CN105845303A - Preparation method of sintered Nd-Fe-B magnet with high performance - Google Patents
Preparation method of sintered Nd-Fe-B magnet with high performance Download PDFInfo
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- CN105845303A CN105845303A CN201610012242.1A CN201610012242A CN105845303A CN 105845303 A CN105845303 A CN 105845303A CN 201610012242 A CN201610012242 A CN 201610012242A CN 105845303 A CN105845303 A CN 105845303A
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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
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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
- B22F3/10—Sintering only
- B22F3/1017—Multiple heating or additional steps
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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
- B22F3/16—Both compacting and sintering in successive or repeated steps
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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
- B22F9/00—Making metallic powder or suspensions thereof
- B22F9/02—Making metallic powder or suspensions thereof using physical processes
- B22F9/04—Making metallic powder or suspensions thereof using physical processes starting from solid material, e.g. by crushing, grinding or milling
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Abstract
The invention discloses a preparation method of a sintered Nd-Fe-B magnet with high performance. The preparation method comprises the following steps of (a) preparing magnet alloy from alloy A and alloy B to obtain a casting sheet; (b) smashing and milling the casting sheet to obtain alloy micro powder, wherein the smashing and milling comprises two steps of rough powder preparation and micro powder preparation which are carried out successively; (c) pressing and forming the alloy micro powder, wherein the alloy micro powder is pressed and formed in an environment where the oxide content is less than 1,000ppm to obtain a blank; and (d) sintering the blank, wherein the blank is subjected to sintering and aging, wherein the constituent of the magnet alloy is R<x>M<y>B<z>Fe<residual>, and in micro powder preparation, the alloy micro powder is obtained by high-pressure water jet ultrafine smashing. According to the scheme, two constituent materials are mixed, cerium is mainly distributed in a centralized manner in a main phase of a crystal grain and is less distributed at the boundary of the crystal gain, the reduction of coercivity of cerium is greatly reduced by improving such a microstructure, so that the magnet with higher coercivity and low cost can be fabricated.
Description
Technical field
The present invention relates to the preparation method of a kind of permanent magnet, the preparation method of a kind of performance Nd Fe B sintered magnet.
Background technology
Neodymium iron boron magnetic body, the intermetallic compound being mainly made up of with ferrum, boron rare-earth element R.R be mainly neodymium or neodymium and other
The combination of rare earth element, the most also replaces part ferrum with elements such as cobalt, aluminum, vanadium.It is broadly divided into sintered NdFeB and bonding neodymium ferrum
Boron two kinds, Agglutinate neodymium-iron-boron all directions are all magnetic, corrosion-resistant；And sintered NdFeB is because of perishable, surface needs coating, one
As have zinc-plated, nickel, zinc electroplating bath, environmental protection nickel, ambrose alloy nickel, environmental protection ambrose alloy nickel etc..And sintered NdFeB typically divide axial charging with
Radial magnetizing, determines according to required work surface.
Nd-Fe-B permanent magnet material is the permanent magnet material based on intermetallic compound RE2FE14B.Be mainly composed of rare earth (RE),
Ferrum (Fe), boron (B).Different performance can other be dilute with part dysprosium (Dy), praseodymium (Pr) etc. in order to obtain for its middle rare earth ND
Earth metal substitutes, and ferrum also can be substituted by other metal parts such as cobalt (Co), aluminum (Al), and the content of boron is less, but to shape
Becoming tetragonal structure intermetallic compound to play an important role, the compound made has high saturation and magnetic intensity, and high single shaft is each
Anisotropy and high Curie temperature.
Neodymium iron boron magnetic body is by a kind of new permanent-magnet of Contemporary Japanese scientist Zuo Chuan true man invention, and November 29 nineteen eighty-three
In metal academic discussion, SUMITOMO CHEMICAL particulate metal company neodymium, ferrum, the manufacture of boron permanent magnet material are proposed at first.
It is main by neodymium, ferrum, three kinds of elementary composition alloy magnets of boron, is the permanent magnet that present magnetic is the strongest, because neodymium atom is
Flat, electron cloud limited, make iron atom to offset, thus form constant magnetic force.
Neodymium iron boron magnetic body has the strongest magnetocrystalline anisotropy and the highest saturation magnetization.In permanent magnet material, sintered Nd-Fe-B
Magnet performance is the highest, maximum magnetic energy product (BH) max=360kJ/m3 of commercial product, but the Curie temperature of this magnet relatively low (314 DEG C),
Temperature stability and corrosion resistance are poor, limit and use at relatively high temperatures, and need as a rule to use protective coating.
The manufacturing process of neodymium iron boron magnetic body has powder metallurgic method and melt-quenching method.Because magnetic property is excellent, Nd-Fe-B type magnet obtains
It is widely applied, is mainly used in motor, electromotor, acoustic wave transducer, various sensor, medical apparatus and instruments and magnetic machinery etc..
Along with the development of sintered NdFeB technology, and the day by day fierce market competition, people are for LREE cerium Ce
Application gradually increase.By the interpolation of cerium, replace the neodymium element in sintered NdFeB, thus form the sintered NdFeB containing cerium.
Owing to the price comparison of Ce elements is low, by this replacement, greatly reduce the cost of magnet.Current this method is at low side
Field application is more.At a temperature of 295K, saturated pole intensity Js=1.17T of Ce2Fe14B, anisotropy field
HA=2069.6kA/m, and saturated pole intensity Js=1.60T of Nd2Fe14B, anisotropy field HA=5810.0kA/m, so
When using cerium Ce to substitute neodymium Nd, magnetic property can reduce, and remanent magnetism Br has a reduction of slight amplitude, but the meeting of coercivity H j
Occur significantly reduce, so containing cerium the general coercivity of sintered NdFeB can ratio relatively low, the most most in the case of, contain
The magnet of cerium is N material (Hcj >=960kA/m) of low-coercivity.Simultaneously because the easily oxidizable of cerium, also can increase to preparation process
The most more difficulty.
Summary of the invention
For solving the problems referred to above, the invention discloses the preparation method of a kind of performance Nd Fe B sintered magnet, by two kinds of compositions
Material mixing, the distribution of cerium is concentrated mainly in the principal phase of crystal grain, and is distributed in the grain boundaries of crystal grain less, by this micro-
See the improvement of structure, substantially reduce cerium to coercitive reduction, such that it is able to prepare the magnet of the low cost of more high-coercive force.
The preparation method of performance Nd Fe B sintered magnet disclosed by the invention, comprises the steps, a, by alloy A and alloy
B prepares magnet alloy, obtains slab；B, slab obtain alloy powder through broken powder process, and broken powder process includes that priority is carried out
Two stages prepared by coarse powder preparation and micropowder；C, compressing: alloy powder is pressed in the oxygen content environment less than 1000ppm
The type of making obtains base substrate；D, sintering: base substrate is sintered, timeliness；
Wherein magnet alloy consist of RxMyBzFeSurplus, R is to comprise one or more in La, Ce, Pr, Nd, Gd, Ho, Dy,
R total mass fraction be x, M be one or more in Co, Al, Cu, Nb, Zr, Ga, M total mass fraction is y,
X=28～32wt%, y=0～2wt%, z=0.9～1.1wt%；
Micropowder is prepared as preparing alloy powder with fine Comminuting Micawith High Pressure Water Jet, and fine Comminuting Micawith High Pressure Water Jet is to use to be oppositely arranged
Injector head injection 15-25MPa high pressure water impact coarse powder obtain.During operation, powder can add in water, it is also possible at height
Setting-out liquidate intersection add.Water under high pressure can be the pulsing jet of 15-60Hz.
A kind of improvement of the preparation method of performance Nd Fe B sintered magnet disclosed by the invention, alloy A consists of
Cex1Hoy1M1z1Bn1FeSurplus, wherein x1=28～31wt%, y1=0～3wt%, z1=0～2wt%, n1=0.9～1.1wt%, M1 is for adding
Element, for one or more in Co, Al, Cu, Nb, Zr.
A kind of improvement of the preparation method of performance Nd Fe B sintered magnet disclosed by the invention, alloy B consists of R ＇x2By2M2z2FeSurplus, wherein x2=28～35wt%, y2=0.9～1.1wt%, z2=0～2wt%, R ＇ be rare earth element nd, Pr, Gd,
One or more in Ho, Dy, M2 is one or more in Co, Al, Cu, Nb, Zr, Ga.
A kind of improvement of the preparation method of performance Nd Fe B sintered magnet disclosed by the invention, the particle mean size that coarse powder prepares
After coarse powder for 50-2000 μm, the alloy powder of the particle mean size 2-4 μm that described micropowder prepares.
A kind of improvement of the preparation method of performance Nd Fe B sintered magnet disclosed by the invention, being prepared as with air-flow pulverizing of micropowder
(fine Comminuting Micawith High Pressure Water Jet technology, can improve capacity usage ratio, it is to avoid occur raising for broken or fine Comminuting Micawith High Pressure Water Jet
Dirt, reduces equipment requirements, and the feature of environmental protection is more preferable, reduces material loss) prepare.
A kind of improvement of the preparation method of performance Nd Fe B sintered magnet disclosed by the invention, also includes accounting for total matter in magnet composition
The titanium elements of amount 0.1～0.5wt%.
A kind of improvement of the preparation method of performance Nd Fe B sintered magnet disclosed by the invention, titanium elements be after slab powder process with
After the addition mixing of titanium valve form, row powder molds base again, and wherein the particle mean size of titanium valve is 2-50 μm.By adopting in this programme
The mode in micropowder obtained by slab is added to, it is achieved the crystal boundary of titanium elements titanium elements in magnet adds in order to titanium valve mixing,
Make titanium elements be distributed mainly on crystal boundary, improve the structure of crystal boundary, refined crystal grain so that coercivity is improved, with
Time titanium elements also improve the mechanical property of crystal boundary richness neodymium phase, it is suppressed that the generation of crackle and extension, so the fragility of magnet obtains
Improve.
A kind of improvement of the preparation method of performance Nd Fe B sintered magnet disclosed by the invention, powder molds alloy powder before base
All cross the screening of 100-300 mesh sieve.
A kind of improvement of the preparation method of performance Nd Fe B sintered magnet disclosed by the invention, sinter molding include sintering circuit and
Aging sequence, described sintering circuit is to be incubated 3-6 hour at 1000-1080 DEG C, and described aging sequence at least includes the first order
Timeliness, described first order timeliness is to be incubated 1-4 hour at 800-950 DEG C.
A kind of improvement of the preparation method of performance Nd Fe B sintered magnet disclosed by the invention, aging sequence is additionally included in the first order
The second level timeliness performed after timeliness, described second level timeliness is to be incubated 3-6 hour at 450-550 DEG C.
Performance Nd Fe B sintered magnet disclosed by the invention, its preparation is simple, stable performance, by crystal boundary doped with cerium element,
Reduce cerium dopping impact coercitive on magnet, reduce the cost of doping and production and processing simultaneously, drastically increase adding of magnet
Work performance.
Detailed description of the invention
Below in conjunction with detailed description of the invention, it is further elucidated with the present invention, it should be understood that following detailed description of the invention is merely to illustrate this
Bright rather than limit the scope of the present invention.
It is configured to be divided into Ce30Ho0.5Co0.5Al0.4Cu0.2Zr0.1B0.98Fe remaining (A composition), and
Pr6.75Nd20.25Gd3Ho1.5Co0.5Al0.8Cu0.2Zr0.1B0.98Febal (B component), content is weight percentage, distribution
Through vacuum rapid hardening furnace melting, it is prepared as slab；The ratio of slab A and slab B proportionally 10%:90% is mixed,
Obtaining blending constituent is more than Pr6.08Nd18.23Gd2.7Ho1.35Ce3.0Co0.5Al0.76Cu0.2Zr0.1B0.98F e, then carries out
Hydrogen breaks and airflow milling, is prepared as the fine powder that particle mean size is 3.0～3.2um, suppresses in the closing press having nitrogen to protect,
Close the oxygen content≤1000ppm in press, be pressed into the pressed compact of square shape, then this pressed compact is put into sintering furnace be sintered,
Sintering temperature is 1040 DEG C, 5 hours sintered heat insulating time, and product carries out after terminating two-stage timeliness, first order timeliness temperature
Degree is 900 DEG C, temperature retention time 2 hours, second level aging temp 500 DEG C, and temperature retention time 5 hours prepares final magnet.
Magnet is made the sample post of D10 × 10, uses ATM-4 magnetic measurement instrument to test, and according to single C composition according to
The magnetic property of magnet prepared by common process contrasts.As shown in the table:
Table 1
By the contrast of above performance, the remanent magnetism of the remanent magnetism of A:B=10%:90% and single C composition substantially close to, but coercive
Power the former improve about 209kA/m than the latter.The magnetic property of A:B=10%:90% meets the requirement of 38M, for the 38M of standard.
Simultaneously compared with traditional 38M without cerium, cost reduces about 6%.
Embodiment 1
In the present embodiment, alloy consists of (PrNd) 27.2Gd4.0Al0.8Cu0.2Co1.0B0.98Febal, and (content is weight hundred
Proportion by subtraction, wt%), through vacuum induction slab stove melting, it is prepared as the alloy casting piece of this composition, then broken by alloy casting piece coarse powder through hydrogen
Essence is the coarse powder that particle mean size is 50 μm, then uses fine Comminuting Micawith High Pressure Water Jet, and it is 3.3 that coarse powder grinds to form particle mean size
The micropowder of μm.It is the micropowder without titanium valve that micropowder is divided into two groups: first group, carries out batch mixing by three-dimensional material mixer, mixed
The material time is 6 hours, then with the sieving machine sieve powder that mesh number is 200 mesh；The second is the micropowder adding titanium valve, in micropowder
Adding percentage by weight is the titanium valve of 0.2wt%, and the particle mean size of titanium valve is 15 μm, carries out batch mixing by three-dimensional material mixer, mixed
The material time is 6 hours, then with the sieving machine sieve powder that mesh number is 200 mesh.By the closing the most under nitrogen protection of two groups of micropowders
Being pressed in press, the specification of pressed compact is the square of 57.5 × 30 × 48, closes the oxygen content in press and requires to be less than
1000ppm.Suppress two groups of samples are put into same sintering furnace under nitrogen protection be sintered and timeliness, sintering temperature
Being 1060 DEG C, be incubated 4.5 hours, first order aging temp is 900 DEG C, is incubated 2 hours, and second level aging temp is 500 DEG C,
It is incubated 4.5 hours.The magnet prepared is contrasted as follows:
1), by magnet it is processed into the sample post of D10 × 10, uses ATM-4 magnetic measurement instrument to test, contrast magnetic property；
2), by magnet it is processed into the sample of 30 × 17.25 × 3,50 respectively, carries out fall-down test, from the height of 1.5 meters, from
By dropping to ground, the ratio of statistics embrittlement, compares the fragility of magnet with this.
Table 1 is not added with titanium valve and adds the sintered NdFeB magnetic property of 0.2wt% titanium valve
| Br(KGs) | Hcj(KOe) | (BH)max(MGO) | Hk/Hcj | |
| It is not added with titanium valve | 12.56 | 15.51 | 38.53 | 96.5% |
| Add 0.2wt% titanium valve | 12.45 | 16.26 | 38.12 | 96.8% |
From result above it can be seen that add the titanium valve of 0.2wt%, coercivity improves 0.75kOe, and remanent magnetism only reduces
0.11kGs.Titanium valve raising coercitive for magnet is that comparison is significant.
Table 2 is not added with titanium valve and adds the performance Nd Fe B sintered magnet fall-down test of 0.2wt% titanium valve
| Sample number (pcs) | Embrittlement sample number (pcs) | Embrittlement percentage ratio | |
| It is not added with titanium valve | 50 | 11 | 22% |
| Add 0.2wt% titanium valve | 50 | 4 | 8% |
Data are it can be seen that add the magnet embrittlement hundred from 1.5 meters of height free-electron model of 0.2wt% titanium valve from the experiment above
Proportion by subtraction reduces 14% than the magnet for interpolation titanium valve, can improve the fragility of magnet with the interpolation of titanium valve.
Embodiment 2
In the present embodiment, alloy consists of (PrNd) 27.2Gd4.0Al0.8Cu0.2Co1.0B0.98Febal, and (content is weight hundred
Proportion by subtraction, wt%), through vacuum induction slab stove melting, it is prepared as the alloy casting piece of this composition, then broken by alloy casting piece coarse powder through hydrogen
Essence is the coarse powder that particle mean size is 100 μm, then uses fine Comminuting Micawith High Pressure Water Jet, and it is 2.7 that coarse powder grinds to form particle mean size
The micropowder of μm.Adding percentage by weight in micropowder is the titanium valve of 0.2wt%, and the particle mean size of titanium valve is 8 μm, by three-dimensional
Batch mixer carries out batch mixing, and mixing time is 6 hours, then with the sieving machine sieve powder that mesh number is 200 mesh.By micropowder respectively at nitrogen
Being pressed in closing press under gas shielded, the specification of pressed compact is the square of 57.5 × 30 × 48, closes the oxygen in press
Content requirement is less than 930ppm.The sample suppressed is put into same sintering furnace under nitrogen protection be sintered and timeliness,
Sintering temperature is 1060 DEG C, is incubated 4.5 hours, and first order aging temp is 860 DEG C, is incubated 1.5 hours, second level timeliness
Temperature is 550 DEG C, is incubated 4.5 hours.
Embodiment 3
In the present embodiment, alloy consists of (PrNd) 27.2Gd4.0Al0.8Cu0.2Co1.0B0.98Febal, and (content is weight hundred
Proportion by subtraction, wt%), through vacuum induction slab stove melting, it is prepared as the alloy casting piece of this composition, then broken by alloy casting piece coarse powder through hydrogen
Essence is the coarse powder that particle mean size is 200 μm, then uses fine Comminuting Micawith High Pressure Water Jet, and it is 3.8 that coarse powder grinds to form particle mean size
The micropowder of μm.Adding percentage by weight in micropowder is the titanium valve of 0.2wt%, and the particle mean size of titanium valve is 47 μm, by three
Dimension batch mixer carries out batch mixing, and mixing time is 6 hours, then with the sieving machine sieve powder that mesh number is 200 mesh.Micropowder is existed respectively
Being pressed in closing press under nitrogen protection, the specification of pressed compact is the square of 57.5 × 30 × 48, closes in press
Oxygen content requires less than 970ppm.The sample suppressed is put into same sintering furnace under nitrogen protection be sintered and timeliness,
Sintering temperature is 1035 DEG C, is incubated 4.6 hours, and first order aging temp is 850 DEG C, is incubated 1.7 hours, second level timeliness
Temperature is 540 DEG C, is incubated 6 hours.
Embodiment 4
In the present embodiment, alloy consists of (PrNd) 27.2Gd4.0Al0.8Cu0.2Co1.0B0.98Febal, and (content is weight hundred
Proportion by subtraction, wt%), through vacuum induction slab stove melting, it is prepared as the alloy casting piece of this composition, then broken by alloy casting piece coarse powder through hydrogen
Essence is the coarse powder that particle mean size is 400 μm, then uses fine Comminuting Micawith High Pressure Water Jet, and it is 2.7 that coarse powder grinds to form particle mean size
The micropowder of μm.Adding percentage by weight in micropowder is the titanium valve of 0.2wt%, and the particle mean size of titanium valve is 34 μm, by three
Dimension batch mixer carries out batch mixing, and mixing time is 6 hours, then with the sieving machine sieve powder that mesh number is 300 mesh.Micropowder is existed respectively
Being pressed in closing press under nitrogen protection, the specification of pressed compact is the square of 57.5 × 30 × 48, closes in press
Oxygen content requires less than 850ppm.The sample suppressed is put into same sintering furnace under nitrogen protection be sintered and timeliness,
Sintering temperature is 1030 DEG C, is incubated 5.2 hours, and first order aging temp is 820 DEG C, is incubated 2.6 hours, second level timeliness
Temperature is 450 DEG C, is incubated 6 hours.
Embodiment 5
In the present embodiment, alloy consists of (PrNd) 27.2Gd4.0Al0.8Cu0.2Co1.0B0.98Febal, and (content is weight hundred
Proportion by subtraction, wt%), through vacuum induction slab stove melting, it is prepared as the alloy casting piece of this composition, then broken by alloy casting piece coarse powder through hydrogen
Essence is the coarse powder that particle mean size is 600 μm, then uses fine Comminuting Micawith High Pressure Water Jet, and it is 3.2 that coarse powder grinds to form particle mean size
The micropowder of μm.Adding percentage by weight in micropowder is the titanium valve of 0.1wt%, and the particle mean size of titanium valve is 26 μm, by three
Dimension batch mixer carries out batch mixing, and mixing time is 6 hours, then with the sieving machine sieve powder that mesh number is 100 mesh.Micropowder is existed respectively
Being pressed in closing press under nitrogen protection, the specification of pressed compact is the square of 57.5 × 30 × 48, closes in press
Oxygen content requires less than 950ppm.The sample suppressed is put into same sintering furnace under nitrogen protection be sintered and timeliness,
Sintering temperature is 1010 DEG C, is incubated 3.6 hours, and first order aging temp is 880 DEG C, is incubated 2.7 hours, second level timeliness
Temperature is 530 DEG C, is incubated 3 hours.
Embodiment 6
In the present embodiment, alloy consists of (PrNd) 27.2Gd4.0Al0.8Cu0.2Co1.0B0.98Febal, and (content is weight hundred
Proportion by subtraction, wt%), through vacuum induction slab stove melting, it is prepared as the alloy casting piece of this composition, then broken by alloy casting piece coarse powder through hydrogen
Essence is the coarse powder that particle mean size is 800 μm, then uses fine Comminuting Micawith High Pressure Water Jet, and it is 2.3 that coarse powder grinds to form particle mean size
The micropowder of μm.Adding percentage by weight in micropowder is the titanium valve of 0.5wt%, and the particle mean size of titanium valve is 50 μm, by three
Dimension batch mixer carries out batch mixing, and mixing time is 6 hours, then with the sieving machine sieve powder that mesh number is 150 mesh.Micropowder is existed respectively
Being pressed in closing press under nitrogen protection, the specification of pressed compact is the square of 57.5 × 30 × 48, closes in press
Oxygen content requires less than 500ppm.The sample suppressed is put into same sintering furnace under nitrogen protection be sintered and timeliness,
Sintering temperature is 1045 DEG C, is incubated 5.5 hours, and first order aging temp is 870 DEG C, is incubated 3 hours, second level timeliness temperature
Degree is 450 DEG C, is incubated 3 hours.
Embodiment 7
In the present embodiment, alloy consists of (PrNd) 27.2Gd4.0Al0.8Cu0.2Co1.0B0.98Febal, and (content is weight hundred
Proportion by subtraction, wt%), through vacuum induction slab stove melting, it is prepared as the alloy casting piece of this composition, then broken by alloy casting piece coarse powder through hydrogen
Essence is the coarse powder that particle mean size is 2000 μm, then uses fine Comminuting Micawith High Pressure Water Jet, and it is 4 that coarse powder grinds to form particle mean size
The micropowder of μm.Adding percentage by weight in micropowder is the titanium valve of 0.4wt%, and the particle mean size of titanium valve is 40 μm, by three
Dimension batch mixer carries out batch mixing, and mixing time is 6 hours, then with the sieving machine sieve powder that mesh number is 250 mesh.Micropowder is existed respectively
Being pressed in closing press under nitrogen protection, the specification of pressed compact is the square of 57.5 × 30 × 48, closes in press
Oxygen content requires less than 600ppm.Put into same sintering furnace under nitrogen protection by suppress two groups to be sintered and timeliness,
Sintering temperature is 1050 DEG C, is incubated 5 hours, and first order aging temp is 830 DEG C, is incubated 3.5 hours, second level timeliness temperature
Degree is 480 DEG C, is incubated 3.7 hours.
Embodiment 8
In the present embodiment, alloy consists of (PrNd) 27.2Gd4.0Al0.8Cu0.2Co1.0B0.98Febal, and (content is weight hundred
Proportion by subtraction, wt%), through vacuum induction slab stove melting, it is prepared as the alloy casting piece of this composition, then broken by alloy casting piece coarse powder through hydrogen
Essence is the coarse powder that particle mean size is 1800 μm, then uses fine Comminuting Micawith High Pressure Water Jet, and it is 2 that coarse powder grinds to form particle mean size
The micropowder of μm.Adding percentage by weight in micropowder is the titanium valve of 0.25wt%, and the particle mean size of titanium valve is 30 μm, by three
Dimension batch mixer carries out batch mixing, and mixing time is 6 hours, then with the sieving machine sieve powder that mesh number is 220 mesh.Micropowder is existed respectively
Being pressed in closing press under nitrogen protection, the specification of pressed compact is the square of 57.5 × 30 × 48, closes in press
Oxygen content requires less than 700ppm.Put into same sintering furnace under nitrogen protection by suppress two groups to be sintered and timeliness,
Sintering temperature is 1040 DEG C, is incubated 6 hours, and first order aging temp is 800 DEG C, is incubated 4 hours, second level aging temp
It is 530 DEG C, is incubated 5.6 hours.
Embodiment 9
In the present embodiment, alloy consists of (PrNd) 27.2Gd4.0Al0.8Cu0.2Co1.0B0.98Febal, and (content is weight hundred
Proportion by subtraction, wt%), through vacuum induction slab stove melting, it is prepared as the alloy casting piece of this composition, then broken by alloy casting piece coarse powder through hydrogen
Essence is the coarse powder that particle mean size is 1500 μm, then uses fine Comminuting Micawith High Pressure Water Jet, and it is 2.5 that coarse powder grinds to form particle mean size
The micropowder of μm.Adding percentage by weight in micropowder is the titanium valve of 0.32wt%, and the particle mean size of titanium valve is 10 μm, by three
Dimension batch mixer carries out batch mixing, and mixing time is 6 hours, then with the sieving machine sieve powder that mesh number is 280 mesh.Micropowder is existed respectively
Being pressed in closing press under nitrogen protection, the specification of pressed compact is the square of 57.5 × 30 × 48, closes in press
Oxygen content requires less than 800ppm.The sample suppressed is put into same sintering furnace under nitrogen protection be sintered and timeliness,
Sintering temperature is 1080 DEG C, is incubated 3.5 hours, and first order aging temp is 930 DEG C, is incubated 1.5 hours, second level timeliness
Temperature is 480 DEG C, is incubated 3.6 hours.
Embodiment 10
In the present embodiment, alloy consists of (PrNd) 27.2Gd4.0Al0.8Cu0.2Co1.0B0.98Febal, and (content is weight hundred
Proportion by subtraction, wt%), through vacuum induction slab stove melting, it is prepared as the alloy casting piece of this composition, then broken by alloy casting piece coarse powder through hydrogen
Essence is the coarse powder that particle mean size is 1300 μm, then uses fine Comminuting Micawith High Pressure Water Jet, and it is 3 that coarse powder grinds to form particle mean size
The micropowder of μm.Adding percentage by weight in micropowder is the titanium valve of 0.14wt%, and the particle mean size of titanium valve is 20 μm, by three
Dimension batch mixer carries out batch mixing, and mixing time is 6 hours, then with the sieving machine sieve powder that mesh number is 160 mesh.Micropowder is existed respectively
Being pressed in closing press under nitrogen protection, the specification of pressed compact is the square of 57.5 × 30 × 48, closes in press
Oxygen content requires less than 900ppm.The sample suppressed is put into same sintering furnace under nitrogen protection be sintered and timeliness,
Sintering temperature is 1000 DEG C, is incubated 6 hours, and first order aging temp is 950 DEG C, is incubated 1 hour, second level aging temp
It is 540 DEG C, is incubated 4.5 hours.
Embodiment 11
In the present embodiment, alloy consists of (PrNd) 27.2Gd4.0Al0.8Cu0.2Co1.0B0.98Febal, and (content is weight hundred
Proportion by subtraction, wt%), through vacuum induction slab stove melting, it is prepared as the alloy casting piece of this composition, then broken by alloy casting piece coarse powder through hydrogen
Essence is the coarse powder that particle mean size is 1100 μm, then uses fine Comminuting Micawith High Pressure Water Jet, and coarse powder grinds to form particle mean size 3.5
The micropowder of μm.Adding percentage by weight in micropowder is the titanium valve of 0.46wt%, and the particle mean size of titanium valve is 2 μm, by three
Dimension batch mixer carries out batch mixing, and mixing time is 6 hours, then with the sieving machine sieve powder that mesh number is 140 mesh.Micropowder is existed respectively
Being pressed in closing press under nitrogen protection, the specification of pressed compact is the square of 57.5 × 30 × 48, closes in press
Oxygen content requires less than 1000ppm.The sample suppressed is put under nitrogen protection same sintering furnace be sintered and time
Effect, sintering temperature is 1080 DEG C, is incubated 3 hours, and first order aging temp is 900 DEG C, is incubated 2 hours.
In above-described embodiment, fine Comminuting Micawith High Pressure Water Jet be use be oppositely arranged injector head injection 15MPa (hydraulic pressure is all right
Other arbitrary value in the range of following any value 17,18,19,20,21,22,23,24,25 and 15-25MPa)
High pressure water pulse jet impulse coarse powder obtain, powder add in water under high pressure (can also water under high pressure liquidate intersection add or
Person adds in injector head exit).The injection frequency of water under high pressure be 15Hz (frequency can also for following any value 17,20,23,
26, other arbitrary value in the range of 29,30,33,37,40,42,46,50,55,58,60 and 15-60Hz).
In above example the composition of alloy can also for include, without being limited to situation as in the table below arbitrary (surplus is Fe, under
Table is no longer indicated):
Above magnet alloy is that raw material obtains by the alloy A included, without being limited to cited by embodiments below and alloy B:
Alloy A embodiment can be to include, without being limited to situation as in the table below arbitrary (surplus is Fe, no longer marks in following table
Bright):
Alloy B embodiment can be to include, without being limited to situation as in the table below arbitrary (surplus is Fe, no longer marks in following table
Bright):
This place embodiment is to right in place of the claimed non-limit of technical scope midrange and in embodiment technical scheme
Single or multiple technical characteristic replace the new technical scheme formed on an equal basis, the most all in the scope of protection of present invention
In；Simultaneously in all embodiments enumerated or do not enumerate of the present invention program, parameters in the same embodiment is merely representative of
One example (i.e. a kind of feasible scheme) of its technical scheme, and between parameters, there is not strict cooperation and restriction
Relation, the most each parameter can mutually be replaced, except special declaration when stating ask without prejudice to axiom and the present invention.
Include, without being limited to above-mentioned cited embodiment scheme, the magnet obtained by technical solution of the present invention enforcement, magnetic coercive force
And magnet fragility is all significantly improved, the titanium elements that additionally crystal boundary adds, the magnetic property of magnet has all been had significantly
Improve.
Technological means disclosed in the present invention program is not limited only to the technological means disclosed in above-mentioned technological means, also include by more than
The technical scheme that technical characteristic combination in any is formed.The above is the detailed description of the invention of the present invention, it is noted that for
For those skilled in the art, under the premise without departing from the principles of the invention, it is also possible to make some improvement and profit
Decorations, these improvements and modifications are also considered as protection scope of the present invention.
Claims (9)
1. the preparation method of a performance Nd Fe B sintered magnet, it is characterised in that: comprise the steps, a, by alloy A and
Alloy B prepares magnet alloy, obtains slab；B, slab obtain alloy powder through broken powder process, and broken powder process includes elder generation
After carry out coarse powder preparation and micropowder prepare two stages；C, compressing: alloy powder at oxygen content less than 1000ppm
Environment in compressing obtain base substrate；D, sintering: base substrate is sintered, timeliness；
Wherein magnet alloy consist of RxMyBzFeSurplus, R be comprise the one in La, Ce, Pr, Nd, Gd, Ho, Dy or
Several, R total mass fraction be x, M be one or more in Co, Al, Cu, Nb, Zr, Ga, M total mass fraction is y,
X=28～32wt%, y=0～2wt%, z=0.9～1.1wt%；
Described micropowder is prepared as preparing alloy powder with fine Comminuting Micawith High Pressure Water Jet, and described fine Comminuting Micawith High Pressure Water Jet is to use
The high pressure water impact coarse powder of the injector head injection 15-25MPa being oppositely arranged obtains.
The preparation method of performance Nd Fe B sintered magnet the most according to claim 1, it is characterised in that: described alloy A's
Consist of Cex1Hoy1M1z1Bn1FeSurplus, wherein x1=28～31wt%, y1=0～3wt%, z1=0～2wt%, n1=0.9～1.1wt%, M1
For one or more in Co, Al, Cu, Nb, Zr.
The preparation method of performance Nd Fe B sintered magnet the most according to claim 1, it is characterised in that: described alloy B's
Consist of R ＇x2By2M2z2FeSurplus, wherein x2=28～35wt%, y2=0.9～1.1wt%, z2=0～2wt%, R ＇ are rare earth unit
One or more in element Nd, Pr, Gd, Ho, Dy, M2 is the one in Co, Al, Cu, Nb, Zr, Ga or several
Kind.
The preparation method of performance Nd Fe B sintered magnet the most according to claim 1, it is characterised in that: prepared by described coarse powder
After the particle mean size obtained is the coarse powder of 50-2000 μm, the alloy of the particle mean size 2-4 μm that described micropowder prepares
Micropowder.
The preparation method of performance Nd Fe B sintered magnet the most according to claim 1, it is characterised in that: described magnet forms
In also include the titanium elements that accounts for gross mass 0.1～0.5wt%.
The preparation method of performance Nd Fe B sintered magnet the most according to claim 5, it is characterised in that: described titanium elements is
After mixing with the addition of titanium valve form after slab powder process, row alloy powder is compressing again, and wherein the particle mean size of titanium valve is
2-50μm。
7. according to the preparation method of the performance Nd Fe B sintered magnet described in claim 4 or 6, it is characterised in that: described alloy
The compressing front alloy powder of micropowder all crosses the screening of 100-300 mesh sieve.
The preparation method of performance Nd Fe B sintered magnet the most according to claim 1, it is characterised in that: described sinter molding
Including sintering circuit and aging sequence, described sintering circuit is to be incubated 3-6 hour at 1000-1080 DEG C, described timeliness work
Sequence at least includes that first order timeliness, described first order timeliness are to be incubated 1-4 hour at 800-950 DEG C.
The preparation method of performance Nd Fe B sintered magnet the most according to claim 8, it is characterised in that: described aging sequence
The second level timeliness performed after being additionally included in first order timeliness, described second level timeliness is that insulation 3-6 is little at 450-550 DEG C
Time.
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Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN106356175A (en) * | 2016-08-29 | 2017-01-25 | 四川省有色冶金研究院有限公司 | Double-main-phase Nd2Fe14B-Ce2Fe14B composite permanent magnet and preparation method thereof |
Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101266857A (en) * | 2007-12-24 | 2008-09-17 | 中国石油大学(华东) | Method for improving sintered neodymium-iron-boron coercive force and working temperature based on nano Ti powder modification |
| CN103996519A (en) * | 2014-05-11 | 2014-08-20 | 沈阳中北通磁科技股份有限公司 | Manufacturing method for high-performance NdFeB rare earth permanent magnet devices |
| CN104439258A (en) * | 2014-11-27 | 2015-03-25 | 北京科技大学 | Method for preparing neodymium-iron-boron permanent magnet alloy powder |
| CN104575904A (en) * | 2014-11-26 | 2015-04-29 | 宁波宏垒磁业有限公司 | NdFeB magnet formed by sintering NdFeB recycling waste and preparation method of NdFeB magnet |
-
2016
- 2016-01-08 CN CN201610012242.1A patent/CN105845303A/en not_active Withdrawn
Patent Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101266857A (en) * | 2007-12-24 | 2008-09-17 | 中国石油大学(华东) | Method for improving sintered neodymium-iron-boron coercive force and working temperature based on nano Ti powder modification |
| CN103996519A (en) * | 2014-05-11 | 2014-08-20 | 沈阳中北通磁科技股份有限公司 | Manufacturing method for high-performance NdFeB rare earth permanent magnet devices |
| CN104575904A (en) * | 2014-11-26 | 2015-04-29 | 宁波宏垒磁业有限公司 | NdFeB magnet formed by sintering NdFeB recycling waste and preparation method of NdFeB magnet |
| CN104439258A (en) * | 2014-11-27 | 2015-03-25 | 北京科技大学 | Method for preparing neodymium-iron-boron permanent magnet alloy powder |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN106356175A (en) * | 2016-08-29 | 2017-01-25 | 四川省有色冶金研究院有限公司 | Double-main-phase Nd2Fe14B-Ce2Fe14B composite permanent magnet and preparation method thereof |
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