CN104003707A - Preparing method of barium permanent-magnetic ferrite materials - Google Patents
Preparing method of barium permanent-magnetic ferrite materials Download PDFInfo
- Publication number
- CN104003707A CN104003707A CN201410066900.6A CN201410066900A CN104003707A CN 104003707 A CN104003707 A CN 104003707A CN 201410066900 A CN201410066900 A CN 201410066900A CN 104003707 A CN104003707 A CN 104003707A
- Authority
- CN
- China
- Prior art keywords
- preparation
- warming
- principal constituent
- hour
- fused salt
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Granted
Links
Landscapes
- Hard Magnetic Materials (AREA)
Abstract
The invention discloses a preparing method of barium permanent-magnetic ferrite materials. According to the preparing method, fused salts are used as media of a solid phase reaction; the barium permanent-magnetic ferrite materials with high magnetic performance are manufactured and obtained through regulating the types and the proportion of the fused salts and controlling the sintering process; and the barium permanent-magnetic ferrite materials have the characteristic that the residual magnetism, the coercive force and the magnetic energy product are higher than those of barium ferrite prepared by a traditional process. The preparing method provided by the invention has the advantages of low reaction temperature and low energy consumption.
Description
Technical field
The present invention relates to a kind of preparation method of permanent-magnet ferrite material, particularly a kind of preparation method of barium permanent-magnet ferrite material.
Background technology
The composite oxides that ferrite is comprised of iron family element ting and other one or more suitable metallic elements.The magneto-plumbite type ferrite with hexaplanar is a class permanent-magnet ferrite, since nineteen fifty-two is developed out, because thering is superior cost performance, higher saturation magnetization and coercive force, high magnetocrystalline anisotropy and Curie temperature, good features such as chemical stability, make its range of application very extensive, can be used for various Denso motors, household electrical appliance motor, all kinds of trolley part motors such as motorcar electric lifting motor, wiper motor, the every field such as CD-ROM drive motor is established in medical treatment, office appliance motor.
The method of now preparing Ferrite Material mainly contains following several:
(1) china-clay method claims again oxidation style, be mainly by powdery starting material by preset ratio mix, high temperature pre-burning, through high temperature solid state reaction, form bulk and through operations such as coarse reduction, secondary fine grinding, moulding, sintering, be prepared from again.This method is current industrialized preparing process, and principal feature is: technological process is simply controlled, and production cost is lower.Shortcoming is: particle size distribution range is wider, granule-morphology is uneven, calcined temperature is higher.
(2) spray burning method, this method is developed by salt decomposition method and the combination of spray burning technology, mainly that metal salt solution is mixed with liquid fuel, at high temperature with atomizing state spray combustion, solution is decomposed by instantaneously heating, obtain highly purified ultra-fine ferrite powder, principal feature is: powder diameter is evenly distributed, stoichiometric ratio accurate, sample sintering temperature is low, purity is higher.Shortcoming is: the gas of decomposition have corrodibility, to environment produce to pollute, requirement for experiment condition is high.This method is difficult to realize suitability for industrialized production at present.
(3) coprecipitation method, is mainly that certain density metal salt solution is evenly mixed by default stoichiometric ratio, with certain density basic solution (NaOH, NH
4oH etc.), as precipitation agent, make precipitation by metallic ion, then after throw out filtration, washing are dried, high temperature sintering obtains product.The feature of this method is: epigranular, chemically reactive are better, solid state reaction temperature is low.Shortcoming is: when formulating of recipe is rare earth ion doped, the co-precipitation of ion is more difficult and homogeneity is poor, and the particle of preparation is more easily reunited.
(4) hydrothermal method, this method is that strong basicity suspension liquid that co-precipitation is obtained is put into below the above He Ling circle temperature of boiling point that autoclave is heated to water, makes to react and obtain ferrite between throw out.The feature of this method is: in the aqueous solution, reaction thereby particle are difficult for reuniting, the ferrite powder good dispersity of preparation, narrow diameter distribution, good crystallinity.Shortcoming is: material purity and equipment requirements are high, and hydro-thermal reaction is uncontrollable in addition, easily generates dephasign.
(5) sol-gel method, is that metal salt solution is hybridly prepared into solution by stoichiometric ratio, then adds organic acid to make part, then regulates pH value, slow evaporation to obtain gel presoma, through high temperature sintering, obtains ferrite.The feature of this method is: easily realize ionic replacement, particle diameter is little and be evenly distributed.Shortcoming is: cost is high, and sample easily ftractures.Be not suitable for suitability for industrialized production, be mainly used at present laboratory study.
Existing the most widely used permanent-magnet ferrite is the Sr ferrite (SrFe with M type hexaplanar structure
12o
19) and Ba ferrite (BaFe
12o
19), along with all kinds of motors in recent years require miniaturizations, lightweight, precise treatment, this just requires M type permanent-magnet ferrite need to have higher magnetic property.The raising M type permanent-magnet ferrite magnetic property of report has following several mode at present: 1) by ionic replacement Sr
2+, Ba
2+, Fe
3+acquisition is than Sr ferrite and the more excellent ferrite of Ba ferrite performance.If number of patent application is 200610169039 to have announced the Ferrite Material that a kind of La, Co replace Sr, Ba, described in patent, after coarse reduction operation, add twice Crushing of Ultrafine operation, Crushing of Ultrafine is milled to 0.08-0.8 μ m by median size for the first time, 0.1-0.2 μ m more preferably, then through Overheating Treatment by the super-fine powder of less than 0.1 μ m with react compared with meal.Crushing of Ultrafine is crushed to the powder after thermal treatment below 0.8 μ m for the second time, 0.1-0.2 μ m more preferably, so thin powder is very difficult in pressing under magnetic field process, shaping efficiency reduces greatly, in this patent working example, be the performance that obtains Br4510Gs and Hcj 5585 Oe in addition, the alternative amount of Co reaches 0.4, and production cost is higher.For another example number of patent application is 201110153849 to have announced the permanent-magnet ferrite material that a kind of rare earth replaces, and its chemical formula is D
1-xr
xonFe
2-y-zln
zco
yo3, described permanent-magnet ferrite material and traditional permanent-magnet ferrite AB
120
19compare, A position and B position all part by lanthanon, replaced, wherein: D be in Ca, Ba and Sr element a kind of, two or three, A position can not comprise La, B position can not comprise Co.In embodiment, D position replaces and has used Nd that mol ratio is 0.41 and 0.23 La, Ln to use Gd that mol ratio is 0.38 and 0.26 Co, magnetic property Br=0.47T, Hcj=430kA/m, maximum magnetic energy product (BH) max=43.3 kJ/m in 3
3performance, but used in a large number expensive Nd
2o
3and Gd
2o
3, significantly increased production cost, lost the characteristic of M type permanent-magnet ferrite high performance-price ratio.
Summary of the invention
The object of the present invention is to provide a kind of preparation method of barium permanent-magnet ferrite material, utilize fused salt as the medium of solid state reaction, to manufacture the barium permanent-magnet ferrite material that obtains high magnetic characteristics, have than the feature of the higher remanent magnetism of traditional technology barium ferrite, coercive force, magnetic energy product, preparation method of the present invention has advantages of that temperature of reaction is low, energy consumption is little.
The technical solution adopted for the present invention to solve the technical problems is:
A preparation method for barium permanent-magnet ferrite material, comprises the following steps:
(1) batching and batch mixing
Principal constituent is by (1-x-y) BaOxAO
r
2o
3nFe
2-zco
zo
3composition formula, A is Ca or Pb, R is La, 0.05≤x≤0.25 wherein, 0.005≤
≤ 0.15, and 0.35≤1-x-y≤0.8,0.05≤z≤0.2,5.1≤n≤6;
The fused salt that accurately takes each raw material gross weight meter of each raw material of principal constituent and principal constituent 10%-20% carries out wet ball-milling and obtains compound;
Median size through wet ball-milling compound is preferably 0.6-1 μ m.Grain diameter is little, and surface-area is large, and particle and fused salt contact area are conducive to more greatly molten salt react ion, improves rate of diffusion, reduces reaction times and temperature.
(2) pre-burning
The compound of step (1) is first incubated to 1-3h under normal atmosphere conditions within the scope of 400-600 ℃, then is warming up to 900-1050 ℃ of insulation 1-5 hour, cooling rear dry-type pulverizing obtains Preburning material;
(3) wash material and fine grinding
After the Preburning material of step (2) is weighed, put into settling tank and add water agitator treating, after washing precipitation, slip is proceeded to sand mill, adding Preburning material weight 0.2-1% grinding aid and 1-1.5% dispersion agent to be milled to median size is 0.5-1.5 μ m, proceed in centrifugal ball mill again, and add minor component ball milling 2.5-4h;
This fine grinding technology coordinates molten-salt growth method can better control fine grinding particle diameter, has improved fine grinding efficiency, and size is even, and complete in crystal formation is normal distribution.Well known in the art, fine grinding particle diameter is meticulous, and median size 0.5 μ m is when following, and water discharge time increases, and shaping efficiency significantly reduces, and affects production efficiency.Particle diameter is excessively thick, and remanent magnetism and coercive force can decline.
(4) moulding
Slip precipitation after step (3) is finished dealing with, reaching water ratio is 25-40%, at 10000-14000Gs magnetic field compacted under;
(5) sintering
The formed body that step (4) is obtained is incubated 1-3 hour at 100 ℃-400 ℃, then is warming up to 800-850 ℃, is then being warming up to 1050 ℃-1200 ℃, insulation 1-3 hour.
The barium permanent-magnet ferrite material that the present invention makes is M type hexgonal screw.
Fused salt is as the medium of high temperature solid state reaction, and itself does not participate in the middle of solid state reaction.While reaching certain temperature, fused salt can present molten state, the mobility of each reactive component in liquid phase obviously increased, reactant is not limited to the direct contact interface of adjacent material, also have along the free surface of reactant particle and carry out simultaneously, rate of diffusion is significantly improved, and this can significantly reduce time and the temperature of reaction.Well known in the art, the sintering temperature of Ferrite Material is up to 1200-1300 ℃, and process contriver's great many of experiments shows, adopt fused salt as reaction media, can make sintering temperature be reduced to 900-1050 ℃ of left and right, reduce energy consumption, this is fairly obvious to the energy-saving effect in production process.On the other hand, dissolve and parcel component particles material after fused salt melting, alleviated the mutual bonding between particle, the Preburning material powder granule therefore obtaining is reunited less, only has slightly weakly agglomerated.
The patent report of high-performance M type ferrite focuses mostly on to improve saturation magnetization and magnetocrystalline anisotropy and add additive to improve the aspects such as magnet density, orientation degree at ion doping and improves magnetic property at present.
Experiment and sem analysis show, the crystalline form with hexangle type sheet, the radius-thickness ratio of crystal in the Preburning material magnet ratio of thickness (crystal particle diameter with) is that the ratio of 2.5-4.5 is more than 20%, preferably more than 50%, about crystal median size 3 μ m, the ratio that the crystal radius-thickness ratio in sintered magnet is 1.5-3.5 is more than 20%, be preferably more than 50%, the ratio of crystal particle diameter 1-1.2 μ m left and right more than 20%, is preferably more than 50%, can obtain high Br, Hcj.If radius-thickness ratio is excessive, crystal is along C direction of principal axis hypertrophy, and hexangle type tabular crystal is long excessively thin, according to formula Hcj=0.48 (Ha-NMs) demagnetizing factor, increases, and demagnetizing field increases, and causes Hcj to reduce.If radius-thickness ratio is too small, along the growth of C direction of principal axis not exclusively, hexagonal plate crystal thickening shortens crystal, causes Br to decline.
Experiment shows pattern and the size of utilizing fused salt can well control crystal, and this is relevant with surface energy, interfacial energy between fused salt and reactant.The reaction starting stage, in reactants dissolved and melting salt, form saturated solution, reaction generates after ferrite, because ferrite is insoluble to melting salt, through slow cooling, ferrite is separated out gradually from melting salt, forms hexagonal plate M type ferrite crystal, ferrite hexangle type tabular crystal production rate prepared by molten-salt growth method is high, and complete in crystal formation meets the requirement of high performance ferrite.
As preferably, described grinding aid is selected from a kind of in Sodium polymetaphosphate, Sodium hexametaphosphate 99, water glass, polyacrylate, ethylene glycol.
As preferably, described dispersion agent is selected from a kind of in calglucon, Sorbitol Powder.
As preferably, described minor component comprises CaCO
3and SiO
2, according to each raw material gross weight meter of principal constituent CaCO
3addition is 0.5-1.5%, SiO
2addition is 0.1-1%.CaCO
3and SiO
2, can form CaSiO
3although the fusing point of itself reaches 1540 ℃, after ferrite combination, can significantly reduce and reach 1150 ℃ of left and right, on the one hand can reduce sintering temperature, on the other hand can acceleration of sintering, increase magnet density, improve remanent magnetism, can also suppress excessively growing up of crystal grain, thereby improve magnetic property.
As preferably, described fused salt is selected from a kind of in following combination: NaCl+KCl+K
2sO
4(molar percentage separately: 40%, 40%, 20%), LiCl+KCl+ Na
2sO
4(molar percentage separately: 50%, 34%, 16%), NaBr+KBr+NaBO
2(molar percentage separately: 26%, 40%, 34%), NaBr+KBr+K
2sO
4(molar percentage separately: 25%, 35%, 40%).A large amount of explorations experiment through the inventor shows, different fused salts is very remarkable on the impact of ferrite matrix, and to meet high performance ferrite crystal very important to generating to choose suitable fused salt.Because combination fused salt can combine the advantage of utilizing different sorts fused salt, therefore combining the easier proportioning of the more single fused salt of fused salt uses, in combination fused salt, can preferably select the fused salt with eutectic, eutectic fused salt has lower fusing point and high boiling point, contributes to convenient collocation fused salt and wider temperature to regulate space.In addition, the fused salt of selecting should have lower vapour pressure, low viscosity, high capillary physical properties.Therefore the present invention has selected above-mentioned specific fused salt combination.
As preferably, the formed body in step (5), step (4) being obtained is incubated 1-3 hour at 100 ℃-400 ℃, temperature rise rate with 0.8-1.5 ℃/min is warming up to 800-850 ℃ again, then at the temperature rise rate with 1.4-2.5 ℃/min, is warming up to 1050 ℃-1200 ℃, insulation 1-3 hour.The ratio that the crystal grain radius-thickness ratio obtaining under this sintering process is 1.5-3.5 is more than 50%, and the ratio of crystal particle diameter 1-1.2 μ m left and right can reach more than 50%, and crystal boundary is clear, and complete in crystal formation is hexagonal plate, meets high magnetic characteristics feature.
The invention has the beneficial effects as follows:
The M type ferrite that adopts processing method of the present invention to coordinate the major-minor composition of specific proportioning to prepare, can obtain the Br about 4200-4400GS, Hcj4000-4400Oe left and right, (BH) max4.3MGOe left and right.
Compared with prior art, the present invention has advantage and the innovation of following uniqueness: be different from traditional method and rely on ionic replacement and introduce the methods such as additive and improve magnetic property, and focus on and utilize the unique advantage of fused salt and adjusting process method to prepare and meet high-performance permanent magnetic ferrite material the control of ferrite microcosmic crystal morphology, grain size.Use fused salt Process, compared with methods such as hydrothermal method, collosol and gels, there are processing condition controlled, without increasing extras, strong with conventional solid-state method associativity, be beneficial to suitability for industrialized production, temperature of reaction is low, low power consumption and other advantages, by adjusting fused salt kind and proportioning, the control of sintering curre, obtains high performance permanent-magnet ferrite.
Embodiment
Below by specific embodiment, technical scheme of the present invention is described in further detail.
In the present invention, if not refer in particular to, the raw material adopting and equipment etc. all can be buied from market or this area is conventional.Method in following embodiment, if no special instructions, is the ordinary method of this area.
Embodiment 1: principal constituent starting material are pressed to (1-x-y) BaOxAO
r
2o
3nFe
2-zco
zo
3composition formula, A is Ca, R is La.X=0.15 wherein, y=0.1, z=0.06, n=5.9 takes weight, and (principal constituent starting material are specially: Fe
2o
3, La
2o
3, Co
2o
3, BaCO
3, CaCO
3), then take fused salt: NaCl+KCl+K
2sO
4(molar percentage 40%, 40%, 20%), fused salt weight is by each raw material gross weight 10% of principal constituent, put into together ball mill wet ball-milling, Ball-milling Time 8 hours (median size 0.6-1 μ m), 550 ℃ of insulations 2 hours under atmospheric condition after the compound obtaining is dry, with 2 ℃/minute, be warming up to 950 ℃ again, be incubated 2 hours, after cooling, Preburning material is powdered by oscillatory type crusher in crushing, recording particle diameter D50 is 3.1 μ m, to after Preburning material powder weighing, proceed in settling tank again, water repeatedly proceeds to sand mill by slip after washing precipitation, the Sodium polymetaphosphate and 1.4% Sorbitol Powder that add Preburning material weight 0.6%, sand milling 2.5 hours, detecting slip D50 is 1.1 μ m, proceed to again in centrifugal ball mill, and add SiO
2each raw material gross weight meter of 0.4%(principal constituent), CaCO
3each raw material gross weight meter of 0.8%(principal constituent), rotating speed is controlled at 800 revs/min, fine grinding 3 hours, and it is 0.45 μ m that slip detects D10, D50 is 0.75 μ m, D90 is that 1.21 μ m proceed to settling tank precipitation by slip, and making its water content is 35% left and right, is using the moulding of forming machine wet type, forming magnetic field 10000Gs-14000 Gs, forming pressure 5MPa, gained molded blank diameter 43.2mm, height 13 mm.Molded blank is incubated to 1 hour at 350 ℃, to remove water and the dispersion agent in formed body, be warming up to again 850 ℃ of left and right, temperature rise rate is controlled at 1.1 ℃/min, after 850 ℃, temperature rise rate is controlled at 1.8 ℃/min, then at 1190 ℃, be incubated 1 hour, will after the sample extraction surface grinding after sintering, measure magnetic property (in Table 1).
Embodiment 2 fused salt consumptions are each raw material gross weight 15% of principal constituent, and all the other are with embodiment 1.
Embodiment 3 fused salt consumptions are each raw material gross weight 20% of principal constituent, and all the other are with embodiment 1.
Embodiment 4 fused salts consist of: LiCl+KCl+Na
2sO
4(molar percentage 50%, 34%, 16%), fused salt consumption is each raw material gross weight 10% of principal constituent, during pre-burning, with 2 ℃/minute, is warming up to 930 ℃, all the other are with embodiment 1.
Embodiment 5 fused salt consumptions are each raw material gross weight 15% of principal constituent, and all the other are with embodiment 4.
Embodiment 6 fused salt consumptions are each raw material gross weight 20% of principal constituent, and all the other are with embodiment 4.
Embodiment 7 presses (1-x-y) BaOxAO by principal constituent starting material
r
2o
3nFe
2-zco
zo
3composition formula, A is Ca, R is La.X=0.2 wherein, y=0.15, z=0.08, n=5.9 takes weight, and (principal constituent starting material are specially: Fe
2o
3, La
2o
3, Co
2o
3, BaCO
3, CaCO
3), all the other are with embodiment 1.
Embodiment 8 fused salt consumptions are each raw material gross weight 15% of principal constituent, and all the other are with embodiment 7.
Embodiment 9 fused salt consumptions are each raw material gross weight 20% of principal constituent, and all the other are with embodiment 7.
Embodiment 10 presses (1-x-y) BaOxAO by principal constituent starting material
r
2o
3nFe
2-zco
zo
3composition formula, A is Ca, R is La.X=0.2 wherein, y=0.15, z=0.08, n=5.9 takes weight, and (principal constituent starting material are specially: Fe
2o
3, La
2o
3, Co
2o
3, BaCO
3, CaCO
3), all the other are with embodiment 4.
Embodiment 11 fused salt consumptions are each raw material gross weight 15% of principal constituent, and all the other are with embodiment 10.
Embodiment 12 fused salt consumptions are each raw material gross weight 20% of principal constituent, and all the other are with embodiment 10.
Comparative example 1: principal constituent starting material are pressed to (1-x-y) BaOxAO
r
2o
3nFe
2-zco
zo
3composition formula, A is Ca, R is La.X=0.15 wherein, y=0.1, z=0.06, n=5.9 takes weight, puts into ball mill wet ball-milling, Ball-milling Time 5 hours, after the raw mixture obtaining is dry, under atmospheric condition, with 4 ℃/minute, be warming up to 1240 ℃ again and be incubated respectively 2 hours, after cooling, Preburning material is powdered by oscillatory type crusher in crushing, recording particle diameter D50 is 3.4 μ m, then by Preburning material powder and SiO
20.4%(principal constituent raw material gross weight meter), CaCO
30.8%(principal constituent raw material gross weight meter), calglucon 1.3%(Preburning material weighing scale) add in ball mill ball milling 19 hours, it is that 0.24 μ m, D50 are that 0.82 μ m, D90 are 2.6 μ m that slip detects D10, slip is proceeded to settling tank precipitation, making its water content is 35% left and right, using the moulding of forming machine wet type, forming magnetic field 10000Gs-14000 Gs, forming pressure 5MPa, gained molded blank diameter 43.2mm, height 13mm.Molded blank is incubated to 1 hour at 350 ℃, to remove water and the dispersion agent in formed body, then is warming up to 1205 ℃ of left and right, temperature rise rate is controlled at 3 ℃/min, is incubated 1 hour, will after the sample extraction surface grinding after sintering, measure magnetic property (in Table 1).
Comparative example 2: principal constituent starting material are pressed to (1-x-y) BaOxAO
r
2o
3nFe
2-zco
zo
3composition formula, A is Ca, R is La.X=0.2 wherein, y=0.15, z=0.08, n=5.9 takes weight.Other is with comparative example 1.
From table 1 data analysis, show, in same recipe situation, adopt the magnetic property of the permanent-magnet ferrite material that technique of the present invention makes to be all better than traditional technology, technological reaction temperature of the present invention is low, and energy consumption is low.
The desired protection domain of the claims in the present invention all can be implemented; the parameter of other each temperature, time, consumption all can be adjusted within the scope of the claims; the performance of gained permanent-magnet ferrite material is similar to the aforementioned embodiment, and therefore not to repeat here in the present invention.
Above-described embodiment is a kind of preferably scheme of the present invention, not the present invention is done to any pro forma restriction, also has other variant and remodeling under the prerequisite that does not exceed the technical scheme that claim records.
Claims (6)
1. a preparation method for barium permanent-magnet ferrite material, is characterized in that, comprises the following steps:
(1) batching and batch mixing
Principal constituent is by (1-x-y) BaOxAO
r
2o
3nFe
2-zco
zo
3composition formula, A is Ca or Pb, R is La, 0.05≤x≤0.25 wherein, 0.005≤
≤ 0.15, and 0.35≤1-x-y≤0.8,0.05≤z≤0.2,5.1≤n≤6;
The fused salt that accurately takes each raw material gross weight meter of each raw material of principal constituent and principal constituent 10%-20% carries out wet ball-milling and obtains compound;
(2) pre-burning
The compound of step (1) is first incubated to 1-3h under normal atmosphere conditions within the scope of 400-600 ℃, then is warming up to 900-1050 ℃ of insulation 1-5 hour, cooling rear dry-type pulverizing obtains Preburning material;
(3) wash material and fine grinding
After the Preburning material of step (2) is weighed, put into settling tank and add water agitator treating, after washing precipitation, slip is proceeded to sand mill, adding Preburning material weight 0.2-1% grinding aid and 1-1.5% dispersion agent to be milled to median size is 0.5-1.5 μ m, proceed in centrifugal ball mill again, and add minor component ball milling 2.5-4h;
(4) moulding
Slip precipitation after step (3) is finished dealing with, reaching water ratio is 25-40%, at 10000-14000Gs magnetic field compacted under;
(5) sintering
The formed body that step (4) is obtained is incubated 1-3 hour at 100 ℃-400 ℃, then is warming up to 800-850 ℃, is then being warming up to 1050 ℃-1200 ℃, insulation 1-3 hour.
2. preparation method according to claim 1, is characterized in that: described grinding aid is selected from a kind of in Sodium polymetaphosphate, Sodium hexametaphosphate 99, water glass, polyacrylate, trolamine, ethylene glycol.
3. preparation method according to claim 1, is characterized in that: described dispersion agent is selected from a kind of in calglucon, Sorbitol Powder.
4. according to the preparation method described in claim 1 or 2 or 3, it is characterized in that: described minor component comprises CaCO
3and SiO
2, according to each raw material gross weight meter of principal constituent CaCO
3addition is 0.5-1.5%, SiO
2addition is 0.1-1%.
5. according to the preparation method described in claim 1 or 2 or 3, it is characterized in that: described fused salt is selected from a kind of in following combination: NaCl+KCl+K
2sO
4, LiCl+KCl+Na
2sO
4, NaBr+KBr+NaBO
2, NaBr+KBr+K
2sO
4.
6. according to the preparation method described in claim 1 or 2 or 3, it is characterized in that: the formed body in step (5), step (4) being obtained is incubated 1-3 hour at 100 ℃-400 ℃, temperature rise rate with 0.8-1.5 ℃/min is warming up to 800-850 ℃ again, then at the temperature rise rate with 1.4-2.5 ℃/min, be warming up to 1050 ℃-1200 ℃, insulation 1-3 hour.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201410066900.6A CN104003707B (en) | 2014-02-27 | 2014-02-27 | Preparing method of barium permanent-magnetic ferrite materials |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201410066900.6A CN104003707B (en) | 2014-02-27 | 2014-02-27 | Preparing method of barium permanent-magnetic ferrite materials |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN104003707A true CN104003707A (en) | 2014-08-27 |
| CN104003707B CN104003707B (en) | 2015-05-27 |
Family
ID=51364647
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201410066900.6A Active CN104003707B (en) | 2014-02-27 | 2014-02-27 | Preparing method of barium permanent-magnetic ferrite materials |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN104003707B (en) |
Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN104609844A (en) * | 2014-12-11 | 2015-05-13 | 安徽龙磁科技股份有限公司 | Single-domain adding calcium permanent magnetic ferrite and preparation method thereof |
| CN111153691A (en) * | 2019-12-27 | 2020-05-15 | 湖南航天磁电有限责任公司 | Barium permanent magnetic ferrite and preparation method thereof |
| CN112645705A (en) * | 2020-12-31 | 2021-04-13 | 中钢天源(马鞍山)通力磁材有限公司 | Process method for improving fracture resistance limit of permanent magnetic ferrite magnetic shoe device |
| CN114464387A (en) * | 2021-08-10 | 2022-05-10 | 浙江安特磁材股份有限公司 | Rolled permanent magnetic ferrite magnetic powder and rubber product thereof |
| CN115057697A (en) * | 2022-06-29 | 2022-09-16 | 横店集团东磁股份有限公司 | Preparation method of W-type hexagonal system microwave ferrite material with low line width |
Citations (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1402696A (en) * | 1999-11-30 | 2003-03-12 | 尤吉马格股份有限公司 | Method for making ferrite magnets |
| CN101013622A (en) * | 2005-12-19 | 2007-08-08 | Tdk株式会社 | Ferrite magnetic material |
| CN101316803A (en) * | 2005-11-25 | 2008-12-03 | 日立金属株式会社 | Oxide based magnetic material, process for producing the same, sintered ferrite magnet and process for producing the same |
| CN101395680A (en) * | 2006-03-10 | 2009-03-25 | 日立金属株式会社 | Rotating machine, bonded magnet, magnet roll, and process for producing ferrite sintered magnet |
| CN101811862A (en) * | 2009-11-11 | 2010-08-25 | 沈阳师范大学 | Method for synthesizing barium ferrite |
| CN102964120A (en) * | 2012-08-31 | 2013-03-13 | 横店集团东磁股份有限公司 | Sintered permanent magnetic ferrite and its preparation method |
| CN103680805A (en) * | 2012-09-12 | 2014-03-26 | Lg电子株式会社 | Ferrite magnet with salt and manufacturing method of the same |
-
2014
- 2014-02-27 CN CN201410066900.6A patent/CN104003707B/en active Active
Patent Citations (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1402696A (en) * | 1999-11-30 | 2003-03-12 | 尤吉马格股份有限公司 | Method for making ferrite magnets |
| CN101316803A (en) * | 2005-11-25 | 2008-12-03 | 日立金属株式会社 | Oxide based magnetic material, process for producing the same, sintered ferrite magnet and process for producing the same |
| CN101013622A (en) * | 2005-12-19 | 2007-08-08 | Tdk株式会社 | Ferrite magnetic material |
| CN101395680A (en) * | 2006-03-10 | 2009-03-25 | 日立金属株式会社 | Rotating machine, bonded magnet, magnet roll, and process for producing ferrite sintered magnet |
| CN101811862A (en) * | 2009-11-11 | 2010-08-25 | 沈阳师范大学 | Method for synthesizing barium ferrite |
| CN102964120A (en) * | 2012-08-31 | 2013-03-13 | 横店集团东磁股份有限公司 | Sintered permanent magnetic ferrite and its preparation method |
| CN103680805A (en) * | 2012-09-12 | 2014-03-26 | Lg电子株式会社 | Ferrite magnet with salt and manufacturing method of the same |
Cited By (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN104609844A (en) * | 2014-12-11 | 2015-05-13 | 安徽龙磁科技股份有限公司 | Single-domain adding calcium permanent magnetic ferrite and preparation method thereof |
| CN111153691A (en) * | 2019-12-27 | 2020-05-15 | 湖南航天磁电有限责任公司 | Barium permanent magnetic ferrite and preparation method thereof |
| CN111153691B (en) * | 2019-12-27 | 2022-05-20 | 湖南航天磁电有限责任公司 | Barium permanent magnetic ferrite and preparation method thereof |
| CN112645705A (en) * | 2020-12-31 | 2021-04-13 | 中钢天源(马鞍山)通力磁材有限公司 | Process method for improving fracture resistance limit of permanent magnetic ferrite magnetic shoe device |
| CN112645705B (en) * | 2020-12-31 | 2023-03-14 | 中钢天源(马鞍山)通力磁材有限公司 | Process method for improving fracture resistance limit of permanent magnetic ferrite magnetic shoe device |
| CN114464387A (en) * | 2021-08-10 | 2022-05-10 | 浙江安特磁材股份有限公司 | Rolled permanent magnetic ferrite magnetic powder and rubber product thereof |
| CN115057697A (en) * | 2022-06-29 | 2022-09-16 | 横店集团东磁股份有限公司 | Preparation method of W-type hexagonal system microwave ferrite material with low line width |
Also Published As
| Publication number | Publication date |
|---|---|
| CN104003707B (en) | 2015-05-27 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN102050619B (en) | Method for preparing permanent magnet oxysome material | |
| CN102473514B (en) | Ferrite sintered magnet producing method and ferrite sintered magnet | |
| TWI434302B (en) | Oxide magnetic material and preparation method thereof, and ferrite iron sintered magnet and preparation method thereof | |
| CN102471162B (en) | Ferrite magnetic material | |
| CN104003707B (en) | Preparing method of barium permanent-magnetic ferrite materials | |
| CN104230323B (en) | M type calcium lanthanum cobalt permanent-magnet ferrite and preparation method thereof | |
| CN104003701B (en) | A kind of not containing the preparation method of rare earth permanent ferrite material | |
| CN102329128B (en) | Hard calcium ferrite and manufacturing method thereof | |
| CN102701721B (en) | Low-cost sintered calcium permanent magnetic ferrite and preparation method thereof | |
| CN101552069A (en) | Magnetoplumbite permanent magnetic ferrite and method of producing the same | |
| CN101640090B (en) | High performance soft magnetic ferrite materials doped with Ni-Zn series and preparation method thereof | |
| CN103030388A (en) | High-performance permanent magnetic ferrite material and preparation method thereof | |
| CN110323025A (en) | Ferrite sintered magnet | |
| CN101209920B (en) | Economic sintering permanent-magnet ferrite and preparing method thereof | |
| CN107293398A (en) | A kind of preparation method of permanent-magnet ferrite material | |
| CN104003703B (en) | A kind of preparation method of high-performance permanent magnetic ferrite material | |
| CN103159469A (en) | Preparation method of Mn-Zn ferrite powder with high permeability | |
| CN104003704B (en) | A kind of preparation method without lanthanum cobalt permanent-magnet ferrite | |
| CN104230321A (en) | M-type calcium permanent magnetic ferrite and preparation method thereof | |
| CN108285348B (en) | Method for manufacturing magnetic powder for dry-pressed anisotropic permanent magnet ferrite | |
| CN104003702B (en) | A kind of preparation method of calcium permanent ferrite material | |
| CN102936130B (en) | Permanent magnetic ferrite material | |
| CN102731080B (en) | Processing method for preparing powder used for ferrite magnetic material | |
| CN102129906A (en) | Permanent ferrite material additive and preparation method and application thereof | |
| CN103086707B (en) | Preparation method for Ni-Mn-Co multi-doped barium ferrite wave-absorbing material |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| C06 | Publication | ||
| PB01 | Publication | ||
| C10 | Entry into substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| C14 | Grant of patent or utility model | ||
| GR01 | Patent grant |