On grain-size-dependent void swelling in pure copper irradiated with fission neutrons

Abstract The effect of grain size on void swelling has its origin in the intrinsic property of grain boundaries as neutral and unsaturable sinks for both vacancies and self-interstitial atoms. The phenomenon had already been investigated in the 1970s and it was demonstrated that the grain-size-dependent void swelling measured under irradiation producing only Frenkel pairs could be satisfactorily explained in terms of the standard rate theory (SRT) and dislocation bias. Experimental results reported in the 1980s demonstrated, on the other hand, that the effect of grain boundaries on void swelling under cascade damage conditions was radically different and could not be explained in terms of the SRT. In an effort to understand the source of this significant difference, the effect of grain size on void swelling under cascade damage conditions has been investigated both experimentally and theoretically in pure copper irradiated with fission neutrons at 623 K to a dose level of about 0.3 displacement per atom. The post-irradiation defect microstructure including voids was investigated using transmission electron microscopy and positron annihilation spectroscopy. The evolution of void swelling was calculated within the framework of the production bias model (PBM) and the SRT. The grain-size-dependent void swelling measured experimentally is in good accord with the theoretical results obtained using the PBM. The implications of these results on the modelling of void swelling under cascade damage conditions are discussed.

[1]  S. Golubov,et al.  Progress in modelling the microstructural evolution in metals under cascade damage conditions , 2000 .

[2]  P. Ehrhart,et al.  On recoil energy dependent void swelling in pure copper Part I. Experimental results , 2000 .

[3]  Stanislav I Golubov,et al.  Defect accumulation in fcc and bcc metals and alloys under cascade damage conditions – Towards a generalisation of the production bias model , 2000 .

[4]  H. Fukushima,et al.  The search for interstitial dislocation loops produced in displacement cascades at 20 K in copper , 2000 .

[5]  Stanislav I Golubov,et al.  Stability and mobility of defect clusters and dislocation loops in metals , 2000 .

[6]  M. Eldrup,et al.  Studies of defects and defect agglomerates by positron annihilation spectroscopy , 1997 .

[7]  H. Trinkaus,et al.  Microstructural evolution adjacent to grain boundaries under cascade damage conditions and helium production , 1996 .

[8]  J. Poulsen,et al.  Sources for positron lifetime spectroscopy produced by ion implantation of 22Na , 1995 .

[9]  A. Horsewell,et al.  Effects of fission neutron and 600 MeV proton irradiations on microstructural evolution in OFHC-copper , 1994 .

[10]  S. Zinkle,et al.  Defect accumulation in pure fcc metals in the transient regime: a review , 1993 .

[11]  Steven J. Zinkle,et al.  Analysis of displacement damage and defect production under cascade damage conditions , 1993 .

[12]  H. Trinkaus,et al.  Glide of interstitial loops produced under cascade damage conditions: Possible effects on void formation , 1992 .

[13]  Manninen,et al.  Edge dislocations in fcc metals: Microscopic calculations of core structure and positron states in Al and Cu. , 1990, Physical review. B, Condensed matter.

[14]  C. Woo,et al.  The Concept of Production Bias and Its Possible Role in Defect Accumulation under Cascade Damage Conditions , 1990 .

[15]  S. Zinkle,et al.  Void swelling and defect cluster formation in reactor-irradiated copper☆ , 1989 .

[16]  A. Horsewell,et al.  Diffusion Mechanisms for Enhanced Vacancy Accumulation Near Planar Sinks , 1987 .

[17]  T. Leffers,et al.  The temperature dependence of void and bubble formation and growth in aluminium during 600 MeV proton irradiation , 1984 .

[18]  T. Leffers,et al.  Grain boundary related effects in aluminium during 600 MeV proton irradiation at different temperatures , 1984 .

[19]  T. Leffers,et al.  Formation of cavities at and away from grain boundaries during 600 MeV proton irradiation , 1982 .

[20]  O. Mogensen,et al.  A positron annihilation investigation of defects in neutron irradiated copper , 1981 .

[21]  P. Hautojärvi,et al.  Positrons in Solids , 1979 .

[22]  B. Henderson.  Defects in solids , 1975, Nature.

[23]  M. Robinson,et al.  A proposed method of calculating displacement dose rates , 1975 .

[24]  A. Seeger.  The stationary distribution of vacancies and interstitials in irradiated plates , 1975 .

[25]  S. J. Rothman,et al.  Steady-state point-defect diffusion profiles in solids during irradiation , 1974 .

[26]  B. N. Singh,et al.  Calculated grain size-dependent vacancy supersaturation and its effect on void formation , 1974 .

[27]  R. S. Nelson,et al.  Void formation in nickel during 20 MeV C++ irradiation at 525 °C , 1971 .

[28]  D. Norris.  The use of the high voltage electron microscope to simulate fast neutron-induced void swelling in metals , 1971 .