CN110079722A - A kind of infusibility high-entropy alloy TiZrNbMoTa and its method for preparing powder metallurgy containing B - Google Patents
A kind of infusibility high-entropy alloy TiZrNbMoTa and its method for preparing powder metallurgy containing B Download PDFInfo
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- CN110079722A CN110079722A CN201910487529.3A CN201910487529A CN110079722A CN 110079722 A CN110079722 A CN 110079722A CN 201910487529 A CN201910487529 A CN 201910487529A CN 110079722 A CN110079722 A CN 110079722A
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- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 73
- 238000000034 method Methods 0.000 title claims abstract description 35
- 238000004663 powder metallurgy Methods 0.000 title claims abstract description 13
- 239000000843 powder Substances 0.000 claims abstract description 64
- 238000005245 sintering Methods 0.000 claims abstract description 34
- 238000005551 mechanical alloying Methods 0.000 claims abstract description 13
- 239000002994 raw material Substances 0.000 claims abstract description 10
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 6
- 229910052758 niobium Inorganic materials 0.000 claims abstract description 6
- 229910052715 tantalum Inorganic materials 0.000 claims abstract description 6
- 229910052726 zirconium Inorganic materials 0.000 claims abstract description 5
- 238000000713 high-energy ball milling Methods 0.000 claims description 12
- 239000000463 material Substances 0.000 claims description 11
- 238000010438 heat treatment Methods 0.000 claims description 5
- 229910052751 metal Inorganic materials 0.000 claims description 5
- 238000002791 soaking Methods 0.000 claims description 5
- 239000002184 metal Substances 0.000 claims description 4
- 229910052719 titanium Inorganic materials 0.000 claims description 3
- 238000000498 ball milling Methods 0.000 claims description 2
- 229910052796 boron Inorganic materials 0.000 claims description 2
- 238000007596 consolidation process Methods 0.000 claims description 2
- 239000011261 inert gas Substances 0.000 claims description 2
- 239000000126 substance Substances 0.000 claims description 2
- 238000002360 preparation method Methods 0.000 abstract description 6
- 239000004615 ingredient Substances 0.000 abstract description 4
- 238000005265 energy consumption Methods 0.000 abstract description 2
- 239000003870 refractory metal Substances 0.000 abstract description 2
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 description 12
- 239000012071 phase Substances 0.000 description 12
- 238000005275 alloying Methods 0.000 description 10
- 239000007789 gas Substances 0.000 description 9
- 239000011159 matrix material Substances 0.000 description 8
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 6
- 229910052786 argon Inorganic materials 0.000 description 6
- 238000005516 engineering process Methods 0.000 description 6
- 229910002804 graphite Inorganic materials 0.000 description 6
- 239000010439 graphite Substances 0.000 description 6
- 239000011812 mixed powder Substances 0.000 description 6
- 238000003723 Smelting Methods 0.000 description 4
- 239000013078 crystal Substances 0.000 description 4
- 238000004519 manufacturing process Methods 0.000 description 4
- IMNFDUFMRHMDMM-UHFFFAOYSA-N N-Heptane Chemical compound CCCCCCC IMNFDUFMRHMDMM-UHFFFAOYSA-N 0.000 description 3
- 238000004026 adhesive bonding Methods 0.000 description 3
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 3
- 239000003795 chemical substances by application Substances 0.000 description 3
- 238000001816 cooling Methods 0.000 description 3
- 238000000227 grinding Methods 0.000 description 3
- 239000001301 oxygen Substances 0.000 description 3
- 229910052760 oxygen Inorganic materials 0.000 description 3
- 239000002244 precipitate Substances 0.000 description 3
- 230000001681 protective effect Effects 0.000 description 3
- 238000007790 scraping Methods 0.000 description 3
- 229910000568 zirconium hydride Inorganic materials 0.000 description 3
- 238000011161 development Methods 0.000 description 2
- 238000011160 research Methods 0.000 description 2
- 238000005204 segregation Methods 0.000 description 2
- 230000015572 biosynthetic process Effects 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- 230000006835 compression Effects 0.000 description 1
- 238000007906 compression Methods 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 125000004122 cyclic group Chemical group 0.000 description 1
- 230000007812 deficiency Effects 0.000 description 1
- 238000013461 design Methods 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- PCHJSUWPFVWCPO-UHFFFAOYSA-N gold Chemical compound [Au] PCHJSUWPFVWCPO-UHFFFAOYSA-N 0.000 description 1
- 239000010931 gold Substances 0.000 description 1
- 229910052737 gold Inorganic materials 0.000 description 1
- 229910052735 hafnium Inorganic materials 0.000 description 1
- 229910000765 intermetallic Inorganic materials 0.000 description 1
- 238000003701 mechanical milling Methods 0.000 description 1
- 239000000203 mixture Substances 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
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Classifications
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
- B22F3/10—Sintering only
- B22F3/105—Sintering only by using electric current other than for infrared radiant energy, laser radiation or plasma ; by ultrasonic bonding
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F9/00—Making metallic powder or suspensions thereof
- B22F9/02—Making metallic powder or suspensions thereof using physical processes
- B22F9/04—Making metallic powder or suspensions thereof using physical processes starting from solid material, e.g. by crushing, grinding or milling
-
- 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
- C22C1/04—Making non-ferrous alloys by powder metallurgy
-
- 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
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F9/00—Making metallic powder or suspensions thereof
- B22F9/02—Making metallic powder or suspensions thereof using physical processes
- B22F9/04—Making metallic powder or suspensions thereof using physical processes starting from solid material, e.g. by crushing, grinding or milling
- B22F2009/043—Making metallic powder or suspensions thereof using physical processes starting from solid material, e.g. by crushing, grinding or milling by ball milling
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F2201/00—Treatment under specific atmosphere
- B22F2201/10—Inert gases
- B22F2201/11—Argon
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F2999/00—Aspects linked to processes or compositions used in powder metallurgy
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- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
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Abstract
The invention discloses a kind of infusibility high-entropy alloy TiZrNbMoTa and its method for preparing powder metallurgy containing B, it is that selection refractory metal element ti, Zr, Nb, Mo, Ta and nonmetalloid B are raw material, first alloy powder is prepared through mechanical alloying, it recycles discharge plasma sintering to be consolidated, obtains block alloy material.The crystallite dimension of gained infusibility high-entropy alloy of the invention is small, and ingredient is uniform, and compactness is good, and preparation method is simple, can be made through once sintered, can significantly reduce energy consumption and reduce equipment loss, have applications well prospect.
Description
Technical field
The invention belongs to field of alloy material preparation, and in particular to a kind of infusibility high-entropy alloy TiZrNbMoTa containing B and
Its method for preparing powder metallurgy.
Background technique
Existing Ni base, Co based high-temperature alloy are widely used in aerospace field with its excellent high temperature resistance.
However as the development of science and technology, the service condition of high temperature alloy is increasingly harsh, on existing high temperature alloy basis, even if
It adds some refractory alloy elements and is also difficult to improve it using temperature, significantly limit its related application.Therefore it develops more
High performance high temperature alloy has great scientific research and engineering significance.Professor Ye Junwei proposes the general of high-entropy alloy first within 2004
It reads, different from traditional alloy design concept, with 5 kinds or 5 kinds or more of alloying element by equimolar ratio or approximate equimolar
The formation of intermetallic compound can be avoided to a certain extent by its distinctive high entropy effect than component alloy, formed simple
FCC or BCC solid solution structure, this is but also high-entropy alloy because of its excellent performance, becomes the research heat of field of alloy material
Point.The high-entropy alloy system studied in the past is mostly the i.e. CoCrFeNi series high-entropy alloy based on transiting group metal elements.With
The development of aeronautical and space technology, it is another kind of with high-melting-point element, such as the high entropy of the infusibility that forms based on Nb, Mo, Ta, Hf closes
Gold is received more and more attention and is studied, and with high-melting-point, higher elevated temperature strength has excellent softening resistant to high temperatures,
The excellent properties such as high-temperature corrosion resistance are expected to be applied to aerospace field as high temperature alloy, open up for the exploitation of high temperature alloy
New direction.
Current existing infusibility high-entropy alloy mostly uses smelting process to prepare greatly, and since element fusing point is high, ingredient is difficult to uniformly,
Macrosegregation is caused, service performance is influenced.In addition, high-melting-point high-entropy alloy hardness is high, brittleness is shown at room temperature, and ingot casting is difficult
To shape.Mechanical Alloying is to gradually form alloying by the impact several times between powder and abrading-ball, is effectively kept away
Component segregation is exempted from；Then when sintering, it can be carried out in various molds, obtain nearly end form shape, avoid asking for processing difficulties
Topic.Therefore, the present invention prepares the infusibility high-entropy alloy containing B using powder metallurgy (mechanical alloying+discharge plasma sintering)
TiZrNbMoTa high-entropy alloy.
Summary of the invention
In order to overcome the deficiencies of the prior art, and further improve alloy property, the present invention provides a kind of, and the infusibility containing B is high
Entropy alloy TiZrNbMoTa and its method for preparing powder metallurgy.
To achieve the above object, the present invention adopts the following technical scheme:
A kind of infusibility high-entropy alloy TiZrNbMoTa containing B, is prepared using powder metallurgy process, i.e. selection refractory metal
Element ti, Zr, Nb, Mo, Ta and nonmetalloid B are raw material, first prepare alloy powder through mechanical alloying (MA), are recycled
Discharge plasma sintering (SPS) is consolidated, and block alloy material is obtained.It specifically comprises the following steps:
1) chemical formula TiZrNbMoTaB is pressedxMolar ratio shown in (wherein, x=0-0.3) weighs Ti, Zr, Nb, Mo, Ta and B respectively
Raw material powder is mixed uniformly and carries out high-energy ball milling under inert gas protection, keeps powder gradually real in mechanical milling process
Existing alloying, obtains TiZrNbMoTaBxHigh-entropy alloy powder；The process conditions of the high-energy ball milling are as follows: ball material mass ratio is
12:1~15:1, rotational speed of ball-mill are 200~300r/min, and Ball-milling Time is 20~40h；
2) high-entropy alloy powder obtained by step 1) is subjected to discharge plasma sintering, makes its consolidation, obtains blocky high-entropy alloy material
Material；The process conditions of the discharge plasma sintering are as follows: sintering temperature is 1300-1600 DEG C, soaking time 20-40min, is burnt
Knot pressure power is 30-50Mpa, and heating rate is 50-100 DEG C/min.
The granularity of raw material powder described in step 1) is 200~400 mesh.
In step 1) mechanical alloying process, powder is during high-energy ball milling, by constantly deforming, being broken, cold
Cyclic process is welded, alloying is done step-by-step, eventually forms the high-entropy alloy powder of single-phase FCC configuration.
Powder is consolidated through step 2, the phase composition of obtained blocky high entropy alloy material be FCC phase+BCC phase and
The microscopic structure of precipitated phase, different B content alloys is similar, with TiZrNbMoTaB 0.1For, Fig. 1 is its microscopic structure SEM-
BSE figure forms matrix by figure it can be observed that bulk canescence region, and tiny black precipitated phase is evenly distributed on matrix
On.
Compare that (Fig. 2 is distinct methods by the TiZrNbMoTa high-melting-point high-entropy alloy being prepared with smelting process
The SEM-BSE for the TiZrNbMoTa high-melting-point high-entropy alloy being prepared schemes), tissue, present invention gained infusibility high-entropy alloy
Crystallite dimension be substantially reduced, and the alloy that displaing micro tissue topography and smelting process obtain also has very big difference；In performance, as cast condition
The vickers microhardness of TiZrNbMoTa infusibility high-entropy alloy is 4.9GPa, compression yield strength 1390MPa, plastic strain
It is 6%, can reach using the vickers microhardness of the TiZrNbMoTa infusibility high-entropy alloy of the identical component of this method preparation
1467Hv, compressed rupture strength can reach 3724Mpa, and breaking strain can reach 12.1%, it is seen that can be fine using powder metallurgy
Strengthen the alloy.
It is compared with the prior art, the present invention has the advantage that:
(1) compared to smelting process, forming technology of the present invention does not need to heat the material to fusing point or more, by primary under solid phase
Sintering can be obtained high-entropy alloy block materials of good performance, can significantly reduce energy consumption and reduce equipment loss, simplify work
Skill, high production efficiency；And the block alloy microscopic structure crystal grain being prepared is tiny, ingredient is uniform, eliminates ingredient well
Segregation, compactness is good, and can realize near-net-shape to block materials in conjunction with shaping dies.
(2) TiZrNbMoTaB prepared by the present inventionx(x=0 ~ 0.3) infusibility high-entropy alloy, wherein TiZrNbMoTaB0.1Room
The lower mechanical property of temperature is best: it compresses maximum breaking strength σmax=4252.1Mpa, maximum breaking strain are ε=11.9%, are had excellent
Different comprehensive mechanical property.
Detailed description of the invention
Fig. 1 is TiZrNbMoTaB prepared by embodiment 1 0.1The SEM-BSE of infusibility high-entropy alloy schemes.
Fig. 2 is the SEM-BSE figure for the TiZrNbMoTa high-melting-point high-entropy alloy that distinct methods are prepared.
Specific embodiment
In order to make content of the present invention easily facilitate understanding, With reference to embodiment to of the present invention
Technical solution is described further, but the present invention is not limited only to this.
Using planetary high-energy ball mill progress high-energy ball milling, the material of abrading-ball and ball grinder is preferably hard alloy.
Embodiment 1
A kind of TiZrNbMoTaB0.1The preparation method of infusibility high-entropy alloy is using mechanical alloying and discharge plasma sintering
The manufacturing process that technology combines comprising:
Step 1: TiZrNbMoTaB is prepared using mechanical alloying method 0.1Alloy powder
(1) Ti powder, the ZrH that granularity is 300 mesh are chosen2Powder (uses ZrH2Powder replace pure Zr powder), Nb powder, Mo powder, Ta powder and
Unsetting B powder is raw material, and 1:1:1:1:1:0.1 weighs powder in molar ratio, and is uniformly mixed；
(2) mixed-powder and hard alloy abrading-ball are put into hard alloy tank and carry out high-energy ball milling, vacuumized simultaneously in ball grinder
High-purity argon gas is filled as protective atmosphere, the technological parameter of high-energy ball milling: ratio of grinding media to material 15:1, rotational speed of ball-mill 250r/min, ball
Time consuming is 30h, and shutting down every 5h will carry out scraping powder in ball grinder feeding glove box, full of argon gas as protection gas in glove box
Body, while adition process controlling agent normal heptane make the abundant alloying of metal powder as far as possible and reduce oxygen to a certain extent
Change；As alloying is done step-by-step in the continuous progress of ma process, mixed-powder during this, being gradually changed into has
The alloy powder of single-phase FCC configuration, meanwhile, the crystal grain inside powder is also constantly refined in this process；
Step 2: discharge plasma sintering
16g alloy powder is weighed into the graphite jig of φ 15mm, one layer of graphite paper of place mat, prevents from gluing between mold and powder
Knot；The technological parameter of sintering are as follows: 1400 DEG C of sintering temperature, soaking time 30min, sintering pressure 50Mpa, 100 DEG C of heating rate/
min；Furnace cooling after the completion of sintering, to be cooled to 100 DEG C or less unloading pressures take out sample to get to having a size of φ 15mm
The block high entropy alloy material of × 10mm.
Gained TiZrNbMoTaB after the present embodiment sintering 0.1The microscopic structure of infusibility high-entropy alloy is FCC+BCC matrix,
And in its matrix Dispersed precipitate tiny precipitated phase, maximum compressive strength reaches 4252.1Mpa, breaking strain at room temperature
It is 11.9%, Vickers hardness 1511.7Hv.
Embodiment 2
A kind of TiZrNbMoTaB0.2The preparation method of infusibility high-entropy alloy is using mechanical alloying and discharge plasma sintering
The manufacturing process that technology combines comprising:
Step 1: TiZrNbMoTaB is prepared using mechanical alloying method0.2Alloy powder
(1) Ti powder, the ZrH that granularity is 300 mesh are chosen2Powder (uses ZrH2Powder replace pure Zr powder), Nb powder, Mo powder, Ta powder and
Unsetting B powder is raw material, and 1:1:1:1:1:0.2 weighs powder in molar ratio, and is uniformly mixed；
(2) mixed-powder and hard alloy abrading-ball are put into hard alloy tank and carry out high-energy ball milling, vacuumized simultaneously in ball grinder
High-purity argon gas is filled as protective atmosphere, the technological parameter of high-energy ball milling: ratio of grinding media to material 12:1, rotational speed of ball-mill 200r/min, ball
Time consuming is 40h, and shutting down every 5h will carry out scraping powder in ball grinder feeding glove box, full of argon gas as protection gas in glove box
Body, while adition process controlling agent normal heptane make the abundant alloying of metal powder as far as possible and reduce oxygen to a certain extent
Change；As alloying is done step-by-step in the continuous progress of ma process, mixed-powder during this, being gradually changed into has
The alloy powder of single-phase FCC configuration, meanwhile, the crystal grain inside powder is also constantly refined in this process；
Step 2: discharge plasma sintering
16g alloy powder is weighed into the graphite jig of φ 15mm, one layer of graphite paper of place mat, prevents from gluing between mold and powder
Knot；The technological parameter of sintering are as follows: 1500 DEG C of sintering temperature, soaking time 15min, sintering pressure 50Mpa, 100 DEG C of heating rate/
min；Furnace cooling after the completion of sintering, to be cooled to 100 DEG C or less unloading pressures take out sample to get being about φ to size
The block high entropy alloy material of 15mm × 10mm.
Gained TiZrNbMoTaB after the present embodiment sintering0.2The microscopic structure of infusibility high-entropy alloy is FCC+BCC matrix,
In matrix Dispersed precipitate tiny precipitated phase, breaking strength reaches 4065.6Mpa at room temperature, breaking strain 11.43%, dimension
Family name's hardness is 1660.1Hv.
Embodiment 3
A kind of TiZrNbMoTaB0.3The preparation method of infusibility high-entropy alloy is using mechanical alloying and discharge plasma sintering
The manufacturing process that technology combines comprising:
Step 1: TiZrNbMoTaB is prepared using mechanical alloying method0.3Alloy powder
(1) Ti powder, the ZrH that granularity is 300 mesh are chosen2Powder (uses ZrH2Powder replace pure Zr powder), Nb powder, Mo powder, Ta powder and
Unsetting B powder is raw material, and 1:1:1:1:1:0.3 weighs powder in molar ratio, and is uniformly mixed；
(2) mixed-powder and hard alloy abrading-ball are put into hard alloy tank and carry out high-energy ball milling, vacuumized simultaneously in ball grinder
High-purity argon gas is filled as protective atmosphere, the technological parameter of high-energy ball milling: ratio of grinding media to material 13:1, rotational speed of ball-mill 300r/min, ball
Time consuming is 20h, and shutting down every 5h will carry out scraping powder in ball grinder feeding glove box, full of argon gas as protection gas in glove box
Body, while adition process controlling agent normal heptane make the abundant alloying of metal powder as far as possible and reduce oxygen to a certain extent
Change；As alloying is done step-by-step in the continuous progress of ma process, mixed-powder during this, being gradually changed into has
The alloy powder of single-phase FCC configuration, meanwhile, the crystal grain inside powder is also constantly refined in this process；
Step 2: discharge plasma sintering
16g alloy powder is weighed into the graphite jig of φ 15mm, one layer of graphite paper of place mat, prevents from gluing between mold and powder
Knot；The technological parameter of sintering are as follows: 1600 DEG C of sintering temperature, soaking time 40min, sintering pressure 30Mpa, 50 DEG C of heating rate/
min；Furnace cooling after the completion of sintering, to be cooled to 100 DEG C or less unloading pressures take out sample to get being about φ to size
The block high entropy alloy material of 15mm × 10mm.
Gained TiZrNbMoTaB after the present embodiment sintering0.3The microscopic structure of infusibility high-entropy alloy is FCC+BCC matrix,
In matrix Dispersed precipitate tiny precipitated phase, breaking strength reaches 3925.6Mpa, breaking strain 11.1%, Vickers at room temperature
Hardness is 1710.2Hv.
The foregoing is merely presently preferred embodiments of the present invention, all equivalent changes done according to scope of the present invention patent with
Modification, is all covered by the present invention.
Claims (6)
1. a kind of method for preparing powder metallurgy of the infusibility high-entropy alloy TiZrNbMoTa containing B, it is characterised in that: select high-melting-point
Metal element Ti, Zr, Nb, Mo, Ta and nonmetalloid B are raw material, first prepare alloy powder through mechanical alloying, are recycled
Discharge plasma sintering is consolidated, and block alloy material is obtained.
2. the method for preparing powder metallurgy of the infusibility high-entropy alloy TiZrNbMoTa containing B, feature exist according to claim 1
In: specifically comprise the following steps:
1) chemical formula TiZrNbMoTaB is pressedxShown molar ratio weighs the raw material powder of Ti, Zr, Nb, Mo, Ta and B respectively, wherein x
=0-0.3；It is mixed uniformly and carries out high-energy ball milling under inert gas protection, obtain TiZrNbMoTaBxHigh-entropy alloy
Powder；
2) high-entropy alloy powder obtained by step 1) is subjected to discharge plasma sintering, makes its consolidation, obtains blocky high-entropy alloy material
Material.
3. the method for preparing powder metallurgy of the infusibility high-entropy alloy TiZrNbMoTa containing B, feature exist according to claim 2
In: the granularity of the raw material powder is 200~400 mesh.
4. the method for preparing powder metallurgy of the infusibility high-entropy alloy TiZrNbMoTa containing B, feature exist according to claim 2
In: the process conditions of high-energy ball milling described in step 1) are as follows: ball material mass ratio is 12:1~15:1, and rotational speed of ball-mill is 200~300r/
Min, Ball-milling Time are 20~40h.
5. the method for preparing powder metallurgy of the infusibility high-entropy alloy TiZrNbMoTa containing B, feature exist according to claim 2
In the process conditions of discharge plasma sintering described in step 2 are as follows: sintering temperature is 1300~1600 DEG C, soaking time is 20~
40min, sintering pressure are 30~50Mpa, and heating rate is 50~100 DEG C/min.
6. a kind of infusibility high-entropy alloy TiZrNbMoTa as made from any the method for claim 1-5 containing B.
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Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN111058076A (en) * | 2019-12-30 | 2020-04-24 | 安徽工业大学 | Zr-based high-entropy alloy material and method for synthesizing porous spherical structure on surface of Zr-based high-entropy alloy |
| CN111118379A (en) * | 2020-01-15 | 2020-05-08 | 福建工程学院 | Co-bonded TiZrNbMoTa refractory high-entropy alloy and preparation method thereof |
| CN113996780A (en) * | 2021-11-02 | 2022-02-01 | 南京国重新金属材料研究院有限公司 | Mixing method of high-entropy alloy powder containing ultralow-atomic-ratio elements |
| CN114737099A (en) * | 2021-01-07 | 2022-07-12 | 湖南工业大学 | NbCrReRuMo high-strength refractory high-entropy alloy and preparation method thereof |
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| CN114737099A (en) * | 2021-01-07 | 2022-07-12 | 湖南工业大学 | NbCrReRuMo high-strength refractory high-entropy alloy and preparation method thereof |
| CN114737099B (en) * | 2021-01-07 | 2024-02-09 | 苏州雷佳诺电子科技有限公司 | NbCrReRuMo high-strength refractory high-entropy alloy and preparation method thereof |
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| CN113996780B (en) * | 2021-11-02 | 2023-08-22 | 南京国重新金属材料研究院有限公司 | Mixing method of high-entropy alloy powder containing ultralow atomic ratio elements |
| CN115213406A (en) * | 2022-06-24 | 2022-10-21 | 中北大学 | Method for preparing refractory high-entropy alloy by explosive loading |
| CN115213406B (en) * | 2022-06-24 | 2024-02-27 | 中北大学 | Method for preparing refractory high-entropy alloy by explosive loading |
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