US20090151822A1 - Titanium aluminide alloys - Google Patents

Titanium aluminide alloys Download PDF

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Publication number
US20090151822A1
US20090151822A1 US12/331,909 US33190908A US2009151822A1 US 20090151822 A1 US20090151822 A1 US 20090151822A1 US 33190908 A US33190908 A US 33190908A US 2009151822 A1 US2009151822 A1 US 2009151822A1
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Prior art keywords
alloy
phase
aluminum
intermediate product
titanium
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Abandoned
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US12/331,909
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Inventor
Fritz Appel
Jonathan Paul
Michael Oehring
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GKSS Forshungszentrum Geesthacht GmbH
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GKSS Forshungszentrum Geesthacht GmbH
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Assigned to GKSS-FORSCHUNGSZENTRUM GEESTHACHT GMBH reassignment GKSS-FORSCHUNGSZENTRUM GEESTHACHT GMBH ASSIGNMENT OF ASSIGNORS INTEREST (SEE DOCUMENT FOR DETAILS). Assignors: APPEL, FRITZ, OEHRING, MICHAEL, PAUL, JONATHAN
Publication of US20090151822A1 publication Critical patent/US20090151822A1/en
Priority to US12/512,451 priority Critical patent/US20100000635A1/en
Priority to US13/931,051 priority patent/US20140010701A1/en
Abandoned legal-status Critical Current

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    • 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
    • C22C1/04—Making non-ferrous alloys by powder metallurgy
    • C22C1/045—Alloys based on refractory metals
    • C22C1/0458—Alloys based on titanium, zirconium or hafnium
    • 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
    • C22C—ALLOYS
    • C22C1/00—Making non-ferrous alloys
    • C22C1/04—Making non-ferrous alloys by powder metallurgy
    • 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
    • C22C1/04—Making non-ferrous alloys by powder metallurgy
    • C22C1/047—Making non-ferrous alloys by powder metallurgy comprising intermetallic compounds
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C30/00—Alloys containing less than 50% by weight of each constituent
    • 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 invention relates to alloys based on titanium aluminide, in particular made through the use of casting or powder metallurgical processes, preferably based on ⁇ (TiAl).
  • Titanium aluminide alloys are characterized by a low density, a high rigidity and good corrosion resistance. In the fixed state, they have domains with hexagonal ( ⁇ ), two-phase structures ( ⁇ + ⁇ ) and cubically body-centered ⁇ phase and/or ⁇ phase.
  • alloys based on an intermetallic phase ⁇ (TiAl) with a tetragonal structure and containing minority shares of intermetallic phase ⁇ 2 (Ti 3 Al) with hexagonal structure in addition to the majority phase ⁇ (TiAl) are particularly interesting.
  • These ⁇ titanium aluminide alloys are characterized by properties like low density (3.85-4.2 g/cm 3 ), high elastic modulus, high rigidity and creep resistance up to 700° C., which make them attractive as lightweight construction materials for high-temperature applications. Examples of such applications include turbine buckets in aircraft engines and in stationary gas turbines, and valves for engines and hot gas ventilators.
  • the mechanical properties of titanium aluminide alloys are strongly anisotropic due to their deformation and breaking behavior but also due to the structural anisotropy of the preferably set lamellar structure or duplex structure. Casting processes, different powder-metallurgical and reshaping processes and combinations of these production processes are used for a targeted setting of structure and texture in the production of components made of titanium aluminides.
  • a titanium aluminide alloy which has a structurally and chemically homogeneous structure, is known from EP 1 015 650 B1.
  • the majority phases ⁇ (TiAl) and ⁇ 2 (Ti 3 Al) are hereby distributed in a finely disperse manner.
  • the disclosed titanium aluminide alloy with an aluminum content of 45 atom percent (at %) is characterized by extraordinarily good mechanical properties and high temperature properties.
  • Titanium aluminides based on ⁇ are characterized in general by relatively high rigidities, high elastic modulus, good oxidation and creep resistance with simultaneously lower density. Based on these properties, TiAl alloys should be used as high temperature materials. These types of applications are heavily impaired through the very low plastic malleability and the low fracture toughness. Rigidity and malleability, as with many other materials, behave hereby inversely. The technically interesting high-strength alloys are thereby often particularly brittle. Comprehensive examinations for the optimization of the structure were performed in order to eliminate these disadvantageous properties.
  • the previously developed structure types can be roughly categorized into a) coaxial gamma structures, b) duplex structures and c) lamellar structures.
  • the currently achieved development state is represented in detail for example in:
  • the alloys are usually subjected to several high temperature reshapings through extruding or forging. Also refer to the following publications:
  • the present invention resides in one aspect in an alloy which contains titanium, 38 to 46 atom percent (at %) aluminum, and 5 to 10 atom percent niobium, and has composite lamella that contain a B19 phase and a ⁇ phase in a volume ratio of B19: ⁇ of 0.05:1 to 20:1.
  • the present invention resides in another aspect in a method for the production of an alloy.
  • the method includes providing a composition that contains titanium, 38 to 46 at % aluminum, and 5 to 10 at % niobium and subjecting the composition to a casting or powder metallurgical technique to produce an intermediate product.
  • the intermediate product is subjected to a heat treatment.
  • the heat treatment includes heating the intermediate product at a temperature above 900° C. for more than sixty minutes, and cooling the intermediate product at a rate of more than 0.5° C. per minute.
  • the present invention resides in another aspect in an alloy made by the method described herein.
  • a component may be made from the alloys described herein.
  • FIG. 1A is an electron photomicrograph of an alloy according to one embodiment of the present invention.
  • FIG. 1B is an electron photomicrograph providing a detailed view of selected lamella structures T of FIG. 1A .
  • FIG. 1C is an electron photomicrograph of an alloy according to another embodiment of the present invention.
  • FIG. 2A is an electron photomicrograph providing a more detailed view of a lamella structure T of FIG. 1A .
  • FIG. 2B is an electron photomicrograph providing a still more detailed view of a lamella structure T of FIG. 1A .
  • FIG. 2C is a diffractogram derived from FIG. 2B .
  • FIG. 3 is an electron photomicrograph of a crack in the alloy of FIG. 1A .
  • FIG. 4 is a graph of a plot of force on the vertical axis vs. deflection on the horizontal axis, for a toughness test of an alloy as described herein.
  • the present invention provides a titanium aluminide alloy with a fine structure morphology, for example, a morphology in the nanometer range.
  • the present invention provides a component made from a homogeneous alloy.
  • the present invention provides an alloy based on titanium aluminides which may optionally be made through the use of casting or powder metallurgical processes, preferably based on ⁇ (TiAl), using a composition that contains titanium (Ti), 38 to 42 atom percent (at %) aluminum (Al), and 5 to 10 at % niobium (Nb), and wherein the composition comprises composite lamella structures with B19 phase and ⁇ phase in each lamella, with a volume ratio of the B19 phase to the ⁇ phase in each lamella between 0.05:1 to 20:1. In an optional embodiment, the volume ratio is between 0.1:1 and 10:1.
  • composite lamella structures including composite lamella structures in the nanometer size, are created.
  • the lamella structures include modulated lamellas made of the crystallographically different, and alternatingly formed, B19 phase and ⁇ phase.
  • the created composite lamella structures are largely surrounded by ⁇ -TiAl.
  • alloys can be established in alloys using known production technologies, i.e. through casting, reshaping and powder technologies.
  • the alloys are characterized by an extremely high rigidity and creep resistance with simultaneously high ductility and fracture toughness.
  • Example alloys as described herein can be provided with any of the following titanium-based compositions (wherein titanium makes up the balance of the at % of each composition):
  • Titanium 38.5 to 42.5 at % Al, 5 to 10 at % Nb, and 0.5 to 5 at % Cr;
  • Titanium 39 to 43 at % Al, 5 to 10 at % Nb, and 0.5 to 5 at % Zr;
  • Titanium 41 to 44.5 at % Al, 5 to 10 at % Nb, and 0.5 to 5 at % Mo,
  • Titanium 41 to 44.5 at % Al, 5 to 10 at % Nb, and 0.5 to 5 at % Fe,
  • Titanium 41 to 45 at % Al, 5 to 10 at % Nb, and 0.1 to 1 at % La;
  • Titanium 41 to 45 at % Al, 5 to 10 at % Nb, and 0.1 to 1 at % Sc;
  • Titanium 41 to 45 at % Al, 5 to 10 at % Nb; and 0.1 to 1 at % Y;
  • Titanium 41 to 45 at % Al, 5 to 10 at % Nb, and 0.5 to 5 at % Ta;
  • Titanium 41 to 45 at % Al, 5 to 10 at % Nb, and 0.5 to 5 at % V;
  • Titanium 41 to 46 at % Al, 5 to 10 at % Nb, and 0.5 to 5 at % W.
  • each of the titanium aluminide alloys disclosed above can optionally include boron (B) and/or carbon (C).
  • B boron
  • C carbon
  • any of the described titanium aluminide alloys may include 0.1 to 1 at % boron and/or 0.1 to 1 at % carbon. The already fine structure of the alloy is hereby further refined.
  • the remainders of the specified alloy compositions are made of titanium and unavoidable impurities.
  • alloys are thus made available, which are suitable as a lightweight construction material for high temperature applications, such as turbine buckets or engine and turbine components.
  • alloys as described herein can be produced using casting metallurgical or powder metallurgical processes or techniques, or using these processes in combination with reshaping techniques.
  • the alloys with composite lamella structures have a very fine microstructure and a high rigidity and creep resistance with simultaneously good ductility and fracture toughness with respect to alloys without the composite lamella structures.
  • titanium aluminide alloys with aluminum contents of 38-45 at % and other additives, for example, refractory elements contain relatively large volume shares of the ⁇ phase, which can also be present in a controlled form as B2 phase.
  • the crystallographic lattices of these two phases are mechanically instable with respect to homogenous shearing processes, which can lead to lattice conversions. This property is mainly attributed to the anistropic bond ratio and the symmetry of the cubically body-centered lattice. The tendency of the ⁇ or B2 phase towards lattice transformation is thus very distinct.
  • Different orthorhombic phases can be formed through a shear transformation of the cubically body-centered lattice of the ⁇ or B2 phase, to which phases B19 and B33 belong in particular.
  • the invention is based on the idea of using lattice transformations through shear conversion for an additional refining of the microstructure of the titanium aluminide alloys.
  • This type of process is not previously known for titanium aluminide alloys in scientific literature.
  • the formation of brittle phases like ⁇ , ⁇ ′ and ⁇ ′′ which are extremely disadvantageous for the mechanical material properties, are also avoided, due to shear conversions.
  • the structural refining of the alloys described herein is achieved without the addition of grain-refining or structure-refining elements or additives such as boron (B) and the alloys thus contain no borides. Since the borides occurring in TiAl alloys are brittle, they lead to the brittleness of TiAl alloys as of a certain content and generally represent potential crack nuclei in boron-containing alloys.
  • some alloys as described herein comprise composite lamella structures with the B19 phase and ⁇ phase in each lamella, wherein the lamellas are surrounded by the TiAl- ⁇ phase.
  • the volume ratio of the B19 phase and ⁇ phase each in a lamella is between 0.05:1 and 20:1, for example, 0.1:1 and 10:1. In some embodiments, the volume ratio of the B19 phase and ⁇ phase in a lamella is between 0.2:1 and 5:1, and the volume ratio may be between 0.25:1 and 4:1. In certain embodiments, the volume ratio of the B19 phase and ⁇ phase in a lamella is between 1:3 and 3:1. For example, the volume ratio may be between 0.5:1 and 2:1.
  • Embodiments having a particularly fine structure in the alloy composition have a ratio, in particular the volume ratio, of the B19 phase and ⁇ phase in a lamella, between 0.75:1 and 1.25:1, for example, particular between 0.8:1 and 1.2:1.
  • the volume ratio may be between 0.9:1 and 1.1:1.
  • lamellas of the composite lamella structures are surrounded by lamellas of type ⁇ (TiAl), preferably on both sides of the lamella.
  • the alloys are further characterized in that the lamellas of the composite lamella structures have a volume share of more than 10%, optionally more than 20%, of the total alloy.
  • the fine lamella-like structure in the composite structures are retained if the lamellas of the composite lamella structures TiAl have the phase ⁇ 2 -Ti 3 Al with a volume share of up to 20%, wherein in particular the (volume) ratio of the B19 phase and ⁇ phase in the lamellas remains unchanged and constant.
  • the alloys according to the invention are suitable as high temperature lightweight construction material for components that are exposed to temperatures of up to 800° C.
  • An alloy as described herein can be produced using casting or powder metallurgical techniques.
  • the casting or powder metallurgical techniques are used to produce an intermediate alloy product containing the titanium, aluminum, niobium and optional other components, if any, in the appropriate proportions.
  • the intermediate alloy product is then subjected to heat treatment including heating at temperatures above 900° C., preferably above 1000° C., in particular at temperatures between 1000° C. and 1200° C., for a predetermined period of time of more than 60 minutes, preferably more than 90 minutes, ⁇ yielding a heat-treated intermediate alloy product.
  • the heat-treated intermediate alloy product is then cooled with a predetermined cooling rate of more than 0.5° C. per minute.
  • the heat-treated intermediate alloy product is cooled with a predetermined cooling rate between 1° C. per minute and 20° C. per minute, preferably up to 10° C. per minute.
  • Light (high temperature) materials or components for use in thermal engines like combustion engines, gas turbines, and aircraft engines may be made of an alloy as described herein, e.g., from an alloy based on an intermetallic bond of type ⁇ -TiAl made through casting or powder metallurgical processes or techniques and heat treatment.
  • an alloy as described herein can be used for the production of a component.
  • the alloys described herein may be created through the use of conventional metallurgical casting methods or through known powder metallurgical techniques, and can for example be processed through hot forging, hot pressing or hot extrusion and hot rolling.
  • composite lamella structures of the type described herein are shown in the figures.
  • the example composite lamella structures are based on an alloy comprised of titanium (Ti), 42 atom % aluminum (Al) and 8.5 atom % niobium (Nb).
  • FIG. 1A shows a picture of a structure alloy, which was taken with the help of a transmission electron microscope.
  • the overview picture in FIG. 1 shows that the composite lamella structures, which are labeled with T in FIG. 1 , have a striped contrast to the structure of the ⁇ phase surrounding the structures.
  • FIG. 1B shows a picture of the alloy structure with a higher magnification, whereby it can be seen that the modulated composite lamella structures (reference letter T) are surrounded by the ⁇ phase respectively are embedded in the ⁇ phase.
  • FIGS. 1A and 1 b The structures shown in FIGS. 1A and 1 b were obtained or set through extrusion.
  • FIG. 1C shows a cast structure of the same alloy, i.e., an alloy containing titanium, 42 at % aluminum, and 8.5 at % niobium, in which a composite lamella structure (indicated in the Figure by the reference letter T) is also formed, which is surrounding by the ⁇ phase.
  • a composite lamella structure indicated in the Figure by the reference letter T
  • FIG. 2A shows a high resolution illustration of the atomic structure of the composite lamella structures above the ⁇ phase.
  • the composite lamella structures are made up of the controlled B19 phase and the uncontrolled ⁇ phase, which border the ⁇ phase (in the lower area). It can be seen from the picture in FIG. 2A that the composite lamella structures contain the two crystallographically different phases B19 and ⁇ /B2, which are arranged at separation distances of a few nanometers.
  • the composite lamella structures contain the phases B19 and ⁇ , which are both considered ductile.
  • the volume ratio of the B19 phases to the ⁇ phases in a composite lamella structure is 0.8:1 to 1.2:1. Due to the ductile phases B19 and ⁇ , the structure is mainly made of easily malleable lamellas, which are embedded in the previously relatively brittle ⁇ phase.
  • FIG. 2B shows an illustration of a B19 structure with a magnified representation.
  • the corresponding diffractogram which was calculated from the section shown in FIG. 2B and is characteristic for the B19 structure, is shown in FIG. 2C .
  • FIG. 3 shows an electron-photomicrograph of a crack C in the aforementioned alloy. It can be seen from the figure that the crack C is diffracted at the modulated composite lamella structures (T) and that the composite lamella structures form ligaments that can bridge the edge of the crack. This type of behavior is considerably different from the crack propagation in the previously known Ti—Al alloys, in which a cleavage fracture occurs in the microscopic dimension observed here. In the alloy according to the invention, crack propagation is prevented due to the formed composite lamella structures.
  • the fracture toughness of structure important for the technical application was determined with the help of notched Chevron samples in the bending test at different temperatures.
  • the recorded register curve of such a test is shown in FIG. 4 .
  • the indentations marked by the arrows can be seen in the curve, which indicate that crack propagation intermittently occurs during the loading of the sample, but is stopped again and again.
  • Such a behavior is typical for alloys that are made up of a brittle phase ( ⁇ phase), in which the relative ductile phases B19 and ⁇ are embedded.
  • the alloys according to the invention can be made through the technologies known for TiAl alloys, i.e. via casting metallurgy, reshaping technologies and powder metallurgy.
  • alloys are melted in an electric arc furnace and are re-melted multiple times and are then subjected to a heat treatment.
  • the production methods of vacuum arc casting, induction casting or plasma casting, which are known for primary cast blocks made of TiAl alloys can be used for production.
  • hot-isostatic presses can also be used as the compression method at temperatures of 900° C. to 1,300° C. or heat treatments in the temperature range of 700° C. to 1,400° C. or a combination of these treatments, in order to close pores and to establish the microstructure in the material as described herein.
US12/331,909 2007-12-13 2008-12-10 Titanium aluminide alloys Abandoned US20090151822A1 (en)

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US13/931,051 US20140010701A1 (en) 2007-12-13 2013-06-28 Titanium aluminide alloys

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DE102007060587A DE102007060587B4 (de) 2007-12-13 2007-12-13 Titanaluminidlegierungen

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EP (3) EP2145967B1 (pt)
JP (1) JP5512964B2 (pt)
KR (1) KR20090063173A (pt)
CN (1) CN101457314B (pt)
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CN103820697A (zh) * 2014-03-10 2014-05-28 北京工业大学 一种多元合金化β相凝固高Nb-TiAl合金及其制备方法
US20150322549A1 (en) * 2012-07-25 2015-11-12 Korea Institute Of Machinery & Materials Lamellar-structure titanium-aluminum based alloy having a beta-gamma phase
US20180230822A1 (en) * 2017-02-14 2018-08-16 General Electric Company Titanium aluminide alloys and turbine components
US20190106778A1 (en) * 2016-09-02 2019-04-11 Ihi Corporation TiAl ALLOY AND METHOD OF MANUFACTURING THE SAME
US10544485B2 (en) 2016-05-23 2020-01-28 MTU Aero Engines AG Additive manufacturing of high-temperature components from TiAl
US10597756B2 (en) 2012-03-24 2020-03-24 General Electric Company Titanium aluminide intermetallic compositions

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DE102009050603B3 (de) * 2009-10-24 2011-04-14 Gfe Metalle Und Materialien Gmbh Verfahren zur Herstellung einer β-γ-TiAl-Basislegierung
WO2012041276A2 (de) 2010-09-22 2012-04-05 Mtu Aero Engines Gmbh Warmfeste tial-legierung
DE102011110740B4 (de) * 2011-08-11 2017-01-19 MTU Aero Engines AG Verfahren zur Herstellung geschmiedeter TiAl-Bauteile
EP2620517A1 (de) 2012-01-25 2013-07-31 MTU Aero Engines GmbH Warmfeste TiAl-Legierung
US20130248061A1 (en) * 2012-03-23 2013-09-26 General Electric Company Methods for processing titanium aluminide intermetallic compositions
CN103320648B (zh) * 2012-03-24 2017-09-12 通用电气公司 铝化钛金属间组合物
RU2502824C1 (ru) * 2012-11-13 2013-12-27 Федеральное государственное автономное образовательное учреждение высшего профессионального образования "Национальный исследовательский технологический университет "МИСиС" Способ термообработки отливок из сплавов на основе гамма алюминида титана
DE102012222745A1 (de) 2012-12-11 2014-06-12 MTU Aero Engines AG Einkristalline Turbinenschaufel aus Titanaluminid
WO2014115921A1 (ko) * 2013-01-23 2014-07-31 한국기계연구원 고온강도 및 내산화성이 향상된 타이타늄-알루미늄계 합금
WO2014149122A2 (en) * 2013-03-15 2014-09-25 United Technologies Corporation Process for manufacturing a gamma titanium aluminide turbine component
CN103484701B (zh) * 2013-09-10 2015-06-24 西北工业大学 一种铸造钛合金晶粒细化的方法
CN103773981B (zh) * 2013-12-25 2016-06-29 西安西工大超晶科技发展有限责任公司 一种高Nb-TiAl基合金的熔炼方法
CN103820677B (zh) * 2014-03-12 2016-03-02 北京工业大学 一种含Mn高Nb新型β-γTiAl金属间化合物材料及其制备方法
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JP6439287B2 (ja) * 2014-06-18 2018-12-19 株式会社デンソー 運転支援装置、運転支援方法、画像補正装置、画像補正方法
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US20100000635A1 (en) 2010-01-07
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DE102007060587B4 (de) 2013-01-31

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