CN104909820A - Porous-ceramic with uniformly through ducts as well as preparation method and use of porous-ceramic - Google Patents
Porous-ceramic with uniformly through ducts as well as preparation method and use of porous-ceramic Download PDFInfo
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Abstract
The invention discloses a porous-ceramic with uniformly through ducts as well as a preparation method and use of the porous-ceramic. The invention discloses a preparation method of the porous-ceramic with three-dimensionally through ducts, uniform porosity distribution and adjustable pore-size linearity. A raw material adopted by the invention is uniform low-activity compact spherical particles, the contact parts of the spherical particles are used for providing ceramic strength while a sintering neck is formed through sintering, and a three-dimensional duct is formed by stacking gap of the spherical particles. The typical preparation method comprises the following steps: mixing a certain amount of organic monomers such as MBAM, (NH4)2S2O4 and TEMED to prepare a premixed solution, pouring the premixed solution into the low-activity compact spherical particles, controlling the adding amount of the premixed solution, and realizing tight stacking of the spherical particles by using a certain method; curing the stacked particle accumulation body at a certain temperature; and drying and sintering the cured blank body to obtain the porous-ceramic. The porous-ceramic prepared through the invention has good separation efficiency and flux on the separation of the oil-water mixture, and can be widely applied to the fields of high-temperature flue gas and melt filtering.
Description
Technical field
The present invention relates to porous ceramics field, particularly relate to that uniform pore diameter is controlled, the three-dimensional through porous ceramics preparation in duct.
Background technology
Porous ceramic film material penetrates into various fields, multiple scientific domain such as environmental protection, energy-conservation, chemical industry, oil, smelting, food, pharmacy, biomedicine all be unable to do without porous ceramic film material, especially in filtration, sound-absorbing, electrode materials, catalysis, heat insulation, biomaterial etc., has irreplaceable effect.
The Pore Characteristics of porous ceramic film material determines its performance, and the homogeneity in duct and connectivity have material impact to porous ceramics performance.Within 2006, Journal of membrane science magazine is at the 285th volume, the first phase, the porous ceramic film preparing mean pore size 6.3 μm with the irregular fly ash grain of form is described in 173-181 page, find that ceramic membrane aperture is uneven, there is obvious duct defect, pore size distribution is wider, is difficult to avoid leaching of fine particle in filtering separation process.Good duct connectivity is not only conducive to improving flux, and when cell channels blocks, still can provide more path for the flowing of fluid, thus can maintain good flux.In addition, uniform through duct has great advantage for the mechanical stability of reduction stress concentration, maintenance strainer.At present, preparation technology's comparatively perfect of porous ceramics, the regulation and control of air hole structure, distribution, size are relatively ripe, but are still difficult to obtain porous ceramics completely evenly through in three dimension scale.
Powder sintering is a kind of traditional pore-creating technique, and it sinters after being piled up by ceramic powder, and particle contacts position is sintered together by mass transfer, provides ceramics strength, and the original position reservation after sintering of particle packing gap, become porous ceramics duct.This technology has simply, directly, without the need to the feature of additionally auxiliary pore-creating.
But when conventional powder prepares porous ceramics by powder sintering, improve diffusion mass transfer speed often through heating up, form neck sintering, this unavoidably can cause melting and the sintering of particle surface, causes the contraction in duct and closes.This is because the particle that conventional ball mill or wet method obtain, all there is numerous defect in its surface and inside, and specific surface area is also often comparatively large, has higher sintering activity.These active crystal faces can impel particle surface melting in sintering process, reduce the significant temp interval that diffusion mass transfer is taken as the leading factor, accelerate mass transfer mode to be become the disadvantageous liquid-flow mass transfer of pore structure from diffusion mass transfer, cause sintering neck intensity and duct original position retain between generation contradiction.Fundamentally say, the source of contradiction is exactly that conventional powder does not have obvious temperature head between surface diffusion mass transfer and melting mass transfer in sintering, can not only rely on to improve the mode of sintering temperature and obtain high-strength sintered neck and the hole that do not affect between particle.In addition, the agglomerating particles existed in powder, also can subside and sharply shrink, having a strong impact on the formation in duct in sintering process.
In order to overcome these problems existed in powder sintering, people take a lot of method, such as, microwave sintering, hot pressed sintering, discharge plasma sintering and electric spark sintering etc., these methods are all the diffusion mass transfers in order to shorten between sintering time and reinforcing particle, make hole have little time shrink and retained; Also can reduce sintering temperature to a certain extent simultaneously, reduce melt surface degree, stop intergranular reunion activated sintering.
In addition, by introducing nanocrystal, improving neck sintering activity, promoting mass transfer, reduce sintering temperature, also while raising sintering neck intensity, the contraction of hole can be reduced.The chemical reaction between feed particles can also be adopted, promote that neck is intensified-sintered, reduce the contraction of hole.Also can generate low melting point oxide in particle surface oxidation, utilize this oxide compound mass transfer sintering carried out between particle to obtain the sintered neck of intensity raising.
In a word, powder sintering piles up the ununiformity in hole and the contraction of later stage sintering process hole early stage, makes porous ceramics often have wide in range pore size distribution, and containing part lipostomous, half through hole, connectivity is not enough, limits the application of porous ceramics at separation field.
Summary of the invention
(1) goal of the invention
The defect of porous ceramics is prepared for existing powder sintering, the technical problem that this patent solves is the compact spheroidal particle adopting sintering activity lower, by pore-creating tightly packed between powder particle, the surface utilizing tightly packed interparticle contact part to form neck sintering and low activity densification is difficult to the feature that melt surface sintering occurs, after high temperature sintering, particle packing neck formation sintering, provides ceramics strength, piles up gap and remains and form even duct.Utilize the method that this patent provides, adopt the compact spheroidal particle that the activity of uniform particle diameter is lower to pile up sintering, the porous ceramics with even through duct can be formed.This duct has evenly, three-dimensional through characteristic, and porous ceramics has higher intensity.
(2) technical scheme
The powder raw material that the present invention uses, having good sphericity, uniform particle sizes, densification, feature that sintering activity is lower, is prepared by heat plasma technology.
Through certain accumulation mode, the particle of good sphericity, uniform particle diameter can be formed tightly packed, piles up gap and can form even, the three-dimensional through hole in duct.
Select injectiong coagulation shaping technology, mainly consider the original advantage that this technique has in spheroidal particle banking process: first particle is formed tightly packed, then organic reaction substance forms network structure in particulate interspaces polymerization, make closelypacked spheroidal particle form bonding, bonding process can not cause any impact to the arrangement of particle.And in organic substance burn off process, degradation production can thoroughly be got rid of from the accumulation gap of particle, particle packing body structure is constant.
In sintering process, fine and close particle can avoid particle to occur self to subside, blocking duct.Low frit activity can make particle be formed in sintered neck process at mass transfer sintering, effectively avoids melt surface to cause particle re-arrangement, pore contraction etc.By optimizing sintering temperature, can realize particle neck and effectively sinter, there is not the rearrangement between melting and particle in particle surface, obtains the porous ceramics that high strength, duct are through.
The preparation of described porous ceramics is divided into three committed steps:
A spheroidal particle is piled up, and obtains and piles up porous nickel, three-dimensional through particle stack.
B adopts the solidifying system of note above-mentioned particle stack to be carried out in-situ consolidation, form green compact.
C, by green sintering, forms sintered neck between particle, and hole original position retains formation duct.
Described even through duct is enclosed heap by spherical wall and is formed, pattern rule.
It should be noted that by controlling the granularity of spheroidal particle, can regulate and control to pile up the size in duct linearly, finally can the pore size of linear regulation porous ceramics.
The invention provides a kind of preparation method of smooth duct, namely by smooth, spherical particle packing boring technique.In addition, also can by controlling the roughness on spheroidal particle surface, the roughness of regulation and control channel surfaces.
The present invention also provides step and the processing parameter of Inject & congeal shaping.The compact spheroidal particle of certain content, organic premixed liquid (organic monomer, linking agent, water), catalyzer, initiator are mixed, spheroidal particle is piled up according to specific mode, then by regulating and controlling temperature initiated polymerization, high strength green compact are obtained after abundant drying, finally sinter, obtain target porous ceramics.
In some embodiments, described organic monomer is acrylamide, and linking agent is N, N-DMAA (MBAM), catalyzer is Tetramethyl Ethylene Diamine (TEMED), and initiator is ammonium persulphate, and the concentration of premixed liquid marks with the concentration of acrylamide.
In some embodiments, described premixed liquid concentration is 2-20wt.%.
In some embodiments, MBAM and organic monomer mass ratio are 1:30-1:10.
In some embodiments, (NH
4)
2s
2o
4occupy the 3-10% of machine monomer mass mark.
In some embodiments, (NH
4)
2s
2o
4be 1:1-1:6 with the mass ratio of TEMED.
In some embodiments, the temperature of reaction of described polyreaction is 30-80 DEG C, and the reaction times is 10-90min.
In some embodiments, the accumulation mode of spheroidal particle is that slurry is piled up, or natural subsidence is piled up, or centrifugal settling is piled up, or tapped bulk again after natural subsidence.
The present inventor, through a series of exploration, by the influence factor of each link of regulation and control injectiong coagulation shaping technology and the accumulation mode of uniform-spherical particle, obtains the porous ceramic film material that duct is evenly through.Be the spheroidal particle of 30-90 μm by selecting median size, ceramic body mean pore size is distributed between 8-20 μm linearly, percentage of open area is between 30-45%, ceramic body intensity can reach 30MPa, and this material has good application prospect in wastewater treatment, dedusting, gas distribution, support body material, filtering high-temperature flue gas or melt filtration etc.
(3) technique effect
The porous ceramics that the present invention obtains have duct evenly, three-dimensional through, aperture linearly can be in harmonious proportion the high feature of intensity, compared with the porous ceramics prepared with existing powder sintering, not only duct is even, and whole duct is through, and the intensity of porous ceramics is high.No matter the porous ceramics that gas or liquid are prepared by the present invention, flux obviously promotes.Porous ceramics of the present invention is applied in oily water separation, obtain good oil-water separation, and velocity of separation is fast.The tubular porous ceramic strainer that the thickness utilizing preparation is 5mm, aperture is 8 μm carries out peanut oil/water separable performance can be tested: through stirring the peanut oil aqueous solution of preparation 1vol.% at 60 DEG C, this oil-water mixture is relatively uniform, oil is dispersed in water with the form of micro emulsion oil droplet, and initial TOC value is 843mg/L.Porous ceramic pipe is carried out oily water separation under 30KPa, and result is shown as: oily water separation efficiency reaches more than 99%; Initial flux reaches 10
5l/ (m
2h), flux stabilized after 40min, and decline degree is less, maintains 4.0 × 10
4l/ (m
2h); Through 10 filtration-backwash cycles, strainer flux still maintains initial level.These results suggest that, the porous nickel prepared by the present invention, strainer without hole defect, have very high filtration efficiency; Its higher flux derives from the connectivity of 3 D pore canal, and fluid flowing is unobstructed, and drag losses is little; Through duct is that the flow multi-path that brings of fluid is selected, and makes porous ceramics have good flux and maintains ability; Smooth duct characteristic makes dirty substance not easily adhere to, and during backwash, fouling product easily washes away, and brings good cycle applications ability.
Accompanying drawing explanation
Accompanying drawing 1 is the schema that the present invention prepares porous ceramics.
Accompanying drawing 2 is the uniform pore diameter prepared by the present invention, three-dimensional through porous ceramics cross-section photographs.
Embodiment
1 preparation process of the present invention is described further by reference to the accompanying drawings.
The preparation flow figure of uniform pore diameter, three-dimensional through porous ceramics is as shown in Figure 1:
(1) compact spheroidal particle of low frit activity refers to the spheroidal particle of specific surface area close to theoretical value of particle, and these particles can be obtained by melting, especially adopts thermal plasma nodularization melting to obtain.
(2) configuration of premixed liquid: be 1:30-1:10 according to organic monomer 2-20wt.%, MBAM and organic monomer mass ratio, configuration premixed liquid.
(3) premixed liquid is poured in spheroidal particle, add catalyzer, initiator, mix, and realize the tightly packed of spheroidal particle by specific method.Wherein (NH
4)
2s
2o
4occupy the 3-10% of machine monomer mass mark, (NH
4)
2s
2o
4be 1:1-1:6 with the mass ratio of TEMED polyvalent alcohol.
(4) by the particle that above-mentioned accumulation is good, carry out polyreaction solidification at being placed in 30-80 DEG C, the reaction times is 10-90min.
(5) proceed solidification at the base substrate be cured being placed in 50-70 DEG C, set time, 5-15h, realized body drying.
(6) for different spheroidal particle, dry base substrate sinters 2-5h at 1200-1700 DEG C, obtains described porous ceramics.The section of porous ceramics as shown in Figure 2.
Embodiment 1
Be 1:30, (NH according to organic monomer 2wt.%, MBAM and organic monomer mass ratio
4)
2s
2o
4occupy 3%, (NH of machine monomer mass mark
4)
2s
2o
4be the ratio of 1:1 with the mass ratio of TEMED polyvalent alcohol, configuration mixed solution.Poured into by mixed solution in the spherical alumina silicon grain of particle diameter 30 μm, control premixed liquid add-on, be configured to uniform slurry, at being placed in 80 DEG C, polymerization reaction time is 10min.After body drying, 1200 DEG C of sintering 2h, obtain mean pore size 8 μm, the porous ceramics of intensity 25MPa.
Embodiment 2
Be 1:20, (NH according to organic monomer 6wt.%, MBAM and organic monomer mass ratio
4)
2s
2o
4occupy 5%, (NH of machine monomer mass mark
4)
2s
2o
4be the ratio of 1:2 with the mass ratio of TEMED polyvalent alcohol, configuration mixed solution.Mixed solution being poured into particle diameter is in the spherical alumina silicon grain of 50 μm, and control premixed liquid add-on, be configured to uniform slurry, at being placed in 70 DEG C, polymerization reaction time is 20min.After body drying, 1200 DEG C of sintering 2h, obtain mean pore size 15 μm, the porous ceramics of intensity 15MPa.
Embodiment 3
Be 1:20, (NH according to organic monomer 10wt.%, MBAM and organic monomer mass ratio
4)
2s
2o
4occupy 7%, (NH of machine monomer mass mark
4)
2s
2o
4be the ratio of 1:3 with the mass ratio of TEMED polyvalent alcohol, configuration mixed solution.Mixed solution being poured into particle diameter is in the spherical alumina silicon grain of 50 μm, adds excessive premixed liquid, and stir and leave standstill, by the particle jolt ramming in liquid phase after natural subsidence, at being placed in 50 DEG C, polymerization reaction time is 40min.After body drying, 1200 DEG C of sintering 2h, obtain mean pore size 10 μm, the porous ceramics of intensity 27MPa.
Embodiment 4
Be 1:15, (NH according to organic monomer 15wt.%, MBAM and organic monomer mass ratio
4)
2s
2o
4occupy 8%, (NH of machine monomer mass mark
4)
2s
2o
4be the ratio of 1:4 with the mass ratio of TEMED polyvalent alcohol, configuration mixed solution.Mixed solution being poured into particle diameter is in the spherical alumina silicon grain of 50 μm, adds excessive premixed liquid, and stir and leave standstill, by the particle jolt ramming in liquid phase after natural subsidence, at being placed in 50 DEG C, polymerization reaction time is 40min.After body drying, 1300 DEG C of sintering 2h, obtain mean pore size 7 μm, the porous ceramics of intensity 35MPa.
Embodiment 5
Be 1:10, (NH according to organic monomer 20wt.%, MBAM and organic monomer mass ratio
4)
2s
2o
4occupy 10%, (NH of machine monomer mass mark
4)
2s
2o
4be the ratio of 1:6 with the mass ratio of TEMED polyvalent alcohol, configuration mixed solution.Mixed solution being poured into particle diameter is in the spherical alumina silicon grain of 50 μm, adds excessive premixed liquid, and stir and leave standstill, by the particle jolt ramming in liquid phase after natural subsidence, at being placed in 50 DEG C, polymerization reaction time is 40min.After body drying, 1300 DEG C of sintering 5h, obtain mean pore size 5 μm, the porous ceramics of intensity 40MPa.
Embodiment 6
Be 1:30, (NH according to organic monomer 2wt.%, MBAM and organic monomer mass ratio
4)
2s
2o
4occupy 3%, (NH of machine monomer mass mark
4)
2s
2o
4be the ratio of 1:1 with the mass ratio of TEMED polyvalent alcohol, configuration mixed solution.Poured into by mixed solution in the Spherical alumina particles of particle diameter 30 μm, control premixed liquid add-on, be configured to uniform slurry, at being placed in 80 DEG C, polymerization reaction time is 10min.After body drying, 1700 DEG C of sintering 2h, obtain mean pore size 8 μm, the porous ceramics of intensity 28MPa.
Embodiment 7
Be 1:30, (NH according to organic monomer 2wt.%, MBAM and organic monomer mass ratio
4)
2s
2o
4occupy 3%, (NH of machine monomer mass mark
4)
2s
2o
4be the ratio of 1:1 with the mass ratio of TEMED polyvalent alcohol, configuration mixed solution.Poured into by mixed solution in the spherical mullite particle of particle diameter 30 μm, control premixed liquid add-on, be configured to uniform slurry, at being placed in 80 DEG C, polymerization reaction time is 10min.After body drying, 1700 DEG C of sintering 2h, obtain mean pore size 8 μm, the porous ceramics of intensity 30MPa.
Embodiment 8
Be 1:12, (NH according to organic monomer 10wt.%, MBAM and organic monomer mass ratio
4)
2s
2o
4occupy 8%, (NH of machine monomer mass mark
4)
2s
2o
4be the ratio of 1:3 with the mass ratio of TEMED polyvalent alcohol, configuration mixed solution.Mixed solution being poured into particle diameter is in the magnesium oxide spheroidal particle of 30 μm, adds excessive premixed liquid, and stir and leave standstill, by the particle jolt ramming in liquid phase after natural subsidence, at being placed in 50 DEG C, polymerization reaction time is 40min.After body drying, 1800 DEG C of sintering 2h, obtain mean pore size 8 μm, the porous ceramics of intensity 50MPa.
Embodiment 9
Be 1:15, (NH according to organic monomer 20wt.%, MBAM and organic monomer mass ratio
4)
2s
2o
4occupy 15%, (NH of machine monomer mass mark
4)
2s
2o
4be the ratio of 1:6 with the mass ratio of TEMED polyvalent alcohol, configuration mixed solution.Mixed solution being poured into particle diameter is 25 μm, and composition is magnesium-aluminium spinel (MgAl
2o
4) spheroidal particle in, add excessive premixed liquid, stir leave standstill, by the particle jolt ramming in liquid phase after natural subsidence, at being placed in 50 DEG C, polymerization reaction time is 40min.After body drying, 1700 DEG C of sintering 5h, obtain mean pore size 5 μm, the porous ceramics of intensity 40MPa.
Embodiment 10
Be 1:8, (NH according to organic monomer 7wt.%, MBAM and organic monomer mass ratio
4)
2s
2o
4occupy 10%, (NH of machine monomer mass mark
4)
2s
2o
4be the ratio of 1:6 with the mass ratio of TEMED polyvalent alcohol, configuration mixed solution.Mixed solution being poured into particle diameter is in the spherical SiC particle of 20 μm, adds excessive premixed liquid, and stir and leave standstill, by the particle jolt ramming in liquid phase after natural subsidence, at being placed in 50 DEG C, polymerization reaction time is 40min.After body drying, 1700 DEG C of sintering 5h, obtain mean pore size 4 μm, the porous ceramics of intensity 45MPa.
Claims (11)
1. the porous ceramics that a duct is evenly through, described porous ceramics comprises the duct between ceramic skeleton and ceramic skeleton, it is characterized in that, described ceramic skeleton by low activity compact spheroidal particle pile up after sintering form, described duct piled up by compact spheroidal particle after gap formed after sintering.
2. porous ceramics according to claim 1, is characterized in that, the percentage of open area of described porous ceramics is between 30-45%, and mean pore size is between 8-20 μm, and described porous ceramics intensity is 15-40MPa.
3. porous ceramics according to claim 1, is characterized in that, described low activity compact spheroidal particle is spherical silica, aluminum oxide, zirconium white, mullite, periclasite, magnesium-aluminium spinel and silicon carbide.
4. porous ceramics according to claim 1, it is characterized in that, the size in described porous ceramics duct can by the particle size adjustment of regulation and control low activity compact spheroidal particle, and the slickness in described porous ceramics duct can be regulated by the surface flatness of regulation and control low activity compact spheroidal particle.
5. the preparation method of the porous ceramics according to the arbitrary claim of claim 1-4, is characterized in that, comprise the following steps:
(1) organic premixed liquid is prepared: organic monomer, linking agent and water are formed organic premixed liquid;
(2) particle packing: added in low activity compact spheroidal particle by organic premixed liquid, mixes after adding catalyzer and initiator, and realizes the tightly packed of spheroidal particle by specific method;
(3) Inject & congeal shaping: regulating and controlling temperature initiated polymerization, obtains high strength green compact after abundant drying;
(4) green sintering: by green sintering, particle forms porous ceramic skeleton, forms sintered neck between particle, and hole original position retains formation duct.
6. method according to claim 5, is characterized in that, the method for step (2) particle packing, comprises jolt ramming after slurry accumulation, natural subsidence, centrifugal settling, natural subsidence.
7. method according to claim 5, is characterized in that, described in step (1), organic monomer is acrylamide, linking agent is N, N-DMAA (MBAM), catalyzer is Tetramethyl Ethylene Diamine (TEMED), and initiator is ammonium persulphate.
8. method according to claim 7, it is characterized in that, the concentration of described organic premixed liquid is labeled as 2-20wt% with the concentration of acrylamide, MBAM and organic monomer mass ratio are 1:30-1:10, ammonium persulphate occupies the 3-10% of machine monomer mass mark, and the mass ratio of ammonium persulphate and TEMED is 1:1-1:6.
9. method according to claim 5, is characterized in that, the temperature of reaction of step (3) polyreaction is 30-80 DEG C, and the reaction times is 10-90min; Drying temperature 50-70 DEG C, time of drying 5-15h.
10. method according to claim 5, is characterized in that, step (4) sintering temperature is 1200-1700 DEG C, sintering time 2-5h.
The purposes of 11. porous ceramicss according to the arbitrary claim of claim 1-5, for wastewater treatment, dedusting, gas distribution, support body material, filtering high-temperature flue gas or melt filtration.
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Cited By (14)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN105906365A (en) * | 2016-04-19 | 2016-08-31 | 中国科学院过程工程研究所 | Method of preparing porous ceramic through low-temperature sintering |
| CN106512103A (en) * | 2016-10-17 | 2017-03-22 | 西南交通大学 | Preparation method of porous structural ceramic material |
| CN106588097A (en) * | 2016-12-09 | 2017-04-26 | 深圳中清环境科技有限公司 | Ceramic support for water treatment and preparation method of ceramic support |
| CN106747399A (en) * | 2016-12-12 | 2017-05-31 | 天津津航技术物理研究所 | A kind of preparation method of fine grain wideband light-weight magnesite-alumina spinel refractories |
| CN106747346A (en) * | 2016-11-15 | 2017-05-31 | 中国科学院过程工程研究所 | A kind of porous ceramic film and preparation method |
| CN106982008A (en) * | 2016-01-18 | 2017-07-25 | 华中科技大学 | One kind evaporation induction liquid TRT |
| CN109516805A (en) * | 2017-09-20 | 2019-03-26 | 德州迈特新材料研究中心 | A kind of super structure composite material and preparation method thereof with stable weak negative dielectric properties |
| CN109689196A (en) * | 2016-09-09 | 2019-04-26 | H.E.F.公司 | More material powders with composite particles for additive synthesis |
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| CN111099913A (en) * | 2020-01-03 | 2020-05-05 | 内蒙古工业大学 | Raw material for preparing porous ceramic material and preparation method of porous ceramic material |
| CN112811928A (en) * | 2021-01-08 | 2021-05-18 | 武汉科技大学 | Lightweight periclase-silicon carbide-carbon refractory material and preparation method thereof |
| CN113387694A (en) * | 2021-06-24 | 2021-09-14 | 重庆奥福精细陶瓷有限公司 | Particle filter and preparation method thereof |
| CN113786689A (en) * | 2021-09-22 | 2021-12-14 | 重庆奥福精细陶瓷有限公司 | Narrow micropore distribution cordierite honeycomb ceramic filter and preparation method and application thereof |
Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101323528A (en) * | 2008-07-15 | 2008-12-17 | 南京工业大学 | Preparation of continuous hole graded ceramic tube |
| CN102390935A (en) * | 2011-08-22 | 2012-03-28 | 沈阳工业大学 | Method for preparing strontium titanate film having spherical grain accumulated porous structure |
| CN103232228A (en) * | 2013-04-26 | 2013-08-07 | 山东大学 | Preparation method of porous aluminum oxide composite ceramic |
-
2015
- 2015-06-10 CN CN201510316543.9A patent/CN104909820B/en active Active
Patent Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101323528A (en) * | 2008-07-15 | 2008-12-17 | 南京工业大学 | Preparation of continuous hole graded ceramic tube |
| CN102390935A (en) * | 2011-08-22 | 2012-03-28 | 沈阳工业大学 | Method for preparing strontium titanate film having spherical grain accumulated porous structure |
| CN103232228A (en) * | 2013-04-26 | 2013-08-07 | 山东大学 | Preparation method of porous aluminum oxide composite ceramic |
Non-Patent Citations (1)
| Title |
|---|
| CHEN LU ET AL.: "Preparation of hollow silica spheres by DC thermal plasma", 《POWDER TECHNOLOGY》 * |
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| CN105906365A (en) * | 2016-04-19 | 2016-08-31 | 中国科学院过程工程研究所 | Method of preparing porous ceramic through low-temperature sintering |
| CN105906365B (en) * | 2016-04-19 | 2018-07-20 | 中国科学院过程工程研究所 | A kind of method that low-temperature sintering prepares porous ceramics |
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