EP2995695A1 - Verfahren zur verarbeitung von intermetallischen titanaluminidzusammensetzungen - Google Patents
Verfahren zur verarbeitung von intermetallischen titanaluminidzusammensetzungen Download PDFInfo
- Publication number
- EP2995695A1 EP2995695A1 EP15184357.0A EP15184357A EP2995695A1 EP 2995695 A1 EP2995695 A1 EP 2995695A1 EP 15184357 A EP15184357 A EP 15184357A EP 2995695 A1 EP2995695 A1 EP 2995695A1
- Authority
- EP
- European Patent Office
- Prior art keywords
- titanium aluminide
- tial
- aluminide intermetallic
- temperature
- composition
- 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.)
- Granted
Links
- 239000000203 mixture Substances 0.000 title claims abstract description 90
- 238000000034 method Methods 0.000 title claims abstract description 72
- OQPDWFJSZHWILH-UHFFFAOYSA-N [Al].[Al].[Al].[Ti] Chemical compound [Al].[Al].[Al].[Ti] OQPDWFJSZHWILH-UHFFFAOYSA-N 0.000 title claims abstract description 52
- 229910021324 titanium aluminide Inorganic materials 0.000 title claims abstract description 51
- 238000012545 processing Methods 0.000 title claims abstract description 15
- 229910010038 TiAl Inorganic materials 0.000 claims abstract description 44
- 238000001513 hot isostatic pressing Methods 0.000 claims abstract description 43
- 229910000765 intermetallic Inorganic materials 0.000 claims abstract description 21
- 239000010936 titanium Substances 0.000 claims abstract description 19
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 claims abstract description 18
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims abstract description 18
- 229910052782 aluminium Inorganic materials 0.000 claims abstract description 18
- 229910052719 titanium Inorganic materials 0.000 claims abstract description 18
- 238000001816 cooling Methods 0.000 claims description 23
- 239000011651 chromium Substances 0.000 claims description 14
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 claims description 13
- 229910052804 chromium Inorganic materials 0.000 claims description 13
- 239000010955 niobium Substances 0.000 claims description 13
- 229910052758 niobium Inorganic materials 0.000 claims description 12
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 claims description 12
- 229910052715 tantalum Inorganic materials 0.000 claims description 12
- GUVRBAGPIYLISA-UHFFFAOYSA-N tantalum atom Chemical compound [Ta] GUVRBAGPIYLISA-UHFFFAOYSA-N 0.000 claims description 12
- 239000012535 impurity Substances 0.000 claims description 7
- 229910006281 γ-TiAl Inorganic materials 0.000 claims description 6
- 238000010438 heat treatment Methods 0.000 abstract description 28
- 238000005266 casting Methods 0.000 description 66
- 229910045601 alloy Inorganic materials 0.000 description 21
- 239000000956 alloy Substances 0.000 description 21
- 230000008901 benefit Effects 0.000 description 7
- 238000004528 spin coating Methods 0.000 description 7
- 230000009286 beneficial effect Effects 0.000 description 3
- 239000000470 constituent Substances 0.000 description 3
- 239000007789 gas Substances 0.000 description 3
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 description 2
- 238000007796 conventional method Methods 0.000 description 2
- 238000004519 manufacturing process Methods 0.000 description 2
- 230000001681 protective effect Effects 0.000 description 2
- 238000007711 solidification Methods 0.000 description 2
- 230000008023 solidification Effects 0.000 description 2
- 238000011282 treatment Methods 0.000 description 2
- 229910004349 Ti-Al Inorganic materials 0.000 description 1
- 229910021330 Ti3Al Inorganic materials 0.000 description 1
- 229910004692 Ti—Al Inorganic materials 0.000 description 1
- 238000005270 abrasive blasting Methods 0.000 description 1
- 238000007792 addition Methods 0.000 description 1
- 229910052786 argon Inorganic materials 0.000 description 1
- 238000013461 design Methods 0.000 description 1
- 230000003467 diminishing effect Effects 0.000 description 1
- 238000009826 distribution Methods 0.000 description 1
- 230000007613 environmental effect Effects 0.000 description 1
- 238000011067 equilibration Methods 0.000 description 1
- 230000001747 exhibiting effect Effects 0.000 description 1
- 230000005484 gravity Effects 0.000 description 1
- 239000011261 inert gas Substances 0.000 description 1
- 238000011835 investigation Methods 0.000 description 1
- 238000001000 micrograph Methods 0.000 description 1
- 238000003801 milling Methods 0.000 description 1
- 230000003647 oxidation Effects 0.000 description 1
- 238000007254 oxidation reaction Methods 0.000 description 1
- 238000010587 phase diagram Methods 0.000 description 1
- 238000003672 processing method Methods 0.000 description 1
- 238000007712 rapid solidification Methods 0.000 description 1
- 230000004044 response Effects 0.000 description 1
- 230000004043 responsiveness Effects 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
- 239000011800 void material Substances 0.000 description 1
Images
Classifications
-
- 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
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/02—Making non-ferrous alloys by melting
-
- 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
-
- 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
Definitions
- the present invention generally relates to compositions containing titanium and aluminum and the processing thereof. More particularly, this invention relates to methods of processing cast titanium aluminide intermetallic compositions that entail hot isostatic pressing and heat treatment to close porosity and yield a desirable microstructure.
- Titanium-based alloy systems are well known in the art as having mechanical properties that are suitable for relatively high temperature applications.
- High temperature capabilities of titanium-based alloys has increased through the use of titanium intermetallic systems based on the titanium aluminide compounds Ti 3 Al (alpha-2 ( ⁇ -2) alloys) and TiAl (gamma (y) alloys).
- These titanium aluminide intermetallic compounds are generally characterized as being relatively light weight, yet are known to be capable of exhibiting high strength, creep strength and fatigue resistance at elevated temperatures.
- Additions of chromium and niobium are known to promote certain properties of TiAl intermetallics, such as oxidation resistance, ductility, strength, etc.
- U.S. Patent No. 4,879,092 to Huang discloses a titanium aluminide intermetallic composition having an approximate formula of Ti 46-50 Al 46-50 Cr 2 Nb 2 , or nominally about Ti-48Al-2Cr-2Nb.
- This alloy, referred to herein as the 48-2-2 alloy is considered to have a nominal temperature capability of up to about 1400°F (about 760°C), with useful but diminishing capabilities up to about 1500°F (about 815°C).
- the 48-2-2 alloy is well suited for low pressure turbine blade (LPTB) applications.
- Hot isostatic pressing is commonly performed to eliminate internal voids and microporosity in titanium aluminide intermetallic castings. Because uncontrolled cooling rates typically performed following HIP are not effective to generate a desired microstructure, responsiveness to post-HIP heat treatments is another desirable characteristic in order to achieve microstructures and mechanical properties needed for specific applications.
- HIP cycles are typically separate from the heat treatment cycle in the processing of castings.
- desired microstructures and mechanical properties have been obtained in castings of the 48-2-2 alloy using a process represented in FIG. 3 .
- a pre-HIP heat treatment is performed at a temperature within a range of about 1800 to about 2000°F (about 980 to about 1090°C) and for a duration of about five to twelve hours.
- the casting is cooled and transferred to a HIP chamber and then subjected to a high pressure HIP step (for example, 25 ksi (about 1720 bar) or more) at about 2165°F for a duration of about three hours.
- a high pressure HIP step for example, 25 ksi (about 1720 bar) or more
- the HIPed casting is then cooled, removed from the HIP chamber, and then subjected to a post-HIP solution treatment at a temperature of about 2200°F for a duration of about two hours.
- This sequence requires the use of at least two different vessels and loading and unloading the casting three times from these vessels. In addition to incurring additional cost and cycle time, this process has been associated with the loss of aluminum from the casting surface, which leads to reduced environmental and/or mechanical properties.
- FIGS. 1 and 2 are photomicrographs showing desirable duplex microstructures present in two conventional TiAl castings.
- a method is needed that is capable of processing TiAl intermetallics, including but not limited to net-shape geometries of the 48-2-2 alloy, to yield a duplex microstructure containing equiaxed and lamellar morphologies. It would be further desirable if such a method did not require a sequence in which a casting is not required to be transferred between multiple different vessels.
- the present invention provides methods capable of processing compositions containing titanium and aluminum, and especially titanium aluminide intermetallic compositions (TiAl intermetallics) based on the TiAl (gamma) intermetallic compound, to yield desirable microstructures.
- the methods have the further capability of being performed in a single vessel, resulting in a less complicated process than conventional methods used to produce compositions that require void closure (for example, by HIPing) and heat treatment.
- a method of processing a titanium aluminide intermetallic composition includes hot isostatic pressing the composition at a temperature of at least 1260°C (about 2300°F), cooling the composition to a temperature of not less than 1120°C (about 2050°F), heat treating the composition at a temperature of about 1150 to about 1200°C (about 2100 to about 2200°F), and then cooling the composition to room temperature.
- the titanium aluminide intermetallic composition exhibits a desirable duplex microstructure containing equiaxed and lamellar morphologies of the gamma TiAl phase.
- a method of processing a titanium aluminide intermetallic composition includes hot isostatic pressing the titanium aluminide intermetallic composition, cooling the composition, heat treating the composition at a temperature of at least 1260°C (about 2300°F) for about 2.5 to about 5 hours, cooling the composition to a temperature of not less than 1120°C (about 2050°F), holding the composition at a hold temperature of about 1150 to about 1200°C (about 2100 to about 2200°F) for a duration of about two to about six hours, and then cooling the composition to room temperature.
- the titanium aluminide intermetallic composition exhibits a desirable duplex microstructure containing equiaxed and lamellar morphologies of the gamma TiAl phase.
- a beneficial effect of the invention is the ability to produce desirable duplex microstructures in TiAl intermetallics that may otherwise be difficult to obtain, particularly if produced by net-shape casting methods such as spin casting and possibly certain other casting techniques.
- Another beneficial effect is the ability to take advantage of the energy available for phase equilibration during cool down from a HIP step to assist in a subsequent heat treatment, which has been determined to eliminate the requirement for conventional pre- and post-heat treatment cycles that may cause aluminum to be lost from the casting surface as well as incur additional cost and cycle time.
- FIGS. 4 and 5 contain flow charts that represent two related methods by which TiAl intermetallic compositions, including but not limited to the 48-2-2 alloy, can be processed to yield a desirable duplex microstructure, with the additional benefit of avoiding the disadvantages of the prior art process summarized in FIG. 3 .
- the methods of FIGS. 4 and 5 avoid the pre- and post-HIP vacuum heat treatments that are believed to promote the loss of aluminum in TiAl intermetallic compositions.
- the invention also takes advantage of the high gas pressures and protective (inert) atmospheres used during HIP, the combination of which is believed to be capable of reducing the loss of aluminum in a TiAl intermetallic composition.
- FIG. 4 and 5 provide for interrupted cooling from a HIP step ( FIG. 4 ) or a temperature that is believed to take advantage of the non-equilibrium phase distribution in TiAl intermetallic compositions following HIP ( FIG. 5 ) to generate (during a subsequent heat treatment) microstructures that are capable of providing desirable mechanical properties, especially if the TiAl intermetallic composition is a cast using a net-shape casting process, such as spin casting or other means.
- FIGS. 4 and 5 are believed to be particularly beneficial to the 48-2-2 alloy, whose composition is based on the gamma (TiAl) intermetallic compound. Castings of the 48-2-2 alloy exhibit improved ductility and other desirable properties if they contain a duplex microstructure containing equiaxed and lamellar gamma phase morphologies.
- FIGS. 6 and 7 are representative of LPTB castings produced from the 48-2-2 alloy. Both castings were produced by spin casting, the casting in FIG. 6 was processed by a HIP and heat treatment procedure corresponding to that represented in FIG. 3 , and the casting in FIG. 7 was processed by a modified HIP and heat treatment procedure corresponding to that represented in FIG. 4 .
- the microstructure of the heat treated casting shown in FIG. 6 possesses an excessive amount of equiaxed gamma phase and an inadequate amount of the lamellar phase (less than 10% volume fraction of the lamellar phase). Such a microstructure would yield a component with insufficiently high temperature creep strength.
- the microstructure of the heat treated casting shown in FIG. 7 has acceptable amounts of the equiaxed gamma phase and the lamellar phase (about 20% volume fraction of the lamellar phase), the sole exception being at the outermost surface of the casting where titanium levels are depleted. However, the outermost surface can be removed by conventional techniques, such as abrasive blasting or chemical milling, with the result that the entire remaining casting would contain acceptable amounts of the equiaxed gamma phase and lamellar phase.
- the invention has been shown to yield particularly advantageous results with the 48-2-2 alloy, the invention is believed to be more generally applicable to titanium aluminide intermetallic compositions, particularly TiAl (gamma) intermetallic compositions modified with elements that are intended to promote various properties.
- the invention has also been shown to be effective with TiAl intermetallic compositions that contain tantalum.
- Particular compositions that have been successfully evaluated include TiAl compositions that contain chromium, niobium and/or tantalum, for example, about 1.8 to about 2 atomic percent chromium, up to about 2 atomic percent niobium, and up to about 4 atomic percent tantalum.
- compositions that were successfully evaluated contained, in atomic percent: about 47.3% aluminum, about 1.9% chromium, about 1.9% niobium and the balance titanium and incidental impurities (roughly corresponding to the 48-2-2 alloy); or about 47.3% aluminum, about 1.8% chromium, about 0.85% niobium, about 1.7% tantalum and the balance titanium and incidental impurities; or about 47.3% aluminum, about 2.0% chromium, about 4.0% tantalum and the balance titanium and incidental impurities. More generally, the levels of titanium and aluminum in these TiAl intermetallic compositions are selected to yield a casting whose predominant constituent is the TiAl (gamma) intermetallic compound.
- compositions evaluated all contained about 47.3 atomic percent aluminum and about 46.7 to 48.9 atomic percent titanium, those skilled in the art will appreciate that aluminum and titanium levels beyond these amounts can be used to yield a casting that is entirely or predominantly the TiAl intermetallic compound, and such variations are within the scope of the invention. Furthermore, those skilled in the art will recognize that other alloy constituents could be included to modify the properties of the TiAl intermetallic compound, and such variations are also within the scope of the invention.
- the process of FIG. 4 generally entails preparing a TiAl intermetallic composition.
- a preferred but not limiting example entails spin casting an appropriate melt containing the desired constituents of the TiAl intermetallic composition.
- the composition (casting) is then loaded in a suitable HIP chamber and heated in a protective atmosphere (for example, argon or another inert gas) to a temperature at which the casting is to undergo HIPing.
- the HIP temperature (T HIP1 ) is at least 2300°F (about 1260°C), more preferably at least 2350°F (about 1290°C), and most preferably in a range of about 2375 to about 2425°F (about 1300 to about 1330°C).
- the pressure applied to the casting during the HIP cycle is intended to eliminate internal voids and microporosity in the castings.
- pressures of at least 15 ksi (about 1030 bar) are believed to be sufficient, with pressures of about 18 ksi (about 1240 bar) and higher believed to be particularly preferred.
- the duration of the HIP cycle may vary depending on the particular composition and pressure used, but suitable results are believed to be obtained with HIP cycles having durations of about 2.5 to about 5 hours, and particularly about 2.5 to about 3.5 hours.
- the casting is cooled to a temperature of not less than 2050°F (about 1120°C), more preferably not less than 2100°F (about 1150°C), and most preferably about 2100 to about 2150°F (about 1150 to about 1175°C).
- the cooling rate may vary, but rates of about 5 to about 20°F/minute (about 3 to about 11 °C/minute) have been found to be acceptable.
- the casting then undergoes a heat treatment at a temperature of about 2100 to about 2200°F (about 1150 to about 1200°C), for example, about 2100 to about 2150°F (about 1150 to about 1175°C).
- the duration of this heat treatment may vary depending on the particular composition and HIP treatment used, but suitable results are believe to be obtained with heat treatment cycles having durations of about two to about six hours, and especially about 4.5 to about 5.5 hours.
- the casting can be cooled directly to room temperature (about 20 to about 25°C) at any desired rate.
- the TiAl intermetallic casting preferably exhibits a duplex microstructure of the type seen in FIG. 7 . From the above, it should be evident that the casting is not required to be removed from the HIP chamber during the steps identified in FIG. 4 , and that the casting can be continuously exposed to the inert atmosphere of the HIP chamber throughout the process represented in FIG. 4 .
- the process set forth in FIG. 5 differs from that set forth in FIG. 4 by the allowance of a full cool down (to room temperature) between the HIP cycle and the heat treatment.
- the process of FIG. 5 additionally involves heating the casting to the T HIP1 temperature prior to the heat treatment. This process is believed to allow more flexibility in the temperature used for the HIP cycle, in that HIPing is not required to be performed at the T HIP1 temperature of FIG. 4 , but instead can be at a temperature (designated as T HIP2 ) that can be higher or lower than the temperatures within the ranges stated above for T HIP1 .
- the process set forth in FIG. 5 generally entails HIPing a TiAl intermetallic composition (typically a casting) at a suitable temperature (T HIP2 ), which can be followed by cooling the casting to essentially any temperature (including room temperature). Thereafter, the casting is heat treated at the T HIP1 temperature (for example, at least 2300°F (about 1260°C)) for a duration sufficient to ensure the entire casting is at T HIP1 .
- T HIP2 suitable temperature
- T HIP1 temperature for example, at least 2300°F (about 1260°C)
- the casting can then be cooled at a suitable rate (for example, about 5 to about 20°F/minute (about 3 to about 11°C/minute)) to a temperature of not less than 2050°F (about 1120°C), more preferably not less than 2100°F (about 1150°C), and most preferably about 2100 to about 2150°F (about 1150 to about 1175°C).
- the casting can then be subjected to the same heat treatment as described for the process of FIG. 4 , after which the casting can be cooled directly to room temperature (about 20 to about 25°C).
- the TiAl intermetallic casting preferably exhibits a duplex microstructure of the type seen in FIG. 7 .
- the casting is not required to be removed from the HIP chamber for any step of FIG. 5 , and that the casting can be continuously exposed to the inert atmosphere of the HIP chamber throughout the process represented in FIG. 5 .
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- Organic Chemistry (AREA)
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- Powder Metallurgy (AREA)
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Applications Claiming Priority (3)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
US201261614751P | 2012-03-23 | 2012-03-23 | |
US13/459,420 US20130248061A1 (en) | 2012-03-23 | 2012-04-30 | Methods for processing titanium aluminide intermetallic compositions |
EP13159885.6A EP2641984B1 (de) | 2012-03-23 | 2013-03-19 | Verfahren zur Verarbeitung von intermetallischen Titanaluminidzusammensetzungen |
Related Parent Applications (2)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
EP13159885.6A Division-Into EP2641984B1 (de) | 2012-03-23 | 2013-03-19 | Verfahren zur Verarbeitung von intermetallischen Titanaluminidzusammensetzungen |
EP13159885.6A Division EP2641984B1 (de) | 2012-03-23 | 2013-03-19 | Verfahren zur Verarbeitung von intermetallischen Titanaluminidzusammensetzungen |
Publications (2)
Publication Number | Publication Date |
---|---|
EP2995695A1 true EP2995695A1 (de) | 2016-03-16 |
EP2995695B1 EP2995695B1 (de) | 2017-11-22 |
Family
ID=47913098
Family Applications (2)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
EP13159885.6A Active EP2641984B1 (de) | 2012-03-23 | 2013-03-19 | Verfahren zur Verarbeitung von intermetallischen Titanaluminidzusammensetzungen |
EP15184357.0A Active EP2995695B1 (de) | 2012-03-23 | 2013-03-19 | Verfahren zur verarbeitung von intermetallischen titanaluminidzusammensetzungen |
Family Applications Before (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
EP13159885.6A Active EP2641984B1 (de) | 2012-03-23 | 2013-03-19 | Verfahren zur Verarbeitung von intermetallischen Titanaluminidzusammensetzungen |
Country Status (6)
Country | Link |
---|---|
US (1) | US20130248061A1 (de) |
EP (2) | EP2641984B1 (de) |
JP (1) | JP6200666B2 (de) |
CN (1) | CN103320647B (de) |
BR (1) | BR102013006917A2 (de) |
CA (1) | CA2809444C (de) |
Families Citing this family (16)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
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 |
US8906292B2 (en) | 2012-07-27 | 2014-12-09 | General Electric Company | Crucible and facecoat compositions |
US8708033B2 (en) | 2012-08-29 | 2014-04-29 | General Electric Company | Calcium titanate containing mold compositions and methods for casting titanium and titanium aluminide alloys |
US8992824B2 (en) | 2012-12-04 | 2015-03-31 | General Electric Company | Crucible and extrinsic facecoat compositions |
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 |
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 |
CN103710606B (zh) * | 2013-12-16 | 2016-07-06 | 北京工业大学 | 一种含Cr高Nbβ-γ TiAl金属间化合物材料及其制备方法 |
US10391547B2 (en) | 2014-06-04 | 2019-08-27 | General Electric Company | Casting mold of grading with silicon carbide |
CN104005023B (zh) * | 2014-06-06 | 2016-05-25 | 江苏大学 | 在钛金属表面制备Ti-Al-Nb合金涂层的方法 |
EP2990141B1 (de) * | 2014-09-01 | 2019-04-03 | MTU Aero Engines GmbH | Herstellungsverfahren für TiAl-Bauteile |
FR3027921A1 (fr) * | 2014-10-31 | 2016-05-06 | Snecma | Alliages a base de titane presentant des proprietes mecaniques ameliorees |
FR3106851B1 (fr) * | 2020-01-31 | 2022-03-25 | Safran Aircraft Engines | Traitement thermique à compression isostatique à chaud de barreaux en alliage d’aluminure de titane pour aubes de turbine basse pression de turbomachine |
CN111975003B (zh) * | 2020-08-14 | 2022-12-27 | 西北工业大学 | 一种钛铝合金全片层组织的调控方法 |
Citations (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US4879092A (en) | 1988-06-03 | 1989-11-07 | General Electric Company | Titanium aluminum alloys modified by chromium and niobium and method of preparation |
US5634992A (en) * | 1994-06-20 | 1997-06-03 | General Electric Company | Method for heat treating gamma titanium aluminide alloys |
US6231699B1 (en) * | 1994-06-20 | 2001-05-15 | General Electric Company | Heat treatment of gamma titanium aluminide alloys |
Family Cites Families (8)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US5149497A (en) * | 1991-06-12 | 1992-09-22 | General Electric Company | Oxidation resistant coatings of gamma titanium aluminum alloys modified by chromium and tantalum |
JPH06228685A (ja) * | 1993-02-01 | 1994-08-16 | Honda Motor Co Ltd | 高強度高延性TiAl系金属間化合物およびその製造方法 |
US5350466A (en) * | 1993-07-19 | 1994-09-27 | Howmet Corporation | Creep resistant titanium aluminide alloy |
US5609698A (en) * | 1995-01-23 | 1997-03-11 | General Electric Company | Processing of gamma titanium-aluminide alloy using a heat treatment prior to deformation processing |
US5545265A (en) * | 1995-03-16 | 1996-08-13 | General Electric Company | Titanium aluminide alloy with improved temperature capability |
CN1055323C (zh) * | 1997-11-03 | 2000-08-09 | 冶金工业部钢铁研究总院 | 钛铝合金铸件的组织均匀细化方法 |
JP3784363B2 (ja) * | 2002-10-10 | 2006-06-07 | 株式会社神戸製鋼所 | Al合金鋳造品の改質法 |
DE102007060587B4 (de) * | 2007-12-13 | 2013-01-31 | Helmholtz-Zentrum Geesthacht Zentrum für Material- und Küstenforschung GmbH | Titanaluminidlegierungen |
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2012
- 2012-04-30 US US13/459,420 patent/US20130248061A1/en not_active Abandoned
-
2013
- 2013-03-14 CA CA2809444A patent/CA2809444C/en active Active
- 2013-03-19 EP EP13159885.6A patent/EP2641984B1/de active Active
- 2013-03-19 JP JP2013055847A patent/JP6200666B2/ja active Active
- 2013-03-19 EP EP15184357.0A patent/EP2995695B1/de active Active
- 2013-03-22 CN CN201310093900.0A patent/CN103320647B/zh active Active
- 2013-03-25 BR BRBR102013006917-5A patent/BR102013006917A2/pt not_active Application Discontinuation
Patent Citations (3)
Publication number | Priority date | Publication date | Assignee | Title |
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US4879092A (en) | 1988-06-03 | 1989-11-07 | General Electric Company | Titanium aluminum alloys modified by chromium and niobium and method of preparation |
US5634992A (en) * | 1994-06-20 | 1997-06-03 | General Electric Company | Method for heat treating gamma titanium aluminide alloys |
US6231699B1 (en) * | 1994-06-20 | 2001-05-15 | General Electric Company | Heat treatment of gamma titanium aluminide alloys |
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CN103320647A (zh) | 2013-09-25 |
EP2641984A3 (de) | 2014-03-12 |
JP2013199705A (ja) | 2013-10-03 |
EP2641984B1 (de) | 2015-10-21 |
CA2809444A1 (en) | 2013-09-23 |
EP2641984A2 (de) | 2013-09-25 |
BR102013006917A2 (pt) | 2015-07-07 |
CA2809444C (en) | 2021-05-18 |
CN103320647B (zh) | 2017-11-07 |
EP2995695B1 (de) | 2017-11-22 |
JP6200666B2 (ja) | 2017-09-20 |
US20130248061A1 (en) | 2013-09-26 |
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