain impurities that are unavoidable during production within the industrially available range.

As B (boron), pure boron or ferroboron can be used, and materials containing AI, Si, G, etc. as impurities can also be used.

The permanent magnet of the present invention has the above-mentioned 8-30XR, 2-28
%B, predetermined 2 additive elements M, remainder Fe (atomic percentage), retention force He≧IKOe, residual magnetic flux density Br4K
Shows magnetic properties of G or higher, maximum energy product (BH) wa
x is equal to or higher than hard ferrite (approximately 4 MGOe).

When R is less than 8 atoms and 2, He becomes lower than 1 KOe. As R increases, Hc increases, but 30
When the number of atoms exceeds 2, the Br value of hard ferrite increases to about 4.
It becomes less than KG. B shows a similar tendency; below 2%, Ha is lower than I KOe, and above 28%, Br
becomes lower than 4KG.

The light rare earth is the main component (i.e. total) of H, 11~24% R, 3~
The composition of 27% B and the remainder m (Fe+M) shows a maximum energy product (BH) maz≧7 MGOe, which is a preferable range.

Most preferably, the light rare earth is the F component of R, and 12 to 2
0% R, 4 to 24
ar≧10MGOe, (BH)saw is maximum 33
NG [He reaches -L.

In the magnet of the present invention, most of M has the effect of increasing iHc. Increasing iHc by adding M increases the stability of the magnet and expands its uses.

However, since M is a non-magnetic element (excluding Ni), as the amount added increases, Br decreases and therefore (BH
) max decreases. M-containing alloys are very useful as there have recently been many applications that require a high iHc even if the (BH)max is a little lower (BH)w
Ishikawa is in the range where ax is 4 MGOe or more.

In order to confirm the effect of each addition of the additive element M on Br, the results of measuring B' by changing the added acid are shown in the first table.
It is shown in Figs. Additional elements M other than Bi, Mn, and Ni (Ti, Zr, Hf, V, Ta,
Nb, Cr.

The upper limit of the addition amount of W, Mo, Sb, Sn, Ge, AI) can be selected within a range equal to or higher than about 4 kg of Br of hard ferrite, as shown in FIGS. 1 to 3. Furthermore, the preferable range from the viewpoint of Br is 8.5.8
．． The division into stages such as IDKG can be clearly read from FIGS. 1 to 3, respectively.

From these figures, the hard ferrite level (BH)m
aw approx. 4 Additive element M as a range equivalent to or higher than KGOe
The upper limit of the amount of addition is as follows.

(Ti 4.5% or less, Ni 8.0% or more)
, Bi5. Q% or less, V 8.5"X or less, Nb 12.5% or less, Ta 10.5% or less, Cr 8.5% or less, Mo 8.5% or less, -9.5% or less, Kn 8 .0% or less, AI
9.5% 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.

When two or more of the above elements are contained, the intermediate value of the characteristic curve of each added element shown in Figures 1 to 3 is generally indicated, and the content of each element is within the range of -1-%. And its content is less than the maximum value of 2% for each element.

As the amount of M added increases, Br generally decreases, but on the other hand, iHc increases for most M, so (
BH)wax has a value equivalent to that without M addition due to the addition of M. Increasing the coercive force contributes to stabilizing the magnetic properties, so that a permanent magnet that is extremely stable in practice and has a high energy product can be obtained.

When Mn and Ni are added in large amounts, iHc decreases, but N
Since i is a ferromagnetic element, Br does not decrease much.

Therefore, the upper limit of Ni is preferably 8% from the viewpoint of Br, and 4.5% or less from the viewpoint of Hc.

Although Mn addition has a larger effect on Br reduction than Ni, it is not as drastic. Thus, the upper limit of Mn is 8 from the viewpoint of Br.
From the viewpoint of z and iHc, Mn is preferably 3.5% or more.

As for Bi, it is actually impossible to produce an alloy whose vapor pressure is extremely high and exceeds 5% Bi, so it is set at 5zF or lower. Type 2 - In the case of alloy containing M in b, Br is 4 KGOe
In order to satisfy the above conditions, it is necessary to add each element mentioned above.
It must be less than or equal to the maximum value (parallel) of the 1-limit.

The permanent magnet of the present invention is a Fe-B-RM system, and does not necessarily contain Go, and as R, a light rare earth which is abundant in resources can be used, and it does not necessarily require Sm or Since there is no need to use Sm as the main ingredient, the raw materials are abundant and inexpensive, making it extremely useful.

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.

Table 1.2 shows various Fe
Showing the characteristics of a permanent magnet made of eB・R@M compound (
Items outside the scope of the present invention are also shown with a C code for comparison).

(1) The alloy is high-frequency melted and cast in a water-cooled copper mold.The starting materials are electrolytic iron with a purity of 98.9% as Fe, B and L-(
7x o poron alloy (19,38%B, 5.32%A
I, 0.74$Si, 0.03%G balance Fe), R
，! = L Te purity of 99.7% or more (impurities are mainly other glazed metals).

'ri, No, Bi, Ge with 99% purity as M
, Ni.

Ta, Sb, 98% glue, 99.9% A1, S
n, 85$ c7) Hf, also ferro containing 81.2% V as V/(Nadium, ferronniobium containing 67.6% Nb as Nb, 61.9% Or as Cr)
Ferrochrome containing, and 75.5% Zr as Zr
Ferrozirconium containing r was used.

(2) Grinding: Coarsely pulverize to mesh-through using a stamp mill, then finely pulverize (3 to 10 mm) using a ball mill for 3 hours.

(3) Orientation and shaping in magnetic field (10KOe) (1,5
pressurized at t/cm').

(4) Sintering 1000-1200℃ 1 hour Ar
Medium, left to cool after sintering.

As shown in Table 1, for a compound t that does not contain B, the coercive force H
Since e is close to 0 (it is set to 0 because it is too small to be measured with a high Hc measuring instrument), it does not become a permanent magnet. However, by adding B in an atomic ratio of 4% and a weight ratio of only 0.84%, Hc becomes as high as 3KOe (sample C7), and as the B content increases, He rapidly increases. Along with this (B
H) Wax reaches 7 to 30 MGOe, a maximum of 31 (MGOe or higher), and exhibits high characteristics comparable to S+++Go magnets, which are the highest grade permanent magnets currently known.

Although Table 1 mainly shows the case of Nd and Pr, the Fe.BRM compound exhibits good permanent magnetic properties also for other H and for various combinations of R. The Fe.BRM compound exhibits good permanent magnetic properties at appropriate magnetization and R content. As B increases from O in the FeeB・R・M system, Hc increases. On the other hand, the residual magnetic flux distribution Iff Br increases monotonically at first, but reaches a peak around 10 atoms 2 , and as B is further increased, Br monotonically decreases as τ increases.

Table 1 Table 2 Table 2 (Continued) Permanent magnets (materials) with at least IKOe or higher H
c is required, so in order to satisfy this, the value along B must be at least 2 atomic % (preferably 3 atomic % or more).
atomic% or more). The permanent magnet of the present invention is characterized by a high Br, and is often used in applications that require high magnetic flux density.

In order to make the Br of hard ferrite approximately 4KG or more,
In the Fe'eB fist R@M compound, the amount of B is 2 days
Must be less than %. In addition, 83 to 27 atomic%
, 4 to 24 atom% are respectively (Bl()IIIax ?MG
Preferable for Oe or more, 10 MGOe or more,
or within the optimal range.

Next, when considering the optimal range of the R amount, the larger the R amount, the higher the He, which is desirable as a permanent magnet. As for Mizuku magnet material shrine, as mentioned earlier, He is more than IKOe [,
Therefore, for this purpose, the amount of R should be 8 atomic % or more.
Must. On the other hand, it is good to have high He as the amount of R increases, but since R is very easily oxidized,
High R alloy powder is easily flammable and difficult to handle. Therefore, in consideration of mass productivity, it is desirable that the amount of R be 30 atoms or less. If the amount of H is more than this, the powder becomes easily flammable and mass production becomes very difficult.

Further, since R is more expensive than Fe, it is desirable that R be as small as possible. In addition, R11-24 atom%, 12-24 atom%
The range of 20 atomic % is (B)l)man and 7MGO, respectively.
"e or more, lOMGOe or more" - is a preferable or optimal range.

Next, in the above method, (2) pulverization was carried out using a sub-s 1 eve-sipe manufactured by Fisher.
The average particle size measured at 1zer) is 0.5 to 100 meters.
The grinding time is changed appropriately to obtain each piece.
．． Samples with each composition shown in Table 2 were prepared.

Comparative example: In order to obtain a crystal grain size of 1100p or more, the sample was held for a long time in an Ar atmosphere at a temperature 5 to 20°C lower than the sintering temperature after sintering (Table 1, No, Cl0).

The magnetization of the thus obtained samples having the respective compositions shown in Table 1.2 was examined, and the magnetic properties and average crystal grain size were measured. The results are shown in Tables 1 and 2. Here, the average grain size is calculated by polishing the sample surface, taking a micrograph at a magnification of X100 to X100O using an optical microscope, drawing a circle with a known area, and drawing straight lines dividing the circle into eight equal parts. The average number of particles on the diameter was counted and calculated. However, particles separated on the boundary (circumference L) are counted as 1l2 (this method is known as Heyn's method).

The part of the hole is omitted from the calculation.

In Table 1, those marked with C indicate comparative examples.

Note that each of 01 to C1l is outside the scope of this patent.

Furthermore, it can be seen from CIO and C1l that when the crystal grain size is outside the range of this patent, Hc decreases to less than 1 KOe.

Next, the relationship between the average grain size and Hc for composition No. 6.20 in Table 2 was examined in detail, and the relationship as shown in FIG. 4 was obtained. From Figure 4, He has a D of 3 to 10.
It can be seen that the value peaks near Bm, then decreases rapidly when it is smaller than that, and gradually decreases when it is larger. Even if the composition changes within the composition range of this patent, the same tendency is exhibited. This means that FeB
This shows that the RM magnet is a small magnet, fine particle type magnet.

In addition, the present inventors further obtained an alloy with the same composition as N017 in Table @2 by the casting method described in (1) above, but although the average crystal grain size of the cast alloy was 20 to 8 Qpm. First, only a low value of less than 1 KOe was obtained for Hc.

From the results shown in Table 1 and Figure 4, in order for the Or of the FeBRM and v-magnet to be approximately 4 KG or higher than that of hard ferrite, and for the Hc to be 1 KOe or higher, the composition must be within the range of this patent and the average crystal grain must be The diameter should be 1 to 99 gm, and in order to obtain high properties of He 4KOe or more,
It is shown that it is 40JLm.

Figure 5 shows typical examples (1) Fe-8B-15Nd,
(2) Fe-8B-158d-INb, (3)
Three kinds of dynamic magnetization curves and demagnetization curves (1 to 3) of Fe-8B-15Nd=2AI are shown. All exhibit squareness useful as permanent magnet materials. Note that the average crystal grain size is 5~
It was used in a range of 10 μm.

The crystal grain size of the sintered body can be controlled by controlling manufacturing conditions such as crushing, sintering, and heat treatment.

As shown below, the FeBRM quaternary magnetic anisotropy of the present invention □
Permanent magnets made of sintered bodies are manufactured by outside manufacturers of Fe, B, R, and H. Although they can tolerate the presence of unavoidable impurities,
Furthermore, the following development is also possible, and the practicality can be further improved. That is, part of Fe can also be replaced with CO. Further, the permanent magnet material of the present invention includes Cu, C, and S.
It is also possible to contain small amounts of , P, etc., making it possible to improve manufacturability and reduce costs. That is, Cu 3.5% or more, F 32.0% or more, C 4.0% or less, P 3.5
% or less (however, the content is less than the maximum value of each element) is still Br (about 4KG), which is the same as hard ferrite.
This is useful. Cu and P are available from inexpensive raw materials.
C may be mixed in from an organic binder, and S may be mixed in from the manufacturing process.

Below-1-1 The present invention realizes a magnetically anisotropic sintered permanent magnet having high residual magnetization, high coercive force, and high energy product using an inexpensive Fe-based alloy that does not contain CO, and is extremely useful for the industry. It has high value.

[Brief explanation of drawings]

Figures 1 to 3 show implementation 01 of the present invention (Fe-8B-1
Graph showing the relationship between the acid (1%) of the additive element M and the residual silver Br (KG) in 5Nd-xM), No. 41Nt±
FIG. 5 is a graph showing the relationship between Hc and average crystal diameter for Example J of the present invention, and FIG. Applicant: Sumitomo Special Metals Co., Ltd. Agent, Patent Attorney Asami Kato Procedural Amendment (Spontaneous) August 11, 1981 Date 1 Case Description 1982 Patent Application No. 84859 (May 14, 1988) 2 Name of the invention Permanent magnetic material 3 Relationship to the case of the person making the amendment Name of applicant Sumitomo Special Metals Co., Ltd. 5 Date of amendment order Spontaneous 6 Number of inventions increased by the amendment None 7 Inventions in the specification subject to the amendment The Detailed Explanation column will be corrected as follows: (1) On page 10, line 17, "is sufficient" will be corrected to "is preferable." (2) On page 11, line 2, the first "wa" will be corrected. Before, especially La
, Sm, Er, Tm, etc.". (3) On the same page, line 5, after “impurities,” “other rare earth elements,”
Add Ca, Mg, Fe, Ti, C, 0, etc. (4) Page 13, line 11, “approximately 4KGOeJ”
Corrected to OeJ. (5) Page 14, line 15, rB rcy)
iHc 1. Corrected to "kOe". (6) On the same page, line 16, delete "wa". (7) Same page, line 18, correct rBrJ to "same as rNi." (8) On the same page, line 19, delete "wa". (8) Page 15, line 3, correct "r4KGOe" to r4kGJ. (lO) Add Roman text to the end of line 6 on the same page. ``The amount of M added should be 0.1 to 3%, considering the effect of increasing iHc and the influence on Brl decreasing tendency BH) max.
is most desirable, and M is VNb, Ta, Mo, W
, Cr, and AI are preferred. The addition of M makes the rise of iHc steeper. General B, R
As the amount increases, Br decreases after reaching its maximum value, but an increase in iHc is obtained in the region where Br is maximum. ” (11) Page 16, line 1, “purity” is changed to “purity (weight ratio, the same applies hereinafter).” (12) On page 16, line 13, "mesh" is corrected to "35 mesh." (13) Table 1 on page 18 is amended as follows. (The following is a margin) No. 1 Notation 14) Page 19, Table 2, rlNbJ of No. 3 is r2
Let NbJ be rS, 4JItr9.4J. (15) Table 2 on the same page, No. 6, rll, 5” is r12
．． (N and L, r30.2J is r33.lJ. (18) Table 2 on the same page, No. 17 (7) rSnJ is r
Correct to S bJ. (I7) Table 2 (continued) on page 20 is amended as follows. (Margin below) Table 2 (Continued) (18) Page 25, line 8, rCa, Mg before "etc." Add Si and OJ. (19) In line 10 of the same page, correct rS2 and OJ to rs2.5J. (20) On the same page, line 11, after the "below" at the beginning, rCa. Insert "Mg 64% or less, Si 5% or less, 0.02% or less". (that's all)

Claims (1)

[Scope of Claims] 8 to 30% R (wherein R is at least one rare element including Y) in atomic percentage, 2 to 28% B, and one of the following two predetermined additive elements M Or two or more types (however, M
In cases where two or more of the above additive elements are included as M, excluding OX, the total amount of M consists of the atomic percentage of the one having the maximum value among the additive elements), and the balance Fe, and the average crystal grain of the sintered body Magnetic anisotropic sintered permanent magnet material with a diameter of 1 to 90 gm: Ti 4.5% or less, Ni 8.0% or more,
Bi 5.0X or less, v 8.5% or more, N
b 12.5% or less, Ta 10.5'X
Below, Cr 8.5% or less, No 9.5X
Below, W 9.5% or less, Mn 8. O
X or less, AI L5% or less, Sb 2.
5% or less, Ge 7.0% or less, Sn 3.
5% or less, Zr 5.5X or less, and Hf 5.5X or less.