CN101320611A

CN101320611A - Soft magnetic phase intensified biphase composite heat distortion magnet and preparation method thereof

Info

Publication number: CN101320611A
Application number: CNA200810060509XA
Authority: CN
Inventors: 潘晶; 刘新才
Original assignee: Ningbo University
Current assignee: Ningbo University
Priority date: 2008-04-03
Filing date: 2008-04-03
Publication date: 2008-12-10
Anticipated expiration: 2028-04-03
Also published as: CN101320611B

Abstract

The invention discloses a dual-phase composite hot-deformed magnet which reinforces soft magnetic phase and a preparation method thereof, and belongs to the technology field of the permanent magnetic material and the rare-earth permanent magnetic material and the preparation thereof, the pulverizing technology and the hot deformation. Aims at the prior art, only when the Alpha-Fe content of the magnet is very low such as 2 to 4 volume percent, the R2Fe14B grain in the composite structure can be hot-pressed to fully deform and the easy magnetization axis C-axis of the magnet to form the texture along the upward pressing direction, the invention discloses a dual-phase composite hot-deformed magnet which reinforces soft magnetic phase and a preparation method thereof, adopts the reinforcement of the soft magnetic phase to enable the strength of the soft magnetic phase at the deformation temperature to exceed the high-temperature strength of the hard magnetic phase R2T14M, thereby ensuring the hot deformation to have priority to occur in the hard magnetic phase, forming the identical easy magnetization axis direction and promoting the cost performance of the dual-phase composite magnet.

Description

Strengthen biphase composite heat distortion magnet of soft magnetism phase and preparation method thereof

Technical field

Strengthen biphase composite heat distortion magnet of soft magnetism phase and preparation method thereof, relate to permanent magnetic material and rare earth permanent-magnetic material and technology of preparing thereof, powder process, thermal deformation technical field.

Background technology

Because the theoretical magnetic energy product of anisotropy nano composite permanent magnetic material is up to 127MGOe, far above the theoretical value 64MGOe of existing powder sintered Nd-Fe-B magnet, and its content of rare earth is lower, so have the potentiality that become high performance permanent magnetic materials of new generation.Preparing bulk, fully dense anisotropy nanocomposite permanent magnets by hot compression deformation is the target that the magnetic material worker pursues.

2003, people such as the breadboard D.Lee of U.S.'s Dayton university magnetics were that raw material is prepared anisotropy (Nd, Pr first by hot-forming/hot compression deformation technology with the fast quenching magnetic, Dy) 2Fe14B/ α-Fe biphase composite permanent magnetic body, data sees reference: D.Lee, J.S.Hilton, S.Liu, Y.Zhang, G.C.Hadjipanayis, and C.H.Chen, Hot-Pressedand Hot-Deformed Nanocomposite (Nd, Pr, Dy) ₂Fe ₁₄B/ α-Fe-based Magnets, IEEE TransMagn, Vol 39, No.5 (2003) 2947-2949.But their research shows simultaneously, and when having only content as α-Fe in the magnet very low (2～4vol%), could make the R of complex tissue by hot pressing ₂Fe ₁₄B crystal grain fully is out of shape and its easy magnetizing axis c-axle forms texture along pressing down direction, thereby the remanent magnetism Br of magnet is increased.And when α in the sample-Fe content increased to 11vol% α-Fe, hot pressing then almost can not make R ₂Fe ₁₄B is out of shape and the formation magnetic texture.The remanent magnetism Br of this magnet does not improve, and magnetic energy product only has (BH) _m24MGOe is as good as with the isotropism Nanocomposite magnet.

Yet, being in the built-up magnet of base mutually, have only α-Fe to reach certain quantity with hard magnetic, as 15～30%, just might obtain high magnetic characteristics, also could embody the cost advantage that its low content of rare earth brings.In disclosed technology, poor rare-earth iron-boron alloy composite permanent-magnetic material is because Nd but up to the present, ₂Fe ₁₄B can't be out of shape the formation magnetic texture mutually, poor rare earth alloy part also can't form magnetic texture in the mixture of poor rare earth alloy and rich rare earth alloy, therefore existing to contain higher volume percent soft magnetism phase thermal deformation built-up magnet magnetic lower, so cost performance of product can't improve.

Summary of the invention

The objective of the invention is to overcome the shortcoming of prior art, disclose a kind of method for preparing biphase composite permanent magnetic material, make that the percentage by volume of soft magnetism phase reaches at 5～80% o'clock in this permanent magnetic material, Hard Magnetic phase R ₂Fe ₁₄B still can form the consistent texture of easy magnetizing axis orientation, and magnet has high cost performance.

Concrete invention is as follows:

The present invention strengthens biphase composite heat distortion magnet of soft magnetism phase and preparation method thereof, and the phase composition of two-phase built-up magnet is R ₂T ₁₄M/Fe _1-x(Co, T ') _xWherein R is the mixing of the element combinations of at least a or rare earth element, yttrium in rare earth element and the yttrium or rare earth, yttrium, T is the combination between at least a transiting group metal elements or the transiting group metal elements, M is at least a element that selects to periodic table IIIA, IVA and the VA family element, and T ' is at least a other transition element except that Fe, Co; Soft magnetism phase Fe _1-x(Co, T ') _xNot only has high saturation magnetization, M _sGreater than 2.0T, and has the R of ratio at 500～1000 ℃ ₂T ₁₄The intensity that the M Hard Magnetic is mutually high; R ₂T ₁₄M just is being divided into branch alloy or rich rare earth alloy elder generation vacuum argon filling induction melting again, then fast quenching, and roll surface speed is 10～45m/s, powder process then; Fe _1-x(Co, T ') _xThe independent vacuum of alloy is argon filling powder by spraying or supersonic speed powder process again; With two kinds of powder, wherein soft magnetism phase volume percentage is greater than 5～80%; The hot repressing thermal deformation; In 500～1000 ℃ of deformation processes, R ₂T ₁₄The M powder particle preferentially is out of shape, R ₂T ₁₄The consistent arrangement of the nanocrystalline easy magnetizing axis orientation of M.

In foregoing invention, Fe _1-x(Co, T ') _xAlloying component Co26～55wt%Co, 0.0～4.0wt%V, 0.0～1.0wt%Cr, 0.0～2.5wt%Nb, 0.0～5.0wt%Cu, 0.0～5.0wt%W, 0.0～7.5wt%Ni, 0.0～5.5wt%Mn, 0.0～2.0wt%Ta, surplus Fe; Fe _1-x(Co, T ') _x500～700 ℃ of yield strengths that have more than the 150MPa, 700～800 ℃ of yield strengths that have more than the 50MPa, 800～900 ℃ of yield strengths that have more than the 10MPa; In relevant temperature, Fe _1-x(Co, T ') _xThe elevated temperature strength of phase is all than R ₂T ₁₄It is high that the elevated temperature strength of M is wanted.

Compared with prior art, the present invention has following advantage: in whole two-phase built-up magnet, and when content of rare earth is low, as less than 11.8at%, Hard Magnetic phase R in the magnet ₂T ₁₄M still can form parallel consistent orientation of its easy magnetizing axis, and built-up magnet has high cost performance.

Embodiment

Embodiment 1

Hard Magnetic phase alloy composition Nd _11.8Dy _0.4Pr _0.6Fe _74.9Co _6.5Al _0.2Ga _0.3B _5.3, first vacuum argon filling induction melting alloy, vacuum argon filling fast quenching again, vacuum degree all is better than 10 ^-1Pa, fast quenching running roller linear velocity is 25m/s, makes the amorphous thin slice; The thin slice fragmentation sieved obtain powder; With 47wt%Co, 2wt%V, 0.3wt%Nb, surplus Fe batching, the powder process of vacuum argon filling supersonic atomization; With Hard Magnetic phase R ₂T ₁₄The soft magnetism of M powder and the 15Vol% that accounts for bulk volume fraction is Fe mutually _1-x(Co, T ') _xPowder is again 700 ℃ of hot pressing, behind hot pressing temperature temperature retention time 60s; And at 700 ℃ of thick 90s of hot pier, deflection is 65%, and built-up magnet forms the magnetic texture along [006] direction.

Embodiment 2

Hard Magnetic phase alloy composition Nd _12.2Dy _0.8Pr _0.2Fe _73.8Co _6.5Ga _0.2B _6.3, first vacuum argon filling induction melting alloy, vacuum argon filling fast quenching again, vacuum degree all is better than 10 ^-1Pa, fast quenching running roller linear velocity is 20m/s, makes the amorphous thin slice; The thin slice fragmentation sieved obtain powder; With 45wt%Co, 3.0wt%V, 0.2wt%Ta, surplus Fe batching, the powder process of vacuum argon filling supersonic atomization; With Hard Magnetic phase R ₂T ₁₄The soft magnetism of M powder and the 20Vol% that accounts for bulk volume fraction is Fe mutually _1-x(Co, T ') _xPowder is again 750 ℃ of hot pressing, behind hot pressing temperature temperature retention time 50s; And at 750 ℃ of thick 90s of hot pier, deflection is 75%, and built-up magnet forms the magnetic texture along [006] direction.

Claims

1, biphase composite heat distortion magnet of reinforcement soft magnetism phase and preparation method thereof is characterized in that:

A. the phase composition of two-phase built-up magnet is R ₂T ₁₄M/Fe _1-x(Co, T ') _xWherein R is the mixing of the element combinations of at least a or rare earth element, yttrium in rare earth element and the yttrium or rare earth, yttrium, T is the combination between at least a transiting group metal elements or the transiting group metal elements, M is at least a element that selects to periodic table IIIA, IVA and the VA family element, and T ' is at least a other transition element except that Fe, Co;

B. soft magnetism phase Fe _1-x(Co, T ') _xNot only has high saturation magnetization, M _sGreater than 2.0T, and has the R of ratio at 500～1000 ℃ ₂T ₁₄The intensity that the M Hard Magnetic is mutually high;

C.R ₂T ₁₄M just is being divided into branch alloy or rich rare earth alloy elder generation vacuum argon filling induction melting again, then fast quenching, and roll surface speed is 10～45m/s, powder process then; Fe _1-x(Co, T ') _xThe independent vacuum of alloy is argon filling powder by spraying or supersonic speed powder process again;

D. with two kinds of powder, wherein soft magnetism phase volume percentage is greater than 5～80%; The hot repressing thermal deformation; In 500～1000 ℃ of deformation processes, R ₂T ₁₄The M powder particle preferentially is out of shape, R ₂T ₁₄The consistent arrangement of the nanocrystalline easy magnetizing axis orientation of M.

2, soft magnetism phase Fe as claimed in claim 1 _1-x(Co, T ') _x, it is characterized in that:

A.Fe _1-x(Co, T ') _xAlloying component Co26～55wt%Co, 0.0～4.0wt%V, 0.0～1.0wt%Cr, 0.0～2.5wt%Nb, 0.0～5.0wt%Cu, 0.0～5.0wt%W, 0.0～7.5wt%Ni, 0.0～5.5wt%Mn, 0.0～2.0wt%Ta, surplus Fe;

B.Fe _1-x(Co, T ') _x500～700 ℃ of yield strengths that have more than the 150MPa, 700～800 ℃ of yield strengths that have more than the 50MPa, 800～900 ℃ of yield strengths that have more than the 10MPa; In relevant temperature, Fe _1-x(Co, T ') _xThe elevated temperature strength of phase is all than R ₂T ₁₄It is high that the elevated temperature strength of M is wanted.