Degradation by high-temperature oxidation, hot corrosion and erosion are the main failure modes of components in the hot sections of gas turbines, boilers, industrial waste incinerators, etc. Superfer 800H have been developed for high temperature applications, superfer finds application in the gas turbine industry, constituting over 50% of the gas turbine weight due to their good mechanical properties at elevated temperatures [1] -[4] . Superfer exhibits superior mechanical strength, surface stability, creep and fatigue resistance at high temperature [5] . The turbine engines are exposed to extremely high temperature and harsh environment and therefore tend to suffer from significant material degradation during service [6] [7] . Low-grade fuel oils and fossil fuels used in energy generation systems contains complex mixtures of molten sodium sulfate (Na₂SO₄) and vanadium pentoxide (V₂O₅) [8] [9] . The Na₂SO₄ can be ingested in the turbine intake air or it can be produced by a reaction between sodium chloride (NaCl) ingested with the intake air and sulfur impurities in the fuel [10] . Vanadium is present in the fuel in the form of vanadium porphyrin, which transforms during combustion into V₂O₅. V₂O₅ and Na₂SO₄ form low melting point inorganic compounds, which undergoes eutectic reaction below 600˚C. NaCl is present in marine environment, and together with Na₂SO₄ it lowers the eutectic melting point to 620˚C. When the temperature exceed melting point of the deposits [11] , these compounds starts slowly depositing on the turbine blades, consequently corrosion rate rapidly increases due to faster transport phenomena in liquid phase which cause catastrophic corrosion phenomena [12] . Hence, for effective and efficient functioning of gas turbine components, it is highly essential to develop superalloy with high-temperature strength as well as good hot corrosion resistance [13] . However, there is still a lack of basic understanding of how these superalloys behave in severe (Na₂SO₄ + 60% V₂O₅) operating environment. Therefore, the hot corrosion behaviour of superfer 800H has been investigated at 900˚C in two most corrosive environments (Na₂SO₄ + 60% V₂O₅ and Na₂SO₄ + 5% V₂O₅ + 5% NaCl) in the present work. The kinetics of corrosion of superalloy substrates was determined from the weight change of the samples calculated during the experiments. Inspections for 10, 20, 35 and 50 reveal the mechanism of hot corrosion via crack propagation. It was found that after 10 cycles Crack has been initiated in the scale and it is clearly visible in the presence of NaCl salt. On subsequent cycles, crack propagates perpendicular to surface and as it encounters inclusions, intermetallics it starts propagating parallel to surface. Through cracks, molten salts attack the substrate and cause hot corrosion. But extent of corrosion is less as the thickness of scale formed after 50 cycles is not more than 50 µm even in most severe environment (Na₂SO₄ + 60% V₂O₅). XRD, SEM and FE- SEM/EDAX, and X-ray mapping were used to characterize the corrosion products in order to render an insight in to the corrosion mechanisms.

The weight change data for superfer 800H subjected to hot corrosion test in molten salt environments are plotted in Figure 1 and Figure 2. It indicates that the superfer 800H followed a parabolic rate law up for both the environment. The higher weight gain of the specimens during the first few cycles might be due to the rapid formation of oxides (formation of Cr₂O₃) at the boundaries and within the open pores due to the penetration of the oxidizing species. Further subsequent increase in weight is gradual. Values of parabolic rate constant Kp (10⁻¹⁰ g²∙cm⁻⁴∙s⁻¹) were obtained from slope of the linear regression fitted line and are tabulated in Table 2. XRD- analysis of hot corroded samples indicates the formation of Fe₂O₃, NiO, Cr₂O₃ and spinel (NiCr₂O₄) as major phases. Surface morphology and composition analysis of corroded sample are shown in (Figure 5 and Figure 6). The EDAX analysis of the surface scale developed on superfer 800H in Na₂SO₄ + 60% V₂O₅ environment (Fig- ures 5(a)-(d)) is crack free with dense clusters mainly consisting of Cr, Fe, Ni and O rich elements, thereby suggesting the formation of Cr₂O₃, Fe₂O₃, NiO and their spinel (NiCr₃O₄). Whereas scale developed on superfer 800H in Na₂SO₄ + 5% V₂O₅ + 5% NaCl environment (Figures 6(a)-(d)) mainly consisting of Cr, Fe, and O rich elements which suggesting the formation of Cr₂O₃ and Fe₂O₃. The formation of spinel of NiCr₂O₄ via solid phase reaction between NiO and Cr₂O₃ in the oxide scales helps to develop oxidation resistance as the spinel phase that usually has lower diffusion coefficients of the cations and anions than those in their parent oxides. The superfer 800H (Figure 5(d) and Figure 6(d)) show the formation of uneven protrusion in entire oxidised surface along the scale grain boundaries, similar protrusion behaviour was reported in the earlier literature [14] [15] during isothermal oxidation studies on plasma-sprayed NiCrAlY bond coat and oxidation and hot corrosion behaviours of superalloys at 900˚C.

X-ray mapping (Figure 7) suggests that in molten salt environments, hot corrosion proceed through initiation and propagation of cracks, diffusion of molten salts through cracks and dissolution and re-precipitation of Cr₂O₃

layer along the path of crack. In Na₂SO₄ + 60% V₂O₅ salt after 20 cycles, cracks are clearly revealed (Figure 7(b)). It is also observed that crack initiated at the surface (scale) first propagates perpendicular to the surface and as it encounters any obstacle (inclusions, inter-metallic) it starts propagating parallel to the surface. Figure 7(c) shows crack propagation and salt penetration through cracks into the substrate. After 50 cycles (Figure 7(d)), there is complete rupture of scale. In case of Na₂SO₄ + 5% V₂O₅ + 5% NaCl environment, presence of Cl⁻ enhances the crack formation. Addition of NaCl accelerates the hot corrosion, as it reacts with the oxides thus releasing chlorine which in turn reacts with the oxides to form the volatile chlorides, as per the following reactions [16] [17] .

Cl₂ is able to penetrate through oxide scales quickly along cracks and react with substrate elements such as Cr. Then volatile chlorides are formed:

The volatile chlorides thus formed tend to diffuse out through the grain boundaries to the surface, and in doing so numerous pits and voids are generated at the grain boundaries, which can be seen clearly in Figure 8. The chlorides may reoxidize on the surface of the scales:

Cl₂ is then regenerated and the corrosion repeated. Other alloy elements, such as Ni, Ti etc. also follow the above reactions. The pits and voids, produced due to the formation of volatile chlorides, provide paths for the further penetration of corrosive species resulting in internal oxidation and sulphidation of the substrates as being reported by sidhu et al. [18] .

It may be noticed that after 10 cycles in Na₂SO₄ + 5% V₂O₅ + 5% NaCl environment (Figure 8(a)), there is no any distinct scale substrate interface, but initiation of crack propagation has been started in the scale and crack propagation path is clearly visible. Through these cracks, molten salt diffuses and attacks the substrate

material by dissolving the Cr₂O₃ layer (Figure 8(c)). Propagation of crack into the material, diffusion of molten salt through the cracks and dissolution and reprecipitation of Cr₂O₃ along the crack path is clearly visible in Figure 8(c). Figure 8(d) further supports the hot corrosion mechanism via crack propagation. Intensive spalling/ sputtering of the scale of the superfer 800H superalloy can be attributed to severe strain developed due to the precipitation of Fe₂O₃ from the liquid phase and interdiffusion of intermediate layers of iron oxide as has been reported by Sachs [19] . Further, the presence of different phases in a thin layer might impose severe strain on the film, which may result in cracking and peeling of the scale. Thermal cycles might have also produced cracks in the scale due to different values of thermal expansion coefficients of the substrate and the oxides formed in the scale. These cracks may have allowed the aggressive molten liquid phase to reach the metal substrate and causes internal oxidation. X-ray mapping of corroded superfer 800H also supports internal oxidation via cracks as there is higher percentage of Cr along with Oxygen along the path of crack.

・ The formation of protective oxide scales such as NiO, Cr₂O₃ and NiCr₂O₄ provide resistance to hot corrosion.

・ Depletion of chromium occurs at scale metal interface, scale initially comprises of Cr₂O₃.

・ During initial cycles Nickel concentration is high at metal interface region, as the number of cycles increase Nickel concentration increase in scale, scale has NiO and Cr₂O₃.

・ Initial scale formed in Na₂SO₄ + 60% V₂O₅ environment is adherent to substrate, while in case of chloride environments (Na₂SO₄ + 10% NaCl, Na₂SO₄ + 5% NaCl + 5% V₂O₅) the initial scale formed is less adherent to substrate and crack propagation path is visible in initial cycles.

・ Crack propagates via formation of Cr₂O₃. Region of crack propagation show Chromium and Oxygen in relatively large quantity.

The authors are very much thankful to Mr. K. Ramesh, General Manager (Commercial), and Mr. I. S. N Murthy, Mishra Dhatu Nigam Limited, Hyderabad (India), for providing the superalloys.