CN1032262A - The optimization of iron-neodymium-Fe-Nd-B sintered magnet texture structure - Google Patents
The optimization of iron-neodymium-Fe-Nd-B sintered magnet texture structure Download PDFInfo
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- CN1032262A CN1032262A CN 88106179 CN88106179A CN1032262A CN 1032262 A CN1032262 A CN 1032262A CN 88106179 CN88106179 CN 88106179 CN 88106179 A CN88106179 A CN 88106179A CN 1032262 A CN1032262 A CN 1032262A
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- sintered magnet
- phase
- magnet
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- neodymium
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- 238000005457 optimization Methods 0.000 title description 2
- 238000005245 sintering Methods 0.000 claims abstract description 12
- 239000000203 mixture Substances 0.000 claims abstract description 11
- 229910052779 Neodymium Inorganic materials 0.000 claims abstract description 5
- 239000007788 liquid Substances 0.000 claims abstract description 4
- 229910052692 Dysprosium Inorganic materials 0.000 claims description 5
- 229910052771 Terbium Inorganic materials 0.000 claims description 3
- 230000005389 magnetism Effects 0.000 claims description 3
- 238000012797 qualification Methods 0.000 claims 1
- 230000005291 magnetic effect Effects 0.000 abstract description 12
- 239000012071 phase Substances 0.000 description 23
- 238000000034 method Methods 0.000 description 6
- 239000000843 powder Substances 0.000 description 4
- 230000008901 benefit Effects 0.000 description 3
- 238000004519 manufacturing process Methods 0.000 description 3
- 239000000956 alloy Substances 0.000 description 2
- 229910045601 alloy Inorganic materials 0.000 description 2
- 238000005275 alloying Methods 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 230000005294 ferromagnetic effect Effects 0.000 description 2
- 239000008188 pellet Substances 0.000 description 2
- 238000003825 pressing Methods 0.000 description 2
- 230000015572 biosynthetic process Effects 0.000 description 1
- 229910052796 boron Inorganic materials 0.000 description 1
- 230000006835 compression Effects 0.000 description 1
- 238000007906 compression Methods 0.000 description 1
- 239000000470 constituent Substances 0.000 description 1
- 238000001816 cooling Methods 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 230000002708 enhancing effect Effects 0.000 description 1
- 230000005307 ferromagnetism Effects 0.000 description 1
- 238000010438 heat treatment Methods 0.000 description 1
- ZWKKPKNPCSTXGA-UHFFFAOYSA-N iron neodymium Chemical compound [Fe].[Fe].[Nd] ZWKKPKNPCSTXGA-UHFFFAOYSA-N 0.000 description 1
- 239000007791 liquid phase Substances 0.000 description 1
- 239000000696 magnetic material Substances 0.000 description 1
- 230000005415 magnetization Effects 0.000 description 1
- 239000000463 material Substances 0.000 description 1
- 229910001172 neodymium magnet Inorganic materials 0.000 description 1
- 230000005408 paramagnetism Effects 0.000 description 1
- 238000010587 phase diagram Methods 0.000 description 1
- 238000004663 powder metallurgy Methods 0.000 description 1
- 238000011160 research Methods 0.000 description 1
- 238000005496 tempering Methods 0.000 description 1
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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
- H01F1/0575—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
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- Chemical & Material Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Inorganic Chemistry (AREA)
- Engineering & Computer Science (AREA)
- Power Engineering (AREA)
- Hard Magnetic Materials (AREA)
Abstract
The characteristics of novel Fe-Nd-B sintered magnet are not have the above Fe of 0.5 μ m in its tissue
4NdB
4Body (η phase), its composition is in Fe under the sintering temperature
14Nd
2B () be rich in Nd and be liquid (L phase) mutually two phase region, the magnetic of this magnet, particularly coercive field strength H more than 655 ℃
CJBe greatly improved with its temperature coefficient.
Description
The present invention relates to the improved iron-neodymium of performance-boron (Fe-Nd-B) sintered magnet and method for making thereof.
Since M.Sagawa at J.Appl.Phys.55,2083(1984) in since the reported first Nd-Fe-B novel permanent magnetic material, for further improving the performance of these materials, carried out many researchs again.The basis of these tests is, the magnet of Fe-Nd-B magnet, particularly this composition, and the feature under the room temperature is that the magnetic characteristic value is high especially.But when having this advantage, yet show shortcoming, its temperature stability mainly is coercive field strength H
CJTemperature stability can not be satisfactory, and the application of this magnet in the machine of heating is restricted.Therefore,, just must improve, so that it also can be used for strong counter field (Gegenfeldern) up to 200 ℃ to this magnet for industrial application the in this field.
Performance can not be satisfactory, is to have non-ferromagnetic structural constituent with the theoretical value one of the main reasons that its coercive field strength is low by comparison particularly.This can cause the ferromagnetism stray magnetic field, thereby forms non magnetic seed crystal in the non magnetic near region that influences easily.This self-demagnetization effect is always very strong under the intensification condition, and is very big because the intrinsic coercive field strength varies with temperature as stray-field effect.
In making the sintered magnet that consists of Fe77 Nd15 B8 for example, mainly contain 3 phases, promptly
1.Fe14 Nd2 B hereinafter referred to as the φ phase, is the carrier of magnetic,
2. be rich in the Nd phase (basically by Nd, Nd
2O
3Form), hereinafter referred to as the L phase, be liquid more than 655 ℃, not only can in the liquid-phase sintering process, reach good concentrating, and can make adjacent φ body reach the magnetic decoupling,
3.Fe4Nd B4 hereinafter referred to as the η phase, has paramagnetism more than the 13K, therefore can think to occur the main cause of above-mentioned shortcoming.
In described known typical magnet, for example consist of that the η phase volume accounts for 5～8%, L accounts for 10% mutually, and all the other are by ferromagnetic φ phase composition.
According to the viewpoint of this professional domain, in Fe-Nd-B magnet manufacture process, do not wish that the formation of the η phase that exists can not stop, therefore must think inevitably (R.K.Mishra, J.Appl.Phys.59,2244(1986)).
The objective of the invention is to improve the magnetic of Fe-Nd-B sintered magnet, particularly improve the relation of coercive field strength and itself and temperature, and enhancing remanent magnetism.
According to the present invention, this purpose reaches by the Fe-Nd-B sintered magnet, it is characterized in that in its tissue not having the above Fe4Nd B4 body (η phase) of 0.5 μ m, its composition is in Fe14 Nd2B(φ phase under the sintering temperature) and be rich in Nd and be (L phase) mutually two phase region of liquid state more than 655 ℃.
Owing to lack bigger η body in the sintered magnet of the present invention, therefore can improve above-mentioned magnetic greatly.
According to known Fe-Nd-B three-phase diagram (K.H.J.Buschow et al., Philips J.Res.40,230(1985)), there is not L+ φ two phase region under the sintering temperature.But, existing unexpectedly find and constitute basis of the present invention be, be mainly two phase region under the sintering temperature, and can come the composition of select magnet alloy like this, promptly under about 1000-1080 ℃ sintering temperature, be in this two phase region.Fig. 1 illustrates this new phasor under 1060 ℃ with the isothermal level form, wherein with the hachure above-mentioned two-phase of drawing.Under 1060 ℃ sintering temperature, two phase alloys just necessarily are in this triangle, and this triangle is limited by following each point:
Fe82.3 Nd11.8 B5.9，
Fe58.5 N38 B3.5 and
Fe60.5 Nd27 B12.5。
Therefore, according to the present invention, the magnet in this compositing range is preferred.
According to the present invention, in the sintering temperature cooling procedure, only in tissue, form very tiny η body in the magnet that occurs under the sintering temperature in the two phase region.Owing to lack inevitably big in the past η body, therefore performance is improved.Fig. 2 a and 2b illustrate the institutional framework difference between known magnet (2a) and the magnet of the present invention (2b).The composition of Fig. 2 a magnet is corresponding to formula Fe77 Nd15 B8.φ is light mutually, and η phase gray, L are black mutually.The magnet of Fig. 2 b is corresponding to forming Fe75 Nd18.5 B5.6.Here no longer can see the η phase that grey occurs.The sintered magnet of this Fe75 of consisting of Nd18.5 B at room temperature presents following typical performance:
Remanent magnetism Br=1.1 T
Coercive field strength H
CJ=1040kA/m.
These values are typical to sintered magnet of the present invention and generally can be above 5% with regard to its deviation of above-mentioned specific composition.
The special benefits of sintered magnet of the present invention is to have improved magnetization coercive field strength H greatly
CJTemperature coefficient.This coefficient of known magnet-0.7～-more than the 0.9%/K, and this coefficient of magnet of the present invention is-0.5%/K, wherein goes up lower deviation and can be 0.1%/K according to the difference of forming.
In the sintered magnet of the present invention except basis Fe-Nd-B and also can add other alloying element, Co particularly, Al, Dy, a kind of and multiple among Tb and the C, its consumption can be learnt from document, thereby influenced the crystalline anisotropy, performances such as Curie temperature and magnetic moment.Contain 0～20At.-% Co, 0～15At.-% Al, 0～20At.-% Dy, 0～20At.-%Tb and 0～12.5 At.-%C in the preferred magnet of the present invention.
Major advantage when adding one or more above-mentioned other alloying elements in the two-phase magnet of the present invention can be as seen from Figure 3, and wherein the correspondence that the temperature relation of the coercive field strength of 3 kinds of Fe-Nd-B magnet in the prior art is added or do not add Al or Dy is formed magnet of the present invention and compared.3 phase group of magnets become Nd15 Fe77 B8, Nd15(Fe75 A12 in the prior art) B8 and Nd13.5 Dy1.5Fe77 B8.Corresponding the present invention's 2 phase group of magnets become Nd18.5 Fe75 B6.5, Nd18.5(Fe73 A12) B6.5 and Nd16.65 Dy1.85 Fe75 B6.5.
The manufacture method of sintered magnet of the present invention is from by known powder metallurgy mode that each pure component (purity 99% or higher) is pre-alloyed.In the preferred manufacture method, on perpendicular to the direction of pressing direction, add a magnetic field, powder axially is pressed into green pellets to mixture of powders, and in inert atmosphere, preferably in rare gas in 1040-1080 ℃ of this raw pellet ore of following sintering, then in 500-700 ℃ of following tempering.
For making the mixture of powders of each component, can adopt the WC-Co-vibrator in the rare gas for example.By on direction, adding the magnetic field of 0.4～0.6T perpendicular to pressing direction, powder is arranged in a linear, and then axial compression.Pressure is preferably 500-800MPa, particularly 450-550MPa.
Sintering preferably carries out in 1050-1070 ℃ of scope, and can continue about 0.5～3 hour according to the difference of used condition.Generally anneal under 500-700 ℃ then, the duration was generally 0.2～4 hour.
Claims (7)
1, Fe-Nd-B sintered magnet is characterized in that not having the above Fe of 0.5 μ m in its tissue
4NdB
4Body (η), its composition is in Fe under the sintering temperature
14Nd
2B (ψ phase) be rich in Nd and be liquid (L phase) mutually two phase region more than 655 ℃.
2, the sintered magnet of claim 1 is characterized in that being in the interior composition of triangle by Fe82.3 Nd11.8 B5.9, Fe58.5 Nd38 B3.5 and 3 qualifications of Fe60.5 Nd27 B12.5.
3, claim 1 and 2 sintered magnet is characterized in that consisting of Fe75 Nd18.5 B6.5.
4, the sintered magnet of one of claim 1～3 is characterized in that the temperature coefficient Hc that magnetizes coercive field strength is-0.5%/K in 10～110 ℃ of scopes.
5, the sintered magnet of claim 3 is characterized in that remanent magnetism B under the room temperature
RBe 1.1 ± 5%T, coercive field strength is 1040 ± 5%kA/m.
6, the sintered magnet of one of claim 1～5 is characterized in that wherein containing at least a Co of being selected from, Al, Dy, the element of Tb and C.
7, the sintered magnet of claim 6 is characterized in that wherein containing 0～20At-%Co, 0-15At-%Al, 0～20At-%Dy, 0～20At-%Tb and 0～12.5At-%C.
Applications Claiming Priority (2)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| DE19873729361 DE3729361A1 (en) | 1987-09-02 | 1987-09-02 | OPTIMIZATION OF THE STRUCTURE OF THE FE-ND-B BASE SINTER MAGNET |
| DEP3729361.3 | 1987-09-02 |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CN1032262A true CN1032262A (en) | 1989-04-05 |
Family
ID=6335083
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN 88106179 Pending CN1032262A (en) | 1987-09-02 | 1988-08-22 | The optimization of iron-neodymium-Fe-Nd-B sintered magnet texture structure |
Country Status (3)
| Country | Link |
|---|---|
| CN (1) | CN1032262A (en) |
| DE (1) | DE3729361A1 (en) |
| WO (1) | WO1989002156A1 (en) |
Families Citing this family (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| AT399415B (en) * | 1991-03-18 | 1995-05-26 | Boehler Ybbstalwerke | METHOD FOR PRODUCING RARE EARTH-CONTAINING PERMANENT MAGNET (S) (MATERIALS) |
| DE4142160C1 (en) * | 1991-12-20 | 1993-03-11 | Heraeus Elektrochemie Gmbh, 6450 Hanau, De | |
| DE19945943B4 (en) * | 1999-09-24 | 2005-06-02 | Vacuumschmelze Gmbh | Borarme Nd-Fe-B alloy and process for its preparation |
Family Cites Families (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS6187825A (en) * | 1984-10-05 | 1986-05-06 | Hitachi Metals Ltd | Manufacture of permanent magnet material |
| JPH0789521B2 (en) * | 1985-03-28 | 1995-09-27 | 株式会社東芝 | Rare earth iron permanent magnet |
-
1987
- 1987-09-02 DE DE19873729361 patent/DE3729361A1/en not_active Withdrawn
-
1988
- 1988-06-23 WO PCT/EP1988/000555 patent/WO1989002156A1/en unknown
- 1988-08-22 CN CN 88106179 patent/CN1032262A/en active Pending
Also Published As
| Publication number | Publication date |
|---|---|
| WO1989002156A1 (en) | 1989-03-09 |
| DE3729361A1 (en) | 1989-03-16 |
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| C06 | Publication | ||
| PB01 | Publication | ||
| C10 | Entry into substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| C01 | Deemed withdrawal of patent application (patent law 1993) | ||
| WD01 | Invention patent application deemed withdrawn after publication |