q are indicated for comparison. According to the procedure adopted for calculation of experimental q values, it is difficult to give a significant relative error. So we consider that Equation 3 is a good mathematical tool for control of the impregnation step, although the associated rate law, Equation 2, is not yet supported by a physical mechanism for charge transfer during impregnation. It is important to note that infiltration of nickel into the alumina compact by electrodeposition (direct or pulsed current) in proportion to t 0.45 ±t 0.61 of deposition time t [10] may be also fitted by a logarithmic law such as Equation 3. Moreover, such a law accounts for the growth of conversion layer on austenitic Z3CN18-10 and ferritic Z6CNb17 steels as demonstrated in a previous paper. [11] Thus Equation 3 and its associated rate law, Equation 2, describe the oxidation reaction of an alloy by some aqueous species and reduction of some aqueous species on a solid surface.We conclude that a logarithmic growth law accounts for metallic ac electrochemical impregnation of the porous part of the anodized layer of aluminum alloys 1050A and 2024T3. Such an equation is valid whatever the structure of the porous layer (columnar or spongy) and deposited metal (Ni or Zn). Further work is in progress for the understanding and the modeling of the influence of the ac impregnation voltage.In this study, a new life-prediction approach that is based on a microcrack propagation model is proposed. Low-cycle fatigue tests were combined with microstructural observations to establish the model parameters. The cyclic J-integral approach was used to describe fatigue-crack growth under elastic±plastic loading conditions in an inert environment. Environmental effects that are accounted for in the model are the formation of an oxygen-embrittled subsurface layer at high temperatures and the effect of water vapor (hydrogen embrittlement) at intermediate temperatures. The model was applied to predict the fatigue life under complex loading conditions of near-a IMI 834 titanium alloy in the temperature range from room temperature to 650 . Model predictions are compared with experimental results from thermomechanical Deposited metal Aluminum alloy Impregnation mode and V i Rate law constants A (lg cm ±2 min ±1 ) B (lg cm ±2 ) Ni 1050 A