JPH0474427B2 - - Google Patents

Description

[Detailed description of the invention]

[Technical Field] The present invention relates to a rare earth/iron permanent magnet material that does not use a large amount of cobalt Co, which is expensive and a scarce resource, and particularly relates to a sintered magnet material with improved press formability. [Technical background/prior art and its issues] Permanent magnetic materials are important electrical and electronic materials used in a wide range of fields, from various household electrical appliances to large computer terminal equipment.
In recent years, with the demand for smaller size and higher efficiency of electrical equipment, permanent magnet materials are required to be smaller and higher in performance. Current typical permanent magnet materials are alnico, hard ferrite, and rare earth cobalt-based magnet materials. With the recent instability in the raw material situation for cobalt, the demand for alnico magnet materials containing 20 to 30% by weight of cobalt has decreased, and inexpensive hard ferrite, whose main component is iron oxide, has become the mainstream magnet material. It became. On the other hand, rare earth cobalt magnet materials contain 50 to 65% by weight of cobalt and use Sm, which is not contained in rare earth ores, so they are very expensive, but they have better magnetic properties than other magnet materials. Because it is much more expensive, it has come to be used primarily in small, high-value-added magnetic circuits. In order for magnetic materials using rare earth elements to be used in large quantities and at low cost in a wide range of fields, it is necessary to
It is necessary that it does not contain expensive cobalt and that the main component is a light rare earth metal, which is contained in large amounts in ores. As one attempt at such a permanent magnet material, an RFe ₂ compound (where R is a symbol representing a rare earth element) was investigated. JJCroat has reported that an ultra-quenched ribbon of Pr _0.4 Fe _0.6 exhibits a coercive force of Hc = 2.8 kOe at 295 K (JJCroat Appl.Phys.Lett.37(12)15
December 1980, pp. 1096-1098). Then Nd _0.4
Even in the ultra-quenched ribbon with Fe _0.6 , Hc= at 295K
reported that it exhibits a coercive force of 7.45 kOe (J.
J.Croat Appl.Phys.Lett.39(4)15 August 1981,
pp. 357-358). However, these ultra-quenched ribbons
Both have low (BH)max (less than 4MGOe). Furthermore, NCKoon et al. (Fe _0.82
We found that when an ultra-quenched amorphous amorphous ribbon of La _0.26 ) _0.9 Tb _0.05 La _0.05 is annealed at 607°C, Hc reaches as high as 9 kOe (Br = 5 kG). However, in this case, the (BH)max is low due to the poor squareness of the magnetization curve (NCKoon et al., Appl.Phys.Lett.39(10),
1981, pp. 840-842). Also, L. Kabacoff et al _.
B _0.2 ) An ultra-quenched amorphous ribbon with a composition of _{1-X Pr}
It has been reported that it has an Hc of about 50e. (L.
Kabakoff et al.: J.Appl.Phys.53(3)March 1982,
(pp. 2255-2257). Most of the ultra-quenched ribbons listed above have light rare earths as their main components, but all of them have lower (BH)max than conventionally used permanent magnet materials, so they cannot be used as practical permanent magnet materials. It was difficult to do so. In addition, these ultra-quenched ribbons are not practical permanent magnets (body) that can be used in general speakers, motors, etc.
It has not been possible to obtain practical permanent magnets having arbitrary shapes and dimensions from these ribbons. The basic object of the present invention is to provide a new practical permanent magnet material that should meet such demands, particularly one useful as a magnetically anisotropic permanent magnet material. In particular, the purpose is to obtain a material mainly composed of Fe, which can effectively use resource-rich light rare earth elements as R. As such a permanent magnet material, the present inventors first developed a completely new type of practical permanent magnet material that requires specific rare earth elements, mainly Nd and Pr, and Fe and B in a specific ratio. was developed and filed by the same applicant as the present application.
(Unexamined Japanese Patent Publication No. 59-46008)). In this FeBR ternary permanent magnet material, boron (B) is not added as a conventional amorphous promoting element when creating an amorphous alloy or a sintering promoting element in a powder metallurgy method. Magnetically stable and with high magnetic anisotropy above room temperature, which is the base of FeBR ternary alloy
It is an essential constituent element of the RFeB ternary compound. This alloy has a sufficiently high Curie temperature (approximately 300°C or higher) for practical use. The FeBR ternary permanent magnet material mentioned above is not necessarily Co.
In addition, as R, light rare earths mainly consisting of Nd and Pr, which are abundant in resources, can be used, and since Sm is not necessarily required or does not need to be mainly Sm, the raw material is inexpensive. Yes, and extremely useful. Furthermore, the magnetic properties of this FeBR-based magnetically anisotropic sintered permanent magnet are superior to those of hard ferrite magnets (coercive force iHc≧1kOe, residual magnetic flux density Br≧4kG, maximum energy product (BH) max≧
4MGOe) In a particularly preferred composition range, it can exhibit an extremely high energy product equal to or higher than that of rare earth cobalt magnets. As mentioned above, this FeBR-based permanent magnet material is a new permanent magnet material that can replace conventional alnico and rare earth cobalt magnet materials.
Curie point (temperature) of FeBR ternary permanent magnet material
is generally 300℃ as disclosed in the patent application No. 57-145072.
The maximum temperature is 370℃ before and after. This Kyrie point is approximately
This is considerably lower than the Kyrie point of 800°C. Therefore, the magnetic properties of FeBR-based permanent magnet materials have greater temperature dependence than conventional alnico-based and RCo-based magnet materials, and magnetic properties deteriorate at high temperatures. According to the results of the inventor's research,
Since the temperature characteristics of FeBR-based sintered magnet materials deteriorate when used at temperatures above about 100°C, it was found that it is appropriate to use them within the normal temperature range of about 70°C or below. As described above, the large temperature dependence of the magnetic properties of permanent magnet materials, that is, the low Curie point, narrows the range of their use. It was necessary to raise the temperature and improve the temperature characteristics. From this point of view, the same applicant as the present application developed and applied for FeCoBR permanent magnet material with improved temperature characteristics of FeBR permanent magnet material (Japanese Patent Application No. 57-166663
(Unexamined Japanese Patent Publication No. 59-64733)). Also, in recent years, permanent magnet materials have been exposed to increasingly harsh environments, such as strong demagnetizing fields due to thinner magnets.
In addition to strong reverse magnetic fields applied by coils and other magnets, devices are often exposed to high-temperature environments due to faster speeds and higher loads, and in order to stabilize characteristics in many applications. (In general, the iHc of a permanent magnet material decreases as the temperature rises. Therefore, if the iHc at room temperature is small, demagnetization will occur when the permanent magnet material is exposed to high temperatures.) However, if iHc at room temperature is high enough, such demagnetization will not occur substantially). From this perspective, the same applicant as the present application has proposed FeBRM-based and FeCoBRM-based permanent magnet materials (M is Al, Ti, V, Cr, Mn, Zr, Hf) that can further improve the coercive force of FeBR-based and FeCoBR-based permanent magnet materials. ,Nb,
Ta, Mo, Ge, Sb, Sn, Bi, Ni, W) was developed and applied for (Japanese Patent Application No. 57-200204
-89401); Japanese Patent Application No. 58-5813 (Japanese Patent Application No. 59-132104)
issue)). These FeBR-based permanent magnet materials are completely new practical materials that can replace traditional alnico and rare earth magnet materials, and are typically made by melting, cooling, and casting an alloy of a predetermined composition, and then producing a powdered alloy. Manufactured by molding and sintering. In this case, since FeBR-based sintered permanent magnets are high-performance magnets, they are often used in small electrical devices, and their unit weight during press molding is extremely small at 0.5 to 5.0 g.
The accompanying improvements in press cycles and die life greatly contribute to improving production efficiency and reducing manufacturing costs of this magnet system. However, FeBR
When manufacturing the base sintered magnet using the powder metallurgy method described above, both dry pressing and wet pressing can be used to form the magnet. Due to the large size, there are drawbacks such as a decrease in raw material cost and yield, and an increase in the complexity of the processing process in the final manufacturing process. On the other hand, in dry presses, the raw material powder tends to get stuck between the dies and punches, which shortens the life of the expensive dies and punches, so in general, a release agent is applied to the dies and punches every predetermined number of presses. This is done to improve the mold release properties of the powder, but this increases the process of applying the mold release agent, so the smaller the unit weight and the more times the product is pressed, the better the product will be.
The problem was that the press cycle was significantly reduced. A further object of the present invention is therefore to further improve the press formability of FeBR-based sintered magnet materials during production without compromising the high performance magnetic properties. [Means for solving the problem, effects, and effects] As a result of intensive studies by the present inventors to improve these press formability, we found that FeBR-based, FeCoBR-based,
Additive elements such as Li, Zn, In,
It has been found that press formability is improved by adding one or more of Ag, Sn, and Pb in a predetermined amount or less. That is, the present inventor achieved the above object by the following means. Rare earth elements R with an atomic percentage of 8 to 30% (however, R
is at least one kind of rare earth element including Y),
The main components are 2 to 28% B and 65 to 82% Fe, and if desired, a part of Fe can be added to less than 25% of the total composition.
Co, and if desired, one or more additive elements M below the specified amount below (the additive element M is
Except M0%, Al 9.5%, Ti 4.5%, V 9.5%, Cr 8.5%, Mn 8.0%, Zr 5.5%, Hf 5.5%, Nb 12.5%, Ta 10.5%, Mo 9.5%, Ge 7.0%, Sb 2.5%, Sn 3.5%, Bi 5.0%, Ni 8.0%, and W 9.5%, and when two or more types of M are included, the total amount of M is the maximum of the above values of each additional element of M contained. Must be less than or equal to the value. ), the sintered magnet material is characterized by containing one or more additive elements A in the following predetermined amounts or less: However, the additive element A does not exceed 0% of A. , Li 0.5%, Zn 2.0%, In 1.0%, Ag 2.0%, Sn 2.0%, Pb 2.0% (excluding the addition of Sn alone), and when two or more types of additive elements A are included, the The total amount shall be equal to or less than the maximum value of the above-mentioned values of each of the additive elements contained in A, and when Sn is included as the additive elements M and A, the total amount of Sn shall be equal to or less than 3.5%. According to the Fe(Co)BR(M)-based sintered magnet material of the present invention, it is possible to improve the apparent density of the starting raw material powder and reduce the punch release pressure during production, thereby shortening the press cycle and die life. Press formability such as improvement can be considerably improved. Of course, good magnetic properties as a Fe(Co)BR(M)-based magnet material are sufficiently ensured as shown by the data described below. [Preferred Embodiment] The present invention will be described in further detail below. The rare earth element R content is set to 8% or more in order to increase the coercive force to 1 kOe or more, and is set to 30% or less because its nature makes it easily flammable and difficult to handle and manufacture industrially, and it is also expensive. The B content is 2 to obtain a coercive force of 1 kOe or more.
% or more, and the residual magnetic flux density (Br) of hard ferrite is 28% or less in order to make it 4kG or more. The content of Fe is 65 to 82%. Fe content is
When it exceeds 82%, the coercive force becomes less than 1kOe, while
If it is less than 65%, the residual magnetic flux density (Br)
This is because it is less than 4kG. The maximum energy product (BH) max of such a sintered magnet of the present invention is that of a hard ferrite magnet (~
4MGOe) or higher. Additive element A has the effect of improving the apparent density of the powder during press molding, improving the press cycle, improving the life of the die, and further reducing the so-called extraction pressure during punch extrusion, contributing to the improvement of the life of the die. Additive element A is the predetermined amount Li0.5%, Zn2%,
If the content exceeds 1.0% In, 2.0% Ag, 2.0% Sn, and 2.0% Pb, the alloy will become sticky, so if the ingot method is used, the grinding time of the alloy will be longer, resulting in less industrial merit. decreases. A preferable effective addition amount is about 0.05% or more in total of A, and about 0.05% or more for each additive element, and more preferably 0.1% or more in total of A.
When used alone, each additive element is contained in an amount of 0.1% or more. In addition, since additive element A has the effect of improving the tap density of powder during press molding, the cycle of powder supply to the die is improved, and the filling of the powder into the supply hopper is improved, which leads to press molding. It significantly contributes to improving efficiency and productivity. A more preferable composition range for FeBR includes light rare earth elements (particularly Nd, Pr) of 50% or more of the total R, and 11 to 24% of R, 3 to 27% of B, and
The main component is 68 to 80% Fe, and the additive elements A are Li 0.3% or less, Zn 1.5% or less, In 0.8% or less, Ag 1.5% or less, Sn 1.5% or less, and Pb 1.5% or less (however, In cases where more than one type of additive element A is included, the total amount of A shall be less than or equal to the atomic percentage of the element having the maximum value among the respective elements of A contained. In this case, the maximum energy product (BH) max will be 7MGOe or more. Furthermore, the most desirable composition range for FeBR that has excellent magnetic properties, press formability, and industrial productivity is light rare earth elements (particularly Nd and Pr).
containing 50% or more of the total R, and 12 to 20% of R,
The main components are 4-24% B, 70-78% Fe, and the additive elements A are Li 0.2% or less, Zn 1.0% or less, In 0.5% or less, Ag 1.0% or less, Sn 1.0% or less, Pb 1.0%. In the case where two or more types of additive elements A are included, the total amount of A is equal to or less than the atomic percentage of the element having the maximum value among the respective elements of A contained. The maximum energy product (BH) max in this case is more than 10MGOe, and the highest energy product reaches more than 38MGOe. The sintered magnet material of the present invention can be manufactured using industrially available materials, and the following metals can be used as starting materials. The central elements of R are Nd and Pr. Nd,
In terms of resources, Pr is more abundant than Sm, etc., and there are generally few uses for it, so there is a surplus.
It is extremely advantageous to use such a light rare earth element as a central element in the alloy for permanent magnets of the present invention. In addition to Nd and Pr, R includes La, Ce, Tb,
Dy, Ho, Er, Eu, Sm, Gd, Pm, Tm, Yb,
Lu and Y are included. R is usually Nd,
It is sufficient to have one or two types of Pr, but these
Other Dy, Ho, with Nd, Pr being 50% or more of R
At least one of Tb, La, Ce, Gd, and Y can be used as a mixture. In practice, a mixture of two or more types (Mitsushimetal, didymium, etc.) can be used for reasons such as convenience of availability. Note that this R does not have to be a pure rare earth element, and may contain impurities that are unavoidable in manufacturing (other rare earth elements, Ca, Mg, Fe, Ti, C, O, etc.) within the industrially available range. do not have. As described above, the present invention is extremely advantageous in that R that is industrially easily available can be mainly used. As B (boron), pure boron or ferroboron can be used, and as impurities Al, Si,
Those containing C or the like can also be used. As Co, commercially available industrial grade Co can be used. [Manufacturing Example] Next, an example of manufacturing the sintered magnet material of the present invention will be explained in the case of a magnetically anisotropic magnet. Other similar manufacturing methods can be adopted. Fe as a starting material is electrolytic iron with a purity of 99.9wt% or more, B is ferroboron or boron with a purity of 99wt% or more, R is a purity of 99.7wt% or more, and additive element A is a purity
Use 98wt% or more. The alloy is obtained by arc melting or radio frequency melting and casting into water-cooled copper molds. Grinding is done by stamp mill.
Coarsely pulverize to 35 meshes (500 μm) through, and then finely pulverize to 0.5 to 10 μm using a ball mill. For press forming, apply a magnetic field of 8kOe or more to
Pressurize at ~2.5ton/ ^cm2 . Sintering at 1000-1200℃
The test is carried out in an Ar atmosphere at a temperature of 0.5 to 4 hours. Further, an aging treatment is performed in an Ar atmosphere at a temperature ranging from 350° C. to the sintering temperature for 0.5 to 8 hours to obtain the alloy magnet of the present system. [Examples] Hereinafter, in order to clarify the effects of the present invention, several examples will be given and compared with comparative examples of peripheral compositions. Example 1 An alloy having the following atomic percentage was weighed, high-frequency melted in argon, cast, and coarsely ground to 40 mesh (420 μm) or less using a stamp mill, and then 2 to 5 μm thick.
The powder was finely ground to obtain an alloy powder. The apparent density, tap density, and ejection pressure of the obtained alloy powder were measured using an Amsler press. This powder was pressure-molded at 1.0t/cm ² in a 10kOe magnetic field to obtain a compact.
It was sintered at 1100°C for 2 hours in Ar with a purity of 99.99wt% and cooled to room temperature. Further, an aging treatment was performed at 550°C for 4 hours to obtain this alloy magnet. The results are shown in Table 1. Example 2 An alloy having the following atomic percentages was weighed, high-frequency melted in argon, cast, and coarsely ground to 40 mesh or less using a stamp mill, and then finely ground to 2 to 5 μm to obtain an alloy powder. The apparent density, tap density, and ejection pressure of the obtained alloy powder were measured using an Amsler press. This powder is placed in a 15kOe magnetic field.
After molding at 1.2t/ ^cm2 to obtain a molded body, 99.99wt
% purity Ar at 1120°C for 2 hours and cooled to room temperature. Further, aging treatment was performed at 650°C for 2 hours to obtain this alloy magnet. The results are shown in Table 2. Example 3 An alloy having the following atomic percentage was weighed, high-frequency melted and cast in argon, and then coarsely ground to 40 mesh or less using a stamp mill, and then finely ground to 2 to 5 μm to obtain an alloy powder. The apparent density, tap density, and ejection pressure of the obtained alloy powder were measured using an Amsler press. This powder is placed in a 10kOe magnetic field.
After molding at 1.0t/ ^cm2 to obtain a molded body, 99.99wt
% purity Ar at 1100°C for 2 hours and cooled to room temperature. Further, an aging treatment was performed at 600°C for 2 hours to obtain an alloy magnet of this type. The results are shown in Table 3. Example 4 An alloy having the following atomic percentage was weighed, high-frequency melted in argon, cast, and then coarsely ground to 40 mesh or less using a stamp mill, and then finely ground to 2 to 5 μm to obtain an alloy powder. The apparent density, tap density, and ejection pressure of the obtained alloy powder were measured using an Amsler press. This powder is placed in a 10kOe magnetic field.
After molding at 1.5t/ ^cm2 to obtain a molded body, 99.99wt
% purity Ar at 1080°C for 2 hours and cooled to room temperature. Further, an aging treatment was performed at 650°C for 2 hours to obtain this alloy magnet. The results are shown in Table 4. Example 5 An alloy having the following atomic percentage was weighed, high-frequency melted in argon, cast, and then coarsely ground to 40 mesh or less using a stamp mill, and then finely ground to 2 to 5 μm to obtain an alloy powder. The apparent density, tap density, and ejection pressure of the obtained alloy powder were measured using an Amsler press. This powder is 1.0t/cm ² in no magnetic field.
After molding to obtain a molded body, it is
It was sintered in Ar at 1120°C for 2 hours and cooled to room temperature.
Further, an aging treatment was performed at 650°C for 2 hours to obtain this alloy magnet. The results are shown in Table 5.

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[Table] As shown in the experimental results of the above comparative test, by adding a predetermined amount of additive element A to the Fe(Co)BR alloy powder, the apparent density of the alloy powder as a starting material can be increased. It can be seen that the examples are also significantly improved compared to the comparative examples. In conjunction with this, it was possible to increase the tap density during press molding, and it was also possible to considerably reduce the extraction pressure during punch extrusion. In addition, in the above embodiments, mainly FeBR ternary system, Fe
Although we have described the FeCoBR system in which a part of is replaced with Co, the effect of improving press formability by the additive element A of the present invention is further enhanced by the addition of a predetermined additive element M (Al, Ti,
V, Cr, Mn, Zr, Hf, Nb, Ta, Mo, Ge,
Fe with a specified amount of Sb, Sn, Bi, Ni, W) added
It is also recognized in the (Co)BRM system. Furthermore, the sintered alloy of the present invention is of course superior in terms of magnetic properties, and as shown in the above experimental results, the sintered alloy of the present invention is superior in magnetic properties.
Coercive force iHc and maximum energy product (BH) max equivalent to or higher than (Co)BR(M) based sintered magnets
etc. In addition, the permanent magnet material of the present invention contains Cu, S, C, P, Ca, Mg,
It may contain elements (x) such as O and Si, especially Cu3.5% or less, S2.0% or less, C4.0% or less, P3.0
% or less, Ca4.0% or less, Mg4.0% or less, O2.0% or less, and Si5.0% or less are practically preferable. In addition, in the state of alloy powder, adsorbed components (moisture, oxygen, etc.) from air during processing are likely to be included, but these can be removed during sintering. However, care should be taken in processing and storage as necessary. Some of the Fe, which is the main component of the FeBRA alloy of the present invention, is replaced by Co.
By replacing it with , the Curie point can be raised and the temperature characteristics can be improved. In Co substitution of Fe, Co
As the amount of Co substitution increases, the Curie point increases rapidly regardless of R, so the temperature characteristics are improved by an arbitrary amount depending on the amount of Co substitution. When Co is less than 25%, the Curie point increases without adversely affecting other magnetic properties, and when Co is more than 5%, the temperature coefficient of Br is approximately 0.1.
%/℃. Co is effective even in small amounts (for example, 0.1 to 1%). In addition, the following additive elements M (M is Al, Ti, V, Cr, Mn,
Zr, Hf, Nb, Ta, Mo, Ge, Sb, Sn, Bi,
Coercive force can be increased by adding a predetermined amount of one or more types of Ni and W.
This permanent magnet can be used not only in applications where strong demagnetizing fields or reverse magnetic fields are applied, but also in applications where it is used in high-temperature environments. The amount of the additional element M is: Al 9.5% or less, Ti 4.5% or less, V 9.5% or less, Cr 8.5% or less, Mn 8.0% or less, Zr 5.5% or less, Hf 5.5% or less, Nb 12.5% or less, Ta 10.5% Below, Mo is 9.5% or less, Ge is 7.0% or less, Sb is 2.5% or less, Sn is 3.5% or less, Bi is 5.0% or less, Ni is 8.0% or less, and W is 9.5% or less. Here, when two or more types of M are used, the total amount of M is set to be less than % of the one having the maximum value among the added elements, and each of them is set to be less than the above-mentioned predetermined value. Also,
Regarding Sn, the total amount of additive elements M and A must be 3.5% or less. When the content of M exceeds the predetermined value, the residual magnetic flux density increases.
Since it deteriorates to less than Br4kG, it cannot be used as a practical permanent magnet. [Effects of the Invention] As detailed above, the present invention is a novel sintered magnet material, that is, mainly Fe-based, and also contains rare earth elements (Nd, R, which are abundant in resources and industrially easy to obtain).
This is a sintered magnet material based on a (Fe, Co)BR compound mainly composed of Pr), and is particularly useful as a magnetically anisotropic permanent magnet material. By using this, it has magnetic properties superior to hard ferrite,
Fe(Co)BR(M)A, which can also be used as a substitute for SmCo-based materials
This makes it possible to provide a system magnetically anisotropic sintered permanent magnet, which has extremely high industrial value. In particular, the advantage as a permanent magnet material is that
When compared with the SmCo system, it becomes extremely remarkable in terms of its main constituent elements. In addition, some Fe may be added if desired.
By substituting with Co, the sintered magnet has a sufficiently high Curie point for practical use, and by containing a specific additive element M, it is possible to increase the coercive force of the sintered magnet.
Furthermore, by allowing the presence of elements such as Cu, S, C, and P, it is possible to use raw materials with low purity, and it can be manufactured at low cost. Furthermore, the inclusion of additive element A can increase the apparent density of the raw material powder and reduce the punching pressure, which can significantly improve press formability, such as increasing the press cycle and die life, which is extremely advantageous industrially and has practical value. It can contribute to increasing the

Claims (1)

[Scope of Claims] 1. 8 to 30% by atomic percentage of a rare earth element R (wherein R is at least one kind of rare earth element including Y),
A sintered magnet material whose main components are 2 to 28% B and 65 to 82% Fe, which is characterized by containing one or more additive elements A in the following predetermined amounts or less: : However, the additive elements A are, excluding A0%, Li 0.5%, Zn 2.0%, In 1.0%, Ag 2.0%, Sn 2.0%, Pb 2.0% (excluding the addition of Sn alone), and two or more types. When the additive element A is included, the total amount of the additive element A is less than or equal to the maximum value of the above-mentioned values of each of the additive elements contained in A. 2 8 to 30% atomic percentage of rare earth element R (however, R is at least one kind of rare earth element including Y),
The main components are 2-28% B, 65-82% Fe, and Fe
25% or less of the total composition (however, Co0
%), the sintered magnet material is characterized by containing one or more additive elements A in the following predetermined amounts or less: However, the additive element A is A0 %, Li 0.5%, Zn 2.0%, In 1.0%, Ag 2.0%, Sn 2.0%, Pb 2.0% (excluding the addition of Sn alone), and if two or more types of additive elements A are included, the additive elements The total amount of A is less than or equal to the maximum value of the above values of each of the added elements contained in A. 3 8 to 30% atomic percentage of rare earth element R (however, R is at least one kind of rare earth element including Y),
The main components are 2 to 28% B, 65 to 82% Fe, and one or more additional elements M are below the specified amounts below (Additional elements M are excluding M0%, Al 9.5%, Ti 4.5% , V 9.5%, Cr 8.5%, Mn 8.0%, Zr 5.5%, Hf 5.5%, Nb 12.5%, Ta 10.5%, Mo 9.5%, Ge 7.0%, Sb 2.5%, Sn 3.5%, Bi 5.0%, Ni 8.0%, and W 9.5%, and if two or more types of M are included, the total amount of M shall be less than or equal to the maximum value of the above values of each additional element of the M contained. A sintered magnet material characterized by containing one or more additive elements A in the following predetermined amounts: However, the additive elements A include 0.5% Li, 2.0% Zn, excluding 0% A. %, In 1.0%, Ag 2.0%, Sn 2.0%, Pb 2.0% (excluding the addition of Sn alone), and when two or more types of additive elements A are included, the total amount of A is the corresponding amount of each addition of A contained. Below the maximum value of the above values for the elements, and as additional elements M and A.
If Sn is included, the total amount of Sn should be 3.5% or less. 4 8 to 30% atomic percentage of rare earth element R (however, R is at least one kind of rare earth element including Y),
The main components are 2 to 28% B, 65 to 82% Fe, and one or more additional elements M are below the specified amounts below (Additional elements M are excluding M0%, Al 9.5%, Ti 4.5% , V 9.5%, Cr 8.5%, Mn 8.0%, Zr 5.5%, Hf 5.5%, Nb 12.5%, Ta 10.5%, Mo 9.5%, Ge 7.0%, Sb 2.5%, Sn 3.5%, Bi 5.0%, Ni 8.0%, and W 9.5%, and if two or more types of M are included, the total amount of M shall be less than or equal to the maximum value of the above values of each additional element of the M contained, A sintered magnet material in which a part of Fe is replaced with 25% or less Co (excluding 0% Co) based on the total composition, containing one or more additive elements A in the following specified amounts or less: A sintered magnet material characterized by: However, the additive elements A are 0.5% Li, 2.0% Zn, 2.0% In, 2.0% Sn, 2.0% Sn, and 2.0% Pb (except for Sn alone). ), and when two or more types of additive elements A are included, the total amount of A shall be less than or equal to the maximum value of the above values of each of the additive elements contained in A, and Sn as the additive elements M and A. If Sn is included, the total amount of Sn shall be 3.5% or less.