U.S. patent application number 10/743604 was filed with the patent office on 2005-06-23 for directionally solidified eutectic superalloys for elevated temperature applications.
Invention is credited to Gigliotti, Michael Francis Xavier JR., Henry, Michael Francis, Jackson, Melvin Robert, Zhao, Ji-Cheng.
Application Number | 20050135962 10/743604 |
Document ID | / |
Family ID | 34678690 |
Filed Date | 2005-06-23 |
United States Patent
Application |
20050135962 |
Kind Code |
A1 |
Henry, Michael Francis ; et
al. |
June 23, 2005 |
Directionally solidified eutectic superalloys for elevated
temperature applications
Abstract
A measurement device for measuring and displaying a physical
quantity such as a heartbeat, an atmospheric pressure or
temperature, or the like, includes a clock for counting time, a
physical quantity measuring device for measuring the physical
quantity to be displayed, a processor for determining a plurality
of values based on the measured physical quantity and the counted
time, a first display for simultaneously displaying the plurality
of values and a second display for magnifying at least one of the
values and displaying the magnified value.
Inventors: |
Henry, Michael Francis;
(Niskayuna, NY) ; Jackson, Melvin Robert;
(Niskayuna, NY) ; Zhao, Ji-Cheng; (Latham, NY)
; Gigliotti, Michael Francis Xavier JR.; (Scotia,
NY) |
Correspondence
Address: |
Paul J. DiConza
GE Global Research Center
1 Research Circle, K-1 3A60
Niskayuna
NY
12309
US
|
Family ID: |
34678690 |
Appl. No.: |
10/743604 |
Filed: |
December 22, 2003 |
Current U.S.
Class: |
420/448 ;
148/410; 148/428 |
Current CPC
Class: |
C22C 19/057
20130101 |
Class at
Publication: |
420/448 ;
148/410; 148/428 |
International
Class: |
C22C 019/05 |
Goverment Interests
[0001] The U.S. Government may have certain rights in the present
invention pursuant to U.S. Air Force Prime Contract No.
F33615-98-C-2807, Subcontract No. 01-S441-58-05-C1.
Claims
What is claimed is:
1. An alloy, comprising: a Ni-based matrix comprising, on a weight
basis, about 5-7% Al, up to about 0.025% B, about 0.1-0.5% C, about
3-13% Co, about 2-7% Cr, up to about 5% Mo, up to about 1% Nb,
about 2-7% Re, about 10-13% Ta, up to about 1.8% Ti, about 4-7% W,
up to about 1% V, up to about 0.2% Hf, and up to about 0.1% Zr, the
balance being essentially Ni and incidental impurities.
2. The alloy of claim 1, wherein the Ni-based matrix comprises, on
a weight basis, about 0.8-1.8% Ti.
3. The alloy of claim 1, wherein the Ni-based matrix comprises, on
a weight basis, about 5-6% Al, up to about 0.01% B, about 0.15-0.3%
C, about 11-13% Co, about 3-5% Cr, about 0.8-1.8% Mo, about
4.5-5.6% Re, about 10-12% Ta, about 5-6% W, up to about 1% V, up to
about 0.2% Hf, and up to about 0.1% Zr, the balance being
essentially Ni and incidental impurities.
4. The alloy of claim 1, wherein the Ni-based matrix comprises, on
a weight basis, about 5-6.1% Al, up to about 0.01% B, about
0.15-0.3%C, about 6.25-7.25% Co, about 2-3.1% Cr, up to about 1.1%
Mo, about 0.1-1% Nb, about 4.75-5.9% Re, about 9-11% Ta, about
0.5-1.5% Ti, about 5.5-6.8% W, up to about 1% V, up to about 0.2%
Hf, and up to about 0.1% Zr, the balance being essentially Ni and
incidental impurities.
5. The alloy of claim 1, further comprising an aligned eutectic
reinforcing fibrous phase disposed within the Ni-based matrix, the
aligned eutectic reinforcing fibrous phase comprising a
carbide.
6. The alloy of claim 5, wherein the carbide comprises
substantially TaC.
7. A directionally solidified eutectic superalloy, comprising: a
Ni-based matrix comprising, on a weight basis, about 5-7% Al, up to
about 0.025% B, about 0.1-0.5% C, about 3-13% Co, about 2-7% Cr, up
to about 5% Mo, up to about 1% Nb, about 2-7% Re, about 10-13% Ta,
up to about 1.8% Ti, about 4-7% W, up to about 1% V, up to about
0.2% Hf, and up to about 0.1% Zr, the balance being essentially Ni
and incidental impurities; and an aligned eutectic reinforcing
fibrous phase disposed within the Ni-based matrix, the aligned
eutectic reinforcing fibrous phase comprising a carbide.
8. The directionally solidified eutectic superalloy of claim 7,
wherein the Ni-based matrix comprises, on a weight basis, about
0.8-1.8% Ti.
9. The directionally solidified eutectic superalloy of claim 7,
wherein the Ni-based matrix comprises, on a weight basis, about
5-6% Al, up to about 0.01% B, about 0.15-0.3% C, about 11-13% Co,
about 3-5% Cr, about 0.8-1.8% Mo, about 4.5-5.6% Re, about 10-12%
Ta, about 5-6% W, up to about 1% V, up to about 0.2% Hf. and up to
about 0.1% Zr, the balance being essentially Ni and incidental
impurities.
10. The directionally solidified eutectic superalloy of claim 7,
wherein the Ni-based matrix comprises, on a weight basis, about
5-6.1% Al, up to about 0.01% B, about 0.15-0.3%C, about 6.25-7.25%
Co, about 2-3.1% Cr, up to about 1.1%-Mo, about 0.1-1% Nb, about
4.75-5.9% Re, about 9-11% Ta, about 0.5-1.5% Ti, about 5.5-6.8% W,
up to about 1% V, up to about 0.2% Hf, and up to about 0.1% Zr, the
balance being essentially Ni and incidental impurities.
11. The directionally solidified eutectic superalloy of claim 7,
wherein the carbide comprises substantially TaC.
12. An article of manufacture comprising an alloy, the alloy
comprising: a Ni-based matrix comprising, on a weight basis, about
5-7% Al, up to about 0.025% B, about 0.1-0.5% C, about 3-13% Co,
about 2-7% Cr, up to about 5% Mo, up to about 1% Nb, about 2-7% Re,
about 10-13% Ta, up to about 1.8% Ti, about 4-7% W, up to about 1%
V, up to about 0.2% Hf, and up to about 0. 1% Zr, the balance being
essentially Ni and incidental impurities.
13. The article of manufacture of claim 12, wherein the Ni-based
matrix comprises, on a weight basis, about 0.8-1.8% Ti.
14. The article of manufacture of claim 12, wherein the Ni-based
matrix comprises, on a weight basis, about 5-6% Al, up to about
0.01% B, about 0.15-0.3% C, about 11-13% Co, about 3-5% Cr, about
0.8-1.8% Mo, about 4.5-5.6% Re, about 10-12% Ta, about 5-6% W, up
to about 1% V, up to about 0.2% Hf, and up to about 0.1% Zr, the
balance being essentially Ni and incidental impurities.
15. The article of manufacture of claim 12, wherein the Ni-based
matrix comprises, on a weight basis, about 5-6.1% Al, up to about
0.01% B, about 0.15-0.3% C, about 6.25-7.25% Co, about 2-3.1% Cr,
up to about 1.1% Mo, about 0.1-1% Nb, about 4.75-5.9% Re, about
9-11% Ta, about 0.5-1.5% Ti, about 5.5-6.8% W, up to about 1% V, up
to about 0.2% Hf, and up to about 0.1% Zr, the balance being
essentially Ni and incidental impurities.
16. The article of manufacture of claim 12, wherein the alloy
further comprises an aligned eutectic reinforcing fibrous phase
disposed within the Ni-based matrix, the aligned eutectic
reinforcing fibrous phase comprising a carbide.
17. The article of manufacture of claim 16, wherein the carbide
comprises substantially TaC.
18. The article of manufacture of claim 12, wherein the article of
manufacture comprises a gas turbine engine component.
19. The article of manufacture of claim 18, wherein the gas turbine
engine component comprises a turbine airfoil.
20. An article of manufacture comprising a directionally solidified
eutectic superalloy, the directionally solidified eutectic
superalloy comprising: a Ni-based matrix comprising, on a weight
basis, about 5-7% Al, up to about 0.025% B, about 0.1-0.5% C, about
3-13% Co, about 2-7% Cr, up to about 5% Mo, up to about 1% Nb,
about 2-7% Re, about 10-13% Ta, up to about 1.8% Ti, about 4-7% W,
up to about 1% V, up to about 0.2% Hf. and up to about 0.1% Zr, the
balance being essentially Ni and incidental impurities; and an
aligned eutectic reinforcing fibrous phase disposed within the
Ni-based matrix, the aligned eutectic reinforcing fibrous phase
comprising a carbide.
21. The article of manufacture of claim 20, wherein the Ni-based
matrix comprises, on a weight basis, about 0.8-1.8% Ti.
22. The article of manufacture of claim 20, wherein the Ni-based
matrix comprises, on a weight basis, about 5-6% Al, up to about
0.01% B, about 0.15-0.3% C, about 11-13% Co, about 3-5% Cr, about
0.8-1.8% Mo, about 4.5-5.6% Re, about 10-12% Ta, about 5-6% W, up
to about 1% V, up to about 0.2% Hf. and up to about 0.1% Zr, the
balance being essentially Ni and incidental impurities.
23. The article of manufacture of claim 20, wherein the Ni-based
matrix comprises, on a weight basis, about 5-6.1% Al, up to about
0.01% B, about 0.15-0.3% C, about 6.25-7.25% Co, about 2-3.1% Cr,
up to about 1.1% Mo, about 0.1-1% Nb, about 4.75-5.9% Re, about
9-11% Ta, about 0.5-1.5% Ti, about 5.5-6.8% W, up to about 1% V, up
to about 0.2% Hf, and up to about 0.1% Zr, the balance being
essentially Ni and incidental impurities.
24. The article of manufacture of claim 20, wherein the carbide
comprises substantially TaC.
25. The article of manufacture of claim 20, wherein the article of
manufacture comprises a gas turbine engine component.
26. The article of manufacture of claim 25, wherein the gas turbine
engine component comprises a turbine airfoil.
Description
FIELD OF THE INVENTION
[0002] The present invention relates generally to directionally
solidified eutectic superalloys for elevated temperature
applications, such as turbine airfoil applications and the like.
More specifically, the present invention relates to directionally
solidified eutectic nickel (Ni)-based superalloys comprising a
matrix containing an aligned carbide reinforcing fibrous phase,
such as an aligned tantalum carbide (TaC) reinforcing fibrous
phase. The aligned carbide reinforcing fibrous phase provides
preferential strengthening in one direction, resulting in enhanced
elevated temperature strength, creep resistance, oxidation
resistance, and corrosion resistance properties.
BACKGROUND OF THE INVENTION
[0003] Directionally solidified eutectic Ni-based superalloys, such
as NiTaC-14B and the like, are well known to those of ordinary
skill in the art. For example, NiTaC-14B has been optimized for use
in turbine airfoil applications due to its favorable elevated
temperature strength, creep resistance, oxidation resistance, and
corrosion resistance properties.
[0004] U.S. Pat. No. 3,904,402 (Smashey) broadly discloses Ni-based
alloys containing rhenium (Re) and a carbide reinforcing fibrous
phase exhibiting favorable elevated temperature strength, creep
resistance, oxidation resistance, and corrosion resistance
properties. Smashey discloses the preferred use of 4-7 wt. %
vanadium (V) for enhancement of the carbide reinforcing fibrous
phase, as well as matrix strengthening. Smashey discloses the
limited use of molybdenum (Mo), up to about 3 wt. %, however, the
use of Mo is preferably omitted. Smashey also discloses the limited
use of tungsten (W), between about 2-4 wt. %.
[0005] U.S. Pat. No. 4,284,430 (Henry) discloses a unidirectionally
solidified anisotropic metallic composite body exhibiting
transverse ductility and elevated temperature strength properties
comprising a eutectic Ni-based superalloy containing about 2-9 wt.
% Re, less than about 0.8 wt. % titanium (Ti), at least about 2 wt.
% Mo, and less than about 1 wt. % V. Embedded in the matrix is an
aligned carbide reinforcing fibrous phase, preferably a
predominantly TaC reinforcing fibrous phase. Specifically, the
Ni-based alloys contain about 2-9 wt. % Re, about 0-0.8 wt. % Ti,
about 0-10 wt. % chromium (Cr), about 0-10 wt. % aluminum (Al),
about 3-15 wt. % tantalum (Ta), about 0.1-1 wt. % carbon (C), about
0-10 wt. % cobalt (Co), about 0-10 wt. % W, about 0-1 wt. % V,
about 2-10 wt. % Mo, and about 0-3 wt. % niobium (Nb) (columbium
(Cb)), the balance being essentially Ni and incidental
impurities.
[0006] U.S. Pat. No. 4,292,076 (Gigliotti et al.) discloses a
unidirectionally solidified anisotropic metallic composite body
exhibiting transverse ductility and elevated temperature strength
properties comprising a eutectic Ni-based refractory
metal-monocarbide-reinforced superalloy containing boron (B). A
reinforcing fibrous phase of the eutectic Ni-based superalloy is an
aligned carbide reinforcing fibrous phase, preferably one selected
from the monocarbides of Ti, V, Nb (Cb), zirconium (Zr), hafnium
(Hf), Ta, and alloys or mixtures thereof. Specifically, the
Ni-based alloys contain about 0.5-7 wt. % Re, less than about 0.8
wt. % Ti, and at least an amount in excess of an impurity amount of
B. Embedded in the matrix is an aligned carbide reinforcing fibrous
phase, preferably a predominantly TaC reinforcing fibrous phase.
These Ni-based alloys exhibit favorable elevated temperature
strength, creep resistance, oxidation resistance, and corrosion
resistance properties. More specifically, the Ni-based alloys
contain about 0.5-7 wt. % Re, less that about 0.8 wt. % Ti, about
0.001-0.02 wt. % B, about 2-8 wt. % Cr, about 4-7 wt. % Al, about
5-13 wt. % Ta, about 0. 1-0.7 wt. % C, less than about 5 wt. % Co,
less than about 6 wt. % W, less than about 0.2 wt. % V, less than
about 5 wt. % Mo, less than about 1 wt. % Nb (Cb), less than about
0.15 wt. % Hf, and less than about 0.15 wt. % Zr, the balance being
essentially Ni and incidental impurities.
[0007] Conventional Ni-based superalloys lose strength at very high
temperatures due to the fact that the gamma prime strengthening
phase begins to dissolve. The addition of an aligned carbide
reinforcing fibrous phase provides an important strengthening
mechanism in this temperature regime. This is especially important
for turbine airfoil applications and the like. The directionally
solidified eutectic Ni-based superalloys described above, however,
still do not demonstrate the elevated temperature strength, creep
resistance, oxidation resistance, and corrosion resistance
properties desired at these very high temperatures, performing
better than their single crystal counterparts in a temperature
regime of only about 100 degrees F. greater. More benefit is
required given the cost of producing directionally solidified
eutectic Ni-based superalloys (due to their relatively slow
directional solidification rates) versus their single crystal
counterparts. Thus, what is needed is a directionally solidified
eutectic Ni-based superalloy that demonstrates enhanced elevated
temperature strength, creep resistance, oxidation resistance, and
corrosion resistance properties.
BRIEF SUMMARY OF THE INVENTION
[0008] In one embodiment of the present invention, an alloy
includes a Ni-based matrix comprising, on a weight basis, about
5-7% Al, up to about 0.025% B, about 0.1-0.5% C, about 3-13% Co,
about 2-7% Cr, up to about 5% Mo, up to about 1% Nb, about 2-7% Re,
about 10-13% Ta, up to about 1.8% Ti, about 4-7% W, up to about 1%
V, up to about 0.2% Hf, and up to about 0.1% Zr, the balance being
essentially Ni and incidental impurities.
[0009] In another embodiment of the present invention, a
directionally solidified eutectic superalloy includes a Ni-based
matrix comprising, on a weight basis, about 5-7% Al, up to about
0.025% B, about 0.1-0.5% C, about 3-13% Co, about 2-7% Cr, up to
about 5% Mo, up to about 1% Nb, about 2-7% Re, about 10-13% Ta, up
to about 1.8% Ti, about 4-7% W, up to about 1% V, up to about 0.2%
Hf. and up to about 0.1% Zr, the balance being essentially Ni and
incidental impurities; and an aligned eutectic reinforcing fibrous
phase disposed within the Ni-based matrix, the aligned eutectic
reinforcing fibrous phase comprising a carbide.
[0010] In a further embodiment of the present invention, an article
of manufacture comprising an alloy includes a Ni-based matrix
comprising, on a weight basis, about 5-7% Al, up to about 0.025% B,
about 0.1-0.5% C, about 3-13% Co, about 2-7% Cr, up to about 5% Mo,
up to about 1% Nb, about 2-7% Re, about 10-13% Ta, up to about 1.8%
Ti, about 4-7% W, up to about 1% V, up to about 0.2% Hf. and up to
about 0.1% Zr, the balance being essentially Ni and incidental
impurities.
[0011] In a still further embodiment of the present invention, an
article of manufacture comprising a directionally solidified
eutectic superalloy includes a Ni-based matrix comprising, on a
weight basis, about 5-7% Al, up to about 0.025% B, about 0.1-0.5%
C, about 3-13% Co, about 2-7% Cr, up to about 5% Mo, up to about 1%
Nb, about 2-7% Re, about 10-13% Ta, up to about 1.8% Ti, about 4-7%
W, up to about 1% V, up to about 0.2% Hf. and up to about 0.1% Zr,
the balance being essentially Ni and incidental impurities; and an
aligned eutectic reinforcing fibrous phase disposed within the
Ni-based matrix, the aligned eutectic reinforcing fibrous phase
comprising a carbide.
BRIEF DESCRIPTION OF THE DRAWINGS
[0012] FIG. 1 is a plot of the temperature in the liquid in front
of the solid/liquid interface for several variations of furnace
parameters related to several directional solidification runs;
[0013] FIG. 2 is a photograph of a microstructure produced using
the compositions and methods of the present invention, specifically
NiTaC-14B with a light gamma prime etch showing the size of the TaC
fibers and the matrix gamma and gamma prime phases;
[0014] FIG. 3 is a photograph of a microstructure produced using
the compositions and methods of the present invention, specifically
NiTaC-14B with a deep gamma prime etch showing the TaC fiber
morphology in the grain centers;
[0015] FIG. 4 is a photograph of a microstructure produced using
the compositions and methods of the present invention, specifically
NiTaC-14B with a medium gamma prime etch showing the TaC fiber
morphology in the grain boundaries;
[0016] FIG. 5 is a photograph of a microstructure produced using
the compositions and methods of the present invention, specifically
NiTaC-14B with a very deep gamma prime etch showing the high aspect
ratio of the TaC fibers;
[0017] FIG. 6 is a plot of the cyclic oxidation results associated
with the compositions of the present invention using 61-min cycles
to 982 degrees C.;
[0018] FIG. 7 is a plot of the creep-rupture results associated
with the compositions of the present invention for testing at 871
degrees C. (1600 degrees F.);
[0019] FIG. 8 is a plot of the creep-rupture results associated
with the compositions of the present invention for testing at 982
degrees C. (1800 degrees F.);
[0020] FIG. 9 is a plot of the creep curves for the compositions of
the present invention for testing at 871 degrees C.;
[0021] FIG. 10 is a plot of the creep curves for the compositions
of the present invention for testing at 982 degrees C.; and
[0022] FIG. 11 is a Larson-Miller parameter plot for
time-to-failure in the creep-rupture tests described above.
DETAILED DESCRIPTION OF THE INVENTION
[0023] As described above, the elevated temperature viability of
directionally solidified eutectic Ni-based superalloys, such as
NiTaC-14B and the like, has been established, however, two key
issues remain. First, the relatively low value of maximum
directional solidification rate makes the cost of producing
components, such as turbine airfoils and the like, from such
directionally solidified eutectic Ni-based superalloys too high.
Second, the properties of NiTaC-14B and the like still fall short
of assumed goals. For example, in some applications it is desired
that a directionally solidified eutectic Ni-based superalloy
demonstrate elevated temperature strength, creep resistance,
oxidation resistance, and corrosion resistance properties similar
to SC RenN5 in a temperature regime of about 200 degrees F.
greater. In general, NiTaC-14B demonstrates a good balance of
elevated temperature properties and has been shown to be superior
to CoTaC, arts and .gamma./.gamma.'-.delta., and
.gamma./.gamma.'-Mo systems.
[0024] Here three alternative directionally solidified eutectic
Ni-based superalloys are presented. The compositions of these three
directionally solidified eutectic Ni-based superalloys are provided
in Table 1.
1TABLE 1 Directionally Solidified Eutectic Ni-Based Superalloy
Compositions Weight Percent Element NiTaC-14B AG207 AG208 AG209 Al
5.300 5.917 5.494 5.604 B 0.015 0.004 0.004 0.000 C 0.430 0.270
0.270 0.270 Co 3.800 7.158 11.944 6.764 Cr 3.800 6.681 4.013 2.561
Mo 3.000 1.432 1.338 0.580 Nb 0.000 0.000 0.000 0.534 Ni 61.555
60.537 55.217 61.102 Re 6.400 2.863 5.160 5.314 Ta 11.400 10.366
11.065 10.018 Ti 0.000 0.000 0.000 1.069 W 4.300 4.772 5.494
6.184
[0025] AG207 is designed to yield TaC fibers in a matrix of RenN5,
AG208 is designed to yield TaC fibers in a matrix of RenN6, and
AG209 is designed to yield TaC fibers in a matrix of CMSX-10Ri. All
three compositions are designed to be slightly hypereutectic so as
to provide good, aligned fibers when the exact eutectic composition
is not known. In general, the compositions may be described as:
AG207 (Ni-5.9A1-0.004B-0.27C-7.2Co-6.7Cr-1.4Mo-2.9Re-10.4Ta-4.8W by
wt. %), AG208
(Ni-5.5A1-0.004B-0.27C-11.9Co-4Cr-1.3Mo-5.2Re-11.1Ta-5.5W by wt.
%), and AG209
(Ni-5.6A1-0.27C-6.8Co-2.6Cr-0.6Mo-0.5Nb-5.3Re-10Ta-1.1Ti-6.- 2W by
wt. %).
[0026] A furnace, such as a modified Bridgman apparatus or the
like, is used to perform directional solidification. For example,
the furnace may use a gradient wound alumina-tube furnace as a
heating element with a water-cooled chill on which an ingot sits
during withdrawal.
[0027] A total of eighteen directional solidification runs were
conducted using the compositions and equipment described above. The
conditions and resulting microstructures of the eighteen ingots are
provided in Table 2.
2TABLE 2 Conditions and Resulting Microstructures of Directionally
Solidified Ingots DS Run Ingot Diameter No. Alloy (mm) DS Rate
(cm/hr) Structure 1 NiTaC-14B 9.5 0.64 dendritic 2 NiTaC-14B 9.5
1.27 cellular 3 NiTaC-14B 9.5 0.64 cellular 4 NiTaC-14B 9.5 1.27
cellular 5 NiTaC-14B 22.2 0.64 cellular 6 NiTaC-14B 22.2 0.64
cellular 7 AG208 9.5 0.64 fibrous 8 AG207 9.5 0.64 fibrous 9 AG209
9.5 0.64 cellular 10 NiTaC-14B 22.2 0.64 fibrous 11 AG209 9.5 0.64
fibrous 12 AG207 22.2 0.64 fibrous 13 AG208 22.2 0.64 dendritic 14
AG208 22.2 0.64 dendritic 15 NiTaC-14B 22.2 0.64 fibrous 16 AG208
9.5 0.64 fibrous 17 AG209 9.5 0.64 N/A 18 NiTaC-14B 9.5 1.27
cellular
[0028] The first seven directional solidification runs produced an
unacceptable microstructure. Two additional ingots were processed
to measure the gradients in the liquid in front of the solid/liquid
interface. Thermocouples were immersed in the liquid in front of
the solid/liquid interface, lowered to just touch the solid/liquid
interface, and then raised up in several increments while measuring
temperature and position. These measurements were repeated for
several combinations of furnace control parameters. The results are
provided in FIG. 1. From these measurements, furnace parameters
were selected to maximize the gradient. In general, some of the 22
mm diameter ingots were run with a thermal gradient of about 55
degrees C./cm and some of the 22 mm diameter ingots were run with a
thermal gradient of about 100 degrees C./cm. Thermal gradients were
not measured for the 9.5 mm diameter ingots.
[0029] A good fibrous microstructure was obtained in at least one
ingot of each composition directionally solidified at 0.64 cm/hr.
The typical microstructures produced are shown in FIGS. 2-5 for
NiTaC-14B. FIG. 2, a cross-section perpendicular to the directional
solidification direction, was prepared with a light gamma prime
etch and shows the relative sizes of the TaC fibers, the
discontinuous gamma prime phase formed upon cooling, and the
continuous gamma phase. FIG. 3, a transverse view with a deep
matrix etch, shows the morphology of the TaC fibers, each of the
TaC fibers having a substantially square cross-sectional shape.
FIG. 4, a cross-section perpendicular to the directional
solidification direction, was prepared with a medium matrix etch
and shows that the morphology of the TaC fibers breaks down to
plate-like in the grain boundaries. FIG. 5, a cross-section
perpendicular to the directional solidification direction, was
prepared with a very deep matrix etch and shows the high aspect
ratio of the TaC fibers. Also visible are minor variations in the
cross-sectional size that likely result from local variations in
the solidification rate.
[0030] Ingots with good, aligned fibers were machined to produce
cyclic oxidation pins and creep-rupture bars. It should be noted
that a higher gradient may be required to produce an aligned
fibrous structure in AG208 and AG209 than is required in NiTaC-14B.
The machined cyclic oxidation pins each had a diameter of about 2.5
mm and a length of about 35 mm. The pins were cycled between room
temperature and about 982 degrees C. (1800 degrees F.) in a 61-min
cycle with 50 min in the 982 degrees C.-furnace and 11 min out of
the 982 degrees C.-furnace. The cyclic oxidation data are provided
in Table 3.
3TABLE 3 Cyclic Oxidation Results (61-Min Cycles to 982 Degrees C.)
NiTaC-14B NiTac-14B (pin 1) (pin 2) AG207 AG208 AG209 Wt. Wt. Wt.
Wt. Wt. Hrs Change Hrs Change Hrs Change Hrs Change Hrs Change
Cycl. (mg/cm.sup.2) Cycl. (mg/cm.sup.2) Cycl. (mg/cm.sup.2) Cycl.
(mg/cm.sup.2) Cycl. (mg/cm.sup.2) 22.4 0.35 22.4 0.32 27.5 0.39
27.5 0.31 25.4 0.45 53.9 0.54 53.9 0.51 51.9 0.39 51.9 0.31 47.8
0.64 82.4 0.54 82.4 0.54 77.3 0.55 77.3 0.38 73.2 0.64 107.8 0.67
107.8 1.02 101.7 0.39 101.7 0.38 148.4 0.55 125.1 0.73 125.1 0.76
170.8 0.47 170.8 0.46 197.2 0.79 197.2 0.86 269.4 0.31 269.4 0.61
296.9 0.98 296.9 1.08 349.7 0.47 349.7 0.54 366.0 0.76 366.0 0.67
448.4 0.55 448.4 0.77 466.7 0.38 466.7 -0.25 519.5 0.47 519.5 0.85
532.7 -0.35 532.7 -0.79 621.2 0.71 621.2 0.85 630.3 -0.79 630.3
-1.08 695.4 0.63 695.4 0.77 701.5 -1.08 701.5 -1.49 796.1 0.71
796.1 0.77 804.2 -1.17 804.2 -1.37 871.3 0.63 871.3 0.77 872.3
-1.78 872.3 -1.81 974.0 0.63 974.0 0.77 976.0 -2.73 976.0 -3.97
1048.2 0.71 1048.2 0.85 1047.2 -3.30 1047.2 -4.29 1145.8 0.79
1145.8 0.61 1139.7 -4.06 1139.7 -5.53 1204.8 0.79 1204.8 0.61
1219.0 -5.08 1219.0 -8.61 1278.0 0.79 1278.0 0.54 1315.6 -6.00
1315.6 -13.51 1353.2 0.71 1353.2 0.46 1384.7 -6.45 1384.7 -15.44
1462.0 -7.43 1462.0 -20.15 1535.2 -7.91 1535.2 -23.67 1632.8 -9.08
1632.8 -26.57 1707.0 -9.65 1707.0 -29.30 1804.6 -10.70 1804.6
-33.46 1879.8 -11.78 1879.8 -37.82 1976.4 -13.11 1976.4 -43.54
2050.6 -15.18 2050.6 -47.73 2151.3 -16.80 2151.3 -52.72 2226.5
-19.43 2226.5 -55.64 2302.8 -22.73 2302.8 -59.77 2380.0 -25.25
2380.0 -62.28 2478.6 -29.15 2478.6 -66.73 2602.7 -33.75 2602.7
-70.32 2701.3 -39.24 2701.3 -74.46 2775.5 -42.64 2775.5 -75.47
2875.1 -49.85 2875.1 -79.48 2970.7 -54.01 2970.7 -81.89 3049.0
-59.37 3049.0 -83.42 3125.2 -64.61 3125.2 -84.27 3223.9 -69.53
3223.9 -85.45 3319.4 -77.37 3319.4 -87.39 3393.6 -81.34 3393.6
-87.80 3470.9 -85.47 3470.9 -89.10 3572.6 -89.50 3572.6 -89.84
3641.7 -90.90 3641.7 -90.69 3740.3 -92.55 3740.3 -92.28 3820.6
-93.25 3820.6 -93.55 3919.3 -93.92 3919.3 -95.40 3990.4 -94.77
3990.4 -96.35 4092.1 -94.90 4092.1 -98.92 4166.3 -95.63 4166.3
-100.00 4267.0 -96.23 4267.0 -101.43
[0031] The data of Table 3 demonstrates that the cyclic oxidation
resistance of AG207 and AG208 is superior to that of NiTaC-14B. The
cyclic oxidation results are plotted in FIG. 6.
[0032] At least two creep-rupture tests were performed for each of
the alloys of the present invention. The duration of the creep
rupture tests ranged from about 22 hours to about 546 hours. The
results are provided in Table 4.
4TABLE 4 Creep Rupture Results Time Time Time Time Time Strain DS
to to to to to at Rate Temp. Stress 0.2% 0.5% 1.0% 2.0% Fail Fail
Alloy (cm/hr) (.degree. C.) (MPa) Env. (hr) (hr) (hr) (hr) (hr) (%)
AG207 0.64 871 455 air 1.2 9.0 18.9 33.5 109.1 17.1 AG207 0.64 982
283 air 0.9 6.7 15.3 21.3 22.2 3.2 AG208 0.64 871 455 air 2.1 17.5
41.3 92.1 545.6 24.1 AG208 0.64 982 283 air 1.3 17.5 62.2 101.9
177.4 15.4 AG209 0.64 871 455 air 27.3 56.0 99.7 159.2 414.0 17.4
AG209 0.64 982 283 air 4.6 20.7 61.5 142.7 222.5 17.7 NiTaC- 0.64
871 455 air 0.4 7.7 33.7 93.5 195.4 10.4 14B NiTaC- 0.64 982 283
air 0.2 3.8 22.3 94.2 126.1 12.0 14B NiTaC- 0.64 982 255 air 1.3
14.1 82.0 255.8 322.7 13.0 14B AG207 0.64 982 283 argon 1.3 6.0
18.0 31.0 49.9 13.3 AG207 0.64 1093 138 argon 9.6 25.6 42.8 57.6
61.3 12.6
[0033] A comparison of the creep-rupture results is shown in FIG. 7
for testing at 871 degrees C. (1600 degrees F.) and in FIG. 8 for
testing at 982 degrees C. (1800 degrees F.). The data of Table 4
demonstrates that the creep-resistance of AG208 and AG209 is
superior to that of NiTaC-14B. AG208 is the superior alloy at 871
degrees C./455 MPa (1600 degrees F./66 ksi) and AG209 is the
superior alloy at 982 degrees C./283 MPA (1800 degrees F./41 ksi).
The creep curves in air are shown in FIGS. 9 and 10 for the testing
at 871 degrees C. and 982 degrees C., respectively.
[0034] The data for the alloys of the present invention are
compared in FIG. 11 via a Larson-Miller parameter plot for
time-to-failure in the creep-rupture tests. In this construction,
the Larson-Miller parameter, LMP, is defined as:
LMP=T[20+log.sub.10(t.sub.f)], (1)
[0035] where T=temperature (K) and t.sub.f=time to fail (hr). FIG.
11 also contains the best fit line from data previously gathered
for NiTaC-14B and a mathematical construct that represents a 20
degrees C. increase above this data.
[0036] Although the present invention has been illustrated and
described with reference to preferred embodiments and examples
thereof, it will be readily apparent to those of ordinary skill in
the art that other embodiments and examples may perform similar
functions and/or achieve similar results. All such equivalent
embodiments and examples are within the spirit and scope of the
present invention and are intended to be covered by the following
claims.
* * * * *