Page 224 - Fiber Fracture
P. 224

STRENGTH AND FRACTURE OF METALLIC FILAMENTS                         209
























                                        In (t. exp(-QkT))   4
             Fig. 25.  Evolution  of  the  yield  stress  during  annealing  treatments  as  a  function  of  the  temperature
             compensated time H for 50 Km thick Au wire (Hausmann, 1987).

               Using the value obtained for Q we can now replot all the curves as given in Fig. 22
             to get  a  single master curve which  is  the  yield  stress as a function of  temperature-
             compensated annealing time 0. Fig. 25 shows this curve for 50 pm thick Au wire. In
             view of the very different annealing conditions, over five time decades and temperatures
             from 200  to  800°C the  description by  a temperature-compensated annealing time  is
             quite satisfactory. Measurement on other Au wires showed master curves of the same
             form  that  were  slightly  shifted to the  right  or to  the  left  according to  the  effective
             activation energy. Another wire of  4N purity gave an activation energy of  0.92 eV and
             two wires of the same material, but with an addition 85 ppm Be, had activation energies
             close to  1.5 eV. The effect of  Be is to slightly increase the strength and to retard the
             recrystallization.
               Several authors (Leslie et al.,  1961; Scheucher, 1969a,b; Murphy and  Ball,  1972;
             Hausmann,  1987) tried  to explain this recrystallization behavior by  the  Avrami and
             Johnson-Mehl  relation.  This  relation  was  originally  derived  by  Avrami  to  explain
             the kinetics of  diffusive phase transitions and  later applied by  Johnson and  Mehl  to
             recrystallization. Accordingly the quantity  1 - R,  where  R  is normalized yield stress,
             should behave as a function of  annealing time like the growth of  the volume of  a new
             phase as a function of  time. The experimental curve can in  fact be fitted by  desired
             relation
               R = e-k.t"
             with k  and n as constants. However, it turns out that the exponent n becomes much too
             small to find a reasonable interpretation. For 3-dimensional growth of the recrystallized
             volume n should have a value between 3 and 4 (n = 4 for continuous nucleation and
             a = 3 when the nuclei are already present at the beginning). Exponents between 2 and 3
   219   220   221   222   223   224   225   226   227   228   229