Papers by Keyword: Transient Creep

Abstract: The effect of fibre reinforcement on Load Induced Thermal Strains (LITS) has not yet been significantly investigated up to now. Creep is becoming a key research topic only in the last few years. A semi-empirical model able to take into account both the thermo-mechanical damage associated to coarse aggregates and the thermo-chemical damage induced in the matrix and calibrated on the basis of the main results on plain concrete available in the scientific literature is presented. Some tests in uniaxial compression on Fibre Reinforced Concrete (FRC) cylinders characterized by a long age – 11-years-old – have been investigated and compared with the model to highlight fibre effects, if any. The uniaxial compressive strength at 28 days of the SFRC was 75 MPa; the specimens after 11 years showed a compressive strength exceeding 110 MPa. A strong increase of SLS residual strength was observed in post-cracking tension due to the long aging, while ULS residual strengths weakly increased. The cylindrical specimens were exposed to a maximum temperature of 200°C and 400°C and loaded with two load thresholds corresponding to 20% and 40% of the compressive strength detected at 28 days of aging, that means about 12.5% and 25% of the 11-years-old specimens. Two paths were investigated: pre-heated specimens up to 200°C or 400°C, then loaded with a compression stress equal to 0.2f_c,28 and 0.4f_c,28; and pre-loaded specimens up to 0.2f_c,28 and 0.4f_c,28 and then heated up to 200°C or 400°C. The duration of each test did not exceed 12 hours. Two main fibre effects were observed: a significant reduction of irreversible strains when the specimens were loaded and then heated and cooled and a different evolution in LITS passing from 200°C to 400°C, characterized by a significant reduction of the expected deformation.

Abstract: The creep behaviour of the solid solution strengthened nickel-based superalloy Haynes 230 has been investigated under constant load and temperature conditions on as received, after conventional solution treatment, and on overaged conditions. The experimental results have shown a very strong dependence of the creep curve shape with the applied stress/temperature: in the tests performed at high stresses/low temperatures, the primary/decelerating stage takes an important portion of the creep curve. At these test conditions, the accelerating creep is mainly caused by the increase of the applied stress with the strain as it happens in constant load creep tests. In the tests performed at low stresses/high temperatures, the primary stage is very small and the following accelerating creep is characterized by different accelerating creep stages. The analysis of the creep curves on the as received and overaged alloys, has shown that a large portion of the accelerating creep at low stresses/high temperatures is caused by microstructural instability.

Abstract: The effect of fine precipitates, excess dislocations and sub-boundary hardening on creep strain behavior in the transient region has been investigated for tempered martensitic 9%Cr steel at 600 and 650oC. The fine precipitates that form during tempering or during creep decrease the creep rate in the transient region, while excess dislocations produced by cold rolling promote the recovery of dislocations during creep, resulting in higher creep rates. The sub-boundary hardening is enhanced by fine precipitates along lath and block boundaries, which retards the onset of acceleration creep. The movement and annihilation process of dislocations in the transient region is controlled by not only the movement of dislocations in the matrix but also the absorption of dislocations at boundaries. The minimum creep rate is basically determined by the time to minimum creep rate.

Abstract: Through the analysis of many creep rate-strain curves of γ-single phase Ni-20mass%Cr alloy single crystals with various stress axes, it has been elucidated that the ratio of transient stage to rupture life becomes larger with decreasing the stress. And the transient stage consists of Stage I and Stage II. In Stage I, the creep rate just after loading remains constant, and in Stage II, a steep decrease in creep rate continues. It is noticeable that there is a marked difference in transient stage among single crystals with different stress axes. The aim of this study is to elucidate the mechanisms leading to the different transient stages as the function of stress axes. The deformation during transient stage in the single crystals except for the single crystals with the stress axes of the [001] and [1,–11] poles in the standard stereographic triangle, proceeds using the primary slip plane. And they are divided into two groups of the single crystals with the angle between stress axis and primary slip plane, θ, less than 45° and the single crystals with θ more than 45°. The deformations of Stage I and Stage II in these single crystals proceed using the slip system of (111)<1,–01> and the slip system of (111)<1,–10>, and in Stage I, the former slip system acts mainly except for that of single crystals with stress axis of [011]. While, in the single crystal with stress axis of [011], two slip systems above described operate at the beginning of Stage I, and the stress axis moves along [011]-[1,–11] line. And this moving gives slight increase in the Schmid factor, therefore, in Stage I slight increase in creep rate was confirmed. The {111} pole figure of the single crystal with stress axis of [1,–11] whose deformation proceeds using the plural slip planes are obtained by SEM-EBSD method. It becomes clear that the smallest strains of Stage I and Stage II derived from the increase in the torsion with creep deformation.