CN105957675B - A kind of preparation method of rare earth permanent-magnetic material - Google Patents
A kind of preparation method of rare earth permanent-magnetic material Download PDFInfo
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- CN105957675B CN105957675B CN201610405246.6A CN201610405246A CN105957675B CN 105957675 B CN105957675 B CN 105957675B CN 201610405246 A CN201610405246 A CN 201610405246A CN 105957675 B CN105957675 B CN 105957675B
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
- B22F3/12—Both compacting and sintering
- B22F3/14—Both compacting and sintering simultaneously
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
- B22F3/24—After-treatment of workpieces or articles
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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
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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
- H01F1/06—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 in the form of particles, e.g. powder
- H01F1/08—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 in the form of particles, e.g. powder pressed, sintered, or bound together
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Abstract
The invention discloses a kind of preparation method of rare earth permanent-magnetic material.The Nd Fe B alloys powder that it is used, neodymium iron boron magnetic body is prepared by mould pressing process twice in succession；Alignment magnetic field need to be applied in one-step mould, obtain anisotropic neodymium iron boron green compact, pressurizeed in secondary mould pressing by heating, obtain the neodymium iron boron magnetic body of densification, and the size for being closely sized to final products of magnet；And magnet magnetic property is improved by special Technology for Heating Processing.The beneficial effects of the invention are as follows：Densification temperature is low, can suppress crystal grain and grow up, and crystal grain is tiny compared with sintered magnet, and magnetic property is high；Using mould pressing process, for magnet size close to the size of final finished, stock utilization is far above conventional sintering neodymium iron boron magnetic body；Special rapidly quenched magnetic powder is not needed, it is not necessary to which thermal deformation, technique is simple, and production efficiency is high, and production cost is far below hot pressing/heat distortion magnet；Magnetic property is high, and maximum magnetic energy product reaches 200kJm‑3More than, far above Agglutinate neodymium-iron-boron magnet.
Description
Technical field
The present invention relates to magnetic material correlative technology field, refers in particular to a kind of preparation method of rare earth permanent-magnetic material.
Background technology
Since the eighties in last century, neodymium iron boron magnetic body came out, because its excellent magnetic property is rapidly in electronics, communication, friendship
The fields such as logical transport, automation, medical treatment and new energy are widely applied.Up to the present, Nd-Fe-B permanent magnet material is comprehensive
The most excellent permanent-magnet material of magnetic property is closed, " magnetic king " is described as, there is important meaning to device miniaturization, integrated and high efficiency
Justice.
By preparation method point, neodymium iron boron magnetic body is broadly divided into sintering, bonding, hot pressing/heat distortion magnet, wherein to sinter neodymium
Iron boron dosage is maximum.The preparation technology of Sintered NdFeB magnet mainly obtains Nd Fe B alloys using strip casting, then will
Alloy grinds to obtain 3-5 μm of powder, and powder is put into oriented moulding in magnetic field obtains green compact, by green compact at 1040-1100 DEG C
Temperature sinters to obtain sintered NdFeB blank, and blank finally gives sintered NdFeB product through over mechanical processing again.Sintered magnet
Major advantage be magnetic property height, the maximum magnetic energy product of general commercial magnet is typically in 200-400kJm-3, Japanese NEOMAX companies
Laboratory level is up to 474kJm-3, this is also the highest record of magnetic material so far.And sintered NdFeB is main
Shortcoming is that stock utilization is low.Because in addition to small part larger product can be molded by monolithic and is made, other
Most of sintered NdFeB product is required for being machined, and compound material utilization rate is about 66%, and for some thin slices and different
Stock utilization is less than 50% for shape product.In addition, the sintering shrinkage of Sintered NdFeB magnet is about 30%, green compact in addition
Density inhomogeneity, so the strain cracking of sintered NdFeB is inevitable, thus Sintered NdFeB magnet improves material
Expect that the space of utilization rate is also very big.
The nanocrystalline fast quenching neodymium-iron-boron that it is about 200 μm by granularity that the preparation technology of hot pressing/thermal deformation neodymium iron boron magnetic body, which is,
Powder obtains isotropic magnet in 500-600 DEG C of hot pressing densification, then passes through thermal deformation at 850-950 DEG C again and obtains anisotropy
Neodymium iron boron magnetic body.In general, the HCJ of hot pressing/heat distortion magnet is more slightly higher than sintered NdFeB, because
The temperature that hot pressing/thermal deformation uses is lower than sintering temperature, and the time is short, so crystal grain is more tiny.And hot pressing/heat distortion magnet can
To realize dead size or connect near-net-shape, while it can also effectively suppress the strain cracking of magnet, so material use
Rate is higher.The major defect of hot pressing/heat distortion magnet is cost height.Nanocrystalline rapidly quenched magnetic powder price first used in hot pressing compared with
It is high；Thermal deformation technique production efficiency is very low simultaneously, so production cost is high.
Agglutinate neodymium-iron-boron magnet is also to be prepared using nanocrystalline rapidly quenched magnetic powder, will by adding a certain proportion of bonding agent
The magnet that magnetic is bonded to.The stock utilization of Agglutinate neodymium-iron-boron magnet is very high, close to 100%, and can realize special-shaped production
The preparation of product.The disadvantage of Agglutinate neodymium-iron-boron is that magnetic property is low, and Agglutinate neodymium-iron-boron magnet magnetic energy product is mostly in 60-90kJm-3。
In summary, it is that magnetic is cheap the advantages of Sintered NdFeB magnet, simple production process, efficiency high, cost is low；Lack
Point is that sintering temperature is high (more than 1040 DEG C), and magnet crystal grain is easily grown up, and stock utilization is low, yielding cracking.Hot pressing/thermal change
The advantages of shape magnet is that magnet crystal grain is tiny, and stock utilization is high；Shortcoming is magnetic (the special quenched powder of hot pressing/thermal deformation) price
Height, thermal deformation efficiency is low, and cost is high.The advantages of Agglutinate neodymium-iron-boron magnet is stock utilization height, it is possible to achieve special-shaped magnet
Production；Major defect is that magnetic property is low, and Agglutinate neodymium-iron-boron magnet magnetic energy product is mostly in 60-90kJm-3。
The content of the invention
The present invention is above-mentioned in order to overcome the shortcomings of to exist in the prior art, there is provided a kind of magnetic property height and production cost
The preparation method of low rare earth permanent-magnetic material.
To achieve these goals, the present invention uses following technical scheme：
A kind of preparation method of rare earth permanent-magnetic material, comprises the following steps：
(1) magnetic prepares：Nd Fe B alloys is prepared using vacuum melting furnace, entered afterwards using the quick-fried method of hydrogen or mechanical crushing method
Row coarse crushing, then obtained Nd Fe B alloys powder is ground using air-flow grinding process；
(2) one-step mould：Powder is put into compression molding in the mould of one-step mould, while 1T's is applied more than to magnetic
Magnetic field；
(3) secondary mould pressing：The product of one-step mould is inserted in the mould of secondary mould pressing, in vacuum or inert gas shielding
Under, after the product heating of one-step mould, then apply pressure and carry out secondary mould pressing, the magnet being densified；
(4) it is heat-treated：Magnet by secondary mould pressing is inserted in vacuum drying oven and is heat-treated, including at least passivation crystal grain
The homogenization heat treatment of wedge angle and the tempering heat treatment of optimization crystal boundary distributed mutually.
In the present invention, the Nd Fe B alloys powder of use, neodymium iron boron magnetic body is prepared by mould pressing process twice in succession；One
Alignment magnetic field need to be applied during secondary molding, obtain anisotropic neodymium iron boron green compact, pressurizeed, obtained by heating in secondary mould pressing
Fine and close neodymium iron boron magnetic body, and the size for being closely sized to final products of magnet；Due to the magnet magnetic obtained after secondary mould pressing
Performance is very low, so needing to improve magnet magnetic property by special Technology for Heating Processing.Using mould pressing process, product is close to most
The size of finally finished, stock utilization are high；Without thermal deformation, production efficiency is high, so cost is far below hot pressing/thermal deformation magnetic
Body；Magnetic property reaches 200kJm-3More than, far above Agglutinate neodymium-iron-boron magnet.
Preferably, in step (1), used Nd Fe B alloys powder is that micron is brilliant or single crystal grain, grinding are made
The Nd Fe B alloys powder average particle size range obtained is controlled at 1-10 μm.Used neodymium iron boron powder is micron crystalline substance, monocrystalline
Grain, so being prepared using conventional vacuum smelting furnace, magnetic cost is low.
Preferably, in step (1), after Nd Fe B alloys powder is made in grinding, rich rare earth alloy powder is added,
The constituent of rich rare earth alloy powder is：One or more in Rare Earth Elements of Praseodymium, neodymium, dysprosium, terbium, other non-rare earths are
One or more in aluminium, copper, gallium, iron, and the mass percent sum of Rare Earth Elements of Praseodymium, neodymium, dysprosium, terbium is more than 50%；It is rich dilute
The adding proportion of native alloy powder is the 0-30% of Nd Fe B alloys powder.The temperature of secondary mould pressing can be so reduced, is helped
Grown up in suppression crystal grain and extend die life, while improve production efficiency.
Preferably, described rich rare earth alloy powder average particle size range is controlled at 0.3-4 μm.It is set to be closed with neodymium iron boron
The average grain diameter at bronze end is close, suppresses crystal grain and grows up.
Preferably, in step (3), the mould of secondary mould pressing be prepared according to needed for final product geomery and
Design, in step (2), the mould of one-step mould is designed according to the mould of secondary mould pressing.So design causes
During using mould pressing process, for product close to the size of final finished, stock utilization is high.
Preferably, in step (3), the product of one-step mould is heated to 550-1000 DEG C, hot pressing time 1-30
Minute, the pressure for then applying 1-500MPa carries out secondary mould pressing.Because the heating-up temperature of secondary mould pressing is far below sintering temperature,
So magnet crystal grain is more tiny than conventional sintering magnet, magnetic property is high.
Preferably, in step (4), the homogenizing heat treatment for being passivated crystal grain wedge angle is as follows：Using 700-1000
DEG C insulation 1-15 hours；The tempering heat treatment process for optimizing crystal boundary distributed mutually is as follows：Using 400-650 DEG C of insulation 1-6 hour.It is logical
Above-mentioned special Technology for Heating Processing is crossed to improve magnet magnetic property so that magnetic property reaches 200kJm-3More than, far above bonding neodymium
Iron boron magnet, this is also the critical process that commercial value magnet can be made in the technique.
Preferably, in step (4) and then increase destressing handling process：It is small using 150-350 DEG C of insulation 0.5-3
When.So it is favorably improved the magnetic property and bending strength of magnet.
The beneficial effects of the invention are as follows：
1st, densification temperature is low, can suppress crystal grain and grow up, and crystal grain is tiny compared with sintered magnet, and magnetic property is high；Pass through micro- knot
Structure is observed it can be found that magnet crystallite dimension produced by the present invention is tiny, is 1-5 μm, the average grain with Nd Fe B alloys powder
Footpath is close, and the phenomenon that obvious crystal grain is grown up does not occur in secondary mould pressing densification process；
2nd, using mould pressing process, for magnet size close to the size of final finished, stock utilization is far above conventional sintering neodymium
Iron boron magnet；
3rd, special rapidly quenched magnetic powder is not needed, it is not necessary to which thermal deformation, technique is simple, and production efficiency is high, and production cost is far below
Hot pressing/heat distortion magnet；
4th, magnetic property is high, and maximum magnetic energy product reaches 200kJm-3More than, far above Agglutinate neodymium-iron-boron magnet.
Embodiment
With reference to embodiment, the present invention will be further described.
Embodiment 1：
1st, Nd Fe B alloys is prepared using vacuum melting furnace, is by master alloying composition using rapid hardening slice technique
Nd26.25Pr8.75Fe64B1 (weight/mass percentage composition) alloy is laminated；Then utilize the quick-fried method of hydrogen and air-flow grinding process will
The powder that average grain diameter is 3.5 μm is made in rapid hardening thin slice；
2nd, 1.5T magnetic field is applied, one-step mould obtains blank dimension R8.1 × R3.6 × 10, blank weight 29.97g；
3rd, the blank for obtaining one-step mould is placed in the mould of secondary mould pressing, and the mould of secondary mould pressing is closed in one
Space, be first evacuated to 8 × 10-3Pa, then applying argon gas are to 8 × 104Pa, 780 DEG C are then heated to, pressurizeed along the direction of thickness 10
200MPa, pressurize are cooled down after 6 minutes and taken out；
4th, the magnet by secondary mould pressing is inserted and secondary heat treatment is carried out in vacuum drying oven, it is small that 900 DEG C of insulations 8 are respectively adopted
When and 500 DEG C insulation 4 hours technique hot pressing blank is heat-treated, be made specification be R8.1 × R3.6 × 5.3 magnet,
Stock utilization 100%, no arrisdefect cracking, yield rate 100%.
Embodiment 2：
1st, using the magnet in embodiment 1,5% is added in obtained Nd Fe B alloys powder after step 1
Nd70Cu30 (weight/mass percentage composition) rich rare earth alloy powder, the wherein average grain diameter of neodymium copper alloy powder are 3 μm；
2nd, in step 3, hot pressing temperature is 680 DEG C, and other techniques are same as Example 1.
Embodiment 3：
By the magnet of embodiment 2 after the heat treatment by step 4, carry out at the destressing tempering of 340 DEG C × 2.5 hours
Reason.
Comparative example 1：
Magnetic oriented moulding, green compact specification 43.56 × 39.6 × 29.82, by conventional sintering work are criticized together using with embodiment 1
Skill is in 1068 DEG C of sintering densifications, technique heat treatment same as Example 1.
Blank specification 33 × 30 × 2 is sintered, wire cutting adds into arc mill inside and outside the black-film of R8.1 × R3.6 × 5.5 and progress
Work, finally gives the magnet of R8.1 × R3.6 × 5.3, stock utilization 76%, and 0.3 yuan of expense of machining/only, process
In have arrisdefect, yield rate 98%.
Embodiment 1, embodiment 2, embodiment 3 and preparation technology and the product performance contrast of comparative example 1 are shown in Table 1.Embodiment 2
Average grain size with magnet after molding densification in embodiment 3 is about 3.6 μm, is approached with the granularity of magnetic；Embodiment 1
Middle magnet average grain size is 3.8 μm, and crystal grain is grown up very small in hot press moulding densification process.The magnet of comparative example 1
Average grain size is about 5.5 μm, and this illustrates that the technology has positive effect to crystal grain refinement.Show the preparation work using the present invention
Skill can significantly reduce magnet crystallite dimension, and Grain-Boundary Phase is more evenly distributed.Due to the magnet production prepared using the invention
Product appearance and size can meet portions of client requirement without processing, so stock utilization is wanted close to 100% for tolerance
Higher product is asked to need simply to be processed.The product prepared using the technology is better than traditional work in terms of machining property
Skill, so yield rate has been lifted, it might even be possible to reach 100%.
Table 1
| Densification temperature | Average grain size | Stock utilization | Machining is taken | Yield rate | |
| Embodiment 1 | 780℃ | 3.8μm | ~100% | 0 | 99% |
| Embodiment 2 | 680℃ | 3.6μm | ~100% | 0 | ~100% |
| Embodiment 3 | 680℃ | 3.6μm | ~100% | 0 | 100% |
| Comparative example 1 | 1068℃ | 5.5μm | 76% | 0.3 yuan/only | 97% |
The neodymium iron boron magnetic body items magnetic property index prepared using different process is shown in Table 2.It is made using secondary mould pressing technique
Neodymium iron boron magnetic body magnetic property, particularly Hcj is very low, does not reach the requirement of commercial magnet, it is necessary to carries out appropriate heat treatment；Two
The Technology for Heating Processing of secondary molding magnet has significantly different with traditional neodymium iron boron magnetic body Technology for Heating Processing, it is necessary first to is homogenized
Then heat treatment optimizes the tempering heat treatment of grain boundary structure to be passivated crystal grain wedge angle.Pass through magnet after above-mentioned heat treatment
Magnetic property have and be obviously improved, it is close with Sintered NdFeB magnet, or even there is part index number to be better than Sintered NdFeB magnet, far
Higher than Agglutinate neodymium-iron-boron.
In example 2, by adding rich rare earth alloy powder, magnet densification temperature can be reduced, so as to further
Crystal grain thinning, magnet Hcj also improve.
In embodiment 3, destressing processing can further improve magnet magnetic property, particularly magnet squareness (Hk/
Hcj), be advantageous to improve the maximum magnetic energy product of magnet and reduce the irreversible loss of flux of magnet.
Table 2
From above-mentioned Tables 1 and 2 it was found from the comparison of embodiment 1, embodiment 2, embodiment 3 and comparative example 1, the present invention passes through
The rare earth permanent-magnetic material that crystal grain is tiny, cost is cheap can be made in hot pressed sintering neodymium iron boron green compact.
Claims (6)
1. a kind of preparation method of rare earth permanent-magnetic material, it is characterized in that, comprise the following steps：
（1）Magnetic prepares：Nd Fe B alloys is prepared using vacuum melting furnace, carried out afterwards using the quick-fried method of hydrogen or mechanical crushing method thick
It is broken, then obtained Nd Fe B alloys powder is ground using air-flow grinding process；After Nd Fe B alloys powder is made in grinding,
Rich rare earth alloy powder is added, the constituent of rich rare earth alloy powder is：One kind or more in Rare Earth Elements of Praseodymium, neodymium, dysprosium, terbium
Kind, other non-rare earths are the one or more in aluminium, copper, gallium, iron, and the quality percentage of Rare Earth Elements of Praseodymium, neodymium, dysprosium, terbium
It is more than 50% than sum；The adding proportion of rich rare earth alloy powder is the 0-30% of Nd Fe B alloys powder；
（2）One-step mould：Powder is put into compression molding in the mould of one-step mould, while 1T magnetic is applied more than to magnetic
；
（3）Secondary mould pressing：The product of one-step mould is inserted in the mould of secondary mould pressing, under vacuum or inert gas shielding,
The product of one-step mould is heated to 550-1000 DEG C, hot pressing time is 1-30 minutes, and the pressure for then applying 1-500MPa is entered
Row secondary mould pressing, the magnet being densified；
（4）Heat treatment：Magnet by secondary mould pressing is inserted in vacuum drying oven and is heat-treated, including at least passivation crystal grain wedge angle
Homogenization heat treatment and optimization crystal boundary distributed mutually tempering heat treatment.
2. a kind of preparation method of rare earth permanent-magnetic material according to claim 1, it is characterized in that, in step（1）In, adopted
Nd Fe B alloys powder is that micron is brilliant or single crystal grain, Nd Fe B alloys powder average particle size range made from grinding control
At 1-10 μm.
3. a kind of preparation method of rare earth permanent-magnetic material according to claim 1, it is characterized in that, described rich rare earth alloy
Powder average particle size scope control is at 0.3-4 μm.
4. a kind of preparation method of rare earth permanent-magnetic material according to claim 1, it is characterized in that, in step（3）In, it is secondary
The mould of molding is to prepare the geomery of product according to needed for final and design, in step（2）In, the mould of one-step mould
It is to be designed according to the mould of secondary mould pressing.
5. a kind of preparation method of rare earth permanent-magnetic material according to claim 1, it is characterized in that, in step（4）In, passivation
The homogenizing heat treatment of crystal grain wedge angle is as follows：Using 700-1000 DEG C of insulation 1-15 hour；Optimize returning for crystal boundary distributed mutually
Burning hot handling process is as follows：Using 400-650 DEG C of insulation 1-6 hour.
6. a kind of preparation method of rare earth permanent-magnetic material according to claim 1, it is characterized in that, in step（4）And then
Increase destressing handling process：Using 150-350 DEG C of insulation 0.5-3 hour.
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| PCT/CN2016/089872 WO2017210957A1 (en) | 2016-06-08 | 2016-07-13 | Method for manufacturing rare-earth permanent magnetic material |
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| CN108417378A (en) * | 2018-03-30 | 2018-08-17 | 严高林 | A kind of neodymium iron boron magnetic body and preparation method thereof containing dysprosium |
| CN110656315A (en) * | 2019-10-28 | 2020-01-07 | 华南理工大学 | Method for improving coercive force and wear-resistant and corrosion-resistant performance of neodymium iron boron magnet |
| CN113096949B (en) * | 2021-04-07 | 2022-12-27 | 重庆科技学院 | Preparation method of compact soft magnetic composite iron core material and soft magnetic composite material |
Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN103123843A (en) * | 2011-11-21 | 2013-05-29 | 中国科学院宁波材料技术与工程研究所 | Preparation method for fine grain anisotropy densified neodymium iron boron permanent magnet |
| CN103680918A (en) * | 2013-12-11 | 2014-03-26 | 烟台正海磁性材料股份有限公司 | Method for preparing high-coercivity magnet |
| WO2014103546A1 (en) * | 2012-12-25 | 2014-07-03 | トヨタ自動車株式会社 | Process for producing rare-earth magnet |
| CN104269238A (en) * | 2014-09-30 | 2015-01-07 | 宁波科田磁业有限公司 | High-performance sintered neodymium-iron-boron magnet and preparation method |
| CN105118649A (en) * | 2015-06-18 | 2015-12-02 | 浙江东阳东磁稀土有限公司 | Method for improving grain boundary phase of neodymium iron boron |
Family Cites Families (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1696324A (en) * | 2005-05-18 | 2005-11-16 | 西北有色金属研究院 | Heat-resistant Nd-Fe-B alloys material with high application temperature, and preparation method |
| CN103594243B (en) * | 2013-11-20 | 2016-03-30 | 宁波科田磁业有限公司 | Prevent the manufacture method that Sintered NdFeB magnet ftractures |
| JP2015225880A (en) * | 2014-05-26 | 2015-12-14 | 大同特殊鋼株式会社 | Sintered magnet manufacturing method |
| CN104851544B (en) * | 2015-05-21 | 2017-01-18 | 新昌县辰逸服饰有限公司 | Production method for low-energy-consumption neodymium-iron-boron magnetic material |
| CN105225782A (en) * | 2015-07-31 | 2016-01-06 | 浙江东阳东磁稀土有限公司 | A kind of Sintered NdFeB magnet without heavy rare earth and preparation method thereof |
-
2016
- 2016-06-08 CN CN201610405246.6A patent/CN105957675B/en active Active
- 2016-07-13 WO PCT/CN2016/089872 patent/WO2017210957A1/en active Application Filing
Patent Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN103123843A (en) * | 2011-11-21 | 2013-05-29 | 中国科学院宁波材料技术与工程研究所 | Preparation method for fine grain anisotropy densified neodymium iron boron permanent magnet |
| WO2014103546A1 (en) * | 2012-12-25 | 2014-07-03 | トヨタ自動車株式会社 | Process for producing rare-earth magnet |
| CN103680918A (en) * | 2013-12-11 | 2014-03-26 | 烟台正海磁性材料股份有限公司 | Method for preparing high-coercivity magnet |
| CN104269238A (en) * | 2014-09-30 | 2015-01-07 | 宁波科田磁业有限公司 | High-performance sintered neodymium-iron-boron magnet and preparation method |
| CN105118649A (en) * | 2015-06-18 | 2015-12-02 | 浙江东阳东磁稀土有限公司 | Method for improving grain boundary phase of neodymium iron boron |
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| CN105957675A (en) | 2016-09-21 |
| WO2017210957A1 (en) | 2017-12-14 |
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