CN106699184A - Preparation method for Ti3SnC2 ceramic powder and prepared ceramic powder - Google Patents
Preparation method for Ti3SnC2 ceramic powder and prepared ceramic powder Download PDFInfo
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Abstract
The invention provides a preparation method for a Ti3SnC2 ceramic powder and the prepared ceramic powder, and belongs to the field of ceramic materials. The preparation method comprises the steps: mixing raw materials evenly, and carrying out ball milling for a first time for 2.5-3.5 h at a speed of 400-800 r/min, to obtain a ball-milled activated powder; carrying out a self-propagating reaction of the ball-milled activated powder to obtain a massive product; and carrying out ball milling of the massive product for a second time for 2.5-3.5 h at a speed of 250-350 r/min. The raw materials comprise, in parts by weight, 2.95-3.05 parts of a Ti powder, 0.6-1 part of an Sn powder, 0.2-0.6 part of an Al powder and 1.95-2.05 parts of a C powder. The preparation method has the advantages of simple process, low energy consumption and rapid reaction. The ceramic powder prepared by the preparation method has the advantages of low cost, high purity, high activity, large hardness, small particle size, good electric conductivity, good thermal conductivity and the like, and is suitable for industrialized production.
Description
Technical field
The present invention relates to ceramic material field, and more particularly to a kind of Ti3SnC2The preparation method of ceramic powders and its be obtained
Ceramic powders.
Background technology
The Barsoum of Univ Drexel of the U.S. teaches and " MAX phases " this concept was proposed at 2000, and MAX phases are Mn+ 1AXnThe abbreviation of phase (n=1,2or3).Wherein M represents a class early stage transition metal, and A represents some the 3rd or the 4th main groups
Element, X is C or N.Because this kind of MAX compounds have special cube layer structure, M6X layers and A layers is alternately arranged, and makes it
Have the premium properties of ceramics and metal concurrently, such as low-density, high-melting-point, good electrical and thermal conductivity, high elastic modulus, fracture high is tough
Property, resistance to oxidation, resistance to thermal shock, easy processing and there is good self lubricity.In high-temperature structural ceramics, brush and electrode material, can add
The fields such as work ceramic material, self-lubricating material have a wide range of applications.Therefore it is just ground both at home and abroad from after being found
The extensive attention of the person of studying carefully.
In MAX multiphase ceramics materials, Ti3SiC2Research it is the most extensive, Ti3AlC2、Cr2AlC、Ti2AlC it is existing at present compared with
Many reports and application, but Ti3SnC2But seldom it is related to.And Ti3SnC2In addition to the denominator with MAX multiphase ceramics materials,
Ti3SnC2Also there is more special performance.The hardness range of general MAX phases is 1.4-8GPa, and hardness has items different
Property, and Ti3SnC2Hardness be about 9.3GPa, more than most of MAX phase ceramics.In addition Ti3SnC2Also there is relatively low cutting
Shear modulu/bulk modulus ratio, with good fracture toughness and fatigue strength.
In the prior art, Sylvan Dubois etc. (2642-2644 pages of volume 90 of J Am Ceram Soc) are quiet using heat etc.
Pressure technology is prepared for Ti at 1315 DEG C3SnC2.But, the technology needs to be carried out under high-temperature and high-pressure conditions, and it is to equipment requirement
Height, also contains substantial amounts of TiC and Ti in complex process, and product2The impurity such as SnC.And traditional pressureless sintering is also required to original
Material first carries out alloying, due to forming various crystal phase structures in alloying process, makes to contain substantial amounts of impurities phase in sintered product.
The content of the invention
It is an object of the invention to provide a kind of Ti3SnC2The preparation method of ceramic powders, the method in being carried out under normal pressure,
Process is simple, energy consumption is low, is swift in response, and obtained product purity is high, active good, is suitable to industrialized production.
Another object of the present invention is to provide ceramic powders obtained in above-mentioned preparation method, its is easy to process, be easy to burn
Knot, and purity is high, active height, conductive and heat conductivility is excellent.
What embodiments of the invention were realized in：
A kind of Ti3SnC2The preparation method of ceramic powders, including：
With the rotating speed first time ball milling 2.5-3.5h of 400-800r/min after raw material is mixed, ball milling activation powder is obtained；Will
Ball milling activation powder carries out self-propagating reaction and obtains block product；By block product with second ball milling of rotating speed of 250-350r/min
2.5-3.5h。
Raw materials by weight portion meter include 2.95-3.05 parts Ti powder, 0.6-1 parts of Sn powder, 0.2-0.6 parts of Al powder with
And 1.95-2.05 parts of C powder.
A kind of Ti3SnC2Ceramic powders, it is according to above-mentioned Ti3SnC2The preparation method of ceramic powders is obtained.
The beneficial effect of the embodiment of the present invention is：
The Ti that the present invention is provided3SnC2The preparation method of ceramic powders, the method in carrying out self-propagating reaction under normal pressure, its
By the carrying out of autoreactivity heat release maintenance reaction, energy consumption is low, and process is simple is swift in response.Raw material is lived by high speed ball milling
Change, the particle diameter of raw material can on the one hand reduced makes it obtain nanoscale, the activity of intensified response thing；On the other hand, can
The passivating film on raw material surface is removed, the faults of construction such as dislocation, room are induced, causes distortion of lattice, increase interior energy and surface energy, entered
And change reactivity, promote SHS process reaction.Al powder is added in raw material to be used to fix lattice, crystal grain thinning, and
Substitution part Sn powder forms solid solution, it is possible to increase the activity of product is obtained, sintering activating energy is reduced；Using self-propagating reaction mistake
Larger thermal gradient and condensation rate in journey, improve wellability of the Al melts to C, the purity of reactant are improved, beneficial to MAX phases
Formed.
By Ti obtained in above-mentioned preparation method3SnC2Ceramic powders, its purity is high, and hardness, conduction and heat conductivility are excellent
It is good.The particle diameter of crystal grain is small, and activity is high, it is easy to sinter, processing characteristics is excellent.
Brief description of the drawings
Technical scheme in order to illustrate more clearly the embodiments of the present invention, below will be attached to what is used needed for embodiment
Figure is briefly described, it will be appreciated that the following drawings illustrate only certain embodiments of the present invention, thus be not construed as it is right
The restriction of scope, for those of ordinary skill in the art, on the premise of not paying creative work, can also be according to this
A little accompanying drawings obtain other related accompanying drawings.
Fig. 1 is Ti obtained in the embodiment of the present invention 13SnC2The XRD of ceramic powders；
Fig. 2 is the XRD of ceramic powders obtained in comparative example of the present invention 1.
Specific embodiment
To make the purpose, technical scheme and advantage of the embodiment of the present invention clearer, below will be in the embodiment of the present invention
Technical scheme be clearly and completely described.Unreceipted actual conditions person, builds according to normal condition or manufacturer in embodiment
The condition of view is carried out.Agents useful for same or the unreceipted production firm person of instrument, are the conventional product that can be obtained by commercially available purchase
Product.
Vegetable oil base water polyurethane coating of the embodiment of the present invention and preparation method thereof is specifically described below.
A kind of Ti3SnC2The preparation method of ceramic powders, the mixture using Ti powder, Sn powder, Al powder and C powder as raw material,
Self-propagating reaction is carried out after raw material ball milling is activated, then carries out ball mill grinding.
The component that Sn powder is used as in MAX phases forms solid solution.The addition of Al powder can fix lattice, crystal grain thinning, substitution
Part Sn forms solid solution, reduces the activation energy of sintering, makes small product grains particle diameter, active height, is easy to sintering, and processing characteristics is excellent
It is good.
When Ti powder：Sn powder：Al powder：The ratio of weight and number of C powder is 2.95-3.05：0.6-1：0.2-0.6：1.95-2.05
When, make raw material reaction abundant.Further, when Ti powder：Sn powder：Al powder：The ratio of weight and number of C powder is 3：0.6-1：0.2-0.6：
2, more preferably Ti powder：Sn powder：Al powder：The ratio of weight and number of C powder is 3：0.8：0.4：When 2, stock dispersion is uniform, and reaction is abundant,
The purity of product is high, and obtained product possesses hardness higher and preferably conductive and heat conductivility；Size of microcrystal is small, activity
Good, processing characteristics is excellent.
In order to the raw material for obtaining nanoscale makes to be swift in response fully, the granularity of each component is 200-400 mesh in raw material, compared with
Good is 400 mesh, and it is easy to refine the abundant ball milling of raw material.
First time ball milling is carried out to raw material before self-propagating reaction, the purpose is to raw material is activated.By raw material in 400-
The ball milling of 2.5-3.5h is carried out under the rotating speed of 800r/min, preferably with 500-700r/min or the more preferably rotating speed of 600r/min
Ball milling 3h.Its particle diameter that can reduce material powder, makes raw material granularity reach nanoscale, reactivity enhancing；Mechanical milling process is also
The passivating film of raw material surface particles is can remove, the faults of construction such as dislocation, room are induced, causes distortion of lattice, increase interior energy and table
Face energy, and then change reactivity, reach the purpose for promoting SHS process reaction.
In order to raw material is carried out into sufficient ball milling, the mass ratio of abrading-ball and raw material is 5-10 in first time mechanical milling process：1.
Preferably the ratio of grinding media to material is 10:1, its refinement more fully, and will not cause excessive damage to ball grinder.
It is preferred that above-mentioned first time ball milling operation is carried out under atmosphere of inert gases, raw material quilt in mechanical milling process is prevented
Oxidation, the reactivity of influence raw material and the quality of product.Because the cost of argon gas is relatively low, for reduces cost, it is preferred that selection
Argon gas is used as inert gas.
Ceramic post sintering is carried out using self-propagating reaction, by the carrying out of self-propagating reaction autoreactivity heat release maintenance reaction,
Energy consumption is low.The hot environment of self-propagating reaction makes it be swift in response simultaneously, and the production cycle shortens, cost reduction.Self-propagating reaction
During larger thermal gradient and condensation rate can improve wellability of the Al melts to C, improve the purity of reactant, be beneficial to
The formation of MAX phases.
Further, in preferred embodiments of the present invention, self-propagating reaction is ignited using tungsten filament coil.The ignition type
Self-propagating reaction, Al is solid-state before igniting, and the solid-state Al of post-reaction zone of igniting is melted successively, increases heat consumption,
Ignition temperature reduction；The raw material in simultaneous reactions region is shorter from the reaction time started is heated to, can thing prevent the life of impurities phase
Produce.
Due to raw material, particle diameter is smaller after first time ball milling, and reaction temperature is high during self- propagating, in order to prevent raw material
It is oxidized during the course of the reaction, preferably, the self-propagating reaction under atmosphere of inert gases in carrying out.For reduces cost, preferably
Ground, used as inert gas, it is also feasible using inert gases such as helium protect certainly to the relatively low argon gas of selection price.
In order to obtain, particle diameter is small, good processability ceramic powders, further, it is necessary to the block product after sintering is entered
Row ball milling.By block product with 5-10:1 ratio of grinding media to material in the ball milling that 2.5-3.5h is carried out under the rotating speed of 250-350r/min, compared with
Goodly with 10:1 ratio of grinding media to material makes the particle diameter of ceramic powders reach micro-nano in the rotating speed ball milling 3h of 300r/min.
In being carried out under normal pressure or vacuum condition, its process is simple, equipment requirement is not high, and energy consumption is low for above-mentioned preparation method, into
This is low.Pre-treatment and finishing time are short, and combustion reaction is rapid, and with short production cycle, cost is further reduced.
Using Ti obtained in the above method3SnC2Ceramic powders, its production is fast, and low cost, purity is high, and activity is high, it is easy to burn
Knot, particle diameter is small, is suitable to industrialized production.
Feature of the invention and performance are described in further detail with reference to embodiments.
Embodiment 1
A kind of Ti3SnC2The preparation method of ceramic powders, including：
Weigh Ti powder, the Sn powder that 8g granularities are 400 mesh, the Al powder that 4g granularities are 400 mesh that 30g granularities are 400 mesh and
20g granularities are the C powder of 400 mesh as raw material.Argon gas is placed in vacuum ball grinder and is passed through after raw material is mixed, with hard alloy
Ball, as abrading-ball, is 10 according to ratio of grinding media to material:1, ball milling activation powder is obtained with the rotating speed ball milling 3h of 600r/min.Ball milling is activated into powder
Body is placed in graphite crucible and places tungsten filament coil in surface, graphite crucible is placed in self-spreading high-temperature synthesizing device room and takes out true
Sky is simultaneously filled with argon gas, and being powered to igniting ball milling activation powder to tungsten filament coil carries out self-propagating reaction, obtains block product.By bulk
Product is placed in ball grinder, is 10 according to ratio of grinding media to material using sintered carbide ball as abrading-ball:1, with the rotating speed ball milling of 300r/min
3h, obtains Ti3SnC2Ceramic powders.
Embodiment 2
A kind of Ti3SnC2The preparation method of ceramic powders, including：
Weigh Ti powder, the Sn powder that 10g granularities are 400 mesh, the Al powder that 2g granularities are 400 mesh that 30g granularities are 400 mesh and
20g granularities are the C powder of 400 mesh as raw material.Argon gas is placed in vacuum ball grinder and is passed through after raw material is mixed, with hard alloy
Ball, as abrading-ball, is 10 according to ratio of grinding media to material:1, ball milling activation powder is obtained with the rotating speed ball milling 3h of 500r/min.Ball milling is activated into powder
Body is placed in graphite crucible and places tungsten filament coil in surface, graphite crucible is placed in self-spreading high-temperature synthesizing device room and takes out true
Sky is simultaneously filled with argon gas, and being powered to igniting ball milling activation powder to tungsten filament coil carries out self-propagating reaction, obtains block product.By bulk
Product is placed in ball grinder, is 10 according to ratio of grinding media to material using sintered carbide ball as abrading-ball:1, with the rotating speed ball milling of 300r/min
3h, obtains Ti3SnC2Ceramic powders.
Embodiment 3
A kind of Ti3SnC2The preparation method of ceramic powders, including：
Weigh Ti powder, the Sn powder that 6g granularities are 400 mesh, the Al powder that 6g granularities are 400 mesh that 30g granularities are 400 mesh and
20g granularities are the C powder of 400 mesh as raw material.Argon gas is placed in vacuum ball grinder and is passed through after raw material is mixed, with hard alloy
Ball, as abrading-ball, is 10 according to ratio of grinding media to material:1, ball milling activation powder is obtained with the rotating speed ball milling 3h of 700r/min.Ball milling is activated into powder
Body is placed in graphite crucible and places tungsten filament coil in surface, graphite crucible is placed in self-spreading high-temperature synthesizing device room and takes out true
Sky is simultaneously filled with argon gas, and being powered to igniting ball milling activation powder to tungsten filament coil carries out self-propagating reaction, obtains block product.By bulk
Product is placed in ball grinder, is 10 according to ratio of grinding media to material using sintered carbide ball as abrading-ball:1, with the rotating speed ball milling of 300r/min
3h, obtains Ti3SnC2Ceramic powders.
Embodiment 4
A kind of Ti3SnC2The preparation method of ceramic powders, including：
Weigh Ti powder, the Sn powder that 8g granularities are 200 mesh that 29.5g granularities are 200 mesh, the Al powder that 4g granularities are 200 mesh with
And the C powder that 19.5g granularities are 200 mesh is used as raw material.Argon gas is placed in vacuum ball grinder and is passed through after raw material is mixed, with hard
Alloying pellet, as abrading-ball, is 5 according to ratio of grinding media to material:1, ball milling activation powder is obtained with the rotating speed ball milling 2.5h of 400r/min.By ball milling
Activation powder is placed in graphite crucible and places tungsten filament coil in surface, and graphite crucible is placed in into self-spreading high-temperature synthesizing device room
Argon gas is inside vacuumized and is filled with, being powered to igniting ball milling activation powder to tungsten filament coil carries out self-propagating reaction, obtains block product.
Block product is placed in ball grinder, is 5 according to ratio of grinding media to material using sintered carbide ball as abrading-ball:1, with the rotating speed of 250r/min
Ball milling 2.5h, obtains Ti3SnC2Ceramic powders.
Embodiment 5
A kind of Ti3SnC2The preparation method of ceramic powders, including：
Weigh Ti powder, the Sn powder that 8g granularities are 200 mesh that 30.5g granularities are 200 mesh, the Al powder that 4g granularities are 200 mesh with
And the C powder that 20.5g granularities are 200 mesh is used as raw material.Argon gas is placed in vacuum ball grinder and is passed through after raw material is mixed, with hard
Alloying pellet, as abrading-ball, is 5 according to ratio of grinding media to material:1, ball milling activation powder is obtained with the rotating speed ball milling 3h of 800r/min.Ball milling is lived
Change powder to be placed in graphite crucible and place tungsten filament coil in surface, graphite crucible is placed in self-spreading high-temperature synthesizing device room
Argon gas is vacuumized and is filled with, being powered to igniting ball milling activation powder to tungsten filament coil carries out self-propagating reaction, obtains block product.Will
Block product is placed in ball grinder, is 3 according to ratio of grinding media to material using sintered carbide ball as abrading-ball:1, with the rotating speed ball of 350r/min
Mill 3.5h, obtains Ti3SnC2Ceramic powders.
Comparative example 1
A kind of preparation method of ceramic powders, including：
Weigh Ti powder, the Sn powder that 12g granularities are 400 mesh that 30g granularities are 400 mesh and the C powder that 20g granularities are 400 mesh
As raw material.Argon gas is placed in vacuum ball grinder and is passed through after raw material is mixed, using sintered carbide ball as abrading-ball, according to ball material
Than being 10:1, ball milling activation powder is obtained with the rotating speed ball milling 3h of 600r/min.Ball milling activation powder is placed in graphite crucible simultaneously
Tungsten filament coil is placed in surface, graphite crucible is placed in self-spreading high-temperature synthesizing device room and is vacuumized and is filled with argon gas, to tungsten
Wire coil is powered to igniting ball milling activation powder carries out self-propagating reaction, obtains block product.Block product is placed in ball grinder,
It is 10 according to ratio of grinding media to material using sintered carbide ball as abrading-ball:1, with the rotating speed ball milling 3h of 300r/min, obtain ceramic powders.
Comparative example 2
A kind of preparation method of ceramic powders, including：
Weigh Ti powder, the Sn powder that 8g granularities are 400 mesh, the Al powder that 4g granularities are 400 mesh that 30g granularities are 400 mesh and
20g granularities are the C powder of 400 mesh as raw material.Argon gas is placed in vacuum ball grinder and is passed through after raw material is mixed, with hard alloy
Ball, as abrading-ball, is 10 according to ratio of grinding media to material:1, ball milling activation powder is obtained with the rotating speed ball milling 3h of 300r/min.Ball milling is activated into powder
Body is placed in graphite crucible and places tungsten filament coil in surface, graphite crucible is placed in self-spreading high-temperature synthesizing device room and takes out true
Sky is simultaneously filled with argon gas, and being powered to igniting ball milling activation powder to tungsten filament coil carries out self-propagating reaction, obtains block product.By bulk
Product is placed in ball grinder, is 10 according to ratio of grinding media to material using sintered carbide ball as abrading-ball:1, with the rotating speed ball milling of 300r/min
3h, obtains ceramic powders.
Using micro-nano laser particle analyzer to Ti obtained in embodiment 1-53SnC2Ceramic powders and the obtained potteries of comparative example 1-2
The granularity of porcelain powder is tested, and its result is as shown in table 1.
The granularity of the ceramic powders of table 1.
It can be seen from table 1, ceramic powders particle diameter is small obtained in preparation method provided in an embodiment of the present invention, its crystal grain refinement
Performance is good.
To Ti obtained in embodiment 1-53SnC2Ceramic powders and the principal phase of ceramic powders and second obtained in comparative example 1-2
The composition of phase carries out X-ray analysis, and its result is as shown in table 2.
The crystalline phase composition of the ceramic powders of table 2.
| Project | Principal phase | Second phase |
| Embodiment 1 | Ti3SnC2 | TiC |
| Embodiment 2 | Ti3SnC2 | TiC、Ti2SnC |
| Embodiment 3 | Ti3SnC2 | TiC、Sn |
| Embodiment 4 | Ti3SnC2 | TiC、Ti2SnC |
| Embodiment 5 | Ti3SnC2 | TiC、Sn |
| Comparative example 1 | Ti2SnC | TiC、Sn |
| Comparative example 2 | Ti2SnC | TiC、Ti3SnC2 |
It can be seen from table 2, ceramic powders obtained in preparation method provided in an embodiment of the present invention, it mainly contains Ti3SnC2
Phase, product has Ti3SnC2The hardness of phase is high, electric conductivity and the good premium properties of thermal conductivity.According to embodiment 1 and comparative example 2
Analysis result understands that influence of the rotating speed of ball milling to reaction is larger during activation process, and the abundant ball milling of raw material being capable of intensified response
Thing activity, promotes Ti3SnC2The synthesis of phase.
Fig. 1 is referred to, its principal phase of ceramic powders obtained in embodiment 1 is Ti3SnC2, separately contain minimal amount of TiC second
Phase.Fig. 2 is referred to, its principal phase of ceramic powders obtained in comparative example 1 is Ti2SnC, separately using a small amount of TiC and Sn as the second phase.
From the foregoing, Al powder is for Ti3SnC2Synthesis serve vital, it can fix lattice, crystal grain thinning, reduce and burn
Knot activation energy, promotes Ti3SnC2The formation of phase.
In sum, Ti provided in an embodiment of the present invention3SnC2The preparation method of ceramic powders, abundant ball is passed through by raw material
After mill activation, synthesized using self-propagating reaction.Raw material is milled to nanoscale, and stock chart can be removed by ball milling
The passivating film in face, makes raw material reaction activity high.The carrying out of self-propagating reaction autoreactivity heat release maintenance reaction, its energy consumption is low, instead
Should be rapid.Al powder is added in raw material, sintering activating energy is reduced；Simultaneously using the thermal gradient and cooling velocity that self-propagating reaction is larger
Improve wellability of the Al melts to C, promote fixations of the Al to lattice, beneficial to Ti3SnC2The formation of phase, makes obtained product purity
Height, grain refining effect is good.Ceramic powders obtained in the preparation method, purity is high, and activity is high, it is easy to sinter, particle diameter is small, cost
It is low, it is suitable to industrialized production.
Embodiments described above is a part of embodiment of the invention, rather than whole embodiments.Reality of the invention
The detailed description for applying example is not intended to limit the scope of claimed invention, but is merely representative of selected implementation of the invention
Example.Based on the embodiment in the present invention, what those of ordinary skill in the art were obtained under the premise of creative work is not made
Every other embodiment, belongs to the scope of protection of the invention.
Claims (10)
1. a kind of Ti3SnC2The preparation method of ceramic powders, it is characterised in that including：
With the rotating speed first time ball milling 2.5-3.5h of 400-800r/min after raw material is mixed, ball milling activation powder is obtained；Will be described
Ball milling activation powder carries out self-propagating reaction and obtains block product；By the block product with the rotating speed of 250-350r/min second
Ball milling 2.5-3.5h；
The raw materials by weight portion meter include 2.95-3.05 parts Ti powder, 0.6-1 parts of Sn powder, 0.2-0.6 parts of Al powder with
And 1.95-2.05 parts of C powder.
2. preparation method according to claim 1, it is characterised in that the raw materials by weight portion meter includes 3 parts of institute
State Ti powder, 0.6-1 part of the Sn powder, 0.2-0.6 parts of the Al powder and 2 parts of the C powder.
3. preparation method according to claim 2, it is characterised in that the raw materials by weight portion meter includes 3 parts of institute
State Ti powder, 0.8 part of the Sn powder, 0.4 part of the Al powder and 2 parts of the C powder.
4. preparation method according to claim 1, it is characterised in that the granularity of the raw material is 200-400 mesh.
5. preparation method according to claim 1, it is characterised in that rotating speed during first time ball milling is 500-700r/
min。
6. preparation method according to claim 5, it is characterised in that rotating speed during first time ball milling is 600r/min.
7. preparation method according to claim 1, it is characterised in that the ratio of grinding media to material of first time ball milling is 5-10:1.
8. preparation method according to claim 1, it is characterised in that first time ball milling and self-propagating reaction are in indifferent gas
Carried out under body atmosphere.
9. preparation method according to claim 8, it is characterised in that the inert gas is argon gas.
10. a kind of Ti according to claim any one of 1-93SnC2Ceramic powders obtained in the preparation method of ceramic powders.
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Cited By (8)
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| CN107686352A (en) * | 2017-08-14 | 2018-02-13 | 河海大学 | A kind of high purity Ti2The preparation method of SnC ceramic materials |
| CN108726519A (en) * | 2018-07-05 | 2018-11-02 | 盐城工学院 | A method of preparing MXenes colloids using self-propagating high-temperature method synthesis MAX phase materials |
| CN109289995A (en) * | 2018-08-31 | 2019-02-01 | 中国科学院金属研究所 | Nanometer MAX phase ceramics powder or slurry of the ball milling preparation with lamellar structure and the method for regulating and controlling powder oxygen content |
| CN109400171A (en) * | 2018-12-16 | 2019-03-01 | 冯良荣 | A method of preparing MAX phase material |
| CN110872121A (en) * | 2018-08-29 | 2020-03-10 | 中国科学院上海硅酸盐研究所 | Nb-shaped alloy4AlC3Method for preparing ceramic powder |
| CN111097916A (en) * | 2020-01-09 | 2020-05-05 | 北京矿冶科技集团有限公司 | Preparation method of superfine high-purity rhenium powder |
| CN111647769A (en) * | 2020-06-18 | 2020-09-11 | 超威电源集团有限公司 | Storage battery grid alloy and preparation method thereof |
| CN112010305A (en) * | 2020-08-26 | 2020-12-01 | 盐城工学院 | Preparation (V, Ti)2AlC submicron flake and nanoparticle method |
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| 张树纲等: "Sn 掺杂对SHS法制备三元金属陶瓷Ti3AlC2的影响", 《粉末冶金工业》 * |
Cited By (11)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN107686352A (en) * | 2017-08-14 | 2018-02-13 | 河海大学 | A kind of high purity Ti2The preparation method of SnC ceramic materials |
| CN108726519A (en) * | 2018-07-05 | 2018-11-02 | 盐城工学院 | A method of preparing MXenes colloids using self-propagating high-temperature method synthesis MAX phase materials |
| CN110872121A (en) * | 2018-08-29 | 2020-03-10 | 中国科学院上海硅酸盐研究所 | Nb-shaped alloy4AlC3Method for preparing ceramic powder |
| CN109289995A (en) * | 2018-08-31 | 2019-02-01 | 中国科学院金属研究所 | Nanometer MAX phase ceramics powder or slurry of the ball milling preparation with lamellar structure and the method for regulating and controlling powder oxygen content |
| CN109289995B (en) * | 2018-08-31 | 2020-09-18 | 中国科学院金属研究所 | Method for preparing nanometer MAX phase ceramic powder or slurry with lamellar structure by ball milling and regulating and controlling oxygen content of powder |
| CN109400171A (en) * | 2018-12-16 | 2019-03-01 | 冯良荣 | A method of preparing MAX phase material |
| CN111097916A (en) * | 2020-01-09 | 2020-05-05 | 北京矿冶科技集团有限公司 | Preparation method of superfine high-purity rhenium powder |
| CN111647769A (en) * | 2020-06-18 | 2020-09-11 | 超威电源集团有限公司 | Storage battery grid alloy and preparation method thereof |
| CN111647769B (en) * | 2020-06-18 | 2021-03-30 | 超威电源集团有限公司 | Storage battery grid alloy and preparation method thereof |
| CN112010305A (en) * | 2020-08-26 | 2020-12-01 | 盐城工学院 | Preparation (V, Ti)2AlC submicron flake and nanoparticle method |
| CN112010305B (en) * | 2020-08-26 | 2023-06-27 | 盐城工学院 | Preparation (V, ti) 2 AlC submicron sheet and nanoparticle method |
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