CN1887797A - Fast prepn process of machinable high-strength SiN-B4C ceramic - Google Patents
Fast prepn process of machinable high-strength SiN-B4C ceramic Download PDFInfo
- Publication number
- CN1887797A CN1887797A CN 200610088995 CN200610088995A CN1887797A CN 1887797 A CN1887797 A CN 1887797A CN 200610088995 CN200610088995 CN 200610088995 CN 200610088995 A CN200610088995 A CN 200610088995A CN 1887797 A CN1887797 A CN 1887797A
- Authority
- CN
- China
- Prior art keywords
- sintering
- ceramic
- strength
- stove
- fast
- 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
- 239000000919 ceramic Substances 0.000 title claims abstract description 30
- 238000000034 method Methods 0.000 title claims description 17
- 230000008569 process Effects 0.000 title description 8
- 238000005245 sintering Methods 0.000 claims abstract description 44
- 238000001035 drying Methods 0.000 claims abstract description 6
- 238000002156 mixing Methods 0.000 claims abstract description 6
- 239000000654 additive Substances 0.000 claims abstract description 4
- 230000000996 additive effect Effects 0.000 claims abstract description 3
- 239000000463 material Substances 0.000 claims description 14
- 239000003595 mist Substances 0.000 claims description 10
- LFQSCWFLJHTTHZ-UHFFFAOYSA-N Ethanol Chemical compound CCO LFQSCWFLJHTTHZ-UHFFFAOYSA-N 0.000 claims description 5
- 238000000498 ball milling Methods 0.000 claims description 5
- 238000012856 packing Methods 0.000 claims description 5
- 238000005303 weighing Methods 0.000 claims description 5
- 229960000935 dehydrated alcohol Drugs 0.000 claims description 2
- 238000002360 preparation method Methods 0.000 abstract description 8
- 239000000843 powder Substances 0.000 abstract description 7
- 238000005452 bending Methods 0.000 abstract description 6
- 238000005516 engineering process Methods 0.000 abstract description 4
- 229910052581 Si3N4 Inorganic materials 0.000 abstract 1
- PNEYBMLMFCGWSK-UHFFFAOYSA-N aluminium oxide Inorganic materials [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 abstract 1
- 229910010293 ceramic material Inorganic materials 0.000 abstract 1
- 238000001816 cooling Methods 0.000 abstract 1
- 229910052593 corundum Inorganic materials 0.000 abstract 1
- 238000007599 discharging Methods 0.000 abstract 1
- 238000011049 filling Methods 0.000 abstract 1
- 238000010438 heat treatment Methods 0.000 abstract 1
- 238000005086 pumping Methods 0.000 abstract 1
- 229910001845 yogo sapphire Inorganic materials 0.000 abstract 1
- 239000013078 crystal Substances 0.000 description 9
- 230000003287 optical effect Effects 0.000 description 4
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 3
- 229910002804 graphite Inorganic materials 0.000 description 3
- 239000010439 graphite Substances 0.000 description 3
- 239000000203 mixture Substances 0.000 description 3
- 239000002245 particle Substances 0.000 description 3
- 230000002776 aggregation Effects 0.000 description 2
- 239000000956 alloy Substances 0.000 description 2
- 229910045601 alloy Inorganic materials 0.000 description 2
- 230000007797 corrosion Effects 0.000 description 2
- 238000005260 corrosion Methods 0.000 description 2
- 238000000280 densification Methods 0.000 description 2
- 239000006185 dispersion Substances 0.000 description 2
- 239000011159 matrix material Substances 0.000 description 2
- 229910052582 BN Inorganic materials 0.000 description 1
- PZNSFCLAULLKQX-UHFFFAOYSA-N Boron nitride Chemical compound N#B PZNSFCLAULLKQX-UHFFFAOYSA-N 0.000 description 1
- 238000005054 agglomeration Methods 0.000 description 1
- 238000004220 aggregation Methods 0.000 description 1
- 238000000576 coating method Methods 0.000 description 1
- 230000007812 deficiency Effects 0.000 description 1
- 230000002950 deficient Effects 0.000 description 1
- 230000006866 deterioration Effects 0.000 description 1
- 238000009792 diffusion process Methods 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- 239000004744 fabric Substances 0.000 description 1
- 239000008187 granular material Substances 0.000 description 1
- 238000007731 hot pressing Methods 0.000 description 1
- 238000009413 insulation Methods 0.000 description 1
- 235000012054 meals Nutrition 0.000 description 1
- 239000000320 mechanical mixture Substances 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 150000002739 metals Chemical class 0.000 description 1
- 238000005498 polishing Methods 0.000 description 1
- 238000001272 pressureless sintering Methods 0.000 description 1
- 230000009467 reduction Effects 0.000 description 1
- 230000035939 shock Effects 0.000 description 1
- 230000009466 transformation Effects 0.000 description 1
Images
Landscapes
- Ceramic Products (AREA)
Abstract
The fast preparation process of machinable high-strength Si3N4-BN ceramic belongs to the field of structural ceramic preparing technology. The present invention prepares compact heterogenous Si3N4-BN ceramic through mixing Si3N4 powder, h-BN powder and sintering additive Y2O3-Al2O3, ball mixing, drying, filling in mold, setting the mold in discharging plasma sintering furnace, vacuum pumping, heating to 1600-1700 deg.c, sintering at 30-50 MPa for 3-8 min and cooling in the furnace. The fast preparation process has short sintering time, low sintering temperature and low cost, and the prepared ceramic material has high bending strength and excellent machinability.
Description
Technical field
A kind of quick method for preparing machinable high-strength SiN-B 4 C ceramic belongs to the structural ceramics preparing technical field.
Background technology
The Si that contains hexagonal boron nitride (h-BN) disperse phase
3N
4Pottery is the most outstanding class processable ceramic of present combination property.Not only keep and improved Si
3N
4The performances such as ceramic good elevated temperature strength, creep resistant, anti-thermal shock, but also give material outstanding preventing corrosion from molten metals performance, low Young's modulus, and can carry out precision optical machinery processing by enough hard alloy cutters, satisfy complex shaped components to the harsh requirement of forming materials.
Because h-BN bending strength very low (about 100MPa), add in the ceramic matrix and can cause strength deterioration, and the h-BN powder reunites and be difficult for opening, in sintering process, be easy to assemble growth and form big defective, cause material actual strength and Si
3N
4Ceramic phase is more excessive than reduction amplitude, and its mechanics reliability can't satisfy the high-end applications requirement.From the preparation method, work as Si
3N
4When-BN pottery had good machinability (BN＞20%), the bending strength that adopts hot-pressing sintering technique to obtain only was 400-500MPa, and the loss of intensity reaches (Si more than 50%
3N
4Pottery is 900-1400MPa), and the Si that adopts pressureless sintering to obtain
3N
4-BN pottery bending strength is then lower.Obtain high strength Si
3N
4-BN processable ceramic, its microscopic structure must satisfy such characteristics, namely with long column shape β-Si
3N
4Crystal grain forms the interlocking frame structure, h-BN crystal grain through may keep tiny and even dispersion at crystal boundary, agglomeration not.The complicated presoma preparation technology of the utilizations such as Japanese Kusunose T is coated to Si with nanoscale BN
3N
4Particle surface eliminate the problem that h-BN crystal grain is reunited with this, and h-BN crystal grain remains in the nanoscale scope behind hot pressed sintering, the Si of their preparation
3N
4Therefore-BN processable ceramic (BN volume content 20%-40%) bending strength reaches about 850-1100MPa (Kusunose T, Sekino T, Choa Y H, Niihara K.J Am Ceram Soc, 2002,85:2678-2688), yet its technology comprises complicated presoma reaction coating process, and adopt hot pressed sintering to need high sintering temperature (1800-1850 ℃) and long-time insulation (2-4h), complex process is tediously long, and the cycle reaches 7 days (even longer), and preparation efficiency is very low, preparation cost is very high, thereby has limited to a great extent the application of materials.
Summary of the invention
For above-mentioned deficiency, the purpose of this invention is to provide the Si that a kind of quick low temperature prepares high strength, easily processes
3N
4The method of-BN complex phase ceramic.This method realizes by following technical though: utilize Si
3N
4With the difference of h-BN sintering diffusion coefficient, adopt suitable sinter additives, utilize fast characteristics of discharge plasma sintering technique low temperature, realize the sintering to this system, make Si
3N
4Full densification forms column β-Si
3N
4Crystal grain interlocking structure, and h-BN does not participate in densification process substantially, crystallite dimension still rest on the primary granule size or the long width of cloth very little; Owing to the effect of Joule heat, the temperature of powder surface raises rapidly, simultaneously the powder in the mould is applied high pressure simultaneously, and the flowability of powder quick can effectively be opened the h-BN powder agglomerates, makes the thin brilliant even dispersion of h-BN at Si
3N
4In the matrix.Form desirable microscopic structure with this, realize the unification of high strength and machinability.
A kind of quick method for preparing machinable high-strength SiN-B 4 C ceramic is characterized in that, comprises the steps:
1) takes by weighing the Si of average grain diameter 0.3-1um
3N
4The h-BN micro mist of micro mist and average grain diameter 0.3-1um, h-BN volume content 20%-40% wherein, all the other are Si
3N
4
2) add additive Y
2O
3-Al
2O
3, its weight is the 6%-10% of material after final the mixing;
3) with material ball milling mixing 12-48 hour in dehydrated alcohol, after drying, in the mould of packing into;
4) mould that material will be housed places the discharge plasma sintering stove, predetermined fixed pressure 30-50MPa is evacuated to below the 10Pa, with the 150-250 degree/minute speed be warmed up to the 1600-1700 degree and carry out sintering, sintering current ratio of pulse length to the total cycle length 12: 1, sintering time 3-8 minute;
5) sample cooled off with stove after sintering finished, and obtained fine and close Si
3N
4-BN complex phase ceramic.
The invention has the advantages that technical process simple (only needing raw meal is carried out mechanical mixture), sintering time short (total process is in 30 minutes) has fast characteristics of efficient energy-saving, for realizing having high strength Si
3N
4Simple, quick, the low-cost preparation of-BN processable ceramic provides a new way.The material that utilizes the inventive method to prepare has high strength, machinable performance characteristics simultaneously.
Description of drawings
Fig. 1 is the prepared Si of embodiment 1-3
3N
4The XRD collection of illustrative plates of-BN complex phase ceramic; Can find out, after sintering, most Si
3N
4Change mutually the β phase into by α, a small amount of α-Si is only arranged
3N
4Remaining, BN content reduces, and phase transformation is more complete.
Fig. 2 is the prepared Si of embodiment 1
3N
4The section SEM photo of-BN complex phase ceramic; Can find out that h-BN behind the sintering (crystal grain that is tabular or sheet among the figure) grows up to some extent, but still remains on about 1um, is evenly distributed.
Fig. 3 is the prepared Si of embodiment 2
3N
4The polishing etch surface SEM photo of-BN complex phase ceramic; Can find out that microscopic structure is meticulous evenly behind the sintering, by the β phase Si of big L/D ratio
3N
4Columnar grain consists of (h-BN is removed) in corrosion process.
Fig. 4 is the prepared Si of embodiment 2
3N
4The section SEM photo of-BN complex phase ceramic; Can find out that h-BN behind the sintering (being tiny bar-shaped or granular crystal grain among the figure) significantly less than 1um, has kept the size of initial h-BN particle substantially, and not have obviously to assemble and big aggregate.
Fig. 5 is the prepared Si of embodiment 3
3N
4The section SEM photo of-BN complex phase ceramic; Can find out that h-BN behind the sintering (among the figure in the form of sheets or granular crystal grain) crystallite dimension is still very little, most of less than 1um, substantially kept the size of initial h-BN particle; Because h-BN content is bigger, some aggregations occurred, a small amount of grain growth surpasses 1um.
Embodiment
Embodiment 1:
Take by weighing the Si of average grain diameter 1 μ m
3N
4The h-BN micro mist of micro mist and average grain diameter 0.5 μ m, wherein the h-BN volume content accounts for 20%, adds Y again
2O
3-Al
2O
3Its weight accounts for final mixture material 6%, ball milling mixed 12 hours in absolute ethyl alcohol, after the drying, in the graphite jig of packing into, place discharge plasma sintering (SPS) stove, fixed pressure 30MPa in advance under the room temperature, be evacuated to 8Pa after, be warmed up to 1600 degree with 250 degrees/mins speed and carry out sintering, sintering current pulse ratio 12: 1, sintering time 3 minutes.Sample cooled off with stove after sintering finished, and obtained Si
3N
4-BN complex phase ceramic.Si after measured
3N
4The relative density of-BN complex phase ceramic is 94.2%, and bending strength is σ f3=1111MPa, can carry out precision optical machinery processing by enough hard alloy cutters.
Embodiment 2:
Take by weighing the Si of average grain diameter 0.5 μ m
3N
4The h-BN micro mist of micro mist and average grain diameter 0.3 μ m makes the h-BN volume content account for 30%, adds Y again
2O
3-Al
2O
3Its weight accounts for final mixture material 8%, ball milling mixed 24 hours in absolute ethyl alcohol, after the drying, in the graphite jig of packing into, place discharge plasma sintering (SPS) stove, fixed pressure 40MPa in advance under the room temperature, be evacuated to 8Pa after, be warmed up to 1650 degree with 150 degrees/mins speed and carry out sintering, sintering current pulse ratio 12: 1, sintering time 5 minutes.Sample cooled off with stove after sintering finished, and obtained Si
3N
4-BN complex phase ceramic.Si after measured
3N
4The relative density of-BN complex phase ceramic is 93.7%, and flexural strength is σ
F3=920MPa can carry out precision optical machinery processing by enough inserted tools.
Embodiment 3:
Take by weighing the Si of average grain diameter 0.3 μ m
3N
4The h-BN micro mist of micro mist and average grain diameter 0.3 μ m makes the h-BN volume content account for 40%, adds Y again
2O
3-Al
2O
3Its weight accounts for final mixture material 10%, ball milling mixed 48 hours in absolute ethyl alcohol, after the drying, in the graphite jig of packing into, place discharge plasma sintering (SPS) stove, fixed pressure 50MPa in advance under the room temperature, be evacuated to 6Pa after, be warmed up to 1700 degree with 200 degrees/mins speed and carry out sintering, sintering current pulse ratio 12: 1, sintering time 8 minutes.Sample cooled off with stove after sintering finished, and obtained Si
3N
4-BN complex phase ceramic.Si after measured
3N
4The relative density of-BN complex phase ceramic is 93.8%, and flexural strength is σ
F3=702MPa can carry out precision optical machinery processing by enough inserted tools.
Claims (1)
1. a method for preparing machinable high-strength SiN-B 4 C ceramic fast is characterized in that, comprises the steps:
1) takes by weighing the Si of average grain diameter 0.3-1um
3N
4The h-BN micro mist of micro mist and average grain diameter 0.3-1um, h-BN volume content 20%-40% wherein, all the other are Si
3N
4
2) add additive Y
2O
3-Al
2O
3, its weight is the 6%-10% of material after final the mixing;
3) with material ball milling mixing 12-48 hour in dehydrated alcohol, after drying, in the mould of packing into;
4) mould that material will be housed places the discharge plasma sintering stove, predetermined fixed pressure 30-50MPa is evacuated to below the 10Pa, with the 150-250 degree/minute speed be warmed up to the 1600-1700 degree and carry out sintering, sintering current ratio of pulse length to the total cycle length 12: 1, sintering time 3-8 minute;
5) sample cooled off with stove after sintering finished, and obtained fine and close Si
3N
4-BN complex phase ceramic.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CNB2006100889957A CN100432017C (en) | 2006-07-28 | 2006-07-28 | Fast prepn process of machinable high-strength SiN-B4C ceramic |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CNB2006100889957A CN100432017C (en) | 2006-07-28 | 2006-07-28 | Fast prepn process of machinable high-strength SiN-B4C ceramic |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN1887797A true CN1887797A (en) | 2007-01-03 |
| CN100432017C CN100432017C (en) | 2008-11-12 |
Family
ID=37577077
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CNB2006100889957A Expired - Fee Related CN100432017C (en) | 2006-07-28 | 2006-07-28 | Fast prepn process of machinable high-strength SiN-B4C ceramic |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN100432017C (en) |
Cited By (10)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101817684A (en) * | 2010-03-25 | 2010-09-01 | 西安交通大学 | Method for coating h-BN coating on surface of porous Si3N4 substrate |
| CN101565308B (en) * | 2009-06-04 | 2012-05-23 | 山东大学 | Silicon nitride ceramics enhanced by boron nitride nanotube and preparation method thereof |
| CN101456739B (en) * | 2008-10-08 | 2012-10-31 | 中国科学院上海硅酸盐研究所 | Si3N4-BN porous ceramic of super lyophobic metal melt, preparation method and use thereof |
| CN101955357B (en) * | 2008-04-25 | 2012-11-28 | 西安交通大学 | Processable complex-phase ceramic material and preparation method thereof as well as secondary hardening heat treatment method |
| CN104284860A (en) * | 2012-05-09 | 2015-01-14 | Esk陶瓷有限两合公司 | Boron nitride agglomerates, method for the production thereof and usage thereof |
| CN104529412A (en) * | 2014-12-27 | 2015-04-22 | 西安交通大学 | Preparation method of nano-scale hexagonal boron nitride/silicon dioxide multi-phase ceramic material |
| CN105036749A (en) * | 2015-06-30 | 2015-11-11 | 陕西科技大学 | Hot-pressing preparation method for hexagonal boron nitride-added silicon nitride |
| CN105272269A (en) * | 2015-10-20 | 2016-01-27 | 西安邮电大学 | Preparation method of Si3N4/h-BN nano-composite ceramics |
| CN108117396A (en) * | 2017-12-11 | 2018-06-05 | 陕西科技大学 | The preparation method of biomedical ceramics material based on silicon nitride |
| CN110105072A (en) * | 2019-06-04 | 2019-08-09 | 宁波市大工新材料科技有限公司 | A kind of preparation method of high hardness silicon nitride material |
Family Cites Families (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS61158868A (en) * | 1984-12-29 | 1986-07-18 | 株式会社東芝 | Manufacture of ceramic sintered body |
| US4883776A (en) * | 1988-01-27 | 1989-11-28 | The Dow Chemical Company | Self-reinforced silicon nitride ceramic of high fracture toughness and a method of preparing the same |
| CN1250762A (en) * | 1999-09-24 | 2000-04-19 | 清华大学 | Process for preparing boron nitride compounded conducting ceramic evaporator by non-pressure sinter method |
| CN1246253C (en) * | 2004-05-17 | 2006-03-22 | 清华大学 | Manufacturing method of high thermoconductivity high trength silicon nitride ceramic |
| US20060084566A1 (en) * | 2004-10-19 | 2006-04-20 | General Electric Company | Multiphase ceramic nanocomposites and method of making them |
| CN1282627C (en) * | 2005-01-26 | 2006-11-01 | 清华大学 | Micro processing process for silicon nitride ceramic parts |
| CN1793042A (en) * | 2006-01-06 | 2006-06-28 | 清华大学 | In-situ flexible silicon nitride base ceramic and super-speed sintering process |
-
2006
- 2006-07-28 CN CNB2006100889957A patent/CN100432017C/en not_active Expired - Fee Related
Cited By (13)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101955357B (en) * | 2008-04-25 | 2012-11-28 | 西安交通大学 | Processable complex-phase ceramic material and preparation method thereof as well as secondary hardening heat treatment method |
| CN101456739B (en) * | 2008-10-08 | 2012-10-31 | 中国科学院上海硅酸盐研究所 | Si3N4-BN porous ceramic of super lyophobic metal melt, preparation method and use thereof |
| CN101565308B (en) * | 2009-06-04 | 2012-05-23 | 山东大学 | Silicon nitride ceramics enhanced by boron nitride nanotube and preparation method thereof |
| CN101817684B (en) * | 2010-03-25 | 2012-08-15 | 西安交通大学 | Method for coating h-BN coating on surface of porous Si3N4 substrate |
| CN101817684A (en) * | 2010-03-25 | 2010-09-01 | 西安交通大学 | Method for coating h-BN coating on surface of porous Si3N4 substrate |
| CN104284860B (en) * | 2012-05-09 | 2018-02-13 | 3M创新有限公司 | Boron nitride aggregate, Its Preparation Method And Use |
| CN104284860A (en) * | 2012-05-09 | 2015-01-14 | Esk陶瓷有限两合公司 | Boron nitride agglomerates, method for the production thereof and usage thereof |
| CN104529412A (en) * | 2014-12-27 | 2015-04-22 | 西安交通大学 | Preparation method of nano-scale hexagonal boron nitride/silicon dioxide multi-phase ceramic material |
| CN104529412B (en) * | 2014-12-27 | 2016-06-29 | 西安交通大学 | A kind of preparation method of nanoscale hexagonal boron nitride/silicon dioxide diphase ceramic material |
| CN105036749A (en) * | 2015-06-30 | 2015-11-11 | 陕西科技大学 | Hot-pressing preparation method for hexagonal boron nitride-added silicon nitride |
| CN105272269A (en) * | 2015-10-20 | 2016-01-27 | 西安邮电大学 | Preparation method of Si3N4/h-BN nano-composite ceramics |
| CN108117396A (en) * | 2017-12-11 | 2018-06-05 | 陕西科技大学 | The preparation method of biomedical ceramics material based on silicon nitride |
| CN110105072A (en) * | 2019-06-04 | 2019-08-09 | 宁波市大工新材料科技有限公司 | A kind of preparation method of high hardness silicon nitride material |
Also Published As
| Publication number | Publication date |
|---|---|
| CN100432017C (en) | 2008-11-12 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN100432017C (en) | Fast prepn process of machinable high-strength SiN-B4C ceramic | |
| CN101456737B (en) | Boron carbide base composite ceramic and preparation method thereof | |
| CN110483085B (en) | Whisker reinforced alumina composite ceramic and preparation method and application thereof | |
| CN109987941B (en) | High-entropy ceramic composite material with oxidation resistance and preparation method and application thereof | |
| CN101462880B (en) | Silicon carbide based reinforced composite ceramic and preparation | |
| CN100432016C (en) | Method of manufacturing aluminium nitride/boron nitride multiple phase ceramic | |
| CN113024257A (en) | Liquid phase sintering slip casting SiC ceramic valve material and preparation method thereof | |
| CN104030686B (en) | A kind of high tenacity silicon carbide ceramics and preparation method thereof | |
| CN1259281C (en) | Silicon nitride - boron nitride- silicon dioxide ceramic wave-transparent material and preparation process thereof | |
| CN115386813A (en) | In-situ growth TiAl 3 Ti of whisker 3 AlC 2 Preparation method of particle reinforced aluminum-based composite material | |
| CN1182069C (en) | Prepn. of submicron high-purity transparent alumina ceramic material | |
| CN1092163C (en) | Heterogeneous zirconia-mullite refractory material with sintered bound phase and its preparation | |
| CN118344167A (en) | MCMB-based laser 3D printing CfSiC composite material and preparation method thereof | |
| CN103849790A (en) | In-situ generated homogenous nano ceramic-metal composite material and preparation method thereof | |
| CN101551012A (en) | A carbonaceous silicon carbide sealed ring and preparation method thereof | |
| CN109231990A (en) | A kind of preparation method of tungsten carbide-diamond composite | |
| CN1793044A (en) | Process for preparing nano complex phase ceramic material by in-situ reaction | |
| CN1234641C (en) | Preparing method for Ti3 SiC2 material without TiC impurity | |
| CN109652679B (en) | Carbon nanotube and endogenous nano TiC particle mixed reinforced aluminum-based composite material and preparation method thereof | |
| Zhang et al. | Research on toughening mechanisms of alumina matrix ceramic composite materials improved by rare earth additive | |
| CN113105250B (en) | Pomegranate-shaped black ceramic particles for additive manufacturing and preparation method and application thereof | |
| CN113186432B (en) | Aluminum oxide reinforced aluminum-based laminated composite material with mineral bridge structure and preparation method thereof | |
| CN115044792A (en) | Particle-reinforced titanium-based composite material and preparation method thereof | |
| CN113957294A (en) | CrCoNi intermediate entropy alloy reinforced Al-based composite material and preparation method thereof | |
| CN114411010A (en) | Preparation method of diamond reinforced aluminum-based high-thermal-conductivity composite 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 | ||
| C17 | Cessation of patent right | ||
| CF01 | Termination of patent right due to non-payment of annual fee |
Granted publication date: 20081112 Termination date: 20110728 |