CN109694979A - Vacuum induction melting prepares high-entropy alloy-base composite material and its method - Google Patents
Vacuum induction melting prepares high-entropy alloy-base composite material and its method Download PDFInfo
- Publication number
- CN109694979A CN109694979A CN201710984945.5A CN201710984945A CN109694979A CN 109694979 A CN109694979 A CN 109694979A CN 201710984945 A CN201710984945 A CN 201710984945A CN 109694979 A CN109694979 A CN 109694979A
- Authority
- CN
- China
- Prior art keywords
- composite material
- particle
- entropy alloy
- reinforcement
- tic
- 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
- 239000002131 composite material Substances 0.000 title claims abstract description 54
- 238000002844 melting Methods 0.000 title claims abstract description 22
- 230000008018 melting Effects 0.000 title claims abstract description 22
- 230000006698 induction Effects 0.000 title claims abstract description 18
- 238000000034 method Methods 0.000 title abstract description 14
- 230000002787 reinforcement Effects 0.000 claims abstract description 36
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 24
- 239000000956 alloy Substances 0.000 claims abstract description 24
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 claims abstract description 20
- 239000011159 matrix material Substances 0.000 claims abstract description 20
- 239000010949 copper Substances 0.000 claims abstract description 19
- 239000007789 gas Substances 0.000 claims abstract description 19
- 238000006243 chemical reaction Methods 0.000 claims abstract description 16
- 229910052802 copper Inorganic materials 0.000 claims abstract description 14
- 229910052786 argon Inorganic materials 0.000 claims abstract description 10
- 238000004321 preservation Methods 0.000 claims abstract description 9
- 238000001816 cooling Methods 0.000 claims abstract description 8
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 claims abstract description 7
- 239000002994 raw material Substances 0.000 claims abstract description 7
- 229910052710 silicon Inorganic materials 0.000 claims abstract description 6
- 239000002245 particle Substances 0.000 claims description 32
- 239000000843 powder Substances 0.000 claims description 23
- 238000002360 preparation method Methods 0.000 claims description 19
- 239000013528 metallic particle Substances 0.000 claims description 12
- 238000010792 warming Methods 0.000 claims description 12
- 238000001035 drying Methods 0.000 claims description 10
- 239000000463 material Substances 0.000 claims description 10
- 238000000498 ball milling Methods 0.000 claims description 9
- 229910052759 nickel Inorganic materials 0.000 claims description 8
- 229910052742 iron Inorganic materials 0.000 claims description 7
- 229910052782 aluminium Inorganic materials 0.000 claims description 6
- 239000000203 mixture Substances 0.000 claims description 6
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims description 6
- 238000000227 grinding Methods 0.000 claims description 3
- 238000007670 refining Methods 0.000 claims description 3
- 229910052719 titanium Inorganic materials 0.000 claims description 3
- PCHJSUWPFVWCPO-UHFFFAOYSA-N gold Chemical compound [Au] PCHJSUWPFVWCPO-UHFFFAOYSA-N 0.000 claims 2
- 229910052737 gold Inorganic materials 0.000 claims 2
- 239000010931 gold Substances 0.000 claims 2
- 239000011856 silicon-based particle Substances 0.000 claims 1
- 238000003723 Smelting Methods 0.000 abstract description 3
- 230000015572 biosynthetic process Effects 0.000 abstract 1
- 238000003786 synthesis reaction Methods 0.000 abstract 1
- 238000010438 heat treatment Methods 0.000 description 10
- 238000003756 stirring Methods 0.000 description 7
- 238000011065 in-situ storage Methods 0.000 description 6
- 230000001681 protective effect Effects 0.000 description 6
- 230000002708 enhancing effect Effects 0.000 description 5
- 239000002184 metal Substances 0.000 description 4
- 229910052751 metal Inorganic materials 0.000 description 4
- -1 after mixing Substances 0.000 description 3
- 238000005275 alloying Methods 0.000 description 3
- 239000000498 cooling water Substances 0.000 description 3
- 238000005516 engineering process Methods 0.000 description 3
- 238000002156 mixing Methods 0.000 description 3
- 238000005086 pumping Methods 0.000 description 3
- 238000005303 weighing Methods 0.000 description 3
- 238000000576 coating method Methods 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 238000005265 energy consumption Methods 0.000 description 2
- 230000004913 activation Effects 0.000 description 1
- 238000010923 batch production Methods 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 238000001514 detection method Methods 0.000 description 1
- 238000010891 electric arc Methods 0.000 description 1
- 238000002149 energy-dispersive X-ray emission spectroscopy Methods 0.000 description 1
- 238000007499 fusion processing Methods 0.000 description 1
- 208000021760 high fever Diseases 0.000 description 1
- 229910000765 intermetallic Inorganic materials 0.000 description 1
- 238000000465 moulding Methods 0.000 description 1
- 238000005096 rolling process Methods 0.000 description 1
- 238000005204 segregation Methods 0.000 description 1
- 230000035939 shock Effects 0.000 description 1
- 238000002791 soaking Methods 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 239000000243 solution Substances 0.000 description 1
- 238000010183 spectrum analysis Methods 0.000 description 1
- 238000001330 spinodal decomposition reaction Methods 0.000 description 1
- 238000010189 synthetic method Methods 0.000 description 1
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C30/00—Alloys containing less than 50% by weight of each constituent
- C22C30/02—Alloys containing less than 50% by weight of each constituent containing copper
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/10—Alloys containing non-metals
- C22C1/1005—Pretreatment of the non-metallic additives
- C22C1/1015—Pretreatment of the non-metallic additives by preparing or treating a non-metallic additive preform
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/10—Alloys containing non-metals
- C22C1/1036—Alloys containing non-metals starting from a melt
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/10—Alloys containing non-metals
- C22C1/1036—Alloys containing non-metals starting from a melt
- C22C1/1047—Alloys containing non-metals starting from a melt by mixing and casting liquid metal matrix composites
- C22C1/1052—Alloys containing non-metals starting from a melt by mixing and casting liquid metal matrix composites by mixing and casting metal matrix composites with reaction
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C32/00—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ
- C22C32/0047—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with carbides, nitrides, borides or silicides as the main non-metallic constituents
- C22C32/0052—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with carbides, nitrides, borides or silicides as the main non-metallic constituents only carbides
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Composite Materials (AREA)
- Chemical Kinetics & Catalysis (AREA)
- Powder Metallurgy (AREA)
- Manufacture Of Metal Powder And Suspensions Thereof (AREA)
- Manufacture And Refinement Of Metals (AREA)
Abstract
The invention discloses a kind of vacuum induction meltings to prepare high-entropy alloy-base composite material and its method, and the composite material is interior raw type, using AlMFeNiCu high-entropy alloy as matrix phase, with (TiC)xFor reinforced phase, it is denoted as (TiC)x/(AlMFeNiCu)1‑xWherein, M is Si or Co, and x is 0.1 ~ 0.2.It the steps include: to weigh reaction sample raw material according to raw material proportioning；Prepare reinforcement test block；Raw material are fitted into high-frequency induction smelting furnace, are vacuumized, are passed through argon gas, vacuum melting, heat preservation；Fused solution alloy after heat preservation is poured into cooling in copper crucible, takes out, obtains the composite material.The present invention synthesizes endogenous high-entropy alloy-base composite material by the way of induction melting, interface cohesion is good between the composite material reinforcement body and matrix of synthesis, reinforcement is uniformly distributed in high-entropy alloy matrix, and the method is easy to operate, safe and reliable, energy- and time-economizing, environmental-friendly.
Description
Technical field
The present invention relates to a kind of high-entropy alloy-base composite material and preparation method thereof, especially a kind of vacuum induction melting system
Standby in-situ authigenic belongs to material invention and preparation field at high-entropy alloy-base composite material and its method.
Technical background
Process for vacuum induction smelting prepares the preparation method of high-entropy alloy-base composite material, refers to the side using induction heating
Formula, makes to prepare raw material self-heating fusing and prepares composite material, and the preparation method degree of reaction is all fast, and easy to operate, low energy consumption, system
Standby high-entropy alloy-base composite material dense structure's property is good, and interface cohesion is stablized.The preparation method is easy to operate, space occupied
It is small.Solve that traditional handicraft heating efficiency is low, the few disadvantage of preparation quantity, it is raw that vacuum induction melting can carry out batch to material
It produces.Heating time, heating power, soaking time, heat preservation power and cooling time is adjusted with automatic control type；It substantially increases and adds
The quality of hot product and the repeatability of heating simplify the operating technology of worker.The high-entropy alloy-base composite material of this method preparation
With high rigidity, high-wear resistance and corrosion resistance.In high-entropy alloy forming process, a nanometer Cu will form in intergranular
Phase can increase the yield strength of material, and certain toughening effect is played to material.The high-entropy alloy-base composite material of preparation is being led
Also electrically there is very superior performance in terms of magnetic conductivity.In addition to this, high-entropy alloy-base composite material, in shock resistance part and
It also has a good application prospect in terms of high-temperature resistance die.
Document one prepares TiC-TiB using vacuum arc melting technology2/ CoCrCuFeNi composite reinforcement high-entropy alloy-base
Composite material, fusion process energy consumption is higher, and the measurer for preparing sample has certain limitation, can only prepare for electric arc heated
A small amount of sample, it is impossible to be used in batch production (Cheng J, Liu D, Liang X, et al. Evolution of
microstructure and mechanical properties of in situ synthesized TiC–TiB 2 /
CoCrCuFeNi high entropy alloy coatings[J]. Surface & Coatings Technology,
2015,281 (7): 109-116).Document two is prepared using the synthetic method that powder agglomates and metal block are used in mixed way
FeCrCoNiCuTi/TiC high-entropy alloy composite material (Lu Suhua, Harbin Institute of Technology, 2008), the sample group of preparation
It knits reinforcement to be unevenly distributed in the base, interfacial combined function is poor, although the wear-resisting property of sample increases, bends
Intensity is taken to be declined.
Summary of the invention
It is an object of that present invention to provide a kind of process for vacuum induction smelting prepare endogenous high-entropy alloy-base composite material and
Its method, the technological operation is simple, safe and reliable, energy- and time-economizing, environmental-friendly, and the tiny TiB of rule2It is in situ for enhancing particle
Reaction generates, surface no-pollution, clean interfaces.
Realize the object of the invention technical solution are as follows: high-entropy alloy-base composite material of the present invention, the composite material
For interior raw type, using AlMFeNiCu high-entropy alloy as matrix phase, with (TiC)xFor reinforced phase, it is denoted as (TiC)x/
(AlMFeNiCu)1-xWherein, M is Si or Co, and x is 0.1 ~ 0.2.
The method for preparing above-mentioned interior raw type high-entropy alloy-base composite material, comprising the following steps:
The first step, according to target composite material composition weighs high-purity Al, M, Ni, Ti, Cu, Fe metallic particles, and to metallic particles
Surface is pre-processed, and surface oxide layer is removed；
Second step, preparation reinforcement test block: it is mixed through ball milling that high-purity Ti powder, C powder, Fe powder are weighed according to target composite material composition
It is dry after conjunction, reinforcement test block is prepared under a certain pressure；
Third step, by the sample prepared according to (TiC)x/(AlMFeNiCu)1-xCorrespondence raw material successively add Al particle, increase
Strong body test block, Ni particle, Fe particle, M particle, Cu particle reach 10 in vacuum degree-3When Pa or more, it is passed through argon gas and keeps air pressure
No more than 10-1Pa, energization induction melting are tentatively warming up to 950 ~ 1050 DEG C, observe in observation window and react in furnace, are warming up to
1450 ~ 1550 DEG C, when melting substantially wait react test block, and then 2000 ~ 2200 DEG C are warming up to, melting 8 ~ 12 minutes, melted repeatedly
Refining 2 ~ 3 times；
4th step, heat preservation cooling: after warm 3 ~ 8 minutes, reaction molten alloy is poured into water jacketed copper crucible, reinforcement particle
It is attached to the growth of fine grain particle surface in the base, obtains fine grain high-entropy alloy-base composite material.
Preferably, in second step, rotational speed of ball-mill 250-300p.r.m；Ball-milling Time is 6 ~ 8h；Ratio of grinding media to material (ball and powder
Mass ratio) be 4.5:1.
Preferably, in second step, drying temperature is 110 ~ 120 DEG C, and drying time is 2 hours, is squeezed under 180MPa
Base sample.
Compared with prior art, remarkable advantage of the invention is: (1) being added using induction melting synthesized activation energy lower than conventional
Hot mode, reaction temperature is lower, is swift in response, and technological operation is simple, safe and reliable, energy- and time-economizing, environmental-friendly.(2) due to
Heating rate fast response process is short, it is suppressed that microstructure coarsening and dendritic segregation, this method can significant thinning microstructure, simultaneously because instead
It answers heat release rapid, can carry out from stirring, the high fever for reacting generation can effectively purify matrix, be conducive to the performance for improving material.(3)
Spinodal decomposition and lattice distortion effect mutually occur for the high-entropy alloy matrix that reaction generates to hinder material to send out since lattice is mobile
Raw stress relaxation deformation.(4) high-entropy alloy-base composite material that reaction generates is at single face-centred cubic structure, the strength of materials
Preferable with moulding, institutional framework does not generate complicated intermetallic compound phase simply, is organized into regular single-phase or two-phase solid solution
Structure.
Detailed description of the invention
Fig. 1 is the XRD diffraction image of 1 high-entropy alloy-base composite material of the embodiment of the present invention.
Fig. 2 is the matrix SEM scanned photograph of 1 high-entropy alloy-base composite material of the embodiment of the present invention.
Fig. 3 is matrix SEM scanned photograph corresponding region A, the B of 1 high-entropy alloy-base composite material of embodiment, C's
EDS energy spectrum analysis figure (wherein, a is region A, and b is region B, and c is region C).
Fig. 4 be 2 high-entropy alloy-base composite material of the embodiment of the present invention SEM scanned picture (a be low power number, b is high power
Number)
Fig. 5 is the SEM microstructure photograph of 3 high-entropy alloy-base composite material of embodiment.
Specific embodiment
Embodiment 1:(TiC)0.1/(AlSiFeNiCu)0.9Composite material
The method that vacuum induction melting of the present invention prepares endogenous high-entropy alloy-base composite material, specifically includes following step
It is rapid:
(1) high-purity Al, Si, Ni, Fe, Cu metallic particles is weighed for 10% according to reinforcement volume fraction, it is preceding to metal using
Particle surface is pre-processed, and takes out surface oxide layer, oxide layer is volatilized at high temperature influences Melting Quality.
(2) it prepares reinforcement test block: weighing high-purity Ti powder C powder according to the volume fraction of reinforcement, Fe powder, after mixing,
Ball powder mass ratio is 4.5:1；Rotational speed of ball-mill is 250-300p.r.m；Ball-milling Time is 6 ~ 8h.Drying temperature is 110 ~ 120
DEG C, drying time is 2 hours, and base sample is squeezed under 180MPa.
(3) it vacuumizes logical protective gas: after opening cooling water, being first evacuated to < 5Pa with mechanical pump, then true with molecule pumping
Sky is to 10-4Pa.After stable gas pressure, it is passed through protective gas (argon gas), air pressure is made to be maintained at 10-1Then Pa or so is vacuumized again
To 10-4Leading to argon gas after Pa makes air pressure reach 10-1Pa leads to 2 ~ 3 times repeatedly.
(4) heating rate: 1, temperature reaction stage is adjusted: adjustment output high-frequency current 400A first, when crucible is shinny,
Adjustment output electric current is 350A, and 2, reinforcement generation phase: after five minutes, occurring reaction in-situ, releases heat and issues white light, with
Being warming up to 1500 DEG C immediately afterwards makes reinforcement test block be fusing into matrix.3, alloying: adjustment output electric current reaches temperature
1500 ~ 2000 DEG C, metallic particles molten alloy, in induction from during stirring, alloy system rolls from inside to outside
Stirring, reinforcement are uniformly distributed in high-entropy alloy matrix.
(5) the 4th steps, heat preservation cooling: warm to react molten alloy after five minutes and pour into water jacketed copper crucible, enhancing
Body particle is attached to the growth of fine grain particle surface in the base, obtains fine grain high-entropy alloy-base composite material.
XRD detection is carried out to sample and sees that Fig. 1 can have found that gained high-entropy alloy-base composite material is the high-entropy alloy of TiC enhancing
Based composites composite material, wherein further including having part SiC reinforced phase and SEM, EDS analysis sample sets prejudice Fig. 2, figure
3, it is possible to find main reinforcement is TiC and growth is more regular, is evenly distributed, matrix at rich Fe, Ni, Si and richness Al, Ni, Cu's
Double structure.
Embodiment 2:(TiC)0.2/(AlSiFeNiCu)0.8Composite material
(1) high-purity Al, Si, Ni, Fe, Cu metallic particles is weighed for 20% according to reinforcement volume fraction, it is preceding to metal using
Particle surface is pre-processed, and takes out surface oxide layer, oxide layer is volatilized at high temperature influences Melting Quality.
(2) it prepares reinforcement test block: weighing high-purity Ti powder C powder according to the volume fraction of reinforcement, Fe powder, after mixing,
Ball powder mass ratio is 4.5:1；Rotational speed of ball-mill is 250-300p.r.m；Ball-milling Time is 6 ~ 8h.Drying temperature is 110 ~ 120
DEG C, drying time is 2 hours, and base sample is squeezed under 180MPa.
(3) it vacuumizes logical protective gas: after opening cooling water, being first evacuated to < 5Pa with mechanical pump, then true with molecule pumping
Sky is to 10-4Pa.After stable gas pressure, it is passed through protective gas (argon gas), air pressure is made to be maintained at 10-1Then Pa or so is vacuumized again
To 10-4Leading to argon gas after Pa makes air pressure reach 10-1Pa leads to 2 ~ 3 times repeatedly.
(4) heating rate: 1, temperature reaction stage is adjusted: adjustment output high-frequency current 400A first, when crucible is shinny,
Adjustment output electric current is 350A, and 2, reinforcement generation phase: after five minutes, occurring reaction in-situ, releases heat and issues white light, with
Being warming up to 1500 DEG C immediately afterwards makes reinforcement test block be fusing into matrix.3, alloying: adjustment output electric current reaches temperature
1500 ~ 2000 DEG C, metallic particles molten alloy, in induction from during stirring, alloy system rolls from inside to outside
Stirring, reinforcement are uniformly distributed in high-entropy alloy matrix.
(5) the 4th steps, heat preservation cooling: warm to react molten alloy after five minutes and pour into water jacketed copper crucible, enhancing
Body particle is attached to the growth of fine grain particle surface in the base, obtains fine grain high-entropy alloy-base composite material.
It can be seen that the good reinforcement particle of sample microscopic structure compactness of reaction preparation is uniformly distributed in from Fig. 4 a
In matrix, it can be seen that reinforcement growth is completely well combined between matrix in Fig. 4 b.
Embodiment 3:(TiC)0.1/(AlCoFeNiCu)0.9Composite material
(1) high-purity Al, Co, Ni, Fe, Cu metallic particles is weighed for 10% according to reinforcement volume fraction, it is preceding to metal using
Particle surface is pre-processed, and takes out surface oxide layer, oxide layer is volatilized at high temperature influences Melting Quality.
(2) it prepares reinforcement test block: weighing high-purity Ti powder C powder according to the volume fraction of reinforcement, Cu powder, after mixing,
Ball powder mass ratio is 4.5:1；Rotational speed of ball-mill is 250-300p.r.m；Ball-milling Time is 6 ~ 8h.Drying temperature is 110 ~ 120
DEG C, drying time is 2 hours, and base sample is squeezed under 180MPa.
(3) it vacuumizes logical protective gas: after opening cooling water, being first evacuated to < 5Pa with mechanical pump, then true with molecule pumping
Sky is to 10-4Pa.After stable gas pressure, it is passed through protective gas (argon gas), air pressure is made to be maintained at 10-1Then Pa or so is vacuumized again
To 10-4Leading to argon gas after Pa makes air pressure reach 10-1Pa leads to 2 ~ 3 times repeatedly.
(4) heating rate: 1, temperature reaction stage is adjusted: adjustment output high-frequency current 400A first after shove charge, to crucible
When shinny, adjustment output electric current is 350A, and 2, reinforcement generation phase: after five minutes, occurring reaction in-situ, releases heat and issues
White light, being immediately warming up to 1700 DEG C makes reinforcement test block be fusing into matrix.3, alloying: adjustment output electric current makes temperature
Reach 1800 ~ 2000 DEG C, metallic particles molten alloy, in induction from during stirring, alloy system occurs from inside to outside
Rolling stirring, reinforcement are uniformly distributed in high-entropy alloy matrix.
(5) the 4th steps, heat preservation cooling: warm to react molten alloy after five minutes and pour into water jacketed copper crucible, enhancing
Body particle is attached to the growth of fine grain particle surface in the base, obtains fine grain high-entropy alloy-base composite material.
Can be seen that black regular object from the SEM picture of Fig. 5 composite material is reinforcement particle TiC.Darker regions
For rich Co phase, matrix is mutually white area.
Claims (8)
1. high-entropy alloy-base composite material, which is characterized in that the composite material is interior raw type, with the conjunction of AlCoFeNiCu high entropy
Gold is matrix phase, with (TiC)xFor reinforced phase, it is denoted as (TiC)x/(AlCoFeNiCu)1-xWherein, x is 0.1 ~ 0.2.
2. high-entropy alloy-base composite material, which is characterized in that the composite material is interior raw type, with the conjunction of AlSiFeNiCu high entropy
Gold is matrix phase, with (TiC)xFor reinforced phase, it is denoted as (TiC)x/(AlSiFeNiCu)1-xWherein, x is 0.1 ~ 0.2.
3. the preparation method of high-entropy alloy-base composite material as described in claim 1, which comprises the following steps:
The first step, according to target composite material composition weighs high-purity Al, Co, Ni, Ti, Cu, Fe metallic particles, and to metallic particles
Surface is pre-processed, and surface oxide layer is removed；
Second step, preparation reinforcement test block: it is mixed through ball milling that high-purity Ti powder, C powder, Fe powder are weighed according to target composite material composition
It is dry after conjunction, reinforcement test block is prepared under a certain pressure；
Third step, by the sample prepared according to (TiC)x/(AlCoFeNiCu)1-xCorrespondence raw material successively add Al particle, increase
Strong body test block, Ni particle, Fe particle, Co particle, Cu particle reach 10 in vacuum degree-3When Pa or more, it is passed through argon gas and keeps air pressure
No more than 10-1Pa, energization induction melting are tentatively warming up to 950 ~ 1050 DEG C, observe in observation window and react in furnace, are warming up to
1450 ~ 1550 DEG C, when melting substantially wait react test block, and then 2000 ~ 2200 DEG C are warming up to, melting 8 ~ 12 minutes, melted repeatedly
Refining 2 ~ 3 times；
4th step, heat preservation cooling: after warm 3 ~ 8 minutes, reaction molten alloy is poured into water jacketed copper crucible, reinforcement particle
It is attached to the growth of fine grain particle surface in the base, obtains the high-entropy alloy-base composite material.
4. preparation method as claimed in claim 3, which is characterized in that in second step, rotational speed of ball-mill 250-300p.r.m；
Ball-milling Time is 6 ~ 8h；Ratio of grinding media to material is 4.5:1.
5. preparation method as claimed in claim 3, which is characterized in that in second step, drying temperature is 110 ~ 120 DEG C, dry
Time is 2 hours, and base sample is squeezed under 180MPa pressure.
6. the preparation method of high-entropy alloy-base composite material as claimed in claim 2, which comprises the following steps:
The first step, according to target composite material composition weighs high-purity Al, Si, Ni, Ti, Cu, Fe metallic particles, and to metallic particles
Surface is pre-processed, and surface oxide layer is removed；
Second step, preparation reinforcement test block: it is mixed through ball milling that high-purity Ti powder, C powder, Fe powder are weighed according to target composite material composition
It is dry after conjunction, reinforcement test block is prepared under a certain pressure；
Third step, by the sample prepared according to (TiC)x/(AlSiFeNiCu)1-xCorrespondence raw material successively add Al particle, increase
Strong body test block, Ni particle, Fe particle, Si particle, Cu particle reach 10 in vacuum degree-3When Pa or more, it is passed through argon gas and keeps air pressure
No more than 10-1Pa, energization induction melting are tentatively warming up to 950 ~ 1050 DEG C, observe in observation window and react in furnace, are warming up to
1450 ~ 1550 DEG C, when melting substantially wait react test block, and then 2000 ~ 2200 DEG C are warming up to, melting 8 ~ 12 minutes, melted repeatedly
Refining 2 ~ 3 times；
4th step, heat preservation cooling: after warm 3 ~ 8 minutes, reaction molten alloy is poured into water jacketed copper crucible, reinforcement particle
It is attached to the growth of fine grain particle surface in the base, obtains fine grain high-entropy alloy-base composite material.
7. preparation method as claimed in claim 6, which is characterized in that in second step, rotational speed of ball-mill 250-300p.r.m；
Ball-milling Time is 6 ~ 8h；Ratio of grinding media to material is 4.5:1.
8. preparation method as claimed in claim 6, which is characterized in that in second step, drying temperature is 110 ~ 120 DEG C, dry
Time is 2 hours, and base sample is squeezed under 180MPa pressure.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201710984945.5A CN109694979B (en) | 2017-10-20 | 2017-10-20 | High-entropy alloy-based composite material prepared by vacuum induction melting and preparation method thereof |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201710984945.5A CN109694979B (en) | 2017-10-20 | 2017-10-20 | High-entropy alloy-based composite material prepared by vacuum induction melting and preparation method thereof |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN109694979A true CN109694979A (en) | 2019-04-30 |
| CN109694979B CN109694979B (en) | 2021-05-07 |
Family
ID=66225389
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201710984945.5A Expired - Fee Related CN109694979B (en) | 2017-10-20 | 2017-10-20 | High-entropy alloy-based composite material prepared by vacuum induction melting and preparation method thereof |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN109694979B (en) |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN110157971A (en) * | 2019-06-06 | 2019-08-23 | 南京理工大学 | A kind of induction melting method of In-sltu reinforcement high-entropy alloy composite material |
| CN110257684A (en) * | 2019-07-22 | 2019-09-20 | 合肥工业大学 | A kind of preparation process of FeCrCoMnNi high-entropy alloy-base composite material |
| CN110387498A (en) * | 2019-07-30 | 2019-10-29 | 南京理工大学 | One kind is in FexOriginal position TiB is synthesized in CoNiCu high-entropy alloy2Method |
Citations (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101215663A (en) * | 2008-01-04 | 2008-07-09 | 哈尔滨工业大学 | High-entropy alloy-base composite material and preparation method thereof |
| US20090074604A1 (en) * | 2007-09-19 | 2009-03-19 | Industrial Technology Research Institute | Ultra-hard composite material and method for manufacturing the same |
| CN105543621A (en) * | 2016-01-18 | 2016-05-04 | 南京工程学院 | Endogenous nano ceramic reinforcement high-entropy alloy composite material and preparing method |
| CN105648297A (en) * | 2016-01-18 | 2016-06-08 | 南京工程学院 | Preparation method for high-entropy alloy composite material with externally-added nanometer ceramic phase reinforced and toughened |
| CN106834878A (en) * | 2017-04-01 | 2017-06-13 | 南京理工大学 | A kind of method that microwave sintering prepares endogenous high-entropy alloy-base composite material |
| CN107034410A (en) * | 2017-05-12 | 2017-08-11 | 南昌大学 | A kind of many pivot high-entropy alloys and preparation method thereof |
-
2017
- 2017-10-20 CN CN201710984945.5A patent/CN109694979B/en not_active Expired - Fee Related
Patent Citations (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US20090074604A1 (en) * | 2007-09-19 | 2009-03-19 | Industrial Technology Research Institute | Ultra-hard composite material and method for manufacturing the same |
| CN101215663A (en) * | 2008-01-04 | 2008-07-09 | 哈尔滨工业大学 | High-entropy alloy-base composite material and preparation method thereof |
| CN105543621A (en) * | 2016-01-18 | 2016-05-04 | 南京工程学院 | Endogenous nano ceramic reinforcement high-entropy alloy composite material and preparing method |
| CN105648297A (en) * | 2016-01-18 | 2016-06-08 | 南京工程学院 | Preparation method for high-entropy alloy composite material with externally-added nanometer ceramic phase reinforced and toughened |
| CN106834878A (en) * | 2017-04-01 | 2017-06-13 | 南京理工大学 | A kind of method that microwave sintering prepares endogenous high-entropy alloy-base composite material |
| CN107034410A (en) * | 2017-05-12 | 2017-08-11 | 南昌大学 | A kind of many pivot high-entropy alloys and preparation method thereof |
Non-Patent Citations (1)
| Title |
|---|
| BASHEV, V.F ET AL.: "《Structure and properties of cast and splat-quenched high-entropy Al–Cu–Fe–Ni–Si alloys》", 《PHYSICS OF METALS AND METALLOGRAPHY》 * |
Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN110157971A (en) * | 2019-06-06 | 2019-08-23 | 南京理工大学 | A kind of induction melting method of In-sltu reinforcement high-entropy alloy composite material |
| CN110257684A (en) * | 2019-07-22 | 2019-09-20 | 合肥工业大学 | A kind of preparation process of FeCrCoMnNi high-entropy alloy-base composite material |
| CN110257684B (en) * | 2019-07-22 | 2021-05-04 | 合肥工业大学 | Preparation process of FeCrCoMnNi high-entropy alloy-based composite material |
| CN110387498A (en) * | 2019-07-30 | 2019-10-29 | 南京理工大学 | One kind is in FexOriginal position TiB is synthesized in CoNiCu high-entropy alloy2Method |
| CN110387498B (en) * | 2019-07-30 | 2021-05-04 | 南京理工大学 | In FexIn-situ TiB synthesized in CoNiCu high-entropy alloy2Method (2) |
Also Published As
| Publication number | Publication date |
|---|---|
| CN109694979B (en) | 2021-05-07 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN106834878B (en) | A kind of method that microwave sintering prepares endogenous high-entropy alloy-base composite material | |
| CN101956094B (en) | Preparation method of high-strength and high-conductivity dispersion-strengthened alloy | |
| CN109182854B (en) | 1GPa high-strength aluminum-based light medium-entropy alloy and preparation method thereof | |
| CN107130125A (en) | A kind of preparation method of high-entropy alloy | |
| CN110157971B (en) | Induction smelting method of in-situ reinforced high-entropy alloy composite material | |
| CN103088242B (en) | Preparation method of aluminum-zinc-magnesium-copper-zirconium series high-strength aluminum alloy | |
| CN109694979A (en) | Vacuum induction melting prepares high-entropy alloy-base composite material and its method | |
| CN101979690B (en) | Method for preparing TiAl-based alloy sheet | |
| CN104894641B (en) | It is a kind of high fine and close（LaxCa1‑x）B6Polycrystalline cathode material and preparation method thereof | |
| CN110938769B (en) | Eutectic medium-entropy alloy and preparation method thereof | |
| CN107557609A (en) | A kind of copper alloy of single phase nano alumina particle dispersion-strengtherning and preparation method thereof | |
| CN108220703A (en) | A kind of cast Al-Si alloy of graphene and rare earth cooperative reinforcing and preparation method thereof | |
| CN113667875A (en) | MoNbTaTiVSix high-entropy alloy and preparation method thereof | |
| CN113337747B (en) | Preparation method of high-strength and high-conductivity copper alloy | |
| CN110408833A (en) | A kind of preparation method of NbTaTiZr high-entropy alloy and its powder | |
| CN108504968B (en) | Zr-Al-Ni-Cu bulk metallic glass with different crystallization phase types and contents and performance | |
| CN102251162B (en) | Preparation method of high performance nanometer lanthanide oxide doped molybdenum-silicon-boron alloy | |
| CN111116206A (en) | Preparation method of compact MoAlB ceramic material, product thereof and preparation method of high-purity MoAlB ceramic powder | |
| CN109082568A (en) | A kind of fabricated in situ nanometer CuAl2/Al2O3The preparation method of reinforced aluminum matrix composites | |
| CN113278863B (en) | Method for preparing titanium diboride copper-based composite material by vacuum hot pressing | |
| CN107099689A (en) | A kind of Al of reaction in-situ generation2O3The preparation method of particle enhanced aluminum-based composite material | |
| CN102534279B (en) | In situ reaction hot-pressing method for manufacturing intermetallic compound T2 phase alloys | |
| CN106636738A (en) | Titanium-silicon alloy material and preparation method thereof | |
| CN1978099A (en) | PbTe powde material formation preparing method | |
| CN112410597B (en) | Preparation method of nano WC dispersion strengthened copper |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| PB01 | Publication | ||
| PB01 | Publication | ||
| SE01 | Entry into force of request for substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| GR01 | Patent grant | ||
| GR01 | Patent grant | ||
| CF01 | Termination of patent right due to non-payment of annual fee |
Granted publication date: 20210507 |