ASTM E1457-07e1

1.1 This test method covers the determination of creep crack growth (CCG) in metals at elevated temperatures using pre-cracked specimens subjected to static or quasi-static loading conditions. The time (CCI), t 0.2 to an initial crack extension a i = 0.2 mm from the onset of first applied force and creep crack growth rate, a or da/dt is expressed in terms of the magnitude of creep crack growth relating parameters, C* or K. With C* defined as the steady state determination of the crack tip stresses derived in principal from C*(t) and C t () . The crack growth derived in this manner is identified as a material property which can be used in modeling and life assessment methods () .

1.1.1 The choice of the crack growth correlating parameter C*, C*(t), C t , or K depends on the material creep properties, geometry and size of the specimen. Two types of material behavior are generally observed during creep crack growth tests; creep-ductile () and creep-brittle () . In creep ductile materials, where creep strains dominate and creep crack growth is accompanied by substantial time-dependent creep strains at the crack tip, the crack growth rate is correlated by the steady state definitions of C t or C*(t), defined as C* (see ). In creep-brittle materials, creep crack growth occurs at low creep ductility. Consequently, the time-dependent creep strains are comparable to or dominated by accompanying elastic strains local to the crack tip. Under such steady state creep-brittle conditions, C t or K could be chosen as the correlating parameter () .

1.1.2 In any one test, two regions of crack growth behavior may be present (, ) . The initial transient region where elastic strains dominate and creep damage develops and in the steady state region where crack grows proportionally to time. Steady-state creep crack growth rate behavior is covered by this standard. In addition specific recommendations are made in as to how the transient region should be treated in terms of an initial crack growth period. During steady state, a unique correlation exists between da/dt and the appropriate crack growth rate relating parameter.

1.1.3 In creep ductile materials, extensive creep occurs when the entire uncracked ligament undergoes creep deformation. Such conditions are distinct from the conditions of small-scale creep and transition creep () . In the case of extensive creep, the region dominated by creep deformation is significant in size in comparison to both the crack length and the uncracked ligament sizes. In small-scale-creep only a small region of the uncracked ligament local to the crack tip experiences creep deformation.

1.1.4 The creep crack growth rate in the extensive creep region is correlated by the C*(t)-integral. The C t parameter correlates the creep crack growth rate in the small-scale creep and the transition creep regions and reduces, by definition, to C*(t) in the extensive creep region () . Hence in this document the definition C* is used as the relevant parameter in the steady state extensive creep regime whereas C*(t) and/or C t are the parameters which describe the instantaneous stress state from the small scale creep, transient and the steady state regimes in creep. The recommended functions to derive C* for the different geometries is shown in is described in .

1.1.5 An engineering definition of an initial crack extension size a i is used in order to quantify the initial period of crack development. This distance is given as 0.2 mm. It has been shown () that this period which exists at the start of the test could be a substantial period of the test time. During this early period the crack tip undergoes damage development as well as redistribution of stresses prior reaching steady state. Recommendation is made to correlate this initial crack growth period defined as t 0.2 at a i = 0.2 mm with the steady state C* when the crack tip is under extensive creep and with K for creep brittle conditions. The values for C* and K should be calculated at the final specified crack size defined as a o + a i where a o initial size of the starter crack.

1.1.6 The recommended specimens for CCI and CCG testing is the standard compact tension specimen C(T) (see ) which is pin-loaded in tension under constant loading conditions. The clevis setup is shown in (see for details). Additional geometries which are valid for testing in this procedure are shown in . These are the C-ring in tension CS(T), middle tension M(T), single notch tension SEN(T), single notch bend SEN(B), and double edge notch bend tension DEN(T). In , the specimens side-grooving position for measuring displacement at the force-line (FLD) crack mouth opening displacement (CMOD) and also and positions for the potential drop (PD) input and output leads are shown. Recommended loading for the tension specimens is pin-loading. The configurations, size range and initial crack size and their extent of side-grooving are given in of , () . Specimen selection will be discussed in .

1.1.7 The state-of-stress at the crack tip may have an influence on the creep crack growth behavior and can cause crack-front tunneling in plane-sided specimens. Specimen size, geometry, crack length, test duration and creep properties will affect the state-of-stress at the crack tip and are important factors in determining crack growth rate. A recommended size range of test specimens and their side-grooving are given in in . It has been shown that for this range the cracking rates do not vary for a range of materials and loading conditions () . Suggesting that the level of constraint, for the relatively short term test durations (less than one year), does not vary within the range of normal data scatter observed in tests of these geometries. However it is recommended that, within the limitations imposed on the laboratory, that tests are performed on different geometries, specimen size, dimensions and crack size starters. In all cases a comparison of the data from the above should be made by testing the standard C(T) specimen where possible. It is clear that increased confidence in the materials crack growth data can be produced by testing a wider range of specimen types and conditions as described above.

1.1.8 Material inhomogenities, residual stresses and material degradation at temperature, specimen geometry and low-force long duration tests (mainly greater that one year) can influence the rate of crack growth properties () . In cases where residual stresses exist, the effect can be significant when test specimens are taken from material that characteristically embodies residual stress fields or the damaged material. For example weldments, and/or thick cast, forged, extruded, components, plastically bent components and complex component shapes where full stress relief is impractical. Specimens taken from such component that contain residual stresses will likewise contain residual stresses which may have altered is their extent and distribution due to specimen fabrication. Extraction of specimens in itself partially relieves and redistributes the residual stress pattern; however, the remaining magnitude can still cause significant effects in the ensuing test. Residual stress is superimposed on applied stress and results in crack-tip stress intensity that is different from that based solely on externally applied forces or displacements. Distortion during specimen machining can also indicate the presence of res