CN105314971A - Method for preparing aluminum oxide based ternary eutectic in-situ composite ceramics through pulsed discharge plasma assisted melting treatment - Google Patents

Method for preparing aluminum oxide based ternary eutectic in-situ composite ceramics through pulsed discharge plasma assisted melting treatment Download PDF

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CN105314971A
CN105314971A CN201510890849.5A CN201510890849A CN105314971A CN 105314971 A CN105314971 A CN 105314971A CN 201510890849 A CN201510890849 A CN 201510890849A CN 105314971 A CN105314971 A CN 105314971A
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欧阳家虎
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王玉金
马永辉
刘占国
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Harbin Institute of Technology
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Abstract

The invention discloses a method for preparing aluminum oxide based ternary eutectic in-situ composite ceramics through pulsed discharge plasma assisted melting treatment, relates to a method for preparing aluminum oxide based eutectic in-situ composite ceramics and aims at solving the technical problems that eutectic ceramics with large sizes and complex shapes are difficult to prepare by using the existing method for preparing aluminum oxide based eutectic in-situ composite ceramics and the eutectic ceramics are thick and big in tissue and low in anisotropy and production efficiency. The method comprises the steps of firstly, preheating raw materials; secondly, carrying out mechanical alloying; thirdly, molding by cold pressing; and fourthly, carrying out pulsed discharge plasma assisted melting. The method is applied to preparation of aluminum oxide based ternary eutectic in-situ composite ceramics with large sizes and complex shapes.

Description

A kind of pulsed discharge plasma assists remelting to prepare the method for the spontaneous composite ceramics of alumina base ternary eutectic
Technical field
The present invention relates to a kind of method preparing alumina base eutectic ceramic in situ composite.
Background technology
Along with the development of the development of the national economy and national science and techniques of defence, thrust-weight ratio is that before the engine turbine of more than 10, inlet temperature, more than 1700 DEG C, therefore proposes more harsh requirement to the research and development of high-temperature structural material of new generation and technology of preparing thereof.Alumina base eutectic ceramic in situ composite is because of the erosion resistance of its high-melting-point, high specific strength, high antioxidant and excellence, and good mechanical property and structure stability can be kept under the ultrahigh-temperature well-oxygenated environment close to fusing point (>1650 DEG C), be considered to be potential most become a new generation can under high temperature oxidation stability atmosphere the first-selected ultrahigh-temperature structured material of long service.
At present, oxide eutectic ceramics processing is mainly divided into two classes: use the directional solidification technique of crucible and the directional solidification technique without the need to crucible, the former mainly comprises: Bridgman method, epitaxial growth method etc.; The latter comprises: floating zone melting, laser zone remelting method and micro-pull method etc.Above-mentioned technology of preparing all exists can not prepare the drawbacks such as oversized shape complicated ceramic component, the highly textured orientation of microtexture and production efficiency are low, Bridgman method can prepare large-size ceramic component, but because thermograde and the speed of growth are very low, significantly limit the application of this technology in preparation ultrahigh-temperature oxide eutectic ceramic component.
Summary of the invention
The present invention is the technical problem that the preparation method in order to solve existing alumina base eutectic ceramic in situ composite is difficult to prepare the complicated eutectic ceramic of oversized shape, eutectic ceramic organizes thick anisotropy and production efficiency is low, and provides a kind of pulsed discharge plasma to assist remelting to prepare the method for the spontaneous composite ceramics of alumina base ternary eutectic.
The method that a kind of pulsed discharge plasma of the present invention assists remelting to prepare the spontaneous composite ceramics of alumina base ternary eutectic is carried out according to the following steps:
One, thermal pretreatment raw material: by nanometer Al 2o 3powder heats 1h ~ 24h under temperature is the condition of 800 DEG C ~ 1500 DEG C, cools to room temperature with the furnace, obtains the Al after thermal pretreatment 2o 3powder; By nanometer ZrO 2powder heats 1h ~ 24h under temperature is the condition of 800 DEG C ~ 1500 DEG C, cools to room temperature with the furnace, obtains the ZrO after thermal pretreatment 2powder; By nanometer Y 2o 3powder heats 1h ~ 24h under temperature is the condition of 800 DEG C ~ 1500 DEG C, cools to room temperature with the furnace, obtains the Y after thermal pretreatment 2o 3powder;
Two, mechanical alloying: by the Al after thermal pretreatment 2o 3powder, ZrO after thermal pretreatment 2powder and the Y after thermal pretreatment 2o 3powder is placed in same ball grinder, adds dehydrated alcohol and aluminum oxide abrading-ball, is ball milling 12h ~ 100h under the condition of 300rpm ~ 500rpm at rotational speed of ball-mill, obtains eutectic proportioning ball milling activation powdery pulp; The Al after thermal pretreatment described in step 2 2o 3powder, ZrO after thermal pretreatment 2powder and the Y after thermal pretreatment 2o 3the gross weight of powder and the weight ratio of dehydrated alcohol are 1:(1 ~ 2); The Al after thermal pretreatment described in step 2 2o 3powder, ZrO after thermal pretreatment 2powder and the Y after thermal pretreatment 2o 3the gross weight of powder and the weight ratio of aluminum oxide abrading-ball are 1:(1 ~ 10); The ZrO after thermal pretreatment described in step 2 2powder and the Al after thermal pretreatment 2o 3the mol ratio of powder is 1:(3.4 ~ 3.5); The Y after thermal pretreatment described in step 2 2o 3powder and the Al after thermal pretreatment 2o 3the mol ratio of powder is 1:(4 ~ 4.1);
Three, coldmoulding: eutectic proportioning ball milling activation powdery pulp step 2 obtained is dry 20min ~ 100min under the condition of 100 DEG C ~ 200 DEG C in temperature, then 100 order ~ 500 mesh sieves are crossed, be the 1min ~ 60min that colds pressing under the pressure of 10MPa ~ 100MPa at pressure, obtain ceramic body;
Four, pulsed discharge plasma assists consolidation: ceramic body step 3 obtained is 10MPa ~ 100MPa at pressure, pulsed discharge plasma heating and temperature rise rate are 50 DEG C/condition of min ~ 200 DEG C/min under from room temperature to 500 DEG C ~ 1000 DEG C, be 10MPa ~ 100MPa at pressure, pulsed discharge plasma heating and temperaturel is be incubated 1min ~ 10min under the condition of 500 DEG C ~ 1000 DEG C, then be 1MPa ~ 20MPa at pressure, pulsed discharge plasma heating and temperature rise rate are 100 DEG C/condition of min ~ 600 DEG C/min under be warming up to 1800 DEG C ~ 2000 DEG C from 500 DEG C ~ 1000 DEG C, be 0.5MPa ~ 20MPa at pressure, pulsed discharge plasma heating and temperaturel is be incubated 1min ~ 10min under the condition of 1800 DEG C ~ 2000 DEG C, obtain fused ceramic, stop heating and pressurization, ON cycle water-cooling system carries out rapid condensation to fused ceramic, obtain Al 2o 3/ Y 3al 5o 12/ ZrO 2the spontaneous composite ceramics of ternary eutectic.
Pulsed discharge plasma of the present invention assists consolidation technology to adopt strong convection circulating water cooling system to control melt solidifying behavior, therefore overcomes the existence of traditional fused craft eutectic ceramic and organizes the problems such as thick anisotropy.
Pulsed discharge plasma of the present invention assists consolidation technology to adopt aux. pressure system stage by stage, realizes eutectic ceramic microstructure optimization and regulation and control.
The advantage of the inventive method:
(1) the inventive method relates to a kind of pulsed discharge plasma and assists consolidation technology, realizes the consolidation integration preparation fast to large size (as diameter is greater than 60mm, is highly the cylinder of 5mm) complex-shaped high-melting-point eutectic ceramic material;
(2) the inventive method is by the technical parameter such as regulation and control temperature rise rate, temperature, applying pressure and dwell time, successfully prepares the little and preparation of isotropic eutectic ceramic in situ composite component of lamellar spacing;
(3) the inventive method adopts multiple step format to be rapidly heated to control the melting of high-melting-point alumina base eutectic composite ceramics and solidify behavior, realizing the large size oxide eutectic ceramic component compared with low residual stress.
Accompanying drawing explanation
Fig. 1 is Al prepared by test one 2o 3/ Y 3al 5o 12/ ZrO 2the XRD figure of the spontaneous composite ceramics of ternary eutectic;
Fig. 2 is Al prepared by test one 2o 3/ Y 3al 5o 12/ ZrO 2the SEM figure of the spontaneous composite ceramics of ternary eutectic.
Embodiment
Embodiment one: present embodiment is that a kind of pulsed discharge plasma assists remelting to prepare the method for the spontaneous composite ceramics of alumina base ternary eutectic, specifically carries out according to the following steps:
One, thermal pretreatment raw material: by nanometer Al 2o 3powder heats 1h ~ 24h under temperature is the condition of 800 DEG C ~ 1500 DEG C, cools to room temperature with the furnace, obtains the Al after thermal pretreatment 2o 3powder; By nanometer ZrO 2powder heats 1h ~ 24h under temperature is the condition of 800 DEG C ~ 1500 DEG C, cools to room temperature with the furnace, obtains the ZrO after thermal pretreatment 2powder; By nanometer Y 2o 3powder heats 1h ~ 24h under temperature is the condition of 800 DEG C ~ 1500 DEG C, cools to room temperature with the furnace, obtains the Y after thermal pretreatment 2o 3powder;
Two, by the Al after thermal pretreatment 2o 3powder, ZrO after thermal pretreatment 2powder and the Y after thermal pretreatment 2o 3powder is placed in same ball grinder, adds dehydrated alcohol and aluminum oxide abrading-ball, is ball milling 12h ~ 100h under the condition of 300rpm ~ 500rpm at rotational speed of ball-mill, obtains eutectic proportioning ball milling activation powdery pulp; The Al after thermal pretreatment described in step 2 2o 3powder, ZrO after thermal pretreatment 2powder and the Y after thermal pretreatment 2o 3the gross weight of powder and the weight ratio of dehydrated alcohol are 1:(1 ~ 2); The Al after thermal pretreatment described in step 2 2o 3powder, ZrO after thermal pretreatment 2powder and the Y after thermal pretreatment 2o 3the gross weight of powder and the weight ratio of aluminum oxide abrading-ball are 1:(1 ~ 10); The ZrO after thermal pretreatment described in step 2 2powder and the Al after thermal pretreatment 2o 3the mol ratio of powder is 1:(3.4 ~ 3.5); The Y after thermal pretreatment described in step 2 2o 3powder and the Al after thermal pretreatment 2o 3the mol ratio of powder is 1:(4 ~ 4.1);
Three, coldmoulding: eutectic proportioning ball milling activation powdery pulp step 2 obtained is dry 20min ~ 100min under the condition of 100 DEG C ~ 200 DEG C in temperature, then 100 order ~ 500 mesh sieves are crossed, be the 1min ~ 60min that colds pressing under the pressure of 10MPa ~ 100MPa at pressure, obtain ceramic body;
Four, pulsed discharge plasma assists consolidation: ceramic body step 3 obtained is 10MPa ~ 100MPa at pressure, pulsed discharge plasma heating and temperature rise rate are 50 DEG C/condition of min ~ 200 DEG C/min under from room temperature to 500 DEG C ~ 1000 DEG C, be 10MPa ~ 100MPa at pressure, pulsed discharge plasma heating and temperaturel is be incubated 1min ~ 10min under the condition of 500 DEG C ~ 1000 DEG C, then be 1MPa ~ 20MPa at pressure, pulsed discharge plasma heating and temperature rise rate are 100 DEG C/condition of min ~ 600 DEG C/min under be warming up to 1800 DEG C ~ 2000 DEG C from 500 DEG C ~ 1000 DEG C, be 0.5MPa ~ 20MPa at pressure, pulsed discharge plasma heating and temperaturel is be incubated 1min ~ 10min under the condition of 1800 DEG C ~ 2000 DEG C, obtain fused ceramic, stop heating and pressurization, ON cycle water-cooling system carries out rapid condensation to fused ceramic, obtain Al 2o 3/ Y 3al 5o 12/ ZrO 2the spontaneous composite ceramics of ternary eutectic.
Embodiment two: the difference of present embodiment and embodiment one is: the nanometer Al described in step one 2o 3the granularity d of powder 50for 50nm ~ 500nm.Other are identical with embodiment one.
Embodiment three: the difference of present embodiment and embodiment one or two is: described in nanometer ZrO 2the granularity d of powder 50for 50nm ~ 500nm.Other are identical with embodiment one or two.
Embodiment four: the difference of present embodiment and embodiment one to three is: the nanometer Y described in step one 2o 3the granularity d of powder 50for 50nm ~ 500nm.Other are identical with embodiment one to three.
Embodiment five: the difference of present embodiment and embodiment one to four is: the diameter of the aluminum oxide abrading-ball described in step 2 is 3mm ~ 10mm.Other are identical with embodiment one to four.
By following verification experimental verification beneficial effect of the present invention:
Test one: this test is that a kind of pulsed discharge plasma assists remelting to prepare the method for the spontaneous composite ceramics of alumina base ternary eutectic, specifically carries out according to the following steps:
One, thermal pretreatment raw material: by nanometer Al 2o 3powder heats 2h under temperature is the condition of 1000 DEG C, cools to room temperature with the furnace, obtains the Al after thermal pretreatment 2o 3powder; By nanometer ZrO 2powder heats 2h under temperature is the condition of 1000 DEG C, cools to room temperature with the furnace, obtains the ZrO after thermal pretreatment 2powder; By nanometer Y 2o 3powder heats 2h under temperature is the condition of 1000 DEG C, cools to room temperature with the furnace, obtains the Y after thermal pretreatment 2o 3powder;
Two, by the Al after thermal pretreatment 2o 3powder, ZrO after thermal pretreatment 2powder and the Y after thermal pretreatment 2o 3powder is placed in same ball milling bottle, adds dehydrated alcohol and aluminum oxide abrading-ball, is ball milling 12h under the condition of 500rpm at rotational speed of ball-mill, obtains eutectic proportioning ball milling activation powdery pulp; The Al after thermal pretreatment described in step 2 2o 3powder, ZrO after thermal pretreatment 2powder and the Y after thermal pretreatment 2o 3the gross weight of powder and the weight ratio of dehydrated alcohol are 1:1.5; The Al after thermal pretreatment described in step 2 2o 3powder, ZrO after thermal pretreatment 2powder and the Y after thermal pretreatment 2o 3the gross weight of powder and the weight ratio of aluminum oxide abrading-ball are 1:4; The ZrO after thermal pretreatment described in step 2 2powder and the Al after thermal pretreatment 2o 3the mol ratio of powder is 1:3.42; The Y after thermal pretreatment described in step 2 2o 3powder and the Al after thermal pretreatment 2o 3the mol ratio of powder is 1:4;
Three, coldmoulding: eutectic proportioning ball milling activation powdery pulp step 2 obtained is dry 20min under the condition of 200 DEG C in temperature, then crosses 200 mesh sieves, is the 5min that colds pressing under the pressure of 50MPa, obtains ceramic body at pressure;
Four, pulsed discharge plasma assists consolidation: ceramic body step 3 obtained is 100MPa at pressure, pulsed discharge plasma heating and temperature rise rate are from room temperature to 800 DEG C under the condition of 100 DEG C/min, be 100MPa at pressure, pulsed discharge plasma heating and temperaturel is be incubated 2min under the condition of 800 DEG C, then be 0.5MPa at pressure, pulsed discharge plasma heating and temperature rise rate are be warming up to 1800 DEG C from 800 DEG C under the condition of 300 DEG C/min, be 0.5MPa ~ 20MPa at pressure, pulsed discharge plasma heating and temperaturel is be incubated 1min under the condition of 1800 DEG C, obtain fused ceramic, stop heating and pressurization, ON cycle water-cooling system carries out rapid condensation to fused ceramic, obtain Al 2o 3/ Y 3al 5o 12/ ZrO 2the spontaneous composite ceramics of ternary eutectic.
Nanometer Al described in step one 2o 3the granularity d of powder 50for 50nm ~ 100nm; Nanometer ZrO described in step one 2the granularity d of powder 50for 50nm ~ 100nm; Nanometer Y described in step one 2o 3the granularity d of powder 50for 50nm ~ 100nm; The diameter of the aluminum oxide abrading-ball described in step 2 is 10mm.
Fig. 1 is Al prepared by test one 2o 3/ Y 3al 5o 12/ ZrO 2the XRD figure of the spontaneous composite ceramics of ternary eutectic, ● be α-Al 2o 3, ■ is Y 3al 5o 12, is c-ZrO 2, as can be seen from the figure test the Al of a preparation 2o 3/ Y 3al 5o 12/ ZrO 2the spontaneous composite ceramics of ternary eutectic has good degree of crystallinity, by α-Al 2o 3, Y 3al 5o 12and c-ZrO (YAG) 2form, do not find that other impurity phases produce.
Fig. 2 is Al prepared by test one 2o 3/ Y 3al 5o 12/ ZrO 2the SEM figure of the spontaneous composite ceramics of ternary eutectic, as can be seen from the figure tests the Al of a preparation 2o 3/ Y 3al 5o 12/ ZrO 2the spontaneous composite ceramics of ternary eutectic does not find crackle and pore.
To Al prepared by test one 2o 3/ Y 3al 5o 12/ ZrO 2the spontaneous composite ceramics of ternary eutectic carries out hardness determination, and its hardness is up to 18.7 ± 0.6GPa.
Test two: this test is the method that the spontaneous composite ceramics of alumina base ternary eutectic is prepared in the consolidation of a kind of impulsive discharge plasma asistance, specifically carries out according to the following steps:
One, thermal pretreatment raw material: by nanometer Al 2o 3powder heats 2h under temperature is the condition of 1000 DEG C, cools to room temperature with the furnace, obtains the Al after thermal pretreatment 2o 3powder; By nanometer ZrO 2powder heats 2h under temperature is the condition of 1000 DEG C, cools to room temperature with the furnace, obtains the ZrO after thermal pretreatment 2powder; By nanometer Y 2o 3powder heats 2h under temperature is the condition of 1000 DEG C, cools to room temperature with the furnace, obtains the Y after thermal pretreatment 2o 3powder;
Two, by the Al after thermal pretreatment 2o 3powder, ZrO after thermal pretreatment 2powder and the Y after thermal pretreatment 2o 3powder is placed in same ball milling bottle, adds dehydrated alcohol and aluminum oxide abrading-ball, is ball milling 12h under the condition of 500rpm at rotational speed of ball-mill, obtains eutectic proportioning ball milling activation powdery pulp; The Al after thermal pretreatment described in step 2 2o 3powder, ZrO after thermal pretreatment 2powder and the Y after thermal pretreatment 2o 3the gross weight of powder and the weight ratio of dehydrated alcohol are 1:1.5; The Al after thermal pretreatment described in step 2 2o 3powder, ZrO after thermal pretreatment 2powder and the Y after thermal pretreatment 2o 3the gross weight of powder and the weight ratio of aluminum oxide abrading-ball are 1:4; The ZrO after thermal pretreatment described in step 2 2powder and the Al after thermal pretreatment 2o 3the mol ratio of powder is 1:3.42; The Y after thermal pretreatment described in step 2 2o 3powder and the Al after thermal pretreatment 2o 3the mol ratio of powder is 1:4;
Three, coldmoulding: eutectic proportioning ball milling activation powdery pulp step 2 obtained is dry 20min under the condition of 200 DEG C in temperature, then crosses 200 mesh sieves, is the 15min that colds pressing under the pressure of 30MPa, obtains ceramic body at pressure;
Four, impulsive discharge plasma asistance consolidation: ceramic body step 3 obtained is 80MPa at pressure, pulsed discharge plasma heating and temperature rise rate are from room temperature to 1000 DEG C under the condition of 60 DEG C/min, be 80MPa at pressure, pulsed discharge plasma heating and temperaturel is be incubated 2min under the condition of 1000 DEG C, then be 2MPa at pressure, pulsed discharge plasma heating and temperature rise rate are be warming up to 1850 DEG C from 1000 DEG C under the condition of 300 DEG C/min, be 2MPa at pressure, pulsed discharge plasma heating and temperaturel is be incubated 2min under the condition of 1850 DEG C, obtain fused ceramic, stop heating and pressurization, ON cycle water-cooling system carries out rapid condensation to fused ceramic, obtain Al 2o 3/ Y 3al 5o 12/ ZrO 2the spontaneous composite ceramics of ternary eutectic.
Nanometer Al described in step one 2o 3the granularity d of powder 50for 50nm ~ 100nm; Nanometer ZrO described in step one 2the granularity d of powder 50for 50nm ~ 100nm; Nanometer Y described in step one 2o 3the granularity d of powder 50for 50nm ~ 100nm; The diameter of the aluminum oxide abrading-ball described in step 2 is 10mm.
To Al prepared by test two 2o 3/ Y 3al 5o 12/ ZrO 2the spontaneous composite ceramics of ternary eutectic carries out hardness test, and its hardness is up to 20.5 ± 0.7GPa.

Claims (5)

1. pulsed discharge plasma assists remelting to prepare a method for the spontaneous composite ceramics of alumina base ternary eutectic, it is characterized in that the method that pulsed discharge plasma assists remelting to prepare the spontaneous composite ceramics of alumina base ternary eutectic is carried out according to the following steps:
One, thermal pretreatment raw material: by nanometer Al 2o 3powder heats 1h ~ 24h under temperature is the condition of 800 DEG C ~ 1500 DEG C, cools to room temperature with the furnace, obtains the Al after thermal pretreatment 2o 3powder; By nanometer ZrO 2powder heats 1h ~ 24h under temperature is the condition of 800 DEG C ~ 1500 DEG C, cools to room temperature with the furnace, obtains the ZrO after thermal pretreatment 2powder; By nanometer Y 2o 3powder heats 1h ~ 24h under temperature is the condition of 800 DEG C ~ 1500 DEG C, cools to room temperature with the furnace, obtains the Y after thermal pretreatment 2o 3powder;
Two, mechanical alloying: by the Al after thermal pretreatment 2o 3powder, ZrO after thermal pretreatment 2powder and the Y after thermal pretreatment 2o 3powder is placed in same ball grinder, adds dehydrated alcohol and aluminum oxide abrading-ball, is ball milling 12h ~ 100h under the condition of 300rpm ~ 500rpm at rotational speed of ball-mill, obtains eutectic proportioning ball milling activation powdery pulp; The nanometer Al after preheating described in step 2 2o 3powder, ZrO after thermal pretreatment 2powder and the Y after thermal pretreatment 2o 3the gross weight of powder and the weight ratio of dehydrated alcohol are 1:(1 ~ 2); The Al after thermal pretreatment described in step 2 2o 3powder, ZrO after thermal pretreatment 2powder and the Y after thermal pretreatment 2o 3the gross weight of powder and the weight ratio of aluminum oxide abrading-ball are 1:(1 ~ 10); The ZrO after thermal pretreatment described in step 2 2powder and the Al after thermal pretreatment 2o 3the mol ratio of powder is 1:(3.4 ~ 3.5); The Y after thermal pretreatment described in step 2 2o 3powder and the Al after thermal pretreatment 2o 3the mol ratio of powder is 1:(4 ~ 4.1);
Three, coldmoulding: eutectic proportioning ball milling activation powdery pulp step 2 obtained is dry 20min ~ 100min under the condition of 100 DEG C ~ 200 DEG C in temperature, then 100 order ~ 500 mesh sieves are crossed, be the 1min ~ 60min that colds pressing under the pressure of 10MPa ~ 100MPa at pressure, obtain ceramic body;
Four, pulsed discharge plasma assists consolidation: ceramic body step 3 obtained is 10MPa ~ 100MPa at pressure, pulsed discharge plasma heating and temperature rise rate are 50 DEG C/condition of min ~ 200 DEG C/min under from room temperature to 500 DEG C ~ 1000 DEG C, be 10MPa ~ 100MPa at pressure, pulsed discharge plasma heating and temperaturel is be incubated 1min ~ 10min under the condition of 500 DEG C ~ 1000 DEG C, then be 1MPa ~ 20MPa at pressure, pulsed discharge plasma heating and temperature rise rate are 100 DEG C/condition of min ~ 600 DEG C/min under be warming up to 1800 DEG C ~ 2000 DEG C from 500 DEG C ~ 1000 DEG C, be 0.5MPa ~ 20MPa at pressure, pulsed discharge plasma heating and temperaturel is be incubated 1min ~ 10min under the condition of 1800 DEG C ~ 2000 DEG C, obtain fused ceramic, stop heating and pressurization, ON cycle water-cooling system carries out rapid condensation to fused ceramic, obtain Al 2o 3/ Y 3al 5o 12/ ZrO 2the spontaneous composite ceramics of ternary eutectic.
2. a kind of pulsed discharge plasma according to claim 1 assists remelting to prepare the method for the spontaneous composite ceramics of alumina base ternary eutectic, it is characterized in that the nanometer Al described in step one 2o 3the granularity d of powder 50for 50nm ~ 500nm.
3. a kind of pulsed discharge plasma according to claim 1 assists remelting to prepare the method for the spontaneous composite ceramics of alumina base ternary eutectic, it is characterized in that the nanometer Y described in step one 2o 3the granularity d of powder 50for 50nm ~ 500nm.
4. a kind of pulsed discharge plasma according to claim 1 assists remelting to prepare the method for the spontaneous composite ceramics of alumina base ternary eutectic, it is characterized in that the nanometer ZrO described in step one 2the granularity d of powder 50for 50nm ~ 500nm.
5. a kind of pulsed discharge plasma according to claim 1 assists remelting to prepare the method for the spontaneous composite ceramics of alumina base ternary eutectic, it is characterized in that the diameter of the aluminum oxide abrading-ball described in step 2 is 3mm ~ 10mm.
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CN107162603A (en) * 2017-06-06 2017-09-15 爱迪特（秦皇岛）科技股份有限公司 A kind of flash sintering method of dental zirconia ceramics
CN107602096A (en) * 2017-10-25 2018-01-19 哈尔滨工业大学 A kind of method of the modified oxidized aluminium base ceramics large-size components surface part nanometer eutectic Strengthening and Toughening of high energy oxyacetylene torch line
CN113354398A (en) * 2021-07-08 2021-09-07 西安石油大学 Aluminum oxide-based high-entropy eutectic ceramic and preparation method thereof

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CN102674819A (en) * 2012-05-16 2012-09-19 台州学院 High-toughness aluminum oxide ceramic, and preparation method and application thereof
CN103586296A (en) * 2013-10-23 2014-02-19 大连理工大学 Mosaic ceramic drawing die and making method thereof

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Publication number Priority date Publication date Assignee Title
WO2011012765A2 (en) * 2009-07-31 2011-02-03 Consejo Superior De Investigaciones Científicas (Cisc) Method for obtaining a nanostructured composite material having a ceramic matrix, which can be machined by electroerosion, and resulting product
CN102674819A (en) * 2012-05-16 2012-09-19 台州学院 High-toughness aluminum oxide ceramic, and preparation method and application thereof
CN103586296A (en) * 2013-10-23 2014-02-19 大连理工大学 Mosaic ceramic drawing die and making method thereof

Cited By (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN107162603A (en) * 2017-06-06 2017-09-15 爱迪特（秦皇岛）科技股份有限公司 A kind of flash sintering method of dental zirconia ceramics
CN107602096A (en) * 2017-10-25 2018-01-19 哈尔滨工业大学 A kind of method of the modified oxidized aluminium base ceramics large-size components surface part nanometer eutectic Strengthening and Toughening of high energy oxyacetylene torch line
CN113354398A (en) * 2021-07-08 2021-09-07 西安石油大学 Aluminum oxide-based high-entropy eutectic ceramic and preparation method thereof

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