JPS63241142A - Ferromagnetic alloy - Google Patents

Abstract

PURPOSE:To provide a ferromagnetic alloy useful as permanent magnet material, by incorporating specific amounts of rare-earth elements, such as Nd and Pr, and B into an iron base which is partly substituted by Co so as to increase coercive force, etc. CONSTITUTION:An Fe-B-R-M ferromagnetic alloy has a composition which consists of, by atomic percentage, 8-30% R (Nd and/or Pr), 2-28% B, one or more additive elements M among <=9.5% Al, <=4.5% Ti, <=9.5% V, <=8.5% Cr, <=8% Mn, <=5.5% Zr, <=5.5% Hf, <=12.5% Nb, <=10.5% Ta, <=9.5% Mo, <=7% Ge, <=2.5% Sb, <=3.5% Sn, <=5% Bi, <=8% Ni, and <=9.5% W, and the balance essentially Fe and in which a part of Fe is substituted by <=50% Co based on the whole composition. Moreover, if necessary, Nd and Pr content in R is regulated to >=50% and one or more elements among Dy, Ho, Tb, La, Ce, Gd, and Y are incorporated.

Description

DETAILED DESCRIPTION OF THE INVENTION The present invention relates to a ferromagnetic alloy mainly containing Fe and rare earth elements, and particularly to a novel Co-added Fe-BR-based ferromagnetic alloy.

Permanent magnet materials have been known as one of the ferromagnetic alloys. Permanent magnet materials are used in various household electrical appliances.
It is one of the extremely important electrical and electronic materials used in a wide range of fields, including peripheral terminals for large computers. With the recent demand for smaller size and higher efficiency of electrical and electronic equipment, permanent magnet materials are required to have even higher performance.

Current typical permanent magnet materials are alnico, hard ferrite, and rare earth cobalt based magnet materials. Due to the recent instability in the raw material situation for cobalt,
The demand for alnico magnet materials containing 0 to 30% by weight has decreased, and inexpensive hard ferrites containing iron oxide as a main component have become the mainstream of magnet materials. On the other hand, rare earth cobalt-based magnet materials contain 50 to 65% by weight of cobalt and use Sm, which is not included in rare earth ores, so they are very expensive compared to other magnet materials.

Because of its extremely high magnetic properties, it has come to be used mainly in small, high-value-added magnetic circuits.

In order for magnetic materials using rare earth elements to be used in a wider range of fields at low cost and in large quantities.

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. + RF e Z-based compounds (where R is a symbol representing a rare earth element) have been studied as one attempt at such a permanent magnet material.

Croat (J, J, Croat) is Pr Fe
reported that a super-0.4 0.6 quenched ribbon exhibits a coercive force of He-2,8 kOc at 295 K (J, J, Croat
Appl.

Phys, Lctt, 37 (12) 15 De
cember 1980. pp. 1098-1098). After that, NdFe super-quenched ribo 0.40.
It has been reported that the coercive force of Hc = 7.45 koc is exhibited at 295 K even at 800 nm (J, J, Cro
at Appl.

Pbys, Lett, 39 (4) 15 Aug.
st 1981.357-35B). However, all of these ultra-quenched ribbons have low (Bll) wax (less than 4 MGOe).

Furthermore, Kuhn (N, C, Koon) et al.
82) It was found that when an ultra-quenched amorphous 0.18 0.9 0.05 0.05 ribbon of TbLa is annealed at 627°C, it reaches lie -9koe (Br -5kG). However, in this case, because the squareness of the magnetization curve is poor (I311) wax
is low (N, C, Koon et al., Appl, Ph
ys, t, ctt, 39(10), 1981.8
40-842).

In addition, Kabakotsu (L, Kabacorf') etc. are (F
e o, gB ) Pr (x=o~0.
reported that an ultra-quenched amorphous ribbon with a composition of 0.2 1-X (
L, Kabakol'r et al.: J, Appl.
Phys, 53 (3) Marcb 1982.22
55-2257).

Most of the ultra-quenched ribbons shown in J- below are mainly composed of light rare earths, but all of them have (all)o+ax compared to conventional permanent magnet materials.
was difficult to use as a practical permanent magnet material. In addition, these ultra-quenched ribbons themselves can be used as practical permanent magnets (
However, it was not possible to obtain a practical permanent magnet with the desired shape and dimensions from these ribbons.

The basic object of the present invention is to provide a novel ferromagnetic alloy that should meet such demands, particularly one useful as a permanent magnet material. In particular, the object is to obtain a material that is mainly composed of Fe and can effectively use light rare earth elements, which are abundant in resources, as R.

The present inventor has previously developed two such ferromagnetic alloys, including Nd
, a ferromagnetic alloy that essentially includes a specific rare earth element characterized by Pr, and Fe and B in a specific ratio, and particularly has magnetic anisotropy or the ability to orient in a magnetic field. Developed a completely new type of practical ferromagnetic alloy.

Filed by the same applicant as the present application (Japanese Patent Application No. 57-145
Patent application No. 59-246897 as a divisional application of No. 072)
.

In this Fe-B-R ternary alloy, boron (B)
is not added as a non-quality promoting element in the production of an amorphous alloy or as a sintering promoting element in powder metallurgy, but is added as a base material for Fe-B-R ternary alloy at room temperature or above. R- which is magnetically stable and has high magnetic anisotropy
It is an essential constituent element of the Fe-B ternary compound. This alloy has a Curie temperature of 3 degrees (approximately 300° C. or higher) which is sufficiently high for practical use.

The above-mentioned Fe-B-R ternary ferromagnetic alloy does not necessarily need to contain Co, and as R, Nd, which is rich in resources,
It is possible to use a light rare earth element mainly composed of Pr, and it does not necessarily require Sm or need to be mainly composed of Sm, so the raw material is inexpensive, and it is very suitable for A. Moreover,
The magnetic properties of the Fe-B-R magnetically anisotropic sintered permanent magnet obtained using this ferromagnetic alloy are better than those of hard ferrite magnets. , maximum energy product (Bll)s
ax≧4MGOe) In a particularly preferred composition range, it can exhibit an extremely high energy product equivalent to or higher than that of a rare earth cobalt magnet.

As mentioned above, this Fe-B-R ferromagnetic alloy is a new ferromagnetic alloy that can replace conventional alnico and rare earth cobalt magnet materials. One point (temperature) is a patent application filed in 1984-246.
As disclosed in 897, generally around 300℃, maximum 370℃
It is. This curie is a traditional alnico or R
This is considerably lower than the Curie point of about 800° C. for -Co-based permanent magnet materials. Therefore, the Fe-B-R permanent magnet (Jr material) is different from conventional alnico or R-Co.
The temperature dependence of the magnetic properties is greater than that of other magnets (materials), and the magnetic properties deteriorate at high temperatures. According to the results of research conducted by the present inventor, Fe-B-R based sintered magnets (materials) deteriorate in temperature characteristics when used at temperatures above about 100°C. It was found to be suitable for use in

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, and in order to use Fe-B-R permanent magnet materials in a wide range of applications. It was necessary to improve the temperature characteristics by raising the temperature by one point.

Another object of the present invention is to improve the temperature characteristics of such Fe-B-R permanent magnet materials.

In the present invention, in order to improve the Curie temperature in a Fe-BR-based ferromagnetic alloy, a part of Fe is replaced with C.

It has been found that it is effective to substitute with Ai, Ti, V, Cr, Mn, Zr.

Hf, Nb, Ta, Mo, Ge, Sb, Sn.

By adding a specific additive element M selected from the group consisting of Bi, Ni, and W at a predetermined percentage, the same as the Fe-B-R ternary ferromagnetic alloy according to the previous application (Japanese Patent Application No. 57-145072) can be obtained. This is to achieve the above-mentioned purpose.

That is, one ferromagnetic alloy of the present invention is as follows.

First invention: R (R is one or two of Nd and Pr) 8 to 30%, 82 to 28% in atomic percentage, below the specified % (0
%) doped light f: one or more types of M (however, when there are two or more types of added elements M, the total amount of 1M is not more than the specified % of the maximum specified % of the added elements), and A ferromagnetic alloy characterized in that the remainder substantially consists of Fe, and a portion of the Fe is replaced with 50% or less (excluding 0%) of the total composition; A 9.5%, Ti4 .5%.

■9.5%, Cr8.5%.

Mn 8%, Zr 5.5%.

Hf 5.5%, Nb 12.5%.

Ta 10.5%, Mo 9.5%.

Ge 7%, Sb 2.5%.

Sn3.5%, Bi5%.

Ni 8% and W 9.5%゜Second invention: R in atomic percentage (R is Nd, Pr.

At least one of Dy, Ha, Tb, La, Ce, Gd, Y, and 50% or more of R is one or two of Nd and Pr) 8-30%, 82-28%, below the specified percentage (
(excluding 0%) of one or more of the additive elements M (however, if there are two or more types of additive elements M, the total amount of 9M is the maximum prescribed % of the said additive elements but not more than the prescribed %), and the remainder A ferromagnetic alloy consisting essentially of Fe, characterized in that a part of the Fe is replaced with 50% or less (excluding 0%) of the total composition (the predetermined percentage of the additive element M is the first same as in invention).

Practical permanent magnets can be manufactured using the Fe-Co-B-R-M alloy of the present invention, similar to the Fe-B-R alloy according to the applicant's earlier application. For example, 9 alloys are melted and cooled 1. For example, by casting the resulting alloy, pulverizing the resulting alloy, and then forming and sintering it in a magnetic field to form an appropriate microstructure, it is possible to most effectively produce a practical high-performance permanent magnet. can be obtained.

In the present invention, a part of Fe is 50% of the total composition.
(Fe, Co)-B by substituting with Co below
Novel Fe-Co-B-R- based on -R compound
The present invention provides an M-based ferromagnetic alloy.

By containing this Co, it is possible to provide a sufficiently high Curie point for practical use based on the Fe-B-R system and reduce temperature dependence. Furthermore, by adding a predetermined amount of M, it is possible to provide a completely new ferromagnetic alloy that has magnetic properties (coercive force, etc.) that are equivalent or superior to conventional hard ferrite magnetic materials, similar to the Fe-B-R ternary system. . M is as described above (A, g, Ti, V, Cr, Mn, Ni, Ge.

Nb, Mo, Sb, Sn, Zr, Hf, Ta.

There are W and Bi, and one or more of them are used. In addition, 111c generally decreases as the temperature rises, but among the above M, V, Ta, Nb, Cr, and W.

By increasing the l Hc at room temperature by including MO, A, 5, etc., it is possible to substantially prevent demagnetization even when exposed to high temperatures. Therefore.

Harsh environments 2 For example, strong demagnetizing fields due to thinner magnets, strong reverse magnetic fields applied by coils and other magnets 2 In addition to these, exposure to high-temperature environments due to higher speeds and higher loads of equipment, etc. The present invention provides four permanent magnetic materials that are suitable for use in the following applications. Like the Fe-B-R ternary system, the Fe-Co-B-R-M alloy of the present invention exhibits a high anisotropic magnetic field and has the ability to orient in a magnetic field, so it is particularly suitable as a material for anisotropic magnets. It is for use.

In addition, when two or more types of M are used, the total amount of 1M is as follows.

The maximum predetermined value of the additive elements is set to a predetermined percentage or less of the additive, and each of the additive elements is set to be below the predetermined value.

In addition, the addition of M increases the residual magnetization B in each embodiment.
The content of 1M is because it causes a gradual decrease in r.

At least the residual magnetization Br is higher than that of conventional hard ferrite.
The object of the present invention is to provide a magnetically anisotropic magnet having a coercive force equivalent to or higher than that of conventional products. Thus, the alloy of the present invention has magnetic properties equivalent to or better than conventional ferrite magnets (energy product of approximately 4 M
GOc or higher) can be provided.

In the ferromagnetic alloy of the present invention, regardless of its form, in addition to materials for permanent magnets in known forms such as ingots or powder,
It also includes permanent magnetic materials in any form.

The reasons for limiting the composition range of the ferromagnetic alloy of the present invention will be explained in detail in the Examples described below, but especially when the present invention is used most effectively, that is, when used as a magnetically anisotropic sintered permanent magnet. We selected a composition range that would allow us to obtain magnetic properties equivalent to or better than hard ferrite.

In the Fe-Co-BRM-based alloy of the present invention, R,
The composition range of B is determined basically in the same manner as in the case of the Fe-B-R alloy according to the second applicant's earlier application. That is, in order to satisfy the coercive force 111c≧1 koc when made into an anisotropic sintered body, B should be 2% or more (atomic ratio, the same applies below unless otherwise specified), and the residual magnetic flux density Br of hard ferrite (approximately 4
KG) or more, B should be 28% or less. R is required to be 8% or more in order to make the coercive force 1 koc or more, and because it is easily flammable and difficult to industrially handle and manufacture, R is 3.
0% or less. In this B and R range, the maximum energy product (B If)ffiaX is equivalent to that of hard ferrite.

The ferromagnetic alloy of the present invention has an R of 8 to 30%, 2 to 28% as described above.
%B, balance Fe in the entire range, Co and additive element M
It has been recognized that the inclusion of Fe-B-R
Outside the range of , there is no q effect.

The ferromagnetic alloy of the present invention can be manufactured using industrially available materials, and the following metals can be used as starting materials.

Rare earth elements R include light rare earths, heavy rare earths, and Y
Rare earth elements that include
Use 2. That is, as this R.

Nd, Pr, La, Ce, Tb, Dy, Ho.

Er, Eu, Sm, Gd, Pm, Tm, Yb.

Lu and Y are included. As R, Nd.

One or two types of Pr are sufficient. Nd.

Pr is more abundant as a resource than Sm.

In addition, since there are generally few uses for these elements, there is a surplus, and it is extremely advantageous to use such a light rare earth element as a central element in the ferromagnetic alloy of the present invention. Furthermore, with these Nd and Pr at 50% or more of R, other Dy, Ho, T
b, La, Ce, Gd.

At least one type of Y can be mixed and used. Practically speaking, a mixture of two or more types (Mitsuhmetal, Didim, etc.) can be used for reasons such as availability. Note that this R does not have to be a pure rare earth element, but may contain impurities (other rare earth elements, Ca, etc.) that are unavoidable in production within an industrially available range.

There is no problem with the storage of Mg, Fe, Ti, C, O, etc.).

Pure boron or ferroboron can be used as B (boron), and AJ as an impurity.

Those containing St, C, etc. can also be used.

As Co, commercially available industrial grade Co can be used. Furthermore, an alloy consisting of two or more of these constituent elements can also be used.

Note that the ferromagnetic alloys of the present invention are C, S, P, and Ca.

The presence of impurities such as Mg, O, and Si that are unavoidable in industrial production can be tolerated. These impurities are often mixed in from raw materials or manufacturing processes, and the total amount of these impurities is preferably 5% or less. It is also possible to partially replace B with C, P, St, or the like.

<Examples> The present invention will be described in detail below with reference to experimental examples and examples, but the present invention is not limited thereto.

Fe-Co-BRM alloy containing various additive elements M (
(However, M is one or more types) Samples were prepared by the following method.

The alloy is radio-frequency melted and cast into water-cooled copper molds.

The starting materials used were Fe with a purity of 99% and 9% electrolytic iron, B with a ferroboron alloy and boron with a purity of 99%, R with a purity of 99.7% or more (impurities were mainly other rare earth metals), and Co with a purity of 99.7% or more. Electrolytic Co with a purity of 99 and 9% was used. As the additive element M, T with a purity of 99%
i, Mo, B i, Mn, Sb.

Ni, Ta, 98% W, 99.9% AJ, 95%
Hf, 99.9% Ge, Sn, and V as 81.
Ferrovanadium with 2% V, 67.6 as Nb
% Nb as ferroniobium, 61.9% Cr as ferrochrome and Zr as 75.5% Z
Ferrozirconium containing r was used (purity is % by weight); a permanent magnet sample was created using this alloy as follows.

(1) Coarsely pulverize to 35 mesh through using a Nistump mill, then finely pulverize into crystal grains that can be oriented in a magnetic field for 3 hours using a ball mill (3 to 1O); (2) Orientation and shaping in a magnetic field (1okoe) (L, 5t/C
(3) Sintering 1000-1200°C for 1 hour in Ar. Allow to cool after sintering.

1llc, Br for the above samples of various compositions.

(1311) As a result of a detailed investigation of the magnetic properties through measurements such as a a
It has been found that there are regions in the alloys that exhibit high permanent magnetic properties. (81,5-x) Fe-10Co-8 using a sample produced in the same manner as the above-mentioned process.
In the 8-xNd-0,5A,g system, X was varied from 0 to 40 to investigate the relationship between NdEilt and Dr, II[c. The results are shown in FIG. Furthermore, (7
4,5-x) Fe-IOc o -x B -15N
In the system of d -0,5A p, the relationship between BW, Dr, and l1lc was investigated by changing X to θ~35, and the results are shown in FIG. The basic tendency of B and R to Br and 111c in the Fe-Co-BRM system is as follows:
The case of rare earth elements other than Nd and M other than A1 is basically the same as that shown in Fig. 6.7. '>'S Table 1 shows the maximum energy product (B H) ta a x, which is the most important permanent magnet characteristic, for typical samples. In Table 1, Fe
is the remainder. In addition, when the characteristics of the alloy (powder state) after being finely pulverized in the process of creating the permanent magnet sample were investigated, 111c showed 1 koc or more.

From Table 1, it can be seen that the Fe-Co-BRM magnet has a high energy product of 10 MGOe or more over a wide composition range. This table mainly includes Nd, P
Although examples of alloys containing r have been listed, the alloys of the present invention are also good in combination with other predetermined R.

Indicates permanent magnet characteristics. However, as mentioned above, Nd and P
r is contained in relatively large amounts in rare earth ores, and Nd in particular has not yet been known to be used in large quantities. , etc.) are required as the main raw materials.

In the Fe-Co-BRM-based ferromagnetic alloy, Co does not play a very large role in wax when the Qm content is 25% or less (Bll). For example, the sample contains 4g and Nα5.
0. Demon 58 and Nα60. Comparing &68 and Ma70, etc., the compositional difference between these alloys is mostly C.

The only difference in quantity (I Co and LOCo) is such that (B II ) m a X differs by only about 1.5%. The role of Co(1) is to raise the performance of these alloys by one point.

Generally, when Co is added to an Fe alloy, it is recognized that the Curie point (Tc) both increases and decreases as the amount of Co added increases. Therefore, replacing Fe with Co generally produces complex results, which are difficult to predict.

For example, when Fe in an RF e s compound is replaced with Co, Te initially increases as Con increases, but as Fe is
/2 substituted R(Fe C.

It reaches a maximum near O, 50, 5) 3, and then decreases. Also F e
In the case of 2B alloy, T is replaced by Co for Fe.
c decreases monotonically.

In the Fe-Co-BRM-based ferromagnetic alloy according to the present invention, the system (76-x) Fe-x illustrated as an example in FIG.
As is clear in Co-8B-15Nd-IM, C
As the amount of o substitution (x) increases, Tc initially increases rapidly,
After that, it gradually increases.

This tendency is confirmed to be similar regardless of the type of R.

Moreover, even if the amount of Co substitution is small (for example, 0.1 to 1%), T
It is effective for increasing c and varies from about 310 to about 7 depending on the amount of Co substitution.
A ferromagnetic alloy with an arbitrary Tc of 50°C is obtained. Furthermore, from Fig. 1, it can be seen that the Curie point increases greatly as the Co content increases, but this tendency does not change as the additive element M
It is confirmed that it does not change much.

When Co9Qr;i exceeds 25%, (Bll)saw gradually decreases, and when it exceeds 35%, a rapid decrease occurs. This is mainly due to the decrease in 111c of the magnetic material. When Coff1 reaches 50% (Bll) a+Hx
decreases to about 4 MGOo (hard ferrite level).

Therefore, the limit for Com is 50%. Furthermore, Co
It is preferable that n is 35% or less because even when a predetermined amount of the additive element M is included, the (Bll)wax exceeds 10 MGOe of the highest grade alnico and the raw material price is lower. In addition, in the case of the preferable additive element M, nearly 20 MGOo is still produced at 35% Co (57.87 etc. in the sample).

The Fe-Co"-BRM-based ferromagnetic alloy of the present invention is Co
Compared to the Fe-B-R ternary ferromagnetic alloy that does not contain Fe-B-R, the Curie point is higher and it shows better temperature characteristics, Br is almost the same, l1lc is equal to or higher than or slightly lower, but C
Since the squareness is improved by the addition of o, (except when the amount of Co is large) (Bll)a+ax is equal to or greater than that.

Also, Co has higher corrosion resistance than Fe.

By containing Co, it is also possible to impart corrosion resistance. That is, the obtained sintered body (first surface magnet 5) was
Place it in a constant temperature and humidity chamber at 0℃ and 90% relative humidity for 200 hours.
Measurement of weight change due to oxidation 9 Samples according to the present invention (
Nα5) is a sample containing no Co (Fe-8B-15Nd
), the rate of increase in 'ifi fit' is significantly lower than that of
Further, the effect was significantly observed depending on the amount of Co added.

Furthermore, even if Co is less than 5%, it contributes to an increase in Tc, especially if it is more than 5%.
In 2, the temperature coefficient of Br is 0.1%/℃ or less, and 25%
The following contributes to increasing Te without impairing other properties.

Figure 2 shows a representative example of a sintered magnet made of a Fe-Co-BRM-based alloy, and a Fe-Co-BRM alloy containing no M for comparison.
The demagnetization curve of a typical example of a Co-BR magnet is shown. 1 in the diagram
is a magnet that does not contain the additive element M.

2 is the demagnetization curve of the Nb-added (sample Nα53) magnet, and 3 is the W-added (sample Nα83) magnet.

A similar 1llc improvement effect was also observed for V, Ta, Cr, Mo, and AJ other than these. The improvement in 1lle due to the addition of M increases the stability of the magnet and expands its applications. However, since M is a non-magnetic element, as the amount added increases, Br decreases, and therefore (BH)wax decreases. (Bll)
These M-containing alloys are very useful for a, as there have recently been many applications that require a high 111c even if a+ax is a little lower.

However, for 1311) mix, the range of 4 MGOe or more is for helmets.

Next, in order to clarify the effect of each addition of the additive element M on Br, an experiment was conducted by varying the amount of addition of the additive element M.
The changes were measured and the results are shown in FIGS. 3 to 5. B
Additional elements M excluding i, Mn, and Ni (Ti, Zr, Hf
, V, Ta, Nb, Cr.

The upper limit of the addition amount of W, Mo, Sb, Sn, Ge, Ai) is as shown in Figs. Furthermore, the preferred range from the viewpoint of Br can be clearly read from Figures 3 to 5 by dividing Br into stages such as 8.5, 8.10 kG, etc. From the figure, the upper limit of the addition of the additive element M is as follows, assuming that the energy product (Bll) at the level of hard ferrite is equal to or higher than approximately 4 MGOe.

Ai! 9.5%, Ti4.5%.

■9.5%, Cr8.5%.

Mn 8%, Zr 5.5%.

Hf 5.5%, Nb 12.5%.

T a 10.5%, Mo 9.5%.

Ge 7%, Sb 2.5%.

Sn 3.5%, Bi 5%.

Ni 8%, and W 9.5%.

When large amounts of Mn and Ni are added, IHc decreases, but since Ni is a ferromagnetic element, Br does not decrease much (see Figure 4). Therefore, the upper limit of Ni is 8% in order to keep I Hc at 1 kOc or more, and from the viewpoint of reducing l1lc, Ni is preferably 4.5% or less.

Although Mn addition has a larger effect on Br reduction than Ni, it is not as drastic. Thus, the upper limit of Mn is Itlc = 1
The Mn content is preferably 8% in order to achieve kOe or more, and 3.5% or less is preferable from the viewpoint of reducing l1lc.

As for Bi, it is virtually impossible to manufacture an alloy in which the vapor pressure is extremely high and exceeds Bi5%, so it is set at 5% or less.

When two or more of the above elements are contained, the curve is almost similar to the one obtained by synthesizing the characteristic curves of each added element shown in Figs. 3 to 5.The content of each element is below the above percentage, In addition, the content is set to be less than or equal to the maximum value of the above percentages for each element.

A more desirable range of the amount of M added is (T311)w
It is determined from the range where ax exceeds 10 MGOe of f & 4th class alnico. In order for (Bit) wax to be 10 MGOe or more, Br is preferably set to [f, 5 kG or more.

From FIGS. 3 to 5, the upper limit of the amount of M added that makes B"(i, 5 kG) is determined as a desirable range as follows (however, Mn and Ni are determined from the viewpoint of l1lc).

Yabu 7.5%, Ti 4%.

■ 8%, Cr8.5%゜M n3.5%, Zr4.5%.

Hf 4.5%, Nb 10.5%.

Ta 9.5%, Mo 7.59o.

G e 5.5%. S b 1.5%゜Sn2
．． 5%, Bi 5%.

Ni 4.5%, and W 7.5%.

Furthermore, the range of R is 11-24% and the range of B is 4-24%.
, the balance being Fe (the amount of Co substitution is 35% or less), it is possible to obtain a magnetically anisotropic sintered permanent magnet with (1311)llax 10 MGOe or more. In a more preferred embodiment, the ferromagnetic alloy of the present invention is (I311) wax 1
5.2G.

It is possible to provide a magnetically anisotropic sintered permanent magnet exhibiting characteristics of 25, 30, and 33 MGOc or higher.

Generally, as the amount of additive element M increases, Br decreases, but within a preferable range, (Bll)ffla
The value of x is about the same as in the case without M addition, and the maximum value is 33M.
Reach GOc or higher. In addition, as mentioned above, the increase in coercive force due to the addition of a specific M contributes to stabilizing the magnetic properties, and together with the increase in the Curie point due to Co, it is possible to create a magnetic field that is extremely stable and has a high energy product in practical terms. An anisotropic sintered permanent magnet is obtained.

In addition, the addition port of M is Br decreasing trend, (BH) + ea
Considering the influence on x, 0.1 to 3% is most desirable.

Also, as for M, as is clear from Figures 3 to 5, V, Ta
, Nb, Cr, W, Mo, Mn, Ni.

Even if Aj) is added in a relatively large amount, it does not significantly reduce B (for example, even if 8% is added, Br is 4kG or more), especially excluding Ni and Mn (V, Ta, Nb.

Cr, W, Mo, Aj! This contributes to improving IC over a wide range of areas.

(Margin below) Table 1 (1) Table 1 (2) Table 1 (3) Table 1 (4) Table 1 (5) Table 1 (8) Table 1 (7) As detailed above, two aspects of the present invention are novel Fe-C.

- B-RM-based ferromagnetic alloy, i.e. mainly composed of Fe, and also rich in resources as R], mainly composed of rare earth elements (Nd, Pr) that are easily available in the industry (Fe, Co )−
It is a ferromagnetic alloy based on a BR compound, and is particularly suitable for q as a permanent magnet material. By using this, we have also made it possible to provide Fe-Co-BRM-based magnetically anisotropic sintered permanent magnets that have magnetic properties superior to hard ferrite and can be substituted for Sm-Co-based materials. It has extremely high industrial value. In particular, its advantages as a permanent magnet material are extremely significant when compared with conventional Sm--Co based elements. In addition, Fe-B-
Even when compared with R ternary ferromagnetic alloys, the inclusion of Co provides a sufficiently high Curie point for practical use, and furthermore, the inclusion of a specific additive element M makes it possible to increase the coercive force of the sintered magnet. It can also contribute to expanding the scope and increasing the practical value.

[Brief explanation of the drawings] Figure 1 shows (7B-x) Fe-xCo-8B-15N
Anisotropic sintered magnet made of d-IM alloy contains Co! (horizontal axis) and one curri point (vertical axis). Figure 2 shows a sample containing no 2M (57Fe-20Co
-8B -15N d ), sample 453 (58F
e -20Co -8B -15N d -IN b
) and sample Na83 (58Fe-20Co-8B-1
5Nd-IW), the demagnetization curve (horizontal axis magnetic field H (kOe), vertical axis magnetization 4 yr I
(kG)). Figures 3 to 5 show (62~x) Fe-15co-8
Regarding the anisotropic sintered magnet made of B-15N d -x M-based alloy, the amount of additive element M added (horizontal axis) and residual magnetization B
Graph showing the relationship with r (kG). Figure 6 shows (81,5-x) Fe-10Co-8
In an anisotropic sintered magnet made of 8-xNd-0,5AJ alloy, Ncl (horizontal axis atomic %), 111c, Br
A graph showing the relationship between Figure 7 shows (74,5-x) Fe-10Co-x
In an anisotropic sintered magnet made of B-15N d -0,5Aβ alloy, BR (horizontal axis atomic %) and IHc, B
The graph showing the relationship with r and FIG. 8 are (94,5-x-y) Fe-5Co
-y B -x N d -0,5A In an anisotropic sintered magnet made of I-based alloy, (94,5-x-y)
(BH)ma for Fe-yB'-xNd three components
x contour map. are shown for each. Applicant Sumitomo Special Metals Co., Ltd. Agent Patent Attorney Asami Kato (and 1 other person) Figure 1 Co-planning ratio X (%) Figure 3 X (%) Figure 4' Figure 5 Figure 6 Figure Nd amount (atomic %) (81,5-x) F e ・10Co ・8 B-x
Nd Φ0.5AJ Figure 7 Daily amount (coolness ÷%)

Claims (2)

[Claims] (1) In atomic percentage, R (R is one or two of Nd and Pr) 8-30%, B2-28%, and one or more additive elements M (excluding 0%) below the specified percentage below ( However, when there are two or more types of additive elements M, the total amount of M is the maximum predetermined percentage of the additive elements, but not more than the predetermined percentage), and the remainder substantially consists of Fe, with a part of the Fe being included in the total composition. A ferromagnetic alloy characterized in that 50% or less (excluding 0%) of Co is substituted with Co; Al9.5%, Ti4.5%, V9.5%, Cr8.5%, Mn8%, Zr5 .5%, Hf5.5%, Nb12.5%, Ta10.5%, Mo9.5%, Ge7%, Sb2.5%, Sn3.5%, Bi5%, Ni8%, and W9.5%. (2) R in atomic percentage (R is Nd, Pr, Dy, Ho,
At least one of Tb, La, Ce, Gd, Y,
and 50% or more of R is one or two of Nd and Pr)8~
30%, B2-28%, below specified % (excluding 0%)
(However, when there are two or more types of additive elements M, the total amount of M is not more than the specified % of the maximum specified % of the added elements), and the remainder is substantially Fe. 50% of the total composition
A ferromagnetic alloy characterized by the following (excluding 0%) substitution with Co: Al 9.5%, Ti 4.5%. V9.5%, Cr8.5%. Mn8%, Zr5.5%, Hf5.5%, Nb12.5%, Ta10.5%, Mo9.5%, Ge7%, Sb2.5%, Sn3.5%, Bi5%, Ni8%, and W9. 5%.