Patent Grant
11967455
The present application claims priority to Chinese Patent Application No. 201811471014.6 filed to the SIPO on Dec. 4, 2018 and entitled “METHOD FOR PREPARING RARE-EARTH PERMANENT MAGNET BY HOT PRESS MOLDING”, the disclosure of which is incorporated herein by reference in its entirety.
The present invention relates to a method for preparing a neodymium-iron-boron rare-earth permanent magnetic material, in particular to a method for preparing a rare-earth permanent magnet by hot press molding.
Chinese Patent Application 201410094229.6 has disclosed a method for preparing a permanent magnetic material by hot pressing. In this method, a first material containing Nd, Fe and B in the form of core powder and a second material containing Dy and Tb in the form of metal alloy or in the form of surface powder are combined to form a coated composite-like material, which has a non-uniform distribution of Dy or Tb constituting the second material. Then, hot press molding is performed on the coated composite-like material. In the prior art or industrial production, it is impossible to coat a film in 1 nm to 10 nm onto the surfaces of particles in 1 μm to 5 μm. The provided coating schemes such as mechanical grinding, vortex coating, ion sputtering and high-pressure particle sputtering are difficult to implement in practice. It is described that a film in 1 μm to 100 μm is coated. The thickness of the film is already close to the size of the particles. Excessive rich phase will definitely reduce the performance of the material, even make it lower than the performance of the existing sintered magnet.
To solve the above-mentioned deficiencies and problems in the prior art, the present invention provides a method for preparing a rare-earth permanent magnet by hot press molding.
The present invention is realized by the following technical solutions. A method for preparing a rare-earth permanent magnet by hot press molding is provided, including steps of:
1) smelting an RFeB alloy, where R is any one of Nd, Pr, Dy, Tb, Ce, La, Gd, Ho and Y, or any combination of two or more of Nd, Pr, Dy, Tb, Ce, La, Gd, Ho and Y, and the content of the rare-earth R in the RFeB alloy is 27.5% to 30.5% by mass; the RFeB alloy further contains 0.2% to 2% by mass of a metal composition; the metal composition is any one of Al, Cu, Ga, Zr and Nb, or any combination of two or more of Al, Cu, Ga, Zr and Nb in any ratio; and 1% to 10% Fe is replaced with Co;
2) performing HD treatment on the master alloy, and permeating an RTM alloy during this process, where RT is any one of Nd, Pr, Dy, Tb, Gd, Ho, Y and Sc, or any combination of two or more of Nd, Pr, Dy, Tb, Gd, Ho, Y and Sc in any ratio, and M is any one of Cu, Al and Ga, or any combination of two or more of Cu, Al and Ga in any ratio;
3) performing jet pulverization on the product obtained in the step 2);
4) molding under a magnetic field at room temperature;
5) preheating the green body in vacuum;
6) performing hot pressing on the green body to further improve the density; and
7) aging to obtain the magnet.
After the saturated hydrogen adsorption in the HD process, the temperature is raised to 750° C. to 950° C. for permeation, and RTM will adhere to the surface of powder and permeate into the alloy along a grain boundary.
During the subsequent jet pulverization, the product obtained in the step 2) is pulverized to 1 μm to 6 μm.
After a magnetic field orientation molding, the green body is fully preheated in vacuum at 650° C. to 950° C. The absorbed gas was discharged, and various organic additives and residual hydrogen are volatilized.
The preheated green body is immediately loaded into a mold having a temperature close to the preheating temperature, and a pressure of 25 to 120 MPa is applied for hot pressing. The density reaches 99.8% to 99.9% of the theoretical density. The melted rich phase squeezes into the gap under pressure, increasing the density.
At this temperature, grains barely grow and are maintained in a size after jet pulverization. If the infiltrated rare-earth element is different from the main phase, during preheating and aging treatment, the rare-earth element will partially diffuse into the surface layer of the main phase. If an element with a high anisotropic field such as Dy, Tb or Ho is used for permeation, the effect of hardening the grain boundary is achieved. The coercive force is greatly improved, while the residual magnetism is reduced less.
As an existing well-known technology, the hot press molding technology has been widely used in ceramics, cemented carbide or other fields. By combining the hot press molding technology with the existing neodymium-iron-boron technology, the coercive force can reach above 1350 KA/m without adding any heavy rate-earth element. By permeating a trace amount of elements with a high anisotropic field such as Dy, Tb and Ho, the coercive force can reach above 2388 KA/m.
Further, in the step 2), the permeation amount of the RTM alloy is 0.5% to 4.5% of the mass of the master alloy. The element and the amount for permeation are selected according to the requirements for the performance of the magnet. Thus, the performance of the magnetic material is ensured, the consumption of materials is optimized, and the cost is reduced.
Furthermore, the infiltration material is RTM alloy in the step 2), RT accounts for 65% to 100%, and M accounts for 0% to 35%. By adding metals Cu, Al and Ga, the wettability and fluidity of the liquid phase can be improved, and it is beneficial to reduce the pressure of hot pressing. The selection of rare-earth elements depends on the required performance of the magnet. For products requiring a coercive force below 1350 KA/m, Nd, Pr and Gd are selected. For products requiring a coercive force above 1350 KA/m, Dy, Tb and Ho elements should be selected.
The performance of the magnetic material obtained by the method of the present invention is greatly improved in comparison to the prior art. The amount of heavy rare-earth elements is reduced or completely saved.
A method for preparing a rare-earth permanent magnet by hot press molding is provided, including steps of:
1) smelting an RFeB alloy, where R is any one of Nd, Pr, Dy, Tb, Ce, La, Gd, Ho and Y, or any combination of two or more of Nd, Pr, Dy, Tb, Ce, La, Gd, Ho and Y, and the content of the rare-earth R in the RFeB alloy is 27.5% to 30.5% (e.g., optionally 27.5%, 28%, 28.5%, 29% or 30.5%) by mass; the RFeB alloy further contains 0.2% to 2% (e.g., optionally 0.2%, 0.5%, 0.8%, 1.0%, 1.5% or 2%) by mass of a metal composition; the metal composition is any one of Al, Cu, Ga, Zr and Nb, or any combination of two or more of Al, Cu, Ga, Zr and Nb in any ratio; and 1% to 10% Fe is replaced with Co;
2) performing HD treatment on the master alloy, and permeating an RTM alloy during this process, where RT is any one of Nd, Pr, Dy, Tb, Gd, Ho, Y and Sc, or any combination of two or more of Nd, Pr, Dy, Tb, Gd, Ho, Y and Sc in any ratio, and M is any one of Cu, Al and Ga, or any combination of two or more of Cu, Al and Ga in any ratio;
3) performing jet pulverization on the product obtained in the step 2);
4) molding under a magnetic field at room temperature;
5) preheating the green body in vacuum;
6) performing hot pressing on the green body to further improve the density; and
7) aging to obtain the magnet.
In the step 2), the permeation amount of the RTM alloy is 0.5% to 4.5% (e.g., optionally 0.5%, 1%, 2%, 3%, 3.5%, 4% or 4.5%) of the mass of the RFeB alloy.
In the RTM alloy in the step 2), RT accounts for 65% to 100%, and M accounts for 0% to 35% (e.g., optionally, RT accounts for 65% and M accounts for 35%; RT accounts for 100% and M accounts for 0%; RT accounts for 75% and M accounts for 25%; RT accounts for 85% and M accounts for 15%; or, RT accounts for 95% and M accounts for 5%).
The RTM alloy may be replaced with an RTFeB alloy. RT is any one of Nd, Pr, Dy, Tb, Gd, Ho, Y and Sc, or any combination of two or more of Nd, Pr, Dy, Tb, Gd, Ho, Y and Sc in any ratio, and the content of RT exceeds 50% of the mass of the RTFeB alloy.
In the step 1), the RFeB alloy is obtained by smelting RFeB alloy quick-setting sheets in which the content of rare-earth R is 27.5% to 30.5% by mass.
In the step 2), the HD treatment process includes steps of:
a) mixing the RTM alloy powder in 1 μm to 100 μm with a quick-setting sheet alloy and loading the mixture into an HD treatment furnace;
b) filling with hydrogen after the vacuum degree reaches 0.1 Pa, maintaining the pressure at 0.05 MPa to 0.2 MPa (e.g., optionally 0.05 MPa, 0.1 MPa, 0.15 MPa or 0.2 MPa), and performing saturated hydrogen absorption;
c) permeating and dehydrogenating for 60 min to 240 min (e.g., optionally 60 min, 120 min, 180 min or 240 min) at 750° C. to 950° C. (e.g., optionally 750° C., 800° C., 850° C., 900° C. or 950° C.);
d) stopping heating, cooling to 200° C., and performing secondary hydrogen absorption, where the hydrogen absorption amount is 500 to 1000 ppm (e.g., optionally 500 ppm, 600 ppm, 700 ppm, 800 ppm, 900 ppm or 1000 ppm); and
e) feeding Ar, cooling with water to room temperature, sealing and taking out from the furnace.
During the jet pulverization in the step 3), compressed N2 is used as power, and grinding is performed until the average particle size is 1 μm to 6 μm (e.g., optionally 1 μm, 2 μm, 3 μm, 4 μm, 5 μm or 6 μm).
In the step 4), molding is performed under a magnetic field at room temperature. Pressing is performed under an orientation magnetic field with an intensity greater than 1.2 T. The density is 3.6 to 4.2 g/cm2, and the exposed space has an oxygen concentration less than 500 PPM. To further improve the density, it is possible to perform secondary molding, i.e., isostatic pressing. The pressure for isostatic pressing is 150 MPa to 300 MPa (e.g., optionally 150 MPa, 210 MPa, 250 MPa or 300 MPa).
During the preheating in the step 5), preheating is performed for 1 h to 10 h (e.g., optionally 1 h, 2 h, 3 h, 4 h, 5 h, 6 h, 7 h, 8 h, 9 h or 10 h) at 650° C. to 950° C. (e.g., optionally 650° C., 700° C., 800° C., 900° C. or 950° C.).
In the step 6), at the end of preheating, the green body is immediately loaded into a mold cavity having a temperature close to the preheating temperature, and a pressure of 25 to 120 MPa (e.g., optionally 25 MPa, 40 MPa, 50 MPa, 60 MPa, 90 MPa or 120 MPa) is applied and maintained for 0.3 min to 10 min (e.g., optionally 0.3 min, 0.5 min, 0.8 min, 1 min, 3 min, 5 min, 6 min, 8 min, 9 min or 10 min). Hot pressing is performed in an inert gas having an oxygen content less than 200 PPM, and the pressure is 0 MPa, that is, there is no pressure difference between the inert gas and the outside. The green body is naturally or forcedly cooled to the room temperature.
The cross-section size of the hot pressing mold in the step 6) is increased by 0.05 mm to 0.2 mm according to the size of the preheated green body after shrinkage, so as to facilitate molding.
In the step 7), the hot-pressed product may be aged at an aging temperature of 450° C. to 950° C. (e.g., optionally 450° C., 500° C., 600° C., 700° C., 800° C., 900° C. or 950° C.).
The material formulation of the RFeB alloy was as follows:
The materials were smelted in vacuum according to the formulation, and treated by quick-setting spinning to obtain the RFeB alloy, i.e., quick-setting sheets, having a thickness of 0.20 mm to 0.45 mm.
The quick-setting sheets were processed by the method of the present application. The RTM alloy infiltrated during the HD process was DyCu alloy powder, where Nd accounted for 90% and Cu accounted for 10%.
To ensure the performance, it was required that there was no oxide layer on the surfaces of the quick-setting sheets and the discharging of the quick-setting furnace was performed in a sealed barrel. When loaded into a hydrogen pulverizating furnace, the quick-setting sheets should be strictly protected from contact with air.
The quick-setting sheets and the DyCu alloy powder in an amount that was 1% of the total mass of the quick-setting sheets were loaded into a treatment furnace. After the vacuum degree reached 0.1 Pa, saturated hydrogen absorption was performed at a hydrogen pressure of 0.05 MPa to 0.2 MPa. Subsequently, dehydrogenation was performed for 120 min at 900° C. Then, heating was stopped, and the vacuum state was maintained. Cooled to 200° C. and subjected to secondary hydrogen absorption in a hydrogen absorption amount of 800 ppm, and then cooled, sealed and discharged. The jet pulverization was performed until the average particle size was 2 μm to 4 μm.
The experimental mold was 25*50 mm in size, and the mold cavity was 150 mm in depth. Molding was performed under a magnetic field in a low-oxygen environment having an oxygen concentration less than 500 ppm, 525 g of magnetic powder was added, a pressure of 15 Ton was applied, to obtain a green body in 25*50*50. The green body was preheated in vacuum at a vacuum degree of 0.01 Pa and at 900° C., then placed into the mold cavity, and maintained for 60 s at 40 MPa to realize a density of 7.6 g/cm2. Cooled and aged at 900° C. to obtain the product with magnetic performance 55 H. The residual magnetism was 14.5 KGs, and the HcJ was 1350 KA/m.
The material formulation of the RFeB alloy was as follows:
The materials were smelted in vacuum according to the formulation, and treated by quick-setting spinning to obtain the RFeB alloy, i.e., quick-setting sheets, having a thickness of 0.20 mm to 0.45 mm.
A TbCuAl alloy and powder thereof were prepared, where Tb accounted for 80%, Cu accounted for 10%, and Al accounted for 10% (mass percentage).
The same implementation method as Embodiment 1 was executed. During this process, part of TbCuAl adhered to the surfaces of coarse particles subjected to hydrogen pulverizating, while part of TbCuAl diffused into coarse powder.
Jet pulverization, molding under a magnetic field, vacuum preheating, hot pressing and tempering were performed by methods the same as those in Embodiment 1. The product with magnetic performance 50 EH was obtained. The residual magnetism was 14.0 KGs, and the HcJ was 2388 KA/m.
| Number | Date | Country | Kind |
|---|---|---|---|
| 201811471014.6 | Dec 2018 | CN | national |
| Filing Document | Filing Date | Country | Kind |
|---|---|---|---|
| PCT/CN2019/122766 | 12/3/2019 | WO |
| Publishing Document | Publishing Date | Country | Kind |
|---|---|---|---|
| WO2020/114398 | 6/11/2020 | WO | A |
| Number | Name | Date | Kind |
|---|---|---|---|
| 9845545 | Kuribayashi et al. | Dec 2017 | B2 |
| 10526715 | Kuribayashi et al. | Jan 2020 | B2 |
| 20150233006 | Kuribayashi et al. | Aug 2015 | A1 |
| 20180044810 | Kuribayashi et al. | Feb 2018 | A1 |
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| Number | Date | Country | |
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| 20210383968 A1 | Dec 2021 | US |
