A comparative study of oxide scales grown on stainless steel and nickel-based superalloys in ultra-high temperature supercritical water at 800 °C
Introduction
The Canadian supercritical water-cooled reactor (SCWR) concept being developed under Canada’s Generation IV National Program [1], [2], [3], [4] requires the selection of candidate fuel cladding alloys that can withstand the peak cladding temperature, which could reach 800 °C. The operating conditions in an SCWR core include high temperature and pressure, and radiation flux. Candidate materials need to have acceptable dimensional stability, be resistant to oxidation and irradiation creep under constant stress and high temperature oxidation, possess acceptable ductility, toughness, creep rupture strength, and resistance to stress corrosion cracking (SCC) [3], [5], [6]. Many commercial alloys, for example, austenitic steels (such as SS 304, SS 316) and nickel-based alloys, suffer from high corrosion rates or SCC in supercritical water (SCW) [3], [6] and are therefore unsuitable for application in an SCWR core.
There have been numerous investigations of the oxidation of alloys in SCW; note that temperatures well above the critical temperature there is no distinction between SCW and water at a temperature above the critical temperature but at a pressure below the critical pressure (typically called superheated steam in the power industry) [6], [7], [8], [9], [10], [11], [12]. Materials research for reactors operating at temperatures above the thermodynamic critical point of water started in the early 1950s [7]. Some of the highest temperatures reported for SCW corrosion tests were those reported by Boyd in 1956 [7], who studied the corrosion behavior of Ni–Cr–Fe alloys such as 410, 302, 347, 309, 310 stainless steels, and nickel-base alloys such as 625, 617, 718 as a function of temperatures. It is known that alloying elements and impurities can change the oxidation and corrosion susceptibility of the base metal at high temperature. In Fe–Ni–Cr alloys, outward diffusion of iron and nickel and reaction with oxygen leads to the formation of oxides such as Fe3O4, Fe2O3, FeO, and NiO, depending on the oxygen content, temperature and exposure time to SCW. Chromium plays an important role in the formation of protective oxide layers on the alloy surface in the form of chromium oxide (Cr2O3) or Cr-based oxides with the spinel structure [12], [13], [14], [15], [16]. More importantly, alloying elements such as molybdenum, titanium, manganese, aluminum and niobium influence oxide layer formation by formation of different phases in the oxide scale [8], [9], [10], [11], [12], [17], [18]. Additionally, as there are differences in the potentials for different oxide compositions, localized corrosion can be accelerated at high temperature leading to pitting. Finally, diffusion rate differences at high temperature may result in the depletion or enrichment of alloying elements leading to localized corrosion. It is worth nothing that at the high operating pressure of the SCWR it is possible for alloying elements and/or oxides to dissolve into the SCW, resulting in loss of the oxide layer [4], [13], [14], [19]. Several mechanisms for oxidation of alloys in SCW, such as solid-state growth and metal dissolution/oxide precipitation, have been proposed [20], [21], [22], [23], [24].
As there have been few studies of the oxidation of candidate alloys in SCW at 800 °C, in this work, several candidate alloys were tested for their corrosion susceptibility in SCW at 800 °C and 25 MPa for 12 h. The oxide scales and pitting formed during exposure to SCW were characterized using weight gain/loss measurements, X-ray diffraction (XRD), and scanning/transmission electron microscopy (SEM) equipped with energy-dispersive X-ray spectroscopy (EDS). Oxidation and pitting mechanisms are discussed.
Section snippets
Material and methods
The materials used in the present study were solution-treated commercial sheets with a thickness of 2 mm. The elemental compositions of the alloys used are given in Table 1 and initial microstructures are illustrated in Fig. 1. Rectangular sample coupons 20 mm in length and 10 mm in width were cut from the sheets, ground with emery paper up to 600-grit, and washed in an ultrasonic bath of pentane, isopropyl alcohol, and acetone to degrease the surfaces. The corrosion tests were conducted using the
Visual observation of the metal surfaces exposed to SCW at 800 °C
Fig. 3 illustrates the colors of the sample surfaces exposed to SCW for 12 h at 25 MPa and 800 °C. The brown color of the SS 347H metal surface (Fig. 3a) indicates moderate oxidation. For SS 316L, a uniform dark oxide scale formed on the surface exposed to SCW (Fig. 3b). The oxide layers on the surfaces of SS 310S, alloy 625, and alloy 800H had a rainbow appearance due to light interference effects and indicative of thicknesses on the order of the wavelength of light, being blueish green (Fig. 3
Conclusions
There are limited experimental data regarding the behavior of alloys in SCW at ultrahigh temperatures, and a larger database is needed to enable the development of SCWR concepts as well as fossil-fired ultrasupercritical power plants. In this work, iron- and nickel-based alloy samples were exposed to SCW for 12 h at 800 °C and 25 MPa, and the samples were examined by weight change measurements, scanning electron microscopy, energy dispersive spectroscopy, and X-ray diffraction. While these tests
Acknowledgments
The authors would gratefully acknowledge the financial support from the NSERC/NRCAN/AECL CRD program. Thanks to Haynes International Inc. for supplying alloys 214 and C2000 for this study. Thanks to EM facility personals at NINT for their assistance in TEM analysis.
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