Patent Application
20200005996
This application claims priority to Chinese Application Serial Number CN201810694252.7 filed on Jun. 29, 2018, the entire disclosure of which is incorporated herein by reference in its entirety.
The present invention generally relates to a gradient Nd—Fe—B magnet and a method of making the gradient Nd—Fe—B magnet.
Nd—Fe—B magnets are well known in the art. Since its invention in 1983, Nd—Fe—B magnets are widely used in a variety of technologies including, but not limited to, computers, automotive, medical, and wind power. During the application of the Nd—Fe—B magnets, the residual magnetism of the Nd—Fe—B magnets decreases which negatively affects the application of the Nd—Fe—B magnets. It was observed that in many applications, the Nd—Fe—B magnets demagnetizesin the edge regions of the Nd—Fe—B magnets. Accordingly, increasing the coercivity of the edge region of the Nd—Fe—B magnets can improve the overall demagnetization resistance of the Nd—Fe—B during its application.
Currently, a diffusion process is widely used to increase the coercivity of the Nd—Fe—B magnets. The conventional diffusion process includes placing the Nd-e-B magnets in an environment containing heavy rare earth elements such as Dy or Tb and carrying out a high temperature diffusion and aging treatment. Accordingly, Dy or Tb are diffused from the grain boundary to the Nd2Fe14B phase of the Nd—Fe B magnets thereby improving the magnetic anisotropy of the Nd2Fe14B phase and effectively increasing the coercivity of the Nd—Fe—B magnets.
One such a process is disclosed in Chinese Patent CN101939804B. The process includes applying heavy rare earth elements to two sides or all sides that are parallel to the magnetization direction of the Nd—Fe—B magnet wherein the heavy rare earth elements is selected from an oxide of Dy or Tb, a fluoride of Dy or Tb, or an alloy containing Dy or Tb. After the diffusion process, the Nd—Fe—B magnets are machined in a directed perpendicular to the magnetization direction. The Nd—Fe—B magnets obtained from the diffusion process has a higher coercivity along its edges and a lower internal coercivity. However, the diffusion process applies the heavy rare earth material to two sides or all sides that are parallel to the magnetization direction of the Nd—Fe—B magnet which does not localize the repulsive region in the actual application of the Nd—Fe—B magnet to improve the coercivity. Instead, the diffusion process enhances the overall coercevity of the Nd—Fe—B magnets using diffusion to improve the demagnetization resistance of the Nd—Fe—B magnets during application. Using the diffusion process, the overall coating area of the heavy rare earth elements is large, and the overall use amount of heavy rare earth elements is relatively large. However, during the diffusion process, the direction of diffusion of heavy rare earth elements is perpendicular to the magnetization direction, and the range of high coercivity zones is completely controlled by the diffusion depth of heavy rare earth elements, resulting in poor controllability, and it is difficult to adjust the size range of the high coercivity zone according to the actual use environment of the Nd—Fe—B magnets.
The present invention overcomes the deficiencies mentioned above and provides a gradient Nd—Fe—B magnet. The present invention reduces the amount of heavy rare earth usage during the diffusion process while improves the demagnization resistance of the Nd—Fe—B magnet. The present invention further provides improved coercivity of the Nd—Fe—B magnets and improves the utilization of the heavy rare earth elements.
It is one aspect of the present invention to provide a gradient Nd—Fe—B magnet. The gradient Nd—Fe—B magnet includes an Nd—Fe—B magnet block extending along a magnetization direction and having a plurality of surfaces perpendicular to the magnetization direction. A first film, containing at least one heavy rare earth element, is disposed on one of the surfaces, attached to the Nd—Fe—B magnet block and extending along a periphery of the one of the surfaces. A second film, containing at least one heavy rare earth element, is disposed on another one of the surfaces, opposite of the one of the surfaces, attached to the Nd—Fe—B magnet block and extending along a periphery of the another one of the surfaces. The first film and the second film are diffused into the Nd—Fe—B magnet block dividing the Nd—Fe—B magnet block into an edge region, a transition region, and a central region along a plane extending perpendicular to the magnetization direction wherein the edge region has a coercivity that remains constant in a direction perpendicular to the magnetization direction, and the coercivity of the edge region, along the magnetization direction, gradually decreases from the one of the surfaces and the another one of the surfaces towards a point located between the one of the surfaces and the another one of the surfaces.
It is another aspect of the present invention to provide a method of making the gradient Nd—Fe—B magnet. The method includes a step of providing an Nd—Fe—B magnet block having a thickness of between 2-10 mm along a magnetization direction and having a plurality of surfaces perpendicular to the magnetization direction. The method also includes placing the Nd—Fe—B magnet block in a chamber containing an inert gas of argon with the magnetization direction of the Nd—Fe—B magnet block being arranged in a vertical direction. The method further includes a step of depositing a powder, containing at least one heavy rare earth element, on one of the surfaces. The next step of the method is forming a first film containing at least one heavy rare earth element on the one of the surfaces and along the periphery of the one of the surfaces. The step of forming the first film further includes a step of melting the powder on the one of the surfaces and along the periphery using a laser to form the first film and adhering the first film to the periphery. Then, the method follows with a step of removing excess powder from the one of the surfaces. After removing the excess powder, the Nd—Fe—B magnet block is rotated 180°. The method follows with a step of depositing the powder, containing at least one heavy rare earth element, on another one of the surfaces opposite of the one of the surfaces. Next, the method proceeds with a step of forming a second film containing the at least one heavy rare earth element on the another one of the surfaces and along a periphery of the another one of the surfaces. The step of forming the second film further includes a step of melting the powder on the another one of the surfaces and along the periphery using a laser to form the second film and adhering the second film to the periphery. Next, excess powder is removed from the another one of the surfaces. Then, the first film and the second film are diffused into the Nd—Fe—B magnet block under a vacuum environment or an inert environment containing argon and at a predetermined temperature.
Other advantages of the present invention will be readily appreciated, as the same becomes better understood by reference to the following detailed description when considered in connection with the accompanying drawings wherein:
Referring to the Figures, wherein like numerals indicate corresponding parts throughout the several views, it is one aspect of the present invention to provide a gradient Nd—Fe—B magnet. The gradient Nd—Fe—B magnet includes an Nd—Fe—B magnet block extending along a magnetization direction and having a plurality of surfaces perpendicular to the magnetization direction. According to one embodiment of the present invention, the Nd—Fe—B magnet block can have a thickness of between 2-10 mm along the magnetization direction. According to another embodiment, the Nd—Fe—B magnet block can have a length and a width of at least 10 mm.
A first film containing at least one heavy rare earth element, disposed on one of the surfaces, attaches to the Nd—Fe—B magnet block and extends along a periphery of the one of the surfaces. A second film containing at least one heavy rare earth element, disposed on another one of the surfaces, opposite of the one of the surfaces, attaches to the Nd—Fe—B magnet block and extending along a periphery of the another one of the surfaces. The at least one heavy rare earth element is selected from a group consisting of Tb, Dy, or an alloy containing Dy or Tb. Preferably, the first film and the second film are attached and formed on the Nd—Fe—B magnet block by melting a powder containing the at least one heavy rare earth metal on the one and the another one of the surfaces and along the periphery using a laser. In other words, the first film and the second film are only formed along the periphery of the one of the surfaces and the another one of the surfaces. According to one embodiment of the present invention, the powder containing the least one heavy rare earth element is selected from a group consisting of Tb, Dy, or an alloy containing Dy or Tb and is present in the powder in an amount of 0.1 wt. % and 2 wt. %. Preferably, according to one embodiment of the present invention, the powder has an average particle size of between 1 μm and 300 μm.
The first film and the second film are diffused into the Nd—Fe—B magnet block dividing the Nd—Fe—B magnet block into an edge region, a transition region, and a central region along a plane extending perpendicular to the magnetization direction. The central portion is located at the center of the Nd—Fe—B magnet block. The transition region is located about the Nd—Fe—B magnet block. The edge region is located about the transition region. In other words, the central, transition, and edge regions of the Nd—Fe—B magnet block are disposed in a concentric relationship with one another with the central regions being disposed at the center region, the transition region extending about the center region, and the edge region extending about the transition region.
The edge region has a coercivity that remains constant in a direction perpendicular to the magnetization direction, and the coercivity of the edge region, along the magnetization direction, gradually decreases from the one of the surfaces and the another one of the surfaces towards a point located between the one of the surfaces and the another one of the surfaces. The transition region also has a coercivity that decreases toward the central portion in the direction perpendicular to the magnetization direction and the coercivity of the transition region, along the magnetization direction, gradually decreases from the one of the surfaces and the another one of the surfaces to the point between the one of the surfaces and the another one of the surfaces. The center region has a coercivity that remains constant in the direction perpendicular to the magnetization direction and along the magnetization direction. It should be appreciated that an average of the coercivity of the edge region is greater than an average of the coercivity of the transition region and the average of the coercivity of the transition region is greater than an average of the coercivity of the central region. In other words, by diffusing the first film and the second film into the periphery of the Nd—Fe—B magnet block improves the coercivity of the edge portion of the Nd—Fe—B thereby improves the de-magnetization resistance of the Nd—Fe—B magnet.
It is another aspect of the present invention to provide a method of making the gradient Nd—Fe—B magnet. The method includes a first step of providing an Nd—Fe—B magnet block having a plurality of surfaces that are perpendicular to a magnetization direction. According to one embodiment of the present invention, the Nd—Fe—B magnet block can have a thickness of between 2-10 mm along the magnetization direction. According to another embodiment, the Nd—Fe—B magnet block can have a length and a width of at least 10 mm. The method then proceeds with placing the Nd—Fe—B magnet block in a chamber containing an inert gas of argon with the magnetization direction of the Nd—Fe—B magnet block being arranged in a vertical direction. The next step of the method includes depositing a powder, containing at least one heavy rare earth element, on the one of the surfaces. According to one embodiment of the present invention, the powder containing the least one heavy rare earth element is selected from a group consisting of Tb, Dy, or an alloy containing Dy or Tb and the powder is present in an amount of 0.1 wt. % and 2 wt. % of the Nd—Fe—B magnet block. Preferably, according to one embodiment of the present invention, the powder has an average particle size of between 1 μm and 300 μm.
Then, the method follows with a step of forming the first film containing the at least one heavy rare earth element on the one of the surfaces and along the periphery of the one of the surfaces. The step of forming the first film further includes a step of melting the powder on the one of the surfaces and along the periphery using a laser to form the first film and adhering the first film to the periphery. Preferably, an area covered by the first film is 10% to 65% of an area covered by the powder on one of the surfaces of the Nd—Fe—B magnet block. Next, excess powder are removed from the one of the surfaces. In other words, the powder of the heavy rare earth elements only forms the first film along the periphery of the one of the surfaces. This significantly reduces the amount of heavy rare earth elements used during the manufacturing process. After removing the excess powder, the Nd—Fe—B magnet block is rotated 180°.
After rotating the magnet block, the powder, containing at least one heavy rare earth element, is deposited on the another one of the surfaces opposite of the one of the surfaces. Then, the method proceeds with forming the second film containing the at least one heavy rare earth element on the another one of the surfaces and along the periphery of the another one of the surfaces. The step of forming the second film further including a step of melting the powder on the another one of the surfaces and along the periphery using a laser to form the second film and adhering the second film to the periphery. Preferably, an area covered by the second film is 10% to 65% of an area covered by the powder on the another one of the surfaces of the Nd—Fe—B magnet block. Next, the excess powder is removed from the another one of the surfaces. Similar to the first film, the powder of the heavy rare earth elements only forms the second film along the periphery of the another one of the surfaces. This also significantly reduces the amount of heavy rare earth elements used during the manufacturing process. Then, the first film and the second film are diffused into the Nd—Fe—B magnet block under a vacuum environment or an inert environment containing argon and at a predetermined temperature. The step of diffusing is further defined as heating the Nd—Fe—B magnet block including the first film and the second film at the predetermined temperature of between 850° C. and 950° C. at a diffusing time of between 6 hours and 72 hours. The diffusing further includes a step of aging the Nd—Fe—B magnet block including the first film and the second film at an aging temperature of between 450° C. and 650° C. at an aging time of between 3 hours and 15 hours.
The examples below provide a better illustration of the present invention. The examples are used for illustrative purposes only and do not limit the scope of the present invention.
In implementing example 1, a plurality of Nd—Fe—B magnet blocks 1, each having a dimension of 20 mm*20 mm*5 mm are provided. Each of the Nd—Fe—B magnet blocks 1 has a plurality of surfaces that are perpendicular to a magnetization direction. Each of the Nd—Fe—B magnet blocks 1 are then placed in a chamber containing an inert gas of argon with the magnetization direction of the Nd—Fe—B magnet block 1 being arranged in a vertical direction. Then, as best illustrated in
After rotating the Nd—Fe—B magnet block, the powder 1, containing at least one heavy rare earth element of Tb, is deposited on the another one of the surfaces opposite of the one of the surfaces. A second film containing the at least one heavy rare earth element of Tb is formed on the another one of the surfaces and along the periphery of the another one of the surfaces. In particular, the Nd—Fe—B magnet block containing the heavy rare earth element is move under a laser wherein the laser melts the powder, in a strip extending approximately 2 mm along the periphery of the another one of the surfaces, to form the second film and adhering the second film to the periphery. Excess powder are then removed from the another one of the surfaces.
Then, the first film and the second film are diffused into the Nd—Fe—B magnet block under a vacuum environment and at a predetermined temperature. In particular, the Nd—Fe—B magnet block including the first film and the second film is heated at the predetermined temperature of between 900° C. at a diffusing time of 24 hours. Then, the Nd—Fe—B magnet block including the first film and the second film is subjected to an aging treatment at an aging temperature of between 500° C. at an aging time of 6 hours.
After diffusing the Nd—Fe—B magnet block, the gradient Nd—Fe—B magnet is formed and includes an edge region 4, a transition region 5, and a central region 6 along a plane extending perpendicular to the magnetization direction. The edge region 4 has a coercivity that remains constant in a direction perpendicular to the magnetization direction, and the coercivity of the edge region 4, along the magnetization direction, gradually decreases from the one of the surfaces and the another one of the surfaces towards a point located between the one of the surfaces and the another one of the surfaces. The transition region 5 also has a coercivity that decreases toward the central portion 6 in the direction perpendicular to the magnetization direction and the coercivity of the transition region 5, along the magnetization direction, gradually decreases from the one of the surfaces and the another one of the surfaces to the point located between the one of the surfaces and the another one of the surfaces. The center region 6 has a coercivity that remains constant in the direction perpendicular to the magnetization direction and along the magnetization direction. An average of the coercivity of the edge region 4 is greater than an average of the coercivity of the transition region 5 and the average of the coercivity of the transition region 6 is greater than an average of the coercivity of the central region 6.
After forming the gradient Nd—Fe—B magnet, the gradient magnet is sliced along the in the length or width direction forming a plurality of 20 mm*1 mmm*5 mm Nd—Fe—B magnets as best illustrated in
In implementing example 2, a plurality of Nd—Fe—B magnet blocks, each having a dimension of 40 mm*40 mm*10 mm are provided. Each of the Nd—Fe—B magnet blocks has a plurality of surfaces that are perpendicular to a magnetization direction. Each of the Nd—Fe—B magnet blocks are then placed in a chamber containing an inert gas of argon with the magnetization direction of the Nd—Fe—B magnet block being arranged in a vertical direction. Then, a powder, containing at least one heavy rare earth element of Tb and having an average particle size of 100 μm, is disposed on the one of the surfaces. The heavy rare earth element is 2.0 wt. % of the total mass of the Nd—Fe—B magnet block. Next, a first film, containing the at least one heavy rare earth element of Tb, is formed on the one of the surfaces and along the periphery of the one of the surfaces. More specifically, the Nd—Fe—B magnet block containing the heavy rare earth element is move under a laser wherein the laser melts the powder, in a strip extending approximately 3 mm along the periphery of the one of the surfaces, to form the first film and adhering the first film to the periphery. The area covered by the first film is approximately 28% the area covered by the powder on one of the surfaces of the Nd—Fe—B magnet block. Excess powder are then removed from the one of the surfaces. The Nd—Fe—B magnet block is rotated 180°.
After rotating the magnet block, the powder, containing at least one heavy rare earth element of Tb, is deposited on the another one of the surfaces opposite of the one of the surfaces. A second film containing the at least one heavy rare earth element of Tb is formed on the another one of the surfaces and along the periphery of the another one of the surfaces. In particular, the Nd—Fe—B magnet block containing the heavy rare earth element is move under a laser wherein the laser melts the powder, in a strip extending approximately 3 mm along the periphery of the another one of the surfaces, to form the second film and adhering the second film to the periphery. Excess powder are then removed from the another one of the surfaces.
Then, the first film and the second film are diffused into the Nd—Fe—B magnet block under a vacuum environment and at a predetermined temperature. In particular, the Nd—Fe—B magnet block including the first film and the second film is heated at the predetermined temperature of between 850° C. at a diffusing time of 72 hours. Then, the Nd—Fe—B magnet block including the first film and the second film is subjected to an aging treatment at an aging temperature of between 500° C. at an aging time of 15 hours.
After diffusing the Nd—Fe—B magnet block, the gradient Nd—Fe—B magnet is formed and includes an edge region, a transition region, and a central region along a plane extending perpendicular to the magnetization direction. The edge region has a coercivity that remains constant in a direction perpendicular to the magnetization direction, and the coercivity of the edge region, along the magnetization direction, gradually decreases from the one of the surfaces and the another one of the surfaces towards a point located between the one of the surfaces and the another one of the surfaces. The transition region also has a coercivity that decreases toward the central portion in the direction perpendicular to the magnetization direction and the coercivity of the transition region, along the magnetization direction, gradually decreases from the one of the surfaces and the another one of the surfaces to the point between the one of the surfaces and the another one of the surfaces. The center region has a coercivity that remains constant in the direction perpendicular to the magnetization direction and along the magnetization direction. An average of the coercivity of the edge region is greater than an average of the coercivity of the transition region and the average of the coercivity of the transition region is greater than an average of the coercivity of the central region.
After forming the gradient Nd—Fe—B magnet, the gradient magnet is sliced along the in the length or width direction forming a plurality of 40 mm*1 mmm*10 mm Nd—Fe—B magnets. Then, the Nd—Fe—B magnets are further sliced into small Nd—Fe—B magnets having a dimension of 1 mm*1 mm*1 mm. It should be noted that the Nd—Fe—B magnet located in the first row and the first column is referred to as “1, 1.” The Nd—Fe—B magnet located in the second row and the first column is referred to as “2, 1.” The Nd—Fe—B magnet located in the third row and the third column is referred to as “3, 3.” Properties of the small Nd—Fe—B magnets are then tested wherein portions of the properties are listed in Table 1 below.
In implementing example 3, a plurality of Nd—Fe—B magnet blocks, each having a dimension of 80 mm*50 mm*5 mm are provided. Each of the Nd—Fe—B magnet blocks has a plurality of surfaces that are perpendicular to a magnetization direction. Each of the Nd—Fe—B magnet blocks are then placed in a chamber containing an inert gas of argon with the magnetization direction of the Nd—Fe—B magnet block being arranged in a vertical direction. Then, a powder, containing at least one heavy rare earth element of Dy and having an average particle size of 200 μm, is disposed on the one of the surfaces. The heavy rare earth element is 0.5 wt. % of the total mass of the Nd—Fe—B magnet block. Next, a first film, containing the at least one heavy rare earth element of Dy, is formed on the one of the surfaces and along the periphery of the one of the surfaces. More specifically, the Nd—Fe—B magnet block containing the heavy rare earth element is move under a laser wherein the laser melts the powder, in a strip extending approximately 2 mm along the periphery of the one of the surfaces, to form the first film and adhering the first film to the periphery. The area covered by the first film is approximately 24% the area covered by the powder on one of the surfaces of the Nd—Fe—B magnet block. Excess powder are then removed from the one of the surfaces. The Nd—Fe—B magnet block is rotated 180°.
After rotating the magnet block, the powder, containing at least one heavy rare earth element of Dy, is deposited on the another one of the surfaces opposite of the one of the surfaces. A second film containing the at least one heavy rare earth element of Dy is formed on the another one of the surfaces and along the periphery of the another one of the surfaces. In particular, the Nd—Fe—B magnet block containing the heavy rare earth element is move under a laser wherein the laser melts the powder, in a strip extending approximately 2 mm along the periphery of the another one of the surfaces, to form the second film and adhering the second film to the periphery. Excess powder are then removed from the another one of the surfaces.
Then, the first film and the second film are diffused into the Nd—Fe—B magnet block under a vacuum environment and at a predetermined temperature. In particular, the Nd—Fe—B magnet block including the first film and the second film is heated at the predetermined temperature of between 950° C. at a diffusing time of 6 hours. Then, the Nd—Fe—B magnet block including the first film and the second film is subjected to an aging treatment at an aging temperature of between 450° C. at an aging time of 8 hours.
After diffusing the Nd—Fe—B magnet block, the gradient Nd—Fe—B magnet is formed and includes an edge region, a transition region, and a central region along a plane extending perpendicular to the magnetization direction. The edge region has a coercivity that remains constant in a direction perpendicular to the magnetization direction, and the coercivity of the edge region, along the magnetization direction, gradually decreases from the one of the surfaces and the another one of the surfaces towards a point located between the one of the surfaces and the another one of the surfaces. The transition region also has a coercivity that decreases toward the central portion in the direction perpendicular to the magnetization direction and the coercivity of the transition region, along the magnetization direction, gradually decreases from the one of the surfaces and the another one of the surfaces to the point between the one of the surfaces and the another one of the surfaces. The center region has a coercivity that remains constant in the direction perpendicular to the magnetization direction and along the magnetization direction. An average of the coercivity of the edge region is greater than an average of the coercivity of the transition region and the average of the coercivity of the transition region is greater than an average of the coercivity of the central region.
After forming the gradient Nd—Fe—B magnet, the gradient magnet is sliced along the in the length or width direction forming a plurality of 20 mm*1 mmm*5 mm Nd—Fe—B magnets. Then, the Nd—Fe—B magnets are further sliced into small Nd—Fe—B magnets having a dimension of 1 mm*1 mm*1 mm. It should be noted that the Nd—Fe—B magnet located in the first row and the first column is referred to as “1, 1.” The Nd—Fe—B magnet located in the second row and the first column is referred to as “2, 1.” The Nd—Fe—B magnet located in the third row and the third column is referred to as “3, 3.” Properties of the small Nd—Fe—B magnets are then tested wherein portions of the properties are listed in Table 1 below.
In implementing example 4, a plurality of Nd—Fe—B magnet blocks, each having a dimension of 80 mm*80 mm*5 mm are provided. Each of the Nd—Fe—B magnet blocks has a plurality of surfaces that are perpendicular to a magnetization direction. Each of the Nd—Fe—B magnet blocks are then placed in a chamber containing an inert gas of argon with the magnetization direction of the Nd—Fe—B magnet block being arranged in a vertical direction. Then, a powder, containing at least one heavy rare earth element of Dy and having an average particle size of 250 μm, is disposed on the one of the surfaces. The powder is an alloy powder containing Tb and Co wherein Tb is present at 90 wt. %). The powder is 0.5% of the mass of the Nd—Fe—B magnet block. Next, a first film, containing the at least one heavy rare earth element of Tb, is formed on the one of the surfaces and along the periphery of the one of the surfaces. More specifically, the Nd—Fe—B magnet block containing the heavy rare earth element is move under a laser wherein the laser melts the powder, in a strip extending approximately 2 mm along the periphery of the one of the surfaces, to form the first film and adhering the first film to the periphery. The area covered by the first film is approximately 10% the area covered by the powder on one of the surfaces of the Nd—Fe—B magnet block. Excess powder are then removed from the one of the surfaces. The Nd—Fe—B magnet block is rotated 180°.
After rotating the magnet block, the powder, containing at least one heavy rare earth element of Tb, is deposited on the another one of the surfaces opposite of the one of the surfaces. A second film containing the at least one heavy rare earth element of Tb is formed on the another one of the surfaces and along the periphery of the another one of the surfaces. In particular, the Nd—Fe—B magnet block containing the heavy rare earth element is move under a laser wherein the laser melts the powder, in a strip extending approximately 2 mm along the periphery of the another one of the surfaces, to form the second film and adhering the second film to the periphery. Excess powder are then removed from the another one of the surfaces.
Then, the first film and the second film are diffused into the Nd—Fe—B magnet block under a vacuum environment and at a predetermined temperature. In particular, the Nd—Fe—B magnet block including the first film and the second film is heated at the predetermined temperature of between 900° C. at a diffusing time of 24 hours. Then, the Nd—Fe—B magnet block including the first film and the second film is subjected to an aging treatment at an aging temperature of between 650° C. at an aging time of 6 hours.
After diffusing the Nd—Fe—B magnet block, the gradient Nd—Fe—B magnet is formed and includes an edge region, a transition region, and a central region along a plane extending perpendicular to the magnetization direction. The edge region has a coercivity that remains constant in a direction perpendicular to the magnetization direction, and the coercivity of the edge region, along the magnetization direction, gradually decreases from the one of the surfaces and the another one of the surfaces towards a point located between the one of the surfaces and the another one of the surfaces. The transition region also has a coercivity that decreases toward the central portion in the direction perpendicular to the magnetization direction and the coercivity of the transition region, along the magnetization direction, gradually decreases from the one of the surfaces and the another one of the surfaces to the point between the one of the surfaces and the another one of the surfaces. The center region has a coercivity that remains constant in the direction perpendicular to the magnetization direction and along the magnetization direction. An average of the coercivity of the edge region is greater than an average of the coercivity of the transition region and the average of the coercivity of the transition region is greater than an average of the coercivity of the central region.
After forming the gradient Nd—Fe—B magnet, the gradient magnet is sliced along the in the length or width direction forming a plurality of 80 mm*1 mmm*5 mm Nd—Fe—B magnets. Then, the Nd—Fe—B magnets are further sliced into small Nd—Fe—B magnets having a dimension of 1 mm*1 mm*1 mm. It should be noted that the Nd—Fe—B magnet located in the first row and the first column is referred to as “1, 1.” The Nd—Fe—B magnet located in the second row and the first column is referred to as “2, 1.” The Nd—Fe—B magnet located in the third row and the third column is referred to as “3, 3.” Properties of the small Nd—Fe—B magnets are then tested wherein portions of the properties are listed in Table 1 below.
In implementing example 5, a plurality of Nd—Fe—B magnet blocks, each having a dimension of 10 mm*10 mm*2 mm are provided. Each of the Nd—Fe—B magnet blocks has a plurality of surfaces that are perpendicular to a magnetization direction. Each of the Nd—Fe—B magnet blocks are then placed in a chamber containing an inert gas of argon with the magnetization direction of the Nd—Fe—B magnet block being arranged in a vertical direction. Then, a powder, containing at least one heavy rare earth element of Tb and having an average particle size of 10 μm, is disposed on the one of the surfaces. The powder is a hydrogenated Tb powder wherein the powder is 0.1% of the mass of the Nd—Fe—B magnet blocks. Next, a first film, containing the at least one heavy rare earth element of Tb, is formed on the one of the surfaces and along the periphery of the one of the surfaces. More specifically, the Nd—Fe—B magnet block containing the heavy rare earth element is move under a laser wherein the laser melts the powder, in a strip extending approximately 2 mm along the periphery of the one of the surfaces, to form the first film and adhering the first film to the periphery. The area covered by the first film is approximately 64% the area covered by the powder on one of the surfaces of the Nd—Fe—B magnet block. Excess powder are then removed from the one of the surfaces. The Nd—Fe—B magnet block is rotated 180°.
After rotating the magnet block, the powder, containing at least one heavy rare earth element of Tb, is deposited on the another one of the surfaces opposite of the one of the surfaces. A second film containing the at least one heavy rare earth element of Tb is formed on the another one of the surfaces and along the periphery of the another one of the surfaces. In particular, the Nd—Fe—B magnet block containing the heavy rare earth element is move under a laser wherein the laser melts the powder, in a strip extending approximately 2 mm along the periphery of the another one of the surfaces, to form the second film and adhering the second film to the periphery. Excess powder are then removed from the another one of the surfaces.
Then, the first film and the second film are diffused into the Nd—Fe—B magnet block under a vacuum environment and at a predetermined temperature. In particular, the Nd—Fe—B magnet block including the first film and the second film is heated at the predetermined temperature of between 900° C. at a diffusing time of 6 hours. Then, the Nd—Fe—B magnet block including the first film and the second film is subjected to an aging treatment at an aging temperature of between 650° C. at an aging time of 3 hours.
After diffusing the Nd—Fe—B magnet block, the gradient Nd—Fe—B magnet is formed and includes an edge region, a transition region, and a central region along a plane extending perpendicular to the magnetization direction. The edge region has a coercivity that remains constant in a direction perpendicular to the magnetization direction, and the coercivity of the edge region, along the magnetization direction, gradually decreases from the one of the surfaces and the another one of the surfaces towards a point located between the one of the surfaces and the another one of the surfaces. The transition region also has a coercivity that decreases toward the central portion in the direction perpendicular to the magnetization direction and the coercivity of the transition region, along the magnetization direction, gradually decreases from the one of the surfaces and the another one of the surfaces to the point between the one of the surfaces and the another one of the surfaces. The center region has a coercivity that remains constant in the direction perpendicular to the magnetization direction and along the magnetization direction. An average of the coercivity of the edge region is greater than an average of the coercivity of the transition region and the average of the coercivity of the transition region is greater than an average of the coercivity of the central region.
In comparative example 1, a plurality of Nd—Fe—B magnet blocks, each having a dimension of 20 mm*20 mm*5 mm are provided. More specifically, the Nd—Fe—B magnet blocks are provided using the saw raw powder as the Nd—Fe—B magnets from Implementing Example 5. The Nd—Fe—B magnet blocks are then sliced along the in the length or width direction forming a plurality of 20 mm*1 mmm*5 mm Nd—Fe—B magnets. Then, the Nd—Fe—B magnets are further sliced into small Nd—Fe—B magnets having a dimension of 1 mm*1 mm*1 mm. It should be noted that the Nd—Fe—B magnet located in the first row and the first column is referred to as “1, 1.” The Nd—Fe—B magnet located in the second row and the first column is referred to as “2, 1.” The Nd—Fe—B magnet located in the third row and the third column is referred to as “3, 3.” Properties of the small Nd—Fe—B magnets are then tested wherein portions of the properties are listed in Table 1 below.
As illustrated in
Obviously, many modifications and variations of the present invention are possible in light of the above teachings and may be practiced otherwise than as specifically described while within the scope of the appended claims. These antecedent recitations should be interpreted to cover any combination in which the inventive novelty exercises its utility. The use of the word “said” in the apparatus claims refers to an antecedent that is a positive recitation meant to be included in the coverage of the claims whereas the word “the” precedes a word not meant to be included in the coverage of the claims.
| Number | Date | Country | Kind |
|---|---|---|---|
| 201810694252.7 | Jun 2018 | CN | national |
