TWI459419B - Modified neodymium-iron-boron magnet and fabrication method thereof - Google Patents

Description

Modified NdFeB magnetic member and manufacturing method thereof

The present invention relates to a magnetic member and a method of manufacturing the same, and more particularly to an improved NdFeB magnetic member and a method of manufacturing the same.

The neodymium iron boron magnetic member is a magnetic element having a high magnetic energy product. In general, a magnetic element having a larger magnetic energy product has a higher magnetic energy per unit volume. In recent years, it has been found that if the neodymium iron boron magnetic member is modified by using dysprosium (Dy), the intrinsic coercive force (iHc) and thermal stability of the modified NdFeB magnetic member will increase, thereby expanding 钕The application of iron-boron magnetic parts in various fields.

In the early stage, the modified NdFeB magnetic parts were manufactured by directly melting bismuth, iron, boron and bismuth into a NdFeB alloy by a melting process. However, niobium is a rare earth element which is expensive, so the NdFeB alloy produced by the melting process is expensive. In order to reduce the amount of antimony, the industry has developed a diffusion method to diffuse germanium into the grain boundaries of the neodymium iron boron magnets that do not contain antimony (hereinafter referred to as grain boundary diffusion method), which are manufactured by using low amounts of antimony. Upgraded NdFeB magnetic parts. In general, the grain boundary diffusion method firstly applies dysprosium fluoride (DyF ₃ ) to the surface of the neodymium-free NdFeB magnetic member, and then heat-treats at about 900 ° C to diffuse the ruthenium to A modified NdFeB magnetic member is formed in the grain boundary of the NdFeB magnetic member. The advantage of this approach is that the amount of helium is less and the cost of helium can be reduced.

However, the disadvantage of the grain boundary diffusion method is that the thickness of the applicable NdFeB magnetic member is limited. When the thickness of the neodymium iron boron magnetic member is greater than 4 mm, the crucible is not easily diffused into the grain boundary of the central region of the neodymium iron boron magnetic member, so that the essential coercive force and thermal stability of the modified NdFeB magnetic member are formed. No effective promotion.

In view of this, it is urgent to propose a modified NdFeB magnetic component and a manufacturing method thereof to solve the problem that the thickness of the modified NdFeB magnetic component, the low enthalpy usage amount, and the high intrinsic coercive force and thermal stability cannot be considered. The problem.

Therefore, an object of the present invention is to provide a method for manufacturing an improved NdFeB magnetic member, which can simultaneously consider the thickness of the modified NdFeB magnetic member and the high-intensity correction on the premise of reducing the amount of bismuth used. Resilience and thermal stability.

Another object of the present invention is to provide a method of manufacturing an improved NdFeB magnetic member that is applicable to a mass production process.

It is still another object of the present invention to provide an improved NdFeB magnetic member which can have a thickness greater than 4 mm and which has magnetic properties in accordance with commercial specifications.

According to the above object of the present invention, a method of manufacturing an improved NdFeB magnetic member is proposed. In one embodiment, a first neodymium iron boron blank and a second neodymium iron boron blank are provided. Forming a first modified layer on the first NdFeB blank, wherein the material of the first modified layer comprises dysprosium oxide (Dy ₂ O ₃ ) or cesium fluoride. A fluxing layer is formed on the first modifying layer to form a first NdFeB body. Forming a second modified layer on the second NdFeB blank to form a second NdFeB body, wherein the material of the second modified layer comprises lanthanum, cerium oxide or lanthanum fluoride. A second NdFeB body is stacked on the first NdFeB body to form a NdFeB stack, wherein the second modified layer is attached to the fluxing layer. The NdFeB stack is subjected to thermal pressure equalization treatment to form a modified NdFeB magnetic member.

According to an embodiment of the invention, the ratio of the thickness of the first modified layer to the thickness of the first NdFeB blank is 1:150 to 1:300.

According to an embodiment of the invention, the material of the fluxing layer comprises copper, aluminum or nickel.

According to an embodiment of the invention, the treatment pressure of the thermal pressure equalization treatment is greater than 120 MPa, the treatment temperature is 700 ° C to 850 ° C, and the duration is 1 hour to 2 hours.

According to another object of the present invention, a method of manufacturing an improved NdFeB magnetic member is proposed. In one embodiment, a plurality of neodymium iron boron blanks are provided. Correspondingly, a plurality of modified layers are formed on the NdFeB blanks, wherein the material of each modified layer comprises ruthenium, ruthenium oxide or ruthenium fluoride. A plurality of fluxing layers are respectively formed on the modified layers to form a plurality of NdFeB bodies. The NdFeB bodies are sequentially stacked to form a NdFeB stack in which adjacent fluxing layers are bonded to each other. The NdFeB stack is subjected to thermal pressure equalization treatment to form a modified NdFeB magnetic member.

According to an embodiment of the invention, the ratio of the thickness of each of the modified layers to the thickness of the corresponding each of the NdFeB blanks is 1:150 to 1:300.

According to an embodiment of the invention, the material of the fluxing layer comprises copper, Aluminum or nickel.

According to an embodiment of the present invention, the treatment pressure of the heat equalization treatment is 120 MPa or more, the treatment temperature is 700 ° C to 850 ° C, and the duration is 1 hour to 2 hours.

According to still another object of the present invention, an improved NdFeB magnetic member is proposed which is produced by the above method.

According to an embodiment of the invention, the modified NdFeB magnetic member has a thickness greater than 4 mm.

The modified NdFeB magnetic member of the present invention is produced by forming a fluxing layer between two or more modified layers of the NdFeB blank and passing through a heat equalizing treatment to make the modified layer The composition diffuses into the grain boundaries of the NdFeB grains of the NdFeB stack, thereby forming a modified NdFeB magnet. Wherein, in the heat equalization treatment, the fluxing layer can react with the reforming layer to form a compound having a melting point lower than that of the modifying layer, which helps to reduce the processing temperature required for the heat equalizing treatment. On the other hand, the heat equalization treatment may be sintered to join the NdFeB bodies to sinter the NdFeB stack formed of the NdFeB stack to form a modified NdFeB magnet. Therefore, the thickness of the modified NdFeB magnetic member of the present invention can be increased by sintering the NdFeB body without a limitation in thickness.

100‧‧‧ method

110, 120, 130, 140, 150, 160‧ ‧ steps

200‧‧‧Modified NdFeB magnetic parts

201‧‧‧The first strontium boron

202‧‧‧Second ferrocene

203‧‧‧NdFeB stack

210‧‧‧First NdFeB blank

211‧‧‧First modified layer

212‧‧‧Fused layer

220‧‧‧Second iron-iron-boring parts

221‧‧‧Second modified layer

230‧‧‧heat equalization treatment

240‧‧‧low melting point alloy

300‧‧‧ method

310, 320, 330, 340, 350 ‧ ‧ steps

400‧‧‧Modified NdFeB magnetic parts

401‧‧‧NdFeB

402‧‧‧NdFeB stack

410‧‧‧NdFeB blanks

411‧‧‧Modified layer

412‧‧‧welding layer

420‧‧‧low melting point alloy

900‧‧‧Stainless steel bottles

910‧‧‧ outer wall

The above and other objects, features, advantages and embodiments of the present invention will become more <RTIgt; <RTIgt; </ RTI> <RTIgt; </ RTI> <RTIgt; A flow chart of a method of manufacturing a magnetic member.

2A to 2F are diagrams showing a modification according to the first embodiment of the present invention Process profile of NdFeB magnetic parts.

The 2G figure shows a schematic diagram of the NdFeB stack placed in a stainless steel bottle for heat equalization treatment.

3 is a flow chart showing a method of manufacturing a modified NdFeB magnetic member according to a second embodiment of the present invention.

4A to 4E are cross-sectional views showing the process of a modified NdFeB magnetic member according to a second embodiment of the present invention.

The technical content, structural features, achieved goals and effects of the present invention will be described in detail below with reference to embodiments of the present invention.

Referring to FIGS. 1 to 2F, FIG. 1 is a flow chart showing a method 100 of fabricating a modified NdFeB magnet 200 in accordance with a first embodiment of the present invention. 2A to 2F are cross-sectional views showing the process of a modified NdFeB magnet 200 in accordance with the first embodiment of the present invention. As shown in FIGS. 1 and 2A, in the method 100 for manufacturing the modified NdFeB magnet 200, the step 110 provides the first NdFeB blank 210 and the second NdFeB blank 220. The first NdFeB blank 210 and the second NdFeB blank 220 can be manufactured in the following manner. First, a raw material such as niobium, iron, and boron in a predetermined composition ratio is formed into a niobium-iron-boron alloy block containing no antimony by a melting process. Next, under the protection of the inert gas, the NdFeB alloy piece was pulverized into a NdFeB alloy powder having a particle diameter of about 2 μm to form a NdFeB alloy powder having a single magnetic domain. Thereafter, under the protection of the blunt gas, a magnetic field is applied to align the NdFeB alloy powders, whereby the magnetic poles of the NdFeB alloy powders are oriented in the same direction. Further, a pressure treatment is performed while arranging the NdFeB alloy powder to form a NdFeB alloy powder. NdFeB alloy embryo. Next, a sintering step is performed to cause the NdFeB alloy preform to form the first NdFeB blank 210 or the second NdFeB blank 220.

As shown in FIGS. 1 and 2B, step 120 forms a first modifying layer 211 on the first NdFeB blank 210, wherein the material of the first modifying layer 211 comprises ruthenium, ruthenium oxide or ruthenium fluoride. In one example, the first modifying layer 211 is formed on the first NdFeB blank 210 by vacuum sputtering. In another example, the thickness of the first modifying layer 211 is adjusted corresponding to the thickness of the first NdFeB blank 210. When the first NdFeB blank 210 is thick, the thickness of the first modifying layer 211 is also It will increase. In an exemplary embodiment, the ratio of the thickness of the first modifying layer 211 to the thickness of the first NdFeB blank 210 is 1:150 to 1:300.

As shown in FIGS. 1 and 2C, step 130 forms a fluxing layer 212 on the first modifying layer 211 to form a first NdFeB body 201. In one example, the fluxing layer 212 is formed on the first modifying layer 211 by vacuum sputtering. In another example, the material of the fluxing layer 212 comprises copper, aluminum or nickel.

As shown in FIGS. 1 and 2D, step 140 forms a second modified layer 221 on the second NdFeB blank 220 to form a second NdFeB body 202, wherein the material of the second modified layer 221 comprises Antimony, antimony oxide or antimony fluoride. In one example, the second modifying layer 221 is formed on the second NdFeB blank 220 by vacuum sputtering. In another example, the thickness of the second modifying layer 221 is adjusted corresponding to the thickness of the second NdFeB blank 220, that is, when the second NdFeB blank 220 is thick, the thickness of the second modifying layer 221 It also increases. In an exemplary embodiment, the ratio of the thickness of the second modifying layer 221 to the thickness of the second NdFeB blank 220 is 1:150 to 1:300.

As shown in FIGS. 1 and 2E, in step 150, a second neodymium iron boron body 202 is stacked on the first neodymium iron boron body 201 to form a neodymium iron boron stack 203, wherein the second modified layer 221 is attached. Melting layer 212. As shown in FIGS. 1 and 2F, in step 160, the neodymium iron boron stack 203 is subjected to heat equalization treatment to form a modified NdFeB magnet 200. Wherein, the heat equalizing treatment can cause the first NdFeB body 201 and the second NdFeB body 202 to be sintered and joined to each other. In an example, please refer to FIG. 2G. FIG. 2G is a schematic diagram showing that the neodymium iron boron stack 203 is placed in the stainless steel bottle 900 for thermal pressure equalization treatment 230. When the hot grading treatment 230 is performed, the neodymium iron boron stack 203 is first placed in the stainless steel bottle 900. The inner space of the stainless steel bottle 900 corresponds to the shape of the neodymium iron boron stack 203. Moreover, the thickness of the outer wall 910 of the stainless steel bottle 900 needs to be thin enough so that the subsequent heat equalizing treatment 230 can pass through the outer wall 910 of the stainless steel bottle 900 and the ferroniobium inside the stainless steel bottle 900 under a preset temperature and pressure environment. The boron stack 203 is subjected to sintering. Next, the stainless steel bottle 900 is subjected to a vacuum sealing treatment in which the degree of vacuum in the stainless steel bottle 900 is 5 × 10 ^-5 Torr or less. Thereafter, the vacuum-sealed stainless steel bottle 900 is placed in a thermal equalizer to perform a heat equalization treatment 230. Wherein, the treatment pressure of the heat equalization treatment 230 is greater than 120 MPa, the treatment temperature is 700 ° C to 850 ° C, and the duration is 1 hour to 2 hours.

As shown in FIGS. 2E and 2F, in an example, when the heat averaging treatment is performed, the first modifying layer 211 and the second modifying layer 221 may form a low melting point alloy 240 with the fluxing layer 212 to lower the melting point. The antimony component contained in the alloy 240 can be diffused into the grain boundary of the first NdFeB blank 210 and the grain boundary of the second NdFeB blank 220 under a relatively low temperature process condition, thereby saving manufacturing costs. In an exemplary embodiment, when the material of the fluxing layer 212 is copper, the fluxing layer 212 may form a crucible (a melting point of about 1412 ° C under normal pressure) in the first modifying layer 211 and the second modifying layer 221 . Dy ₃ Cu alloy (melting point is about 750 ° C). Therefore, the heat equalization treatment can be carried out using a process condition in which the treatment pressure is greater than 120 MPa, the treatment temperature is about 770 ° C, and the duration is 2 hours. In another exemplary example, when the material of the fluxing layer 212 is nickel, the fluxing layer 212 may form a Dy ₃ Ni alloy with the germanium component in the first modifying layer 211 and the second modifying layer 221 (at normal pressure) The melting point is about 690 ° C). Therefore, the heat equalization treatment can be carried out using a process condition in which the treatment pressure is greater than 120 MPa, the treatment temperature is about 700 ° C, and the duration is 2 hours. In another exemplary example, when the material of the fluxing layer 212 is aluminum, the fluxing layer 212 may form a Dy ₃ Al alloy with the lanthanum in the first modifying layer 211 and the second modifying layer 221 (the melting point under normal pressure) About 850 ° C). Therefore, the heat equalization treatment can be carried out using a process condition in which the treatment pressure is greater than 120 MPa, the treatment temperature is about 850 ° C, and the duration is 2 hours.

According to the above paragraph, the method for producing the modified NdFeB magnetic member of the present invention is to simultaneously perform the improved grain boundary diffusion method and the sintered joint by means of thermal pressure equalization treatment. On the one hand, in the improved grain boundary diffusion method, the germanium component is diffused into the grain boundary of the first neodymium iron boron blank 210 and the grain boundary of the second neodymium iron boron blank 220 by diffusion, so that the use of germanium is used. The advantage of low volume. Moreover, since the fluxing layer 212 can reduce the processing temperature at the time of the heat equalization treatment, it has an effect of saving energy costs. On the other hand, the first NdFeB body 201 and the second NdFeB body 202 are sintered to each other to form the modified NdFeB magnet 200, so the thickness of the modified NdFeB magnet 200 can be greater than 4mm. In an exemplary embodiment, the first neodymium iron boron blank 210 and the second neodymium iron boron blank 220 have a thickness of 3 mm, so when the heat equalization treatment is performed, the first modified layer 211 and the second modified layer 221 The germanium component can be diffused into the grain boundaries in the central region of the first neodymium iron boron blank 210 and in the grain boundaries of the central region of the second neodymium iron boron blank 220. In addition, the first NdFeB body 201 and the second NdFeB body 202 are sintered and joined to each other by heat equalization treatment to form the modified NdFeB magnet 200. Therefore, the modified NdFeB magnet 200 increases the intrinsic coercive force and thermal stability of the modified NdFeB magnet 200 in addition to the modification of the niobium-boron magnet 200, and the modified NdFeB magnet 200 as a whole It also has a thickness of 6 mm. Therefore, the method for manufacturing the modified NdFeB magnetic member of the present invention can simultaneously reduce the thickness of the modified NdFeB magnetic member and the high intrinsic coercive force and thermal stability while reducing the amount of niobium used.

Please refer to FIG. 3 to FIG. 4E. FIG. 3 is a flow chart showing a method 300 for manufacturing the modified NdFeB magnet 400 according to the second embodiment of the present invention. 4A to 4E are cross-sectional views showing the process of a modified NdFeB magnetic member 400 in accordance with a second embodiment of the present invention. As shown in FIGS. 3 and 4A, in the method 300 of fabricating the modified NdFeB magnet 400, step 310 provides a plurality of NdFeB blanks 410. The method of manufacturing the neodymium iron boron blank 410 may be similar to the manufacturing method of the first neodymium iron boron blank 210 or the second neodymium iron boron blank 220, and thus will not be described again.

As shown in FIGS. 3 and 4B, step 320 corresponds to forming a plurality of modified layers 411 on opposite surfaces of the neodymium iron boron blanks 410, wherein the material of each of the modified layers 411 comprises tantalum and niobium oxide. Or cesium fluoride. In an example, the modified layer 411 is formed by vacuum sputtering on NdFeB On the blank member 410. In another example, the thickness of the modified layer 411 is adjusted corresponding to the thickness of the neodymium iron boron blank 410. When the neodymium iron boron blank 411 is thick, the thickness of the modified layer 411 also increases. In an exemplary embodiment, the ratio of the thickness of the modified layer 411 to the thickness of the neodymium iron boron blank 410 is 1:150 to 1:300.

As shown in FIGS. 3 and 4C, step 330 is formed by forming a plurality of fluxing layers 412 on the modified layers 411 to form a plurality of neodymium iron boron bodies 401. In one example, the fluxing layer 412 is formed on the modified layer 411 by vacuum sputtering. In another example, the material of the fluxing layer 412 comprises copper, aluminum or nickel.

As shown in FIGS. 3 and 4D, step 340 sequentially stacks the NdFeB bodies 401 to form a NdFeB stack 402 in which adjacent fluxing layers 412 are bonded to each other. As shown in FIGS. 3 and 4E, step 350 performs thermal pressure equalization treatment on the neodymium iron boron stack 402 to form a modified neodymium iron boron magnetic member 400. Wherein, the heat equalizing treatment can cause the NdFeB bodies 401 to be sintered and joined to each other. In the step 350 of the second embodiment, the manner of the heat equalization treatment can be performed in a manner similar to the vacuum sealing of the bottle in the first embodiment. In addition, as shown in FIGS. 4D and 4E, when the heat equalizing treatment is performed, the fluxing layer 412 of each of the NdFeB bodies 401 may form a low melting point alloy 420 with the adjacent modifying layer 411 to make the low melting point alloy 420. The antimony component contained in the crucible can be diffused into the neodymium iron boron blanks 410 under a relatively low temperature process condition, thereby saving production costs.

Hereinafter, an embodiment and a comparative example are listed, thereby demonstrating that the modified NdFeB magnetic member of the present invention can simultaneously consider the thickness of the modified NdFeB magnetic member and enhance the essence under the premise of reducing the use amount of bismuth. Coercive force and heat stability. Moreover, the modified NdFeB magnetic member of the present invention may also have a thickness greater than 4 mm and a magnetic property in accordance with commercial specifications.

In the embodiment, three neodymium iron boron blanks having a length, a width, and a thickness of 50 mm, 40 mm, and 3 mm, respectively, are first prepared. The upper surface and the lower surface of the NdFeB blank are ground and sanded, and then ultrasonically cleaned with acetone and alcohol. After the cleaned NdFeB blank is dried, a modified layer of yttrium and a fluxing layer made of copper are sequentially plated on the NdFeB blank by vacuum sputtering to form lanthanum iron. Boron body. The thickness of the modified layer was 10 μm, and the thickness of the fluxing layer was 2 μm. Next, these NdFeB bodies are sequentially stacked to form a NdFeB stack. The NdFeB stack was placed in a stainless steel bottle in an air-insulated environment, and then subjected to vacuum sealing treatment to form a vacuum state of 5×10 ^-5 Torr in the stainless steel bottle. Thereafter, the stainless steel bottle subjected to vacuum sealing treatment was placed in a thermal pressure equalizer for thermal pressure equalization treatment to form a modified NdFeB magnetic member having a thickness of 9 mm. Wherein, the treatment pressure of the heat equalization treatment is greater than 120 MPa, the treatment temperature is about 810 ° C, and the duration is 2 hours. After the physical and magnetic properties were tested, the modified NdFeB magnetic member of the example had an average grain size of 10 μm, an oxygen content of 1255 ppm, a density of 7.52 g/cm ³ , and a residual magnetization (Br) of 12.9 kG. (kG), the intrinsic coercive force is 22.4 kOe and the maximum magnetic energy product ((BH) _max ) is 41.3 million Gauss-Oster (MGOe).

In the comparative example, a neodymium iron boron blank having a length, a width, and a thickness of 50 mm, 40 mm, and 3 mm, respectively, was prepared. The upper surface and the lower surface of the NdFeB blank were ground and sanded, and then ultrasonically washed with acetone and alcohol. After the cleaned NdFeB blank was dried, the NdFeB blank was plated with DyF ₃ by vacuum sputtering. Thereafter, a grain boundary diffusion method is performed on the sputtered NdFeB blank, and a ruthenium fluoride is diffused into the interior of the NdFeB blank by a vacuum heat treatment at a treatment pressure of 120 MPa or more and a treatment temperature of 900 ° C, thereby forming Modified NdFeB magnetic piece with a thickness of 3 mm. After the physical and magnetic properties were tested, the modified NdFeB magnetic member of this comparative example had an average grain size of 10 μm, an oxygen content of 1,250 ppm, a density of 7.52 g/cm ³ , and a residual magnetization (Br) of 12.9 thousand. Gauss, the intrinsic coercive force is 22.5 kOe and the maximum magnetic energy product is 41.4 million Gauss-Oersted.

In summary, the modified NdFeB magnetic member obtained by the method for manufacturing the modified NdFeB magnetic member of the embodiment of the present invention has physical properties and magnetic properties similar to those obtained by the comparative example of the grain boundary diffusion method. The modified NdFeB magnetic parts, and the physical and magnetic properties are in line with today's commercial specifications. On the other hand, the modified NdFeB magnetic member of the embodiment has a thickness of 9 mm, which is far more than the thickness of the modified NdFeB magnetic member of the comparative example, and far exceeds the grain boundary diffusion method and can only be applied to the maximum. Modified NdFeB magnet with a thickness of 4mm. It can be seen that the manufacturing method of the modified NdFeB magnetic member of the present invention can surely take into consideration the thickness of the modified NdFeB magnetic member and the high intrinsic coercive force and heat on the premise of reducing the use amount of antimony. stability. On the other hand, the vacuum sputtering and the vacuum sealing of the bottle can be applied to the mass production process, so the manufacturing method of the modified NdFeB magnetic component of the invention is also suitable for mass production of modified NdFeB. Magnetic parts.

Although the present invention has been disclosed in the above embodiments, it is not used The invention is defined by the general knowledge of the present invention, and various modifications and refinements can be made without departing from the spirit and scope of the invention. The scope is defined.

100‧‧‧ method

110, 120, 130, 140, 150, 160‧ ‧ steps

Claims (10)

A method for manufacturing a modified NdFeB magnetic component, comprising: providing a first NdFeB blank and a second NdFeB blank; forming a first modified layer on the first NdFeB blank The material of the first modified layer comprises ruthenium, iridium oxide or ruthenium fluoride; forming a fluxing layer on the first modified layer to form a first samarium boron body; forming a second modified layer Forming a second NdFeB body on the second NdFeB blank, wherein the material of the second modified layer comprises ruthenium, ruthenium oxide or ruthenium fluoride; stacking the second NdFeB body a first NdFeB body to form a NdFeB stack, wherein the second modified layer is attached to the fluxing layer; and the NdFeB stack is subjected to a heat equalizing treatment to form the modification Quality iron and boron magnetic parts. The method for manufacturing a modified NdFeB magnetic member according to claim 1, wherein a ratio of a thickness of the first modified layer to a thickness of the first NdFeB blank is 1:150 to 1:300. The method for manufacturing a modified NdFeB magnetic member according to claim 1, wherein the material of the fluxing layer comprises copper, aluminum or nickel. The method for manufacturing a modified NdFeB magnetic member according to claim 1, wherein one of the heat equalization treatments has a pressure system greater than 120 MPa and a processing temperature. It is from 700 ° C to 850 ° C and for a duration of from 1 hour to 2 hours. A method for manufacturing a modified NdFeB magnetic component, comprising: providing a plurality of NdFeB blanks; respectively forming a plurality of modified layers on the plurality of NdFeB blanks, wherein each of the plurality of modified The material of the layer comprises bismuth, yttrium oxide or lanthanum fluoride; respectively forming a plurality of fluxing layers on the plurality of modified layers to form a plurality of yttrium iron boron bodies; stacking the plurality of yttrium iron boron bodies in sequence, Forming a stack of neodymium iron boron, wherein the plurality of fluxing layers are adjacent to each other; and subjecting the neodymium iron boron stack to a heat equalizing treatment to form the modified neodymium iron boron magnetic member. The method for manufacturing a modified NdFeB magnetic member according to claim 5, wherein a ratio of a thickness of each of the plurality of modified layers to a thickness of each of the plurality of NdFeB blanks is 1:150 to 1 :300. The method for manufacturing a modified NdFeB magnetic member according to claim 5, wherein the material of the plurality of fluxing layers comprises copper, aluminum or nickel. The method for manufacturing a modified NdFeB magnetic member according to claim 5, wherein one of the heat equalization treatments has a treatment pressure of 120 MPa or more, a treatment temperature of 700 ° C to 850 ° C, and a duration of 1 hour. Up to 2 hours. A modified NdFeB magnetic member produced by the method of any one of claims 1 to 8. The modified NdFeB magnetic member according to claim 9, wherein the modified NdFeB magnetic member has a thickness greater than 4 mm.