Patent Application
20240331937
The present disclosure relates to the technical field of rare earth permanent magnet materials, and in particular to a method for preparing an anisotropic flake nanocrystalline rare earth permanent magnet material and a rare earth permanent magnet material.
RE-Fe—B rare earth permanent magnet materials have become an important foundation for the development of industries such as high-tech and clean energy due to their excellent magnetic properties, and serve as indispensable functional materials in supporting the implementation of Chinese national strategies such as “Made in China 2025” and “Internet+”.
The RE2Fe14B phase in the RE-Fe—B rare earth permanent magnet material has a tetragonal structure and shows strong uniaxial anisotropy. Ideally, the magnetic properties of anisotropic permanent magnet materials are twice those of isotropic permanent magnet materials. Anisotropic permanent magnet materials include anisotropic powder materials and anisotropic bulk materials. The anisotropic powder material can be oriented and arranged in an adhesive under the action of a magnetic field force or mechanical force, thereby preparing an anisotropic bonded bulk material. In addition to directly from the anisotropic powder materials, the anisotropic bulk material can also be prepared from isotropic powder materials through hot deformation, which causes RE2Fe14B grains to undergo dissolution and precipitation to allow preferential growth, thereby forming an oriented texture to achieve anisotropy. It can be seen that an orientation degree of anisotropic permanent magnet materials is a key determinant of the magnetic properties of the materials.
Chinese patent No. 200610147137.5 provided a preparation method of an anisotropic nanocrystalline rare earth permanent magnet magnetic powder. By conducting hot rolling on a rapid-quenching magnetic powder, the rapid-quenching magnetic powder is plastically deformed, thereby forming an oriented texture. Due to a short hot rolling time, the magnetic powder shows a poor orientation degree, and the hot rolling is conducted twice to improve the orientation degree. However, a large amount of residual stress may inevitably be generated in the powder after repeated hot rolling. As a result, the prepared magnetic powder shows a poor coercivity (10.7 kOe), and the magnetic properties need to be improved. Chinese patent No. 201110428088.3 provided an anisotropic nanocrystalline composite permanent magnet material and a preparation method thereof. A nanocrystalline magnetic powder is prepared by rapid quenching or mechanical alloying, and an anisotropic magnet is prepared by hot pressing and hot deformation. After crushing, a rare earth-rich phase in the magnet is removed by acid etching to obtain anisotropic flake grains. A surface of the anisotropic flake grains is coated or cladded with a soft magnetic phase to obtain nanocomposite flake grains. The nanocomposite flake grains are prepared into a full-density anisotropic nanocrystalline composite magnetic material by hot pressing, with a magnetic energy product reaching not less than 42 MGOe. However, the preparation method has a complex process that is difficult to control, a long production cycle, and a poor production efficiency, and is not conducive to large-scale industrial promotion.
Therefore, there is an urgent need to develop a preparation method of an anisotropic rare earth permanent magnet material, thus enhancing magnetic properties of the anisotropic rare earth permanent magnet material while simplifying the process and improving a production efficiency.
An object of the present disclosure is to provide a method for preparing an anisotropic flake nanocrystalline rare earth permanent magnet material and a rare earth permanent magnet material. The present disclosure is intended to enhance magnetic properties of the anisotropic rare earth permanent magnet material while simplifying a process and improving a production efficiency.
In a first aspect, the present disclosure provides a method for preparing an anisotropic flake nanocrystalline rare earth permanent magnet material, including the following steps:
In some embodiments, the magnetic powder of the rare earth permanent magnet has a nominal composition of RExFe100-x-y-zTMyBz, where RE is one or more selected from the group consisting of La, Ce, Pr, Nd, Y, Dy, and Tb, TM is one or more selected from the group consisting of Co, Zr, Cr, V, Nb, Si, Ti, Mo, Mn, W, Ga, Cu, Al, and Zn, and x, y, and z each represent a mass fraction of an element, and 26.0≤x≤36.0, 0.14≤y≤8.0, and 0.8≤z≤1.36.
In some embodiments, the preparation of the precursor flake nanocrystalline magnetic powder in step 1 is conducted by subjecting the magnetic powder of the rare earth permanent magnet to the heat preservation at the temperature of 710° C. to 740° C. for 5 min to 100 min under vacuum or the protective atmosphere to obtain the precursor flake nanocrystalline magnetic powder, where the number of the grains of the flake nanocrystals inside the precursor flake nanocrystalline magnetic powder accounts for not less than 85% of the total number of the grains inside the precursor flake nanocrystalline magnetic powder; and the flake nanocrystals have the average grain size of 50 nm to 150 nm in the grain thickness direction and the average grain size of 150 nm to 600 nm in the grain length direction.
In some embodiments, the preparation of the precursor flake nanocrystalline magnetic powder in step 1 is conducted by subjecting the magnetic powder of the rare earth permanent magnet to the heat preservation at the temperature of 710° C. to 740° C. for 15 min to 60 min under vacuum or the protective atmosphere to obtain the precursor flake nanocrystalline magnetic powder, where the number of the grains of the flake nanocrystals inside the precursor flake nanocrystalline magnetic powder accounts for not less than 85% of the total number of the grains inside the precursor flake nanocrystalline magnetic powder; and the flake nanocrystals have the average grain size of 60 nm to 100 nm in the grain thickness direction and the average grain size of 180 nm to 400 nm in the grain length direction.
In some embodiments, the hot deformation in the orientation treatment by the hot deformation in step 2 is conducted by one or more selected from the group consisting of hot rolling deformation, hot pressing deformation, and hot extrusion deformation.
In some embodiments, the hot rolling deformation is conducted by subjecting the precursor flake nanocrystalline magnetic powder to the hot rolling deformation under vacuum or a protective atmosphere at a temperature of 600° C. to 850° C. with a deformation amount of 50% to 90% in a thickness direction of the precursor flake nanocrystalline magnetic powder, such that the flake nanocrystals are regularly arranged.
In some embodiments, the hot pressing deformation is conducted by vacuum packaging the precursor flake nanocrystalline magnetic powder with a packaging material to obtain the package, and subjecting the package to the hot pressing deformation at a temperature of 600° C. to 850° C. with a deformation rate of 0.02 mm/s to 3 mm/s and a deformation amount of the package of 50% to 90% in a hot pressing direction, such that the flake nanocrystals are regularly arranged.
In some embodiments, the hot pressing deformation is conducted by preparing the precursor flake nanocrystalline magnetic powder into a green body with a density of 65.0% to 99.9% at a temperature of room temperature to 800° C., and subjecting the green body to the hot pressing deformation at a temperature of 600° C. to 850° C. with a deformation rate of 0.02 mm/s to 3 mm/s and a deformation amount of the green body of 50% to 90% in a hot pressing direction, such that the flake nanocrystals are regularly arranged.
In some embodiments, the hot extrusion deformation is conducted by preparing the precursor flake nanocrystalline magnetic powder into a green body with a density of 65.0% to 99.9% at a temperature of room temperature to 800° C., and subjecting the green body to the hot extrusion deformation at a temperature of 600° C. to 850° C. with a deformation rate of 0.02 mm/s to 3 mm/s, such that the flake nanocrystals are regularly arranged.
In a second aspect, the present disclosure provides an anisotropic flake nanocrystalline rare earth permanent magnet material prepared by the above method for preparing an anisotropic flake nanocrystalline rare earth permanent magnet material.
To sum up, the present disclosure has at least one of the following beneficial effects:
The present disclosure provides a method for preparing an anisotropic flake nanocrystalline rare earth permanent magnet material and a rare earth permanent magnet material. To make the objects, technical solutions, and effects of the present disclosure clear, the following further describes the present disclosure in detail. It should be understood that the specific embodiments described herein are only intended to explain the present disclosure and are not intended to limit the present disclosure.
A RE2Fe14B phase in the RE-Fe—B rare earth permanent magnet material has a tetragonal structure and shows strong uniaxial anisotropy. Ideally, the magnetic properties of anisotropic permanent magnet materials are twice those of isotropic permanent magnet materials. Dense anisotropic RE-Fe—B permanent magnets can be divided into sintered magnets and hot deformation magnets according to the preparation method. Compared with sintered magnets with a micron crystal structure, the hot deformation magnets have a unique nanocrystalline structure and rich grain boundary structure, achieving higher magnetic properties without using medium and heavy rare earths. This type of magnet is considered to be the most promising rare earth permanent magnet material. The anisotropy of hot deformation magnets comes from the dissolution and precipitation of RE2Fe14B grains under the action of temperature field and stress field, forming flake structure grains regularly arranged along the direction of hot deformation and then obtaining an oriented texture. The formation of the oriented texture is mainly through the dissolution and precipitation of RE2Fe14B grains under the action of temperature field and stress field. The precursors used in conventional hot deformation methods are generally amorphous or equiaxed nanocrystalline magnetic powders. These precursor powders require a long enough time for the RE2Fe14B grains to dissolve, precipitate, and preferentially grow to form an oriented texture. Therefore, there is an extremely poor deformation rate of conventional processes, generally less than 0.2 mm/s, which greatly limits the production efficiency of hot deformation-based magnets. In terms of preparation of anisotropic RE-Fe—B magnetic powder, the traditional preparation methods of anisotropic magnetic powder mainly include anisotropic hot deformation magnet crushing, hydrogenation-disproportionation-desorption-recombination (HDDR), and mechanical ball milling, which are time-consuming and complicated. In addition, the magnetic powder prepared by these methods is basically irregular in shape, and an oriented magnetic field is required in subsequent molding to obtain anisotropic bonded magnets, thus greatly increasing the preparation cost. After long-term experimental research, the applicant has surprisingly found that nanocrystalline magnetic powder or amorphous magnetic powder can be used to prepare precursor flake nanocrystalline magnetic powder with a specific structure through a specific preparation process. The number of grains of flake nanocrystals inside the precursor flake nanocrystalline magnetic powder accounts for not less than 85% of a total number of grains inside the precursor flake nanocrystalline magnetic powder. Since the flake nanocrystals with a specific structure show shape anisotropy, it can easily rotate under the action of the subsequent hot deformation stress field, forming an oriented texture in which the flake nanocrystals are regularly arranged in a way that the thickness direction of the flake nanocrystals are parallel to the direction of the hot deformation, thereby increasing an orientation degree. Furthermore, by optimizing the orientation through post-processing in a specific process, the anisotropic rare earth permanent magnet material is obtained with excellent magnetic properties. The present disclosure is proposed on the basis of this research.
In the present disclosure, the magnetic powder of the rare earth permanent magnet has a nominal composition of RExFe100-x-y-zTMyBz, where RE is one or more selected from the group consisting of La, Ce, Pr, Nd, Y, Dy, and Tb, TM is one or more selected from the group consisting of Co, Zr, Cr, V, Nb, Si, Ti, Mo, Mn, W, Ga, Cu, Al, and Zn, and x, y, and z each represent a mass fraction of an element, and 26.0≤x≤36.0, 0.14≤y≤8.0, and 0.8≤z≤1.36. Rare earth permanent magnet materials with better magnetic properties can be prepared by using the magnetic powder of the rare earth permanent magnet with the above formula. The magnetic powder of the rare earth permanent magnet is one or more selected from the group consisting of a rapid-quenching magnetic powder, an HDDR magnetic powder, a ball milling magnetic powder, a mechanical crushing magnetic powder, and a mechanical alloying magnetic powder.
The present disclosure provides a method for preparing an anisotropic flake nanocrystalline rare earth permanent magnet material, including the following steps:
Step 1, preparation of a precursor flake nanocrystalline magnetic powder: subjecting a magnetic powder of a rare earth permanent magnet to heat preservation at a temperature of 710° C. to 740° C. for 5 min to 120 min under vacuum or a protective atmosphere to obtain the precursor flake nanocrystalline magnetic powder, where the magnetic powder of the rare earth permanent magnet is one selected from the group consisting of a nanocrystalline magnetic powder and an amorphous magnetic powder, and the nanocrystalline magnetic powder has an average grain size of not more than 200 nm: a number of grains of flake nanocrystals inside the precursor flake nanocrystalline magnetic powder accounts for not less than 85% of a total number of grains inside the precursor flake nanocrystalline magnetic powder; and the flake nanocrystals have an average grain size of 10 nm to 300 nm in a grain thickness direction and an average grain size of 30 nm to 800 nm in a grain length direction.
The nanocrystalline magnetic powder or amorphous magnetic powder is prepared into the precursor flake nanocrystalline magnetic powder with a specific flake nanocrystal structure through the above-mentioned specific preparation process. The number of grains of a flake nanocrystal inside the precursor flake nanocrystalline magnetic powder accounts for not less than 85% of a total number of grains inside the precursor flake nanocrystalline magnetic powder. Since the flake nanocrystal shows shape anisotropy, it can easily rotate under the action of stress field, forming an oriented texture in which the flake nanocrystals are regularly arranged in a way that a thickness direction of the flake nanocrystals is parallel to a direction of hot deformation. On one hand, the flake nanocrystal of the precursor flake nanocrystalline magnetic powder is prone to rotate and orient, and anisotropic permanent magnet materials with excellent magnetic properties can be prepared under conventional hot deformation rates. On the other hand, the anisotropic permanent magnet materials with better magnetic properties can still be prepared under rapid hot deformation rates, which is beneficial to improving the production efficiency. In some embodiments, the precursor flake nanocrystalline magnetic powder is prepared at the temperature of 710° C. to 740° C. for 5 min to 100 min, preferably 15 min to 60 min. In some embodiments, the flake nanocrystals inside the precursor flake nanocrystalline magnetic powder have an average grain size of 50 nm to 150 nm in a grain thickness direction and an average grain size of 150 nm to 600 nm in a grain length direction. In some embodiments, the flake nanocrystals have an average grain size of 60 nm to 100 nm in the grain thickness direction and an average grain size of 180 nm to 400 nm in the grain length direction. In some embodiments, a number of grains of flake nanocrystals inside the precursor flake nanocrystalline magnetic powder accounts for not less than 90%, preferably not less than 94%, and more preferably not less than 98% of a total number of grains inside the precursor flake nanocrystalline magnetic powder.
Step 2, orientation treatment by hot deformation: subjecting the precursor flake nanocrystalline magnetic powder or a package or a green body prepared from the precursor flake nanocrystalline magnetic powder to hot deformation at a temperature of 500° C. to 850° C., such that the flake nanocrystals are regularly arranged to obtain an oriented flake nanocrystalline rare earth permanent magnet material.
Specifically, the hot deformation in the orientation treatment by the hot deformation in step 2 is conducted by one or more selected from the group consisting of hot rolling deformation, hot pressing deformation, and hot extrusion deformation.
In some embodiments, the hot rolling deformation is conducted by subjecting the precursor flake nanocrystalline magnetic powder to the hot rolling deformation under vacuum or a protective atmosphere at a temperature of 600° C. to 850° C. with a deformation amount in a thickness direction of the precursor flake nanocrystalline magnetic powder of 50% to 90%, such that the flake nanocrystals are regularly arranged. In some embodiments, the hot rolling deformation is conducted at a temperature of 700° C. to 850° C., preferably 750° C. to 850° C. with a deformation amount in the thickness direction of the precursor flake nanocrystalline magnetic powder of 60% to 80%.
In some embodiments, the hot pressing deformation is conducted by subjecting the precursor flake nanocrystalline magnetic powder to vacuum packaging using a packaging material to obtain the package, and subjecting the package to the hot pressing deformation at a temperature of 600° C. to 850° C. with a deformation rate of 0.02 mm/s to 3.00 mm/s and a deformation amount of the package along a hot pressing direction of 50% to 90%, such that the flake nanocrystals are regularly arranged. In some embodiments, the packaging material is a plastic material, preferably a copper tube or stainless steel tube. In some embodiments, the hot pressing deformation is conducted at a temperature of 700° C. to 850° C., preferably 750° C. to 850° C. with a deformation rate of 0.02 mm/s to 1.00 mm/s or 1.00 mm/s to 3.00 mm/s, preferably 0.02 mm/s to 0.2 mm/s or 0.2 mm/s to 3.00 mm/s and a deformation amount of the package along a hot pressing direction of 60% to 80%.
In some embodiments, the hot pressing deformation is conducted by preparing the precursor flake nanocrystalline magnetic powder into a green body with a density of 65.0% to 99.9% at a temperature of room temperature to 800° C., and subjecting the green body to the hot pressing deformation at a temperature of 600° C. to 850° C. with a deformation rate of 0.02 mm/s to 3 mm/s and a deformation amount of the green body along a hot pressing direction of 50% to 90%, such that the flake nanocrystals are regularly arranged. In some embodiments, the hot pressing deformation is conducted at a temperature of 700° C. to 850° C., preferably 750° C. to 850° C. with a deformation rate of 0.02 mm/s to 1.00 mm/s or 1.00 mm/s to 3.00 mm/s, preferably 0.02 mm/s to 0.2 mm/s or 0.2 mm/s to 3.00 mm/s and a deformation amount of the green body along a hot pressing direction of 60% to 80%.
Step 3, post-processing for optimizing orientation: subjecting the oriented flake nanocrystalline rare earth permanent magnet material to heat preservation at a temperature of 600° C. to 850° C. for 3 min to 120 min under vacuum or a protective atmosphere to obtain the anisotropic flake nanocrystalline rare earth permanent magnet material.
The above-mentioned specific post-processing for optimizing orientation is beneficial to further growth of oriented grains, improves anisotropy, can optimize the distribution of rare earth-rich phases at grain boundaries to be uniform, and is beneficial to eliminating the residual stress caused by hot deformation and further improving the magnetic properties. In some embodiments, the heat preservation is conducted at a temperature of 750° C. to 850° C. for 5 min to 60 min.
The present disclosure further provides an anisotropic flake nanocrystalline rare earth permanent magnet material prepared by the above method for preparing an anisotropic flake nanocrystalline rare earth permanent magnet material. In some embodiments of the present disclosure, the rare earth permanent magnet material includes a powder material and a bulk material. In some embodiments, the powder material is a flake magnetic powder, and the flake magnetic powder shows shape anisotropy. Due to the anisotropy of the magnetic properties of the flake magnetic powder itself, the flake magnetic powder can be oriented by both stress field and magnetic field, and can also be oriented by stress field and magnetic field at the same time. This powder material can be adapted to different industrial scenarios when preparing magnets, and has broad application prospects. The bulk material has excellent magnetic properties and can be directly prepared into corresponding device shapes according to different application requirements, thus exhibiting broad application prospects.
In the anisotropic flake nanocrystalline rare earth permanent magnet material of the present disclosure, the flake nanocrystals inside the rare earth permanent magnet material are regularly arranged in a way that the thickness direction of the flake nanocrystals is parallel to the hot deformation direction. Since an easy magnetization direction of the nanocrystals is parallel to the thickness direction of the grains, the flake nanocrystalline rare earth material exhibits magnetic anisotropy. In the anisotropic flake nanocrystalline rare earth permanent magnet material, the anisotropic flake nanocrystals have an average grain size of 30 nm to 200 nm in a thickness direction and an average grain size of 150 nm to 800 nm in a length direction, showing excellent magnetic properties. In some embodiments, the anisotropic flake nanocrystals have an average grain size of 50 nm to 150 nm in a thickness direction and an average grain size of 200 nm to 600 nm in a length direction.
The present disclosure is further described below through specific examples.
This example provided a method for preparing an anisotropic flake nanocrystalline rare earth permanent magnet material, consisting of the following steps:
Step 1, preparation of a precursor flake nanocrystalline magnetic powder: an alloy ingot with a nominal composition of Nd29.89Fe62.62Co5.93Ga0.64B0.92 (wt. %) was subjected to melt-spinning at a linear speed of a rapid-quenching roller of 25 m/s to obtain a nanocrystalline rapid-quenching magnetic powder with a particle size of 50 μm to 450 μm. The nanocrystalline rapid-quenching magnetic powder was an equiaxed crystal, as shown in
Step 2, orientation treatment by hot deformation: the precursor flake nanocrystalline magnetic powder prepared in step 1 was subjected to hot rolling deformation using a double-roller mill at a temperature of 780° C. in an argon protective atmosphere. The deformation amount in a thickness direction of the magnetic powder after hot rolling deformation was 65%, as shown in
Step 3, post-processing for optimizing orientation: the oriented flake nanocrystalline magnetic powder prepared in step 2 was subjected to heat preservation at a temperature of 800° C. for 5 min under vacuum with a vacuum degree of 1×10−2 Pa. As shown in
Comparative Example 1 was different from Example 1 in that the nanocrystalline rapid-quenching magnetic powder obtained in the preparation of precursor flake nanocrystalline magnetic powder in step 1 of Example 1 was subjected to the heat preservation at a temperature of 700° C. for 20 min instead of at the temperature of 720° C. for 15 min, while the remaining preparation steps were the same as those in Example 1.
Comparative Example 2 was different from Example 1 in that the nanocrystalline rapid-quenching magnetic powder obtained in the preparation of precursor flake nanocrystalline magnetic powder in step 1 of Example 1 was subjected to the heat preservation at the temperature of 750° C. for 30 min instead of at the temperature of 720° C. for 15 min, while the remaining preparation steps were the same as those in Example 1.
Comparative Example 3 was different from Example 1 in that the nanocrystalline rapid-quenching magnetic powder obtained in the preparation of precursor flake nanocrystalline magnetic powder in step 1 of Example 1 was not subjected to the heat preservation at the temperature of 720° C. for 15 min, while the remaining preparation steps were the same as those in Example 1.
Comparative Example 4 was different from Example 1 in that the deformation amount in the thickness direction of the magnetic powder after the hot rolling deformation in the orientation treatment by hot deformation in step 2 of Example 1 was changed from 65% to 30%, while the remaining preparation steps were the same as those in Example 1.
The properties of the anisotropic magnetic powders prepared according to Example 1 and Comparative Examples 1 to 4 were measured using a vibrating sample magnetometer (VSM). The results are shown in Table 1.
The anisotropic magnetic powders prepared according to Example 1 and Comparative Examples 1 to 4 were separately mixed with 1 wt. % epoxy resin, and then molded at room temperature under the action of an orientation magnetic field of 3 T, obtaining an anisotropic bonded magnet with a diameter of φ10 mm and a density of 5.9 g/cm3. The XRD pattern of the bonded magnet was tested, and the orientation degrees of the anisotropic magnetic powders prepared according to Example 1 and Comparative Examples 1 to 4 were characterized by a ratio of the diffraction peak intensity at (006) of the orientation surface of the anisotropic bonded magnet to the diffraction peak intensity at (105) of the orientation surface of the anisotropic bonded magnet, as shown in
As shown in Table 1 and
In Comparative Example 1, since the proportion of flake nanocrystals is significantly lower than that in Example 1, the equiaxed crystals that did not form flake nanocrystals need to undergo a process of dissolution, precipitation, and orientation during hot deformation. The grains need a long orientation time, and thus are not fully oriented during the hot rolling deformation. The orientation degree of the prepared magnetic powder is obviously lower than that in Example 1, and the orientation degree is a key factor affecting the remanence. Correspondingly, the remanence and maximum energy product of Comparative Example 1 are significantly lower than those of Example 1.
In Comparative Example 2, after the magnetic powder underwent the preparation of precursor flake nanocrystalline magnetic powder in step 1, a large number of coarse crystals formed, which hindered the dissolution, precipitation, and orientation of the grains during subsequent hot deformation, making the orientation degree of Comparative Example 2 significantly lower than that in Example 1. Correspondingly, the remanence of Comparative Example 2 is significantly lower than that of Example 1. Moreover, the influence of coarse grain causes the coercivity of Comparative Example 2 to significantly decrease, resulting in the maximum energy product of Comparative Example 2 being significantly lower than that of Example 1.
In Comparative Example 3, since the rapid-quenching nanocrystalline magnetic powder is not subjected to heat preservation, the grains remain as fine equiaxed crystals, which are conducive to the dissolution and precipitation of the grains during the subsequent hot deformation to form finer grains, such that the coercivity is higher than that of Example 1. However, the equiaxed crystals could not be fully oriented during the hot deformation, and the orientation degree of Comparative Example 3 is significantly lower than that of Example 1. Correspondingly, the remanence and maximum energy product are also significantly lower than those in Example 1.
In Comparative Example 4, since the deformation amount of the magnetic powder prepared by the preparation of precursor flake nanocrystal magnetic powder of step 1 during the hot deformation is significantly lower than that in Example 1, the flake nanocrystals are not fully oriented during the hot deformation. Therefore, the orientation degree of Comparative Example 4 is significantly lower than that of Example 1, while the remanence and maximum energy product are significantly lower than those of Example 1.
This example provided a method for preparing an anisotropic nanocrystalline rare earth permanent magnet material, consisting of the following steps:
Comparative Example 5 was different from Example 2 in that the amorphous rapid-quenching magnetic powder obtained in the preparation of precursor flake nanocrystalline magnetic powder in step 1 of Example 2 was not subjected to the heat preservation at the temperature of 730° C. for 20 min, while the remaining preparation steps were the same as those in Example 2.
The properties of the anisotropic magnetic powders prepared according to Example 2 and Comparative Example 5 were measured using a VSM. The results are shown in Table 2.
The anisotropic magnetic powder prepared according to Example 2 was used to prepare an anisotropic bonded magnet using the same process conditions as those in Example 1. It was measured that the Nd2Fe14B phase had a diffraction peak I(006)/I(105)=0.75, indicating that the flake nanocrystals of the anisotropic magnetic powder prepared according to Example 2 showed regular orientation. As shown in Table 2, the magnetic properties of the anisotropic flake nanocrystalline magnetic powder of Example 2 are significantly better than those of Comparative Example 5. The main reason is analyzed as that the precursor flake nanocrystalline magnetic powder in Example 2, prepared from the rapid-quenching nanocrystalline magnetic powder through the preparation of precursor flake nanocrystalline magnetic powder of step 1, has a relatively high number of internal flake nanocrystalline grains, and the grains could be fully oriented. While in Comparative Example 5, the amorphous rapid-quenching magnetic powder was directly subjected to hot deformation. In the process of hot deformation, the amorphous structure needs to be nucleated before the texture can be formed, which requires sufficient time. It can be seen from the magnetic properties of Comparative Example 5 that the amorphous rapid-quenching magnetic powder could not achieve an oriented texture directly through hot rolling deformation, and exhibits isotropy.
This example provided a method for preparing an anisotropic nanocrystalline rare earth permanent magnet material, consisting of the following steps:
Comparative Example 6 was different from Example 3 in that the ball-milled nanocrystalline magnetic powder obtained in the preparation of precursor flake nanocrystalline magnetic powder of step 1 in Example 3 was not subjected to the heat preservation at the temperature of 710° C. for 30 min, while the remaining preparation steps were the same as those in Example 3.
The properties of the anisotropic magnetic powders prepared according to Example 3 and Comparative Example 6 were measured using a VSM. The results are shown in Table 3.
The anisotropic magnetic powders prepared according to Example 3 and Comparative Example 6 were separately used to prepare an anisotropic bonded magnet using the same process conditions as those in Example 1. It was measured that the Nd2Fe14B phase of Example 3 has a diffraction peak I(006)/I(105)=0.77, while the Nd2Fe14B phase of Comparative Example 6 has a diffraction peak I(006)/I(105)=0.75, indicating that the flake nanocrystal of the anisotropic magnetic powder prepared according to Example 3 shows regular orientation, and has an orientation degree better than that of Comparative Example 6. As shown in Table 3, the magnetic properties of the anisotropic flake nanocrystalline magnetic powder of Example 3 are significantly better than those of Comparative Example 6. The main reason is analyzed as that the precursor flake nanocrystalline magnetic powder of Example 3, prepared from the ball-milled nanocrystalline magnetic powder through the preparation of precursor flake nanocrystalline magnetic powder of step 1, has a relatively high number of internal flake nanocrystalline grains, which was beneficial to the grain orientation of the anisotropic magnetic powder. Since a-Fe impurities are inevitably introduced during the ball milling using stainless steel ball milling tank, the magnetic properties of the anisotropic flake nanocrystalline magnetic powder in Example 3 are lower than those of the anisotropic flake nanocrystalline magnetic powder in Example 1.
This example provided a method for preparing an anisotropic nanocrystalline rare earth permanent magnet material, consisting of the following steps:
Comparative Example 7 was different from Example 4 in that the nanocrystalline rapid-quenching magnetic powder obtained in the preparation of precursor flake nanocrystalline magnetic powder of step 1 in Example 4 was not subjected to the heat preservation at the temperature of 730° C. for 30 min, while the remaining preparation steps were the same as those in Example 4.
The properties of the anisotropic magnets prepared according to Example 4 and Comparative Example 7 were measured using a VSM. The results are shown in Table 4.
Example 5 was different from Example 4 in that the hot deformation rate in the orientation treatment by hot deformation of step 2 was 0.1 mm/s in Example 5 instead of 0.86 mm/s in Example 4, while the remaining preparation steps were the same as those in Example 4. The flake nanocrystals of the anisotropic magnet prepared in Example 5 had an average grain size of 101 nm in the thickness direction and an average grain size of 330 nm in the length direction.
Comparative Example 8 was different from Example 5 in that the nanocrystalline rapid-quenching magnetic powder obtained in the preparation of precursor flake nanocrystalline magnetic powder of step 1 of Example 5 was not subjected to the heat preservation at the temperature of 730° C. for 30 min in Comparative Example 8, while the remaining preparation steps were the same as those in Example 5.
The properties of the anisotropic magnets prepared according to Example 5 and Comparative Example 8 were measured using a VSM. The results are shown in Table 5.
Through the same test method as in Example 4, it was measured that the Nd2Fe14B phase of Example 5 has a diffraction peak I(006)/I(105)=1.21, while the Nd2Fe14B phase of Comparative Example 8 has a diffraction peak I(006)/I(105)=1.05, indicating that the flake nanocrystals of the anisotropic magnetic powder prepared according to Example 5 show regular orientation, and has an orientation degree better than that of Comparative Example 8. As shown in Table 5, the magnetic properties of the anisotropic flake nanocrystalline magnet of Example 5 are significantly better than those of Comparative Example 8. The main reason is analyzed as that the precursor flake nanocrystalline magnetic powder of Example 5, prepared from the rapid-quenching nanocrystalline magnetic powder prepared through the preparation of precursor flake nanocrystalline magnetic powder of step 1, has a high number of internal flake nanocrystalline grains, which was beneficial to the grain orientation of the anisotropic magnet. Combining Example 4 and Example 5, it can be seen taht the deformation rate in Example 5 is lower, which is more conducive to the rotational orientation of the flake nanocrystals during the hot deformation to obtain a more excellent oriented texture.
This example provided a method for preparing an anisotropic nanocrystalline rare earth permanent magnet material, consisting of the following steps:
Comparative Example 9 was different from Example 6 in that the nanocrystalline rapid-quenching magnetic powder obtained in the preparation of precursor flake nanocrystalline magnetic powder of step 1 of Example 6 was not subjected to the heat preservation at the temperature of 740° C. for 60 min, while the remaining preparation steps were the same as those in Example 6.
The properties of the anisotropic magnets prepared according to Example 6 and Comparative Example 9 were measured using a VSM. The results are shown in Table 6.
Through the same test method as in Example 4, it was measured that the Nd2Fe14B phase of Example 6 had a diffraction peak I(006)/I(105)=1.08, while the Nd2Fe14B phase of Comparative Example 9 had a diffraction peak I(006)/I(105)=1.02, indicating that the flake nanocrystal of the anisotropic magnet prepared according to Example 6 showed regular orientation, and had an orientation degree better than that of Comparative Example 9. As shown in Table 6, the magnetic properties of the anisotropic flake nanocrystalline magnet of Example 6 are significantly better than those of Comparative Example 9. The main reason is analyzed as that the precursor flake nanocrystalline magnetic powder of Example 6, prepared from the rapid-quenching nanocrystalline magnetic powder of step 1, has a relatively high number of internal flake nanocrystalline grains, which is beneficial to the grain orientation of the anisotropic magnet. Due to the rotational orientation of the flake nanocrystals under the stress field, the anisotropic magnet could still achieve excellent oriented texture under the rapid deformation of 0.80 mm/s.
This example provided a method for preparing an anisotropic nanocrystalline rare earth permanent magnet material, consisting of the following steps:
Comparative Example 10 was different from Example 7 in that the nanocrystalline rapid-quenching magnetic powder obtained in the preparation of precursor flake nanocrystalline magnetic powder of step 1 of Example 7 was not subjected to the heat preservation at the temperature of 740° C. for 60 min, while the remaining preparation steps were the same as those in Example 7.
The properties of the anisotropic magnetic rings prepared according to Example 7 and Comparative Example 10 were measured using a VSM. The results are shown in Table 7.
Through the same test method as in Example 4, it was measured that the Nd2Fe14B phase of the orientation plane of Example 7 had a diffraction peak I(006)/I(105)=1.07, while the Nd2Fe14B phase the orientation plane of Comparative Example 9 had a diffraction peak I(006)/I(105)=1.02, indicating that the flake nanocrystals of the anisotropic magnet prepared according to Example 7 showed regular orientation, and had an orientation degree better than that of Comparative Example 10. As shown in Table 7, the magnetic properties of the anisotropic flake nanocrystalline magnet of Example 7 are significantly better than those of Comparative Example 10. The main reason is analyzed as the precursor flake nanocrystalline magnetic powder of Example 7, prepared from the rapid-quenching nanocrystalline magnetic powder through the preparation of precursor flake nanocrystalline magnetic powder of step 1, has a relatively high number of internal flake nanocrystalline grains, which was beneficial to the grain orientation of anisotropic magnet. Due to the rotational orientation of the flake nanocrystals under the stress field, the anisotropic magnetic ring could still achieve excellent oriented texture under the rapid deformation of 0.70 mm/s.
It should be understood that those of ordinary skill in the art can make improvements or transformations based on the above description, and all these improvements and transformations should fall within the scope of the appended claims of the present disclosure.
| Number | Date | Country | Kind |
|---|---|---|---|
| 202211487970.X | Nov 2022 | CN | national |
This application is a national stage application of International Patent Application No. PCT/CN2023/133993, filed on Nov. 24, 2023, which claims priority to, and the benefit of, the Chinese Patent Application No. CN202211487970.X, filed with the China National Intellectual Property Administration (CNIPA) on Nov. 25, 2022, and entitled “METHOD FOR PREPARING ANISOTROPIC FLAKE NANOCRYSTALLINE RARE EARTH PERMANENT MAGNET MATERIAL AND RARE EARTH PERMANENT MAGNET MATERIAL”. The disclosure of the two patent applications is incorporated by references in their entireties.
| Filing Document | Filing Date | Country | Kind |
|---|---|---|---|
| PCT/CN2023/133993 | 11/24/2023 | WO |
