CN1060531C - Method for preparation of composite ceramic-Ni-Al intermetallic material - Google Patents
Method for preparation of composite ceramic-Ni-Al intermetallic material Download PDFInfo
- Publication number
- CN1060531C CN1060531C CN98101296A CN98101296A CN1060531C CN 1060531 C CN1060531 C CN 1060531C CN 98101296 A CN98101296 A CN 98101296A CN 98101296 A CN98101296 A CN 98101296A CN 1060531 C CN1060531 C CN 1060531C
- Authority
- CN
- China
- Prior art keywords
- hours
- powder
- incubated
- described method
- temperature
- 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.)
- Expired - Fee Related
Links
Landscapes
- Manufacture Of Alloys Or Alloy Compounds (AREA)
- Powder Metallurgy (AREA)
Abstract
The present invention belongs to the field of manufacturing a metal ceramic composite material, particularly to a preparation method suitable for an in-situ near termination ceramic/Ni3Al composite material. In the method of the present invention, ceramic powder and nickel alloy powder with a certain granularity are mixed with an adhesive for casting and molding; after the adhesive is removed, the powder is sintered in a vacuum furnace, and carries out calorizing reaction in liquid aluminium; finally, a ceramic/Ni3Al composite material with good toughness and high intensity is obtained by high-temperature homogenization processing. Compared with the prior art, the preparation method has the advantages of simple fabrication process and convenient operation. Particularly, the preparation method has an obviously superior effect on near termination molding of a component with a large size and a complicated shape.
Description
The invention belongs to the manufacturing field of ceramic-metal composite.Be specially adapted to the nearly end form pottery/Ni of original position
3The preparation method of Al matrix material.
Has in the high-temperature material of development prospect intermetallic compound Ni in the prior art
3Al possesses unusual yield strength-temperature effective, and very high wear-resistant and corrosion resistance nature.If adopt the Ni of boracic malleableize
3Al alloy network is as the toughness phase in the pottery, the pottery/Ni that develops like this
3The Al matrix material will have more wide application prospect in the high-temperature structural material field.At present both at home and abroad to adopting Ni
3Al also reports to some extent as the production method that tough cohesive prepares ceramic composite mutually.For example a kind of method is to adopt powder metallurgical technique (Materials Science and EngineeringA209 (1996) 243), and this preparation technology is with a certain amount of Ni
3Al powdered alloy and ceramic powder (Al
2O
3, WC, TiC etc.) behind the uniform mixing, hot compacting under 1300 ℃ of-1500 ℃ of high temperature, and form pottery/Ni
3Al matrix material, the shortcoming of this method are the technological operation complexity, and large size and complex-shaped member just are difficult to realize that having is exactly the pottery/Ni that adopts this method preparation again
3Ni in the Al matrix material
3Al toughness is easy to form the arc island mutually, and its performance is obviously reduced.This explained hereafter cost is higher in addition.Another prepares pottery/Ni
3The production method of Al matrix material is to adopt (to be higher than Ni under the pyroprocessing condition
31390 ℃ of the fusing points of Al) make liquid Ni
3Al infiltrates pottery to be strengthened in the batch mixing of body.(Adv.Iudus,Mater,Prog.Ann.Prog,Rep,ORNL,TM2763,(1994)252)。The shortcoming of this method is because liquid Ni
3Al infiltration temperature is too high, and operation is difficult to support and holds.In addition, ceramic phase is not linked to be network, makes composite material rigidity low.
The objective of the invention is to propose a kind ofly have operating procedure simply, economically and reasonably, and be not subjected to the nearly end form pottery/Ni of original position of product size, shape restriction
3The preparation method of Al matrix material.
The inventive method is to adopt at ceramic size or in ceramic powder to stir behind a certain amount of nickel powder of adding, adopt traditional ceramics forming technology (slurry casting or cold-press moulding) to prepare the ceramics preparative blank again, again this prefabricated component is obtained having the ceramics preparative spare of three-dimensional communication hole behind the sintering in High Temperature Furnaces Heating Apparatus, and then this ceramics preparative spare is immersed in the crucible of liquid aluminium, generate the Ni of intermetallic compound by nickel in the ceramics preparative spare and aluminium generation thermopositive reaction
3Al (volumetric shrinkage) makes liquid aluminium constantly penetrate into connected holes in the ceramics preparative spare under the reaction pressure effect, and continues reaction and form the Ni that is communicated with nickel in the ceramics preparative spare
3The Al network.Then product is taken out to be cooled to and carry out a homogenizing after the room temperature again and handle and just obtain even pottery/Ni
3The Al matrix material.According to purpose of the present invention, pottery/Ni that we proposed
3The preparation method of Al intermetallic compound composite material prepares the sintering processes of carrying out different systems after powder and binding agent uniform mixing, the moulding again by planner's composition requirement, it is characterized in that batching, be mixed and moulding with organic binder bond after should getting the nickelalloy powder uniform mixing of ceramic powder that granularity is 0.2-60 μ m and granularity 5-40 μ m, available slurry casting method is made ceramics preparative green bodies when powder is made slurry in emulsion hydrosol after again.Also can with the powder that is mixed and paraffin wax or resin aqueous solution be cold-pressed into prefabricated blank after being mixed.Then prefabricated blank being put into 200 ℃-400 ℃ anti-oxidation gas heating stove is incubated 1-2 hours and sloughs binding agent.The prefabricated component that to slough binding agent again puts into that vacuum tightness is not less than the 2.7Pa vacuum oven or an oxygen-proof property institute part stove carries out high temperature sintering, sintering temperature is that the aluminum melt that the prefabricated component behind 1150 ℃-1350 ℃, sintering should be put into oxygen-proof property gas again carries out the aluminising reaction, the temperature of aluminising reaction is 850 ℃-1000 ℃, soaking time is 0.5-10 hours, aluminising finishes back taking-up prefabricated component and is cooled to room temperature, and then with prefabricated component in 1100 ℃-1250 ℃, be incubated 5-10 hours and carry out the homogenizing processing, just can obtain pottery/Ni
3The matrix material of Al.At pottery/Ni of the present invention
3In the Al composite material and preparation method thereof, it is 0.5-30 μ m that other feature also includes the better size range of ceramic powder.The better size range of nickelalloy powder is 10-20 μ m.The optimum treatment temperature that removes tackiness agent is 200 ℃-300 ℃, is incubated 2 hours.The high temperature sintering optimum treatmenting temperature of prefabricated component is 1250 ℃-1350 ℃, is incubated 2 hours.The aluminising optimum temps is 850 ℃-950 ℃, is incubated 2-4 hours.Remove the protection of binding agent and aluminising processing optimal gas and should adopt rare gas element.1200 ℃-1250 ℃ of the optimum tempss that homogenizing is handled are incubated 5-10 hours.The ceramic powder that is proposed is meant SiC, Al in the method for the invention
2O
3, ceramics powder such as WC.The nickelalloy powder that is proposed in the methods of the invention is meant nickel content in the nickel alloy powder more than 95%, can also include boron or other element below 0.2% in nickel alloy powder.In the method for the invention, as the proportion of ceramic enhancement phase and volume fraction and toughness Ni mutually
3After the weight % content of nickel alloy powder was determined in the Al alloy, it importantly adopted this method can make the nickel alloy powder in the ceramics preparative spare want to generate Ni with the liquid aluminium generation thermopositive reaction of being infiltrated fully
3Al, and make the Ni that is generated
3All be full of the volume that original nickel alloy powder is occupied in connected holes in the prefabricated component and the prefabricated component after Al solidifies, reach the good pottery/Ni of strength high toughness
3The Al intermetallic compound composite material.
Adopt the inventive method compared with prior art, it is simpler than powder metallurgy process technology to have a prepared matrix material of this method.Economical and easy to operate, especially more obvious superior to large size and complex-shaped member near-net forming.Adopt this method to prepare matrix material, Ni in addition
3The Al malleableize can not form the arc island mutually, but is the contiguous network shape.
Embodiment
According to pottery/Ni of the present invention
3The preparation method of Al intermetallic compound composite material, we have done following 6 groups of tests altogether and have compared, and the technical parameter of its test and performance are listed in respectively in the following table, and wherein table 1 is the preparation technology parameter contrast table of nickel-containing alloys powder ceramics preparative spare.Table 2 is pottery/Ni
3The preparation technology of Al intermetallic compound composite material and performance comparison table.
Table 1 contains the preparation technology parameter contrast table of Ni alloy powder ceramics preparative
Table 2 pottery/Ni
3The preparation technology of Al intermetallic compound composite material and performance comparison table
Sequence number | Raw material | Granularity (μ m) | Ceramics powder/Ni powder weight ratio | Binding agent | Forming method | Forming pressure (Mpa) | Preform sizes (mm) | Remove the technology of binding agent | Sintering condition | ||||
Temperature (℃) | Time (h) | Gas part | Temperature (℃) | Time (h) | Environment | ||||||||
1 | WC/Ni | 20/10 | 12.9 | The 4vol% emulsion hydrosol | Cold pressing | 35 | 8×10×50 | 200 | 2.0 | H 2 | 1350 | 2 | Vacuum |
2 | SiC/Ni | 50/20 | 1.85 | Paraffin wax | Cold pressing | 50 | 8×10×50 | 250 | 1.5 | Ar | 1250 | 2 | Ar |
3 | SiC/Ni | 25/35 | 3.3 | The 3.0vol% resin | Cast | / | φ1.5×50 | 350 | 1.5 | H 2 | 1250 | 3.5 | Vacuum |
4 | Al 2O 3/Ni | 0.5/10 | 3.0 | Paraffin wax | Cold pressing | 50 | 8×10×50 | 250 | 2.0 | Ar | 1300 | 2 | Vacuum |
5 | Al 2O 3/Ni | 2.0/5 | 11.5 | Paraffin wax | Cold pressing | 40 | 8×10×50 | 250 | 2.5 | H 2 | 1350 | 2 | Vacuum |
6 | WC/Ni | 10/10 | 1.6 | The 8vol% emulsion hydrosol | Cast | / | 10×10×55 | 250 | 2 | H 2 | 1200 | 3 | Ar |
Sequence number | Temperature in the prefabricated component immersion aluminium liquid (℃) | Shielding gas | The aluminising reaction process | Be chilled to | Homogenization process | The finished product tissue | End properties | |||
Gas | Temperature ℃ | Time h | Temperature ℃ | Time h | Fracture toughness property Mpa m 1/2 | Hardness GPa | ||||
1 | 750 | Ar | 900 | 2.5 | Room temperature | 1250 | 5 | Evenly | 15 | 14 |
2 | 800 | N 2 | 950 | 2.0 | Room temperature | 1200 | 8 | Evenly | 10.8 | 10.3 |
3 | 750 | N 2 | 900 | 3.0 | Room temperature | 1250 | 4 | Evenly | 8.5 | 12.6 |
4 | 800 | Ar | 950 | 2.5 | Room temperature | 1200 | 9 | Evenly | 10.2 | 10.5 |
5 | 780 | N 2 | 1000 | 2.0 | Room temperature | 1250 | 6 | Evenly | 16.7 | 12.9 |
6 | 800 | N 2 | 850 | 4.5 | Room temperature | 1150 | 12 | Evenly | 12.6 | 9.6 |
Claims (9)
1, a kind of pottery/Ni
3The preparation method of Al intermetallic compound composite material, this method are that powder and the binding agent through preparation mixes, carry out the sintering processes of different systems after the moulding again, it is characterized in that preparing burden and get the SiC that granularity is 0.2-60 μ m, Al
2O
3Among the WC any one ceramic powder and granularity be 5-40 μ m content less than 1%B and greater than behind the nickelalloy powder uniform mixing of 99%Ni again with emulsion hydrosol, paraffin wax, in the resin glue any one is mixed and moulding, then, the prefabricated component base being put into anti-oxidation gas part process furnace of 200 ℃-400 ℃ is incubated 1-2 hours and removes above-mentioned binding agent again, the prefabricated component that will remove binding agent is again put into the vacuum oven that vacuum tightness is not less than 2.7Pa and is carried out high temperature sintering, its sintering temperature is 1150 ℃-1350 ℃, be incubated 2-4 hours, the aluminum melt that prefabricated component after vacuum high-temperature sintering is handled should be put into oxygen-proof property gas again carries out the aluminising reaction, the aluminising temperature of reaction is 850 ℃-1000 ℃, be incubated 0.5-10 hours, aluminising finishes back taking-up prefabricated component and is cooled to room temperature, carrying out homogenizing at last handles, the homogenizing treatment temp is 1100 ℃-1250 ℃, and soaking time is 5-10 hours.
2, according to the described method of claim 1, it is characterized in that high temperature sintering is handled also can carry out in oxygen-proof property gas part stove.
3, according to the described method of claim 1, the size range that it is characterized in that ceramic powder is 0.5-30 μ m.
4, according to the described method of claim 1, the size range that it is characterized in that the nickelalloy powder is 10-20 μ m.
5, according to the described method of claim 1, the thermal treatment temp that it is characterized in that removing tackiness agent is 200 ℃-300 ℃, is incubated 2 hours.
6, according to the described method of claim 1, the high temperature sintering treatment temp that it is characterized in that prefabricated component is 1250 ℃-1350 ℃, is incubated 2 hours.
7,, it is characterized in that the aluminising temperature is 850 ℃-950 ℃, is incubated 2-4 hours according to the described method of claim 1.
8, according to the described method of claim 1, it is characterized in that the temperature that homogenizing is handled is 1200 ℃-1250 ℃, be incubated 5-10 hours.
9,, it is characterized in that removing the gas shield that binding agent and aluminising handle and to adopt protection of inert gas according to claim 1,5,7 described methods.
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
CN98101296A CN1060531C (en) | 1998-04-21 | 1998-04-21 | Method for preparation of composite ceramic-Ni-Al intermetallic material |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
CN98101296A CN1060531C (en) | 1998-04-21 | 1998-04-21 | Method for preparation of composite ceramic-Ni-Al intermetallic material |
Publications (2)
Publication Number | Publication Date |
---|---|
CN1199102A CN1199102A (en) | 1998-11-18 |
CN1060531C true CN1060531C (en) | 2001-01-10 |
Family
ID=5216593
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
CN98101296A Expired - Fee Related CN1060531C (en) | 1998-04-21 | 1998-04-21 | Method for preparation of composite ceramic-Ni-Al intermetallic material |
Country Status (1)
Country | Link |
---|---|
CN (1) | CN1060531C (en) |
Cited By (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN1331541C (en) * | 2005-11-18 | 2007-08-15 | 山东大学 | Hydroxy apatite Ni3Al composite material and its preparing method |
Families Citing this family (4)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN1325431C (en) * | 2005-10-18 | 2007-07-11 | 中国海洋大学 | Gel molding-injection base from high-strength ceramic composite materials and shaping method thereof |
CN101648272B (en) * | 2009-09-12 | 2011-08-31 | 陕西宝光陶瓷科技有限公司 | Method for coating surface of ceramic metalized envelope with nickel |
CN103352199B (en) * | 2013-07-04 | 2015-06-03 | 南京摄炉(集团)有限公司 | High purity aluminizing furnace |
CN108277515A (en) * | 2017-12-25 | 2018-07-13 | 南京悠谷新材料科技有限公司 | A kind of preparation method of nickel aluminum metal composite |
Citations (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
WO1997041368A1 (en) * | 1996-05-02 | 1997-11-06 | The Dow Chemical Company | Ceramic metal composite brake components and manufacture thereof |
-
1998
- 1998-04-21 CN CN98101296A patent/CN1060531C/en not_active Expired - Fee Related
Patent Citations (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
WO1997041368A1 (en) * | 1996-05-02 | 1997-11-06 | The Dow Chemical Company | Ceramic metal composite brake components and manufacture thereof |
Cited By (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN1331541C (en) * | 2005-11-18 | 2007-08-15 | 山东大学 | Hydroxy apatite Ni3Al composite material and its preparing method |
Also Published As
Publication number | Publication date |
---|---|
CN1199102A (en) | 1998-11-18 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
JP7164906B2 (en) | METHOD FOR PREPARATION OF METAL MATERIAL OR METAL COMPOSITE MATERIAL | |
US4770701A (en) | Metal-ceramic composites and method of making | |
CN105803236B (en) | A kind of aluminum matrix composite of non-crystaline amorphous metal enhancing and preparation method thereof | |
CN104120291B (en) | A kind of TiC, TiB2The preparation method of particle enhanced nickel base composite material | |
CN110846547A (en) | High-entropy alloy combined tungsten carbide hard alloy and preparation method thereof | |
CN108642361B (en) | High-strength high-hardness ceramic material and production process thereof | |
CN105734387B (en) | A kind of TiB2Based ceramic metal and preparation method thereof | |
CN103938006B (en) | The preparation method of the corrosion of resistance to aluminium cermet material | |
CN114635069A (en) | High-strength-toughness medium-entropy alloy binding phase Ti (C, N) -based metal ceramic and preparation method thereof | |
CN109576546A (en) | A kind of preparation method of the high-strength tenacity without magnetic Ti (C, N) based ceramic metal | |
CN1060531C (en) | Method for preparation of composite ceramic-Ni-Al intermetallic material | |
CN113817933B (en) | Ceramic reinforced titanium-based composite material, preparation method and application thereof | |
CN108048685B (en) | TiC/SiC/Al composite material | |
CN110129631A (en) | A kind of internal combustion engine high-toughness heat-resistant aluminum alloy materials and preparation method thereof | |
CN110183231A (en) | A kind of preparation method and its ceramic material of high-strength and high ductility carbonization boryl ceramic material | |
CN102731071A (en) | Preparation method of Al-Ti-B and rare metal synergistically-toughened alumina | |
CN109266950A (en) | Cubic boron nitride enhances steel-based composite material and preparation method thereof | |
CN109231990A (en) | A kind of preparation method of tungsten carbide-diamond composite | |
Hanyaloglu et al. | Reactive sintering of electroless nickel-plated aluminum powders | |
CN114737095B (en) | Rare earth doped WC-Co hard alloy material and preparation method and application thereof | |
EP0250414B1 (en) | Method in producing a molding of an iron alloy | |
JPH0578708A (en) | Production of aluminum-based grain composite alloy | |
CN103938046B (en) | The corrosion of resistance to aluminium cermet material | |
JP2003513877A (en) | Method of obtaining carbide refractory composite material | |
CN110004346B (en) | Cr-C-N-based metal ceramic and preparation method thereof |
Legal Events
Date | Code | Title | Description |
---|---|---|---|
C10 | Entry into substantive examination | ||
SE01 | Entry into force of request for substantive examination | ||
C06 | Publication | ||
PB01 | Publication | ||
C14 | Grant of patent or utility model | ||
GR01 | Patent grant | ||
C19 | Lapse of patent right due to non-payment of the annual fee | ||
CF01 | Termination of patent right due to non-payment of annual fee |