Engineering Physics of High-Temperature Materials. Nirmal K. Sinha. Читать онлайн. Newlib. NEWLIB.NET

Автор: Nirmal K. Sinha
Издательство: John Wiley & Sons Limited
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Жанр произведения: Техническая литература
Год издания: 0
isbn: 9781119420460
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1.4, on a polycrystalline nickel‐base superalloy Waspaloy at 1005 K (732 °C) for initial stresses 450–650 MPa. Note the delayed elastic recovery and viscous strains after unloading.

      Source: N. K. Sinha.

      Figure 1.6 points out that the time to mcr, t m , decreased significantly, over an order of magnitude, with increase in engineering stress from 450 to 650 MPa. The dependence of t m on stress, σ, may be expressed by the following relationship:

      (1.2)t Subscript normal m Baseline equals upper M sigma Superscript negative p

      where M = 1.61 × 1029 and p = 9.36. Such a relationship has commonly been seen for the dependence of rupture or fracture time on stress, leading to popular ideas on relating mcr to failures at high temperatures (see Chapter 6). Note that the total strain, ε min (which includes the elastic strain, ε e), corresponding to mcr increased only from 0.38% for 450 MPa to about 0.64% for 650 MPa. The corresponding values of the creep strain (ε minε e) increased from 0.12 to 0.27%. This type of diminished stress dependency of ε min agrees with general observations available in the literature on the relatively small increase in strain at mcr with increase in stress. In fact, the elongation at fracture hardly varies with stress. However, note the increase in the permanent or viscous strain, ε v, at unloading time of the tests, with increase in stress. Viscous strain thus provides a measure of the permanent change in the structure.

Schematic illustration of stress–strain diagram.

      Source: N. K. Sinha.

      Stress–strain (σε) diagrams for engineering materials are commonly “reserved” for constant displacement (nominally constant strain rate) tests from which some sort of “effective elastic modulus” is evaluated. Most textbooks on mechanics talk about this aspect and define engineering properties of materials accordingly. Hysteresis loop or stress–strain diagrams for constant stress (load) creep tests are unheard or not commonly discussed, perhaps because of uncertainty of the loading and unloading phases of the common creep tests using dead loads.

      Computer‐controlled SRRTs provide unique opportunities for examining the effective elastic modulus during both loading and unloading times, and examine the differences (if any) associated with creep damages. An example is shown in Figure 1.7a for the 200 s SRRT of Figures 1.4 and 1.5 and this illustrates the possibilities of determining E during loading and unloading sequences. Such stress–strain diagrams for creep tests are unheard of to most materials scientists.

      Comparing the E values of 180.0 GPa during the rise time to apply the full load and that of 177.6 GPa obtained for fall time (unloading) demonstrates that these values are complimentary and close to the dynamic values of previously undeformed and undamaged Young's modulus E of Waspaloy at comparable temperatures determined from seismic methods.

      Figure 1.7 also reveals a particularly important aspect of constant‐stress creep tests by noting the experimentally determined amounts of the three components of strain: elastic, delayed elastic, and viscous. Most important is the fact that the delayed elastic contribution to the total strain is measurable and not negligible. In the case of the 200 s test, ε d is comparable to ε v, whereas it is significantly lower in the case of the longer‐term 2341 s test. There was, therefore, a significant contribution of delayed elastic (anelastic) strain to the total “inelastic strain” at the time of the minimum creep rate. Realistic rheological models for high‐temperature engineering applications cannot ignore the contributions of delayed elastic strain, known to be associated with grain‐boundary shearing processes (Sinha 1979).

      Rheological models must be able to quantify the trinity or three‐component aspects of creep and relate to failure processes; this is covered in Chapters 58. It is shown in Chapter 5 that the delayed elastic effect could vary from a linear to a highly nonlinear response, but during primary creep the ratio, n v/s, of stress exponents, n v, for viscous flow (dislocation creep) and, s, for delayed elasticity could be very similar for crystalline materials in general. Since delayed elasticity has been linked strongly to grain‐boundary shearing processes, metallurgical and process engineering for superalloys may be directed toward (grain‐boundary engineering) increasing this n v/s ratio to decrease the propensity for generating intergranular voids and cracks.