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Hydrogen Embrittlement and Galvanic Corrosion of Titanium Alloys

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Hydrogen Embrittlement and Galvanic Corrosion of Titanium Alloys KR0000541 KAERl/AR-570/2000 Hydrogen Embrittlement and Galvanic Corrosion of Titanium Alloys 31/47 Please be aware that all of the Missing Pages in this document were originally blank pages 2000. 6. 30. ^ A • AS 71 ^- 300 "C £7]- ef 2000 ppm PWR 5 of 700 ppm eq -8-Sfe- ^ 120 ppm nfl^-ofl 4. 1/10 S. 60^) ppm 200 °C jl-g-5l«H SI7] xt))^ - 11 - 3 1 7fl -S- 3 2 3 1. 3 2. 4 3. 6 4. 11 3 14 41 41 1. 41 2. 41 3. 42 4. 43 5. 45 47 56 58 - in - 2-1 A comparison of crack growth rates observed in AISI-4130 2 steel (a y = 1330 mn/m ) exposed to three different hydrogen containing environments, all other parameters being identical 20 - iv - =L m 2-1 Schematics of possible transport reaction steps involved in the embrittlement of a structural alloy by an external molecular hydrogen environment 21 2-2 Hydrogen induced, stage II slow crack growth in a high strength martensitic AISI-4340 exposed to various hydrogen -containing environments 22 2-3 Schematics of crack growth in a high strength steel 23 2-4 Schematics of the hydrogen-sweep model for concentrating hydrogen 24 2-5 Schematics of crack growth by hydrogen-lattice-bond interactions 25 2-6 Schematic diagram of cavity nucleation and growth by diffusion of hydrogen from a supersaturated metal lattice 26 2-7 General form of the rate by hydrogen-induced slow crack growth as a function of applied stress intensity 27 2-8 The relationship between the nature of the interaction of hydrogen with metals and the position of the metals in the periodic table 28 2-9 General form of the rate oh hydrogen-induced slow crack growth as a function of applied stress intensity 29 2-10 Schematic diagram of fatigue crack growth in a hydrogen environment • 30 2-11 The phase diagram of Ti-H binary system 31 2-12 Primitive unit cell of a hep metal (open circles) with tetrahedral (full circles) and octahedral (open squares) interstitial site •••• 32 2-13 The effect of displacement rate on the tensile reduction in area of the Ti-140A alloy containing 375ppm hydrogen 33 - v - 2-14 Temperature dependence of crack growth rate in the Ti-6A1 alloy and the Ti-6A1-4V alloy containing different bulk hydrogen concentrations 34 2-15 The fracture surface of the Ti-6A1-4V alloy having an acicular microstructure and failed in gaseous hydrogen at a pressure of 90.6 kN/m2 35 2-16 The hydrogen pressure dependence of the embrittlement ratio observed in the Ti-6A1-4V alloy heat treated to give a continuous a phase and continuous ft phase matrix 36 2-17 Hydrogen-induced cracking observed in Ti-6A1-4V alloy having a continuous ft -phase matrix with acicular a phase platelets 37 2-18 Titanium potentials in 10 % NaCl solution at 25 V after standing 48 hours natural aeration 38 2-19 Hydrogen absorption of titanium in synthetic sea water at increasing cathodic potential 39 2-20 Schematics of the central role of the passive film on titanium and the consequences of film breakdown under various conditions 40 3-1 Activation polarization curves for a reversible electrode system 50 3-2 Polarization behavior of iron in 1.0 N Sodium sulfate 51 3-3 Mixed potential behavior of galvanically coupled Metals A and B 52 3-4 Factors affecting galvanic corrosion • 53 3-5 The galvanic series of various metals in flowing water at 2.4 to 4.0 m/s for 5 to 15 days at 5 to 30 °C 54 3-6 The effect of coupling of titanium to other metals on corrosion rates in seawater 55 - vi - M pickling, electroplating, stripping -§-£} Sj-S)- (delayed failure) 1875id Johnson [1] <*fl *H ^4: ^-fr ^^7loflA-1 Tda^l «V^ ^-8-A] ^I^JIE ^4. n ^ 1965^d NASA(National Aeronautics and Space Administration) ^^ 5000psi -§--§- gaseous hydrogen storage vessel ^ ^^^ti 4^1- ##$ . ^-^^- w>7ll£l$i4 [2,3]. ^12:, ^^ ^ -g-g-^1 ^i (perturbation) 7]- ^ ZL - 1 - noble t!r - 2 - 2 g- ^ ±: m 717|| 2-1 171 2-1 3 5171- XI 2 ^ 1. ^r^^l -B-2fl(The origin of hydrogen) S^ bulk *1)jS. 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