CHEM02200704003 Nilamadhab Pandhy - Homi Bhabha National ...

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Chapter 2 their segregation to the grain boundaries. The mechanism of attack is not understood fully, however it is suggested that dissolution of weak passive film formed at the grain boundaries causes the intergranular corrosion [15]. Increase in phosphorus content results in progressive increase in intergranular corrosion. The effect of silicon is more complex, and no intergranular corrosion attack is observed in low (< 0.1 %) and high (> 2 %) silicon levels. Maximum rate of attack occurs at approximately 0.7 % silicon. 2.10.2 End-grain attack This is an unusual form of localized corrosion in austenitic stainless steel that occurs in nuclear fuel reprocessing plant as well as other chemical processing plant handling concentrated nitric acid. End-grain attack otherwise known as tunnel corrosion occurs along the cross section normal to the rolling direction, and is considered to have significant effect on the corrosion resistance of austenitic stainless steel in highly oxidizing nitric acid solution. The schematic of end-grain attack is shown in Fig. 2.8a and a typical example of end-grain attack in 18 Cr-10 Ni austenitic stainless steel in simulated dissolver solution containing highly oxidizing nitric acid is shown in Fig. 2.8b [43]. Fig. 2.8 (a) Fig. 2.8 (b) Fig. 2.8: (a) Schematic of end-grain (b) a typical end-grain attack in austenitic stainless steel [43].
Chapter 2 The end-grains (Fig. 2.8a) i.e. exposed grains normal to the rolling direction in austenitic stainless steel shows inferior corrosion resistance in nitric acid solution as compared to other grains. The general corrosion rate of austenitic stainless steel in nitric acid depends up on the exposed part of the surface follows the order top surface < side
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Page 8 and 9: 2.3 Effect of alloying elements on
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Page 12 and 13: 6.2.3.2 Open circuit potential vs.
Page 14 and 15: eprocessing can be recovered, and c
Page 16 and 17: The ex-situ study of passive film w
Page 18 and 19: Fig.3.10: Schematic of electrical e
Page 20 and 21: Fig.6.11: Polarization study of unc
Page 22 and 23: AISI: American Institute of Steel I
Page 24 and 25: Chapter 1 C H A P T E R 1 Spent Nuc
Page 26 and 27: Chapter 1 1.3 Challenges in spent n
Page 28 and 29: Chapter 1 corrosion resistance. The
Page 30 and 31: Chapter 1 choice of zirconium is du
Page 32 and 33: C H A P T E R2
Page 34 and 35: Chapter 2 temperature, (c) higher i
Page 36 and 37: Chapter 2 Chromium in excess of 12
Page 38 and 39: Chapter 2 2. 3 Effect of alloying e
Page 40 and 41: Chapter 2 The twins are identified
Page 42 and 43: Chapter 2 and at temperature around
Page 44 and 45: Chapter 2 of adsorption of oxygen o
Page 46 and 47: Chapter 2 transpassive dissolution
Page 48 and 49: Chapter 2 healing chromium oxide fi
Page 52 and 53: Chapter 2 is intimately related to
Page 54 and 55: Chapter 2 in nature because the dis
Page 58 and 59: Chapter 3 3.1.1.2 Specimen preparat
Page 60 and 61: Chapter 3 ionized. However, differe
Page 62 and 63: Chapter 3 various industrial applic
Page 64 and 65: Chapter 3 In the present investigat
Page 66 and 67: Chapter 3 3.1.3.2 Atomic force micr
Page 68 and 69: Chapter 3 present on the surface fo
Page 70 and 71: Chapter 3 necessary condition is th
Page 72 and 73: Chapter 3 Y m is the sputter yield.
Page 74 and 75: Chapter 3 Fig. 3.7: Schematic of X-
Page 76 and 77: Chapter 3 rate of 10Å/min using 5
Page 78 and 79: Chapter 3 different doses of nitrog
Page 80 and 81: Chapter 3 The modulus of electroche
Page 82 and 83: Chapter 3 equivalent circuit as sho
Page 84 and 85: Chapter 3 reference electrode with
Page 86 and 87: Chapter 3 for understanding the pas
Page 90 and 91: Chapter 4 encountered by all materi
Page 92 and 93: Chapter 4 pitting, and intergranula
Page 94 and 95: Chapter 4 The ridged structure, and
Page 96 and 97: Chapter 4 nitric acid is that the b
Page 98 and 99: Chapter 4 Potential (V) Vs Ag/AgCl
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Chapter 4 4.2.3 In-situ electrochem
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Chapter 4 The surface morphologies
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Chapter 4 a b c d Opening up of gra
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Chapter 4 Intensity (Arbitrary unit
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Chapter 4 The chromium, and oxygen
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Chapter 4 Intensity (Arbitrary unit
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C H A P T E R5
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Chapter 5 elements, and often impar
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Chapter 5 5.2 Results and discussi
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Chapter 5 Presence of oxygen is due
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Chapter 5 was an increase in marten
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Chapter 5 formation of Cr 2 N was a
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Chapter 5 electrochemical environme
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Chapter 5 N + Dose E corr (mV vs. A
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Chapter 5 layer capacitance (C dl )
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Chapter 5 correlation between surfa
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Chapter 5 boundary dissolution was
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Chapter 6 C H A P T E R 6
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Chapter 6 193]. As a single phase c
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Chapter 6 particles range from 8×1
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Chapter 6 Results revealed that in
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Chapter 6 The change over from capa
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Chapter 6 The impedance parameters
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Chapter 6 Conc. Substrate condition
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Chapter 6 6.6a-d. The uncoated spec
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Chapter 6 (55.18°) respectively, w
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Chapter 6 OCP shifted in noble dire
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Chapter 6 The high phase angle over
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Chapter 6 Fig. 6.10d: Log f vs. Log
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Chapter 6 Fig. 6.11b: Polarization
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Chapter 6 Covalent aspect of lattic
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Chapter 6 As compared to uncoated s
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Chapter 6 6.2.3.2 Open circuit pote
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Chapter 6 Similarly, the plots for
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Chapter 6 for the duplex coating, a
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Chapter 6 Fig.6.16b: Polarization s
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Chapter 6 6.2.3.5 Morphological exa
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Chapter 7 C H A P T E R 7 The cha
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Chapter 7 1. Surface morphology exa
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Chapter 7 6 Duplex Ti-TiO 2 coated
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Chapter 7 EC-SPM study on effect
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[1] Baldev Raj, U. Kamachi Mudali,
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[37] G. Okamoto, T. Shibata, Corros
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[79] M. Moens, M. Van Craen, F.C. A
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[117] R.E.Williford, C.F.Windisch J
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[157] N. Mottu, M. Vayer, R. Erre,
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[197] M. Metikos Hukovic, M. Ceraj
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[19] H. H. Uhlig, Corros Sci, 19 (1
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[57] J. F. Ziegler, J. P. Biersack,
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[97] I. Betova, M. Bojinov, V. Kara
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[139] V. Ashworth, R. P. M. Procter
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[176] G. Frankel, G. Grundmeier, H.
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List of publications 1. Referred
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CHEM02200704003 Nilamadhab Pandhy - Homi Bhabha National ...

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