CN103320647A - Methods for processing titanium aluminide intermetallic compositions - Google Patents
Methods for processing titanium aluminide intermetallic compositions Download PDFInfo
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- CN103320647A CN103320647A CN2013100939000A CN201310093900A CN103320647A CN 103320647 A CN103320647 A CN 103320647A CN 2013100939000 A CN2013100939000 A CN 2013100939000A CN 201310093900 A CN201310093900 A CN 201310093900A CN 103320647 A CN103320647 A CN 103320647A
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C14/00—Alloys based on titanium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C1/00—Making non-ferrous alloys
- C22C1/02—Making non-ferrous alloys by melting
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/16—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of other metals or alloys based thereon
- C22F1/18—High-melting or refractory metals or alloys based thereon
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/16—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of other metals or alloys based thereon
- C22F1/18—High-melting or refractory metals or alloys based thereon
- C22F1/183—High-melting or refractory metals or alloys based thereon of titanium or alloys based thereon
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Abstract
Methods of processing compositions containing titanium and aluminum, especially titanium aluminide intermetallic compositions (TiAl intermetallics) based on the TiAl (gamma) intermetallic compound. The methods entail processing steps that include a hot isostatic pressing (HIP) cycle and a heat treatment cycle that can be performed in a single vessel. TiAl intermetallic compositions processed in this manner preferably exhibit a duplex microstructure containing equiaxed and lamellar morphologies.
Description
The cross reference of related application
The application's request U.S. Provisional Application number 61/614,751(2012 submitted to March 23) rights and interests, its content is incorporated this paper by reference into.
Background of invention
The present invention relates generally to composition and the processing thereof that contains titanium and aluminium.More particularly, the present invention relates to process the method for foundry goods titanium aluminide intermetallic composition, the method also produces the microtexture of expectation with closed vesicular structure with hot isostatic pressing (hot isostatic pressing) and thermal treatment.
Because weight and high temperature strength are main considerations in the gas-turbine engine design, ongoing effort is to make the alloy/composition that has at elevated temperatures high-intensity relative light weight.Well known in the art, the titanium base alloy system has the mechanical properties that is suitable for the relatively-high temperature application.The high-temperature behavior of titanium base alloy is by using based on titanium aluminide compound Ti
3Al (alpha-2(α-2) alloy) and TiAl(gamma (γ) alloy) titanium metal between system and improving.These titanium aluminide intermetallic compounds (or, for simplicity, TiAl intermetallic thing) general feature is relatively light weight, however known its can present high intensity, creep strength and resistance to fatigue at elevated temperatures.The interpolation of known chromium and niobium promotes some character of TiAl intermetallic thing, such as oxidation resistance, ductility, intensity etc.As limiting examples, the U.S. Patent number 4,879,092 of Huang discloses a kind of Ti of having
46 50Al
46 50Cr
2Nb
2The titanium aluminide intermetallic composition of approximate expression (nominally or approximately Ti-48Al-2Cr-2Nb).Think that this alloy (this paper is called the 48-2-2 alloy) has the at most approximately nominal temperature performance of 1400 ℉ (approximately 760 ℃), has the useful of maximum approximately 1500 ℉ (approximately 815 ℃) but the performance of attenuating.At the gas-turbine engine that is used for commercial aircraft, the 48-2-2 alloy is well suited for using for low-pressure turbine blade (LPTB).
From TiAl intermetallic thing produce assembly since their relatively low ductility and typical case expect these compositions can extrude, malleable, can roll and/or castable complicating.Generally carry out hot isostatic pressing (HIP) to eliminate internal voids and the microvoid structure in the titanium aluminide intermetallic thing foundry goods.Because the not controlled rate of cooling of generally carrying out behind HIP can not effectively produce the microtexture of expectation, be that the feature of another expectation is to obtain the required microtexture of application-specific and mechanical properties to the responsiveness of HIP postheat treatment.
The heat treatment cycle independence that HIP circulation is general in processing with foundry goods.For example, use process shown in Figure 3 in the foundry goods of 48-2-2 alloy, to obtain microtexture and the mechanical properties of expectation.After producing foundry goods, carry out thermal treatment before the HIP, temperature range be approximately 1800-approximately 2000 ℉ (approximately 980-is approximately 1090 ℃) and time length are approximately 5-12 hour.With foundry goods cooling with transfer to HIP chamber, then under approximately 2165 ℉s stand high pressure HIP step (for example, 25ksi(approximately 1720bar) or higher thereafter) about time length of 3 hours.Then will shift out from the HIP chamber through the cooling of the foundry goods of HIP, then about time length of 2 hours of solution treatment after standing HIP under the temperature of about 2200 ℉.This sequence need to use at least two different vessels and with foundry goods from these container loading and unloading three times.Except causing extra cost and cycling time, this process interrelates with the loss of aluminium from cast(ing) surface, it causes the environment and/or the mechanical properties that reduce.
Unexpectedly, for example by rotational casting from the 48-2-2 alloy production, other process (for example gravitational casting (gravity casting) and overstocked foundry goods (overstock casting)) response that the end form foundry goods (net-shape casting) that is used for producing low-pressure turbine blade adopts to above-mentioned heat treatment process or to conventional TiAl foundry goods is well.Especially, 48-2-2 alloy end form foundry goods by end form castmethod processing does not produce the dual microtexture of the expectation that axle and the stratiform γ TiAl form such as contains, these forms improve the ductility of foundry goods, particularly when the volume fraction of laminate structure be about 10-approximately 90% time, if particularly the volume fraction of laminate structure is about 20-approximately 80% and be desirably approximately 30-approximately 70%.Fig. 1 and Fig. 2 are the Photomicrographs that shows the dual microtexture of the expectation that is present in two conventional TiAl foundry goods.
In view of above, need a kind of method, it can process TiAl intermetallic thing (including but not limited to the end form geometrical shape of 48-2-2 alloy) contains etc. axle and lamellar morphologies with generation dual microtexture.Also expect the sequence that this method does not need its medium casting to shift between a plurality of different vessels.
The invention summary
The invention provides and to process the composition that contains titanium and aluminium, especially based on the titanium aluminide intermetallic composition (TiAl intermetallic thing) of TiAl (γ) intermetallic compound, with the method for the microtexture that produces expectation.The method has the further ability of carrying out in single container, obtain comparing the more uncomplicated process of ordinary method, and described ordinary method is for the production of needs space closed (for example passing through HIP) and heat treated composition.
According to a first aspect of the invention, a kind of method of processing titanium aluminide intermetallic composition comprises: under the temperature of at least 1260 ℃ (approximately 2300 ℉) with the composition hot isostatic pressing, with composition cools to the temperature that is not less than 1120 ℃ (approximately 2050 ℉), thermally treated composition under the temperature of approximately 1200 ℃ of about 1150-(approximately 2100-approximately 2200 ℉), then with composition cools to room temperature.After above program, described titanium aluminide intermetallic composition presents the dual microtexture of expectation, and described dual microtexture contains axle such as grade and the lamellar morphologies of γ TiAl phase.
According to a second aspect of the invention, a kind of alternative method of processing titanium aluminide intermetallic composition comprises: with titanium aluminide intermetallic composition hot isostatic pressing, the cooling said composition, under the temperature of at least 1260 ℃ (approximately 2300 ℉) with the about 2.5-approximately 5 hours of composition thermal treatment, with composition cools to the temperature that is not less than 1120 ℃ (approximately 2050 ℉), under the maintenance temperature of approximately 1200 ℃ of about 1150-(approximately 2100-approximately 2200 ℉), composition kept approximately about time length of 6 hours of 2-, then with composition cools to room temperature.After this program, described titanium aluminide intermetallic composition presents the dual microtexture of expectation, and described dual microtexture contains axle such as grade and the lamellar morphologies of γ TiAl phase.
Technique effect of the present invention is the dual microtexture that can produce expectation in TiAl intermetallic thing, and it may be difficult to other acquisition, if particularly produce by end form castmethod (for example rotational casting) and some other foundry engieering of possibility.Another technique effect is to utilize the energy during cooling down from the HIP step to can be used for balancing each other, to assist thermal treatment subsequently, this has determined to get rid of the needs to circulate before the thermal treatment of routine and after the thermal treatment (it may cause aluminium from the cast(ing) surface loss and cause extra cost and cycling time).With the end form foundry goods of producing by end form castmethod (for example rotational casting), in aforesaid 48-2-2 alloy, observed especially these advantages, but other TiAl intermetallic composition is also benefited from treatment process provided by the invention.
The present invention asks for protection:
1. a processing contains the method for the dual microtexture that waits axle and lamellar morphologies of γ TiAl phase with generation based on the titanium aluminide intermetallic composition of TiAl intermetallic compound, and the method comprises:
Under at least 1260 ℃ temperature with described titanium aluminide intermetallic composition hot isostatic pressing;
With described titanium aluminide intermetallic composition cools to the temperature that is not less than 1120 ℃;
At the about described titanium aluminide intermetallic of the thermal treatment composition under 1200 ℃ the temperature of about 1150-; Then
With described titanium aluminide intermetallic composition cools to room temperature;
Wherein with described titanium aluminide intermetallic composition cools after the step of room temperature, described titanium aluminide intermetallic composition presents described dual microtexture.
2. the method for project 1, wherein said hot isostatic pressing step is carried out under the pressure of 1030bar at least.
3. the method for project 1, wherein said hot isostatic pressing step is carried out under the pressure of 1240bar at least.
4. the method for project 1, wherein said hot isostatic pressing step is carried out under at least 1290 ℃ temperature.
5. the method for project 1, wherein said hot isostatic pressing step is approximately carried out under 1330 ℃ the temperature at about 1300-.
6. the method for project 1, the time length that wherein said hot isostatic pressing step is carried out is about 2.5-approximately 5 hours.
7. the method for project 1, wherein during described cooling step with described titanium aluminide intermetallic composition cools to the temperature that is not less than 1150 ℃.
8. the method for project 1, wherein during described cooling step with described titanium aluminide intermetallic composition cools to about 1175 ℃ the temperature of 1150-.
9. the method for project 1, wherein said heat treatment step approximately carries out under 1175 ℃ the temperature at about 1150-.
10. the method for project 1, the time length that wherein said heat treatment step carries out is about 2-approximately 6 hours.
11. the method for project 1, wherein said titanium aluminide intermetallic composition is comprised of following: produce titanium and the aluminium of the amount of TiAl intermetallic compound, one or more in chromium, niobium and the tantalum, and the impurity of following.
12. the method for project 1, wherein said titanium aluminide intermetallic composition is comprised of following by atomic percent: about about 2% chromium of 1.8-, and at most about 2% niobiums, at most approximately 4% tantalums are produced titanium and the aluminium of the amount of TiAl intermetallic compound, and the impurity of following.
13. the method for project 12, wherein said titanium aluminide intermetallic composition contains the titanium of the 46.7-48.9 atomic percent of having an appointment.
14. the method for project 12, wherein said titanium aluminide intermetallic composition contains the aluminium of 47.3 atomic percents of having an appointment.
15. the method for project 12, wherein said titanium aluminide intermetallic composition contains by atomic percent: about 1.9% chromium, and about 1.9 atomic percent niobiums, and have a mind to the tantalum of amount.
16. the method for project 12, wherein said titanium aluminide intermetallic composition contains by atomic percent: about 1.8% chromium, about 0.85 atomic percent niobium, and about 1.7% tantalum.
17. the method for project 12, wherein said titanium aluminide intermetallic composition contains by atomic percent: about 2% chromium, and about 4% tantalum, and have a mind to the niobium of amount.
18. a processing contains the method for the dual microtexture that waits axle and lamellar morphologies of γ TiAl phase with generation based on the titanium aluminide intermetallic composition of TiAl intermetallic compound, the method comprises:
With described titanium aluminide intermetallic composition hot isostatic pressing;
Cool off described titanium aluminide intermetallic composition;
Under at least 1260 ℃ of temperature with the about 2.5-approximately 5 hours of described titanium aluminide intermetallic composition thermal treatment;
With described titanium aluminide intermetallic composition cools to the temperature that is not less than 1120 ℃;
Described titanium aluminide intermetallic composition is approximately kept approximately about time length of 6 hours of 2-under 1200 ℃ the maintenance temperature at about 1150-; Then
With described titanium aluminide intermetallic composition cools to room temperature;
Wherein with described titanium aluminide intermetallic composition cools after the step of room temperature, described titanium aluminide intermetallic composition presents described dual microtexture.
19. the method for project 18, wherein behind described heat treatment step with described titanium aluminide intermetallic composition cools to the temperature that is not less than 1150 ℃, be described maintenance step afterwards, and described maintenance temperature is approximately 1200 ℃ of 1150-.
20. the method for project 18, wherein said titanium aluminide intermetallic composition is comprised of following: produce titanium and the aluminium of the amount of described TiAl intermetallic compound, one or more in chromium, niobium and the tantalum, and the impurity of following.
Other side of the present invention and advantage will be able to better understanding by following detailed description.
The accompanying drawing summary
Fig. 1 and Fig. 2 are the Photomicrographs that shows the microtexture of two foundry goods that formed by TiAl intermetallic composition (with the dual microtexture of expectation).
Fig. 3 is that expression is according to the schema of the method for the foundry goods of the processing TiAl intermetallic composition formation of prior art HIP and heat treatment process.
Fig. 4 and Fig. 5 are the schemas that represents to process according to embodiments of the present invention two kinds of methods of the foundry goods that TiAl intermetallic composition forms.
Fig. 6 and Fig. 7 are the Photomicrographs of the microtexture of two foundry goods showing that identical TiAl intermetallic composition forms, wherein the foundry goods of Fig. 6 is processed according to prior art HIP and the heat treatment process of Fig. 3, and the foundry goods of Fig. 7 is processed according to HIP and the heat treatment process of Fig. 4.
Detailed Description Of The Invention
Fig. 4 and Fig. 5 contain the schema that represents two kinds of methods involvings, can process the TiAl intermetallic composition that includes but not limited to the 48-2-2 alloy by described method, to produce the dual microtexture of expectation, it is with the additional benefit of the art methods shortcoming of avoiding Fig. 3 to summarize.Especially, the method for Fig. 4 and Fig. 5 is avoided before the HIP and the thermal treatment of HIP final vacuum, thinks that described vacuum heat treatment promotes the loss of aluminium in the TiAl intermetallic composition.The present invention also utilizes high atmospheric pressure and protectiveness (inertia) atmosphere of using during the HIP, thinks that its combination can reduce the loss of aluminium in the TiAl intermetallic composition.In addition, each method that Fig. 4 and Fig. 5 summarize provides from HIP step (Fig. 4) or certain temperature (think that this temperature utilize the non-equilibrium phase the TiAl intermetallic composition distributes after the HIP) interruption cooling (Fig. 5), can provide the microtexture of the mechanical properties of expectation to produce (at during Heat Treatment subsequently), if especially TiAl intermetallic composition is the foundry goods that uses end form castingprocesses (for example rotational casting or other method).
As previously discussed, think that the process that Fig. 4 and Fig. 5 summarize is particularly useful for the 48-2-2 alloy, the composition of described alloy is based on γ (TiAl) intermetallic compound.If it contains the dual microtexture that axle and the stratiform γ phase morphology such as comprises, then the foundry goods of 48-2-2 alloy presents the ductility of raising and the character of other expectation.Fig. 6 and Fig. 7 are the representatives by the LPTB foundry goods of 48-2-2 alloy production.Two foundry goods are by rotational casting production, and the foundry goods among Fig. 6 is by processing with corresponding HIP shown in Figure 3 and heat treatment process, and the foundry goods among Fig. 7 is by processing with HIP and the heat treatment process of corresponding modification shown in Figure 4.Microtexture through heat treated foundry goods shown in Figure 6 has the excessive lamellar phase (less than the lamellar phase of 10% volume fraction) that waits axle γ phase and insufficient amount.This microtexture has generation the assembly of not enough high temperature creep strength.But the microtexture through heat treated foundry goods shown in Figure 7 has axle γ phase such as grade and the lamellar phase (the approximately lamellar phase of 20% volume fraction) of receiving amount, and unique exception is the outmost surface at foundry goods, and wherein the amount of titanium is by dilution.Yet, can remove described outmost surface by routine techniques, for example sandblast or chemical milling, but the result is whole remaining foundry goods contain receiving amount wait axle γ phase and lamellar phase.
Produce particularly advantageous result although shown the present invention with the 48-2-2 alloy, think that the present invention more generally is applicable to titanium aluminide intermetallic composition, particularly with element modified TiAl (γ) the intermetallic composition that is intended to promote various character.For example, show that also the present invention is effective to the TiAl intermetallic composition that contains tantalum.The particular composition estimated of success comprises the TiAl composition, and it contains chromium, niobium and/or tantalum, for example, and the about about chromium of 2 atomic percents of 1.8-, the at most about niobiums of 2 atomic percents, and the at most about tantalum of 4 atomic percents.The particular composition that success is estimated contains by atomic percent: approximately 47.3% aluminium, approximately 1.9% chromium, approximately 1.9% niobium and the titanium of surplus and the impurity (roughly being equivalent to the 48-2-2 alloy) of following; Or approximately 47.3% aluminium, approximately 1.8% chromium, approximately 0.85% niobium, approximately 1.7% tantalum and the titanium of surplus and the impurity of following; Or approximately 47.3% aluminium, approximately 2.0% chromium, approximately 4.0% tantalum and the titanium of surplus and the impurity of following.More generally, select the amount of titanium in these TiAl intermetallic compositions and aluminium to produce its main component as the foundry goods of TiAl (γ) intermetallic compound.Although the composition of estimating all contains the have an appointment aluminium of 47.3 atomic percents and the about titanium of 46.7-48.9 atomic percent, the amount that it will be appreciated by those skilled in the art that the aluminium that surpasses this tittle and titanium can be used for the foundry goods producing integral body or be mainly the TiAl intermetallic compound, and these change within the scope of the present invention.In addition, those skilled in the art will admit to comprise other alloying constituent with the character of change TiAl intermetallic compound, and these change also within the scope of the present invention.
During obtaining research of the present invention, be cured modeling, the zone that demonstrates low-pressure turbine blade (LPTB) foundry goods that forms by end form casting (comprising rotational casting) is being less than curing in several seconds.Infer with other castmethod and/or other type foundry goods and compare, this fast setting speed can change the path through the Ti-Al phasor that alloy/composition is during curing taked, and can cause the conventional heat treated accident of carrying out at foundry goods is subsequently responded.These afterclaps affect the end form foundry goods and negatively through the consistence of the microtexture of heat treating assembly, for example chemical and the consistence of the whole wing chord (chord) in the end form TiAl aerofoil and the microtexture in the span (span).Process shown in Figure 4 is cool to room temperature betwixt with HIP circulation and combined with heat treatment and not, and described process is rebuild balancing each other of the dual microtexture that can produce the mechanical properties that expectation is provided.
The process of Fig. 4 is generally with preparation TiAl intermetallic composition.A preferred and nonrestrictive example contains the suitable melt of the desired constituents of TiAl intermetallic composition with rotational casting.Then said composition (foundry goods) is loaded in the suitable HIP chamber and in protective atmosphere (for example argon or another kind of rare gas element) and is heated to certain temperature, foundry goods experience HIP under this temperature.According to a preferred aspect of the present invention, HIP temperature (T
HIP1) be that at least 2300 ℉ (approximately 1260 ℃), more preferably at least 2350 ℉ (approximately 1290 ℃), and most preferred range are about about 2425 ℉ (approximately 1300-is approximately 1330 ℃) of 2375-.The pressure that is applied to foundry goods in HIP cycle period is intended to eliminate internal voids and the microvoid structure in the foundry goods.For this purpose, think approximately 1030bar of 15ksi(at least) pressure be sufficient, think approximately approximately 1240bar of 18ksi() and higher pressure be particularly preferred.The time length of HIP circulation can be depending on used particular composition and pressure and changes, but the result who sees fit is by having approximately 2.5-approximately 5 hours, and particularly approximately the HIP of approximately 3.5 hours time length of 2.5-circulation obtains.
After HIP circulation, foundry goods is cooled to following temperature: be not less than 2050 ℉ (approximately 1120 ℃), more preferably be not less than 2100 ℉ (approximately 1150 ℃), and about 2150 ℉ (approximately 1150-is approximately 1175 ℃) of 2100-most preferably from about.Rate of cooling can change, but find about 5-approximately the speed of 20 ℉/minute (approximately 3-is approximately 11 ℃/minutes) be acceptable.Need not to shift out from the HIP chamber, foundry goods is then in the thermal treatment of following temperature experience: about about 2200 ℉ (approximately 1150-is approximately 1200 ℃) of 2100-, for example, about about 2150 ℉ (approximately 1150-is approximately 1175 ℃) of 2100-.This heat treated time length can be depending on used particular composition and HIP and processes and change, but the result who sees fit is resulting by the heat treatment cycle with about time length of 2-approximately 6 hours (especially approximately 4.5-is approximately 5.5 hours).
After the thermal treatment, can be with foundry goods with the direct cool to room temperature of the speed of any expectation (approximately 20-be approximately 25 ℃).In the result of this process, TiAl intermetallic foundry goods preferably presents the dual microtexture of Fig. 7 finding type.During the step that Fig. 4 determines, do not need to shift out foundry goods from the HIP chamber by above it is evident that, and foundry goods can run through the inert atmosphere that process shown in Figure 4 continues to be exposed to the HIP chamber.
Cool down fully (to room temperature) between HIP circulation and thermal treatment by permission, the process that Fig. 5 sets forth is different from the process that Fig. 4 sets forth.The process of Fig. 5 is heated to T with foundry goods before being included in addition thermal treatment
HIP1Temperature.Thinking that this process circulates at HIP allows higher handiness aspect the used temperature, because HIP need to be at the T of Fig. 4
HIP1Carry out under the temperature, but replace, can be to T on comparable
HIP1The higher or lower temperature of temperature in the described scope (is called T
HIP2) under carry out.
In view of above, the process that Fig. 5 sets forth is generally with at suitable temperature (T
HIP2) under TiAl intermetallic composition (being generally foundry goods) is carried out HIP, foundry goods can be cooled to substantially any temperature (comprising room temperature) after the described process.Thereafter, at T
HIP1With heat treating castings, process is enough to guarantee that whole foundry goods is in T under the temperature (for example at least 2300 ℉ (approximately 1260 ℃))
HIP1Time length.Then speed that can be suitable (for example approximately 5-approximately 20 ℉/minute (approximately 3-approximately 11 ℃/minute)) is cooled to following temperature with foundry goods: be not less than 2050 ℉ (approximately 1120 ℃), more preferably be not less than 2100 ℉ (approximately 1150 ℃), and about 2150 ℉ (approximately 1150-is approximately 1175 ℃) of 2100-most preferably from about.Foundry goods is stood as to the described identical thermal treatment of Fig. 4 process, after this can be with the direct cool to room temperature of foundry goods (approximately 20-be approximately 25 ℃).As the result of this process, TiAl intermetallic foundry goods preferably presents the dual microtexture of Fig. 7 finding type.As the process of Fig. 4, should it is evident that, for any step of Fig. 5, do not need to shift out foundry goods from the HIP chamber, and foundry goods can run through the inert atmosphere that process shown in Figure 5 continues to be exposed to the HIP chamber.
Although describe the present invention with regard to particular, obviously those skilled in the art can adopt other form.Therefore, scope of the present invention will only be limited by claim.
Claims (10)
1. a processing contains the method for the dual microtexture that waits axle and lamellar morphologies of γ TiAl phase with generation based on the titanium aluminide intermetallic composition of TiAl intermetallic compound, and the method comprises:
Under at least 1260 ℃ temperature with described titanium aluminide intermetallic composition hot isostatic pressing;
With described titanium aluminide intermetallic composition cools to the temperature that is not less than 1120 ℃;
At the about described titanium aluminide intermetallic of the thermal treatment composition under 1200 ℃ the temperature of about 1150-; Then
With described titanium aluminide intermetallic composition cools to room temperature;
Wherein with described titanium aluminide intermetallic composition cools after the step of room temperature, described titanium aluminide intermetallic composition presents described dual microtexture.
2. the process of claim 1 wherein that described hot isostatic pressing step carries out under the pressure of 1030bar at least.
3. the process of claim 1 wherein that described hot isostatic pressing step carries out under at least 1290 ℃ temperature.
4. the process of claim 1 wherein that time length that described hot isostatic pressing step is carried out is about 2.5-approximately 5 hours.
5. the process of claim 1 wherein during described cooling step described titanium aluminide intermetallic composition cools to the temperature that is not less than 1150 ℃.
6. the process of claim 1 wherein that described heat treatment step approximately carries out under 1175 ℃ the temperature at about 1150-.
7. the process of claim 1 wherein that time length that described heat treatment step carries out is about 2-approximately 6 hours.
8. the process of claim 1 wherein that described titanium aluminide intermetallic composition is comprised of following: produce titanium and the aluminium of the amount of TiAl intermetallic compound, one or more in chromium, niobium and the tantalum, and the impurity of following.
9. the process of claim 1 wherein that described titanium aluminide intermetallic composition is comprised of following by atomic percent: about about 2% chromium of 1.8-, at most about 2% niobiums, at most approximately 4% tantalums are produced titanium and the aluminium of the amount of TiAl intermetallic compound, and the impurity of following.
10. a processing contains the method for the dual microtexture that waits axle and lamellar morphologies of γ TiAl phase with generation based on the titanium aluminide intermetallic composition of TiAl intermetallic compound, and the method comprises:
With described titanium aluminide intermetallic composition hot isostatic pressing;
Cool off described titanium aluminide intermetallic composition;
Under at least 1260 ℃ of temperature with the about 2.5-approximately 5 hours of described titanium aluminide intermetallic composition thermal treatment;
With described titanium aluminide intermetallic composition cools to the temperature that is not less than 1120 ℃;
Described titanium aluminide intermetallic composition is approximately kept approximately about time length of 6 hours of 2-under 1200 ℃ the maintenance temperature at about 1150-; Then
With described titanium aluminide intermetallic composition cools to room temperature;
Wherein with described titanium aluminide intermetallic composition cools after the step of room temperature, described titanium aluminide intermetallic composition presents described dual microtexture.
Applications Claiming Priority (4)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| US201261614751P | 2012-03-23 | 2012-03-23 | |
| US61/614751 | 2012-03-23 | ||
| US13/459,420 US20130248061A1 (en) | 2012-03-23 | 2012-04-30 | Methods for processing titanium aluminide intermetallic compositions |
| US13/459420 | 2012-04-30 |
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| Publication Number | Publication Date |
|---|---|
| CN103320647A true CN103320647A (en) | 2013-09-25 |
| CN103320647B CN103320647B (en) | 2017-11-07 |
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| CN201310093900.0A Active CN103320647B (en) | 2012-03-23 | 2013-03-22 | The method for handling titanium aluminide intermetallic complex |
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| US (1) | US20130248061A1 (en) |
| EP (2) | EP2641984B1 (en) |
| JP (1) | JP6200666B2 (en) |
| CN (1) | CN103320647B (en) |
| BR (1) | BR102013006917A2 (en) |
| CA (1) | CA2809444C (en) |
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN104005023A (en) * | 2014-06-06 | 2014-08-27 | 江苏大学 | Method for preparing Ti-Al-Nb alloy coating on titanium metal surface |
| CN111975003A (en) * | 2020-08-14 | 2020-11-24 | 西北工业大学 | Method for regulating and controlling titanium-aluminum alloy full lamellar structure |
| CN115151676A (en) * | 2020-01-31 | 2022-10-04 | 赛峰飞机发动机公司 | Hot isostatic pressure heat treatment of rods made of titanium aluminide alloy for low-pressure turbine blades of turbomachines |
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| US8858697B2 (en) | 2011-10-28 | 2014-10-14 | General Electric Company | Mold compositions |
| US9011205B2 (en) | 2012-02-15 | 2015-04-21 | General Electric Company | Titanium aluminide article with improved surface finish |
| US8932518B2 (en) | 2012-02-29 | 2015-01-13 | General Electric Company | Mold and facecoat compositions |
| US10597756B2 (en) | 2012-03-24 | 2020-03-24 | General Electric Company | Titanium aluminide intermetallic compositions |
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| US8992824B2 (en) | 2012-12-04 | 2015-03-31 | General Electric Company | Crucible and extrinsic facecoat compositions |
| US9511417B2 (en) | 2013-11-26 | 2016-12-06 | General Electric Company | Silicon carbide-containing mold and facecoat compositions and methods for casting titanium and titanium aluminide alloys |
| US9192983B2 (en) | 2013-11-26 | 2015-11-24 | General Electric Company | Silicon carbide-containing mold and facecoat compositions and methods for casting titanium and titanium aluminide alloys |
| CN103710606B (en) * | 2013-12-16 | 2016-07-06 | 北京工业大学 | A kind of containing Cr height Nb β-γ TiAl intermetallic compound material and preparation method thereof |
| US10391547B2 (en) | 2014-06-04 | 2019-08-27 | General Electric Company | Casting mold of grading with silicon carbide |
| ES2728527T3 (en) * | 2014-09-01 | 2019-10-25 | MTU Aero Engines AG | TiAl component manufacturing procedure |
| FR3027921A1 (en) * | 2014-10-31 | 2016-05-06 | Snecma | TITANIUM-BASED ALLOYS HAVING IMPROVED MECHANICAL PROPERTIES |
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| CN104005023A (en) * | 2014-06-06 | 2014-08-27 | 江苏大学 | Method for preparing Ti-Al-Nb alloy coating on titanium metal surface |
| CN104005023B (en) * | 2014-06-06 | 2016-05-25 | 江苏大学 | Prepare the method for Ti-Al-Nb alloy coat in surface of metal titanium |
| CN115151676A (en) * | 2020-01-31 | 2022-10-04 | 赛峰飞机发动机公司 | Hot isostatic pressure heat treatment of rods made of titanium aluminide alloy for low-pressure turbine blades of turbomachines |
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| CN111975003B (en) * | 2020-08-14 | 2022-12-27 | 西北工业大学 | Method for regulating and controlling titanium-aluminum alloy full lamellar structure |
Also Published As
| Publication number | Publication date |
|---|---|
| EP2995695A1 (en) | 2016-03-16 |
| CN103320647B (en) | 2017-11-07 |
| JP2013199705A (en) | 2013-10-03 |
| CA2809444A1 (en) | 2013-09-23 |
| EP2641984A2 (en) | 2013-09-25 |
| EP2641984B1 (en) | 2015-10-21 |
| EP2641984A3 (en) | 2014-03-12 |
| CA2809444C (en) | 2021-05-18 |
| BR102013006917A2 (en) | 2015-07-07 |
| EP2995695B1 (en) | 2017-11-22 |
| JP6200666B2 (en) | 2017-09-20 |
| US20130248061A1 (en) | 2013-09-26 |
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