CN104278173A - High-strength high-ductility TiAl alloy material and preparation method thereof - Google Patents
High-strength high-ductility TiAl alloy material and preparation method thereof Download PDFInfo
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- CN104278173A CN104278173A CN201410529844.5A CN201410529844A CN104278173A CN 104278173 A CN104278173 A CN 104278173A CN 201410529844 A CN201410529844 A CN 201410529844A CN 104278173 A CN104278173 A CN 104278173A
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- 239000000956 alloy Substances 0.000 title claims abstract description 95
- 229910010038 TiAl Inorganic materials 0.000 title claims abstract description 60
- 238000002360 preparation method Methods 0.000 title claims abstract description 26
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 65
- 238000000034 method Methods 0.000 claims abstract description 41
- 238000010438 heat treatment Methods 0.000 claims abstract description 28
- 238000007667 floating Methods 0.000 claims abstract description 22
- 239000013078 crystal Substances 0.000 claims abstract description 19
- 238000007711 solidification Methods 0.000 claims abstract description 14
- 230000008023 solidification Effects 0.000 claims abstract description 14
- 230000005674 electromagnetic induction Effects 0.000 claims abstract description 9
- 239000000725 suspension Substances 0.000 claims abstract description 9
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 claims abstract description 8
- 238000003723 Smelting Methods 0.000 claims abstract description 8
- 238000005266 casting Methods 0.000 claims abstract description 8
- 229910052802 copper Inorganic materials 0.000 claims abstract description 8
- 239000010949 copper Substances 0.000 claims abstract description 8
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 claims description 22
- 239000000470 constituent Substances 0.000 claims description 12
- 238000007669 thermal treatment Methods 0.000 claims description 12
- 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
- 238000002844 melting Methods 0.000 claims description 8
- 230000008018 melting Effects 0.000 claims description 8
- 230000001105 regulatory effect Effects 0.000 claims description 7
- 239000000446 fuel Substances 0.000 claims description 6
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims description 6
- 230000026267 regulation of growth Effects 0.000 claims description 4
- 238000005204 segregation Methods 0.000 abstract description 3
- 238000000137 annealing Methods 0.000 abstract description 2
- 241000446313 Lamella Species 0.000 abstract 1
- 230000007547 defect Effects 0.000 abstract 1
- 238000010309 melting process Methods 0.000 abstract 1
- 230000003287 optical effect Effects 0.000 abstract 1
- 239000012071 phase Substances 0.000 description 19
- 239000000203 mixture Substances 0.000 description 8
- 239000000463 material Substances 0.000 description 5
- 238000005516 engineering process Methods 0.000 description 4
- 229910000765 intermetallic Inorganic materials 0.000 description 3
- 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
- 238000001228 spectrum Methods 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
- 238000002441 X-ray diffraction Methods 0.000 description 1
- MCMNRKCIXSYSNV-UHFFFAOYSA-N Zirconium dioxide Chemical compound O=[Zr]=O MCMNRKCIXSYSNV-UHFFFAOYSA-N 0.000 description 1
- PNEYBMLMFCGWSK-UHFFFAOYSA-N aluminium oxide Inorganic materials [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 description 1
- 238000012512 characterization method Methods 0.000 description 1
- 239000012141 concentrate Substances 0.000 description 1
- 238000010276 construction Methods 0.000 description 1
- 230000007423 decrease Effects 0.000 description 1
- 230000007812 deficiency Effects 0.000 description 1
- 229910002804 graphite Inorganic materials 0.000 description 1
- 239000010439 graphite Substances 0.000 description 1
- 238000000227 grinding Methods 0.000 description 1
- 239000012535 impurity Substances 0.000 description 1
- 239000007791 liquid phase Substances 0.000 description 1
- 230000008520 organization Effects 0.000 description 1
- TWNQGVIAIRXVLR-UHFFFAOYSA-N oxo(oxoalumanyloxy)alumane Chemical compound O=[Al]O[Al]=O TWNQGVIAIRXVLR-UHFFFAOYSA-N 0.000 description 1
- 230000001737 promoting effect Effects 0.000 description 1
- 230000001681 protective effect Effects 0.000 description 1
- 239000002994 raw material Substances 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
- 229910000601 superalloy Inorganic materials 0.000 description 1
Abstract
The invention discloses a high-strength high-ductility TiAl alloy material and a preparation method thereof. The high-strength high-ductility TiAl alloy material comprises Ti, Al and Nb, wherein the atomic percent is (44-51)Ti-(43-47)Al-(6-9)Nb. The preparation method of the high-strength high-ductility TiAl alloy material comprises the following steps of carrying out electromagnetic induction suspension smelting on a TiAl alloy mother alloy ingot by adopting a water-cooled copper crucible, and carrying out suction casting to obtain a mother alloy rod; carrying out directional solidification on the mother alloy rod by adopting a four-mirror optical floating region directional solidification furnace, controlling the orientation of a TiAl alloy lamella, and acquiring a PST crystal; carrying out heat treatment and stress relief annealing on the PST crystal in an alpha single-phase region through a vacuum heat treatment furnace, and removing B2-phase segregation and residual stress to finally form the high-strength high-ductility TiAl alloy material. The high-strength high-ductility TiAl alloy material prepared through the method disclosed by the invention prevents the pollution of the water-cooled copper crucible on a TiAl alloy in a melting process, overcomes the defects of nonuniform component property and complicated processing of the traditional seed crystal method, is enhanced in strength and obtains outstanding room temperature tensile ductility.
Description
Technical field
The invention belongs to inter-metallic compound material technical field, specifically on the basis of appropriate design alloying constituent, adopt optics floating region directional solidification process and vacuum heat treatment, there is under preparing a kind of room temperature the TiAl alloy material of high strength and high-ductility.
Background technology
TiAl intermetallic compound has low density, high elastic coefficient and good hot strength, creep resistance and resistance of oxidation.Its use temperature can reach 750 ~ 900 DEG C, close with Ni based high-temperature alloy; But its density is only the half of superalloy, because of but the equivalent material of desirable Ni based high-temperature alloy, the high-temperature component of automobile or aircraft engine can be widely used in as blade, the turbine disk and vent valve etc.
But due to the intrinsic fragility of intermetallic compound, TiAl alloy brittleness at room temperature difference becomes the major cause hindering its industrial applications.So large quantity research concentrates on and controls TiAl alloy weave construction by directional freeze means.Due to the obvious anisotropy that intensity and plasticity in TiAl alloy PST crystal present, the method of directional freeze TiAl alloy is adopted to produce complete lamellar structure PST crystal, and make its lamellar structure orientation be parallel to the direction of growth of crystal in directional freeze, the mechanical property of TiAl alloy can be improved.
Tradition directional solidification process adopts crucible for smelting, and in TiAl alloy, Ti element is at high temperature very active, can react, as aluminum oxide, zirconium white and graphite etc. with most of crucible material.These reactants exist as impurity and change alloying constituent, cause the significantly decline of tissue change and performance.And floating zone method directional freeze to be the melting zone between crystal and fuel rod utilizing the liquid phase surface tension of molten state to maintain to grow stablize, whole process without the need to containers such as crucibles, thus avoids the pollution of container alloy.The people such as Johnson D.R with Yamaguchi solidify seed-grain method by α phase, select Ti-Al-Si system alloy as seed crystal, obtain by necking down crystal separation method the monocrystalline PST that lamellar orientation is parallel to the direction of growth completely.Seed crystal composition usually and mother alloy composition there are differences cause the composition of directional solidificating alloy and performance uneven, and the complicated process of preparation of seed crystal.Therefore, seed-grain method has obvious deficiency.
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, and improving use temperature about 60 ~ 100, DEG C is the TiAl alloy having future in engineering applications most.But because Nb element is the very capable element of stable β phase, be easy under growth velocity slower in directional freeze process form a large amount of β segregations, be cooled to room temperature and form B2 phase; B2 phase is at room temperature brittlement phase, has a strong impact on the room-temperature property of TiAl alloy.
Therefore, the composition performance that must the pollution of crucible alloy and seed-grain method avoided in directional freeze process to cause uneven, and eliminate brittlement phase by thermal treatment, to obtain the TiAl alloy with excellent properties.
Summary of the invention
The object of the present invention is to provide and a kind of there is TiAl alloy material of excellent room temperature strength and stretching plastic and preparation method thereof.By adopting non-seed-grain method optics floating region directional freeze, and completely eliminating fragility B2 phase by thermal treatment, successfully obtaining and there is desirable lamellar orientation, the free of contamination TiAl alloy monocrystalline of homogeneous microstructure,
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 constituent 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 mother alloy button ingot, adopts gravitation casting method or suction casting method to obtain mother alloy bar;
(2) mother alloy bar is cut into upper and lower bar two portions, 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 axial relative rotation speed of upper and lower bar is regulated to be 20 ~ 30rpm, start heating, the opposite side of upper and lower bar is first melted, adjusts the position of upper and lower bar, make its opposite side move closer to rear joint, regulating power is to 55 ~ 70% of total power, when floating region smooth surface and when melting even, growth regulation speed is 2.5 ~ 20mm/h, start directional freeze;
(3) the TiAl alloy monocrystalline bar of preparation is carried out vacuum heat treatment; Adopt the thermal treatment process 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 mother 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 in 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) adopt non-seed crystal floating zone method directional solidification technique, while preventing alloy contamination, avoid the shortcoming of processed complex in seed-grain method, composition uneven microstructure.
(3) a large amount of fragility B2 phases remained in tissue after using vacuum heat treatment to completely eliminate TiAl alloy directional freeze, thus obtain the alloy material of homogeneous microstructure, room-temperature property excellence.
(4) the method preparation technology is simple, and cost is low, improves brittleness at room temperature Be very effective, 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 freeze monocrystalline (a) and lamellar orientation (b) microstructure.
Fig. 3 is the microstructure (a is before thermal treatment, and b is after thermal treatment) of segregation before and after TiAl alloy monocrystalline different heat treatment technique.
Fig. 4 is the XRD diffractogram of TiAl alloy monocrystalline before and after different heat treatment technique.
Fig. 5 is TiAl alloy room temperature tensile mechanical curves.
Embodiment
A kind of high-strength high-ductility TiAl alloy material of the present invention and preparation method thereof, below in conjunction with accompanying drawing, 1 couple of the present invention is described in further detail, and its embodiment is as follows:
(1) composition graphs 1, a kind of high-strength high-ductility TiAl alloy material of the present invention, its alloying constituent atomic percent is: (44 ~ 51) Ti-(43 ~ 47) Al-(6 ~ 9) Nb.By the proportion relation between adjustment atomic component, its first precipitated phase is made to be all β phase.
(2) choose water jacketed copper crucible electromagnetic induction suspension smelting TiAl alloy mother alloy button ingot, adopt suction casting method to obtain mother alloy bar.
(3) mother alloy bar is cut into fuel rod and seed crystal rod two portions, carries out directional freeze by floating zone method; Pass into high-purity argon gas as atmosphere protection, regulate upper-lower section relative rotation speed, heating power and growth velocity control TiAl alloy lamellar orientation and obtain single crystal growing.
(4) the TiAl alloy monocrystalline bar of preparation is carried out vacuum heat treatment; Adopt and be incubated after annealing after α single phase region heating certain hour; Eliminate fragility B2 phase and unrelieved stress completely, obtain high-strength high-ductility TiAl alloy material.
(5) utilize OM, XRD TiAl alloy to preparation to carry out Microstructure characterization, and further mechanical property sign is carried out to it, to determine that there is the TiAl alloy material microtexture of 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-materially to select:
It is Ti47Al45Nb8 (atomic percent) that the present invention prepares the alloying constituent that master alloy ingot selects, and purity Ti, the Al of each metal constituent element are 99.999%, 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 surperficial mechanical grinding of raw metal being 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, be evacuated to 5 × 10
-3pa; In stove, be filled with the high-purity argon gas (99.999%) of a certain amount of pressure, argon pressure scope is 0.8 ~ 1MPa.Multi-pass melting obtains the master alloy ingot mixed for 3 ~ 4 times.Subsequently master alloy ingot is inhaled and cast Φ 6 × 120mm bar.
(3) optics floating region directional freeze:
Mother alloy bar is cut into upper and lower bar two portions, 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 axial relative rotation speed 30rpm of upper and lower bar, start heating, the opposite side of upper and lower bar is first melted, adjusts the position of upper and lower bar, make its opposite side move closer to rear joint, regulating power is to 68% of total power, when smooth surface fusing in floating region is even (floating region is without when obviously shaking), growth regulation speed is 5mm/h, starts directional freeze; Directional freeze process is stopped when growing to 80mm.
(4) vacuum heat treatment
Directional freeze bar mono crystalline portion is put into alundum tube, is evacuated to tube sealing after 10-3Pa, puts into heat treatment furnace, adopt the thermal treatment process that 1300 DEG C × 24h+900 DEG C × 30min/ stove is cold.
(5) stuctures and properties characterizes
Fig. 2 a is the coupon photomacrograph after the directional freeze of optics floating region, and visible sample experiences after of short duration competition is eliminated in directional freeze becomes single crystal growing rapidly, and Fig. 2 b shows that monocrystalline lamellar orientation is parallel to the direction of growth.Fig. 3 (a) and Fig. 3 (b) are micro-organization charts before and after thermal treatment, and before the XRD figure spectrum of composition graphs 4 can find out thermal treatment, organization internal is dispersed with a large amount of B2 phases, and after 24h thermal treatment, B2 eliminates completely.Fig. 5 is the room temperature tensile stress-strain curve of prepared high-strength high-ductility TiAl alloy, and its yield strength is 729MPa, and plastix strain simultaneously reaches 6.9%, has very excellent room-temperature mechanical property.
Embodiment 2
Adopt the preparation method identical with embodiment 1, alloying constituent is Ti44Al47Nb9 (atomic percent), optics floating region directional solidification processes is relative rotation speed 20rpm, heating power 55%, growth velocity is 2.5mm/h, and vacuum heat treatment process is 1250 DEG C × and 12h+900 DEG C × 30min/ stove is cold, and B2 phase is eliminated completely, obtaining TiAl alloy material room temperature tensile yield strength is 550MPa, and plastix strain is 6.0%.
Embodiment 3
Adopt the preparation method identical with embodiment 1, alloying constituent is Ti51Al40Nb9 (atomic percent), optics floating region directional solidification processes is relative rotation speed 25rpm, heating power 70%, growth velocity is 10mm/h, and vacuum heat treatment process is 1300 DEG C × and 20h+900 DEG C × 30min/ stove is cold, and B2 phase is eliminated completely, obtaining TiAl alloy material room temperature tensile yield strength is 628MPa, and plastix strain is 6.5%.
Embodiment 4
Adopt the preparation method identical with embodiment 1, alloying constituent is Ti48Al43Nb9 (atomic percent), optics floating region directional solidification processes is relative rotation speed 20rpm, heating power 68%, growth velocity is 15mm/h, and vacuum heat treatment process is 1350 DEG C × and 24h+900 DEG C × 30min/ stove is cold, and B2 phase is eliminated completely, obtaining TiAl alloy material room temperature tensile yield strength is 660MPa, and plastix strain is 6.2%.
Embodiment 5
Adopt the preparation method identical with embodiment 1, alloying constituent is Ti48Al43Nb9 (atomic percent), optics floating region directional solidification processes is relative rotation speed 20rpm, heating power 70%, growth velocity is 15mm/h, and vacuum heat treatment process is 1350 DEG C × and 12h+900 DEG C × 30min/ stove is cold, and B2 phase is eliminated completely, obtaining TiAl alloy material room temperature tensile yield strength is 593MPa, and plastix strain is 6.8%.
Embodiment 6
Adopt the preparation method identical with embodiment 1, alloying constituent is Ti48Al46Nb6 (atomic percent), optics floating region directional solidification processes is relative rotation speed 30rpm, heating power 60%, growth velocity is 20mm/h, and vacuum heat treatment process is 1250 DEG C × and 12h+900 DEG C × 30min/ stove is cold, B2 phase is not eliminated completely, as in the XRD figure spectrum of Fig. 3 b, 12h thermal treatment finds that a small amount of B2 phase remains, obtaining TiAl alloy material room temperature tensile yield strength is 656MPa, and plastix strain is 3.0%.
Claims (7)
1. a high-strength high-ductility TiAl alloy material, is characterized in that, with atomic percentage, its alloying constituent is: (44 ~ 51) Ti-(43 ~ 47) Al-(6 ~ 9) Nb.
2. high-strength high-ductility TiAl alloy material according to claim 1, it is characterized in that, described alloy is prepared by the following method:
(1) electromagnetic induction suspension smelting TiAl alloy mother alloy button ingot, adopts gravitation casting method or suction casting method to obtain mother alloy bar;
(2) mother alloy bar is cut into upper and lower bar two portions, 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 axial relative rotation speed of upper and lower bar is regulated to be 20 ~ 30rpm, start heating, the opposite side of upper and lower bar is first melted, adjusts the position of upper and lower bar, make its opposite side move closer to rear joint, regulating power is to 55 ~ 70% of total power, when floating region smooth surface and when melting even, growth regulation speed is 2.5 ~ 20mm/h, start directional freeze;
(3) the TiAl alloy monocrystalline bar of preparation is carried out vacuum heat treatment; Adopt the thermal treatment process that 1250 DEG C ~ 1350 DEG C × 12h ~ 24h+900 DEG C × 30min/ stove is cold.
3. high-strength high-ductility TiAl alloy material according to claim 2, is characterized in that, the electromagnetic induction suspension melting described in step (1) adopts water jacketed copper crucible, and described mother alloy bar size is Φ (4 ~ 6) mm × 120mm.
4. high-strength high-ductility TiAl alloy material according to claim 2, is characterized in that, in step (2), the flow of high-purity argon gas is 3 ~ 5L/min.
5. a preparation method for high-strength high-ductility TiAl alloy material as claimed in claim 1, is characterized in that, comprise the steps:
(1) electromagnetic induction suspension smelting TiAl alloy mother alloy button ingot, adopts gravitation casting method or suction casting method to obtain mother alloy bar;
(2) mother alloy bar is cut into upper and lower bar two portions, 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 axial relative rotation speed of upper and lower bar is regulated to be 20 ~ 30rpm, start heating, the opposite side of upper and lower bar is first melted, adjusts the position of upper and lower bar, make its opposite side move closer to rear joint, regulating power is to 55 ~ 70% of total power, when floating region smooth surface and when melting even, growth regulation speed is 2.5 ~ 20mm/h, start directional freeze;
(3) the TiAl alloy monocrystalline bar of preparation is carried out vacuum heat treatment; Adopt the thermal treatment process that 1250 DEG C ~ 1350 DEG C × 12h ~ 24h+900 DEG C × 30min/ stove is cold.
6. the preparation method of high-strength high-ductility TiAl alloy material as claimed in claim 5, it is characterized in that, electromagnetic induction suspension melting described in step (1) adopts water jacketed copper crucible, and described mother alloy bar size is Φ (4 ~ 6) mm × 120mm.
7. the preparation method of high-strength high-ductility TiAl alloy material as claimed in claim 5, is characterized in that, in step (2), the flow of high-purity argon gas is 3 ~ 5L/min.
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| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201410529844.5A CN104278173B (en) | 2014-10-09 | 2014-10-09 | A kind of high-strength high-ductility TiAl alloy material and preparation method thereof |
| EP15849516.8A EP3205753B1 (en) | 2014-10-09 | 2015-10-09 | Preparation method for a tial intermetallic compound single crystal material |
| 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 |
| JP2017538285A JP6944874B2 (en) | 2014-10-09 | 2015-10-09 | Single crystal material of TiAl intermetallic compound and its manufacturing method |
| 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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| CN201410529844.5A CN104278173B (en) | 2014-10-09 | 2014-10-09 | A kind of high-strength high-ductility TiAl alloy material and preparation method thereof |
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| CN104278173B CN104278173B (en) | 2016-07-06 |
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Cited By (9)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| 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 |
| CN104878444A (en) * | 2015-05-13 | 2015-09-02 | 南京理工大学 | Preparation method of TiAl-base alloy monocrystal |
| CN105088329A (en) * | 2015-02-02 | 2015-11-25 | 西北工业大学 | Preparation method of TiAl alloy quasi seed crystals |
| WO2016055013A1 (en) * | 2014-10-09 | 2016-04-14 | 南京理工大学 | Tial intermetallic compound single crystal material and preparation method therefor |
| CN106435268A (en) * | 2016-10-12 | 2017-02-22 | 攀枝花学院 | High-Nb Ti-Al alloy and preparation method thereof |
| 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 |
| CN113122756A (en) * | 2021-04-20 | 2021-07-16 | 西北工业大学 | Titanium-aluminum alloy with multistage twin crystal staggered structure and preparation method thereof |
| CN114150242A (en) * | 2021-11-25 | 2022-03-08 | 南京理工大学 | Method for inhibiting coarsening of light high-strength TiAl alloy lamella |
| CN115386780A (en) * | 2022-09-13 | 2022-11-25 | 南京工业大学 | Light high-strength high-toughness Gao Shangchao alloy and preparation method thereof |
Citations (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2001328899A (en) * | 2000-05-18 | 2001-11-27 | Tokyo Inst Of Technol | METHOD FOR CONTROLLING LAMELLA ORIENTATION OF TiAl 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 |
| CN102011195A (en) * | 2010-11-23 | 2011-04-13 | 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 |
| CN103789598A (en) * | 2014-02-28 | 2014-05-14 | 南京理工大学 | Directional TiAl-based alloy and preparation method thereof |
| CN103820697A (en) * | 2014-03-10 | 2014-05-28 | 北京工业大学 | Multi-alloying beta-phase-solidified high Nb-TiAl alloy and preparation method thereof |
-
2014
- 2014-10-09 CN CN201410529844.5A patent/CN104278173B/en active Active
Patent Citations (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2001328899A (en) * | 2000-05-18 | 2001-11-27 | Tokyo Inst Of Technol | METHOD FOR CONTROLLING LAMELLA ORIENTATION OF TiAl 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 |
| CN102011195A (en) * | 2010-11-23 | 2011-04-13 | 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 |
| CN103789598A (en) * | 2014-02-28 | 2014-05-14 | 南京理工大学 | Directional TiAl-based alloy and preparation method thereof |
| CN103820697A (en) * | 2014-03-10 | 2014-05-28 | 北京工业大学 | Multi-alloying beta-phase-solidified high Nb-TiAl alloy and preparation method thereof |
Non-Patent Citations (4)
| Title |
|---|
| Y. UMAKOSHI ETAL.: ""Contribution of a single set of lamellae to the plastic behavior of TiAl crystals grown by a floating zone method"", 《SCRIPTA METALLURGICA ET MATERIALIA》 * |
| Y.J. BI ETAL.: ""Directional solidification of TiAl alloys by vertical float zoning"", 《SCRIPTA METALLURGICA ET MATERIALIA》 * |
| 刘荣华等: ""光学浮区定向生长Ti-43Al-3Si合金"", 《金属学报》 * |
| 胡轶嵩等: ""光学浮区法制备定向生长Ti-44.5Al-3Nb-0.8Si-0.2C合金"", 《材料热处理学报》 * |
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