JP2000100609A - Material alloy for nanocomposite rare earth magnets and manufacture thereof - Google Patents

Abstract

PROBLEM TO BE SOLVED: To reduce the heating of a material alloy itself by using a specified molten Fe-R-B-M2 alloy which has a structure of a substantially amorphous phase and contains aggregates of M2 atoms having a specified diameter at a specified concentration in an amorphous matrix. SOLUTION: The material is formulated by Fe100-x-y-uRxByM2u (R contains one or two types of Nd and Pr 50% or more, M2 is one or two or more types of Cu, Ag and Au, x: 1-6 at.%, y: 15-30 at.%, u: 0.005-2 at.%) and the structure has an amorphous phase of 95% or more. Aggregates of M2 elements having 1-50 nm diameter are formed at a concentration of 5 at.% or more in an amorphous matrix and acts crystal nuclei in an Fe3B phase in a following heat treatment wherein the crystal nucleus concentration is 1022-1025 nuclei/m3.

Description

DETAILED DESCRIPTION OF THE INVENTION

[0001]

BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a raw material alloy for a rare earth sintered magnet or a material alloy for a bonded magnet, which is most suitable for a motor or an actuator, etc., and has a rare earth element content of one or less of Cu, Ag, and Au. Of a specific composition containing two or more
After rapidly solidifying the Fe-BR alloy melt and the Fe-Co-BR alloy melt under relatively slow quenching conditions, let them pass for a specified time within a specific temperature range and cool them, or use ordinary ultra-rapid cooling conditions. After rapid solidification and rapid cooling to around room temperature, the whole is made amorphous, and then heat-treated for a short time at a specific temperature to have an atom aggregate (cluster) of a predetermined atom in the amorphous matrix. Accordingly, the present invention relates to a nanoalloy raw material alloy for a rare-earth magnet in which productivity is improved by reducing heat generation during crystallization heat treatment, and a method for producing the same.

[0002]

BACKGROUND OF THE INVENTION Nd-Fe-B based magnet, in recent years, Nd ₄ Fe
₇₇ B ₁₉ (at%) magnetic material is proposed as a main phase an Fe ₃ B type compound in the vicinity composition (R.Coehoorn like, J.de Phys, C8,1988,669~670
Page). This permanent magnet material is a metastable structure permanent magnet material having a crystal texture in which a soft magnetic Fe ₃ B phase and a hard magnetic Nd ₂ Fe ₁₄ B phase are mixed by heat-treating an amorphous ribbon.

[0003] Such a permanent magnet material has Br of about 10 kG and 2 kOe
Since it has iHc of 3 kOe and the content of expensive Nd is as low as about 4 at%, the compounding raw material price is Nd-Fe-B with Nd ₂ Fe ₁₄ B as the main phase
Although it is cheaper than a system-bonded magnet, it is an essential condition that an amorphous alloy of a compounding material is required, and the conditions for liquid quenching are narrowly limited. Therefore, conventionally, various improvements in composition have been made.

[0004] The above-mentioned Fe ₃ B type Nd-Fe-B-based nanocomposite magnet is obtained by producing a raw material alloy in an amorphous state by a rapid quenching method, and then heat-treating the alloy to obtain an Fe ₃ B phase and an Nd ₂ Fe ₁₄ B phase. It is manufactured by making a nanometer-sized composite structure (nanocomposite structure) having as its main structure.

[0005]

The Nd-Fe-B-based raw material alloy is a flake or powder of an amorphous alloy obtained by a rapid quenching method, and has a rapid cooling rate of about 10 ⁶ K / s. The amorphous phase is adjusted to be 90% or more by the method, and in order to express high magnetic properties in the final product magnet, the crystal grain size is several nm to several tens nm in the crystallization heat treatment step.
It is necessary to adjust to the range.

[0006] In the conventional raw material alloy, the heat generated by crystallization is remarkable, so that a large amount of heat treatment makes it difficult to control the temperature of the raw material alloy, crystal growth tends to occur, the supply rate of the raw material alloy during heat treatment and the temperature rise. Strict control of the speed was required, which reduced productivity.

[0007] The present invention is to reduce the heat generation of the raw material alloy itself in the crystallization heat treatment step of the Fe ₃ B type Nd-Fe-B-based nanocomposite magnet, to easily control the crystal grain size, and to improve the productivity. It is an object of the present invention to provide a raw material alloy for a nanocomposite rare earth magnet and a method for producing the same, which is possible.

[0008]

As a result of various studies, the inventors of the present invention have set the cooling rate excessively in the conventional ultra-quenching method because the emphasis was on the amorphousization of the raw material alloy, and the structure of the raw material alloy was changed. To a nearly perfect amorphous structure, or a sub-nanometer to nanometer size
Since the structure is such that metastable phases such as the Fe ₃ B phase and the Nd ₂ Fe _{2 3} B phase are non-uniformly present, crystallization of the Fe ₃ B phase already exists, It was found that it progressed instantaneously and easily became a coarse tissue.

[0009] The present inventors have proposed an element M2 (Cu, Ag, Au) which has no solid solubility in Fe ₃ B type Nd-Fe-B nanocomposite magnet alloy system and has a large positive mixing enthalpy with Fe. Add a small amount, slow down the cooling rate in the ultra-quenching process, and specify the transit time in a temperature range (800 ° C to 500 ° C) where element diffusion in the solid is likely to occur, or in the normal ultra-quenching condition After rapid solidification and rapid cooling to around room temperature to make the whole amorphous, heat treatment at a specific temperature for a short time optimizes the structure of the raw alloy powder, crystallization of Fe ₃ B A high concentration of atoms of the M2 element (Cu, Ag, Au), which is the nucleus of, forms a structure in which atomic aggregates (clusters) with a diameter of 1 nm to 50 nm are uniformly dispersed in an amorphous matrix in a specific amount. are possible, with crystallization of the Fe ₃ B phase occurs uniformly, as in the conventional, instantaneous formation Rather than reduction, by proceeding gradually crystallized in the temperature raising process,
It has been found that the generation of heat of crystallization reaction is dispersed over a wide temperature range, and that a large amount of processed products can be heat-treated.

[0010] That is, the present inventors have a method of rapidly solidifying a molten alloy having a specific composition under a relatively slow quenching condition, and then passing the molten alloy through a specific temperature range for a predetermined time to cool it. After rapid solidification under quenching conditions and rapid cooling to around room temperature to make the whole amorphous, heat treatment at a specific temperature sufficiently lower than the crystallization temperature for a short time to obtain the desired metal composition Having found that the adjustment can be made, the present invention has been completed.

[0011] This invention is a composition _{formula, Fe 100-xyu R x B} y M2
_u , Fe _100-xywu R _x B _y M1 _w M2 _u , Fe _100-xyzu R _x B _y Co _z M
_{2 u, Fe 100-xyzwu R} x B y Co z M1 w M2 u ( where R is Nd or Pr
Containing 50% or more of one or two of M1, Al, Si, Ti, V, Cr, Mn,
One or more of Ni, Ga, Zr, Nb, Mo, Hf, Ta, W, Pt, Pb, M2
Is one or more of Cu, Ag, and Au), and the symbols x, y, z, w, and u that define the composition range are alloy melts satisfying the following values: 1) Cooling rate 10 After rapid solidification by ultra-rapid cooling in the range of ³ K / s to ³ × 10 ⁵ K / s, cool in the temperature range of 800 ° C to 500 ° C with a passage time of 1 ms to 1 s, or 2) Cooling rate 10 ⁴ K / s to 10 ⁶ K /
After rapid solidification by ultra-rapid cooling in the range of s, cool down to a temperature of 800 to 500 ° C so that the transit time is less than 1 ms, 400 ° C
By performing heat treatment for 1 minute to 60 minutes at a temperature range of ~ 550 ° C, 95% or more of the structure is a substantially amorphous phase,
M2 with a diameter of 1 nm to 50 nm in an amorphous matrix
For nanocomposite rare earth magnets using solute clusters, characterized by containing an atomic aggregate (cluster) in which atoms are accumulated at a concentration of 5 at% or more at a concentration of 10 ²² / m ³ to 10 ²⁵ / m ³ This is to obtain a raw material alloy. x: 1at% to 6at% y: 15at% to 30at% z: 0.01at% to 20at% w: 0.01at% to 7at% u: 0.005at% to 2at%

[0012]

BEST MODE FOR CARRYING OUT THE INVENTION Composition Reasons Rare earth element R is
In essential element of R ₂ Fe ₁₄ B AiAkirade necessary for coercivity expression, 50% or more of R is Pr, it is one or two Nd is R ₂ Fe
₁₄ It is necessary to impart uniaxial crystal magnetic anisotropy to the B phase, and any rare earth element can be selected for components other than Pr and Nd, but Tb and Dy It is preferred because it enhances.

[0013] When R is less than 1 at%, the effect of generating coercive force (iHc) is small.
No, and when it exceeds 6 at%, Fe _ThreeNo B phase is generated, α-F
The e phase becomes the main phase, and the coercive force (iHc) is significantly reduced.
Because it is not preferable, the range is 1 at% to 6 at%.

If B is less than 15 at% or more than 30 at%, the required coercive force (iHc) cannot be obtained, so B is set to 15 at% to 30 at%.

[0015] Co is preferable for stabilizing the jetting speed of the molten metal in the ultra-quenching process by improving the stability of the magnetic properties against temperature change by improving the Curie temperature and reducing the viscosity of the molten metal. If it is less than at%, such an effect cannot be obtained, and if it exceeds 20 at%, the magnetization is lowered, which is not preferable. Therefore, it is set to 0.01 at% to 20 at%.

[0016] The M1 element is Al, Si, Ti, V, Cr, Mn, Ni, Ga, Zr, Nb, Mo,
One or more of Hf, Ta, W, Pt, Pb is effective in increasing the coercive force (iHc), but less than 0.01 at%, the effect of increasing the coercive force (iHc) is small, and 7 at% If it exceeds, the magnetization decreases, so the addition amount is set to 0.01 at% to 7 at%.

The M2 element is an element having a large positive enthalpy of mixing with Fe and having a large negative enthalpy of mixing with R, specifically, one or more of Cu, Ag, and Au. M2
Has a large positive enthalpy of mixing with Fe in the amorphous phase, so that it separates from Fe and forms clusters at an extremely early stage of the heat treatment. In addition, since the M2 element has a large negative enthalpy of mixing with R at the same time, R aggregates into the M2 cluster to form an M2-R composite cluster.

As a result, B enrichment and R deficient regions occur at the cluster / amorphous interface, where fine Fe ₃ B is dispersed by nucleation of the Fe ₃ B phase. Since the R ₂ Fe ₁₄ B phase is formed from the remaining amorphous region, it is possible to refine the final nanocomposite structure by refining the first-stage crystallized structure in this way.

[0019] The M2 element is an essential element of the present invention, and after quenching and solidifying at a specific cooling rate, is cooled at a relatively slow cooling rate in a specific temperature range. Alternatively, after rapid solidification, when heat-treated for a short time at a temperature sufficiently lower than the crystallization temperature, the diameter is 1 nm to 50 n.
An m2 element aggregate (cluster) is formed at a specific concentration in the amorphous matrix, and acts as a crystallization nucleus of the Fe ₃ B phase during the subsequent heat treatment, suppressing the rapid progress of crystallization in the heat treatment process. This has the effect of suppressing the problem that the heat of reaction is generated due to the generation of reaction heat in a short time.

The concentration of the crystallization nuclei is 10 ²² / m ³ to 10 ²⁵ /
m ³ , when the concentration is less than 10 ²² / m ³ , the effect is small, and when it exceeds 10 ²⁵ / m ³ , Fe,
It is not preferable because the composition difference between the Nd and B phases is reduced, and the mechanism that the atomic cluster provides the preferential nucleation site of Fe ₃ B does not work.

[0021] The addition amount of the M2 element exhibiting the above mechanism is 0.01 at
If it is less than 2 at%, the effect is not obtained. If it exceeds 2 at%, the squareness of the demagnetization curve is deteriorated, and a high (BH) max cannot be obtained.

[0022] The concentration of the M2 element in the atomic aggregate (cluster) was measured by an atom probe and found to be 5 vol% or more. The structure was basically amorphous, and a specific long-period crystal structure was observed. I have nothing.

[0023] The raw material alloy according to the present invention solidifies a molten alloy having a specific composition by ultra-rapid cooling to a specific cooling rate.
It can be manufactured by controlling the transit time in a specific temperature range, or by quenching and solidifying by a rapid quenching method, and then heat-treating it under specific heat treatment conditions. Phase or a small amount of α-Fe phase (γ-Fe at the time of formation, which is considered to be phase transformed) may contain less than 5 vol%, but the amorphous phase
If the content is less than 95 vol%, the magnetic properties, particularly the squareness of the demagnetization curve are reduced after the heat treatment, and the (BH) max value is undesirably reduced.

Reasons for Limiting Manufacturing Conditions There are two methods for manufacturing the raw material alloy of the present invention. The first method is to rapidly solidify a molten alloy having a specific composition under relatively slow quenching conditions. After that, it is a method of cooling by passing through a specific temperature range for a predetermined time, the second method is rapidly solidified under normal ultra-quenching conditions, and rapidly cooled to around room temperature to make the whole amorphous rear,
Heat treatment at a specific temperature for a short time
(Cluster).

That is, in the first method, if the cooling rate in the ultra-quenching process of the molten alloy exceeds 3 × 10 ⁵ K / s, the whole becomes a homogeneous amorphous phase, and the crystallization nuclei of the Fe ₃ B phase The concentration of M2 atomic clusters (clusters) that act as a catalyst decreases, and crystallization in the subsequent crystallization heat treatment process proceeds rapidly and instantaneously, making it difficult to control the structure.If it is less than 10 ³ K / s, amorphous No phase is formed, and the α-Fe phase
-Fe, which is considered to be a phase transformation), is not preferable because a coarse resin layer is formed, and a required nanocomposite structure cannot be obtained by a subsequent heat treatment.

The reason why the cooling time after rapid solidification by the ultra-quenching method is limited to a time of 1 msec to 1 sec in a temperature section of 800 ° C. to 500 ° C. is that an aggregate (cluster) of M2 atoms is less than 1 ms. If it does not grow sufficiently, and if it exceeds 1 s, the cooling rate is too slow and crystallization proceeds, and the structure becomes uneven due to local fluctuation of the cooling rate, and it becomes difficult to control the structure in the subsequent crystallization heat treatment. Not preferred.

[0027] The temperature range from 800 ° C to 500 ° C is a temperature range in which solidification of the quenched alloy is completed and becomes metallic glass, and is a temperature range in which atom diffusion in a solid occurs. The cooling rate is preferably 10 ³ K / s to ³ × 10 ⁵ K / s,
If the temperature is lower than 00 ° C, the diffusion of the element is generally slow.Therefore, it is not necessary to particularly limit the passage time in the cooling process. ) Causes a change in the metal structure such as coarsening and progress of crystallization, which makes it difficult to control crystallization in the subsequent heat treatment process, which is not preferable.

In the present invention, by dispersing the M2 element as a fine aggregate in the amorphous matrix,
To act as a crystallization nucleus of Fe ₃ B phase, to facilitate finely dispersed microstructure control of the rare earth magnet of Fe ₃ B phase, which is generated by the subsequent heat treatment process and Nd ₂ Fe ₁₄ B phase, excellent magnetic properties It is intended to provide a raw material alloy from which a rare-earth magnet can be obtained.

[0029] The second method is to perform ordinary ultra-rapid cooling,
After the whole is substantially amorphized, the temperature is raised again and a short-time heat treatment is performed at 400 ° C. to 550 ° C. to obtain M2.
It is a method of generating atomic aggregates (clusters) of elements,
Since a crystallization reaction does not occur in the heat treatment at 400 ° C. to 550 ° C., a large amount of heat treatment can be performed at a time, and this method is suitable as an industrial practice method.

In the alloy system of the present invention, the
10^FourK / s ~ 10⁶Ultra-rapid cooling at a cooling rate of K / s
Preferably, even more preferably 3-8 × 10^FiveK / s is good.
Cooling rate of 10 in the rapid quenching method^FourAmo below K / s
It does not become Rufus, and 10 ⁶Extremely rapid at cooling rates above K / s
Cooling measures for the cooling rolls of the refrigeration equipment are large and preferable.
No, 10⁶It is not necessary to have a cooling rate higher than K / s.

[0031]

Example 1 An alloy having a composition of Nd _4.5 Fe _73-x Co ₃ Ga ₁ B _18.5 Cu _x (x = 0.3) was melt-spinned at a cooling rate of about 4 × 10 ⁵ K / s at 800 ° C.
Cooling time of about 0.8ms from 600 ° C to 530 ° C
For 7 minutes and cooled to room temperature at a cooling rate of about 50 ° C./min to obtain a raw material for a nanocomposite magnet.

This raw material alloy was a thin ribbon having a thickness of about 90 μm.
The thin ribbon was measured for powder X-ray pattern using characteristic X-rays of Cu.
ol% or less of a metastable phase diffraction line was observed. From this ribbon carved acicular sample further was subjected to by processing the atom probe microscope article 3-dimensional atom probe analysis by electrolytic polishing, Cu atoms aggregate diameter approximately 1~2nm approximately 10 ²⁴ / it was observed that present at a density of m ^3.

[0033] The raw material alloy, width 100mm, heating section length 900mm,
100μm thickness in 1000mm metal hoop belt furnace with cooling section length
Using a stainless steel hoop belt in an argon gas flow, feed rate 200 mm / min, raw material feed rate 5 kg / hour, when the continuous heat treatment was performed at furnace atmosphere temperature 600 ° C., on average (BH) max = 136 kJ Magnet properties of / m ³ , Br = 1.1T and HcJ = 310 kA / m were obtained.

Comparative Example 1 In the composition formula of Example 1, x = 0 (that is, containing no Cu)
Cooling rate of alloy about 10 ⁶Cool at K / s condition, and 800 ℃
From 600 ° C to about 600μs to cool rapidly
This was used as a raw material alloy without heat treatment.

According to X-ray diffraction, the alloy ribbon was almost completely amorphous, and no diffraction line of a crystalline phase was observed. Further, according to the result of analysis by a transmission microscope, Fe ₃ fine crystalline phase is sparsely 10 B in an amorphous matrix ²²
It was confirmed that the particles were dispersed at a density of about particles / m ³ . If this raw material alloy was subjected to heat treatment under the same conditions as in Example 1, sufficient magnet properties could not be obtained, (BH) max = 86 kJ / m ³ , Br = 0.93 T, H
Only magnet properties of cJ = 220 kA / m were obtained.

In the comparative example, in order to obtain the same magnetic properties as in Example 1, it is necessary to set the feed speed of the hoop belt to 100 mm / S, the raw material feed rate to 1 kg / min, and the furnace atmosphere temperature to 620 ° C. It was found that the productivity of the heat treatment process was significantly different.

Example 2 Alloys having the compositions shown in Table 1 were rapidly solidified by the melt spinning method under the conditions shown, and some of them were subjected to heat treatment to obtain a raw material for a nanocomposite magnet. These materials are at least 97 vol% from X-ray diffraction results
The above was amorphous and had a structure in which some metastable crystal phases were present.

These raw materials were heat-treated at a temperature shown in Table 2 at a raw material feed rate of 20 kg / h using a rotary tube type heat treatment furnace having an inner diameter of 130 mm and a total length of 3 m (including a heating section of 1.2 m and a cooling section of 1.8 m). The magnet properties obtained at this time were as shown in Table 2.

Comparative Example 2 The alloy of Table 3 (composition obtained by removing the M2 element from the composition shown in Table 1) was rapidly solidified at a cooling rate of about 6 × 10 ⁵ K / s,
Cooled rapidly with a residence time above 500C for about 500 μs. X-ray diffraction showed that nearly 100% of these alloys were in the amorphous phase. Using these alloys as raw materials, using the same apparatus as shown in Example 2 and performing heat treatment under the same conditions, the demagnetization curves were all bad in square shape, and (BH) max was all 95k.
It was less than J / m ^3.

[0040] In the comparative example, in order to obtain the same magnetic properties as the alloy shown in Example 2, it is necessary to set the feed rate of the raw material to about 5 kg / h. It was found that the productivity of the products differed greatly.

[0041]

【table 1】

[0042]

[Table 2]

[0043]

[Table 3]

[0044]

According to the present invention, the element M2 (Cu, Ag, Au) is added in a small amount, the cooling rate in the ultra-quenching process is reduced, and the temperature range (800 ° C. (500 ° C), or by increasing the cooling rate in the ultra-quenching process and then heat-treating it to a specific temperature, to optimize the structure of the raw alloy powder and the core of Fe ₃ B crystallization. Atoms of the M2 element (Cu, Ag, Au) accumulate in high concentration
By forming a structure in which an atomic aggregate (cluster) of 1 nm to 50 nm is uniformly dispersed in a specific amount in an amorphous matrix, crystallization of the Fe ₃ B phase occurs uniformly, and instead of instantaneous crystallization as in the related art, By gradually progressing the crystallization during the temperature raising process, the generation of heat of crystallization reaction is dispersed in a wide temperature range, and a large amount of the alloy can be heat-treated, thereby improving the productivity.

 ──────────────────────────────────────────────────続 き Continuing on the front page (72) Inventor Hirokazu Kanei 2-15-17 Egawa, Shimamoto-cho, Mishima-gun, Osaka Sumitomo Special Metals Co., Ltd. Yamazaki Works (72) Inventor Yasuhiko Shigeki Shimamoto-cho, Mishima-gun, Osaka 2-15-17 Egawa Sumitomo Special Metals Co., Ltd.Yamazaki Works (72) Inventor Kazuhiro Takano 1-2-1 Sengen, Tsukuba-shi, Ibaraki Prefectural Agency for Science and Technology Agency Metal Materials Research Laboratory (72) Inventor Tokuumi Taira Ibaraki 1-2-1 Sengen, Tsukuba, Japan F-term (Reference) 4K018 AA27 BA18 BB06 BB07 BC01 BD01 KA45 KA46 5E040 AA04 AA19 BD00 BD03 CA01 HB07 HB11 HB15 NN01 NN06 NN17 NN18

Claims (6)

[Claims] 1. A composition formula _{Fe 100-xyu R x B y} M2 u ( where R is Nd
Or containing 50% or more of one or two types of Pr, M2 is one of Cu, Ag, Au
Species or two or more), the symbols x, y,
u satisfies the following values, and the structure is 95% or more of a substantially amorphous phase and has a diameter within the amorphous matrix.
A solute cluster characterized by containing an atomic aggregate (cluster) in which M2 atoms of 1 nm to 50 nm are accumulated at a concentration of 5 at% or more at a concentration of 10 ²² / m ³ to 10 ²⁵ / m ³ is used. Raw material alloy for nanocomposite rare earth magnets. x: 1at% to 6at% y: 15at% to 30at% u: 0.005at% to 2at% 2. A method composition formula _{Fe 100-xywu R x B y} M1 w M2 u ( where R
Contains 50% or more of one or two kinds of Nd or Pr, and M1 is Al, Si, T
One or two of i, V, Cr, Mn, Ni, Ga, Zr, Nb, Mo, Hf, Ta, W, Pt, Pb
Or more, M2 represents one or more of Cu, Ag, and Au), and the symbols x, y, w, and u defining the composition range satisfy the following values, and the structure is substantially 95 vol% or more. 5at% of M2 atoms in the amorphous phase and 1-50nm in diameter in the amorphous matrix
10 ²² atomic aggregates (clusters) accumulated at the above concentrations
/ m ³ to 10 ²⁵ cells / m nanocomposite rare earth material alloy for a magnet using solute clusters characterized in that it contains a concentration of ^3. x: 1at% to 6at% y: 15at% to 30at% w: 0.01at% to 7at% u: 0.005at% to 2at% The 3. A composition formula _{Fe 100-xyzu R x B y} Co z M2 u ( where R
Contains 50% or more of one or two of Nd or Pr, M2 is Cu, Ag, A
(one or more of u) and a symbol that defines the composition range
x, y, z, u satisfy the following values, and the structure is an atomic group in which 95 vol% or more is a substantially amorphous phase and M2 atoms with a diameter of 1 nm to 50 nm are accumulated in an amorphous matrix at a concentration of 5 at% or more. A raw material alloy for a nanocomposite rare earth magnet using a solute cluster, characterized by containing a body (cluster) at a concentration of 10 ²² / m ³ to 10 ²⁵ / m ³ . x: 1at% to 6at% y: 15at% to 30at% z: 0.01at% to 20at% u: 0.005at% to 2at% The 4. A composition formula _{Fe 100-xyzwu R x B y} Co z M1 w M2
_u (where R contains 50% or more of one or two of Nd or Pr, M1 is
Al, Si, Ti, V, Cr, Mn, Ni, Ga, Zr, Nb, Mo, Hf, Ta, W, Pt, Pb, one or more, M2 is one of Cu, Ag, Au or 2 or more), the symbols x, y, z, w, u that define the composition range satisfy the following values, the structure is 95% or more of a substantially amorphous phase, and a diameter of 1 nm to Atomic aggregate (cluster) of 50nm M2 atoms accumulated at a concentration of 5at% or more
10 ²² / m ³ to 10 ²⁵ cells / m nanocomposite rare earth magnet material alloy that utilizes a solute clusters characterized in that it contains a concentration of ^3. x: 1at% to 6at% y: 15at% to 30at% z: 0.01at% to 20at% w: 0.01at% to 7at% u: 0.005at% to 2at% 5. A composition formula _{Fe 100-xyu R x B y} M2 u, Fe
_{100-xywu R x B y M1} w M2 u, Fe 100-xyzu R x B y Co z M2 u, F
_{e 100-xyzwu R x B y} Co z M1 w M2 u ( where R is 50% or more of one or two kinds of Nd or Pr, M1 is Al, Si, Ti, V, Cr, Mn, Ni, Ga , Z
One or more of r, Nb, Mo, Hf, Ta, W, Pt, Pb, M2 is Cu, A
g, one or more of Au), the symbols x, y, z, w, u that define the composition range satisfy the following values, and the cooling rate is 10 ³ K / s or more. After rapid solidification by the rapid quenching method in the range of 3 × 10 ⁵ K / s, the passage time in the temperature range of 800 ° C to 500 ° C is 1 ms.
A method for producing a raw alloy for a nanocomposite rare earth magnet using a solute cluster, characterized in that the alloy is cooled in 1 second. x: 1at% to 6at% y: 15at% to 30at% z: 0.01at% to 20at% w: 0.01at% to 7at% u: 0.005at% to 2at% 6. A composition formula _{Fe 100-xyu R x B y} M2 u, Fe
_{100-xywu R x B y M1} w M2 u, Fe 100-xyzu R x B y Co z M2 u, F
_{e 100-xyzwu R x B y} Co z M1 w M2 u ( where R is 50% or more of one or two kinds of Nd or Pr, M1 is Al, Si, Ti, V, Cr, Mn, Ni, Ga , Z
One or more of r, Nb, Mo, Hf, Ta, W, Pt, Pb, M2 is Cu, A
g, one or two or more of Au), and the symbols x, y, z, w, u that define the composition range satisfy the following values, and the cooling rate is 10 ⁴ K / s or more. After rapid solidification by the rapid quenching method in the range of 10 ⁶ K / s, it is cooled so that the passage time in the temperature range of 800 ° C to 500 ° C is less than 1 ms, and 1 minute in the temperature range of 400 ° C to 550 ° C. A method for producing a raw alloy for a nanocomposite rare-earth magnet using a solute cluster, wherein a heat treatment is performed for up to 60 minutes. x: 1at% to 6at% y: 15at% to 30at% z: 0.01at% to 20at% w: 0.01at% to 7at% u: 0.005at% to 2at%