CN106830902A - A kind of method that use phase transition under high pressure method prepares polycrystalline alpha-aluminium oxide - Google Patents
A kind of method that use phase transition under high pressure method prepares polycrystalline alpha-aluminium oxide Download PDFInfo
- Publication number
- CN106830902A CN106830902A CN201710128089.3A CN201710128089A CN106830902A CN 106830902 A CN106830902 A CN 106830902A CN 201710128089 A CN201710128089 A CN 201710128089A CN 106830902 A CN106830902 A CN 106830902A
- Authority
- CN
- China
- Prior art keywords
- sintering
- sample
- high pressure
- under high
- phase transition
- 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.)
- Pending
Links
Classifications
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B35/00—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
- C04B35/01—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on oxide ceramics
- C04B35/10—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on oxide ceramics based on aluminium oxide
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B35/00—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
- C04B35/01—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on oxide ceramics
- C04B35/10—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on oxide ceramics based on aluminium oxide
- C04B35/111—Fine ceramics
- C04B35/1115—Minute sintered entities, e.g. sintered abrasive grains or shaped particles such as platelets
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B35/00—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
- C04B35/622—Forming processes; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B35/00—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
- C04B35/622—Forming processes; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
- C04B35/64—Burning or sintering processes
- C04B35/645—Pressure sintering
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
- C04B2235/70—Aspects relating to sintered or melt-casted ceramic products
- C04B2235/74—Physical characteristics
- C04B2235/78—Grain sizes and shapes, product microstructures, e.g. acicular grains, equiaxed grains, platelet-structures
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
- C04B2235/70—Aspects relating to sintered or melt-casted ceramic products
- C04B2235/74—Physical characteristics
- C04B2235/78—Grain sizes and shapes, product microstructures, e.g. acicular grains, equiaxed grains, platelet-structures
- C04B2235/781—Nanograined materials, i.e. having grain sizes below 100 nm
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
- C04B2235/70—Aspects relating to sintered or melt-casted ceramic products
- C04B2235/96—Properties of ceramic products, e.g. mechanical properties such as strength, toughness, wear resistance
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
- C04B2235/70—Aspects relating to sintered or melt-casted ceramic products
- C04B2235/96—Properties of ceramic products, e.g. mechanical properties such as strength, toughness, wear resistance
- C04B2235/9607—Thermal properties, e.g. thermal expansion coefficient
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Ceramic Engineering (AREA)
- Manufacturing & Machinery (AREA)
- Materials Engineering (AREA)
- Structural Engineering (AREA)
- Organic Chemistry (AREA)
- Inorganic Chemistry (AREA)
- Compositions Of Oxide Ceramics (AREA)
Abstract
The present invention relates to a kind of method that use phase transition under high pressure method prepares polycrystalline alpha-aluminium oxide, methods described is with γ Al2O3It is raw material, by carrying out purified treatment and pre-molding to raw material, after assembling sintering unit, at 300 1500 DEG C, is sintered under the conditions of 1 25 GPa superhigh-pressure high-temps, then subsequent sample is processed and performance detection is carried out.This method makes γ Al2O3It is directly translated into polycrystalline α Al2O3, can prepare that thing is mutually single, even structure, with superperformance, the purity such as hardness and consistency high polycrystalline α Al higher2O3Material.
Description
Technical field
The present invention relates to using γ-Al2O3It is raw material, purified treatment is carried out by raw material, under the conditions of superhigh-pressure high-temp
High-performance polycrystal Alpha-alumina is prepared by phase transition under high pressure method(That is α-Al2O3)Method.Belong to Inorganic Non-metallic Materials neck
Domain.
Technical background
Aluminum oxide has many allomorphisms, and what is be currently known has kind more than 10, mainly there is 3 kinds of crystal formations, i.e. α-Al2O3、β-
Al2O3、γ-Al2O3。γ-Al2O3With α-Al2O3It is that aluminum oxide is primarily present form.γ-Al2O3Belong to transitional form oxidation
Aluminium, is powdery, microspheroidal or column white solid.Its crystal structure is different from commercial alumina.α-Al2O3It is a kind of important
Inorganic Non-metallic Materials, is most stable of thing phase in all aluminum oxide.
Nanometer α-Al2O3Polycrystalline, with good mechanical property(High rigidity, high tenacity, high intensity);Fracture strength be α-
Al2O3The several times of monocrystalline.Due to α-Al2O3Crystal grain is easily grown up and loses its nanostructured at high temperature, and synthesis is this to be caused completely
Close nano-multicrystal bulk material is challenging,
The preparation of nano-multicrystal ceramic material is more with nanometer powder as original material, and nanometer powder is present reunites, adsorbs, being difficult to point
Scattered problem constrains the mechanical property of sintering gained polycrystalline material.How nanocrystal length in high-temperature sintering process is suppressed
Greatly, it is kept nano-meter characteristic and sintered body high-compactness, be also that nano-multicrystal material prepares the technical barrier for facing.
The content of the invention
The purpose of the present invention is just being directed to the weak point in the presence of above-mentioned prior art and is providing one kind and use high pressure
The method that phase transition method prepares polycrystailine alpha alumina.
The purpose of the present invention can be realized by following technique measures:
It is of the invention use the method that phase transition under high pressure method prepares polycrystailine alpha alumina with purity higher than 80%, crystallite dimension as 5nm-
500 μm of γ-Al2O3It is raw material, is prepared under high-temperature and high-pressure conditions, its processing step is as follows:
A, Feedstock treating detection:Purity is processed higher than the 80%, γ-Al that crystallite dimension is 5nm-500 μm with absolute ethyl alcohol2O3It is former
Material, after pouring out waste liquid, is dried under the conditions of 120 DEG C;Afterwards plus deionized water carries out pre-molding, in vacuum after to be formed
Molded samples are vacuum dried in drying oven;
B, assembling sintering unit:The raw material of pre-molding is wrapped up with Metal Inclusions, sample is prevented at high temperature under high pressure
It is contaminated;The raw material of the pre-molding after parcel is put into treated metal cup again, being fitted into high-pressure synthesizer is carried out
Assembling, the sintering unit that then will be assembled is put into standby in 120 DEG C of baking ovens of freeze-day with constant temperature;
C, HTHP sintering:HTHP sintering is carried out using press, sintering pressure is 1-25GPa, when pressure reaches setting
After pressure, heat up heating, heat preservation sintering under conditions of being 300-1500 DEG C in sintering temperature;Soaking time is -50 minutes 10 seconds;
After insulation terminates, stop heating, then slowly start step-down;
D, following process treatment:The sample in synthetic cavity is taken out, external metallization inclusion enclave is removed, to inner sample polishing, thrown
Light obtains α-Al2O3Polycrystal, α-Al2O3The crystallite dimension of polycrystal is 5nm-500 μm;
E, properties of sample detection:Sample thing phase and sample crystallite dimension are detected by XRD and SEM.
Heretofore described γ-Al2O3The crystal formation of raw material uses XRD determining, and utilizes laser particle size detection assay crystal grain chi
It is very little.
In the present invention material of Metal Inclusions described in step b be titanium, molybdenum or tantalum, carried out polishing before parcel and
Polishing, then deoiled, ultrasonic wave cleaning, infrared drying.
Unit is sintered in the present invention described in step b with graphite-pipe as heater element, magnesia and pyrophyllite are pressure transmission Jie
Matter.
Beneficial effects of the present invention are as follows:
Nano-multicrystal α-Al prepared by the present invention2O3Material, the raw material of use is the γ-Al of pure phase2O3In powder, and sample not
Containing other impurity, with purity it is high, thing is mutually single the characteristics of.
Nano-multicrystal α-Al prepared by the present invention2O3Material, it is possible to use micron-scale γ-Al2O3It is raw material.Avoid
With manocrystalline powders as original material, the reunion that exists, adsorb, be difficult to scattered problem.
Nano-multicrystal α-Al prepared by the present invention2O3Material, is prepared using superhigh-pressure high-temp phase transition method.Using super
High pressure makes raw material be broken into uniform crystal grain, and ultra-high pressure condition can suppress the crystal grain that high temperature orders about and grow up problem.This method
Successfully solve nanocrystal growing up in high-temperature sintering process.
Brief description of the drawings
Fig. 1 is sintering unit assembling schematic diagram.
Sequence number in figure:1 is plug, and 2 is dolomite sleeve pipe, and 3 is pyrophyllite in lumps, and 4 is graphite flake, and 5 is graphite-pipe, and 6 is sample
Product, 7 is magnesia tube, and 8 is oxidation magnesium sheet, and 9 is titanium sheet.
Specific embodiment
The present invention is below with reference to embodiment(Accompanying drawing)It is further described:
Embodiment 1:
A, Feedstock treating detection:It is the γ-Al that 99%, crystallite dimension is 5 μm by purity2O3Raw material is processed with absolute ethyl alcohol,
Go out waste liquid, the raw material after treatment is put into 120 DEG C of drying in baking oven;Raw material after drying adds deionized water as binding agent, precompressed
Shaping;Molded samples are put into vacuum drying oven and are vacuum dried;Crystal formation by XRD, grain size analysis with laser grain size analyzer raw material is four
Square γ-Al2O3。
B, assembling sintering unit:The raw material of pre-molding is wrapped up with Metal Inclusions, prevents sample high in high temperature
Pressure is contaminated;The raw material of the pre-molding after parcel is put into treated metal cup again, is fitted into high-pressure synthesizer
Assembled, the sintering unit that then will be assembled is put into standby in 120 DEG C of baking ovens of freeze-day with constant temperature;Described sintering unit with
Graphite-pipe is heater element, and magnesia and pyrophyllite are transmission medium.As shown in figure 1, being burnt according to the installation diagram assembling of sintering unit
Statement of account unit.
C, HTHP sintering:HTHP sintering is carried out using press, sintering pressure is 3GPa, and pressure reaches setting pressure
After power, heat temperature raising, under conditions of being 1300 DEG C in sintering temperature, soaking time is 5 minutes;After insulation terminates, stop adding
Heat, then slowly starts step-down.
D, following process treatment:The sample in synthetic cavity is taken out, external metallization inclusion enclave is removed, inner sample is beaten
Mill, polishing obtain α-Al2O3Polycrystal, α-Al2O3The crystallite dimension of polycrystal is 5nm-500 μm.
E, properties of sample detection:Sample thing phase and sample crystallite dimension are detected by XRD and SEM.
Show that sample has high rigidity and high tenacity by hardness and toughness test.By XRD diffraction pattern analysis, sample
Comprise only α-Al2O3Single-phase, and crystalline phase stabilization, the average crystal grain size of SEM detection samples is nano particle, and sample is microcosmic
Structure is than more uniform.High quality alpha-the Al prepared using this technique2O3Material thing is mutually single, even structure, with hardness high and
Consistency, heat endurance high.
Embodiment 2
A, Feedstock treating detection:It is the γ-Al that 99.5%, crystallite dimension is 20 μm by purity2O3Raw material is used at absolute ethyl alcohol
Reason, pours out waste liquid, and the raw material after treatment is put into 120 DEG C of drying in baking oven;Raw material after drying adds deionized water as bonding
Agent, pre-molding;Molded samples are put into vacuum drying oven and are vacuum dried;By XRD, the crystalline substance of grain size analysis with laser grain size analyzer raw material
Type is square γ-Al2O3。
The step of the present embodiment, b was same as Example 1, was not repeated.
C, HTHP sintering:HTHP sintering is carried out using press, sintering pressure is 5GPa, and pressure reaches setting pressure
After power, heat temperature raising, under conditions of being 1500 DEG C in sintering temperature, soaking time is 50 minutes;After insulation terminates, stop adding
Heat, then slowly starts step-down.
The step of the present embodiment, d, e were same as Example 1, were not repeated.
Claims (4)
1. a kind of method that use phase transition under high pressure method prepares polycrystailine alpha alumina, it is characterised in that:Methods described processing step is such as
Under:
A, Feedstock treating detection:Purity is processed higher than the 80%, γ-Al that crystallite dimension is 5nm-500 μm with absolute ethyl alcohol2O3It is former
Material, after pouring out waste liquid, is dried under the conditions of 120 DEG C;Afterwards plus deionized water carries out pre-molding, in vacuum after to be formed
Molded samples are vacuum dried in drying oven;
B, assembling sintering unit:The raw material of pre-molding is wrapped up with Metal Inclusions, sample is prevented at high temperature under high pressure
It is contaminated;The raw material of pre-molding after parcel is put into treated metal cup again, being fitted into high-pressure synthesizer carries out group
Dress, the sintering unit that then will be assembled is put into standby in 120 DEG C of baking ovens of freeze-day with constant temperature;
C, HTHP sintering:HTHP sintering is carried out using press, sintering pressure is 1-25GPa, when pressure reaches setting
After pressure, heat up heating, heat preservation sintering under conditions of being 300-1500 DEG C in sintering temperature;Soaking time is -50 minutes 10 seconds;
After insulation terminates, stop heating, then slowly start step-down;
D, following process treatment:The sample in synthetic cavity is taken out, external metallization inclusion enclave is removed, to inner sample polishing, thrown
Light obtains α-Al2O3Polycrystal, α-Al2O3The crystallite dimension of polycrystal is 5nm-500 μm;
E, properties of sample detection:Sample thing phase and sample crystallite dimension are detected by XRD and SEM.
2. the method that use phase transition under high pressure method according to claim 1 prepares polycrystailine alpha alumina, it is characterised in that:It is described
γ-Al2O3The crystal formation of raw material uses XRD determining, and utilizes laser particle size detection assay crystallite dimension.
3. the method that use phase transition under high pressure method according to claim 1 prepares polycrystailine alpha alumina, it is characterised in that:Step
The material of Metal Inclusions described in b is titanium, molybdenum or tantalum, carries out needing grinding and buffing to process before parcel, is then gone
Oil, ultrasonic wave cleaning, infrared drying.
4. the method that use phase transition under high pressure method according to claim 1 prepares polycrystailine alpha alumina, it is characterised in that:Step
Unit is sintered described in b with graphite-pipe as heater element, magnesia and pyrophyllite are transmission medium.
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
CN201710128089.3A CN106830902A (en) | 2017-03-06 | 2017-03-06 | A kind of method that use phase transition under high pressure method prepares polycrystalline alpha-aluminium oxide |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
CN201710128089.3A CN106830902A (en) | 2017-03-06 | 2017-03-06 | A kind of method that use phase transition under high pressure method prepares polycrystalline alpha-aluminium oxide |
Publications (1)
Publication Number | Publication Date |
---|---|
CN106830902A true CN106830902A (en) | 2017-06-13 |
Family
ID=59137956
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
CN201710128089.3A Pending CN106830902A (en) | 2017-03-06 | 2017-03-06 | A kind of method that use phase transition under high pressure method prepares polycrystalline alpha-aluminium oxide |
Country Status (1)
Country | Link |
---|---|
CN (1) | CN106830902A (en) |
Cited By (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN111592360A (en) * | 2020-06-09 | 2020-08-28 | 欧阳晓平 | Polycrystal B4C-diamond double-layer composite material and preparation method thereof |
CN111606711A (en) * | 2020-06-09 | 2020-09-01 | 欧阳晓平 | Polycrystal B4C-SiC double-layer composite material and preparation method thereof |
CN113754431A (en) * | 2021-09-09 | 2021-12-07 | 浙江大学 | Method for preparing nano polycrystalline composite phase zirconia by ultrahigh pressure/high temperature phase change method |
Citations (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
KR20050068439A (en) * | 2003-12-30 | 2005-07-05 | 한국기계연구원 | Method for manufacturing alumium based alloyed powder having superior compactability |
CN101704680A (en) * | 2009-11-18 | 2010-05-12 | 中国地质大学(北京) | Submicron alumina ceramic material and preparation method thereof |
CN106007687A (en) * | 2016-05-11 | 2016-10-12 | 河南工业大学 | Method for preparing nano-polycrystalline coesite through high-pressure phase transition method |
-
2017
- 2017-03-06 CN CN201710128089.3A patent/CN106830902A/en active Pending
Patent Citations (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
KR20050068439A (en) * | 2003-12-30 | 2005-07-05 | 한국기계연구원 | Method for manufacturing alumium based alloyed powder having superior compactability |
CN101704680A (en) * | 2009-11-18 | 2010-05-12 | 中国地质大学(北京) | Submicron alumina ceramic material and preparation method thereof |
CN106007687A (en) * | 2016-05-11 | 2016-10-12 | 河南工业大学 | Method for preparing nano-polycrystalline coesite through high-pressure phase transition method |
Non-Patent Citations (1)
Title |
---|
陈玮等: "影响γ-Al2O3 →α-Al2O3 物相转变过程的因素研究", 《轻金属》 * |
Cited By (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN111592360A (en) * | 2020-06-09 | 2020-08-28 | 欧阳晓平 | Polycrystal B4C-diamond double-layer composite material and preparation method thereof |
CN111606711A (en) * | 2020-06-09 | 2020-09-01 | 欧阳晓平 | Polycrystal B4C-SiC double-layer composite material and preparation method thereof |
CN113754431A (en) * | 2021-09-09 | 2021-12-07 | 浙江大学 | Method for preparing nano polycrystalline composite phase zirconia by ultrahigh pressure/high temperature phase change method |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
Wan et al. | Effect of sintering temperature on the properties of fused silica ceramics prepared by gelcasting | |
Lee et al. | Preparation of nanostructured TiO2 ceramics by spark plasma sintering | |
CN106830902A (en) | A kind of method that use phase transition under high pressure method prepares polycrystalline alpha-aluminium oxide | |
JP6250817B2 (en) | Method for producing titanium nitride-titanium diboride-cubic boron nitride composite material | |
JP5485765B2 (en) | Method for producing aluminum titanate ceramic body | |
WO2010053122A1 (en) | Method for producing aluminum titanate ceramic | |
JP2014507509A (en) | α-Alumina abrasive and preparation method thereof | |
Jayaseelan et al. | Powder characteristics, sintering behavior and microstructure of sol–gel derived ZTA composites | |
JP7354247B2 (en) | High purity alpha alumina with high relative density, method for producing the alpha alumina, and use of the alpha alumina | |
WO2016073393A1 (en) | Microwave heating for gypsum manufacturing processes | |
Yang et al. | Effects of alumina sols on the sintering of α-alumina ceramics | |
CN114315361A (en) | Nanocrystalline silicon carbide superhard block and preparation method thereof | |
JP5057193B2 (en) | Manufacturing method of cubic boron nitride sintered body with high homogeneity, high density and high hardness | |
CN110092650B (en) | Light high-strength acicular mullite porous ceramic, preparation method thereof and filter | |
CN106829968B (en) | A method of nano-multicrystal stishovite is prepared using phase transition under high pressure method | |
CN107935576B (en) | Silicon nitride combined mullite-silicon carbide ceramic composite material and preparation method thereof | |
CN109734427A (en) | A kind of carbide composite ceramic crystallite abrasive material and preparation method thereof | |
Yasuda et al. | Microstructure and mechanical property of synthesized hydroxyapatite prepared by colloidal process | |
Kulkov et al. | Structure and mechanical properties of ZrO2-based systems | |
WO2016021464A1 (en) | α-ALUMINA MOLDED BODY AND METHOD FOR PRODUCING SAME | |
Shen et al. | Ordered coalescence of nanocrystals: a path to strong macroporous nanoceramics | |
Shujing et al. | Influences of composition of starting powders and sintering temperature on the pore size distribution of porous corundum-mullite ceramics | |
Borrell et al. | ZrTiO4 materials obtained by spark plasma reaction-sintering | |
CN103667845A (en) | Method for preparing nanostructure tungsten carbide composite bulk by high temperature and ultra high pressure | |
JP6502495B2 (en) | Ceramic powder with controlled size distribution |
Legal Events
Date | Code | Title | Description |
---|---|---|---|
PB01 | Publication | ||
PB01 | Publication | ||
SE01 | Entry into force of request for substantive examination | ||
SE01 | Entry into force of request for substantive examination | ||
WD01 | Invention patent application deemed withdrawn after publication |
Application publication date: 20170613 |
|
WD01 | Invention patent application deemed withdrawn after publication |