CN107275027A - Cerium-rich rare earth permanent magnet using yttrium and preparation method thereof - Google Patents

Cerium-rich rare earth permanent magnet using yttrium and preparation method thereof Download PDF

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CN107275027A
CN107275027A CN201710330274.0A CN201710330274A CN107275027A CN 107275027 A CN107275027 A CN 107275027A CN 201710330274 A CN201710330274 A CN 201710330274A CN 107275027 A CN107275027 A CN 107275027A
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permanent magnet
principal phase
cerium
earth permanent
yttrium
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CN107275027B (en
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严密
彭白星
金佳莹
马天宇
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Zhejiang University ZJU
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    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
    • H01F1/00—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties
    • H01F1/01—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials
    • H01F1/03—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity
    • H01F1/032—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of hard-magnetic materials
    • H01F1/04—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of hard-magnetic materials metals or alloys
    • H01F1/047—Alloys characterised by their composition
    • H01F1/053—Alloys characterised by their composition containing rare earth metals
    • H01F1/055—Alloys characterised by their composition containing rare earth metals and magnetic transition metals, e.g. SmCo5
    • H01F1/057—Alloys characterised by their composition containing rare earth metals and magnetic transition metals, e.g. SmCo5 and IIIa elements, e.g. Nd2Fe14B
    • H01F1/0571—Alloys characterised by their composition containing rare earth metals and magnetic transition metals, e.g. SmCo5 and IIIa elements, e.g. Nd2Fe14B in the form of particles, e.g. rapid quenched powders or ribbon flakes
    • H01F1/0573—Alloys characterised by their composition containing rare earth metals and magnetic transition metals, e.g. SmCo5 and IIIa elements, e.g. Nd2Fe14B in the form of particles, e.g. rapid quenched powders or ribbon flakes obtained by reduction or by hydrogen decrepitation or embrittlement
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
    • H01F1/00—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties
    • H01F1/01—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials
    • H01F1/03—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity
    • H01F1/032—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of hard-magnetic materials
    • H01F1/04—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of hard-magnetic materials metals or alloys
    • H01F1/047—Alloys characterised by their composition
    • H01F1/053—Alloys characterised by their composition containing rare earth metals
    • H01F1/055—Alloys characterised by their composition containing rare earth metals and magnetic transition metals, e.g. SmCo5
    • H01F1/057—Alloys characterised by their composition containing rare earth metals and magnetic transition metals, e.g. SmCo5 and IIIa elements, e.g. Nd2Fe14B
    • H01F1/0571—Alloys characterised by their composition containing rare earth metals and magnetic transition metals, e.g. SmCo5 and IIIa elements, e.g. Nd2Fe14B in the form of particles, e.g. rapid quenched powders or ribbon flakes
    • H01F1/0575—Alloys characterised by their composition containing rare earth metals and magnetic transition metals, e.g. SmCo5 and IIIa elements, e.g. Nd2Fe14B in the form of particles, e.g. rapid quenched powders or ribbon flakes pressed, sintered or bonded together
    • H01F1/0576—Alloys characterised by their composition containing rare earth metals and magnetic transition metals, e.g. SmCo5 and IIIa elements, e.g. Nd2Fe14B in the form of particles, e.g. rapid quenched powders or ribbon flakes pressed, sintered or bonded together pressed, e.g. hot working
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
    • H01F1/00—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties
    • H01F1/01—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials
    • H01F1/03—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity
    • H01F1/032—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of hard-magnetic materials
    • H01F1/04—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of hard-magnetic materials metals or alloys
    • H01F1/047—Alloys characterised by their composition
    • H01F1/053—Alloys characterised by their composition containing rare earth metals
    • H01F1/055—Alloys characterised by their composition containing rare earth metals and magnetic transition metals, e.g. SmCo5
    • H01F1/057—Alloys characterised by their composition containing rare earth metals and magnetic transition metals, e.g. SmCo5 and IIIa elements, e.g. Nd2Fe14B
    • H01F1/0571—Alloys characterised by their composition containing rare earth metals and magnetic transition metals, e.g. SmCo5 and IIIa elements, e.g. Nd2Fe14B in the form of particles, e.g. rapid quenched powders or ribbon flakes
    • H01F1/0575—Alloys characterised by their composition containing rare earth metals and magnetic transition metals, e.g. SmCo5 and IIIa elements, e.g. Nd2Fe14B in the form of particles, e.g. rapid quenched powders or ribbon flakes pressed, sintered or bonded together
    • H01F1/0577—Alloys characterised by their composition containing rare earth metals and magnetic transition metals, e.g. SmCo5 and IIIa elements, e.g. Nd2Fe14B in the form of particles, e.g. rapid quenched powders or ribbon flakes pressed, sintered or bonded together sintered
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
    • H01F41/00—Apparatus or processes specially adapted for manufacturing or assembling magnets, inductances or transformers; Apparatus or processes specially adapted for manufacturing materials characterised by their magnetic properties
    • H01F41/02—Apparatus or processes specially adapted for manufacturing or assembling magnets, inductances or transformers; Apparatus or processes specially adapted for manufacturing materials characterised by their magnetic properties for manufacturing cores, coils, or magnets
    • H01F41/0253—Apparatus or processes specially adapted for manufacturing or assembling magnets, inductances or transformers; Apparatus or processes specially adapted for manufacturing materials characterised by their magnetic properties for manufacturing cores, coils, or magnets for manufacturing permanent magnets
    • H01F41/0266—Moulding; Pressing

Abstract

The present invention discloses cerium-rich rare earth permanent magnet of application yttrium and preparation method thereof.Rare-earth permanent magnet prepared by the present invention contains the rich cerium principal phase of a kind of RE Fe B principal phases and one or more kinds of addition yttriums.Different principal phases is separately designed after composition, dispensing and powder processed, and corresponding main-phase alloy powder is proportionally uniformly mixed, and then through magnetic field die mould, sintering and heat treatment, prepares the rare-earth permanent magnet with many principal phase structures.By optimizing sintering and Technology for Heating Processing, further alleviate magnetic dilution effect, improve the comprehensive magnetic energy of magnet.The present invention realizes extensive application of the yttrium in rare-earth permanent magnet, and the performance of permanent magnet can reach the standard of commercialization, and the demand in market is also met while reducing the cost of raw material.

Description

Cerium-rich rare earth permanent magnet using yttrium and preparation method thereof
Technical field
The present invention relates to cerium-rich rare earth permanent magnet of application yttrium and preparation method thereof
Background technology
In recent years, due to receiving the extensive concern of domestic and international researcher, part Nd (neodymium) is replaced with Ce (cerium) element The rich Ce rare-earth permanent magnets prepared after element have been achieved for larger progress.Although Ce2Fe14B intrinsic magnetic properties can (saturation magnetic Polarization intensity JS=1.17T, the different field H of magnetocrystallineA=26kOe) compare Nd2Fe14B intrinsic magnetic properties can (saturated pole intensity JS =1.60T, the different field H of magnetocrystallineA=73kOe) want it is weak a lot, but researcher changes tradition by optimizing preparation technology Preparation method, Ce is weakened significantly and is added to the produced serious magnetic dilution effect after neodymium iron boron magnetic body.And be used as in addition A kind of reserves are very high, the relatively low rare earth element y of price (yttrium), but fail to be applied in the production of rare-earth permanent magnet always.So Y element is applied in the manufacture of permanent magnet, whether from reducing cost or balance for the angle that rare earth resources are utilized all There is highly important meaning.
Y2Fe14The different field H of magnetocrystalline of B compoundsAAt room temperature not only and Ce2Fe14B is close, but also has bigger Saturated pole intensity JS(1.41T) and higher Curie temperature TC(565K), it 2:14:1 compound is due in the absence of 3d electricity The coupling of son and 4f electronics, is related generally in basic research.And Ce2Fe14B Curie temperature (424K) is all RE2Fe14It is minimum in B compounds, so individually replacing the magnetic property ratio of the Sintered NdFeB magnet of part Nd elements with Ce Magnet before not replacing will deteriorate a lot, and be unfavorable for use of the magnet in complex environment.The present invention not only can be by Y members Element is widely applied into the manufacture of rare-earth permanent magnet, but also can keep or even improve the magnetic property of richness Ce magnets.In rare earth Price goes up all the way, and global Rare-earth Industry is faced under the present situation of cost control problem, two kinds of high abundance rare earths is used in conjunction with, energy Enough usage amounts for further reducing the rare earth elements such as price height, abundance low praseodymium, neodymium, terbium, dysprosium, effectively realize the control of cost of material System.The utilization of rare earth resources, the precious rare earth resources of protection China so can be also balanced simultaneously.
The content of the invention
The purpose of the present invention is to overcome the shortcomings of that yttrium can not be applied in rare-earth permanent magnet that there is provided application for a long time Cerium-rich rare earth permanent magnet of yttrium and preparation method thereof.
There are many principal phase structures using the cerium-rich rare earth permanent magnet of yttrium, including a kind of RE-Fe-B principal phases and a kind of or many Plant the rich cerium principal phase of addition yttrium.
The mass percent formula of RE-Fe-B principal phase compositions is REaFe100-a-b-cMbBc, one or more addition yttrium The mass percent formula of rich cerium principal phase composition is [(YxCe1-x)yRE1-y]aFe100-a-b-cMbBc, in formula RE be Nd, Pr, Dy, One or more in Tb, Gd, Er, Ho, M be Al, C, Co, Cr, Cu, F, Ga, Mn, Mo, N, Nb, Ni, P, Pb, S, Si, Ta, It is one or more of in Ti, V, Zr element；X, y, a, b, c meet following relation：0<X≤0.6,0.01≤y<1,28≤a≤33, 0.5≤b≤2,0.8≤c≤1.5.
Described RE-Fe-B principal phases account for the 10%~90% of principal phase gross mass, and the rich cerium principal phase of all addition yttriums accounts for principal phase The 10%~90% of gross mass；When including the rich cerium principal phase of two kinds or two or more addition yttriums in rare-earth permanent magnet, then respectively It is different to add the rich cerium principal phase composition of yttrium.
Preparation method using the cerium-rich rare earth permanent magnet of yttrium is specific as follows：
1) dispensing is carried out respectively according to the principal phase composition of design, be higher than 10 in vacuum-2In Pa vacuum medium frequency induction furnace Melting difference main-phase alloy, uses strip cast alloys technology to obtain different main-phase alloy rejection tablets of the thickness for 0.2~0.5mm, then By the corresponding main-phase alloy powder that hydrogen is quick-fried and air-flow grinding process preparation particle mean size is 3~4 μm；
2) corresponding main-phase alloy powder is proportionally uniformly mixed, obtains the mixing principal phase powder of different Y-Ce substitution amount End；
3) mixing principal phase powder is subjected to orientation die mould under 1.5~2T magnetic field, obtains green compact；
4) obtained green compact are subjected to 1~3min of isostatic cool pressing between Vacuum Package, 15~20MPa, are put into high vacuum malleation Sintering furnace, sinters between 1000~1080 DEG C and carries out carrying out between one-level tempering, 480~680 DEG C between 2.5~5h, 850~950 DEG C Second annealing, obtains rare-earth permanent magnet.
The present invention has the advantage that compared with prior art：1) present invention solves yttrium for a long time and can not answered The problem in rare-earth permanent magnet is used, extensive application of the yttrium in rare-earth permanent magnet is realized；2) by rich cerium principal phase The higher yttrium of abundance is added in alloy, keeps even improving the magnetic property of rich cerium principal phase, so that the magnetic of permanent magnet Performance reaches the standard of commercialization, can carry out widely production application；3) the cerium-rich rare earth permanent magnetism of application yttrium provided by the present invention The preparation method of body, selects suitable sintering process and process of thermal treatment according to the different qualities of each rare earth element, makes magnet Further growing up for main phase grain is prevented while full densification again, actual application demand is met；4) by addition The rich cerium principal phase composition of yttrium carries out the optimization design of alloying element, further suppresses magnetic dilution effect, in higher yttrium and cerium content When magnet can also keep good magnetic property；5) by applied cost relatively low rare earth element yttrium and cerium, it have effectively achieved original Expect the control of cost, while decreasing the usage amount of the rare earth elements such as praseodymium, neodymium, terbium, dysprosium, protect the rare earth money that China is precious Source.
Embodiment
There are many principal phase structures using the cerium-rich rare earth permanent magnet of yttrium, including a kind of RE-Fe-B principal phases and a kind of or many Plant the rich cerium principal phase of addition yttrium；
The mass percent formula of RE-Fe-B principal phase compositions is REaFe100-a-b-cMbBc, one or more addition yttrium The mass percent formula of rich cerium principal phase composition is [(YxCe1-x)yRE1-y]aFe100-a-b-cMbBc, in formula RE be Nd, Pr, Dy, One or more in Tb, Gd, Er, Ho, M be Al, C, Co, Cr, Cu, F, Ga, Mn, Mo, N, Nb, Ni, P, Pb, S, Si, Ta, It is one or more of in Ti, V, Zr element；X, y, a, b, c meet following relation：0<X≤0.6,0.01≤y<1,28≤a≤33, 0.5≤b≤2,0.8≤c≤1.5.
Described RE-Fe-B principal phases account for the 10%~90% of principal phase gross mass, and the rich cerium principal phase of all addition yttriums accounts for principal phase The 10%~90% of gross mass；When including the rich cerium principal phase of two kinds or two or more addition yttriums in rare-earth permanent magnet, then respectively It is different to add the rich cerium principal phase composition of yttrium.
Preparation method using the cerium-rich rare earth permanent magnet of yttrium is specific as follows：
1) dispensing is carried out respectively according to the principal phase composition of design, be higher than 10 in vacuum-2In Pa vacuum medium frequency induction furnace Melting difference main-phase alloy, uses strip cast alloys technology to obtain different main-phase alloy rejection tablets of the thickness for 0.2~0.5mm, then By the corresponding main-phase alloy powder that hydrogen is quick-fried and air-flow grinding process preparation particle mean size is 3~4 μm；
2) corresponding main-phase alloy powder is proportionally uniformly mixed, obtains the mixing principal phase powder of different Y-Ce substitution amount End；
3) mixing principal phase powder is subjected to orientation die mould under 1.5~2T magnetic field, obtains green compact；
4) obtained green compact are subjected to 1~3min of isostatic cool pressing between Vacuum Package, 15~20MPa, are put into high vacuum malleation Sintering furnace, sinters between 1000~1080 DEG C and carries out carrying out between one-level tempering, 480~680 DEG C between 2.5~5h, 850~950 DEG C Second annealing, obtains rare-earth permanent magnet.
With reference to specific embodiment, the present invention will be further described, but the present invention is not limited only to following implementation Example：
Embodiment 1：
1) it is calculated in mass percent, composition is [(Y0.2Ce0.8)0.5Nd0.5]30.5Fe67.11Co0.8Zr0.59B1Principal phase A and Nd30.5Fe67.11Co0.8Zr0.59B1Principal phase B difference dispensing, vacuum be higher than 10-2After Pa vacuum medium frequency induction furnace melting, Strip cast alloys technology is used to obtain corresponding principal phase rejection tablet of the thickness for 0.31mm；
2) corresponding principal phase rejection tablet is prepared into the respective alloy powder that particle mean size is 3.3 μm with air-flow grinding process by hydrogen is quick-fried End；
3) according to 3:7 mass ratio will mix principal phase powder under nitrogen protection by after A, B main-phase alloy powder uniformly mixing End oriented moulding under 2T magnetic field, and green compact are made through 17MPa isostatic cool pressings；
4) green compact are placed in vacuum sintering furnace and be sintered, sintering temperature is 1075 DEG C, sintering time 3h, at 890 DEG C Between carry out one-level tempering, carry out second annealing between 560 DEG C, obtain rare-earth permanent magnet.
5) magnet magnetic property is Br=13.2kGs, Hcj=11.8kOe, (BH)max=43.6MGOe.
Comparative example 1：
1) it is calculated in mass percent, composition is (Ce0.5Nd0.5)30.5Fe68.5B1Principal phase A and Nd30.5Fe68.5B1Principal phase B Dispensing, is higher than 10 in vacuum respectively-2After Pa vacuum medium frequency induction furnace melting, use strip cast alloys technology obtain thickness for 0.31mm corresponding principal phase rejection tablet；
2) corresponding principal phase rejection tablet is prepared into the respective alloy powder that particle mean size is 3.3 μm with air-flow grinding process by hydrogen is quick-fried End；
3) according to 3:7 mass ratio will mix principal phase powder under nitrogen protection by after A, B main-phase alloy powder uniformly mixing End oriented moulding under 2T magnetic field, and green compact are made through 17MPa isostatic cool pressings；
4) green compact are placed in vacuum sintering furnace and be sintered, sintering temperature is 1080 DEG C, sintering time 3h, at 890 DEG C Between carry out one-level tempering, carry out second annealing between 580 DEG C, obtain rare-earth permanent magnet.
5) magnet magnetic property is Br=12.8kGs, Hcj=11.4kOe, (BH)max=41.8MGOe；
Explanation：By the comparison of comparative example 1 and embodiment 1 it can be found that adding each of the rich cerium magnet of yttrium in embodiment 1 Item magnetic property index is all better than the magnet in comparative example, and further illustrating the present invention not only realizes yttrium in rare earth permanent magnet Application in body, and the magnetic property of rich cerium magnet can be improved.And the comprehensive magnetic of magnet can also reach the commercial trade mark Standard, reduce the cost of raw material, meet application demand.Meanwhile, found by contrasting, in (embodiment 1) of the invention The improvement optimization of the optimization design and Technology for Heating Processing of composition alloy element is all to ensure the reason for magnet performance is higher.
Embodiment 2：
1) it is calculated in mass percent, composition is [(Y0.25Ce0.75)0.6Nd0.4]30.2Fe67.45Co0.8Ga0.55B1Principal phase A, Composition is [(Y0.25Ce0.75)0.4Nd0.6]30.2Fe67.45Co0.8Ga0.55B1Principal phase B and composition be Nd30.2Fe67.45Co0.8Ga0.55B1Principal phase C difference dispensing, vacuum be higher than 10-2After Pa vacuum medium frequency induction furnace melting, Strip cast alloys technology is used to obtain corresponding principal phase rejection tablet of the thickness for 0.33mm；
2) corresponding principal phase rejection tablet is prepared into the respective alloy powder that particle mean size is 3.1 μm with air-flow grinding process by hydrogen is quick-fried End；
3) according to 2:2:1 mass ratio will be mixed under nitrogen protection by after A, B and C main-phase alloy powder uniformly mixing Principal phase powder oriented moulding under 2T magnetic field, and green compact are made through 17MPa isostatic cool pressings；
4) green compact are placed in vacuum sintering furnace and be sintered, sintering temperature is 1080 DEG C, sintering time 3h, at 890 DEG C Between carry out one-level tempering, carry out second annealing between 560 DEG C, obtain rare-earth permanent magnet；
5) magnet magnetic property is Br=12.7kGs, Hcj=8.8kOe, (BH)max=36.1MGOe.
Embodiment 3：
1) it is calculated in mass percent, composition is [(Y0.3Ce0.7)0.5Nd0.5]30.5Fe67.11Co1.39B1Principal phase A and Nd30.5Fe67.11Co1.39B1Principal phase B difference dispensing, vacuum be higher than 10-2After Pa vacuum medium frequency induction furnace melting, use Strip cast alloys technology obtains the corresponding principal phase rejection tablet that thickness is 0.31mm；
2) corresponding principal phase rejection tablet is prepared into the respective alloy powder that particle mean size is 3.3 μm with air-flow grinding process by hydrogen is quick-fried End；
3) according to 1:4 mass ratio will mix principal phase powder under nitrogen protection by after A, B main-phase alloy powder uniformly mixing End oriented moulding under 2T magnetic field, and green compact are made through 17MPa isostatic cool pressings；
4) green compact are placed in vacuum sintering furnace and be sintered, sintering temperature is 1075 DEG C, sintering time 3h, at 890 DEG C Between carry out one-level tempering, carry out second annealing between 580 DEG C, obtain rare-earth permanent magnet.
5) magnet magnetic property is Br=13.5kGs, Hcj=12.1kOe, (BH)max=45.1MGOe.

Claims (3)

1. the cerium-rich rare earth permanent magnet of application yttrium, it is characterised in that：The permanent magnet has many principal phase structures, including a kind of RE-Fe- The rich cerium principal phase of B principal phases and one or more kinds of addition yttriums；
The mass percent formula of RE-Fe-B principal phase compositions is REaFe100-a-b-cMbBc, the rich cerium of one or more addition yttrium The mass percent formula of principal phase composition is [(YxCe1-x)yRE1-y]aFe100-a-b-cMbBc, in formula RE be Nd, Pr, Dy, Tb, One or more in Gd, Er, Ho, M be Al, C, Co, Cr, Cu, F, Ga, Mn, Mo, N, Nb, Ni, P, Pb, S, Si, Ta, Ti, V, It is one or more of in Zr elements；X, y, a, b, c meet following relation：0<X≤0.6,0.01≤y<1,28≤a≤33,0.5≤b ≤ 2,0.8≤c≤1.5.
2. the cerium-rich rare earth permanent magnet of application yttrium according to claim 1, it is characterised in that：RE-Fe-B principal phases account for principal phase The 10%~90% of gross mass, the rich cerium principal phase of all addition yttriums accounts for the 10%~90% of principal phase gross mass；Work as rare-earth permanent magnet In comprising two kinds or two or more addition yttriums rich cerium principal phase when, then the rich cerium principal phase composition of each addition yttrium is different.
3. a kind of preparation method of the cerium-rich rare earth permanent magnet of application yttrium as claimed in claim 1 or 2, it is characterised in that：Institute State preparation method specific as follows：
1) dispensing is carried out respectively according to the principal phase composition of design, be higher than 10 in vacuum-2Melting in Pa vacuum medium frequency induction furnace Different main-phase alloys, use strip cast alloys technology to obtain different main-phase alloy rejection tablets of the thickness for 0.2~0.5mm, then pass through Hydrogen is quick-fried and air-flow grinding process prepares the corresponding main-phase alloy powder that particle mean size is 3~4 μm；
2) corresponding main-phase alloy powder is proportionally uniformly mixed, obtains the mixing principal phase powder of different Y-Ce substitution amount；
3) mixing principal phase powder is subjected to orientation die mould under 1.5~2T magnetic field, obtains green compact；
4) obtained green compact are subjected to 1~3min of isostatic cool pressing between Vacuum Package, 15~20MPa, are put into high vacuum malleation sintering Stove, sinters between 1000~1080 DEG C and carries out carrying out two grades between one-level tempering, 480~680 DEG C between 2.5~5h, 850~950 DEG C Tempering, obtains rare-earth permanent magnet.
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CN108022708A (en) * 2017-12-20 2018-05-11 包头金山磁材有限公司 A kind of rich cerium yttrium Nd-Fe-B permanent magnet for sintering argentiferous and preparation method thereof
CN108766703A (en) * 2018-06-08 2018-11-06 江西理工大学 A kind of more main phase high abundance rare earth permanent-magnetic materials of high temperature resistant and preparation method thereof
CN109585112A (en) * 2018-11-23 2019-04-05 钢铁研究总院 A kind of high-performance rare-earth permanent magnet material with improved crystal structure
CN110364325A (en) * 2018-04-09 2019-10-22 有研稀土新材料股份有限公司 A kind of rare earth permanent-magnetic material and preparation method thereof adding yttrium
CN111161949A (en) * 2019-12-31 2020-05-15 浙江大学 YCe co-doped nanocrystalline rare earth permanent magnet and preparation method thereof
CN112071544A (en) * 2020-08-20 2020-12-11 钢铁研究总院 Low-density Y-containing permanent magnet and preparation method thereof
CN113782292A (en) * 2021-06-04 2021-12-10 钢铁研究总院 Yttrium cerium-based rare earth permanent magnetic material with improved temperature stability

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CN105225781A (en) * 2015-10-27 2016-01-06 钢铁研究总院 A kind of high corrosion-resistant many Hard Magnetics principal phase Ce permanent magnet and preparation method thereof

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