Abstract
With Nimonic 105, the dependence of the secondary creep rate εs on stress σ and temperature T can be described as
εs = Aσn exp - Q c/RT
with n ≃ 7 and Q c ≃ 515 kJ mol−1. Using a technique which involves making consecutive small stress reductions during creep, definitive values of the friction stress σ0 can be determined such that these large values of n and Q c can be rationalized as
εs = A*(σ-σ0)4 exp - Q c */RT
where Q c *, derived from the temperature dependence of the creep rate at constant (σ-σ0), is equal to the activation energy for creep of single phase nickel–chromium alloys (∼ 310 kJ mol−1). This suggests that processes occurring in the matrix are rate-controlling during creep of nickel-base superalloys. Differences in the stress and temperature-dependence of creep resulting from variations in creep testing procedure are shown to be attributable to micro-structural instability. Furthermore, measurements of σ0 during conventional creep tests and during tests in which the specimens were subjected to creep/heat-treatment cycles demonstrate that, under the conditions studied, tertiary creep commences as a result of precipitate coarsening rather than as a consequence of grain boundary cavity and crack development. Improved creep rupture lives can then be achieved by periodically reheat-treating the material to restore the original particle distribution.