CN105632673B - The preparation method and permanent-magnet material of permanent-magnet material - Google Patents
The preparation method and permanent-magnet material of permanent-magnet material Download PDFInfo
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Abstract
The invention provides a kind of preparation method of permanent-magnet material and permanent-magnet material.The preparation method comprises the following steps：A powder and B powder are prepared respectively, and the main component of A powder is SmxFe(1‑x‑y)My, wherein M is selected from any of Ti, V, Mo and Co or a variety of, and x scope is 40~50wt%, and y scope is 0~5wt%, and A powder is the powder of crystalline state；The main component of B powder is RM, and wherein R is at least one rare earth element, and M is selected from least one of Fe and Co, and R mass percent is 85~95% in B；A powder and B powder are mixed to get hybrid alloys powder, and the mass percent of B powder is 3~10wt% in hybrid alloys powder；Hot compression deformation is carried out to hybrid alloys powder to handle to permanent-magnet material of the formation with anisotropic crystal grain.The preparation method improves formability of the permanent-magnet material in preparation process.
Description
Technical field
The present invention relates to permanent-magnet material technical field, in particular to the preparation method and permanent magnetism of a kind of permanent-magnet material
Material.
Background technology
In recent years, it is very fast as the Trend of Permanent of representative using rare earth permanent-magnetic material.Found from the 1960s
Since first generation rare earth permanent-magnetic material, SmCo is successively developed5、Sm2Co17And Nd2Fe14Three generations's rare-earth permanent magnet such as B,
And the maximum magnetic energy product of rare-earth permanent magnet performance is represented from 20MGOe liftings to 59.6MGOe.The technique for preparing rare-earth permanent magnet
Generally include prior powder metallurgy technique for preparing sintered rare-earth permanent magnetic body and for preparing binding rare earth permanent magnet
M elt-spun overqu- enching.Wherein, the rare-earth permanent magnet prepared by prior powder metallurgy technique has excellent magnetic property and approached
The magnet structure of theoretical density, it is set to be obtained a wide range of applications in magneto field；And m elt-spun overqu- enching with its it is near eventually into
The characteristic of type also obtains important application.
At present, the research of rare earth permanent-magnetic material is concentrated mainly on new material system and new preparation method aspect.Wherein,
Metastable state Sm systems rare earth permanent magnet causes the research interest of people, this be primarily due to its have high intrinsic magnetic property and
Complicated structure transformation, makes people constantly be optimized from structure, composition, microstructure etc. to it.For example, Katter etc.
People uses the technique study of magnetron sputtering Sm5(Fe, Ti)17Compound, it is found that it has high-coercive force.Shenyang metal is used
The technique study of mechanical alloying SmFeTi serial rare-earth permanent-magnet materials.The neat rattan wise man of Chiba, Japan polytechnical university, which controls et al., to adopt
Sm is have studied with quick-quenching method5Fe17Compound, it is found that its coercivity can be up to 35kOe.
But due to Sm5Fe17Sm too high levels in permanent-magnet material, cause powder body material mobility poor, so as to cause most
End form into permanent-magnet material formability it is poor, to preparing block Sm5Fe17Permanent-magnet material bring certain difficulty.Moreover,
Conventional preparation Sm5Fe17The method of permanent-magnet material can only prepare amorphous Sm by rapid quenching5Fe17Permanent-magnet powder, then
To amorphous Sm5Fe17Permanent-magnet powder is heat-treated (sintering) so that magnetic, then the side by being bonded with binding agent is prepared
Formula come be prepared bulk Sm5Fe17Permanent-magnet material.Meanwhile Sm5Fe17The principal crystalline phase of permanent-magnet material is metastable
Sm5Fe17Phase, the Sm5Fe17Easily decomposed under phase high temperature, therefore, it is difficult to fine and close burning is prepared by traditional sintering process
Tie magnet.
The content of the invention
It is a primary object of the present invention to provide the preparation method and permanent-magnet material of a kind of permanent-magnet material, to improve permanent magnetism material
Expect the formability in preparation process.
To achieve these goals, according to an aspect of the invention, there is provided a kind of preparation method of permanent-magnet material, is somebody's turn to do
Preparation method comprises the following steps：A powder and B powder are prepared respectively, and the main component of A powder is SmxFe(1-x-y)My, wherein M
Selected from any of Ti, V, Mo and Co or a variety of, x scope is 40~50wt%, and y scope is 0~5wt%, and A powder
For the powder of crystalline state；The main component of B powder is RM, and wherein R is at least one rare earth element, M in Fe and Co at least
One kind, and R mass percent is 85~95% in B powder；A powder and B powder are mixed to get hybrid alloys powder, and it is mixed
The mass percent for closing B powder in alloy powder is 3~10wt%；Hot compression deformation is carried out to hybrid alloys powder to handle to formation
Permanent-magnet material with anisotropic crystal grain.
Further, the step of preparing A powder includes：Prepare main component and A powder identical amorphous powders；To amorphous
Powder is heat-treated to form A powder.
Further, the method that amorphous powder and B powder is prepared is rapid quenching method or gas atomization.
Further, the temperature of heat treatment is 600~900 DEG C, and the time of heat treatment is 0.5~2h.
Further, the step of hot compression deformation is handled includes：Carrying out hot-pressing processing to formation to hybrid alloys powder has
The blank of isotropic crystal grain；And thermal deformation field is carried out to blank to form permanent-magnet material.
Further, the step of hot-pressing processing includes：Hybrid alloys powder is put into hot-press equipment, and in vacuum or lazy
Property atmosphere under to applying the pressure that pressure is 100~300MPa on hybrid alloys powder；At the uniform velocity be warming up to 600~850 DEG C it is laggard
Row insulation；Release obtains blank after being cooled to normal temperature and pressure.
Further, the step of thermal deformation field includes：Blank is put into hot-press equipment, and in 600~800 DEG C of temperature
It is incubated under degree；Gradually pressure is applied pressure to blank reach 100~300MPa；Release obtains after being cooled to normal temperature and pressure
Permanent-magnet material.
Further, temperature of the temperature of hot compression deformation processing less than heat treatment.
Further, the temperature of hot compression deformation processing is lower than the temperature of heat treatment more than 50 DEG C.
Further, y scope is 0~3wt%.
Further, the particle size range of B powder is 30~150 μm.
Further, the particle size range of B powder is 50~120 μm.
Further, the mass percent of B powder is 5~10wt% in hybrid alloys powder.
According to an aspect of the invention, there is provided a kind of permanent-magnet material, permanent-magnet material permanent magnetism provided by the present invention
The preparation method of material is prepared.
Apply the technical scheme of the present invention, it is of the invention by the way that A powder and B powder are mixed to get into hybrid alloys powder, and
There is the characteristic of low melting point using B powder so that form permanent-magnet material after carrying out hot compression deformation processing to hybrid alloys powder
Formability, that is, improve formability of the permanent-magnet material in preparation process.Simultaneously as R is at least one rare earth in B powder
Element, and R is close with the Sm in A powder, so that the introducing of B powder will not reduce the magnetic property of formed permanent-magnet material,
And then make it that forming permanent-magnet material has preferable magnetic property.
Brief description of the drawings
The Figure of description for forming the part of the application is used for providing a further understanding of the present invention, and of the invention shows
Meaning property embodiment and its illustrate be used for explain the present invention, do not form inappropriate limitation of the present invention.In the accompanying drawings：
Fig. 1 shows the schematic diagram of the preparation method of the permanent-magnet material provided according to the embodiment of the present invention.
Embodiment
It should be noted that in the case where not conflicting, the feature in embodiment and embodiment in the application can phase
Mutually combination.Describe the application in detail below with reference to the accompanying drawings and in conjunction with the embodiments.
It should be noted that term used herein above is merely to describe embodiment, and be not intended to restricted root
According to the illustrative embodiments of the application.As used herein, unless the context clearly indicates otherwise, otherwise singulative
It is also intended to include plural form, additionally, it should be understood that, when in this manual using term "comprising" and/or " bag
Include " when, it indicates existing characteristics, step, operation, device, component and/or combinations thereof.
From background technology, formability of the existing permanent-magnet material in preparation process is poor.The present inventor's pin
Above mentioned problem is studied, it is proposed that a kind of preparation method of permanent-magnet material.As shown in figure 1, the preparation method is including following
Step：A powder and B powder are prepared respectively, and the main component of A powder is SmxFe(1-x-y)My, wherein M is in Ti, V, Mo and Co
It is any one or more, x scope is 40~50wt%, and y scope is 0~5wt%, and A powder is the powder of crystalline state；B powder
The main component at end is RM, and wherein R is at least one rare earth element, and M is selected from least one of Fe and Co, and R in B powder
Mass percent is 85~95%；A powder and B powder are mixed to get hybrid alloys powder, and B powder in hybrid alloys powder
Mass percent be 3~10wt%；Hybrid alloys powder progress hot compression deformation, which is handled to formation, has anisotropic crystalline substance
The permanent-magnet material of grain.
Above-mentioned preparation method has using B powder low by the way that A powder and B powder are mixed to get into hybrid alloys powder
The characteristic of fusing point so that the formability to forming permanent-magnet material after the progress hot compression deformation processing of hybrid alloys powder, that is, improve
Formability of the permanent-magnet material in preparation process.Simultaneously as R is at least one rare earth element in B powder, and R and A powder
In Sm it is close so that the introducing of B powder will not reduce the magnetic property of formed permanent-magnet material, and then to be formed forever
Magnetic material has preferable magnetic property.
The illustrative embodiments of the preparation method according to permanent-magnet material provided by the invention are described in more detail below.
However, these illustrative embodiments can be implemented by many different forms, and it should not be construed to be limited solely to this
In the embodiment that is illustrated.It should be appreciated that these embodiments are provided so that disclosure herein thoroughly and
Completely, and by the design of these illustrative embodiments those of ordinary skill in the art are fully conveyed to.
First, A powder and B powder are prepared respectively, and the main component of A powder is SmxFe(1-x-y)My, wherein M be selected from Ti, V,
Any of Mo and Co or a variety of, x scope is 40~50wt%, and y scope is 0~5wt%, and A powder is crystalline state
Powder；The main component of B powder is RM, and wherein R is at least one rare earth element, and M is selected from least one of Fe and Co, and B
R mass percent is 85~95% in powder.
The main component of above-mentioned A powder is SmFe bases, can add a certain amount of M (M=Ti, V, Mo, Co) wherein to change
The performances such as kind corrosion resistance.Wherein, M is preferably Co；M content y scope is 0~5wt.%, it is further preferable that y scope
For 0~3wt%, in y=0, it is SmFe binary to represent whole composition, and y content can not be more than 5wt.%, otherwise can significantly drop
The magnetic property of low A powder, preferably y scope is in the range of 3wt.%.And Sm content x scopes are somebody's turn to do between 40~50wt.%
Scope can ensure that the principal crystalline phase of A powder is Sm5Fe17Phase, and the scope is left, more SmFe occurs in material2、SmFe3
Grade crystalline phase, so as to cause the performance of A powder to deteriorate.By modifying ingredients and preparation technology, para-crystal Phase Proportion is set to exist
Within 5wt.%, so as to ensure that A powder has high magnetic characteristics.It should be noted that rare earth elements of the present invention are mainly Sm, but
It is unavoidably to contain the rare earth impurities such as Pr, Nd, and requires that the content of rare earth impurities is less than 1wt.%.
In above-mentioned B powder, R is preferably Ce, Nd, Pr, and more preferably R is Ce.Meanwhile R mass percent is 85 in B powder
~95%.By taking Ce as an example, when Ce content is within the scope of this, R and Fe easily forms the RM compounds of low melting point, so exists
At a temperature of follow-up hot compression deformation processing, RM compounds play wetting action between particles, so as to be advantageous to whole permanent magnetism material
The shaping of material；When Ce content range deviates the scope, deviation occurs for the fusing point that will result in RM compounds, so that RM
It is higher to play the temperature of wetting action that thawing occurs for compound, bigger difficulty is brought to preparation process, while can make preparation temperature
Degree improves, and ultimately results in principal crystalline phase crystal grain and grows up substantially, and formed permanent magnetic material performance is declined to a great extent.
Preferably, the step of preparing above-mentioned A powder be：Prepare main component and A powder identical amorphous powders；To amorphous
Powder is heat-treated to form A powder.The method that amorphous powder is prepared can be rapid quenching or gas atomization.When adopting
When preparing amorphous powder with rapid quenching, it is preferable that comprise the following steps：According to carrying out melting, fast after certain composition proportion
Quench, fast quenching process is carried out under Ar protective atmospheres, and injection pressure is 40~80kPa, and molten steel is sprayed onto with 30~80m/s rotations
On disk roller, amorphous powder is obtained after fast quenching.Wherein, preferably fast quenching roller speed is difficult in more than 30m/s, too low fast quenching wheel speed
Non crystalline structure needed for being formed, and it is easier to SmFe occur2, SmFe3Grade crystalline phase；And with the raising of wheel speed, on the one hand can be with
Non crystalline structure is effectively obtained, on the other hand can suppress the appearance of time crystalline phase, ensures the final high-performance for obtaining permanent-magnet material.
In the step of being heat-treated to above-mentioned amorphous powder, amorphous powder is heat-treated to by certain temperature and time
Make principal crystalline phase Sm5Fe17Separate out.Preferably, the temperature of heat treatment is 600~900 DEG C.If temperature is less than 600 DEG C, heat treatment
Effect is more weaker, and temperature is higher than 900 DEG C of decomposition that may result in principal crystalline phase.The time of heat treatment is to there is complete crystalline state
Sm5Fe17Principal crystalline phase is defined, it is preferable that heat treatment time is 0.5~2h.It should be noted that in order to avoid Sm is oxidized,
Whole heat treatment process is preferably carried out in the environment of Ar protections.Quickly quenched it should be noted that above-mentioned B powder can also use
Fire or gas atomization are prepared.
Then, A powder and B powder are mixed to get hybrid alloys powder, and in hybrid alloys powder B powder quality hundred
It is 3~10wt% to divide ratio.In the step, if the content of B powder is too low, wetting action, global formation performance boost are not had
Unobvious；If the amount of the powder containing B is too high to be deteriorated to overall performance.Therefore the scope of B powder is more excellent in 3~10wt.%
Elect 5~10wt.% as.Preferably, the granularity of B powder is in 30~150 μ ms.If the granularity of B powder is excessive, A powder
It is poor with the mixing uniformity of B powder；If the undersized of B powder, the preparation of B powder also brings some difficult.It is more excellent
Selection of land, the granularity of B powder is preferably 50~120 μm in the present invention.
Finally, hot compression deformation is carried out to hybrid alloys powder to handle to permanent magnetism material of the formation with anisotropic crystal grain
Material.Preferably, the step of hot compression deformation is handled includes：Hot-pressing processing to formation is carried out to hybrid alloys powder has isotropism
Crystal grain blank；And thermal deformation field is carried out to blank to form permanent-magnet material.
Wherein, the step of hot-pressing processing is preferably：Hybrid alloys powder is put into hot-press equipment, and in vacuum or inertia
To the pressure that application pressure is 100~300MPa on hybrid alloys powder under atmosphere；Carried out after being at the uniform velocity warming up to 600~850 DEG C
Insulation；Release obtains blank after being cooled to normal temperature and pressure.Now, obtaining blank has isotropic crystal grain.The blank
In preparation process, it is intended merely to make the material obtain preliminary densification, therefore, does not make Sm5Fe17Compound structure occurs to divide
In the case of solution, the blank of even compact can also be prepared by the method that discharge plasma sintering (SPS), electric heating sinter.
Preferably, the step of thermal deformation field includes：Blank is put into hot-press equipment, and in 600~800 DEG C of temperature
Under be incubated；Gradually pressure is applied pressure to blank reach 100~300MPa；Release obtains forever after being cooled to normal temperature and pressure
Magnetic material.In this step, a certain amount of thermal deformation field is key prepared by whole complete fine and close high performance permanent magnetic materialses, at this
During, sliding deformation growth occurs for the crystal grain of material under the short time, and material grains size is not occurred significantly
In the case of growing up, the crystal grain of material from the crystal grain of former isotropism, No yield point is transformed into columnar grain, and (its major axis is more than short
Axle), and be distributed each along stress direction, so that whole material magnetic moment orientation in magnetic history is uniform, and cause institute's shape
Performance into permanent-magnet material greatly improves.
Because the permanent-magnet powder of the crystalline state before the processing of above-mentioned hot compression deformation is to come after Overheating Treatment, therefore in order to protect
Demonstrate,prove the performance of final permanent-magnet material, it is preferable that the temperature of hot compression deformation processing shape process is less than the temperature of heat treatment process, hot pressing
Pressure in deformation process is preferably in 100~300MPa.It is further preferable that the temperature of hot compression deformation processing is than heat treatment
Temperature is low more than 50 DEG C.Further, since material therefor is the material of rich samarium, and in order to avoid the oxidation of material, whole hot compression deformation
Processing procedure preferably vacuum environment or be filled with Ar protection in the environment of carry out.
The preparation method of permanent-magnet material provided by the invention is further illustrated below in conjunction with embodiment.
Embodiment S1 to S10
Raw material composition is as shown in table 1 used by the preparation method for the permanent-magnet material that embodiment S1 to S10 is provided, the system
The specific process parameter of Preparation Method is as shown in table 2.The step of preparation method of lower permanent-magnet material is detailed below：
First, according to carry out obtaining after melting, fast quenching after certain component ratio proportioning (as shown in table 1) main component with
A powder identical amorphous powders, and amorphous powder is carried out to be heat-treated to principal crystalline phase Sm5Fe17Separate out, so as to obtain A powder；And
And according to acquisition B powder after progress melting, fast quenching after certain component ratio proportioning (as shown in table 1)；Wherein fast quenching process exists
Carried out under Ar protective atmospheres, injection pressure is 50kPa, and molten steel is sprayed onto with the disk roller of 40m/s rotations.
Then, it is a certain proportion of A powder and B powder is (as shown in table 1) well mixed, so as to obtain hybrid alloys powder
End.
Next, hybrid alloys powder is put into hot pressing die, hot pressing die is put into vacuum hot-pressing equipment, and protected
The vacuum of hot-press equipment is held in below 1Pa, while opens heating system and hydraulic system, and corrective action is in the pressure on mould
By force, then at the uniform velocity heated up from room temperature, at the desired temperature heat-insulation pressure keeping, release cooling after completion, obtain blank (i.e. hot pressing
The process of processing)；
Finally, blank is placed again into hot-press equipment, after being incubated under vacuo, opens hydraulic system, slowly apply
Pressure, make hot pressing blank that thermal deformation at the uniform velocity occur, slow cooling obtains permanent-magnet material (i.e. thermal deformation field after the completion of thermal deformation
Process).
Comparative example D1
The preparation method for the permanent-magnet material that this comparative example provides comprises the following steps：
First, according to melting, fast quenching is carried out after certain component ratio proportioning (as shown in table 1), wherein fast quenching process exists
Carried out under Ar protective atmospheres, injection pressure is 50kPa, molten steel is sprayed onto on the disk roller of 40m/s rotations, to be obtained after fast quenching
Amorphous permanent-magnet powder；
Then, amorphous permanent-magnet powder is carried out being heat-treated to principal crystalline phase Sm5Fe17Separate out (the technological parameter such as institute of table 2
Show), so as to obtain the permanent-magnet material of crystalline state.
Table 1
Table 2
As can be seen from Table 1 and Table 2, the remanent magnetism of S1~S10 sample, HCJ and maximum magnetic energy product are obvious big
Preferable magnetic property is achieved in the sample of D1 sample, therefore S1~S10, and the good moldability of S1~S10 sample is in D1
Sample.In addition, S6 and S10 sample, because granularity is thicker, uniformity is more poor in A powder and B powder mixed processes, makes
, the overall magnetic property of S6 and S10 sample is more relatively low.When the particle size range of B powder is in 50~120 μ ms, simultaneously
During the ratio mixing that the ratio of B powder is 5~10wt.% in hybrid alloys powder, the performance of resulting permanent-magnet material is best.
As can be seen from the above embodiments, the above-mentioned example of the present invention realizes following technique effect：The present invention is by by A
Powder and B powder are mixed to get hybrid alloys powder, and have the characteristic of low melting point using B powder so as to hybrid alloys powder
The formability of permanent-magnet material is formed after the progress hot compression deformation processing of end, that is, improves shaping of the permanent-magnet material in preparation process
Property.Simultaneously as R is at least one rare earth element in B powder, and R is close with the Sm in A powder, so that B powder draws
Enter to reduce the magnetic property of formed permanent-magnet material, and then make it that forming permanent-magnet material has preferable magnetic property.
The preferred embodiments of the present invention are these are only, are not intended to limit the invention, for those skilled in the art
For member, the present invention can have various modifications and variations.Any modification within the spirit and principles of the invention, being made,
Equivalent substitution, improvement etc., should be included in the scope of the protection.
Claims (14)
1. a kind of preparation method of permanent-magnet material, it is characterised in that the preparation method comprises the following steps：
A powder and B powder are prepared respectively, and the main component of the A powder is SmxFe(1-x-y)My, wherein M be selected from Ti, V, Mo and
Any of Co or a variety of, x scope are 40~50wt%, and y scope is 0~5wt%, and the A powder is crystalline state
Powder；The main component of the B powder is RM, and wherein R is at least one rare earth element, and M is selected from least one of Fe and Co,
And R mass percent is 85~95% in the B powder；
The A powder and the B powder are mixed to get hybrid alloys powder, and in the hybrid alloys powder B powder matter
Amount percentage is 3~10wt%；
Hot compression deformation is carried out to the hybrid alloys powder to handle to the permanent-magnet material of the formation with anisotropic crystal grain.
2. preparation method according to claim 1, it is characterised in that the step of preparing the A powder includes：
Prepare main component and the A powder identical amorphous powder；
The amorphous powder is heat-treated to form the A powder.
3. preparation method according to claim 2, it is characterised in that the amorphous powder and the B powder is prepared
Method be rapid quenching method or gas atomization.
4. preparation method according to claim 2, it is characterised in that the temperature of the heat treatment is 600~900 DEG C, institute
The time for stating heat treatment is 0.5~2h.
5. preparation method according to claim 2, it is characterised in that the step of hot compression deformation is handled includes：
Hot-pressing processing is carried out to the hybrid alloys powder to blank of the formation with isotropic crystal grain；And
Thermal deformation field is carried out to the blank to form the permanent-magnet material.
6. preparation method according to claim 5, it is characterised in that include the step of the hot-pressing processing：
The hybrid alloys powder is put into hot-press equipment, and in a vacuum or inert atmosphere on the hybrid alloys powder
Apply the pressure that pressure is 100~300MPa；
It is incubated after being at the uniform velocity warming up to 600~850 DEG C；
Release obtains the blank after being cooled to normal temperature and pressure.
7. preparation method according to claim 6, it is characterised in that include the step of the thermal deformation field：
The blank is put into the hot-press equipment, and is incubated at a temperature of 600~800 DEG C；
Gradually pressure is applied pressure to the blank reach 100~300MPa；
Release obtains the permanent-magnet material after being cooled to normal temperature and pressure.
8. preparation method according to claim 5, it is characterised in that the temperature of the hot compression deformation processing is less than the heat
The temperature of processing.
9. preparation method according to claim 8, it is characterised in that the temperature of hot compression deformation processing than the heat at
The temperature of reason is low more than 50 DEG C.
10. preparation method according to any one of claim 1 to 9, it is characterised in that the scope of the y be 0~
3wt%.
11. preparation method according to any one of claim 1 to 9, it is characterised in that the particle size range of the B powder
For 30~150 μm.
12. preparation method according to claim 11, it is characterised in that the particle size range of the B powder is 50~120 μ
m。
13. preparation method according to any one of claim 1 to 9, it is characterised in that B in the hybrid alloys powder
The mass percent of powder is 5~10wt%.
14. a kind of permanent-magnet material, it is characterised in that the permanent-magnet material is as the preparation any one of claim 1 to 13
Method is prepared.
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| CN113628822B (en) * | 2021-07-20 | 2023-07-18 | 华为技术有限公司 | SmFeN permanent magnet, preparation method thereof and motor |
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Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH03247703A (en) * | 1990-02-23 | 1991-11-05 | Seiko Epson Corp | Manufacture of permanent magnet |
| CN1818121A (en) * | 2005-02-07 | 2006-08-16 | Tdk株式会社 | Method for producing magnetostrictive element |
| CN101476055A (en) * | 2009-01-16 | 2009-07-08 | 北京工业大学 | Preparation of fully dense massive anisotropic nanocrystalline SmCo5 magnet |
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2014
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Patent Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH03247703A (en) * | 1990-02-23 | 1991-11-05 | Seiko Epson Corp | Manufacture of permanent magnet |
| CN1818121A (en) * | 2005-02-07 | 2006-08-16 | Tdk株式会社 | Method for producing magnetostrictive element |
| CN101476055A (en) * | 2009-01-16 | 2009-07-08 | 北京工业大学 | Preparation of fully dense massive anisotropic nanocrystalline SmCo5 magnet |
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