Disclosure of Invention
The invention aims to overcome the defects of the prior art and provides a rare earth permanent magnet.
The invention also aims to provide a preparation method of the rare earth permanent magnet.
It is a further object of the present invention to provide the use of the above rare earth permanent magnet.
The technical scheme of the invention is as follows:
a rare earth permanent magnet comprises the following raw materials in percentage by mass:
R:28-34wt%:
Fe:60-71wt%;
B:0.84-1.15wt%;
M:0-5wt%;
wherein R is at least one of Pr, Nd, Dy, Tb, Ho, Pm, Sm, Eu, Gd, Er, Tm, Yb and Lu, M is at least one of Co, Al, Cu, Zn, In, Si, V, Cr, Mn, Ni, Ga, Ge, Zr, Nb, Mo, Pd, Ag, Cd, Sn, Sb, Ti, Hf, Ta, W, O, C, N, S and P, B is11The content of B isotope is at least 85 percent, wherein11The B isotope is mainly distributed in R of the rare earth permanent magnet material2Fe14B in the crystal lattice of the main phase grains.
In a preferred embodiment of the present invention, in B11The content of B isotope is at least 88%.
In a preferred embodiment of the invention, the density is from 7.50 to 7.90g/cm3。
The preparation method of the rare earth permanent magnet material comprises11The raw material of B isotope of B is added as initial raw material in the alloy smelting stage.
In a preferred embodiment of the invention, the method comprises alloy smelting, hydrogen crushing, airflow milling, oriented press forming, sintering, aging treatment and machining.
In the present invention, the raw material of the rare earth permanent magnet material is known to those skilled in the art as a raw material satisfying the element content percentage by mass of the R-Fe-B system permanent magnet material as described above.
In the present invention, the melting operation and conditions may be conventional in the art.
Preferably, the raw material is smelted in a high-frequency vacuum smelting furnace.
Preferably, the vacuum degree of the smelting furnace is less than 0.1Pa, and more preferably less than 0.02 Pa.
Preferably, the melting temperature is 1450-1550 ℃, more preferably 1500-1550 ℃.
In the invention, the casting operation and conditions can be conventional in the field and are generally carried out in an inert atmosphere to obtain the R-Fe-B permanent magnetic material alloy cast sheet.
The rare earth permanent magnet material is applied to the preparation of special permanent magnet motors operating under irradiation working conditions.
In the present invention, the operation and conditions for the hydrogen destruction may be conventional in the art. Generally, the hydrogen breaking comprises a hydrogen adsorption process and a dehydrogenation process, and the R-T-B series permanent magnet material alloy cast sheet can be subjected to hydrogen breaking treatment to obtain R-T-B series permanent magnet material alloy powder.
Preferably, the hydrogen absorption temperature of the hydrogen breaker is 20-300 ℃, for example, 25 ℃.
Preferably, the hydrogen absorption pressure of the hydrogen breaker is 0.12 to 0.19MPa, such as 0.19 MPa.
Preferably, the dehydrogenation time of the hydrogen destruction is 0.5 to 5 hours, for example, 2 hours.
Preferably, the dehydrogenation temperature of the hydrogen cracker is 450-600 ℃, for example 550 ℃.
In the present invention, the operation and conditions of the jet mill may be conventional in the art. Preferably, the air flow mill is used for sending the R-Fe-B series permanent magnet material alloy powder into an air flow mill for carrying out air flow mill continuous crushing to obtain R-Fe-B series permanent magnet material fine powder.
More preferably, the content of oxygen in the milling chamber of the jet mill in the jet mill is below 120 ppm.
More preferably, the rotation speed of the sorting wheel in the jet mill is 3500-4300 rpm/min, preferably 3900-4100 rpm/min, such as 4000 rpm/min.
More preferably, the grinding pressure of the jet mill is 0.3 to 0.5MPa, such as 0.4 MPa.
More preferably, the median diameter D50 of the R-Fe-B series permanent magnet material fine powder is 3 to 5.5pm, such as 4 μm.
In the present invention, the operation and conditions of the molding may be conventional in the art.
Preferably, the molding is performed under a magnetic field strength of 1.8T or more, for example, 1.8T, and under a nitrogen atmosphere.
In the present invention, the operation and conditions of the sintering may be conventional in the art.
Preferably, the sintering temperature is 900-1300 ℃, more preferably 1000-1100 ℃.
Preferably, the sintering time is 3-10 h, such as 8 h.
In the present invention, the operation and conditions of the primary or secondary aging may be conventional in the art.
Preferably, the primary ageing temperature is 880 ℃, 900 ℃ or 920 ℃.
Preferably, the secondary aging temperature is 450 ℃ to 560 ℃, more preferably 480 ℃ to 535 ℃, for example 485 ℃, 495 ℃, 505 ℃, 515 ℃ or 525 ℃.
Preferably, the time of the primary aging treatment is 2 to 5 hours, for example, 3 hours.
Preferably, the time of the secondary aging treatment is 2 to 5 hours, for example, 3 hours
On the basis of the common knowledge in the field, the above preferred conditions can be combined randomly to obtain the preferred embodiments of the invention.
The reagents and starting materials used in the present invention are commercially available, enriched with11The boron-containing raw material of the B isotope can be a simple substance of boron or an alloy containing boron.
In a preferred embodiment of the invention, the irradiation conditions include outer space and nuclear power plants.
The invention has the beneficial effects that: the invention has good heat resistance, wherein the element B is11The content of the B isotope is at least 85 wt%, so that the absorption of the neodymium iron boron magnet to neutron irradiation can be greatly reduced, the demagnetization phenomenon of the magnet in irradiation can be effectively avoided, and the use requirement of the special permanent magnet motor under the irradiation working condition can be met.
Detailed Description
The technical solution of the present invention is further illustrated and described by the following detailed description.
Examples 1 to 7
The raw materials used for preparing the Re-Fe-B series permanent magnet material in the embodiment are shown in Table 1, and the preparation process is as follows:
(1) according to the formula shown in Table 1, the prepared raw materials are put into a crucible made of alumina, and vacuum melting is carried out in a high-frequency vacuum induction melting furnace at the temperature of 1500 ℃ under the condition that the vacuum degree is less than 0.02 Pa.
(2) Alloy smelting and casting processes: introducing Ar gas into a smelting furnace after vacuum smelting to enable the air pressure to reach 5.0 ten thousand Pa, then casting, and enabling the molten liquid to pass through a copper roller with the rotating speed of 40 revolutions per minute to prepare a rapid hardening alloy sheet with the thickness of 0.12-0.35mm, wherein in the casting process, chilled water needs to be introduced into the copper roller, and the water inlet temperature is less than or equal to 25 ℃; the quenched alloy is obtained at a cooling rate of 102-104 ℃/sec.
(3) Hydrogen crushing to obtain powder: placing the alloy sheet in a hydrogen breaking furnace, vacuumizing the hydrogen breaking furnace at room temperature, introducing hydrogen with the purity of 99.9% into the hydrogen breaking furnace, and maintaining the hydrogen pressure at 90kPa to ensure that the alloy sheet fully absorbs hydrogen; then vacuumizing and heating to 550 ℃, fully dehydrogenating the alloy sheet, and finally cooling to obtain powder.
(4) Milling powder by airflow: and (4) carrying out jet milling on the powder obtained in the step (3) under the nitrogen atmosphere of 0.65MPa to obtain fine powder.
(5) Orientation compression molding: and (4) pressing and forming the fine powder prepared in the step (4) in a magnetic field intensity of 1.5-1.6T to obtain a formed body.
(6) And (3) sintering: transferring the molded body to a sintering furnace, sintering at 1000-1100 ℃ for 2-8h under the conditions of helium atmosphere and vacuum degree lower than 0.5Pa, and cooling to room temperature to obtain a sintered body;
(7) aging treatment: carrying out two-stage aging treatment on the sintered body obtained in the step (6) in high-purity argon, wherein the temperature of the first-stage aging treatment is 900 ℃; the temperature of the secondary ageing was 500 ℃. The treatment time of the first-stage aging is 3h, the treatment time of the second-stage aging is 3h, and the magnet is cooled to room temperature to obtain a finished product magnet. The finished magnet was tested for density using the drainage method and the results are shown in table 2 below.
(8) And (3) machining: and (4) machining the material obtained in the step (7) to obtain a test sample with the diameter of 10mm and the thickness of 10 mm.
(8) Detecting the magnetic property before irradiation: and magnetizing the test sample, and measuring the magnetic flux value of the sample by using a fluxmeter.
(10) Neutron irradiation: placing the magnetized magnet in a non-magnetic fixture, placing in a CFBR-II fast neutron pulse reactor for neutron irradiation, wherein the neutron fluence at the irradiation distance is 4 multiplied by 1014n/cm2And stopping irradiating for 2 hours, taking out the sample, standing the sample for 24 hours, measuring the magnetic flux value of the sample after irradiation by using a fluxmeter after the induced radioactive decay of the sample reaches a safe dose, and calculating the magnetic flux decay rate of the sample before and after irradiation, wherein the test results are listed in the following table 2.
The contents of the respective components in the magnet were measured using a high frequency inductively coupled plasma emission spectrometer (ICP-OES, Horiba), in which the isotopic content of boron was measured using a multi-reception plasma mass spectrometer (MC-ICP-MS) (Neptune plus), and the detection results of the components were as shown in table 3 below. The flux values were measured using a fluxgate and a helmholtz coil.
TABLE 1 weight percentages of raw materials in each example and comparative example
Number/wt%
|
Nd
|
Pr
|
Dy
|
10B
|
11B
|
Ti
|
Nb
|
Ga
|
Fe
|
11/B/(10B+11B)
|
Example 1
|
18.3
|
9.2
|
1.5
|
0.001
|
0.999
|
0.25
|
0
|
0.6
|
69.15
|
99.90%
|
Example 2
|
24.7
|
5
|
0.4
|
0.005
|
0.995
|
0
|
0.5
|
0.5
|
67.9
|
99.50%
|
Example 3
|
15
|
17
|
0
|
0.01
|
0.99
|
0.2
|
0.2
|
0.3
|
66.3
|
99.00%
|
Example 4
|
15
|
17
|
0
|
0.05
|
0.95
|
0.2
|
0.2
|
0.3
|
66.3
|
95.00%
|
Example 5
|
15
|
17
|
0
|
0.08
|
0.92
|
0.2
|
0.2
|
0.3
|
66.3
|
92.00%
|
Example 6
|
15
|
17
|
0
|
0.12
|
0.88
|
0.2
|
0.2
|
0.3
|
66.3
|
88.00%
|
Example 7
|
15
|
17
|
0
|
0.145
|
0.855
|
0.2
|
0.2
|
0.3
|
66.3
|
85.50%
|
Comparative example 1
|
15
|
17
|
0
|
0.2
|
0.8
|
0.2
|
0.2
|
0.3
|
66.3
|
80.00%
|
Comparative example 2
|
15
|
17
|
0
|
0.3
|
0.7
|
0.2
|
0.2
|
0.3
|
66.3
|
70.00%
|
Comparative example 3
|
15
|
17
|
0
|
0.5
|
0.5
|
0.2
|
0.2
|
0.3
|
66.3
|
50.00%
|
Comparative example 4
|
15
|
17
|
0
|
0.9
|
0.1
|
0.2
|
0.2
|
0.3
|
66.3
|
10.00% |
TABLE 2 magnetic flux and magnet loss rate of each of examples and comparative examples
TABLE 3 results of measurement of magnet component in examples and comparative examples
The above description is only a preferred embodiment of the present invention, and therefore should not be taken as limiting the scope of the invention, which is defined by the appended claims.