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Research Papers: Materials and Fabrication

Influence of Data Scattering on Estimation of 100,000 hrs Creep Rupture Strength of Alloy 617 at 700 °C by Larson–Miller Method

[+] Author and Article Information
Fujio Abe

National Institute for Materials Science,
1-2-1 Sengen,
Tsukuba 305-0047, Japan
e-mail: ABE.Fujio@nims.go.jp

M. Tabuchi, M. Hayakawa

National Institute for Materials Science,
1-2-1 Sengen,
Tsukuba 305-0047, Japan

Contributed by the Pressure Vessel and Piping Division of ASME for publication in the JOURNAL OF PRESSURE VESSEL TECHNOLOGY. Manuscript received November 13, 2015; final manuscript received March 28, 2016; published online August 5, 2016. Assoc. Editor: Haofeng Chen.

J. Pressure Vessel Technol 139(1), 011403 (Aug 05, 2016) (9 pages) Paper No: PVT-15-1253; doi: 10.1115/1.4033290 History: Received November 13, 2015; Revised March 28, 2016

The 100,000 hrs creep rupture strength of Alloy 617 at 700 °C is estimated by Larson–Miller method using the rupture data of longer duration than 500 hrs in the temperature range between 593 and 816 °C, corresponding to 700 ± 100 °C. The maximum time to rupture was 40,126.7 hrs. The rupture data exhibit large scattering, especially at 760 °C. After eliminating the shorter time to rupture data at 760 °C, the regression analysis gives us the Larson–Miller constant C = 12.70 and the 100,000 hrs creep rupture strength of 100 MPa at 700 °C, by Swindeman program. The present regression analysis underestimates the constant C and 100,000 hrs creep rupture strength. The linear extrapolation of log tr versus reciprocal temperature 1/T plots to 1/T = 0 gives us an average C value of Cav = 18.5, which is much larger than the constant C of 12.70 obtained by the Swindeman program. It is concluded that the origin of underestimation of the constant C and corresponding 100,000 hrs creep rupture strength is large data scattering. Using an appropriate constant C of 18.45, the 100,000 hrs creep rupture strength at 700 °C is estimated to be 123 MPa. Using the rupture data including the shorter time to rupture data at 760 °C and using C = 18.45, the 100,000 hrs creep rupture strength at 700 °C is estimated to be 116 MPa.

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References

Abe, F. , 2015, “ Research and Development of Heat-Resistant Materials for Advanced USC Power Plants With Steam Temperatures of 700 °C and Above,” Engineering, 1(2), pp. 211–224. [CrossRef]
Tschaffon, H. , 2006, “ The European Way to 700 °C Coal Fired Power Plant,” 8th Liege Conference on Materials for Advanced Power Engineering, Liege, Belgium, Sept. 18–20, pp. 61–67.
Fukuda, M. , Saito, E. , Semba, H. , Iwasaki, J. , Izumi, S. , Takano, S. , Takahashi, T. , and Sumiyoshi, Y. , 2013, “ Advanced USC Technology Development in Japan,” Proceedings of the Seventh International Conference on Advances in Materials Technology for Fossil Power Plants (EPRI 2013), Waikoloa, HI, Oct. 22–25, D. Gandy , and J. Shingledecker , eds., ASM International, Materials Park, OH, pp. 24–40.
Shingledecker, J. , Purgert, R. , and Rawls, P. , 2013, “ Current Status of the U.S. DOE/OCDO A-USC Materials Technology Research and Development Program,” Proceedings of the Seventh International Conference on Advances in Materials Technology for Fossil Power Plants (EPRI 2013), Waikoloa, HI, Oct. 22–25, D. Gandy , and J. Shingledecker , eds., ASM International, Materials Park, OH, pp. 41–52.
Allen, T. , Burlet, H. , Nanstad, R. K. , Samaras, M. , and Ukai, S. , 2009, “ Advanced Structural Materials and Cladding,” MRS Bull., 34(1), pp. 1–8. [CrossRef]
Chandra, S. , Cotgrove, R. , Holdsworth, S. R. , Schwienheer, M. , and Spindler, M. W. , 2005, “ Creep Data Assessment of Alloy 617,” ECCC International Conference on Creep & Fracture in High Temperature Components, London, Sept. 12–14, pp. 178–188.
Special Metals, 2015, “ Inconel Alloy 617,” Special Metals Corp., New Hartford, NY.
Mankins, W. L. , Hosier, J. C. , and Bassford, T. H. , 1974, “ Microstructure and Phase Stability of Inconel Alloy 617,” Metall. Trans., 5(12), pp. 2579–2590. [CrossRef]
Viswanathan, R. , 1995, “ Damage Mechanisms and Life Assessment of High-Temperature Components,” ASM International, Materials Park, OH, pp. 59–110.
ASME, 2015, “ Guidelines on the Approval of New Materials Under the ASME Boiler and Pressure Vessel Code,” Boiler and Pressure Vessel Code, Section II, Part D, Mandatory Appendix 5, American Society of Mechanical Engineers, New York, pp. 940–947.
Wu, Q. , Shingledecker, J. P. , Swindeman, R. W. , and Vasudevan, V. K. , 2005, “ Microstructure Characterization of Advanced Boiler Materials for Ultra Supercritical Coal Power Plants,” Fourth International Conference on Advances in Materials Technology for Fossil Power Plants, Hilton Head Island, SC, Oct. 25–28, pp. 748–761.
Gierschner, G. , Ullrich, C. , Tschaffon, H. , and Hansknecht, F. , 2012, “ Latest Developments for the Flexible High Efficient Power Plant of the Future,” 38th MPA-Seminar, Stuttgart, Germany, Oct. 1–2, pp. 353–373.
Speicher, M. , Klenk, A. , Maile, K. , and Roos, E. , 2009, “ Investigations on Advanced Materials for 700 °C Steam Power Plant Components,” 3rd Symposium on Heat Resistant Steels and Alloys for High Efficiency USC Power Plants 2009, Tsukuba, Japan, June 1–4.
Toda, Y. , 2015, private communication.
ASME, 2015, “ Maximum Allowable Stress Values for Nonferrous Materials,” Boiler and Pressure Vessel Code, Section II, Part D, American Society of Mechanical Engineers, New York, pp. 218–221.
Abe, F. , 2014, “ Grade 91 Heat-Resistant Martensitic Steel,” Coal Power Plant Materials and Life Assessment, A. Shibli , ed., Woodhead Publishing, Cambridge, UK, pp. 3–51.
Special Metals, 2015, “ Inconel Alloy 740; A Developmental Precipitation-Hardenable Ni–Cr–Co Superalloy for High Temperature Service in the Automotive and Power Industries,” Special Metals Corp., New Hartford, NY.

Figures

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Fig. 2

Mole fraction of γ′ precipitates in Alloy 617 and Alloy 740 as a function of temperature

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Fig. 1

Creep rupture data for Alloy 617

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Fig. 3

Creep rupture data for Alloy 617 at respective temperatures. (a) 593, (b) 649, (c) 704, (d) 760, and (e) 816 °C.

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Fig. 4

(a) Creep rupture data and (b) correlation between sulfur and boron concentration and rupture elongation for Alloy 617 at 760 °C

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Fig. 14

SEE for second order regression curves of Larson–Miller parameter for Alloy 617 as a function of Larson–Miller constant C. The regression curves with C = 12.70, 18.45, and 30 are shown in Figs. 5 and 13.

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Fig. 16

(a) SEE for second-order regression curves of Larson–Miller parameter for Alloy 617 and (b) 100,000 hrs creep rupture strength at 700 °C, as a function of Larson–Miller constant C

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Fig. 18

SEE for second-order regression curves of Larson–Miller parameter for Alloy 617 as a function of Larson–Miller constant C

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Fig. 19

Stress versus Larson–Miller parameter plots of test data Δ = 1 and second-order regression curve of Larson–Miller parameter with C = 18.45

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Fig. 5

Creep rupture data for Alloy 617 at 593–816 °C and second-order regression curves of Larson–Miller parameter

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Fig. 20

Creep rupture data for Alloy 617 at 593–816 °C and second-order regression curves of Larson–Miller parameter. The solid and dotted lines show regression curves for creep rupture data excluding and including shorter time to rupture data at 760 °C, respectively.

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Fig. 13

Creep rupture data for Alloy 617 at 593 °C–816 °C and second-order regression curves of Larson–Miller parameter with (a) C = 18.45 and (b) C = 30

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Fig. 15

Creep rupture data for Alloy 617 with different data scattering of Δ = 0, 0.5 and 1 and second order regression curve of Larson–Miller parameter with C = 18.45

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Fig. 17

Stress versus Larson–Miller parameter plots of data with no scattering Δ = 0 and second-order regression curve of Larson–Miller parameter with C = 18.45

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Fig. 6

Second order regression curves of Larson–Miller parameter for Alloy 617 using long-term creep rupture data above (a) 2000 hrs and (b) 5000 hrs

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Fig. 7

Creep rupture data for Alloy 617 at 649–760 °C and second-order regression curves of Larson–Miller parameter

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Fig. 10

Logarithm of time to rupture versus reciprocal temperature lines for Alloy 617 at constant stresses, based on Fig. 9

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Fig. 11

Larson–Miller constant C estimated from log tr versus reciprocal temperature plot for Alloy 617 and Alloy 740, together with constant C for Alloy 617 and Alloy 740 obtained by Swindeman program. The Cav = 18.5 shown by dotted line is average value of C = 17–20 obtained by log tr versus reciprocal temperature plot for Alloy 617 and Alloy 740.

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Fig. 12

Creep rupture data for Alloy 740 at 600–850 °C and second-order regression curves of Larson–Miller parameter

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Fig. 8

Schematic illustration for obtaining constant C by linear extrapolation of log tr versus reciprocal temperature 1/T plots to 1/T = 0 at constant stresses, according to Eq. (1)

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Fig. 9

Isothermal rupture curves and some horizontal lines showing constant stress conditions, together with creep rupture data for Alloy 617

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