WO1996030552A1 - Castable gamma titanium-aluminide alloy containing niobium, chromium and silicon - Google Patents
Castable gamma titanium-aluminide alloy containing niobium, chromium and silicon Download PDFInfo
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- WO1996030552A1 WO1996030552A1 PCT/US1996/003850 US9603850W WO9630552A1 WO 1996030552 A1 WO1996030552 A1 WO 1996030552A1 US 9603850 W US9603850 W US 9603850W WO 9630552 A1 WO9630552 A1 WO 9630552A1
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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
Definitions
- the present invention relates generally to alloys of titanium and aluminum. - More particularly, it relates to gamma alloys of titanium and aluminum which have
- the alloy of titanium and aluminum having a tetragonal Ll 0 crystal structure has a stoichiometric ratio of approximately one. It is an intermetallic compound having l w density, high modulus, good elevated temperature tensile properties and good creep resistance. With respect to all aforementioned properties, gamma TiAl is superior to all other conventional titanium alloys and, on a specific basis, is frequently 5 superior to nickel alloys. For this reason, gamma TiAl alloys have been the subject of intense research as a replacement for nickel alloys in various aerospace applications. for example turbine blades.
- the stoichiometric ratio of gamma TiAl can vary over a range without varying its crystal structure. Between about SO and 60 atom percent, the compound can exist as a single phase material having the LI o, known as the gamma phase. Between about SO and 60 atom percent, the compound can exist as a single phase material having the LI o, known as the gamma phase. Between
- the material will consist of a two phase mixture
- alpha-two ( ⁇ ) phase consisting of the formula Ti 3 Al.
- Current gamma alloys are, in
- the present invention provides a gamma titanium aluminide alloy consisting essentially of the formula Ti-Al 1 Cr b Nb c Sid, where "a” , “b”, “c” and “d” are in atomic 15 percent, “a” ranges from about 44 to about 48, “b” ranges from about 2 to about 6; “c” ranges from about 2 to about 6 and “d” ranges from about 0.5 to about 1.0
- the invention provides a process for casting a gamma titanium
- aluminide alloy comprising the steps of: (a) forming a melt of a gamma titanium aluminide alloy consisting essentially of the formula Ti-Al,Cr* > NbcSid, where "a” , "b",
- Niobium is generally beneficial to creep strength and oxidation but is prone to segregation at levels above about 6 at%
- niobium levels above about 6 at% increase alloy density and cost, while niobium levels below about 2 4 at % are generally insufficient to produce the improved oxidation and creep prope ⁇ ies exhibited by alloys of the invention.
- Si levels above about 1 at% tend to result in
- the melt can be formed using standard titanium alloy melt practice, including that of induction melting in an inert atmosphere or vacuum. Adequate clean melt
- FIG. 1 is a graph depicting the ultimate tensile strength and tensile elongation
- TiAl would have many uses in industry, owing to its light weight, high strength at high
- TiAl suffers from a number of problems, including brittleness and low strength of the castings Another problem with cast gamma TiAl is low fluidity in the molten state
- the present invention provides a gamma titanium aluminide alloy consisting essentially of the formula Ti-Al,Cr b Nb e Sid, where "a” , "b", “c” and “d" are
- the gamma titanium aluminide alloy of the invention can be cast by a process comprising the steps of forming a melt of the alloy and casting it into a mold Castings
- Niobium is generally beneficial to creep strength and oxidation but is prone to segregation at levels above about 6 at%
- niobium levels above about 6 at% increase alloy density and cost, while niobium levels below about 2 at % are generally insufficient to produce the improved oxidation and creep properties exhibited by alloys of the invention.
- Si levels above about 1 at% tend result in reduced 30 oxidation resistance.
- the melt can be formed using standard titanium alloy melt practice, including 35 that of induction melting in an inert atmosphere or vacuum Adequate clean melt practice must be observed to limit contamination of impu ⁇ ties such as oxygen. nitrogen, and carbon to levels of less than about 2000 ppm oxygen, 500 ppm nitrogen , and 1000 ppm carbon which can embrittle the alloy
- silicon between 2 and 6 % while holding silicon constant at 0.5 %. Variations in silicon of between 0 and 1.0 % were made holding aluminum, chromium, and niobium constant at 46Al-2Cr-2Nb. Samples were cast into graphite test bar molds and were HIPed for
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Abstract
A gamma titanium aluminide alloy has a composition consisting essentially of the formula Ti-AlaCrbNbcSid, where 'a', 'b', 'c' and 'd' are in atomic percent, 'a' ranges from about 44 to about 48, 'b' ranges from about 2 to about 6; 'c' ranges from about 2 to about 6 and 'd' ranges from about 0.5 to about 1.0. The alloy is castable into molds containing fine detail and sharp angle. Molded parts composed of the alloy exhibit excellent strength and toughness.
Description
CASTABLE GAMMA TTTANIUM-ALUMINIDE ALLOY
CONTAINING NIOBIUM- CHROMIUM AND SILICON
BACKGROUND OF THE INVENTION 1. Field Of The Invention
The present invention relates generally to alloys of titanium and aluminum. - More particularly, it relates to gamma alloys of titanium and aluminum which have
been modified both with respect to stoichiometric ratio and with respect to chromium, niobium and silicon.
5 2. Description Of The Prior Art
The alloy of titanium and aluminum having a tetragonal Ll0 crystal structure has a stoichiometric ratio of approximately one. It is an intermetallic compound having l w density, high modulus, good elevated temperature tensile properties and good creep resistance. With respect to all aforementioned properties, gamma TiAl is superior to all other conventional titanium alloys and, on a specific basis, is frequently 5 superior to nickel alloys. For this reason, gamma TiAl alloys have been the subject of intense research as a replacement for nickel alloys in various aerospace applications. for example turbine blades.
Several characteristics of gamma TiAl have thus far prevented its utilization in the aerospace industry These include poor room temperature ductility, low fracture toughness, and low oxidation resistance when compared with nickel base superalloys 5 The goal of most recent research has been to improve these properties to the degree
which would allow for the successful substitution of relatively dense nickel superalloys with low density gamma TiAl alloys.
5
The stoichiometric ratio of gamma TiAl can vary over a range without varying its crystal structure. Between about SO and 60 atom percent, the compound can exist as a single phase material having the LI o, known as the gamma phase. Between
10 approximately 35 and SO atom percent, the material will consist of a two phase mixture
containing both the Ll0 face centered tetragonal gamma phase and the hexagonal DO .
alpha-two (α ) phase, consisting of the formula Ti3Al. Current gamma alloys are, in
1 fact, two phase mixtures consisting of α-> and γ which have been found to have a more
desirable combination of strength and ductility than true single phase γ alloys. Heat
treatment of these alloys can result in a substantial change in the morphology and
20 distribution of the two phases, resulting in a considerable range in mechanical properties. Additional alloying with other elements can further modify the mechanical
properties.
There has been considerable research devoted to improving the mechanical properties of γ TiAl alloys. Publications describing such research include a review
paper Young- Won Kim, Intermetallic Alloys Based on Gamma Titamum-Alumimde - ° JOM, (1989), pg. 24. A second review paper has been published by Shih-Chin Huang and Donald S Shi , Microstructure-Property Correlation in TiAl-Base Alloys, in Microstructure-Property Relationships in Titanium Aluminides and Alloys, ed Y W
35 Kim and R.R. Boyer, TMS, (1991) Additionally, there exists a number of patents describing alloy development of γ TiAl alloys U S Patents 5,213,635 to Huang, 5.045.406 to Huang, 4.879.092 to Huang, 5,080.860 to Huang, 4,836,983 to Huang
and Gigliotti, and U.S. Patent 4,983,357 to Mitao et. al are representative of recent patents in which ternary and quaternary additions have been added to TiAl for the 5 purpose of improving mechanical properties.
x 0 SUMMARY OF THE IN VENTION
The present invention provides a gamma titanium aluminide alloy consisting essentially of the formula Ti-Al1CrbNbcSid, where "a" , "b", "c" and "d" are in atomic 15 percent, "a" ranges from about 44 to about 48, "b" ranges from about 2 to about 6; "c" ranges from about 2 to about 6 and "d" ranges from about 0.5 to about 1.0
In addition, the invention provides a process for casting a gamma titanium
20 aluminide alloy comprising the steps of: (a) forming a melt of a gamma titanium aluminide alloy consisting essentially of the formula Ti-Al,Cr*>NbcSid, where "a" , "b",
"c" and "d" are in atomic percent, "a" ranges from about 44 to about 48, "b" ranges
25 from about 2 to about 6, "c" ranges from about 2 to about 6 and "d" ranges from about 0.5 to about 1.0; and (b) casting the melt.
Levels of aluminum above 48 at% range result in reduced yield strength and the
30 tendency to form only single phase gamma microstructures. Aluminum levels below
44 at% tend to result in low plastic elongation during tensile deformation. Levels of
Cr at about the 2 at% range tend to boost tensile ductility; but higher levels tend to
- -> embrittle the material Niobium is generally beneficial to creep strength and oxidation but is prone to segregation at levels above about 6 at% In addition, niobium levels above about 6 at% increase alloy density and cost, while niobium levels below about 2
4 at % are generally insufficient to produce the improved oxidation and creep propeπies exhibited by alloys of the invention. Si levels above about 1 at% tend to result in
5 reduced oxidation resistance.
The melt can be formed using standard titanium alloy melt practice, including that of induction melting in an inert atmosphere or vacuum. Adequate clean melt
10 practice must be observed to limit contamination of impurities such as oxygen, nitrogen, and carbon to levels of less than about 2000 ppm oxygen, 500 ppm nitrogen, and 1000 ppm carbon which can embrittle the alloy
15
BRIEF DESCRIPTION OF THE DRAWINGS
The invention will be more fully understood and further advantages will become apparent when reference is had to the following detailed description and the accompanying drawings, in which: 20
FIG. 1 is a graph depicting the ultimate tensile strength and tensile elongation
measured at 760°C for alloys cast in accordance with the invention
25 DESCRD7TION OF THE PREFERRED EMBODIMENTS
It is known that, except for its brittleness, the intermetallic compound gamma
TiAl would have many uses in industry, owing to its light weight, high strength at high
30 temperatures and relatively low cost. It has also been recognized that cast gamma
TiAl suffers from a number of problems, including brittleness and low strength of the castings Another problem with cast gamma TiAl is low fluidity in the molten state
- -1 thereof This condition prevents adequate filling in castings, such as automobile turbocharger turbine wheels, which contain fine detail and shaφ angle
The present invention provides a gamma titanium aluminide alloy consisting essentially of the formula Ti-Al,CrbNbeSid, where "a" , "b", "c" and "d" are
5 in atomic percent, "a" ranges from about 44 to about 48, "b" ranges from about 2 to about 6; "c" ranges from about 2 to about 6 and "d" ranges from about 0.5 to about
1.0.
- 0 The gamma titanium aluminide alloy of the invention can be cast by a process comprising the steps of forming a melt of the alloy and casting it into a mold Castings
containing fine details and sharp angle are readily filled by the molten alloy, and the i c ultimate strength and tensile elongation of the alloy is increased.
Levels of aluminum above 48 at% range result in reduced yield strength and the
tendency to form only single phase gamma microstructures. Aluminum levels below 0 44 at% tend to result in low plastic elongation during tensile deformation. Levels of
Cr at about the 2 at% range tend to boost tensile ductility, but higher levels tend to embrittle the material. Niobium is generally beneficial to creep strength and oxidation but is prone to segregation at levels above about 6 at% In addition, niobium levels above about 6 at% increase alloy density and cost, while niobium levels below about 2 at % are generally insufficient to produce the improved oxidation and creep properties exhibited by alloys of the invention. Si levels above about 1 at% tend result in reduced 30 oxidation resistance.
The melt can be formed using standard titanium alloy melt practice, including 35 that of induction melting in an inert atmosphere or vacuum Adequate clean melt practice must be observed to limit contamination of impuπties such as oxygen.
nitrogen, and carbon to levels of less than about 2000 ppm oxygen, 500 ppm nitrogen, and 1000 ppm carbon which can embrittle the alloy
The improvement in properties and castability of the gamma titanium aluminide alloy of the invention is illustrated by the following examples, which are presented to provide a more complete understanding of the invention. The specific techniques,
conditions, materials, proportions and reported data set forth to illustrate the principles
and practice of the invention are exemplary and shall not be construed as limiting the
scope of the invention.
EXAMPLES 1-9
Individual melts were prepared to contain titanium and aluminum in various binary stoichiometric rations approximating TiAl with various additions. All compositions are listed in atomic percent. Variations of Cr and Nb were performed
between 2 and 6 % while holding silicon constant at 0.5 %. Variations in silicon of between 0 and 1.0 % were made holding aluminum, chromium, and niobium constant at 46Al-2Cr-2Nb. Samples were cast into graphite test bar molds and were HIPed for
8 hr. at 30 ksi pressure at 1250°C, followed by a furnace cool from the HIP unit
Button head tensile bars were then machined from the HIP test bar blanks and yield
strength, ultimate strength and tensile elongation were measured at 760°C test
temperature.
From the test data included in Table I, it is evident that the 46Al-2Cr-2Nb alloy containing 1 OSi evidenced a superior combination of ultimate strength and tensile elongation, as compared with the alloys containing no silicon or 0 5 Si This improved combination of strength and elongation is further evidenced by Figure 1 which plots
the ultimate tensile strength and tensile elongation measured at 760°C. In this figure,
properties increase along the diagonal away from the origin. It is clear from the plot that the 46Al-2Cr-Nb-l OSi alloy evidenced a superior combination of strength and
toughness.
Table I
Example Nominal YS( si) UTS(kii) El(%) Number Composition (At )
1 4 Al-2Cr-4Nb-0.5Si 46Al-2Cr-4Nb-0.5Sι 2 46Al-2Cr-6Nb-0.5Si 46Al-2Cr-6Nb-0.5Si 3 46Al-4Cr-2Nb-0.5Si 46Al-4Cr-2Nb-0.5Si 4 46Al**6Cr-2Nb-0.5Si
5 48Al-2Cr-2Nb-0.5Si
6 48Al-2Cr-4Nb-0.5Si 48Al-2Cr-4Nb-0.5Si
7 44Al-2Cr-2Nb-0.5Si 8 46Al-2Cr-2Nb-1.0Si 46Al-2Cr-2Nb-1.0Si 9 46Al-2Cr-2Nb-0.5Si 46Al-2Cr-2Nb-0.5Si 10 46Al-2Cr-2Nb 46Al-2Cr-2Nb
Having thus described the invention in rather full detail, it will be understood that such detail need not be strictly adhered to but that various changes and
modifications may suggest themselves to one skilled in the art, all falling within the scope of the present invention as defined by the subjoined claims.
Claims
What is claimed is:
1 A composition consisting essentially of the formula Ti-Al.CrbNbeSid, where "a" , "b", "c" and "d" are in atomic percent, "a" ranges from about 44 to about 48, "b" ranges from about 2 to about 6; "c" ranges from about 2 to about 6 and "d" ranges o from about 0.5 to about 1.0.
2. A composition as recited by claim 1, wherein "a" is 46.
3. A composition as recited by claim 1, wherein "a" is 48, "b" is 2 and "c" is 2. 5 4. A composition, as recited by claim 1, wherein "a" is 48, "b" is 2 and "c" is 4
0
5
0
5
Applications Claiming Priority (2)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| US41223795A | 1995-03-28 | 1995-03-28 | |
| US08/412,237 | 1995-03-28 |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| WO1996030552A1 true WO1996030552A1 (en) | 1996-10-03 |
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Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| PCT/US1996/003850 WO1996030552A1 (en) | 1995-03-28 | 1996-03-22 | Castable gamma titanium-aluminide alloy containing niobium, chromium and silicon |
Country Status (1)
| Country | Link |
|---|---|
| WO (1) | WO1996030552A1 (en) |
Cited By (10)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| 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 |
| US8858697B2 (en) | 2011-10-28 | 2014-10-14 | General Electric Company | Mold compositions |
| US8906292B2 (en) | 2012-07-27 | 2014-12-09 | General Electric Company | Crucible and facecoat compositions |
| US8932518B2 (en) | 2012-02-29 | 2015-01-13 | General Electric Company | Mold and facecoat compositions |
| US8992824B2 (en) | 2012-12-04 | 2015-03-31 | General Electric Company | Crucible and extrinsic facecoat compositions |
| US9011205B2 (en) | 2012-02-15 | 2015-04-21 | General Electric Company | Titanium aluminide article with improved surface finish |
| 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 |
| US9592548B2 (en) | 2013-01-29 | 2017-03-14 | General Electric Company | Calcium hexaluminate-containing mold and facecoat compositions and methods for casting titanium and titanium aluminide alloys |
| US10391547B2 (en) | 2014-06-04 | 2019-08-27 | General Electric Company | Casting mold of grading with silicon carbide |
Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US5196162A (en) * | 1990-08-28 | 1993-03-23 | Nissan Motor Co., Ltd. | Ti-Al type lightweight heat-resistant materials containing Nb, Cr and Si |
| EP0545614A1 (en) * | 1991-12-02 | 1993-06-09 | General Electric Company | Gamma titanium alloys modified by chromium, niobium, and silicon |
| EP0581204A1 (en) * | 1992-07-28 | 1994-02-02 | ABBPATENT GmbH | Heat-resistant material |
| JPH06240428A (en) * | 1993-02-17 | 1994-08-30 | Sumitomo Metal Ind Ltd | Production of ti-al intermetallic compound base alloy |
| JPH06299276A (en) * | 1993-04-09 | 1994-10-25 | Daido Steel Co Ltd | Ti-al alloy parts |
-
1996
- 1996-03-22 WO PCT/US1996/003850 patent/WO1996030552A1/en active Application Filing
Patent Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US5196162A (en) * | 1990-08-28 | 1993-03-23 | Nissan Motor Co., Ltd. | Ti-Al type lightweight heat-resistant materials containing Nb, Cr and Si |
| EP0545614A1 (en) * | 1991-12-02 | 1993-06-09 | General Electric Company | Gamma titanium alloys modified by chromium, niobium, and silicon |
| EP0581204A1 (en) * | 1992-07-28 | 1994-02-02 | ABBPATENT GmbH | Heat-resistant material |
| JPH06240428A (en) * | 1993-02-17 | 1994-08-30 | Sumitomo Metal Ind Ltd | Production of ti-al intermetallic compound base alloy |
| JPH06299276A (en) * | 1993-04-09 | 1994-10-25 | Daido Steel Co Ltd | Ti-al alloy parts |
Non-Patent Citations (2)
| Title |
|---|
| CHEMICAL ABSTRACTS, vol. 122, no. 12, 20 March 1995, Columbus, Ohio, US; abstract no. 139960, NODA, TOSHIHARU ET AL: "Titanium-aluminum alloy products with good strength and heat resistance" XP002004165 * |
| PATENT ABSTRACTS OF JAPAN vol. 018, no. 632 (C - 1280) 2 December 1994 (1994-12-02) * |
Cited By (12)
| 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 |
| US9802243B2 (en) | 2012-02-29 | 2017-10-31 | General Electric Company | Methods for casting titanium and titanium aluminide alloys |
| 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 |
| US9803923B2 (en) | 2012-12-04 | 2017-10-31 | General Electric Company | Crucible and extrinsic facecoat compositions and methods for melting titanium and titanium aluminide alloys |
| US9592548B2 (en) | 2013-01-29 | 2017-03-14 | General Electric Company | Calcium hexaluminate-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 |
| 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 |
| US10391547B2 (en) | 2014-06-04 | 2019-08-27 | General Electric Company | Casting mold of grading with silicon carbide |
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