CN1251252C - Iron-boron-rare earth type pemanent magnetic material containing cerium, neodymium and/or praseodymium and its production method - Google Patents
Iron-boron-rare earth type pemanent magnetic material containing cerium, neodymium and/or praseodymium and its production method Download PDFInfo
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- CN1251252C CN1251252C CN 99102207 CN99102207A CN1251252C CN 1251252 C CN1251252 C CN 1251252C CN 99102207 CN99102207 CN 99102207 CN 99102207 A CN99102207 A CN 99102207A CN 1251252 C CN1251252 C CN 1251252C
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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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- 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
Abstract
The present invention relates to a Fe-B-R type permanent magnet which comprises 13 to 19 (atom) % of R, 4 to 20 (atom) % of B and Fe as the rest, wherein R is basically composed of a rare earth element Nd and/or the mixture of Pr and Ce; Ce is 0.2 to 5.0 wt% of R; the content of R is preferably 15 to 16 (atom) %, and the content of Ce is about 0.5%; the ratio of the rest rare earth Pr to Nd is 3: 1. The present invention also discloses a method or preparing the Fe-B-R permanent magnet shown as the figure and Fe-B-R permanent magnetic material prepared by the method.
Description
Technical field
The present invention relates to magnetic material and form and production method, specifically, relate to iron-boron-rare earth type (Fe-B-R) characteristic magnetic material.
Background technology
Since the eighties, be that the high characteristic permanent magnetic material of Fe-B-R type that contains the rare earth element of high-load element neodymium (Nd) becomes common at industrial use R.For example, computer hardware manufactory needs permanent magnet in this kind equipment of making little track, big capacity computer data-storing and retrieval hardware.Because size that these data-storing equipment are intrinsic and the strictness of weight restriction, the permanent magnet that comprises in these equipment must have smaller volume and also have very strong magnetic to produce needed magnetic field.It is necessary in this kind equipment, use high performance Fe-B-R rare-earth permanent magnet.
In addition, the medical diagnostic apparatus in medical domain, i.e. magnetic resonance imaging (MRI) equipment use the permanent magnetic material of a large amount of (up to 1.5 tons), and it is generally the rare earth Nd that the contains high percentage Fe-B-R type magnet as rare earth composition.
Therefore, because since the eighties is early stage, started selling the equipment that these utilize the Fe-B-R permanent magnet that its rare earth composition mainly is made up of Nd, so the demand of Nd is constantly increased.The result is, the price that is used to make the raw material Nd of these permanent magnets increases greatly.
A kind of real needs are to utilize less Nd to develop the essentially identical Fe-B-R magnet of performance, thereby reduce the cost of making these magnets and containing the equipment of these magnets.
The R of now known Fe-B-R type permanent magnet is one or more rare earth elements, and its R of at least 50% is Nd and/or praseodymium (Pr).For example, United States Patent (USP) 4,684,406 and 4,597,938 have all introduced a kind of high performance Fe-B-R type agglomeration permanent magnetic material.The high-performance magnet of these two pieces of patent disclosures is made of following composition by atomic percent: (i) R of 12.5-20%, wherein R is at least a rare earth element, (being selected from Nd, Pr, La, Ce, Tb, Dy, Ho, Er, Eu, Sm, Gd, Pm, Tm, Yb, Lu and Y), and at least 50% R is Nd and/or Pr; (ii) 4-20%B; And the (iii) Fe and the impurity of surplus.Similarly, with US 4,597,938, US 4,975,130 and US 4,684,606 can see that the method for this class permanent magnet of the disclosed preparation of these patents comprises: form metal dust with mentioned component; Fusion forms alloy pig; It is the alloy powder of 0.3-80 micron that alloy pig is ground the formation average grain diameter; Under the pressure of 0.5-8 ton/square centimeter with powder pressing; Compacts is to carry out under the magnetic field intensity of 7-13 kilo-oersted; At last, carry out sintering at 900-1200 ℃ (preferred 1000-1180 ℃).By the permanent magnet of specifically being made up of 77Fe-9B-9Nd-5Pr (wherein rare earth element consists of Nd and Pr) of method for preparing, sintering can obtain very high maximum magnetic energy product (BH) in 4 hours under 1120 ℃ of inert atmospheres
Maximum, be about 31.0MGOe.Equally, form the permanent magnet that sintering obtained in 1 hour in 1120 ℃ of air, its maximum magnetic energy product (BH) by 79Fe-7B-14Nd
MaximumBe about 33.8MGOe (referring to US 4,975,130 tables 1).Form by 77Fe-7B-16Pr, at 1040 ℃, 1 * 10
-42 hours permanent magnet of sintering under the vacuum of torr, its maximum magnetic energy product is less a little, i.e. 24.5MGOe.
When all unexposed the or hint of these patents of prior art is the concentration of Ce if any the amount of Ce or part R, what influence the Fe-B-R magnet performance is had.Do not have instruction or hint can substitute the concentration range of Nd in the prior art yet, thereby obtain having Fe-B-(Nd and/or the Pr) permanent magnet of identical or better magnetic as the Ce of Fe-B-R type magnet middle rare earth elemental composition.
Summary of the invention
The applicant finds: in containing the natural Rare Earth Mine of Nd, the percentage composition of cerium (Ce) is relatively low usually, and in certain percentage scope, the relatively low Ce of these percentage compositions can be used as a part of rare earth composition of Fe-B-R magnet.R comprises 70-76%Pr in addition, and 29.8-23.8%Nd and Ce do not have significantly or have only slight decline up to 5%Ce to the magnetic of resulting permanent magnet.
The applicant further finds, when in the manufacturing of Fe-B-R permanent magnet,, can further use up to 76% when replacing Nd with the Ce of low content (R weight 0.5%), and particularly 75% Pr replaces Nd.With make by the identical rare earth element of total percentage composition but do not contain the magnetic material of Ce, or make by the identical rare earth element of total percentage composition, and contain Ce but magnetic material with higher Nd content is compared, this substitution does not contain the reduction magnetic properties, in fact much at one or even increased magnetic properties.
According to the present invention, partly replace Nd with the Ce of specific little percentage composition and relatively large Pr, when making Fe-B-R type high-performance permanent magnet, can greatly reduce cost, keep the magnetic of magnet simultaneously basically.Although compare with the Fe-B-R magnetic material that uses pure basically Nd to make, add or carry a certain amount of Ce secretly and may cause that Fe-B-R type magnetic material magnetic reduces, but can use the other magnetic material of described in the present invention Ce of containing and Pr, thereby the deficiency of compensation MRI equipment magnetic field intensity.
Therefore, from aspect more widely, the present invention includes a kind of high performance permanent magnetic materials of Fe-B-R type, this material is made up of following component basically:
(i) 13-19 (atom) %R, wherein R is a rare earth element nd, the mixture of Pr and Ce, wherein Ce is about 0.2% to 5.0 (weight) % of R, and Pr is the 70-76% of R, Nd is the 29.8-23.8% of R;
(ii) 4-20 (atom) %B;
The (iii) Fe of surplus and impurity.
In preferred embodiments, Fe-B-R magnet of the present invention, in atomic percent, consist essentially of the R of 15-16%, wherein Ce accounts for 0.5-3 (weight) % of R, and is preferred 0.5%, and remaining R is made up of Pr and/or Nd basically, be preferably 71.6% Pr and 24.9 Nd, promptly the ratio of Pr and Nd is 3: 1.
The invention still further relates to the Fe-B-R type agglomeration permanent magnetic material that is prepared by following method, this method is:
(a) the preparation average grain diameter is the metal dust of 0.3-80 micron, described metal dust is basically by the R of 15-16 (atom) %, B and at least 52 (atom) %Fe of 4-8 (atom) % forms, wherein R is basically by light rare earth Nd, Pr and Ce form, Ce is 0.2-5.0 (weight) % of R, and the R of surplus is made up of the Nd of 29.8-23.8% and the Pr of 70-76% basically;
(b) at least 0.5 ton/cm
2Pressure under, with described powder pressing;
(c) under non-oxide or reducing atmosphere, at 900-1200 ℃ with resulting compacts sintering.
In the above-mentioned Fe-B-R type agglomeration permanent magnetic material, preferred B is the 5-7% atomic percent.
In addition, the applicant finds, although add Ce the magnetic property of the Fe-B-R type magnet that has only Nd is descended, and when Ce content is low, replaces Nd that the magnetic that loses is recovered greatly with Pr.Therefore, the applicant finds, uses low content Ce (the 0.5 weight % of R), and remaining R is made up of about 74.6 (weight) %Pr and about 24.9 (weight) %Nd basically, adopt aforesaid method can obtain a kind of have standard magnetic Hci with (BH)
MaximumThe permanent magnet of value, the Fe-B-R type magnet that it is substantially equal to or only is made up of Nd and/or Pr above the R component to a certain degree.
The present invention also comprises a kind of method of producing sintered permanent magnet.Specifically, the invention still further relates to a kind of method of the Fe-B-R of production type sintered permanent magnet, this method comprises:
(a) the preparation average grain diameter is the metal dust of 0.3-80 micron, preferably be not more than 4.0 microns, described metal dust is basically by the R of 15-16 (atom) %, B and at least 52 (atom) %Fe preferred 78 (atom) %Fe of the B of 4-24 (atom) % preferred 6.5 (atom) % forms, wherein R is basically by light rare earth Nd, and Pr and Ce form, and wherein Ce is 0.1-5.0 (weight) % of R, be preferably 0.5% of R, Pr be preferably about 74% and Nd be preferably 25%;
(b) at least 0.5 ton/cm
2Pressure under, with described powder pressing;
(c) under non-oxide or reducing atmosphere, at 900-1200 ℃ with resulting compacts sintering.
Description of drawings:
Following description of drawings specific embodiment of the present invention, wherein:
Fig. 1 is the curve that is selected from table 1 result, the expression when the Ce component be R 0.5% the time, the intrinsic coercive force Hci of Fe-B-R type permanent magnetic material is the function of Pr component among the R.
Fig. 2 is the curve that is selected from table 1 result, represents when the Ce component is the 5.0-5.3% of R the function that this special coercivity H i of Fe-B-R type permanent magnetic material is a Pr component among the R.
Fig. 3 is the curve of similar Fig. 4, expression be the result who is selected from table 1, the expression when Pr content is the 22.5-25% of R, the intrinsic coercive force Hci of Fe-B-R type permanent magnetic material is the function of Ce component among the R.
Fig. 4 is the curve of similar Fig. 3, expression be the result who is selected from table 1, the expression when Pr content is the 50-60% of R, the intrinsic coercive force Hci of Fe-B-R type permanent magnetic material is the function of Ce component among the R.
Fig. 5 is the curve of similar Fig. 4, expression be the result who is selected from table 1, the expression when Pr content is the 74.6-100% of R, the intrinsic coercive force Hci of Fe-B-R type permanent magnetic material is the function of Ce component among the R.
Embodiment
Because Rare-Earth Ce generally exists with Nd and Pr jointly at occurring in nature, and the content of Nd helps cost in the minimizing rare-earth permanent magnet, and the applicant tests as the Fe-B-R type permanent magnet of rare earth composition having various Ce content.The applicant also further changes the Nd of rare earth elements and/or the relative scale and the concentration of the relative Ce amount of Pr, and the magnetic of the Fe-B-R permanent magnet that manufacturing is obtained is measured.Table 1 has been listed the result of 35 Fe-B-R type permanent magnet samples, wherein utilizes the composition of the different proportion change R of Ce, Pr and Nd, and wherein Pr, Ce and Nd are based on the percentage by weight of R.
Table 1
| Sample | Pr (wt％) | Ce (wt.％) | Nd (wt.％) | iHc (kOe) |
| B1-1 B1-2 B1-3 B2-1 B2-2 B2-3 B3-1 B3-2 B3-3 B4-1 B4-2 B4-3 B5-1 B5-2 B5-3 E0 E1 E2 E3 E4 E5 E6 E7 E-A E-B1 E-B2 E-C1 E-C2 E-D1 E-D2 E-AB1 E-AB2 E-CD1 E-CD2 E-ABCD | 24.9 24.9 24.9 24.0 24.0 24.0 22.5 22.5 22.5 4.5 4.5 4.5 74.6 74.6 74.6 0.0 25.0 24.0 22.5 4.5 74.6 48.6 53.8 50.0 60.0 60.0 90.0 90.0 100.0 100.0 55.0 55.0 95.0 95.0 75.0 | 0.5 0.5 0.5 4.0 4.0 4.0 10.0 10.0 10.0 0.5 0.5 0.5 0.5 0.5 0.5 0.0 0.0 4.0 10.0 0.5 0.5 5.3 4.3 10.0 0.0 0.0 10.0 10.0 0.0 0.0 5.0 5.0 5.0 5.0 5.0 | 74.7 74.7 74.7 72.0 72.0 72.0 67.5 67.5 67.5 95.0 95.0 95.0 24.9 24.9 24.9 100.0 75.0 72.0 67.5 95.0 24.9 46.2 41.9 40.0 40.0 40.0 0.0 0.0 0.0 0.0 40.0 40.0 0.0 0.0 20.0 | 11.1 11.3 9.7 9.5 9.3 9.8 5.8 6.2 6.1 10.0 10.3 10.3 13.3 10.5 10.5 11.1 11.2 10.0 5.8 11.5 15.7 9.5 11.7 6.6 11.7 12.1 7.7 7.2 9.8 10.7 7.9 9.0 9.0 9.3 7.7 |
Appended Fig. 1-the 5th, by the curve of table 1 data institute banknotes-system, it is woven together is for the data of interpret table 1 better, and shows the caused magnetic variation tendency of variation that the 78Fe-B6.5-R15.5 permanent magnet R that tested forms.
Data and curves is the relation of magnetic Hci to Ce concentration, and at Pr with Nd% is constant or the constant substantially banknotes-system of down carrying out, the percentage composition of Nd=(100[Ce]-[Pr]) %.Fig. 3 is illustrated under the constant relatively situation of Pr (for the 22.5-25% weight of R) magnetic Hci with the change curve of Ce addition.
Fig. 4 is illustrated under the constant relatively situation of Pr (for the 50-60% weight of R), and magnetic Hci is with the change curve of Ce addition.Similarly, Fig. 5 is illustrated under the constant relatively situation of Pr (74.6-100%), and magnetic Hci is with the change curve of Ce addition.
Can see that from Fig. 3-5 under above-mentioned every kind of situation, in a broad sense, the Ce addition in the scope of 5-10% can cause that Hci descends at least, be that 0% o'clock 10-12kOe changes to 10% o'clock the 6.1-7.8kOe that Ce content is R by Ce concentration.
Yet, importantly, by scrutinizing table 1 and Fig. 3-5, the applicant observes, when the Ce addition be 0%-up to about 5% the time reduction of magnetic (Hci) not remarkable, and in some cases, the upper limit of Hci was 0% o'clock height than Ce content when Ce content was 4-5%.
The trend analysis that his-and-hers watches 1 data are reflected has obtained the result of shock.Particularly, when Ce content kept roughly constant, Hci with the variation tendency of Pr (weight) % was: be 0.5-10% for Ce concentration at least, along with Pr percentage increases, magnetic Hci rises.
Fig. 1 and 2 represent when Ce be 0.5% (Fig. 1) and Ce when being 5.0-5.3% (Fig. 2), the magnetic Hci of sample changes with the Pr addition.As seen from Figure 2, for Ce is 5.0-5.3% (Fig. 2), replaces Nd and makes Pr concentration be elevated to 95% (being that Nd content reduces to 0% by 47%) by 48% with Pr, and Hci has an evenness, to not influence of Hci, this point can be seen from " best fit " curve of Fig. 2.
For Ce is 0.5% (Fig. 1), makes Pr be increased to 74.6% by 4.5% Hci is increased, by mean value 10.5kOe[promptly, (10.0+10.3+10.3+11.5)/4] rise to i.e. (13.3+10.5+10.5+15.7)/4 of 12.5kOe[].Hci is descended there is no tangible influence owing to add 0.5% Ce, so cheeringly be to add Pr and replace Nd (Pr/Nd=3: the 1) height of the Hci that can make permanent magnet when not adding Ce.Particularly, when Ce be 0.5% (Pr=74.6%, in the time of Nd=24.9%), Hci mean value is 12.5kOe, and as previously mentioned, when above-mentioned Pr and Nd scope did not add Ce, Hci mean value only was 11.1kOe.In fact, (Pr=74.6%, Ce=0.5%) be far longer than Ce is 0% maximum (12.1 kilo-oersted) to the maximum 15.7kOe of Hci.
Below the method for preparing sample and acquisition table 1 data is described.
(1) takes by weighing to contain and predetermined different form the raw material that is used for each different magnet samples, and melted with the high-frequency induction method.In cold mould, the casting of gained melt is obtained the blank sample.
(2) with the crushing of gained blank, in ball mill, grind then until obtaining the powder that particle diameter is the 0.3-80 micron.
(3) powder that grinds is applied the magnetic field of 7-20kOe, make powder particle along magnetic direction be arranged in rows (Co-align).
(4) at 1.5 tons/cm
2Pressure under, powder is pressed into compacts, its density is about 6g/cm
3
(5) under 1120 ℃ inert atmosphere with compacts sintering 2 hours.
(6) measure the Hci value of each sample, and write down and tabulate in table 1.
Be applied to and make magnetic field that powder particle arranges 7kOe at least on the powder.In addition, magnetic field can be the about 30kOe of 7-.In another embodiment, magnetic field is 7-20kOe.In further embodiment, magnetic field is 13kOe.
Adopt the powder metallurgy sintered method of preparation said sample can make the Fe-B-R magnet that contains particular percentile Ce of the present invention.Be described with regard to the method for making new compositions of the present invention below.
To generate average grain diameter is the 0.3-80 micron by having the following composition formed, preferably less than 10 microns metal dust:
I) 13-19 (atom) %, the R of preferred 15-16 (atom) %, wherein R is made up of light rare earth Nd and/or Pr and Ce basically, and Ce is 0.2-5.0 (weight) % among the R, and is preferred 0.5%, and surplus R is essentially Nd and Pr, preferably about 74.6%Pr and 24.9%Nd.
Ii) 4-8 (atom) %, the B of preferred 6.5 (atom) %, and
The iii) Fe of surplus is preferably the Fe of 78 (atom) %.
This powder can be produced by known ball-milling method or Alpine jet mill (jet mill).Because it is wideer than the powder that Alpine jet mill obtains that ball milling obtains the particle size distribution of powder, and particle size distribution can influence magnet arrangements, Br and (BH) really
Max, the therefore preferred employing latter grinds method.
As sample, the gained powder can be put in case of necessity under the magnetic field intensity of 7.0-20kOe and handle.Then, with metal dust at least 1.5 tons/cm
2Pressure under compacting, obtain density and be at least 5g/cm
3Compacts.
Then, with the gained compacts in reducing atmosphere, inert atmosphere or vacuum, in 900-1200 ℃, preferred 1000-1180 ℃ of sintering 15 minutes to 8 hours, preferably at least 1 hour.
Although this paper to preferred and exemplary embodiment of the present invention in addition description, yet should understand, for those of ordinary skill in the art, after having read the application's text, can obviously carry out some changes and adjustment to the present invention.Protection scope of the present invention should be with reference to appended claim.
Claims (20)
1. high performance Fe-B-R type permanent magnetic material, described material is grouped into by following one-tenth basically:
(i) R of the atomic percent of 13-19%, wherein R is made up of the mixture of rare earth element nd, Pr and Ce basically, and the amount of Ce is the percentage by weight of 0.2-5.0% among the R, and Pr is the percentage by weight of 70-76%, Nd is the percentage by weight of 29.8-23.8%;
The (ii) B of the atomic percent of 4-20%;
(iii) surplus is Fe and impurity.
2. the Fe-B-R type permanent magnetic material of claim 1, wherein Ce content is the percentage by weight of the 0.5-5.0% of R.
3. the Fe-B-R type permanent magnetic material of claim 1, wherein R is the atomic percent of 14.0-16.0%.
4. the Fe-B-R type permanent magnetic material of claim 1, wherein B is the atomic percent of 5.0-7.0%.
5. the Fe-B-R type permanent magnetic material of claim 1, wherein the weight ratio of Pr among the R and Nd is 3: 1.
6. the Fe-B-R type permanent magnetic material of claim 1 is used for magnetic resonance imaging apparatus.
7. the Fe-B-R type permanent magnetic material of claim 1, wherein Ce is the percentage by weight of the 0.5-3.0% of R, the R of surplus percentage is essentially Nd.
8. the Fe-B-R type permanent magnetic material of claim 7, wherein Pr is 74.6% the percentage by weight of R, and Ce is 0.5% the percentage by weight of R, and the R of remaining percentage is essentially Nd.
9. the Fe-B-R type permanent magnetic material of claim 4, wherein B is 6.5% atomic percent.
10. the Fe-B-R type permanent magnetic material of claim 9, wherein R is 15.5% atomic percent.
11. a method for preparing Fe-B-R type agglomeration permanent magnetic material, it may further comprise the steps:
(a) the preparation average grain diameter is the alloy powder of 0.3-80 micron, described alloy powder is basically by the R of the atomic percent of 15-16%, the Fe of the B of the atomic percent of 4-8% and at least 52% atomic percent forms, wherein R is basically by light rare earth Nd, Pr and Ce form, Ce is the percentage by weight of the 0.2-5.0% of R, and the R of surplus is made up of the Pr of the percentage by weight of the Nd of the percentage by weight of 29.8-23.8% and 70-76% basically;
(b) at least 0.5 ton/cm
2Pressure under, with described powder pressing;
(c) under non-oxide or reducing atmosphere, at 900-1200 ℃ with resulting compacts sintering.
12. the method for claim 11 wherein with metal material fusing, cooling gained alloy, is ground the described powder of formation with alloy.
13. the method for claim 12, the step of wherein grinding alloy comprises that the described alloy of ball milling generates described powder.
14. the method for claim 12, the step of wherein grinding alloy comprises that the described alloy of jet mill generates described powder.
15. the method for claim 11 when also being included in the described powder of compacting, applies the magnetic field of 7kOe at least.
16. the method for claim 15 wherein by grinding, obtains the alloy powder that average grain diameter is not more than 10.0 microns.
17. a Fe-B-R type agglomeration permanent magnetic material is prepared according to the following steps:
(a) the preparation average grain diameter is the metal dust of 0.3-80 micron, described metal dust is basically by the R of the atomic percent of 15-16%, the Fe of the B of the atomic percent of 4-8% and at least 52% atomic percent forms, wherein R is basically by light rare earth Nd, Pr and Ce form, Ce is the percentage by weight of the 0.2-5.0% of R, and Pr is the percentage by weight of 70-76%, and Nd is the percentage by weight of 29.8-23.8%;
(b) at least 0.5 ton/cm
2Pressure under, with described powder pressing;
(c) under non-oxide or reducing atmosphere, at 900-1200 ℃ with resulting compacts sintering.
18. the permanent magnetic material of claim 17, wherein B is the 5-7% atomic percent.
19. the permanent magnetic material of claim 18, wherein compacts is at 1000-1180 ℃ of sintering.
20. the permanent magnetic material of claim 18 wherein by grinding, makes the average grain diameter of metal dust be not more than 7.0 microns.
Priority Applications (6)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN 99102207 CN1251252C (en) | 1999-02-12 | 1999-02-12 | Iron-boron-rare earth type pemanent magnetic material containing cerium, neodymium and/or praseodymium and its production method |
| AU27515/00A AU2751500A (en) | 1999-02-12 | 2000-02-02 | Permanent magnetic materials of the r-fe-b type and process of manufacture |
| US09/673,045 US6669788B1 (en) | 1999-02-12 | 2000-02-02 | Permanent magnetic materials of the Fe-B-R tpe, containing Ce and Nd and/or Pr, and process for manufacture |
| PCT/US2000/002649 WO2000048208A1 (en) | 1999-02-12 | 2000-02-02 | Permanent magnetic materials of the r-fe-b type and process of manufacture |
| EP00905918A EP1072043B1 (en) | 1999-02-12 | 2000-02-02 | Permanent magnetic materials of the r-fe-b type and process of manufacture |
| DE60010385T DE60010385T2 (en) | 1999-02-12 | 2000-02-02 | PERMANENT MAGNETIC MATERIALS OF TYPE R-FE-B AND MANUFACTURING METHOD THEREFOR |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN 99102207 CN1251252C (en) | 1999-02-12 | 1999-02-12 | Iron-boron-rare earth type pemanent magnetic material containing cerium, neodymium and/or praseodymium and its production method |
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| Publication Number | Publication Date |
|---|---|
| CN1263349A CN1263349A (en) | 2000-08-16 |
| CN1251252C true CN1251252C (en) | 2006-04-12 |
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| CN 99102207 Expired - Fee Related CN1251252C (en) | 1999-02-12 | 1999-02-12 | Iron-boron-rare earth type pemanent magnetic material containing cerium, neodymium and/or praseodymium and its production method |
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| Country | Link |
|---|---|
| EP (1) | EP1072043B1 (en) |
| CN (1) | CN1251252C (en) |
| AU (1) | AU2751500A (en) |
| DE (1) | DE60010385T2 (en) |
| WO (1) | WO2000048208A1 (en) |
Families Citing this family (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US6518867B2 (en) | 2001-04-03 | 2003-02-11 | General Electric Company | Permanent magnet assembly and method of making thereof |
| US7148689B2 (en) | 2003-09-29 | 2006-12-12 | General Electric Company | Permanent magnet assembly with movable permanent body for main magnetic field adjustable |
| US7423431B2 (en) | 2003-09-29 | 2008-09-09 | General Electric Company | Multiple ring polefaceless permanent magnet and method of making |
| US7218195B2 (en) | 2003-10-01 | 2007-05-15 | General Electric Company | Method and apparatus for magnetizing a permanent magnet |
| CN100461308C (en) * | 2005-05-22 | 2009-02-11 | 横店集团东磁有限公司 | Ultra-high coercive force sintered Nd-Fe-B magnetic material and preparing process thereof |
| CN101694797B (en) * | 2009-10-27 | 2012-08-22 | 麦格昆磁（天津）有限公司 | Novel neodymium iron boron magnetic material |
| CN102969112B (en) * | 2012-12-05 | 2016-04-27 | 麦格昆磁（天津）有限公司 | Rare earth permanent magnet powder and preparation method thereof and magnet prepared therefrom and magnetic device |
| CN106448987A (en) * | 2016-10-16 | 2017-02-22 | 桂林电子科技大学 | Method for preparing high-coercivity rare earth permanent magnetic ribbon with optimized composition proportion |
Family Cites Families (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS60228652A (en) * | 1984-04-24 | 1985-11-13 | Nippon Gakki Seizo Kk | Magnet containing rare earth element and its manufacture |
| KR880013194A (en) * | 1987-04-06 | 1988-11-30 | 원본미기재 | Permanent magnet and its manufacturing method |
| JPH06346200A (en) * | 1993-06-14 | 1994-12-20 | Daido Steel Co Ltd | Permanent magnet alloy |
-
1999
- 1999-02-12 CN CN 99102207 patent/CN1251252C/en not_active Expired - Fee Related
-
2000
- 2000-02-02 AU AU27515/00A patent/AU2751500A/en not_active Abandoned
- 2000-02-02 DE DE60010385T patent/DE60010385T2/en not_active Expired - Lifetime
- 2000-02-02 EP EP00905918A patent/EP1072043B1/en not_active Expired - Lifetime
- 2000-02-02 WO PCT/US2000/002649 patent/WO2000048208A1/en active IP Right Grant
Also Published As
| Publication number | Publication date |
|---|---|
| WO2000048208A9 (en) | 2001-08-09 |
| DE60010385D1 (en) | 2004-06-09 |
| EP1072043A1 (en) | 2001-01-31 |
| CN1263349A (en) | 2000-08-16 |
| DE60010385T2 (en) | 2005-05-04 |
| AU2751500A (en) | 2000-08-29 |
| EP1072043B1 (en) | 2004-05-06 |
| WO2000048208A1 (en) | 2000-08-17 |
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