JAEA-Conf 2011-002 - 日本原子力研究開発機構
JAEA-Conf 2011-002 - 日本原子力研究開発機構
JAEA-Conf 2011-002 - 日本原子力研究開発機構
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High energy<br />
particle<br />
Vacancy<br />
<strong>JAEA</strong>-<strong>Conf</strong> <strong>2011</strong>-<strong>002</strong><br />
<br />
Figure 8. Multiscale modeling of irradiation effects by high energy particles.<br />
<br />
To estimate the PKA energy spectrum under high energy proton irradiation, the PHITS code was used. The<br />
code was the first general-purpose heavy ion transport Monte Carlo code covering the incident energies from<br />
several MeV/nucleon to several GeV/nucleon. It was developed for general purpose calculations based on the<br />
NMTC/JAM code [9], which is widely used for hadron transport calculations. In the PHITS code, the HIC code<br />
[10], which is used in the HETC-CYRIC code [11], was revised into the JQMD code [12] for heavy ion nuclear<br />
reaction simulation. This is because the JQMD code is based on a more modern nucleus-nucleus reaction model<br />
than QMD, while the HIC is based on a traditional intranuclear-cascade-evaporation model. The PKA energy<br />
spectrum of 3 mm thick Ni irradiated by 3GeV protons was calculated. The PKA energy dependence of damage<br />
energy deposition indicated that the highest energy deposition was caused by 65 keV PKAs.<br />
<br />
As mentioned in 2.1, a high energy PKA produces a large cascade, which can be divided into subcascades.<br />
The subcascade formation energy of Ni was estimated to 10 keV [8]. Therefore we assumed the formation of<br />
several 10 keV subcascades for the initial damage structure instead of large cascades. The number of 10 keV<br />
subcascades during irradiation was obtained from the PKA energy spectrum calculated by the PHITS and by<br />
PKA energy spectrum analysis [1, 2].<br />
Molecular dynamics (MD) was employed to calculate the defect clusters and freely migrating defects from<br />
subcascades of 10 keV. The size of the model lattice was 35×35×35 lattice constants. An EAM potential with<br />
the parameters proposed by Daw and Baskes [13] was used. A periodic boundary condition in three directions<br />
and an NVE ensemble (i.e., fixed number of atoms, cell volume and energy) were used for the simulation.<br />
Three MD runs were performed and the results indicated that, on average, seventeen vacancies and seventeen<br />
interstitials were formed in each 10 keV subcascade. Using the point defect distribution determined by MD, the<br />
kinetic Monte-Carlo simulation was performed and a cluster of three point defects was formed on average.<br />
These values were then used in a defect structural evolution.<br />
<br />
The damage structural evolution was estimated using reaction kinetic analysis [14]. The following<br />
assumptions were used in the calculation. (1) Mobile defects: interstitials, di-interstitials, tri-interstitials,<br />
vacancies and di-vacancies. (2) Point defect clusters of four point defects or more were assumed to be stable<br />
clusters. (3) The time dependence of ten variables: concentration of interstitials, di-interstitials, tri-interstitials,<br />
interstitial clusters (interstitial type dislocation loops), vacancies, di-vacancies, tri-vacancies, vacancy clusters<br />
(voids), the total interstitials in interstitial clusters, and the total vacancies in vacancy clusters. (4) Interstitial<br />
clusters (three interstitials) and vacancy clusters (three vacancies) were also formed directly in cascades. The<br />
formation rates were obtained by MD simulation. (5) The material temperature was 423 K during irradiation.<br />
The result of 10 dpa irradiation was as follows: the void concentration was 5.93x10 -4 /atoms, the void size was<br />
four vacancies and the dislocation density was 1.1x10 9 cm/cm 3 .<br />
<br />
Changes in mechanical property were calculated by three dimensional DDD [15]. In the usual DDD<br />
simulation [16], a curved dislocation line was treated as a connection of short straight segments to simplify the