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TECHNICAL PAPERS: Gas Turbines: Vehicular and Small Turbomachines

Selecting and Developing Advanced Alloys for Creep-Resistance for Microturbine Recuperator Applications

[+] Author and Article Information
P. J. Maziasz, R. W. Swindeman

Metals and Ceramics Division, Oak Ridge National Laboratory, 1 Bethel Valley Road, Oak Ridge, TN 37831-6115

J. Eng. Gas Turbines Power 125(1), 310-315 (Dec 27, 2002) (6 pages) doi:10.1115/1.1499729 History: Received December 01, 2000; Revised March 01, 2001; Online December 27, 2002
Copyright © 2003 by ASME
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References

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McDonald, C. F., 2000, “Low Cost Recuperator Concept for Microturbine Applications,” ASME Paper No. 2000-GT-0167.
Ward, M. E., 1995, “Primary Surface Recuperator Durability and Applications,” Turbomachinery Technology Seminar Paper No. TTS006/395, Solar Turbines, San Diego, CA.
Oswald, J. I., Dawson, D. A., and Clawley, L. A., 1999, “A New Durable Gas Turbine Recuperator,” ASME Paper No. 99-GT-369.
Child, S. C., Kesseli, J. B., and Nash, J. S., 1999, “Unit Construction Plate-Fin Heat Exchanger,” U.S. Patent No. 5,983,992, Nov. 16.
Advanced Microturbine Systems—Program Plan for fiscal Years 2000–2006, Office of Power Technologies, Office of Energy Efficiency and Renewable Energy, U.S. Department of Energy, Washington, D.C., Mar.
Swindeman,  R. W., and Marriott,  D. L., 1994, “Criteria for Design with Structural Materials in Combined-Cycle Applications Above 815°C,” Trans. ASME, 116, pp. 352–359.
Kane, R. H., 1991, “The Evolution of High Temperature Alloys: A Designer’s Perspective,” Heat-Resistant Materials, K. Natesan and D. J. Tillack, eds., ASM-International, Materials Park, OH, pp. 1–8.
Stringer, J., 1995, “Applications of High-Temperature Materials,” Heat-Resistant Materials II, K. Natesan, P. Ganesan, and G. Lai, eds., ASM-International, Materials Park, OH, pp. 19–29.
Maziasz,  P. J., , 1999, “Improved Creep-Resistance of Austenitic Stainless Steel for Compact Gas Turbine Recuperators,” Mat. High Temp., 16 , pp. 207–212.
Stoloff, N. S., 1990, “Wrought and P/M Superalloys,” Properties and Selection: Irons, Steels, and High-Performance Alloys, 1 , Metals Handbook, 10th Ed. ASM-International, Materials Park, OH, pp. 950–980.
Harper, M. A., Smith, G. D., Maziasz, P. J., and Swindeman, R. W., 2001, “Materials Selection for High-Temperature Metal Recuperators,” paper to be presented at ASME Turbo Expo 2001 Conference.
Pint, B. A., and Rakowski, J. M., 2000, “Effects of Water Vapor on the Oxidation Resistance of Stainless Steels,” Corrosion 2000 Paper No. 00259, NACE International, Houston, TX.
Rakowski, J. M., and Pint, B. A., 2000, “Observations of the Effects of Water Vapor on the Elevated Temperature Oxidation of Austenitic Stainless Steel Foil,” Corrosion 2000 Paper No. 00517, NACE International, Houston, TX.
Pint, B. A., Swindeman, R. W., More, K. L., and Tortorelli, P. F., 2001, “Materials Selection for High Temperature (750–1000°C) Metallic Recuperators for Improved Efficiency Microturbines,” paper to be presented at ASME Turbo Expo 2001 Conference.

Figures

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Optical metallography of polished and etched specimens of as-processed 0.1-mm thick foils to show grain sizes of (a) type 347 stainless steel, (b) alloy 740 (formerly thermie-alloy), and (c) alloy 214
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Plots of creep strain versus time for creep-rupture testing of foils ranging from type 347 stainless steel to alloy 740 (formerly thermie alloy) at 750°C and 100 MPa
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Plots of creep strain versus time for creep-rupture testing of foils ranging from type 347 stainless steel to alloys 625 and 214 at 750°C and 100 MPa
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Plots of creep strain versus time for creep-rupture testing at 750°C and 100 MPa of foils of alloy 625 processed at different conditions (FG = fine grained) or with 2.5% cold prestrain
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Plots of creep strain versus time for creep-rupture testing at 800°C and 80 MPa of foils of alloy 214 processed at different conditions that slightly vary final grain size, with 2s at 1150°C being finer
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TEM images showing the microstructures within grains and along grain boundaries for as-processed foils of (a) alloy 214 with a final solution anneal (SA) of 30s at 1100°C, and (b) alloy 625 (FG) with a final recrystallization anneal of 30s at 900°C. The superimposed diffraction pattern shows the characteristic extra spots from the γ(Ni3Al) coherent precipitates shown as black spots in the image. The alloy 625 had coarser precipitate particles of Ti and Nb-rich MC carbides and finer η phase silicides.

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