CN103555999A - High-strength cast Ti-Si-Al-B-Zr base alloy - Google Patents
High-strength cast Ti-Si-Al-B-Zr base alloy Download PDFInfo
- Publication number
- CN103555999A CN103555999A CN201310546083.XA CN201310546083A CN103555999A CN 103555999 A CN103555999 A CN 103555999A CN 201310546083 A CN201310546083 A CN 201310546083A CN 103555999 A CN103555999 A CN 103555999A
- Authority
- CN
- China
- Prior art keywords
- alloy
- strength
- titanium
- base
- base alloy
- 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.)
- Pending
Links
Images
Abstract
The invention provides high-strength cast Ti-Si-Al-B-Zr base alloy containing intermetallic compound reinforcing phases. The high-strength cast Ti-Si-Al-B-Zr base alloy comprises the following components in parts by weight: 2.5-7.2% of Si, 3-8.5% of Al, 0.01-1.5% of B, 0.01-3% of Zr and the balance of Ti. The intermetallic compound reinforcing phases comprise titanium silicide and titanium boride, at least one of the intermetallic compound reinforcing phases is Ti5Si or Ti3Si, and the titanium silicide and titanium boride reinforcing phases are contained in an alpha-titanium alloy matrix through liquid reaction or solid reaction. The high-strength cast Ti-Si-Al-B-Zr base alloy has excellent strength and heat stability, and high wear resistance, fracture resistance and oxidation resistance through the mutual combination of various elements such as Ti, Si, Al, B and Zr and combines the characteristics of ceramic materials. The room-temperature tensile strength of the alloy is 700MPa-1200MPa, the compression strength of the alloy is 1500MPa-1980MPa, and the compression elongation percentage of the alloy can reach more than 13%. The alloy is suitable for high-temperature high-load supporting, such as pistons and air cylinder parts of high compression generators and various pumps, valves and impellers having requirements on wear resistance and corrosion resistance, parts of aircraft engines and gas compressors as well as screw propellers, water spraying propellers and the like in a ship and warship power propelling system.
Description
Technical field
The present invention relates to a kind of casting Ti-Si base alloy, more specifically relate to a kind of Ti of containing, Si, Al, B and Zr element, the high-strength casting Ti-Si alloy that the titanium silicide being formed by liquid reaction or titanium boride strengthen.
Background technology
Cast titanium alloy refers to for being cast into the titanium alloy of definite shape foundry goods.At present to be widely used in the fields such as aerospace, naval vessel, chemical industry, automobile, physical culture and medicine equipment.In the cast titanium alloy early stage of development, be mainly to select some wrought titanium alloys to pour into a mould experiment in the world, result shows, most of wrought titanium alloy has comparatively satisfied Production Practice of Casting Technologies.Along with cast titanium alloy range of application constantly expands, the shape of foundry goods becomes increasingly complex, wall thickness is more and more thinner, and traditional cast titanium alloy also more and more exposes the weakness in its castability, as high in fusing point, chemical property is active, freezing range is wide and when casting superheating temperature shortcoming such as low.
The people such as Flower have studied martensite Ti-Si binary alloy and have precipitated (Metallurgical Transactions, 1971, Vol.2, No.12, P3289-3297) containing the silicide in the more complex alloys of zirconium and aluminium.In the titanium composite material containing zirconium and aluminium, the maximum silicone content of research is 1.0%.Recently, Guangxi University's Zhan forever clock etc. has been developed a kind of at room temperature have high strength and oxidation resistant titanium silicon at high temperature, and its feed composition and content are by weight percentage: Ti78.87-88.3, Si7.33-8.2, Al and/or Nb2.8-12.3%.The compressive strength at room temperature of this alloy can reach 1498-1828MPa, and under 800-1000 ℃ of high temperature, the oxidation weight gain of alloy is few, and the oxide film densification that alloy surface forms can play a very good protection by alloy.But the density of Nb is 8.66g/m
3, a large amount of Nb add, and have improved on the one hand the density of alloy, increase the difficulty of alloy melting, on the other hand, have also improved the cost of alloy.
Xu Yanfei etc. have studied Ce and the impact of Zr element on the microtexture of Ti-11%at alloy of adding different content, and the impact that adds 16at%Al alloy microstructure mechanical property and high temperature friction and wear performance in Ti-Si eutectic alloy.History small echo etc. research Al is the impact lower than 7.7% Ti-Si eutectic alloy high-temperature oxidation resistance on Si content, they have also studied containing 0-25wt%Nb high-temperature oxidation resistance, result shows, changed Ti-Si eutectic alloy high-temperature oxidation resistance appropriate adding of alloy element, improved the resistance to high temperature oxidation temperature of alloy, extend the Alloy Anti high temperature oxidation time, improved generally the high-temperature oxidation resistance of alloy.The experimental tests such as Wu He room temperature and the high temperature tensile properties of hypoeutectic Ti-7%Si alloy and eutectic Ti-8.5%Si alloy.Discovery is along with the increase of Si content, hard crisp phase Ti
5si
3volume fraction increases, and alloy plasticity declines.Dissimilar Ti-Si is associated gold, and fracture mechanism is not quite similar.Hypoeutectic alloy be fractured into quasi-cleavage crack; The fracture of hypereutectic alloy is cleavage brittleness fracture; The fracture mode of eutectic alloy, between between the two, is the fracture of class cleavage brittleness.Hypoeutectic T-7%Si alloy and eutectic alloy, at 500 ℃ of high temperature, have certain intensity and plasticity, have engineering using value.
In sum, existing Ti-Si alloy is paid attention to the research and development of Ti-Si eutectic composition mostly.But due to hard crisp phase Ti
5si
3volume fraction is more, so the fragility of alloy is large, is difficult to meet the demand of engineering materials.And after Si content reduces, the intensity of alloy will reduce, and needs on wear-resisting parts in being applied to engine, existing too low Si content also can cause the wear resistance of alloy not enough.Therefore how by composition modulate develop have simultaneously high strength and well the Ti-Si alloy of plasticity be a very important problem in science.
Summary of the invention
An object of the present invention is to provide a kind of Ti-Si-Al base alloy that contains titanium based solid solution and titanium silicide and titanium boride intermetallic compound wild phase, this alloy has sufficiently high obdurability.By adding lower Si and the Al element of density ratio Ti, obtain low density Ti-Si-Al base alloy, thereby make alloy obtain high specific strength.
A Ti-Si-Al-B-Zr base alloy, is characterized in that containing intermetallic compound wild phase in Ti-Si-Al-B-Zr base alloy, comprises titanium silicide and titanium boride, and in these wild phases, at least one is Ti
5si
3or Ti
3si, these wild phases by liquid reaction or solid state reaction in alpha titanium alloy matrix; Ti-Si-Al-B-Zr base weight alloy per-cent is Si3.5-7.2%, Al3-8.5%, B0.01-1.5%, Zr0.01-3%, Ti surplus.
Above-mentioned Ti-Si-Al-B-Zr base alloy preferred weight percent is: Si4.5-7.2%, Al3.5-7.5%, B0.01-0.2%, Zr0.5-2.5%, Ti surplus.
Al is the α phase stable element extensively adopting in Ti alloy, adds Al in Ti, can reduce fusing point, by β phase transition temperature, plays solution strengthening effect, thereby has improved yield strength.In the higher alloy of silicone content, add Al, in the time of can passing through in matrix, validity response produces tiny and stable diffusing particle.Research shows, Ti
5si
3middle Si can be substituted by Al.Ti
5si
3the existence of Al in type silicide, has increased the lattice parameter of silicide.The interpolation of Al makes eutectic silicide roughen, the separating out of other silicides that slowed down.Therefore first the present invention considers to put forward heavy alloyed intensity by adding Al.But, at Ti-Si alloy, add Al, need to keep reasonable content, the too high or too low raising that is all unfavorable for alloy mechanical property.
In order further to put forward heavy alloyed intensity, the present invention selects to add Zr element.Zr has identical lattice types with α-Ti, infinitely dissolves each other with α-Ti, so Zr element can dissolve in α-Ti in a large number with substitute mode, produces lattice distortion, and Zr is to β-Ti
change the unconspicuous element of impact, this element, when improving α-Ti intensity, is also put forward heavy alloyed heat resistance, and they reduce under the prerequisite of plasticity in little amplitude, also help press working and welding.Hypoeutectic titanium silicon is carried out to Zr element doping, make Zr element play the effect of " reinforcer ", by solution strengthening effect, in titanium alloy substrate, also there is no so far the report of Zr element on the impact of hypoeutectic titanium silicon.
In order to guarantee that alloy has higher intensity, Si content need to reach certain numerical value, that is to say that alloy must form a certain amount of intermetallic compound, the Plasticity Decreasing that causes alloy, therefore need to be by adding fining agent to come refinement silication phase and α-Ti dendrite, research discovery, indium addition B can improve compressive strength and the plasticity of Ti-Si alloy greatly.In Ti-Si eutectic alloy, when adding 0.21at%B, the compressive strength of alloy and plasticity ratio Ti-Si two component eutectic improve 26% and 480%.Research also finds, B can also remarkably influenced hypoeutectic Ti-5wt%Si alloy process of cooling in the growth of primary dendrite, thereby change the dendrite morphology in microtexture.For hypoeutectic titanium silicon, adding of micro-B will have a huge impact, before this without any the report affecting in hypoeutectic titanium silicon for B.Because the density of B element is low, the trace of B element (wt%) doping all can embody considerable influence on atomic ratio (at%).Therefore another object of the present invention is by adding appropriate B element, refinement α-Ti dendrite, Ti
5si
3or Ti
3si intermetallic compound, obtains excellent comprehensive mechanical property.
Due to adding of Si, in alloy, formed high rigidity silication phase, these silication phases are distributed in high tenacity Ti matrix, thereby have played the effect that improves Wear Resistance.Therefore further aim of the present invention is by reasonable interpolation Si, at titanium base Solid solution, forms titanium silicide and titanium boride intermetallic compound wild phase, makes Ti-Si-Al base alloy have good wear resistance.Meanwhile, the Ti forming in Ti-Si-Al base alloy
5si
3or Ti
3si intermetallic compound, makes alloy have low-expansion coefficient, low heat conductivity and good volume stability.
In sum, the present invention has designed a kind of new high-strength casting titanium silicon-base alloy.In this alloy, by cooperatively interacting of Ti, Si, Al, B and the various elements of Zr, make this Ti-Si-Al base alloy not only there is good intensity, wear resistance and thermostability, also there is high wear resistance, resistance to fracture and oxidation-resistance, in addition, this alloy combines the characteristic of stupalith, as low density and low heat conductivity.These properties make this casting Ti-Si-Al base alloy be highly suitable for high temperature high loading supporting purposes, for example, for piston, the cylinder part of high compression generator, the pump of various requirement wear resistant corrosion resistant, valve and impeller, aero-engine compressor position, the water screw in ship power propulsion system and water-jet propulsor etc.
Accompanying drawing explanation
Fig. 1 is according to the Ti-6.3Si-3.6Al-0.01B-0.02Zr alloy scanning electron microscope (SEM) photograph of method 1 preparation.
Fig. 2 is according to the Ti-6.3Si-3.6Al-0.01B-0.02Zr alloy XRD figure of method 1 preparation.
Fig. 3 is according to the room temperature tensile curve of the Ti-6.3Si-3.6Al-0.01B-0.02Zr alloy of method 1 preparation.
Fig. 4 is according to the stretching fracture scanning electron microscope pattern of the Ti-6.3Si-3.6Al-0.01B-0.02Zr alloy of method 1 preparation.
Fig. 5 is according to the room temperature compression curve of the Ti-6.3Si-3.6Al-0.01B-0.02Zr alloy of method 1 preparation.
Fig. 6 stretches fracture scanning electron microscope pattern according to the room temperature of the Ti-6.3Si-3.6Al-0.01B-0.02Zr alloy of method 1 preparation.
Fig. 7 is according to the Ti-6.3Si-4.9Al-0.01B-0.02Zr alloy scanning electron microscope (SEM) photograph of method 1 preparation.
Fig. 8 is according to the Ti-6.3Si-4.9Al-0.01B-0.02Zr alloy XRD figure of method 1 preparation.
Fig. 9 is according to the room temperature tensile curve of the Ti-6.3Si-4.9Al-0.01B-0.02Zr alloy of method 1 preparation.
Figure 10 is according to the room temperature compression curve of the Ti-6.3Si-4.9Al-0.01B-0.02Zr alloy of method 1 preparation.
Figure 11 is according to the room temperature tensile curve of the Ti-6.4Si-6.2Al-0.01B-0.02Zr alloy of method 1 preparation.
Figure 12 is according to the room temperature compression curve of the Ti-6.4Si-6.2Al-0.01B-0.02Zr alloy of method 1 preparation.
Figure 13 is according to the room temperature tensile curve of the Ti-6.4Si-7.5Al-0.01B-0.02Zr alloy of method 1 preparation.
Figure 14 is according to the room temperature tensile curve of the Ti-6.3Si-3.6Al-0.04B-0.02Zr alloy of method 2 preparations.
Figure 15 is according to the room temperature compression curve of the Ti-6.3Si-3.6Al-0.04B-0.02Zr alloy of method 2 preparations.
Figure 16 is according to the room temperature tensile curve of the Ti-6.3Si-3.6Al-0.01B-2Zr alloy of method 2 preparations.
Figure 17 is according to the room temperature compression curve of the Ti-6.3Si-3.6Al-0.01B-2Zr alloy of method 2 preparations.
Embodiment
Implementation process
According to above-mentioned mentality of designing, the present invention selects multiple Ti-Si-Al-RE-BTi-Si composition, has prepared alloy sample, and has carried out performance test.Implementation method of the present invention is as follows:
Castmethod 1: prepare the raw metal that mother alloy adopts and be the pure metal simple substance element that purity is greater than 99.9%, according to the chemical constitution batching of alloy, use non-consumable water jacketed copper crucible electric arc furnace under argon atmospher joined raw material, with the melting of non-consumable tungsten electrode, adopt water cooled copper mould negative pressure to inhale casting, making diameter is the alloy bar ingot casting of 10mm.With ingot casting, prepare metallographic, physics and chemistry research, and mechanical test sample used.
Castmethod 2, prepares each element by weight percentage, then melting in suspension smelting furnace, and crucible is water jacketed copper crucible, and melting vacuum tightness is 0.01-1Pa, and the frequency of shower furnace is 8000Hz, and melting electric current is 100-500A, voltage is 100-380V.After band alloy melting, pour into diameter 45mm, in the steel die of long 300mm.
Select Ti-6.3Si-3.6Al-0.01B-0.02Zr (being called for short TS11), according to castmethod 1, prepared alloy sample, carried out analytical test.Fig. 1 is according to the TS11 alloy stereoscan photograph of method 1 preparation.Visible, tissue is by black matrix and white herring-bone form phase composite.Herring-bone form has again particulate state and corynebacterium, particle size to be less than 5 μ m mutually, and corynebacterium is slightly less than 3 μ m mutually, and length is less than 10 μ m.Fig. 2 is the XRD curve of TS11.Illustrate that tissue is by α-Ti and Ti
5si
3form mutually.According to the Solidification Characteristics of this alloy, can think, in Fig. 1, black matrix is α-Ti phase, white herring-bone form is Ti mutually
5si
3phase.Ti
5si
3to form from liquid phase by eutectic reaction mutually, during due to eutectic reaction after Ti dendrite is separated out, so eutectic structure is distributed in α-Ti phase interdendritic.Ti
5si
3compare α-Ti and there is mutually higher hardness, so Ti
5si
3in this alloy, play the effect of wild phase.
Fig. 3 is according to the room temperature tensile curve of the TS11 alloy of method 1 preparation.Fig. 4 is the stretching fracture scanning electron microscope pattern of this alloy.Visible, the tensile strength of material can be up to 1165MPa, the TC4 of current industrial widespread use, and the Ti alloy of the compositions such as ZTA15 is all difficult to reach mechanical properties more than 1100MPa.As can be seen from Figure 4, material monolithic presents fragility, but has had a small amount of dimple, there is no the appearance of big area cleavage surface, illustrates that alloy has certain plasticity.
Fig. 5 is according to the room temperature compression curve of the TS11 alloy of method 1 preparation, and as can be seen from Figure 5, the ultimate compression strength of material is up to 1828MPa, and plastix strain is about 7.35%.Its performance is better than the Ti alloy of the compositions such as the TC4 of current industrial widespread use and ZTA15.Fig. 6 is the compression fracture scanning electron microscope pattern of TS11 alloy.As seen from the figure, fracture presents the mode that toughness and fragility mixes and ruptures.On fracture there is cleavage fracture face in some on the one hand, and fracture step appears in another part, in whole fracture, can also observe train of thought shape style and a small amount of dimple, illustrates that alloy also presents certain toughness.
In preferred embodiment of the present invention, wherein a kind of is to have the Ti-Si-Al-B base alloy that eutectic forms titanium alloy wild phase, the chemical composition of tested alloys is Ti-6.3Si-4.9Al-0.01B-0.02Zr (being called for short TS12), raw material is added in 3Kg vacuum melting furnace according to this proportioning, according to method 1 molten alloy and be cast into ingot casting.
Fig. 7 is according to the TS12 alloy stereoscan photograph of method 1 preparation.Visible, tissue is by black matrix and white herring-bone form phase composite.Herring-bone form has again particulate state and corynebacterium, particle size to be less than 5 μ m mutually, and corynebacterium is slightly less than 3 μ m mutually, and length is less than 10 μ m.But compare with TS11, white herring-bone form is more thicker mutually.Fig. 8 is the XRD curve of TS12.Illustrate that tissue is by α-Ti and Ti
5si
3form mutually.In conjunction with Fig. 7 and Fig. 8, in explanatory view 7, black matrix is α-Ti phase, and white herring-bone form is Ti mutually
5si
3phase.
Fig. 9 is according to the room temperature tensile curve of the TS12 alloy of method 1 preparation, and as seen from the figure, the tensile strength of this alloy reaches 980MPa, has a small amount of viscous deformation.The room temperature compression curve of the TS12 alloy that Figure 10 is prepared according to method 1, can find out, the ultimate compression strength of material is up to 1774MPa, and plastix strain is about 10.2%.Comprehensive its stretches and compression performance is seen, this mechanical property is better than the Ti alloy of the compositions such as the TC4 of current industrial widespread use and ZTA15.
In preferred embodiment of the present invention, wherein a kind of is to have the Ti-Si-Al-B base alloy that eutectic forms titanium alloy wild phase, the chemical composition of tested alloys is Ti-6.4Si-6.2Al-0.01B-0.02Zr (being called for short TS13), raw material is joined in vacuum melting furnace according to this proportioning, according to method 1 molten alloy and be cast into ingot casting.Figure 11 is according to the room temperature tensile curve of the TS12 alloy of method 1 preparation, and as seen from the figure, the tensile strength of this alloy reaches 980MPa, has a small amount of viscous deformation.The room temperature compression curve of the TS12 alloy that Figure 12 is prepared according to method 1, can find out, the ultimate compression strength of material is up to 1784MPa, and plastix strain is about 10.2%.
In preferred embodiment of the present invention, wherein a kind of is to have the Ti-Si-Al-B base alloy that eutectic forms titanium alloy wild phase, the chemical composition of tested alloys is Ti-6.4Si-7.5Al-0.01B-0.02Zr (being called for short TS14), raw material is joined in vacuum melting furnace according to this proportioning, according to method 1 molten alloy and be cast into ingot casting.The room temperature compression curve of the TS12 alloy that Figure 13 is prepared according to method 1, can find out, the ultimate compression strength of material is up to 1718MPa, and plastix strain is about 5.9%.Visible, too high Al content, has caused the compression plasticity of alloy to decline.
In preferred embodiment of the present invention, wherein a kind of is to have the Ti-Si-Al-B base alloy that eutectic forms titanium alloy wild phase, the chemical composition of tested alloys is Ti-6.3Si-3.65Al-0.04B-0.02Zr (being called for short TS15), and the composition characteristic of the present embodiment is that the addition of B increases to 0.04%.Figure 14 is according to the room temperature tensile curve of the TS15 alloy of method 1 preparation, and the breaking tenacity of this alloy has reached 940MPa.The room temperature compression curve of the TS15 alloy that Figure 15 is prepared according to method 1, can find out, the ultimate compression strength of material is up to 1960MPa, and plastix strain is about 13.3%.The mechanical property that has greatly improved alloy that adds of B is described, particularly improves the plastic deformation ability of alloy, far away higher than the compressive strength of the Ti-Si alloy of announcing in patent 200910113890.6.
In preferred embodiment of the present invention, wherein a kind of chemical composition of alloy is Ti-6.3Si-3.65Al-0.01B-2Zr (being called for short TS16), and the composition characteristic of the present embodiment is that the addition of Zr increases to 2%.Figure 16 is according to the room temperature tensile curve of the TS15 alloy of method 1 preparation, and the breaking tenacity of this alloy has reached 894MPa.The room temperature compression curve of the TS15 alloy that Figure 17 is prepared according to method 1, can find out, the ultimate compression strength of material is up to 1860MPa, and plastix strain is about 12.0%.The mechanical property that has greatly improved alloy that adds of Zr is described, particularly improves the plastic deformation ability of alloy, far away higher than the compressive strength of the Ti-Si alloy of announcing in patent 200910113890.6.
Claims (8)
1. a high-strength casting Ti-Si-Al-B-Zr base alloy, is characterized in that containing intermetallic compound wild phase in Ti-Si-Al-B-Zr base alloy, comprises titanium silicide and titanium boride, and in these wild phases, at least one is Ti
5si
3or Ti
3si, these wild phases by liquid reaction or solid state reaction in alpha titanium alloy matrix; Ti-Si-Al-B-Zr base weight alloy per-cent is Si3.5-7.2%, Al3-8.5%, B0.01-1.5%, Zr0.01-3%, Ti surplus.
2. according to high-strength casting Ti-Si-Al-B-Zr base alloy claimed in claim 1, it is characterized in that Ti-Si-Al-B-Zr base weight alloy per-cent is: Si4.5-7.2%, Al3.5-7.5%, B0.01-0.2%, Zr0.5-2.5%, Ti surplus.
3. according to high-strength casting Ti-Si-Al-B-Zr base alloy claimed in claim 1, it is characterized in that Ti-Si-Al-B-Zr base weight alloy per-cent is: Si6.3, Al3.6, B0.01, Zr0.1, Ti surplus.
4. according to high-strength casting Ti-Si-Al-B-Zr base alloy claimed in claim 1, it is characterized in that Ti-Si-Al-B-Zr base weight alloy per-cent is: Si6.3, Al4.9, B0.01, Zr0.1, Ti surplus.
5. according to high-strength casting Ti-Si-Al-B-Zr base alloy claimed in claim 1, it is characterized in that Ti-Si-Al-B-Zr base weight alloy per-cent is: Si6.4, Al6.2, B0.01, Zr0.1, Ti surplus.
6. according to high-strength casting Ti-Si-Al-B-Zr base alloy claimed in claim 1, it is characterized in that Ti-Si-Al-B-Zr base weight alloy per-cent is: Si6.4, Al7.5, B0.01, Zr0.1, Ti surplus.
7. according to high-strength casting Ti-Si-Al-B-Zr base alloy claimed in claim 1, it is characterized in that Ti-Si-Al-B-Zr base weight alloy per-cent is: Si6.4, Al7.5, B0.04, Zr0.1, Ti surplus.
8. according to high-strength casting Ti-Si-Al-B-Zr base alloy claimed in claim 1, it is characterized in that Ti-Si-Al-B-Zr base weight alloy per-cent is: Si6.4, Al7.5, B0.01, Zr2.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201310546083.XA CN103555999A (en) | 2013-11-06 | 2013-11-06 | High-strength cast Ti-Si-Al-B-Zr base alloy |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201310546083.XA CN103555999A (en) | 2013-11-06 | 2013-11-06 | High-strength cast Ti-Si-Al-B-Zr base alloy |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CN103555999A true CN103555999A (en) | 2014-02-05 |
Family
ID=50010343
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201310546083.XA Pending CN103555999A (en) | 2013-11-06 | 2013-11-06 | High-strength cast Ti-Si-Al-B-Zr base alloy |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN103555999A (en) |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN104911399A (en) * | 2015-07-10 | 2015-09-16 | 哈尔滨工业大学 | Ti-based composite material of two-stage mesh structure and preparation method thereof |
| CN111394613A (en) * | 2020-04-09 | 2020-07-10 | 清华大学 | Anti-cavitation titanium-aluminum-zirconium alloy and preparation process thereof |
Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1121359A (en) * | 1993-03-02 | 1996-04-24 | I·N·弗兰特塞维奇材料科学研究所 | Titanium matrix composites |
| CN101074464A (en) * | 2007-06-21 | 2007-11-21 | 上海交通大学 | Composite heat-resisting enhance titanium alloy |
| JP2008506838A (en) * | 2004-07-13 | 2008-03-06 | エルケム アクシエセルスカプ | High strength, oxidation resistance, wear resistance titanium-silicon substrate alloy |
| CN101497952A (en) * | 2009-02-25 | 2009-08-05 | 广西大学 | High strength high temperature oxidation resistant titanium silicon |
| CN102329983A (en) * | 2010-07-13 | 2012-01-25 | 宝山钢铁股份有限公司 | Titanium alloy capable of resisting high temperature higher than 600 DEG C |
-
2013
- 2013-11-06 CN CN201310546083.XA patent/CN103555999A/en active Pending
Patent Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1121359A (en) * | 1993-03-02 | 1996-04-24 | I·N·弗兰特塞维奇材料科学研究所 | Titanium matrix composites |
| JP2008506838A (en) * | 2004-07-13 | 2008-03-06 | エルケム アクシエセルスカプ | High strength, oxidation resistance, wear resistance titanium-silicon substrate alloy |
| CN101074464A (en) * | 2007-06-21 | 2007-11-21 | 上海交通大学 | Composite heat-resisting enhance titanium alloy |
| CN101497952A (en) * | 2009-02-25 | 2009-08-05 | 广西大学 | High strength high temperature oxidation resistant titanium silicon |
| CN102329983A (en) * | 2010-07-13 | 2012-01-25 | 宝山钢铁股份有限公司 | Titanium alloy capable of resisting high temperature higher than 600 DEG C |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN104911399A (en) * | 2015-07-10 | 2015-09-16 | 哈尔滨工业大学 | Ti-based composite material of two-stage mesh structure and preparation method thereof |
| CN111394613A (en) * | 2020-04-09 | 2020-07-10 | 清华大学 | Anti-cavitation titanium-aluminum-zirconium alloy and preparation process thereof |
| CN111394613B (en) * | 2020-04-09 | 2021-06-25 | 清华大学 | Anti-cavitation titanium-aluminum-zirconium alloy and preparation process thereof |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| Li et al. | Heat treatment and mechanical properties of a high-strength cast Mg–Gd–Zn alloy | |
| EP1516074A1 (en) | Creep resistant magnesium alloy | |
| EP2924137A1 (en) | Aluminium die casting alloys | |
| CN105568083B (en) | It is a kind of suitable for high tough aluminum alloy materials of semi-solid rheological die casting and preparation method thereof | |
| CN109082582B (en) | A kind of the magnesium-based high-entropy alloy and preparation method of high-strength tenacity high rigidity | |
| CN110643851A (en) | TiAl-based composite material and thermal mechanical treatment method thereof | |
| Hao et al. | Microstructure and mechanical properties of extruded Mg–8.5 Gd–2.3 Y–1.8 Ag–0.4 Zr alloy | |
| Tseng et al. | Effects of Fe content on microstructure and mechanical properties of A206 alloy | |
| CN110952002A (en) | Non-heat-treatment-strengthened high-strength high-toughness aluminum alloy material applied to 5G mobile phone middle plate and preparation method thereof | |
| CN110029252A (en) | Plate high-strength and high ductility antioxidation aluminium magnesium alloy materials and preparation method thereof in a kind of 5G mobile phone | |
| CN113862514B (en) | High-strength high-plasticity metastable beta-type titanium alloy and preparation method thereof | |
| GAO et al. | Recent progress in high-temperature resistant aluminum-based alloys: Microstructural design and precipitation strategy | |
| CN103555999A (en) | High-strength cast Ti-Si-Al-B-Zr base alloy | |
| CN105886854A (en) | Preparing method for reducing Fe intermediate phase harm and improving mechanical performance of A356 cast alloy containing scandium and zircon | |
| CN103556000A (en) | Ti-Si-Al-based alloy containing RE (rare earth) and intermetallic compound reinforcing phase | |
| CN112063885A (en) | Ruthenium-containing multi-component TiAl alloy suitable for 800 DEG C | |
| CN113897520A (en) | High-strength heat-resistant cast aluminum-silicon alloy for engine piston | |
| CN103710572B (en) | A kind of casting Ti-Si-Al base superalloy | |
| CN110863124A (en) | High-strength high-plasticity medium-entropy alloy and preparation method thereof | |
| CN105838937A (en) | Aluminum-silicon-magnesium-strontium-scandium-titanium casting alloy with high mechanical property and preparation method thereof | |
| Chen et al. | Effects of Nd or Zr addition on microstructure and mechanical properties of as-cast Mg-Zn-Y alloy | |
| CN110592440A (en) | Short-process preparation method of high-performance and high-stability Al-Si-Cu series cast aluminum alloy component | |
| CN104451254B (en) | Cast Ti-Si eutectic alloy containing intermetallic compound reinforcement phase | |
| CN109338188A (en) | A kind of high-performance magnesium-alloy material of high temperature resistant creep and preparation method thereof | |
| CN114807714B (en) | Zr-rich high-entropy alloy and preparation method thereof |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| C06 | Publication | ||
| PB01 | Publication | ||
| SE01 | Entry into force of request for substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| C02 | Deemed withdrawal of patent application after publication (patent law 2001) | ||
| WD01 | Invention patent application deemed withdrawn after publication |
Application publication date: 20140205 |