JP3472358B2 - Permanent magnet for heat bonding and method of manufacturing the same - Google Patents

Description

Detailed Description of the Invention

[0001]

BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a heat-bonding permanent magnet and a method for manufacturing the same.

[0002]

Permanent magnets containing BACKGROUND ART rare earth elements are very fragile because of poor machinability, also when exposed to a high temperature, the magnetic properties deteriorate along with it the metal structure is changed,
It has such a property.

Therefore, when the permanent magnet is joined to, for example, a metal rotor of a motor, which is a dissimilar metal part, it is not possible to adopt a mounting structure such as an insertion structure, screwing or welding. Conventionally, an adhesive has been used (see, for example, JP-A-55-58760).

[0004]

However, the use of an adhesive causes a problem that the adhesive strength is low because the wettability of the permanent magnet is poor, and the adhesive strength is remarkably reduced as the temperature rises. Under such circumstances, it is impossible to meet the demand for high-speed rotation of the motor. Permanent magnet, including or rare earth element, it is necessary to some kind of anti-rust treatment so poor in corrosion resistance.

In view of the above, it is an object of the present invention to provide a heat-bonding permanent magnet that can be firmly bonded to dissimilar metal members and that has a rust preventive property, and a method for manufacturing the same.

[0006]

In order to achieve the above object , according to the present invention, a permanent magnet that is heat bonded to a dissimilar metal member is used.
A stone in front of a permanent magnet body containing rare earth elements
On the surface to be joined to the dissimilar metal member,
A liquid phase state is maintained at a heating temperature that can avoid a decrease in coercive force _I H _c
And rare-earth element system
It has a joint material layer made of gold,
Elemental alloys consist of alloy elements AE and the balance rare earth elements.
And its alloying element AE is Cu, Al, Ga, Co, F
e, Ag, Ni, Au, Mn, Zn, Pd, Sn, S
less selected from b, Pb, Bi, Cd and In
Both are one kind, and the content is 5 atomic% ≤ AE ≤ 50
%, And the rare earth element is Y, La, Ce, P
r, Nd, Sm, Eu, Gd, Tb, Dy, Ho, E
r, Tm, Yb, Mm (Misch metal) and Lu
At least one permanent magnet for heating and joining
Will be provided.

Further, according to the present invention, the permanent magnet body is
However , the entire surface excluding the bonding material layer is Al, Ni,
Provided is a permanent magnet for heating bonding, which is covered with a rust preventive film made of one of Au, Ti and TiN .

Further according to the present invention , a rare earth element is included.
The surface of the permanent magnet body that is heat bonded to the dissimilar metal member
The process of forming a rust preventive film on all surfaces except
And a step of forming a bonding material layer on the surfaces to be thermally bonded,
The anticorrosion film is selected from Al, Ni, Au , Ti and TiN.
One of the permanent magnets, and the bonding material layer is a permanent magnet.
Liquid phase at a heating temperature that can avoid a decrease in coercive force _I H _c of the main body
Element in one of the solid state and solid-liquid coexisting state
It is composed of a series alloy, and the rare earth element alloy is an alloy element.
AE and the balance rare earth element, its alloy element AE
Is Cu, Al, Ga, Co, Fe, Ag, Ni, A
u, Mn, Zn, Pd, Sn, Sb, Pb, Bi, Cd
And at least one selected from In,
Content of 5 atomic% ≤ AE ≤ 50 atomic%,
Earth elements are Y, La, Ce, Pr, Nd, Sm, Eu,
Gd, Tb, Dy, Ho, Er, Tm, Yb, Mm (Mi
Metal) and at least one selected from Lu
A method of manufacturing a permanent magnet for heat bonding, which is a seed, is provided.

[0009]

[Action] When the bonding material layer that make up as described above, it is possible to avoid damage to the magnetic properties of the permanent magnet the body at the time of junction. The liquid phase resulting from the bonding material layer mainly composed of a rare earth element is a highly active, permanent magnet body and a heterologous gold
Since excellent wettability to the genus member, it is possible to firmly bond the permanent magnet body relative dissimilar metal member. Furthermore, since the permanent magnet has the bonding material layer integrally,
Good joining workability.

However, in the rare earth element-based alloy, the content of the alloy element AE is AE <5 atomic% or A
When E> 50 atomic%, the volume fraction Vf of the liquid phase in the solid-liquid coexisting state becomes low, so that the bonding strength decreases. From this, it is desirable that the content of the alloy element AE is set so as to have a eutectic composition or a composition close thereto in relation to the rare earth element. In addition, two or more alloy elements AE
In the case of containing, the total content thereof is 5 atomic% ≦
AE ≦ 50 atomic%.

The permanent magnet for heat bonding exhibits excellent corrosion resistance because it has the rust preventive film specified as described above on the entire surface other than the bonding material layer.

Further, according to the above-mentioned manufacturing method, it is possible to easily obtain the permanent magnet for heating and joining which is provided with the rust preventive film. In this case, either of the above steps may be performed first.

[0013]

EXAMPLES Referring to FIGS. 1 and 2, a permanent magnet 1 for heating and joining.
Is a permanent magnet body 2 containing a rare earth element and a bonding material layer 4 integrally formed on the surface 3 of the permanent magnet body 2 to be bonded to a dissimilar metal member and made of a rare earth element alloy.
And the entire surface 5 of the permanent magnet body 2 excluding the bonding material layer 4
And a rust preventive film 6 for covering the. This rust preventive film 6 is provided as needed.

The rare earth element-based alloy is composed of the alloy element AE and the remaining rare earth element, and basically the alloy element AE undergoes a eutectic reaction with the rare earth element . Rare earth elements Y, La, Ce,
Pr, Nd, Sm, Eu, Gd, Tb, Dy, Ho, E
It is at least one selected from r, Tm, Yb, Mm (Misch metal) and Lu. In addition, alloy element AE
Is Cu, Al, Ga, Co, Fe, Ag, Ni, A
u, Mn, Zn, Pd, Sn, Sb, Pb, Bi, Cd
And at least one selected from In. The content of the alloy element AE is set to 5 atomic% ≦ AE ≦ 50 atomic%.

Table 1 shows examples of eutectic alloys in rare earth element-based alloys.

[0016]

[Table 1]

Further, examples of the hypoeutectic and hypereutectic alloys in the rare earth element type alloys include the following. In each chemical formula, the unit of the numerical value is atomic% (the same applies hereinafter). Nd ₆₀ Cu ₄₀ alloy, Nd ₈₀ Cu ₂₀ alloy, Nd ₅₀ C
u ₅₀ alloy, Nd ₉₀ Al ₁₀ alloy, Nd ₈₀ Co ₂₀ alloy, Sm
₇₅ Cu ₂₅ alloy, Sm ₆₅ Cu ₃₅ alloy, La ₈₅ Ga ₁₅ alloy.
Further, as a ternary alloy, Nd ₆₅ Fe ₅ Cu ₃₀ alloy (liquid phase generation temperature 501 ° C.) and Nd ₇₀ Cu ₂₅ Al
₅ (liquid phase generation temperature 474 ° C.).

The rust preventive film 6 is made of one of Al, Ni, Au, Ti or TiN.

To form the bonding material layer 4, or the bonding material layer 4 and the rustproof film 6, an electroplating process or a vapor phase plating process, for example, a physical vapor deposition method (ion plating, sputtering, etc.) is applied.

By applying the physical vapor deposition method as described above, it is possible to efficiently form the bonding material layer 4 and the rust preventive film 6 which are thin and have a uniform composition and high adhesion strength. This is achieved by the wraparound effect even if the surface 3 and the surface 5 of the permanent magnet body 2 are complicated.

The bonding material layer 4 is easily made amorphous because the rare earth element-based alloy forming it is a eutectic alloy and has a relatively low liquidus generation temperature. Amorphous bonding material layer 4
Has excellent oxidation resistance because it has few crystal grain boundaries, contains almost no oxides that become impurities during bonding, and has a uniform composition. In order to improve the oxidation resistance of the bonding material layer 4, the volume fraction Vf of the amorphous phase in the layer 4 is Vf ≧.
It is preferably 50% (including Vf = 100%).

In manufacturing the permanent magnet 1 for heating and joining,
A surface 3 of the permanent magnet body 2 to be joined to a dissimilar metal member
A step of masking with a Cu plate, an Al plate, a tetrafluoroethylene resin plate or the like, and forming a rust preventive film 6 on all surfaces 5 except the surface 3, and after removing the masking, the surface 3 is removed. And the step of forming the bonding material layer 4.

[0023] The heating bonding permanent magnet 1 hitting the joining the dissimilar metal members, superimposing the dissimilar metal <br/> member in the bonding material layer 4 of the permanent magnet 1, then a vacuum heating furnace and the superposition thereof A method is employed in which the bonding material layer 4 is placed inside, the bonding material layer 4 is brought into a liquid phase state or a solid-liquid coexisting state under heating, and then the furnace is cooled.

In this case, the heating temperature T varies depending on the composition of the bonding material layer 4 , but various rare earth element-based alloys having the above-mentioned composition are in a liquid phase state or a solid-liquid coexisting state at a relatively low heating temperature T, so that the permanent magnet is used. The characteristics of the main body 2 and the dissimilar metal member are not changed.

A bonding material layer 4 containing a rare earth element as a main component
The resulting liquid phase is highly active, and members made of various materials,
For example, it exhibits excellent wettability with respect to a steel member, a permanent magnet body 2 containing a rare earth element (which has very poor wettability with respect to an adhesive or a brazing material), and the like. By using such a bonding material layer 4, the permanent magnet body 2 can be firmly bonded to a dissimilar metal member.

If the heating time t is too long, the characteristics of the permanent magnet body 2 and the dissimilar metal member will change, so t ≦ 10 hours is desirable, and t ≦ from the viewpoint of productivity improvement. It's an hour.

Example 1 Nd having a purity of 99.9% and Cu having a purity of 99.9% were weighed so as to obtain an Nd ₇₀ Cu ₃₀ alloy having a eutectic composition, and then the weighed materials were vacuumed. The Nd ₇₀ Cu ₃₀ alloy ingot was obtained by melting using a melting furnace and then casting.

As shown in FIG. 3, as the permanent magnet body 2, an NdFeB type permanent magnet having a length of 20 mm, a width of 20 mm, and a thickness of 3 mm (manufactured by Sumitomo Special Metals Co., Ltd., trade name NEOMAX-28U) is used.
H) was selected.

First, the surface 3 of the permanent magnet body 2 is masked by using a Cu plate, and a purity of 9 is used as an evaporation source.
Using 9.9% Al ingot, power supply voltage 4kV, A
r atmosphere 10 ^-3 Torr, heating temperature of Al ingot about 14
Ion plating was performed under the condition of 00 ° C, and the surface 3
An Al anticorrosion film 6 having a thickness of about 10 μm was formed on the entire surface 5 except for.

Next, the masking is removed from the permanent magnet body 2, and the Nd ₇₀ Cu ₃₀ alloy ingot is used as the evaporation source, the power supply voltage is 5 kV, the Ar atmosphere is 10 ^-3 Torr, and the N atmosphere is 10 ^-3 Torr.
Ion plating is performed under the condition that the heating temperature of the d ₇₀ Cu ₃₀ alloy ingot is about 1300 ° C., and the Nd ₇₀ Cu ₃₀ alloy bonding material layer 4 having a thickness of about 50 μm is formed on the surface 3 of the permanent magnet body 2. The permanent magnet 1 for heating and joining shown in FIG. 3 was obtained.

As a dissimilar metal member, a cold rolled steel plate 7 having a thickness of 0.4 mm is laminated as shown in FIG.
A rectangular parallelepiped laminated body 8 having m, a width of 10 mm and a length of 20 mm was selected. In the laminated body 8, the cold rolled steel sheets 7 are joined by the caulking means 9. Further, the through hole 1 of the laminated body 8
0 is used for connection with the chuck in the tensile test.

In the heat-bonding, on the bonding material layer 4 of the permanent magnet 1 for heat-bonding, the laminate 8 is superposed with the joint surfaces consisting of the steel plate end faces facing downward, and the superposed product is vacuum-heated. The permanent magnet 1 and the laminated body 8 are installed as shown in FIG. 4 by performing a joining process of heating temperature T = 530 ° C. and heating time t = 10 minutes, followed by furnace cooling.
To obtain a joined body 11. In this bonding treatment, the heating temperature T is T = 530 ° C., which exceeds the eutectic point 520 ° C. shown in FIG. 5, so that the bonding material layer 4 has a eutectic composition and thus is in a liquid phase state. .

For comparison, a permanent magnet body 2 similar to the above and a laminate 8 similar to the above are laminated with an epoxy resin adhesive (manufactured by Nippon Ciba-Gaigi Co., Ltd., trade name Araldite) to prepare a laminate. The superposed product is placed in a drying furnace, a heating process at a heating temperature of 200 ° C. and a heating time of 60 minutes, and then a joining process consisting of furnace cooling are performed, and the permanent magnet body 2 and the laminated body 8 are bonded together with an epoxy resin. A joined body joined through a system adhesive was obtained.

When a tensile test was conducted on each of the bonded bodies at room temperature and under heating at 150 ° C., the results shown in Table 2 were obtained.

[0035]

[Table 2]

As is clear from Table 2, the bonded body 11 using the bonding material layer 4 has a higher bonding strength at room temperature and under heating at 150 ° C. than that using the epoxy resin adhesive, The bonding strength was almost the same under both environments, and the variation was small.

The bonded body using the adhesive has a low bonding strength at room temperature and has a large variation, and is 150 ° C.
Under heating, its bonding strength decreased to one-third of that at room temperature.

The permanent magnet body 2 containing a rare earth element such as NdFeB system permanent magnet and SmCo system permanent magnet has its magnetic characteristics when the heating temperature T during the joining process becomes T> 650 ° C.
In particular, the coercive force _I H _c (magnetization intensity I = 0) tends to decrease. However, the residual magnetic flux density Br and the coercive force _B H _c (magnetic flux density B = 0) hardly change, and therefore the maximum magnetic energy product (BH) max is substantially constant. In the joining process using the joining material layer 4, the heating temperature T is T = 5.
Since 30 ° C. and T ≦ 650 ° C., the magnetic characteristics of the permanent magnet body 2 are not changed.

The poor wettability of the permanent magnet body 2 is due to the rare earth element concentration at the crystal grain boundaries, which is N in this embodiment.
This is due to the existence of a phase having a high d concentration. In the joining process using the joining material layer 4, the joining material layer 4 is in a liquid phase state and contains Nd ₇₀ Cu containing Nd as a main component.
_The liquid phase generated from the No. ₃₀ alloy exhibits high wettability with respect to the permanent magnet main body 2 because it has a high activity and shares the main component with the phase having a high Nd concentration existing in the grain boundaries.
In addition, the wettability of the laminated body 8 made of the cold-rolled steel sheet 7 is extremely good due to the high activation.

Therefore, by using the bonding material layer 4 as described above, the permanent magnet body 2 can be firmly bonded to the laminated body 8 without impairing the magnetic characteristics of the permanent magnet body 2. . This joining technique is applied to the joining of the permanent magnet body 2 to the motor rotor, and makes it possible to realize a high-speed rotation motor having a rotation speed of 10,000 rpm or more.

Further, the joint body 11 was subjected to a corrosion resistance test such that the joint body 11 was kept in an environment of 60 ° C. and a relative humidity of 90% for 30 days. It was found that the rust preventive film 6 surely prevented the rust.

Example 2 The same Nd ₇₀ Cu ₃₀ alloy ingot as in Example 1 was crushed by a stamp mill and then classified to obtain Nd ₇₀ Cu ₃₀ alloy powder having a particle size of 106 μm or less.

As the permanent magnet main body 2, a NdFeB system permanent magnet having a length of 10 mm, a width of 10 mm and a thickness of 3 mm, which is the same as that of the first embodiment (manufactured by Sumitomo Special Metals Co., Ltd., trade name NEOMAX-28UH).
Was selected.

Then, as shown in FIG. 6, both sides 3 forming a square of the permanent magnet main body 2 were subjected to flash vapor deposition using Nd ₇₀ Cu ₃₀ alloy powder to obtain Nd ₇₀ having a thickness of 20 μm.
The Cu ₃₀ alloy bonding material layer 4 was formed, and thereby the permanent magnet 1 for heat bonding was obtained.

The conditions of the flash vapor deposition method are as follows: the temperature of the Pt heating boat is 900 ° C., the supply amount of Nd ₇₀ Cu ₃₀ alloy powder to the heating boat is 15 mg / min, and the atmospheric pressure is 5 × 10 ⁻⁵ To.
It is rr. When the Nd ₇₀ Cu ₃₀ alloy powder is supplied to the heating boat in the supply amount was reached heating boat Nd ₇₀ Cu
The entire ₃₀ alloy powder immediately evaporates and adheres to the surface 3 of the permanent magnet body 2, so that the composition of the bonding material layer 4 is N.
It is almost the same as that of the d ₇₀ Cu ₃₀ alloy, and the composition change is suppressed.

As shown in FIG. 6, as the dissimilar metal member, a cold rolled steel plate 7 having a thickness of 0.3 mm similar to that of Example 1 is laminated, and two rectangular parallelepipeds having a length of 10 mm, a width of 10 mm and a length of 15 mm are formed. The laminated body 8 was selected. In the laminated body 8, the cold rolled steel sheets 7 are joined by the caulking means 9. The through hole 10 of the laminated body 8 is used for connection with the chuck in the tensile test.

In heat bonding, as shown in FIG.
The heating-bonding permanent magnet 1 is superposed on the joint surface formed by the steel plate end faces of the one laminate 8 with one of the joining material layers 4 thereof facing downward, and the other of the joining material layers 4 is laminated. 8
Were laminated with the joint surface consisting of the end faces of the respective steel plates facing downward, thereby producing a laminated product. Then, the stack is placed in a vacuum heating furnace and the heating temperature T = 530.
A heating step at a temperature of 30 ° C. for a heating time of t = 30 minutes, followed by a joining process consisting of furnace cooling to join the permanent magnets 1 and 8 with the two laminated bodies 8 as shown in FIG. A joined body 11 joined through the layer 4 was obtained.

For comparison, the same Nd ₇₀ Cu ₃₀ alloy ingot as described above was cut with a micro-cutter to obtain N
A thin plate-like bonding material made of a d ₇₀ Cu ₃₀ alloy and having a length of 10 mm, a width of 10 mm and a thickness of 0.2 mm was obtained.

Then, the same NdFeB-based permanent magnet and the two laminated bodies were heat-bonded by using two bonding materials under the same conditions as described above, whereby a bonded body similar to the bonded body 11 shown in FIG. 7 was obtained. Obtained.

A tensile test was conducted on each of the bonded bodies at room temperature and under heating at 150 ° C., and the results shown in Table 3 were obtained.

[0051]

[Table 3]

As is clear from Table 3, the bonded body 11 using the bonding material layer 4 has higher bonding strength at room temperature and under heating at 150 ° C. than the bonded body using the thin plate-shaped bonding material. The joint strength does not change at all under both environments,
The variation was also small. This is because the composition of the bonding material layer 4 formed by flash vapor deposition is uniform and its strength is higher than that of the bonding material formed by casting.

[Example 3] As the permanent magnet body 2, the same NdFeB-based permanent magnet (length 10 mm, width 10 mm, thickness 3 mm, manufactured by Sumitomo Special Metals Co., Ltd., trade name NEOMAX-28UH) as in Example 2 was selected. .

Then, as shown in FIG. 6, Nd target and Cu are formed on both sides 3 of the permanent magnet body 2 forming a square.
Multi-source sputtering method using target (N in Example 2
d, Cu binary sputtering method) and the deposition rate is about 0.
A Nd ₇₀ Cu ₃₀ alloy bonding material layer 4 having a thickness of 20 μm was formed at 3 μm / min, whereby a permanent magnet 1 for heating bonding was obtained. In this case, the Nd ₇₀ Cu ₃₀ alloy had an amorphous single phase structure (ie, Vf = 100%).

The conditions of the multi-source sputtering method are as follows.
Equipment used Magnetron type three-way simultaneous high frequency sputtering apparatus (only two elements are used in the embodiment); Cooling method of permanent magnet body Water cooling; Rotation speed of permanent magnet body 30 rpm; Nd purity of Nd target 99.9%; Nd target size
Diameter 80 mm, thickness 5 mm; Cu target Cu purity 9
9.9%; Cu target dimensions 80 mm diameter, 5 thickness
mm; Sputter gas Ar; Sputter gas pressure 1 Pa; Reverse sputter input power 1 for cleaning the surface of the permanent magnet body
00W, 10 minutes; Pre-sputtering for etching and cleaning Nd, Cu target surface Input power 100
W, 20 minutes; Sputtering at the time of forming the bonding material layer Input power 300 W for Nd target, input power 250 W for Cu target (Since the sputtering rate of Cu is 3 times that of Nd, the input power is adjusted as described above. ).

In the heat-bonding, the heat-bonding permanent magnet 1 and the two laminated bodies 8 were superposed in the same manner as in Example 2 to produce a superposed product (see FIG. 6), and then in Example 2. Heat bonding was performed under the same conditions, and thereby a bonded body 11 was obtained (Fig. 7).
reference).

About the bonded body 11 at room temperature and 150 ° C.
When the tensile test was performed under heating, the results shown in Table 4 were obtained. For comparison, Table 4 also shows the measured values when the thin plate-like bonding material of Table 3 was used.

[0058]

[Table 4]

As is clear from Table 4, the bonded body 11 using the bonding material layer 4 has higher bonding strength at room temperature and under heating at 150 ° C. than the bonded body using the thin plate-shaped bonding material. The joint strength does not change at all under both environments,
The variation was also small. This is because the composition of the bonding material layer 4 formed by the multi-source sputtering method is an amorphous single-phase structure, so that the composition is extremely uniform and the amount of oxide is small, and the strength thereof is higher than that of the bonding material formed by casting. Is also high.

[0060]

According to the invention of claim 1 to 3, wherein, according to the present invention, with the structure described above, with respect to members of different metals,
Permanent magnets containing rare earth elements may be damaged by their magnetic properties.
It is possible to provide a heating-bonding permanent magnet that can be firmly bonded without exception . Having integrated or permanent magnet body and the bonding material layer, thereby improving the bonding workability.

According to the invention described in claim 4 , it is possible to provide a permanent magnet for heating bonding which has the rust preventive effect in addition to the above effects.

According to the invention described in claims 5 to 7 , it is possible to easily mass-produce the heat-bonding permanent magnet having the rust preventive ability.

[Brief description of drawings]

FIG. 1 is a perspective view of a permanent magnet for heating and joining.

FIG. 2 is a sectional view taken along line 2-2 of FIG.

FIG. 3 is a perspective view showing a superposition relationship between a heat-bonding permanent magnet and a laminated body.

FIG. 4 is a front view of a joined body.

FIG. 5 shows a main part of a Cu—Nd system phase diagram.

FIG. 6 is a perspective view showing a superposition relationship between a heating-bonding permanent magnet and a laminated body.

FIG. 7 is a perspective view of a joined body.

[Explanation of symbols]

1 Permanent Magnet for Heating and Bonding 2 Permanent Magnet Main Body 3 Surface 4 Bonding Material Layer 5 Surface 6 Anticorrosion Film 8 Laminate ( Different Metal Member)

Continuation of front page (51) Int.Cl. ⁷ Identification code FI // C23C 30/00 H01F 1/04 Z (56) References JP-A-6-86512 (JP, A) JP-A-2-14502 (JP , A) JP-A-7-116866 (JP, A) (58) Fields investigated (Int.Cl. ⁷ , DB name) H01F 1/04 C22C 28/00 C22C 45/00 H01F 41/02 C23C 30/00 H01F 7/02 H02K

Claims (7)

(57) [Claims] 1. A permanent magnet that is heat-bonding to dissimilar metal member (8) (1), the surface (3 joined to the dissimilar metal member (8) in the permanent magnet body (2) containing a rare earth element ), The coercive force _I H _c of the permanent magnet body (2) is low.
Liquid phase and solid-liquid coexisting state at heating temperature that can avoid lowering
The rare earth element-based alloy that integrally has the bonding material layer (4) composed of the rare earth element-based alloy in one state
It consists of The alloy element AE and the remainder rare earth elements, the alloy
The element AE is Cu, Al, Ga, Co, Fe, Ag, N
i, Au, Mn, Zn, Pd, Sn, Sb, Pb, B
i, at least one Der selected from Cd and In
I, the content is 5 atomic% ≦ AE ≦ 50 atomic% der
And the rare earth elements are Y, La, Ce, Pr, Nd, S
m, Eu, Gd, Tb, Dy, Ho, Er, Tm, Y
b, selected from Mm (Misch metal) and Lu
Permanent magnets for heat-bonding, wherein at least one Der Rukoto. 2. The permanent magnet for heat bonding according to claim 1, wherein the bonding material layer (4) is a thin layer formed by physical vapor deposition. 3. The volume fraction Vf of the amorphous phase in the bonding material layer (4) is Vf ≧ 50%.
The heat-bonding permanent magnet described. 4. The permanent magnet body (2) has Al, Ni, A on the entire surface (5) excluding the bonding material layer (4).
u, Ti or TiN of being covered by the anti-corrosion film (6) consisting of one claim 1, 2 or a permanent magnet for heat-bonding of the 3 described. Forming an anti Sabimaku (6) to the dissimilar metal member (8) and heat-bonding the surface to (3) obtained by removing all of the surface of the permanent magnet body (2) (5) containing 5. A rare earth element process and, using a step of forming a junction material layer (4) on the surface (3) which is the heat-bonding, the anti-corrosion film (6) is Al, Ni,
Consisting of one selected from Au, Ti and TiN,
The bonding material layer (4) is a coercive force of the permanent magnet body (2).
At the heating temperature that can avoid the decrease of the force _I H _c
Than one state and ing rare earth element-based alloy of the solid-liquid coexistence state
The rare earth element alloy is composed of alloy element AE and the balance
It is composed of rare earth elements, and its alloying element AE is Cu, A
l, Ga, Co, Fe, Ag, Ni, Au, Mn, Z
n, Pd, Sn, Sb, Pb, Bi, Cd and In
At least one selected from the group, the content of which is 5
Atomic% ≦ AE ≦ 50 atomic%, and the rare earth element is
Y, La, Ce, Pr, Nd, Sm, Eu, Gd, T
b, Dy, Ho, Er, Tm, Yb, Mm (Mischme
At least one Der manufacturing method of heat-bonding permanent magnet, characterized in Rukoto selected from tall) and Lu. 6. The method for producing a permanent magnet for heat bonding according to claim 5 , wherein a physical vapor deposition method is applied to the formation of the bonding material layer (4). 7. The bonding material layer (4) and the rust preventive film (6)
The method for producing a permanent magnet for heat bonding according to claim 5 , wherein a physical vapor deposition method is applied to the formation of the.