CN104278173B - A kind of high-strength high-ductility TiAl alloy material and preparation method thereof - Google Patents
A kind of high-strength high-ductility TiAl alloy material and preparation method thereof Download PDFInfo
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- 239000000956 alloy Substances 0.000 title claims abstract description 95
- 229910010038 TiAl Inorganic materials 0.000 title claims abstract description 59
- 238000002360 preparation method Methods 0.000 title claims abstract description 26
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 66
- 238000000034 method Methods 0.000 claims abstract description 40
- 238000010438 heat treatment Methods 0.000 claims abstract description 32
- 238000007711 solidification Methods 0.000 claims abstract description 31
- 230000008023 solidification Effects 0.000 claims abstract description 31
- 238000007667 floating Methods 0.000 claims abstract description 22
- 239000013078 crystal Substances 0.000 claims abstract description 18
- 230000005674 electromagnetic induction Effects 0.000 claims abstract description 9
- 239000000725 suspension Substances 0.000 claims abstract description 9
- 238000003723 Smelting Methods 0.000 claims abstract description 8
- 238000005266 casting Methods 0.000 claims abstract description 8
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 claims abstract description 7
- 229910052802 copper Inorganic materials 0.000 claims abstract description 7
- 239000010949 copper Substances 0.000 claims abstract description 7
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims abstract description 7
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 claims description 22
- 238000005275 alloying Methods 0.000 claims description 11
- 229910052786 argon Inorganic materials 0.000 claims description 11
- 239000007789 gas Substances 0.000 claims description 10
- 238000005516 engineering process Methods 0.000 claims description 8
- 230000008018 melting Effects 0.000 claims description 8
- 238000002844 melting Methods 0.000 claims description 8
- 239000000446 fuel Substances 0.000 claims description 6
- 239000000155 melt Substances 0.000 claims description 4
- 230000026267 regulation of growth Effects 0.000 claims description 4
- 230000001105 regulatory effect Effects 0.000 claims description 3
- 239000000203 mixture Substances 0.000 abstract description 7
- 239000000463 material Substances 0.000 abstract description 6
- 238000005204 segregation Methods 0.000 abstract description 3
- 238000000137 annealing Methods 0.000 abstract description 2
- 238000007499 fusion processing Methods 0.000 abstract 1
- 239000012071 phase Substances 0.000 description 18
- PNEYBMLMFCGWSK-UHFFFAOYSA-N Alumina Chemical compound [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 description 4
- 229910000765 intermetallic Inorganic materials 0.000 description 3
- 238000012512 characterization method Methods 0.000 description 2
- 238000011109 contamination Methods 0.000 description 2
- 229910052751 metal Inorganic materials 0.000 description 2
- 239000002184 metal Substances 0.000 description 2
- 230000003647 oxidation Effects 0.000 description 2
- 238000007254 oxidation reaction Methods 0.000 description 2
- 239000002994 raw material Substances 0.000 description 2
- 229910018125 Al-Si Inorganic materials 0.000 description 1
- 229910018520 Al—Si Inorganic materials 0.000 description 1
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 1
- 241000446313 Lamella Species 0.000 description 1
- 230000000740 bleeding effect Effects 0.000 description 1
- 239000012141 concentrate Substances 0.000 description 1
- 239000000470 constituent Substances 0.000 description 1
- 230000007423 decrease Effects 0.000 description 1
- 229910002804 graphite Inorganic materials 0.000 description 1
- 239000010439 graphite Substances 0.000 description 1
- 239000012535 impurity Substances 0.000 description 1
- 238000009413 insulation Methods 0.000 description 1
- 239000007791 liquid phase Substances 0.000 description 1
- 230000008520 organization Effects 0.000 description 1
- RVTZCBVAJQQJTK-UHFFFAOYSA-N oxygen(2-);zirconium(4+) Chemical compound [O-2].[O-2].[Zr+4] RVTZCBVAJQQJTK-UHFFFAOYSA-N 0.000 description 1
- 230000001737 promoting effect Effects 0.000 description 1
- 230000001681 protective effect Effects 0.000 description 1
- 239000000376 reactant Substances 0.000 description 1
- 238000007789 sealing Methods 0.000 description 1
- 238000000926 separation method Methods 0.000 description 1
- 238000006467 substitution reaction Methods 0.000 description 1
- 230000002277 temperature effect Effects 0.000 description 1
- 229910001928 zirconium oxide Inorganic materials 0.000 description 1
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Abstract
The invention discloses a kind of high-strength high-ductility TiAl alloy material and preparation method thereof.The TiAl alloy material of the present invention is made up of Ti, Al, Nb, and its atomic percent is: (44 ~ 51) Ti-(43 ~ 47) Al-(6 ~ 9) Nb.The preparation method of the high-strength high-ductility TiAl alloy material of the present invention is: water jacketed copper crucible electromagnetic induction suspension smelting TiAl alloy master alloy ingot, and obtains foundry alloy bar by inhaling casting；Adopt four mirror optics floating region directional solidification furnaces, foundry alloy bar is oriented solidification, control TiAl alloy lamellar orientation and obtain PST crystal；Again through vacuum heat treatment furnace to PST crystal in α monophase field heat treatment and stress relief annealing, eliminate B2 phase segregation and eliminate residual stress, ultimately forming the TiAl alloy material with high-strength high-plasticity.TiAl alloy material prepared by the present invention avoids the crucible pollution to TiAl alloy in fusion process, and overcomes that tradition seed-grain method composition performance is uneven, the shortcoming of processed complex, and this material is while improving intensity, it is thus achieved that significant room-temperature tensile plasticity.
Description
Technical field
The invention belongs to inter-metallic compound material technical field, specifically on the basis of appropriate design alloying component, adopt optics floating region directional freeze method and vacuum heat, prepare the TiAl alloy material under a kind of room temperature with high intensity and high-ductility.
Background technology
TiAl intermetallic compound has low-density, high elastic modulus and good elevated temperature strength, creep resistant and oxidation resistance.It uses temperature up to 750～900 DEG C, close with Ni based high-temperature alloy；But its density is only the half of high temperature alloy, thus it is the substitution material of desirable Ni based high-temperature alloy, can be widely applied to the high-temperature component of automobile or aero-engine such as blade, the turbine disk and air bleeding valve etc..
But due to the intrinsic fragility of intermetallic compound, TiAl alloy brittleness at room temperature difference becomes the main cause hindering its industrial applications.So, big quantity research concentrates on and controls TiAl alloy organizational structure by directional solidification means.Due to the obvious anisotropy that intensity and plasticity in TiAl alloy PST crystal present, the method that TiAl alloy adopts directional solidification produces complete lamellar structure PST crystal, and make the direction of growth that its lamellar structure is oriented parallel in directional solidification crystal, it is possible to improve the mechanical property of TiAl alloy.
Tradition directional freeze method adopts crucible for smelting, and in TiAl alloy, Ti element is at high temperature extremely active, can react with major part crucible material, such as aluminium oxide, zirconium oxide and graphite etc..These reactants exist as impurity and change alloying component, cause the significantly decline of tissue change and performance.And floating zone method directional solidification is to utilize the liquid phase surface tension of molten state to maintain the melting zone between crystal and the fuel rod grown to stablize, whole process is without containers such as crucibles, thus avoiding the pollution of container alloy.JohnsonD.R and Yamaguchi et al. solidifies seed-grain method by α phase, selects Ti-Al-Si system alloy as seed crystal, obtains lamellar orientation by necking down crystal separation method and be completely parallel to the monocrystalline PST of the direction of growth.Seed crystal composition generally there are differences cause that the composition of directional solidificating alloy and performance are uneven with foundry alloy composition, and the complicated process of preparation of seed crystal.Therefore, seed-grain method has clearly disadvantageous.
Its mechanical behavior under high temperature of high Nb containing TiAl based alloy, creep-resistant property and oxidation susceptibility are significantly higher than general T iAl alloy, carry operation at high temperature about 60～100, DEG C are the TiAl alloy having future in engineering applications most.But owing to Nb element is the very capable element of stable β phase, under growth rate slower in directional solidification process, it is readily formed substantial amounts of β segregation, is cooled to room temperature and forms B2 phase；B2 phase is at room temperature brittlement phase, has a strong impact on the room-temperature property of TiAl alloy.
Therefore, it is necessary to avoid the uneven of composition performance that the pollution of crucible alloy and seed-grain method cause in directional solidification process, and eliminate brittlement phase by heat treatment, to obtain the TiAl alloy with excellent properties.
Summary of the invention
It is an object of the invention to provide a kind of TiAl alloy material with excellent room temperature strength and stretching plastic and preparation method thereof.By adopting non-seed-grain method optics floating region directional solidification, and completely eliminate fragility B2 phase by heat treatment, successfully obtain and there is desirable lamellar orientation, the free of contamination TiAl alloy monocrystalline of even tissue,
The technical solution realizing the object of the invention is: a kind of high-strength high-ductility TiAl alloy material, and with atomic percentage, its alloying component is: (44～51) Ti-(43～47) Al-(6～9) Nb.
The preparation method of above-mentioned high-strength high-ductility TiAl alloy material, its preparation technology is:
(1) electromagnetic induction suspension smelting TiAl alloy foundry alloy button ingot, adopts gravitation casting method or suction casting method to obtain foundry alloy bar；
(2) foundry alloy bar is cut into upper and lower bar two parts, respectively as fuel rod and the seed crystal rod of optics floating region directional solidification furnace；Distance between upper and lower bar is 3～5mm；Pass into high-purity argon gas as atmosphere protection; the axially opposing rotating speed regulating upper and lower bar is 20～30rpm; start heating; the opposite side making upper and lower bar first melts, and adjusts the position of upper and lower bar so that it is opposite side engages after moving closer to; regulate power to the 55～70% of general power; when floating region smooth surface and when melting uniform, growth regulation speed is 2.5～20mm/h, starts directional solidification；
(3) the TiAl alloy monocrystalline bar of preparation is carried out vacuum heat；Adopt the Technology for Heating Processing that 1250 DEG C～1350 DEG C × 12h～24h+900 DEG C × 30min/ stove is cold.
Electromagnetic induction suspension melting described in step (1) adopts water jacketed copper crucible, and described foundry alloy bar size is Φ (4～6) mm × 120mm.
In step (2), the flow of high-purity argon gas is 3～5L/min.
Compared with prior art, its remarkable advantage is the present invention:
(1) the TiAl alloy material process of preparing that the present invention proposes can increase substantially the room-temperature mechanical property of this alloy, especially improves brittleness at room temperature.
(2) non-seed crystal floating zone method directional solidification technique is adopted, it is prevented that the shortcoming avoiding processed complex in seed-grain method, composition uneven microstructure while alloy contamination.
(3) a large amount of fragility B2 phases remained in tissue after using vacuum heat to completely eliminate TiAl alloy directional solidification, thus obtaining the alloy material of even tissue, room-temperature property excellence.
(4) the method preparation technology is simple, and cost is low, improves brittleness at room temperature effect notable, has general applicability and promotional value.
Accompanying drawing explanation
Fig. 1 is the preparation flow figure for high-strength high-ductility TiAl alloy material.
Fig. 2 is TiAl alloy directional solidification monocrystalline (a) and lamellar orientation (b) microscopic structure.
Fig. 3 is the microstructure (a is before heat treatment, and b is after heat treatment) of segregation before and after TiAl alloy monocrystalline different heat treatment technique.
Fig. 4 is the XRD diffraction pattern of TiAl alloy monocrystalline before and after different heat treatment technique.
Fig. 5 is TiAl alloy room temperature tensile mechanical curves.
Detailed description of the invention
A kind of high-strength high-ductility TiAl alloy material of the present invention and preparation method thereof, is described in further detail the present invention below in conjunction with accompanying drawing 1, and its detailed description of the invention is as follows:
(1) in conjunction with Fig. 1, a kind of high-strength high-ductility TiAl alloy material of the present invention, its alloying component atomic percent is: (44～51) Ti-(43～47) Al-(6～9) Nb.By adjusting the proportion relation between atomic component so that it is first precipitated phase is all β phase.
(2) choose water jacketed copper crucible electromagnetic induction suspension smelting TiAl alloy foundry alloy button ingot, adopt suction casting method to obtain foundry alloy bar.
(3) foundry alloy bar is cut into fuel rod and seed crystal rod two parts, is oriented solidification by floating zone method；Pass into high-purity argon gas as atmosphere protection, regulate upper-lower section relative rotation speed, heating power and growth rate and control TiAl alloy lamellar orientation and obtain crystal growth.
(4) the TiAl alloy monocrystalline bar of preparation is carried out vacuum heat；Adopt insulation after annealing after α monophase field heats certain time；Fragility B2 phase and residual stress are completely eliminated, it is thus achieved that high-strength high-ductility TiAl alloy material.
(5) utilize OM, XRD that the TiAl alloy of preparation is carried out Microstructure characterization, and further it is carried out mechanical property sign, to determine the TiAl alloy material microstructure with best comprehensive mechanical property and corresponding preparation technology parameter thereof.
Below in conjunction with specific embodiment, the invention will be further described.
Embodiment 1
(1) raw-material selection:
It is Ti47Al45Nb8 (atomic percent) that the present invention prepares the alloying component of master alloy ingot selection, and purity Ti, the Al of each metal constituent element is 99.999%, and Nb is 99.95%.
(2) preparation of master alloy ingot:
Under high-purity argon gas protective condition, found master alloy ingot with water jacketed copper crucible electromagnetic induction suspension smelting furnace: after the surface mechanical grinding of raw metal is removed the oxide skin on surface, get the raw materials ready according to the composition proportion material designed；According to the weight of every ingot about 70g, the material prepared is put into the water jacketed copper crucible of smelting furnace, is evacuated to 5 × 10-3Pa；Being filled with the high-purity argon gas (99.999%) of a certain amount of pressure in stove, argon pressure ranges for 0.8～1MPa.The master alloy ingot that multi-pass melting is uniformly mixed for 3～4 times.Subsequently master alloy ingot is inhaled and cast Φ 6 × 120mm bar.
(3) optics floating region directional solidification:
Foundry alloy bar is cut into upper and lower bar two parts, respectively as fuel rod and the seed crystal rod of optics floating region directional solidification furnace；Distance between upper and lower bar is 3～5mm；Pass into the high-purity argon gas of 5L/min as atmosphere protection; regulate the axially opposing rotating speed 30rpm of upper and lower bar; start heating; the opposite side making upper and lower bar first melts, and adjusts the position of upper and lower bar so that it is opposite side engages after moving closer to; regulate power to the 68% of general power; when smooth surface fusing in floating region is uniform (floating region is without when substantially shaking), growth regulation speed is 5mm/h, starts directional solidification；Directional solidification process is stopped when growing to 80mm.
(4) vacuum heat
Directional solidification bar mono crystalline portion is put into alundum tube, is evacuated to tube sealing after 10-3Pa, put into heat-treatment furnace, adopt the Technology for Heating Processing that 1300 DEG C × 24h+900 DEG C × 30min/ stove is cold.
(5) structure and performance characterization
Fig. 2 a is the coupon photomacrograph after the directional solidification of optics floating region, it is seen that sample experiences in directional solidification after of short duration competition is eliminated and rapidly becomes crystal growth, and Fig. 2 b shows that monocrystalline lamella is oriented parallel to the direction of growth.Fig. 3 (a) and Fig. 3 (b) are micro-organization charts before and after heat treatment, compose organization internal before can be seen that heat treatment in conjunction with the XRD figure of Fig. 4 and are dispersed with substantial amounts of B2 phase, and after 24h heat treatment, B2 is completely eliminated.Fig. 5 is the room temperature tensile load-deformation curve of prepared high-strength high-ductility TiAl alloy, and its yield strength is 729MPa, and plastic strain simultaneously reaches 6.9%, has very excellent room-temperature mechanical property.
Embodiment 2
Adopt the preparation method identical with embodiment 1, alloying component is Ti44Al47Nb9 (atomic percent), optics floating region directional solidification processes is relative rotation speed 20rpm, heating power 55%, growth rate is 2.5mm/h, and vacuum heat treatment process is that 1250 DEG C × 12h+900 DEG C × 30min/ stove is cold, and B2 phase is completely eliminated, obtaining TiAl alloy material room temperature tensile yield strength is 550MPa, and plastic strain is 6.0%.
Embodiment 3
Adopt the preparation method identical with embodiment 1, alloying component is Ti51Al40Nb9 (atomic percent), optics floating region directional solidification processes is relative rotation speed 25rpm, heating power 70%, growth rate is 10mm/h, and vacuum heat treatment process is that 1300 DEG C × 20h+900 DEG C × 30min/ stove is cold, and B2 phase is completely eliminated, obtaining TiAl alloy material room temperature tensile yield strength is 628MPa, and plastic strain is 6.5%.
Embodiment 4
Adopt the preparation method identical with embodiment 1, alloying component is Ti48Al43Nb9 (atomic percent), optics floating region directional solidification processes is relative rotation speed 20rpm, heating power 68%, growth rate is 15mm/h, and vacuum heat treatment process is that 1350 DEG C × 24h+900 DEG C × 30min/ stove is cold, and B2 phase is completely eliminated, obtaining TiAl alloy material room temperature tensile yield strength is 660MPa, and plastic strain is 6.2%.
Embodiment 5
Adopt the preparation method identical with embodiment 1, alloying component is Ti48Al43Nb9 (atomic percent), optics floating region directional solidification processes is relative rotation speed 20rpm, heating power 70%, growth rate is 15mm/h, and vacuum heat treatment process is that 1350 DEG C × 12h+900 DEG C × 30min/ stove is cold, and B2 phase is completely eliminated, obtaining TiAl alloy material room temperature tensile yield strength is 593MPa, and plastic strain is 6.8%.
Embodiment 6
Adopt the preparation method identical with embodiment 1, alloying component is Ti48Al46Nb6 (atomic percent), optics floating region directional solidification processes is relative rotation speed 30rpm, heating power 60%, growth rate is 20mm/h, and vacuum heat treatment process is that 1250 DEG C × 12h+900 DEG C × 30min/ stove is cold, B2 phase is not completely eliminated, during XRD figure such as Fig. 3 b is composed, 12h heat treatment finds that a small amount of B2 phase remains, it is thus achieved that TiAl alloy material room temperature tensile yield strength is 656MPa, and plastic strain is 3.0%.
Claims (6)
1. a high-strength high-ductility TiAl alloy material, it is characterised in that with atomic percentage, its alloying component is: (44～51) Ti-(43～47) Al-(6～9) Nb, and described alloy is prepared by the following method:
(1) electromagnetic induction suspension smelting TiAl alloy foundry alloy button ingot, adopts gravitation casting method or suction casting method to obtain foundry alloy bar；
(2) foundry alloy bar is cut into upper and lower bar two parts, respectively as fuel rod and the seed crystal rod of optics floating region directional solidification furnace；Distance between upper and lower bar is 3～5mm；Pass into high-purity argon gas as atmosphere protection; the axially opposing rotating speed regulating upper and lower bar is 20～30rpm; start heating; the opposite side making upper and lower bar first melts, and adjusts the position of upper and lower bar so that it is opposite side engages after moving closer to; regulate power to the 55～70% of general power; when floating region smooth surface and when melting uniform, growth regulation speed is 2.5～20mm/h, starts directional solidification；
(3) the TiAl alloy monocrystalline bar of preparation is carried out vacuum heat；Adopt the Technology for Heating Processing that 1250 DEG C～1350 DEG C × 12h～24h+900 DEG C × 30min/ stove is cold.
2. high-strength high-ductility TiAl alloy material according to claim 1, it is characterised in that the electromagnetic induction suspension melting described in step (1) adopts water jacketed copper crucible, and described foundry alloy bar size is Φ (4～6) mm × 120mm.
3. high-strength high-ductility TiAl alloy material according to claim 1, it is characterised in that in step (2), the flow of high-purity argon gas is 3～5L/min.
4. the preparation method of a high-strength high-ductility TiAl alloy material as claimed in claim 1, it is characterised in that comprise the steps:
(1) electromagnetic induction suspension smelting TiAl alloy foundry alloy button ingot, adopts gravitation casting method or suction casting method to obtain foundry alloy bar；
(2) foundry alloy bar is cut into upper and lower bar two parts, respectively as fuel rod and the seed crystal rod of optics floating region directional solidification furnace；Distance between upper and lower bar is 3～5mm；Pass into high-purity argon gas as atmosphere protection; the axially opposing rotating speed regulating upper and lower bar is 20～30rpm; start heating; the opposite side making upper and lower bar first melts, and adjusts the position of upper and lower bar so that it is opposite side engages after moving closer to; regulate power to the 55～70% of general power; when floating region smooth surface and when melting uniform, growth regulation speed is 2.5～20mm/h, starts directional solidification；
(3) the TiAl alloy monocrystalline bar of preparation is carried out vacuum heat；Adopt the Technology for Heating Processing that 1250 DEG C～1350 DEG C × 12h～24h+900 DEG C × 30min/ stove is cold.
5. the preparation method of high-strength high-ductility TiAl alloy material as claimed in claim 4, it is characterized in that, electromagnetic induction suspension melting described in step (1) adopts water jacketed copper crucible, and described foundry alloy bar size is Φ (4～6) mm × 120mm.
6. the preparation method of high-strength high-ductility TiAl alloy material as claimed in claim 4, it is characterised in that in step (2), the flow of high-purity argon gas is 3～5L/min.
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| CN201410529844.5A CN104278173B (en) | 2014-10-09 | 2014-10-09 | A kind of high-strength high-ductility TiAl alloy material and preparation method thereof |
| JP2017538285A JP6944874B2 (en) | 2014-10-09 | 2015-10-09 | Single crystal material of TiAl intermetallic compound and its manufacturing method |
| US15/517,165 US10570531B2 (en) | 2014-10-09 | 2015-10-09 | TiAl intermetallic compound single crystal material and preparation method therefor |
| RU2017115945A RU2701438C2 (en) | 2014-10-09 | 2015-10-09 | Monocrystalline material of intermetallic compound of titanium and aluminium and methods for production thereof |
| EP15849516.8A EP3205753B1 (en) | 2014-10-09 | 2015-10-09 | Preparation method for a tial intermetallic compound single crystal material |
| PCT/CN2015/091508 WO2016055013A1 (en) | 2014-10-09 | 2015-10-09 | Tial intermetallic compound single crystal material and preparation method therefor |
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| CN104878452A (en) * | 2015-05-13 | 2015-09-02 | 南京理工大学 | High-temperature high-strength TiAl-Nb monocrystal and preparation method thereof |
| JP6944874B2 (en) * | 2014-10-09 | 2021-10-06 | 南京理工大学Ｎａｎｊｉｎｇ Ｕｎｉｖｅｒｓｉｔｙ Ｏｆ Ｓｃｉｅｎｃｅ Ａｎｄ Ｔｅｃｈｎｏｌｏｇｙ | Single crystal material of TiAl intermetallic compound and its manufacturing method |
| CN105088329B (en) * | 2015-02-02 | 2017-11-14 | 西北工业大学 | A kind of preparation method of the quasi- seed crystal of TiAl alloy |
| CN104878444A (en) * | 2015-05-13 | 2015-09-02 | 南京理工大学 | Preparation method of TiAl-base alloy monocrystal |
| CN106868338A (en) * | 2015-12-10 | 2017-06-20 | 南京理工大学 | Enhanced tungstenic high niobium containing titanium aluminium alloy of one kind orientation and preparation method thereof |
| CN106435268B (en) * | 2016-10-12 | 2017-12-01 | 攀枝花学院 | Alloy material of high niobium-titanium-aluminum and preparation method thereof |
| CN113122756B (en) * | 2021-04-20 | 2022-03-22 | 西北工业大学 | Titanium-aluminum alloy with multistage twin crystal staggered structure and preparation method thereof |
| CN114150242B (en) * | 2021-11-25 | 2023-07-18 | 南京理工大学 | Method for inhibiting coarsening of light high-strength TiAl alloy sheet |
| CN115386780B (en) * | 2022-09-13 | 2023-03-21 | 南京工业大学 | Lightweight high-strength high-toughness Gao Shangchao alloy and preparation method thereof |
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| JP3459980B2 (en) * | 2000-05-18 | 2003-10-27 | 東京工業大学長 | Lamellar orientation control method for TiAl-based single crystal alloy |
| US6436208B1 (en) * | 2001-04-19 | 2002-08-20 | The United States Of America As Represented By The Secretary Of The Navy | Process for preparing aligned in-situ two phase single crystal composites of titanium-niobium alloys |
| CN102011195B (en) * | 2010-11-23 | 2012-06-06 | 北京科技大学 | Preparation method of directional solidification high-Nb TiAl alloy single crystal |
| CN103074536A (en) * | 2013-01-31 | 2013-05-01 | 南京理工大学 | Carbon-silicon-tungsten-yttrium lamellar structure high-niobium titanium-aluminum alloy and preparation method thereof |
| CN103789598B (en) * | 2014-02-28 | 2015-12-02 | 南京理工大学 | A kind of directed TiAl-base alloy and preparation method thereof |
| CN103820697B (en) * | 2014-03-10 | 2016-08-17 | 北京工业大学 | A kind of multi-element alloyed β phase solidifies high Nb containing TiAl based alloy and preparation method thereof |
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Application publication date: 20150114 Assignee: Shenyang Foundry Research Institute Co., Ltd. of China National Machinery Research Institute Group Assignor: NANJING University OF SCIENCE AND TECHNOLOGY Contract record no.: X2024980000998 Denomination of invention: A high-strength and high plastic TiAl alloy material and its preparation method Granted publication date: 20160706 License type: Common License Record date: 20240119 Application publication date: 20150114 Assignee: Xi'an Supercrystalline Technology Co.,Ltd. Assignor: NANJING University OF SCIENCE AND TECHNOLOGY Contract record no.: X2024980000995 Denomination of invention: A high-strength and high plastic TiAl alloy material and its preparation method Granted publication date: 20160706 License type: Common License Record date: 20240119 Application publication date: 20150114 Assignee: Zhongke Hangxing Technology Co.,Ltd. Assignor: NANJING University OF SCIENCE AND TECHNOLOGY Contract record no.: X2024980000985 Denomination of invention: A high-strength and high plastic TiAl alloy material and its preparation method Granted publication date: 20160706 License type: Common License Record date: 20240119 Application publication date: 20150114 Assignee: Jiangsu Jianghangzhi Aircraft Engine Components Research Institute Co.,Ltd. Assignor: NANJING University OF SCIENCE AND TECHNOLOGY Contract record no.: X2024980000975 Denomination of invention: A high-strength and high plastic TiAl alloy material and its preparation method Granted publication date: 20160706 License type: Common License Record date: 20240119 |
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