JPS62158854A - Permanaent magnet material - Google Patents

Abstract

PURPOSE:To improve residual magnetic flux density, coercive force, and maximum energy product by blending specific amounts of a group consisting Al, Cu, and Zn and N with rare earth element-Fe-Co-B. CONSTITUTION:A permanent magnet material has a composition satisfying a composition formula R1-x-y-z-alpha-betaFexCoyBzMalphaNbeta: where R represents a combination of 1 or >=2 kinds among rare earth elements including Y; M means one or more elements among Al, Cu, and Zn; and, as to the symbols 'x', 'y', 'z', 'alpha', and 'beta', 0.50<=x<=0.85, 0<=y<=0.20, 0.01<=z<=0.15, 0.01<=alpha<=0.10, and 0.015<=beta<=0.03. Owing to the above composition, magnetic properties such as residual magnetic flux density, coercive force, maximum energy product, etc., are improved and permanent magnets can be made highly efficient.

Description

DETAILED DESCRIPTION OF THE INVENTION Field of the Invention The present invention relates to a novel permanent magnet material mainly containing rare earth elements, iron, and boron.

Conventional technology Intermetallic compounds mainly composed of rare earth elements (R), iron (Fe), and boron (B) exhibit large crystal magnetism and high saturation magnetic flux density, and have high coercive force and high energy product. It is attracting attention as a permanent magnet material. It is particularly promising as a permanent magnet because it is cheaper than rare earth-cobalt materials and has a high saturation magnetic flux density.

Furthermore, it has been found that replacing a portion of Fe with CO increases the Curie point and improves thermal stability.

Problem 1 to be solved by the present invention is the magnetic flux density expressed by residual magnetic flux density, coercive force, and maximum energy product in the above-mentioned rare earth-iron-boron system and rare earth-iron-cobalt monosystem permanent magnet materials. The purpose is to further improve the characteristics.

Means for solving problems Book R Akino Ii 1 Stone n Ha, RI -X-V-1-a-
It is represented by the compositional formula j3F eXCOVBZMαNβ. In the above compositional formula, R is a rare earth element containing Y, that is, Y
SLa, Ce, Pr, Nd, Pm, Sm SE
u, Gd.

Tb, Dy %Ho, Er, Tm SYb, L
One type or a combination of two or more types selected from u,
M is one or a combination of two or more selected from AI, Cu, and Zn. Moreover, ×, ylz, Lx, and β are respectively 0.50≦X≦0.85, O≦y≦0.20.0.
01≦z≦0.15.0.01≦α≦0.10.

It is characterized in that 0.015≦β≦0.03.

In the present invention, R, -Fe-X or R-Fe-Go-
By adding one or more selected from AI, Cu, and Zn and N (nitrogen) to the X-based alloy, magnetic properties,
In particular, the residual magnetic flux density, coercive force and maximum energy product are improved.

The additive elements AI, Cu, and Zn have the effect of improving coercive force, maximum energy product, and residual magnetic flux density.

When α is less than 0.01, there is little improvement effect, and when it is larger than 0.10, deterioration of magnetic properties such as a decrease in the maximum energy product is observed. These elements can be added singly or
More than one type may be used in combination.

On the other hand, the additive element N, like B, has the function of expanding the Fe lattice, and this effect is a factor that increases the coercive force. When part of B is replaced with N, the magnetic properties are further enhanced compared to B and N11 alone. However, if the amount of N is too large, nitrides will be generated excessively and the magnetic properties will decrease, and if the amount of Nl is too small, the effect will be small, so 0.015≦
The range was β≦0.03.

Note that if there is too much Fe darkness, the residual magnetic flux density will improve, but the coercive force and the maximum energy product will decrease. on the other hand,
If it is too small, the residual magnetic flux density and the maximum energy product will decrease, so the range is set to 0.50≦x≦0.85.

Addition of Co is effective in raising the Curie point by one point and improving thermal stability, but if the amount y added exceeds 0.20, the coercive force decreases, which is not preferable.

The ratio of B is 0.01≦z≦0.15 from the viewpoint of magnetic properties.
The range of

The permanent magnet of the present invention can be produced by melting each component using a conventionally known method and casting the molten metal into a mold, etc., or by pulverizing the molten alloy, forming it in a magnetic field using powder metallurgy, and sintering it. Manufactured by Melting is performed in an inert gas using high frequency melting or arc melting.

Grinding is carried out using a combination of stamp mills, disc mills, vibration mills, ball mills, etc. Inert gas and organic solvents are used to prevent oxidation. For the purpose of improving the degree of orientation, magnetic field shaping is preferably performed in a transverse magnetic field in which the direction of the applied force and the direction of the magnetic field are perpendicular.

Sintering is preferably carried out in an inert gas, and after sintering, the material is rapidly cooled. The heat treatment is performed at 500 to 800°C, but it is desirable to vary the time depending on the composition.

Examples Example 1 Ndo, +Rs -αFe o, eoco 0.13
B 0.07Al aNO,015 (α-0,0
1) An alloy having the following composition was melted in an argon atmosphere using an arc)8 furnace.

Next, the ingot alloy was coarsely ground with a stamp mill, and then ground with a vibration mill to an average particle size of about 3.2 A1 m. 1 of this powder
Approximately 1.2′ci perpendicular to the magnetic field direction in a magnetic field of 3KOe
The resulting molded body was sintered at 1200°C for 2 hours in an argon atmosphere, then rapidly cooled to room temperature in mineral oil, and further heat-treated at 750°C to produce a magnet. .

Residual magnetic flux density (Br), coercive force (tHc), maximum energy product (BH) max of the obtained magnet material
When investigated, the results shown in Table 1 were obtained.

Example 2.3 Magnets were manufactured in the same manner as in Example 1 except that the ratio α of A1 was as shown in Table 1, and the characteristics are shown in Table 1.

Comparative Example 1 A magnet was manufactured in the same manner as in Example 1 except that no AI was added, and the characteristics are shown in Table 1.

Comparative Example 2.3 A magnet was manufactured in the same manner as in Example 1 except that the ratio α of AI was as shown in Table 1, and the characteristics are shown in Table 1.

Examples 4-6 Nd Q, +87-aFe o, 6oco o, +s
An alloy having the composition B o,o5Cu txNO,013 (α is as shown in Table 2) was melted in an argon atmosphere using a high frequency melting furnace. Next, the molten alloy was coarsely ground using a stainless steel mortar and ground to an average particle size of about 4.04 using a ball mill. This powder was molded by applying a pressure of 15 KOe and a magnetic field width of about 1.6 t/Cd, and the resulting molded body was sintered at 1050°C for 1 hour in an argon atmosphere, and then rapidly cooled to room temperature in mineral oil. , further 750℃
A magnet was produced by heat treatment. Table 2 shows the properties of the obtained magnet.

Comparative Examples 4 to 6 Magnets were manufactured in the same manner as in Example 4 except that the Cu ratio α was as shown in Table 2, and the characteristics are shown in Table 2.

Table 1 Table 2 Examples 7 to 9 pro, 2118-aFe o, 6o-aZn
An alloy magnet having the composition a Bo, +o NO, 0I2 (α is as shown in Table 3) was manufactured in the same manner as in Example 4, and the characteristics are shown in Table 3. However, the sintering temperature was 950°C.

Comparative Examples 7 to 9 Magnets were manufactured in the same manner as in Example 7 except that the ratio α of 7-n was as shown in Table 3, and the characteristics are shown in Table 3.

Table 3 Examples 10 to 18 Ndo, +z=6F8 0.70BO, IOM
0.03NI3 (However, M is AI, Cu, or Zn
and β=0.015 to 0.03) were respectively melted in an argon atmosphere using a high frequency melting furnace. Next, the molten alloy is coarsely ground in a stamp mill,
Subsequently, the average particle size was 4.3 mm using a vibration mill. It was crushed to about o. This powder has a magnetic field width of about 2.5 KOe. The molded body was molded under a pressure of Ot/c, and the resulting molded body was sintered at 1000° C. for 1 hour in an argon atmosphere, then rapidly cooled to room temperature, and further heat treated to produce a magnet. Table 4 shows the characteristics of the obtained magnet.

Comparative Examples 10 to 18 Magnets were manufactured in the same manner as in Example 10, except that the addition m of N was as shown in Table 4, and the characteristics are shown in Table 4.

Table 4 Effects of the Invention As is clear from the practical example, the permanent magnet material of the present invention is a conventional R-Fe-X or R-FB-C0-X alloy with one type selected from AI, CLI, and Zn. or 2
Remains by adding species or more and N.

It has improved magnetic flux density, coercive force, and maximum energy product, and has achieved high performance, making it an extremely excellent magnetic material for practical use.

Claims (1)

[Claims] 1 R_1_-_x_-_y_-_z_-_α_-_β
It is represented by the composition formula Fe_xCo_yB_zM_αN_β, and in the above composition formula, R is 1 of a rare earth element containing Y.
species or a combination of two or more species, M is Al, Cu, Z
One or a combination of two or more selected from n, 0.50≦x≦0.85, 0≦y≦0.20, 0.01
≦z≦0.15, 0.01≦α≦0.10, 0.015
A permanent magnetic material characterized in that ≦β≦0.03.