阅读说明：本技术 一种稀土磁体的氮化方法及氮化稀土磁体 (Nitriding method of rare earth magnet and nitrided rare earth magnet ) 是由 孙永阳 李军华 孔佳元 李玉平 韩相华 陈文洪 于 2020-12-16 设计创作，主要内容包括：本发明公开了一种稀土磁体的氮化方法,所述方法包括以下步骤：1)抽真空,向装有稀土磁体的反应器中加入氮源,进行三段加热处理,得到半成品；所述三段加热处理的加热温度逐段升高；2)将半成品升温至第一设定温度,之后将温度调节至第二设定温度并抽真空,通入惰性气体,并在第二设定温度下进行保温,得到氮化稀土磁体；所述第二设定温度低于第一设定温度。本发明提供的稀土磁体的氮化方法可以在提高氮含量的同时,使氮元素在磁体中分布更加均匀。(The invention discloses a nitriding method of a rare earth magnet, which comprises the following steps: 1) vacuumizing, adding a nitrogen source into a reactor filled with a rare earth magnet, and carrying out three-stage heating treatment to obtain a semi-finished product; the heating temperature of the three-stage heating treatment is increased section by section; 2) heating the semi-finished product to a first set temperature, then adjusting the temperature to a second set temperature, vacuumizing, introducing inert gas, and preserving heat at the second set temperature to obtain a rare earth nitride magnet; the second set temperature is lower than the first set temperature. The nitriding method of the rare earth magnet can improve the nitrogen content and ensure that the nitrogen element is more uniformly distributed in the magnet.)

1. A method of nitriding a rare earth magnet, comprising the steps of:

(1) vacuumizing, adding a nitrogen source into a reactor filled with a rare earth magnet, and carrying out three-stage heating treatment to obtain a semi-finished product; the heating temperature of the three-stage heating treatment is increased section by section;

(2) heating the semi-finished product in the step (1) to a first set temperature, then adjusting the temperature to a second set temperature, vacuumizing, introducing inert gas, and preserving heat at the second set temperature to obtain a rare earth nitride magnet; the second set temperature is lower than the first set temperature.

2. The method according to claim 1, wherein the rare earth magnet of step (1) has a general formula of ReTm, wherein Re is a rare earth metal, Tm is a 3d transition group element and/or a 4d transition group element;

preferably, the general formula of the nitrided rare earth magnet is ReTmN;

preferably, the evacuation of step (1) reduces the reactor pressure to below 1000Pa, preferably to below 10 Pa;

preferably, the nitrogen source of step (1) comprises a gaseous nitrogen source and/or a solid nitrogen source;

preferably, the gaseous nitrogen source is a nitrogen element-containing gas;

preferably, the gaseous nitrogen source comprises nitrogen and/or ammonia;

preferably, the gaseous nitrogen source further comprises hydrogen;

preferably, the solid nitrogen source comprises ammonium bicarbonate and/or ammonium chloride;

preferably, the nitrogen source in step (1) is a gaseous nitrogen source, and the pressure of the gaseous nitrogen source in the reactor is 0.001-10MPa, preferably 0.01-2 MPa;

preferably, the nitrogen source in the step (1) is a solid nitrogen source, and before the three-stage heating treatment, protective gas is introduced into the reactor until the pressure is 0.001-10MPa, preferably 0.01-2 MPa.

3. The method as claimed in claim 1 or 2, wherein the first temperature of the three-stage heating treatment in step (1) is 330-;

preferably, the first holding time of the three-stage heat treatment in the step (1) is 0 to 24 hours and does not include 0, and preferably 0.1 to 5 hours.

4. The method as claimed in any one of claims 1 to 3, wherein the temperature of the second stage of the three-stage heating treatment in step (1) is 670-730K and does not include 730K, preferably 690-710K;

preferably, the second period of the three-period heat treatment in the step (1) has the holding time of 0-24h, excluding 0, and preferably 0.1-5 h.

5. The method as claimed in any one of claims 1 to 4, wherein the temperature of the third section of the three-section heating treatment in step (1) is 730-830K and excludes 830K, preferably 750-780K;

preferably, the third holding time of the three-stage heat treatment in the step (1) is 0-24h and does not include 0, and preferably 0.1-5 h.

6. The method as claimed in any one of claims 1 to 5, wherein the first set temperature in step (2) is 830-860K and does not include 860K, preferably 830-840K;

preferably, in the step (2), the temperature rise time for raising the temperature to the first set temperature is 0-24h and does not include 0, and preferably 0.5-5 h.

7. The process of any one of claims 1 to 6, wherein the evacuation of step (2) reduces the reactor pressure to below 1000Pa, preferably to below 10 Pa;

preferably, the pressure of the reactor is adjusted to 0.001-1MPa by introducing inert gas in the step (2);

preferably, the second set temperature in the step (2) is 600-700K, preferably 620-670K;

preferably, the holding time for holding at the second set temperature in the step (2) is 0-24h and does not include 0, preferably 0.5-5 h.

8. The method of any one of claims 1-7, wherein step (2) further comprises: and cooling to room temperature after the heat preservation is carried out at the second set temperature.

9. Method according to any of claims 1-8, characterized in that the method comprises the steps of:

(1) placing the rare earth magnet in a reactor, vacuumizing to below 1000Pa, introducing gas containing nitrogen elements, heating to 370-420K and preserving heat for 0.1-5h, heating to 690-710K and preserving heat for 0.1-5h, and heating to 750-780K and preserving heat for 0.1-5h to obtain a semi-finished product;

(2) and (2) heating the semi-finished product in the step (1) to 830-840K within 0.5-5h, then adjusting the temperature to 620-670K, vacuumizing to reduce the pressure of the reactor to below 1000Pa, adjusting the pressure of the inert gas reactor to 0.001-1MPa, keeping the temperature at a second set temperature for 0.5-5h, and cooling to room temperature to obtain the rare earth nitride magnet.

10. A nitrided rare earth magnet obtained by the nitriding method for a rare earth magnet according to any one of claims 1 to 9.

Technical Field

The invention belongs to the technical field of magnetic materials, and relates to a rare earth magnet nitriding method and a nitrided rare earth magnet.

Background

In recent years, with the progress and development of science and technology, the application range of magnetic materials is wider and wider, and people's lives are more and more unable to leave the magnetic materials. The magnetic materials are divided into permanent magnetic materials and soft magnetic materials, and have different functions due to different properties. Rare earth magnetic materials are widely used because of their excellent magnetic properties.

The most commonly used rare earth permanent magnet material is NdFeB, which is the rare earth permanent magnet material with the highest permanent magnet performance and magnetic energy product at present. However, since rare earth elements are contained in the earth crust only in a small amount, the mining and purification costs are high, resulting in high cost of NdFeB materials along with high performance.

The samarium iron nitrogen magnet avoids the defects of low Curie temperature, easy oxidation, high cost and the like of the neodymium iron boron magnet, and becomes a hot spot for the research of a new generation of rare earth permanent magnet material. The introduction of nitrogen atoms does not change the crystal structure of the samarium-iron alloy, but causes lattice expansion, so that the magnetic coupling exchange effect of alloy iron is enhanced, the Curie temperature of the alloy is greatly improved, the anisotropic field is enhanced, and the key for improving the permanent magnet performance of the samarium-iron alloy is realized, so that the nitriding treatment process plays a vital role in the preparation of the samarium-iron-nitrogen magnet. At present, the mature nitriding process at home and abroad is to obtain alloy powder by a mechanical method and then carry out nitriding treatment, and the solid powder nitriding has the defects of non-uniform nitriding, incomplete nitriding, low efficiency, easy powder oxidation and the like.

Rare earth-iron-nitrogen materials, including SmFeN, NdFeN, CeFeN and the like, are made of permanent magnetic properties of materials and soft magnetic properties of materials, but the preparation method comprises the steps of firstly forming rare earth iron alloy and then nitriding the alloy in the preparation process.

Computers, mobile phones, network equipment and the like for modern communication can generate electromagnetic interference and electromagnetic radiation in the use process. In order to effectively reduce and eliminate electromagnetic interference and radiation, a wave-absorbing material with high complex permeability is required. The ferrite material widely used at present has the defects of narrow frequency band, low complex permeability under high frequency and the like, and the metal soft magnetic material has low high-frequency soft magnetic performance due to eddy current loss. The materials such as CeFeN and the like can keep high magnetic conductivity and wide resonance frequency under high frequency, can realize electromagnetic shielding in a wide frequency band and reduce signal noise, meet the requirements of modern technology, and are widely applied to the fields of instruments, communication and the like.

The rare earth transition metal magnetic material can show excellent magnetic performance after nitridation, but the performance of the material can be seriously influenced by insufficient nitrogen content and uneven nitrogen element distribution in the nitridation process.

CN101699578A discloses a rare earth iron nitrogen high-frequency soft magnetic material, a composite material and a preparation method thereof, wherein the rare earth iron nitrogen high-frequency soft magnetic material is prepared by firstly smelting 10-30 wt% of rare earth elements and 70-90 wt% of iron into iron-based alloy, then crushing the iron-based alloy into small particles, grinding the small particles into powder, and then performing nitriding treatment, wherein the treatment temperature is 250-550 ℃, and the chemical formula of the material is R₂Fe₁₇N_3-δ. However, the nitrogen content and uniformity of the product obtained by the method need to be improved.

CN 107557551A discloses a preparation method of samarium-iron-nitrogen permanent magnet material, which is characterized in that metastable samarium-iron alloy is subjected to large plastic deformation, then nitriding treatment and annealing crystallization treatment are carried out, and defects generated by large plastic deformation are utilized, so that the introduction and diffusion of nitrogen atoms are facilitated, and the nitrogen permeation quantity and uniformity of the alloy are remarkably improved. However, the process of this scheme is too complicated, resulting in an increase in production cost.

Disclosure of Invention

Aiming at the defects in the prior art, the invention aims to provide a rare earth magnet nitriding method and a nitrided rare earth magnet. The method provided by the invention solves the problems of insufficient nitrogen content and uneven nitrogen element distribution after the rare earth magnet is nitrided.

In order to achieve the purpose, the invention adopts the following technical scheme:

in a first aspect, the present invention provides a method of nitriding a rare earth magnet, the method comprising the steps of:

(1) vacuumizing, adding a nitrogen source into a reactor filled with a rare earth magnet, and carrying out three-stage heating treatment to obtain a semi-finished product; the heating temperature of the three-stage heating treatment is increased section by section;

(2) heating the semi-finished product in the step (1) to a first set temperature, then adjusting the temperature to a second set temperature, vacuumizing, introducing inert gas, and preserving heat at the second set temperature to obtain a rare earth nitride magnet; the second set temperature is lower than the first set temperature.

In the method provided by the invention, three-stage heating treatment is a main nitriding process, so that nitrogen-containing gas molecules adsorbed on the surface of the alloy can enter the alloy (rare earth magnet) through diffusion to form a nitrogen-containing alloy (namely a semi-finished product), and the nitrogen element can be adsorbed on the surface of the powder and then reasonably utilize the diffusion kinetics, so that the penetration depth of the nitrogen element is improved, and the nitrogen content is improved; the first set temperature heating is a homogenization treatment step, so that the adsorption and diffusion of nitrogen elements into the alloy can be further promoted, and the nitrogen elements are distributed more uniformly in the alloy; and the second set temperature heating makes the nitrogen element in the alloy diffuse uniformly.

In the method provided by the invention, the step (2) of adjusting the temperature to the second set temperature and vacuumizing may be directly cooling to the second set temperature and then vacuumizing, or may be cooling to room temperature, vacuumizing, and then reheating to the second set temperature.

In the method provided by the invention, three different parts can be selected on the obtained rare earth nitride magnet, and the mass fraction of the nitrogen element is measured by using a nitrogen element content detection device so as to investigate whether the distribution of the nitrogen element is uniform or not.

In the invention, the rare earth magnet in the step (1) can be block or powder, and more preferably is powder, and the effect is better.

The following is a preferred technical solution of the present invention, but not a limitation to the technical solution provided by the present invention, and the technical objects and advantageous effects of the present invention can be better achieved and achieved by the following preferred technical solution.

As a preferable technical scheme of the invention, the general formula of the rare earth magnet in the step (1) is ReTm, wherein Re is rare earth metal, and Tm is 3d transition group element and/or 4d transition group element. The 3d transition group element comprises at least one of Sc, Ti, V, Cr, Mn, Fe, Co, Ni, Cu or Zn, and the 4d transition group element refers to at least one of Y, Zr, Nb, Mo, Tc, Ru, Rh, Pd, Ag or Cd.

Preferably, the general formula of the nitrided rare earth magnet is ReTmN. In the present invention, the specific ratio of Re to Tm is not limited as long as phase formation is possible.

Preferably, the evacuation in step (1) reduces the reactor pressure to 1000Pa or less, such as 900Pa, 500Pa, 100Pa, 50Pa, 10Pa, 5Pa, etc., preferably to 10Pa or less.

Preferably, the nitrogen source of step (1) comprises a gaseous nitrogen source and/or a solid nitrogen source.

Preferably, the gaseous nitrogen source is a nitrogen element-containing gas.

Preferably, the gaseous nitrogen source comprises nitrogen and/or ammonia.

Preferably, the gaseous nitrogen source further comprises hydrogen.

Preferably, the solid nitrogen source comprises ammonium bicarbonate.

Preferably, the nitrogen source in step (1) is a gaseous nitrogen source having a pressure in the reactor of 0.001 to 10MPa, such as 0.001MPa, 1MPa, 2MPa, 5MPa, 8MPa or 10MPa, and preferably 0.01 to 2 MPa.

Preferably, the nitrogen source in step (1) is a solid nitrogen source, and before the three-stage heating treatment, a protective gas is introduced into the reactor to a pressure of 0.001 to 10MPa, such as 0.001MPa, 1MPa, 2MPa, 5MPa, 8MPa or 10MPa, and preferably 0.01 to 2 MPa.

As a preferred technical solution of the present invention, the first-stage temperature of the three-stage heating treatment in step (1) is 330-470K, such as 330K, 350K, 380K, 400K, 420K, 450K or 470K, preferably 370-420K.

Preferably, the first holding time of the three-stage heat treatment in step (1) is 0-24h and does not include 0, such as 0.1h, 0.5h, 1h, 5h, 10h, 20h or 24, and the like, and preferably 0.1-5 h.

In the invention, the first stage of the three-stage heating in the step (1) is to discharge gas, particularly oxygen, adsorbed in the ReTm alloy so as to prevent oxidation of the alloy during subsequent nitridation.

As a preferred technical solution of the present invention, the temperature of the second stage of the three-stage heating treatment in step (1) is 670-.

Preferably, the second period of the three-stage heat treatment in the step (1) has a holding time of 0-24h and does not include 0, such as 0.1h, 0.5h, 1h, 5h, 10h, 20h or 24h, and the like, and preferably 0.1-5 h.

In the invention, the second stage of heating in the three-stage heating of the step (1) has the function of preheating and adsorbing the ReTm and N element atmosphere, so that the nitrogen element atmosphere is fully adsorbed on the surface of the ReTm.

As a preferable technical solution of the present invention, the temperature of the third stage of the three-stage heating treatment in step (1) is 730-830K and does not include 830K, such as 730K, 740K, 750K, 760K, 770K, 780K, 790K, 800K, 810K or 820K, and preferably 750-780K.

Preferably, the third holding time of the three-stage heat treatment in the step (1) is 0-24h and does not include 0, such as 0.1h, 0.5h, 1h, 5h, 10h, 20h or 24h, and the like, and preferably 0.1-5 h.

In the invention, the third stage of heating in the three-stage heating of the step (1) aims at gas molecules adsorbed on the surface of the alloy, and the gas molecules can enter the alloy through diffusion to form the ReTmN alloy.

As a preferred technical solution of the present invention, in the step (2), the first set temperature is 830-860K and does not include 860K, such as 830K, 835K, 840K, 845K or 850K, and preferably 830-840K. In the present invention, if the first set temperature is too high, this will cause decomposition of ReTmN into ReN and Tm phases, and the product will deviate from the desired components; if the first set temperature is too low, the N content is low and non-uniform.

Preferably, in the step (2), the temperature raising time for raising the temperature to the first set temperature is 0-24h and does not include 0, for example, 1h, 5h, 10h, 15h, 20h or 24h, and the like, and preferably 0.5-5 h.

In a preferred embodiment of the present invention, the evacuation in step (2) is performed to reduce the reactor pressure to 1000Pa or less, for example, 900Pa, 500Pa, 100Pa, 50Pa, 10Pa, 5Pa, etc., preferably to 10Pa or less.

Preferably, the pressure in the reactor is adjusted to 0.001-1MPa, such as 0.001MPa, 0.01MPa, 0.1MPa, 0.5MPa or 1MPa, etc., by introducing an inert gas as described in step (2).

Preferably, the second set temperature in step (2) is 600-.

Preferably, the incubation time for the incubation at the second set temperature in the step (2) is 0-24h excluding 0, such as 1h, 5h, 10h, 15h, 20h or 24h, etc., preferably 0.5-5 h.

As a preferable embodiment of the present invention, the step (2) further comprises: and cooling to room temperature after the heat preservation is carried out at the second set temperature.

As a further preferred technical solution of the method of the present invention, the method comprises the steps of:

(1) placing the rare earth magnet in a reactor, vacuumizing to below 1000Pa, introducing gas containing nitrogen elements, heating to 370-420K and preserving heat for 0.1-5h, heating to 690-710K and preserving heat for 0.1-5h, and heating to 750-780K and preserving heat for 0.1-5h to obtain a semi-finished product;

(2) and (2) heating the semi-finished product in the step (1) to 830-840K within 0.5-5h, then adjusting the temperature to 620-670K, vacuumizing to reduce the pressure of the reactor to below 1000Pa, adjusting the pressure of the inert gas reactor to 0.001-1MPa, keeping the temperature at a second set temperature for 0.5-5h, and cooling to room temperature to obtain the rare earth nitride magnet.

In a second aspect, the present invention provides a nitrided rare earth magnet obtained by the method for nitriding a rare earth magnet according to the first aspect.

Compared with the prior art, the invention has the following beneficial effects:

the nitriding method of the rare earth magnet provided by the invention can improve the nitrogen content and simultaneously make the nitrogen element distributed in the magnet more uniformly, thereby solving the problems of insufficient nitrogen content and non-uniform nitrogen element distribution after the rare earth magnet is nitrided in the prior art.

Detailed Description

In order to better illustrate the present invention and facilitate the understanding of the technical solutions of the present invention, the present invention is further described in detail below. The following examples are merely illustrative of the present invention and do not represent or limit the scope of the claims, which are defined by the claims.

The following are typical but non-limiting examples of the invention:

example 1

This example performs nitridation of a rare earth magnet as follows:

(1) taking Sm₂Fe₁₇Putting the alloy block into a nitriding furnace, vacuumizing until the pressure is reduced to 95Pa, closing a vacuumizing system, and filling 1.2MPa ammonia gas;

(2) heating to 450K, and keeping the temperature for 2 hours;

(3) after the temperature preservation at 450K is finished, heating to 710K, and preserving the heat for 1 hour;

(4) after the 710K heat preservation is finished, heating to 780K, and preserving heat for 5 hours to obtain a semi-finished product;

(5) after the 780K heat preservation is finished, heating to 850K after 1 hour;

(6) cooling to 680K after the heat preservation of 850K is finished, pumping out gas in the nitriding furnace, vacuumizing until the pressure is reduced to 90Pa, introducing argon of 0.05MPa, and preserving the heat for 3 hours;

(7)680K, cooling to room temperature after heat preservation, taking out the nitrided SmFeN alloy, taking out materials at three different positions, and measuring the mass fraction of nitrogen element by using a nitrogen element content detection device, wherein the test results are shown in Table 1.

Example 2

This example performs nitridation of a rare earth magnet as follows:

(1) taking Sm₂Fe₁₇Alloy powder with the powder granularity of 0.1 mu m-10 mm is put into a nitriding furnace, vacuumized until the pressure is reduced to 9Pa, a vacuumizing system is closed, and 1.2MPa ammonia gas is filled;

(2) heating to 420K, and keeping the temperature for 2 hours;

(3) after the temperature preservation at 420K is finished, heating to 680K, and preserving the heat for 1 hour;

(4) after the heat preservation at 680K is finished, heating to 750K, and preserving the heat for 4 hours;

(5) after the 750K heat preservation is finished, heating to 830K after 1 hour to obtain a semi-finished product;

(6) cooling to 670K after the 830K heat preservation is finished, pumping out gas in the nitriding furnace, vacuumizing until the pressure is reduced to 9Pa, introducing argon gas of 0.03MPa, and preserving the heat for 1 hour;

(7)670K, cooling to room temperature after heat preservation, taking the nitrided SmFeN alloy powder out, taking the materials at three different positions, and measuring the mass fraction of nitrogen element by using a nitrogen element content detection device, wherein the test results are shown in Table 1.

Example 3

The same as the example 2 except for the step (6), in the step (6) of the present example, after the heat preservation at 830K is finished, the temperature is cooled to room temperature, the gas in the nitriding furnace is pumped out, the nitriding furnace is vacuumized until the pressure is reduced to below 10Pa, then 0.03MPa argon is introduced, the temperature is raised to 670K, and the heat preservation is carried out for 1 hour.

Example 4

The same as example 2 except for the step (1), in the step (1) of this example, the vacuum-pumping system was closed, and a mixed gas of ammonia and hydrogen at 1.2MPa (mixed molar ratio 1:1) was introduced.

Example 5

Except that Sm is₂Fe₁₇Alloy powder is changed into SmFe₉A SmFeN alloy was prepared under the same conditions as in example 2 except for the alloy powder.

Example 6

Except that Sm is₂Fe₁₇Replacement of alloy powder by Ce₂Fe₁₇Except for the alloy powder, a CeFeN alloy was prepared under the same conditions as in example 2.

Example 7

Except that Sm is₂Fe₁₇Alloy powder changed into Nd₂Fe₁₇An NdFeN alloy was produced under the same conditions as in example 2 except for the alloy powder.

Example 8

Except that Sm is₂Fe₁₇Alloy powder replaced by NdFe₁₂An NdFeN alloy was produced under the same conditions as in example 2 except for the alloy powder.

Example 9

This example performs nitridation of a rare earth magnet as follows:

(1) taking Sm₂Fe₁₇Alloy powder with the powder granularity of 0.1 mu m-10 mm is put into a nitriding furnace, vacuumized until the pressure is reduced to 5Pa, a vacuumizing system is closed, and mixed gas of nitrogen and ammonia with the pressure of 0.01MPa is filled (the mixing molar ratio is 1: 1);

(2) heating to 400K, and keeping the temperature for 0.1 hour;

(3) after the heat preservation at the temperature of 400K is finished, heating to 700K, and preserving the heat for 0.1 hour;

(4) after the 700K heat preservation is finished, heating to 770K, and preserving heat for 0.1 hour;

(5)770K, after the heat preservation is finished, heating to 840K after 0.5 hour to obtain a semi-finished product;

(6)840K, cooling to 650K after heat preservation, pumping out gas in the nitriding furnace, vacuumizing until the pressure is reduced to 5Pa, introducing argon of 0.01MPa, and preserving heat for 0.5 hour;

(7) and cooling to room temperature after the 650K heat preservation is finished, taking the nitrided SmFeN alloy powder out, taking the materials at three different positions, and measuring the mass fraction of nitrogen element by using a nitrogen element content detection device, wherein the test results are shown in Table 1.

Example 10

This example performs nitridation of a rare earth magnet as follows:

(1) taking Sm₂Fe₁₇Alloy powder with the powder granularity of 0.1-10 mm is put into a nitriding furnace, vacuumized until the pressure is reduced to 5Pa, a vacuumizing system is closed, and 2MPa ammonia gas is filled;

(2) heating to 370K, and keeping the temperature for 5 hours;

(3) after the temperature preservation at 370K is finished, heating to 690K, and preserving the heat for 5 hours;

(4)690K, heating to 770K after the heat preservation is finished, and preserving the heat for 5 hours;

(5)770K, heating to 835K after 5 hours to obtain a semi-finished product;

(6)835K, cooling to 620K after heat preservation is finished, pumping out gas in the nitriding furnace, vacuumizing until the pressure is reduced to 5Pa, introducing 1MPa argon, and preserving heat for 5 hours;

(7) and cooling to room temperature after the heat preservation of 620K is finished, taking the nitrided SmFeN alloy powder out, taking the materials at three different positions, and measuring the mass fraction of nitrogen element by using a nitrogen element content detection device, wherein the test results are shown in Table 1.

Example 11

Except that Sm is added in the operation of step (1)₂Fe₁₇Alloy powder (the powder granularity is 0.1 mu m-10 mm) and ammonium bicarbonate with mass are mixed and placed in a nitriding furnace, the nitriding furnace is vacuumized until the pressure is reduced to 9Pa, a vacuumizing system is closed, 1.2MPa of argon is filled, and SmFeN alloy is prepared under the same conditions as those of the embodiment 2.

Comparative example 1

This comparative example differs from the process of example 2 only in that the operations of step (2) and step (3) are not carried out and the operation of step (3) is carried out by raising the temperature to 750K and holding it for 4 hours.

Comparative example 2

The present example differs from example 2 only in that the operation of step (5) is not carried out, but in step (6) the cooling is carried out directly from 750K to room temperature.

Comparative example 3

This comparative example differs from the method of example 2 only in that the operation of step (3) is not performed, but the operation of step (4) is changed to 420K, and after the completion of the temperature maintenance, the temperature is raised to 750K, and the temperature is maintained for 4 hours.

Test method

For each example and comparative example, the mass fraction of nitrogen element was measured by a nitrogen element content measuring device using three materials of different parts of the obtained nitrided rare earth magnet, and the test results are shown in table 1.

TABLE 1

Numbering	Nitrogen content/% (site 1)	Nitrogen content/% (site 2)	Nitrogen content/% (site 3)
				Example 1	3.61	3.68	3.65
Example 2	3.83	3.81	3.85
				Example 3	3.73	3.71	3.70
Example 4	3.21	3.18	3.25
				Example 5	3.36	3.40	3.43
Example 6	3.82	3.85	3.80
				Example 7	0.95	0.93	0.97
Example 8	0.92	0.95	0.93
				Example 9	3.08	3.02	3.05
Example 10	3.90	3.93	3.97
				Example 11	3.15	3.12	3.10
Comparative example 1	2.78	2.75	2.80
				Comparative example 2	2.58	2.70	2.82
Comparative example 3	2.91	2.95	2.97

It can be known from the above embodiments and comparative examples that the nitriding method of the rare earth magnet provided by the embodiments can improve the nitrogen content and make the nitrogen element distributed more uniformly in the magnet, thereby solving the problems of insufficient nitrogen content and non-uniform nitrogen element distribution after the nitriding of the rare earth magnet in the prior art.

The nitrogen content in the products of examples 7 and 8 was low because the types of rare earth elements used were different from those in example 1, and the nitrogen content was not comparable to that in example 1.

Comparative example 1 when preparing a semi-finished product, multi-stage heating was not performed, only one stage heating was performed, resulting in incomplete exhaust, insufficient adsorption of nitrogen elements, low nitrogen content after nitriding, and poor nitriding effect.

Comparative example 2, which was not subjected to the homogenization treatment (i.e., heating at the first set temperature), resulted in a large fluctuation in the nitrogen content, and was very uneven.

Comparative example 3 no two-stage heating was performed during the preparation of the semi-finished product, resulting in insufficient adsorption of nitrogen and a lower nitrogen content after nitriding.

The applicant states that the present invention is illustrated in detail by the above examples, but the present invention is not limited to the above detailed methods, i.e. it is not meant that the present invention must rely on the above detailed methods for its implementation. It should be understood by those skilled in the art that any modification of the present invention, equivalent substitutions of the raw materials of the product of the present invention, addition of auxiliary components, selection of specific modes, etc., are within the scope and disclosure of the present invention.