CN104505206A - Preparation method of high-coercivity sintered Nd-Fe-B and product - Google Patents

Preparation method of high-coercivity sintered Nd-Fe-B and product Download PDF

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CN104505206A
CN104505206A CN201410736135.4A CN201410736135A CN104505206A CN 104505206 A CN104505206 A CN 104505206A CN 201410736135 A CN201410736135 A CN 201410736135A CN 104505206 A CN104505206 A CN 104505206A
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phase alloy
alloy powder
coercive force
sintered ndfeb
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CN104505206B (en
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严密
张玉晶
王新华
金佳莹
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Zhejiang University ZJU
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Abstract

The invention discloses a preparation method of high-coercivity sintered Nd-Fe-B. The preparation method comprises the following steps: preparing a main phase alloy powder and a grain boundary phase alloy powder; protecting the prepared main phase alloy powder and the grain boundary phase alloy powder by using nitrogen or argon in a protective medium, and uniformly mixing, wherein the mass percent of the added grain boundary phase alloy powder accounts for 0.1-10 percent; carrying out orientation profiling and cold isostatic pressing on the mixed alloy powder; in a vacuum sintering furnace, sintering a profiled magnet block for 2-4h at the temperature of 1000-1100 DEG C, then carrying out primary tempering for 2-4h at the temperature of 800-950 DEG C, and carrying out secondary tempering for 2-4h at the temperature of 450-650 DEG C to prepare the sintered Nd-Fe-B. The invention also discloses the high-coercivity sintered Nd-Fe-B. According to the preparation method disclosed by the invention, by virtue of low melting point auxiliary alloy, the wetting temperature between a grain boundary phase and a main phase is lowered, the wetting time is prolonged, the utilization ratio of heavy rare earth is increased, the used amount of rare earth is lowered, the process is simple, the cost is low, and the high-coercivity sintered Nd-Fe-B is suitable for mass production.

Description

A kind of preparation method of high-coercive force sintered NdFeB and product
Technical field
The invention belongs to permanent magnetic material technical field, be specifically related to a kind of preparation method and product of high-coercive force sintered NdFeB.
Background technology
Nineteen eighty-three Japan the people such as the true benevolence in assistant river on the basis of RE-Fe-X ternary alloy three-partalloy being carried out to extensively research, adopt powder metallurgical technique to prepare magnetic energy product up to 290kJ/m 3neodymium iron boron (Nd-Fe-B) sintered magnet, started third generation rare earth permanent-magnetic material.Sintered Nd-Fe-B is widely used in military industry equipment, electro-acoustic element, motor, generator, computer hard disc driver (HDD), voice coil motor (VCM), human body NMR imaging instrument (MRI), short-wave communication tedhnology, controller, instrument, magnetic separating apparatus, magnetic card dish and other devices that need use permanent-magnetic field and equipment.
Sintered NdFeB magnet is with Nd 2fe 14b compound is principal phase, is coated with the structure of Nd-rich phase around.Its main technical indicator comprises remanent magnetism B r, maximum magnetic energy product (BH) max, coercive force H cj, Curie temperature T c.Through 20 years of researches development, have devised rational alloying component and ripe preparation technology, make the remanent magnetism B of magnet rreach more than 96% of theoretical value, the most high energy of magnetic energy product reaches 474kJ/m 3, close to theoretical magnetic energy product 512kJ/m 393%.Although coercive force obtains the lifting of certain depth, for its theoretical value 5600kA/m, still have very large gap, the chances are for the level that can reach at present in 1/10 ~ 1/3 of its coercive force theoretical value.So just greatly limit neodymium iron boron magnetic body to apply under high working temperature environment.In order to address this problem, scientific worker has been engaged in large quantifier elimination, mainly comprises heavy rare earth alloy, like this can the coercive force of raising magnet easily and effectively, but, because heavy rare earth atom is coupled with the antiferromagnetism of iron atom, the indexs such as the remanent magnetism of magnet and maximum magnetic energy product can reduce greatly, in addition, traditional DIRECT ALLOYING, need more heavy rare earth, generally speaking need to add mass fraction 2 ~ 10% heavy rare earth, also can improve the production cost of magnet.More domestic and international enterprises and R&D institution, have employed the method for magnet surface diffusion at present, can have and improve on coercitive basis in effect, reduces heavy rare earth consumption.But this method, complex technical process, is not suitable for actual production, and heavy rare earth diffusion length limited (<5 μm), so just makes the magnet size for spreading too little, is not suitable for actual application market.
Summary of the invention
The invention provides a kind of reduction heavy rare earth consumption, improve the coercitive method of Sintered NdFeB magnet.
Present invention also offers a kind of Sintered NdFeB magnet prepared by said method, coercive force is higher.
A preparation method for high-coercive force sintered NdFeB, comprising:
(1) principal phase Nd Fe B alloys adopts casting technique or rapid hardening belt-rejecting technology to make ingot casting or rapid casting, principal phase ingot casting or rapid casting fragmentation are made the master alloying particle powder that average particulate diameter is 2-10 μm by method with airflow milling quick-fried by hydrogen again, described master alloying is with atomic percentage, and its composition is (Nd apr 1-a) bfe 100-b-c-db cm d;
Wherein: Nd is neodymium element, Pr is praseodymium element, Fe is ferro element, B is boron element, and M is one or more in Dy (dysprosium), Tb (terbium), Ce (cerium), Co (cobalt), Ni (nickel), V (vanadium), Ti (thallium), Mo (molybdenum), Mn (manganese), Ga (gallium), Al (aluminium), Cu (copper), Zr (zirconium), Ta (tantalum), Ag (silver), Si (silicon), Nb (niobium) element; A, b, c, d meet following relation: 0.7≤a≤1,10≤b≤20,5.5≤c≤6.5,0≤d≤2.
Wherein, the M more preferably combination of Dy, Al and Nb or the combination of Al, Co, Cu, Zr and Ga.Principal phase Nd Fe B alloys is further preferably: (Pr, Nd) 13.62fe balm 1.58b 5.98, wherein M=Al, Co, Cu, Zr, Ga; Or (Pr, Nd) 13.05dy 0.12fe balal 0.25nb 0.07b 5.7;
Wherein, as preferably, a, b, c, d meet following relation: a=0.8,13.05≤b≤13.62,5.7≤c≤5.98,0.44≤d≤1.58;
The average particulate diameter more preferably 2-5 μm of described master alloying particle powder, is further preferably 3-4 μm;
(2) the rich heavy rare earth alloy end of Grain-Boundary Phase adopts melting; band is got rid of in rapid hardening, Mechanical Crushing, and it is 0.1 ~ 2 μm of crystal-boundary phase alloy powder that protective medium ball milling or direct atomization are prepared into average particulate diameter; described crystal-boundary phase alloy is with atomic percentage, and its composition is (R xr ' 1-x) ym ' 100-y;
Wherein: R is one or more in La (lanthanum), Ce, Pr, Nd, R ' is one or more in Tb, Dy, Ho (holmium), M ' is Fe, Cr (chromium), Co, Ni, V, Ti, Mo, Mn, Ga, Al, Cu, Zr, Ta, Ag, Si, Ca, B, Mg, Zn, In (indium), one or more in Sn element; Wherein x, y meet following relation: 0≤x<1,0<y<100;
Wherein said R is preferably Pr; Described R ' is preferably Dy; Described M ' be preferably in Fe, Cu, Co one or more; Described x, y meet following relation further: 0≤x<0.6,20<y<70; Described crystal-boundary phase alloy is preferably Pr 37dy 30cu 33, Dy 32.5fe 62cu 5.5, Dy 6co 13cu 5;
In step (1) and step (2), preferred principal phase Nd Fe B alloys, crystal-boundary phase alloy are combined as further:
(Pr 0.2nd 0.8) 13.62fe 78.82m 1.58b 5.98with Pr 37dy 30cu 33combination;
Or (Pr 0.2nd 0.8) 13.05dy 0.12fe 80.81al 0.25nb 0.07b 5.7with Dy 32.5fe 62cu 5.5combination;
Or (Pr 0.2nd 0.8) 13.62fe balm 1.58b 5.98with Dy 6co 13cu 5combination.
Particularly adopt (Pr 0.2nd 0.8) 13.62fe balm 1.58b 5.98with Dy 6co 13cu 5combination time, the coercive force of the Sintered NdFeB magnet obtained is up to 1629.0kA/m;
The average particulate diameter of described crystal-boundary phase alloy is preferably 0.1 ~ 1.5 μm, is further preferably 0.8 ~ 1.5 μm;
(3) crystal-boundary phase alloy powder and principal phase Nd Fe B alloys powder will be prepared with mass fraction for 0.1 ~ 10%, in gasoline, benzinum or other organic protective mediums, fully mix with the batch mixer of nitrogen or argon shield;
In this step, the mass percent that crystal-boundary phase alloy powder adds is preferably 1 ~ 5%, and more preferably 2 ~ 3%;
(4) alloy powder mixed is carried out orientation die mould under the magnetic field of 1.2 ~ 3.0T; The magnetic patch completed by die mould carries out the isostatic cool pressing of 100 ~ 220MPa, makes its die mould become green compact;
The preferred of described whereabouts die mould carries out under 1.8T condition; Described isostatic cool pressing is carried out under 200MPa;
(5) in vacuum sintering furnace, the magnetic patch completed by die mould at 1000 ~ 1100 DEG C of sintering 2 ~ 4h, then through 800 ~ 950 DEG C of one-level tempering 2 ~ 4h and 450 ~ 650 DEG C second annealing 2 ~ 4h, obtains final magnet;
In this step, preferred sintering condition is further: 1050 ~ 1090 DEG C of sintering 3 ~ 4h, then through 890 ~ 900 DEG C of one-level tempering 2 ~ 3h and 500 ~ 520 DEG C second annealing 2 ~ 4h.Preferred sintering condition is further: 1050 ~ 1085 DEG C of sintering 3 ~ 4h, then through 890 ~ 900 DEG C of one-level tempering 2h and 500 ~ 520 DEG C second annealing 3 ~ 4h, the coercive force of the Sintered NdFeB magnet adopting this sintering condition process to obtain is greater than 1400kA/m; Especially at 1050 DEG C of sintering 3h, then after 890 DEG C of one-level tempering 2h and 520 DEG C of second annealing 3h process, coercive force is greater than 1600kA/m.
Coercive force, as a structure sensitive magnetics parameter, be it is generally acknowledged, tiny and the uniform coated one deck of principal phase particle surface 2 ~ 5nm is thick, evenly and continuous print Nd-rich phase, is the desirable heterogeneous microstructure of high-coercive force Sintered NdFeB magnet.The present invention adds low melting point heavy rare earth alloy at crystal boundary, optimizes grain boundary structure further, eliminates grain boundary defects, and in sintering and tempering heat treatment process, heavy rare earth, to the diffusion of main phase grain boundary layer, realizes border magnetic hardening; Add the rich heavy rare earth crystal-boundary phase alloy of low melting point by crystal boundary, reduce the wetting temperature between principal phase and Grain-Boundary Phase, extend wetting time, correspondingly can reduce sintering and heat treatment temperature, suppress the abnormal growth of solid-phase sintering and crystal grain.Thus under realizing not adding or add on a small quantity the condition of heavy rare earth in main-phase alloy, reduce heavy rare earth consumption, preparation low cost high-coercive force Sintered NdFeB magnet.
Present invention also offers a kind of high-coercive force sintered NdFeB, this sintered NdFeB is prepared by the preparation method of the high-coercive force sintered NdFeB described in above-mentioned arbitrary technical scheme.
The present invention utilizes the rich heavy rare earth crystal-boundary phase alloy of low melting point in the sintering and heat treatment process of magnet, reduces the wetting temperature between Grain-Boundary Phase and principal phase, extends wetting time, improve heavy rare earth utilance by the auxiliary alloy of low melting point; By low melting point Grain-Boundary Phase, improve crystal boundary mobility, reduce sintering and heat treatment temperature, optimize grain boundary structure, reduce grain boundary defects, suppress magnetic reversal forming core; By heavy rare earth to the diffusion of principal phase boundary layer, realize the magnetic hardening on main phase grain border.Do not contain initial or contain in the master alloying of a small amount of heavy rare earth, only crystal boundary adds the rich heavy rare earth alloy of a small amount of low melting point, keeps remanent magnetism, increases substantially coercive force, realize an efficiency utilization of heavy rare earth.Method provided by the invention, technique is simple, and cost is lower, is applicable to large-scale production.
The present invention compared with prior art, the beneficial effect had:
1) the present invention designs the rich heavy rare earth Grain-Boundary Phase of low melting point, optimizes the wet processes of liquid sintering process, extends wetting time, improve heavy rare earth toward the diffuser efficiency in principal phase boundary layer, realize the efficiency utilization of grain boundary magnetic hardening and heavy rare earth.
2) improve grain boundary structure, eliminate grain boundary defects, reduce sintering and heat treatment temperature, suppress the abnormal growth of crystal grain, improve coercive force.
3) preparation technology provided by the invention is simple, and heavy rare earth consumption is lower, and coercive force is higher, the real preparation achieving low cost high-coercive force sintered NdFeB.
Embodiment
A preparation method for high-coercive force low cost sintered NdFeB, the principal phase Nd Fe B alloys described in it is with atomic percentage, and its composition is (Nd apr 1-a) bfe 100-b-c-db cm d, wherein Nd is neodymium element, and Pr is praseodymium element, and Fe is ferro element, and B is boron element, and M is one or more in Dy, Tb, Ce, Co, Ni, V, Ti, Mo, Mn, Ga, Al, Cu, Zr, Ta, Ag, Si, Nb element; A, b, c, d meet following relation: 0.7≤a≤1,10≤b≤20,5.5≤c≤6.5,0≤d≤2.
Crystal-boundary phase alloy is with atomic percentage, and its composition is (R xr ' 1-x) ym ' 100-yr is one or more in La, Ce, Pr, Nd, R ' is one or more in Tb, Dy, Ho, and M ' is one or more in Fe, Cr, Co, Ni, V, Ti, Mo, Mn, Ga, Al, Cu, Zr, Ta, Ag, Si, Ca, B, Mg, Zn, In, Sn element; Wherein x, y meet following relation: 0≤x<1,0<y<100.
A preparation method for high-coercive force low cost sintered NdFeB, the rich heavy rare earth alloy of described crystal boundary, its fusing point is between 300 ~ 900 DEG C, and after making powder particle, its size is between 0.1 ~ 1 μm.
A kind of high-coercive force low-cost sintered neodymium iron boron preparation method, the rich heavy rare earth crystal-boundary phase alloy of low melting point, in sintering and tempering heat treatment process, heavy rare earth, to the diffusion of main phase grain boundary layer, realizes border magnetic hardening; Utilize low melting point crystal-boundary phase alloy, extend wetting time, improve Grain-Boundary Phase mobility, optimize grain boundary structure, reduce grain boundary defects; Add the rich heavy rare earth crystal-boundary phase alloy of low melting point by crystal boundary, reduce sintering and heat treatment temperature, suppress the abnormal growth of solid-phase sintering and crystal grain.Do not add or add on a small quantity the condition of heavy rare earth in main-phase alloy under, crystal boundary adds, and reduces heavy rare earth consumption, preparation low cost high-coercive force Sintered NdFeB magnet.
A preparation method for high-coercive force low cost sintered NdFeB, its step is:
1) principal phase Nd Fe B alloys adopts casting technique or rapid hardening belt-rejecting technology to make ingot casting or rapid casting, principal phase ingot casting or rapid casting fragmentation are made the particle powder that average particulate diameter is 2 ~ 10 μm by method with airflow milling quick-fried by hydrogen again, described master alloying is with atomic percentage, and its composition is (Nd apr 1-a) bfe 100-b-c-db cm d;
2) the rich heavy rare earth alloy end of Grain-Boundary Phase adopts melting, and band is got rid of in rapid hardening, Mechanical Crushing, and it is 0.1 ~ 1 μm of powder that protective medium ball milling or direct atomization are prepared into average particulate diameter, and described crystal-boundary phase alloy is with atomic percentage, and its composition is (R xr ' 1-x) ym ' 100-y;
3) crystal-boundary phase alloy powder and master alloying powder will be prepared with mass fraction for 0.1 ~ 10%, in gasoline, benzinum or other organic protective mediums, fully mix with the batch mixer of nitrogen or argon shield;
4) alloy powder mixed is carried out orientation die mould under the magnetic field of 1.2 ~ 3.0T; The magnetic patch completed by die mould carries out the isostatic cool pressing of 100 ~ 220MPa, makes its die mould become green compact;
5) in vacuum sintering furnace, the magnetic patch completed by die mould at 1000 ~ 1100 DEG C of sintering 2 ~ 4h, then through 800 ~ 950 DEG C of one-level tempering 2 ~ 4h and 450 ~ 650 DEG C second annealing 2 ~ 4h, obtains final magnet.The present invention compared with prior art, the beneficial effect had: 1) the present invention designs the rich heavy rare earth Grain-Boundary Phase of low melting point, optimize the wet processes of liquid sintering process, extend wetting time, improve heavy rare earth toward the diffuser efficiency in principal phase boundary layer, realize the efficiency utilization of grain boundary magnetic hardening and heavy rare earth.2) improve grain boundary structure, eliminate grain boundary defects, reduce sintering and heat treatment temperature, suppress the abnormal growth of crystal grain, improve coercive force.3) preparation technology provided by the invention is simple, and heavy rare earth consumption is lower, and coercive force is height, the real preparation achieving low cost high-coercive force sintered NdFeB.
Below in conjunction with instantiation, the present invention will be further described, but the present invention is not only confined to following instance.
Embodiment 1:
1) main-phase alloy adopted rapid hardening slab, hydrogen three kinds of alloy techniques that are quick-fried and airflow milling to prepare master alloying powder, particle diameters is roughly at about 3.5 μm, and described master alloying is in atomic percentage, and its composition is (Pr 0.2nd 0.8) 13.62fe 78.82m 1.58b 5.98, wherein Pr:Nd=1:4, M are Al=0.72, Co=0.49, Cu=0.14, Zr=0.14, Ga=0.09;
2) crystal-boundary phase alloy is by electric arc melting, and Mechanical Crushing, protective medium is milled to average grain size and is about 0.85 μm, and auxiliary alloy is in atomic percentage, and its composition is Pr 37dy 30cu 33;
3) will prepare crystal-boundary phase alloy powder and master alloying powder in gasoline, benzinum or other organic protective mediums, fully mix with the batch mixer of nitrogen or argon shield, wherein mass fraction shared by auxiliary alloy powder is 2.0%;
4) alloy powder mixed is carried out orientation die mould under the magnetic field of 1.8T; The magnetic patch completed by die mould carries out the isostatic cool pressing of 200MPa, makes its die mould become green compact;
5) in vacuum sintering furnace, the magnetic patch completed by die mould at 1085 DEG C of sintering 4h, then through 900 DEG C of one-level tempering 2h and 500 DEG C second annealing 4h, obtains final magnet.
The Sintered NdFeB magnet prepared is put into VSM and measures its magnetic property, result is as follows: B r=1.35T, H cj=1450.2kA/m, (BH) max=351.75kJ/m 3.
Embodiment 2:
1) main-phase alloy adopted rapid hardening slab, hydrogen three kinds of alloy techniques that are quick-fried and airflow milling to prepare master alloying powder, particle diameters is roughly at about 3.5 μm, and described master alloying is in atomic percentage, and its composition is (Pr 0.2nd 0.8) 13.05dy 0.12fe 80.81al 0.25nb 0.07b 5.7
2) crystal-boundary phase alloy is by electric arc melting, and Mechanical Crushing, protective medium is milled to average grain size and is about 1.5 μm, and auxiliary alloy is calculated in mass percent, and its composition is Dy 32.5fe 62cu 5.5.
3) will prepare crystal-boundary phase alloy powder and master alloying powder in gasoline, benzinum or other organic protective mediums, fully mix with the batch mixer of nitrogen or argon shield, wherein mass fraction shared by auxiliary alloy powder is 3.0%:
4) alloy powder mixed is carried out orientation die mould under the magnetic field of 1.8T; The magnetic patch completed by die mould carries out the isostatic cool pressing of 200MPa, makes its die mould become green compact;
5) in vacuum sintering furnace, the magnetic patch completed by die mould at 1090 DEG C of sintering 4h, then through 890 DEG C of one-level tempering 2h and 520 DEG C second annealing 3.5h, obtains final magnet.
The Sintered NdFeB magnet prepared is put into VSM and measures its magnetic property, result is as follows: B r=1.35T, H cj=1329.0kA/m, (BH) max=369.71kJ/m 3.
Embodiment 3:
1) main-phase alloy adopted rapid hardening slab, hydrogen three kinds of alloy techniques that are quick-fried and airflow milling to prepare master alloying powder, particle diameters is roughly at about 3.5 μm, and described master alloying is in atomic percentage, and its composition is (Pr 0.2nd 0.8) 13.62fe balm 1.58b 5.98, wherein M is Al=0.72, Co=0.49, Cu=0.14, Zr=0.14, Ga=0.09;
2) crystal-boundary phase alloy is by electric arc melting, and Mechanical Crushing, protective medium is milled to average grain size and is about 1.3 μm. and described auxiliary alloy is in atomic percentage, and its composition is Dy 6co 13cu 5.
3) will prepare crystal-boundary phase alloy powder and master alloying powder in gasoline, benzinum or other organic protective mediums, fully mix with the batch mixer of nitrogen or argon shield, wherein mass fraction shared by auxiliary alloy powder is 3.0%:
4) alloy powder mixed is carried out orientation die mould under the magnetic field of 1.8T; The magnetic patch completed by die mould carries out the isostatic cool pressing of 200MPa, makes its die mould become green compact;
5) in vacuum sintering furnace, the magnetic patch completed by die mould at 1050 DEG C of sintering 3h, then through 890 DEG C of one-level tempering 2h and 520 DEG C second annealing 3h, obtains final magnet.
The Sintered NdFeB magnet prepared is put into VSM and measures its magnetic property, result is as follows: B r=1.38T, H cj=1629.0kA/m, (BH) max=398.63kJ/m 3.

Claims (10)

1. a preparation method for high-coercive force sintered NdFeB, is characterized in that, comprising:
(1) utilize main-phase alloy to prepare the main-phase alloy powder that average particulate diameter is 2-10 μm, described master alloying is with atomic percentage, and its composition is (Nd apr 1-a) bfe 100-b-c-db cm d;
Wherein: M is one or more in Dy, Tb, Ce, Co, Ni, V, Ti, Mo, Mn, Ga, Al, Cu, Zr, Ta, Ag, Si, Nb element; A, b, c, d meet following relation: 0.7≤a≤1,10≤b≤20,5.5≤c≤6.5,0≤d≤2;
(2) utilizing crystal-boundary phase alloy to prepare average particulate diameter is 0.1 ~ 2 μm of crystal-boundary phase alloy powder, and described crystal-boundary phase alloy is with atomic percentage, and its composition is (R xr ' 1-x) ym ' 100-y;
Wherein: R is one or more in La, Ce, Pr, Nd element, R ' is one or more in Tb, Dy, Ho element, and M ' is one or more in Fe, Cr, Co, Ni, V, Ti, Mo, Mn, Ga, Al, Cu, Zr, Ta, Ag, Si, Ca, B, Mg, Zn, In, Sn element; Wherein x, y meet following relation: 0≤x<1,0<y<100;
(3) crystal-boundary phase alloy powder and main-phase alloy powder will be prepared in protective medium, mix with nitrogen or argon shield; The mass percent that crystal-boundary phase alloy powder adds is 0.1 ~ 10%;
(4) alloy powder mixed is carried out orientation die mould under the magnetic field of 1.2 ~ 3.0T; The magnetic patch completed by die mould carries out the isostatic cool pressing of 100 ~ 220MPa, makes its die mould become green compact;
(5) in vacuum sintering furnace, the magnetic patch completed by die mould at 1000 ~ 1100 DEG C of sintering 2 ~ 4h, then through 800 ~ 950 DEG C of one-level tempering 2 ~ 4h and 450 ~ 650 DEG C second annealing 2 ~ 4h, obtains final Sintered NdFeB magnet.
2. the preparation method of high-coercive force sintered NdFeB according to claim 1, is characterized in that, described M is the combination of Dy, Al and Nb or the combination of Al, Co, Cu, Zr and Ga.
3. the preparation method of high-coercive force sintered NdFeB according to claim 1, is characterized in that, the average particulate diameter of described master alloying particle powder is 2-5 μm.
4. the preparation method of high-coercive force sintered NdFeB according to claim 1, is characterized in that, described R is Pr; Described R ' is Dy; Described M ' is one or more in Fe, Cu, Co; Described x, y meet following relation further: 0≤x<0.6,20<y<70.
5. the preparation method of high-coercive force sintered NdFeB according to claim 1, is characterized in that, in step (1) and step (2), described main-phase alloy, crystal-boundary phase alloy are combined as:
(Pr 0.2nd 0.8) 13.62fe 78.82m 1.58b 5.98with Pr 37dy 30cu 33combination;
Or (Pr 0.2nd 0.8) 13.05dy 0.12fe 80.81al 0.25nb 0.07b 5.7with Dy 32.5fe 62cu 5.5combination;
Or (Pr 0.2nd 0.8) 13.62fe balm 1.58b 5.98with Dy 6co 13cu 5combination.
6. the preparation method of high-coercive force sintered NdFeB according to claim 1, is characterized in that, the average particulate diameter of described crystal-boundary phase alloy powder is 0.1 ~ 1.5 μm.
7. the preparation method of high-coercive force sintered NdFeB according to claim 1, is characterized in that, the mass percent that described crystal-boundary phase alloy powder adds is 1 ~ 5%.
8. the preparation method of high-coercive force sintered NdFeB according to claim 1, is characterized in that, the preferred of described whereabouts die mould carries out under 1.8T condition; Described isostatic cool pressing is carried out under 200MPa.
9. the preparation method of high-coercive force sintered NdFeB according to claim 1, it is characterized in that, sintering condition in step (5) is: 1050 ~ 1090 DEG C of sintering 3 ~ 4h, then through 890 ~ 900 DEG C of one-level tempering 2 ~ 3h and 500 ~ 520 DEG C second annealing 2 ~ 4h.
10. a high-coercive force sintered NdFeB, is characterized in that, described sintered NdFeB adopts the preparation method described in the arbitrary claim of claim 1-9 to prepare.
CN201410736135.4A 2014-12-04 2014-12-04 A kind of preparation method and product of high-coercive force sintered NdFeB Expired - Fee Related CN104505206B (en)

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CN105405555A (en) * 2015-11-20 2016-03-16 湖南航天磁电有限责任公司 Cerium-holmium contained sintered neodymium iron boron permanent magnet material
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CN106601464A (en) * 2016-12-14 2017-04-26 安徽大地熊新材料股份有限公司 Preparation method for permanent magnet material with low content of heavy rare earth and high coercivity
CN106782971A (en) * 2016-12-05 2017-05-31 湖南航天磁电有限责任公司 A kind of NdFeB material and preparation method thereof
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