Analysis of the extended defects in 3C-SiC.pdf - Nelson Mandela ...
Analysis of the extended defects in 3C-SiC.pdf - Nelson Mandela ...
Analysis of the extended defects in 3C-SiC.pdf - Nelson Mandela ...
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62<br />
with direction. Values published by Perlado et al. (2000) range from 42 – 112 eV for<br />
Si and 26 – 58 eV for C depend<strong>in</strong>g on <strong>the</strong> direction. He<strong>in</strong>isch et al. (2004), <strong>in</strong> a study<br />
on displacement damage <strong>in</strong> <strong>SiC</strong> <strong>in</strong> fission reactors, stated that <strong>the</strong> displacement value<br />
for Si could be taken as 35 eV and for C as 20 eV s<strong>in</strong>ce <strong>the</strong>se are <strong>the</strong> average values<br />
taken over all directions <strong>in</strong> <strong>the</strong> <strong>SiC</strong> <strong>the</strong> also stated that <strong>the</strong>re are actually four<br />
m<strong>in</strong>imum recoil damage energies that should be considered to create displacements <strong>in</strong><br />
<strong>SiC</strong>, depend<strong>in</strong>g on <strong>the</strong> projectile/target comb<strong>in</strong>ations: 41 eV (C/Si), 35 eV (Si/Si), 24<br />
eV (Si/C) and 20 eV (C/C). Vladimirov et al. (1998) used values <strong>of</strong> 93 eV for Si and<br />
16.3 eV for C <strong>in</strong> <strong>the</strong>ir calculations as well as Ryazanov et al. (2002).<br />
Thus it is obvious that <strong>the</strong>re is still a lot <strong>of</strong> uncerta<strong>in</strong>ty about <strong>the</strong> correct values for<br />
TDE to be used <strong>in</strong> calculations for <strong>SiC</strong> and is as mentioned before, a result <strong>of</strong> <strong>the</strong><br />
anisotropy with<strong>in</strong> <strong>the</strong> material. Hence <strong>the</strong> method <strong>of</strong> computer simulation is used to<br />
determ<strong>in</strong>e <strong>the</strong> displacement mechanisms and TDE <strong>in</strong> <strong>the</strong> material.<br />
Gao et al. (2001) used molecular dynamics (MD) s<strong>of</strong>tware to simulate Si<br />
displacement cascades <strong>in</strong> <strong>SiC</strong>. Their simulation showed that dur<strong>in</strong>g a high energy Si<br />
primary knock on atom (PKA), multiple sub-cascades were generated. This prevented<br />
both a compact structure <strong>of</strong> displaced atoms to form dur<strong>in</strong>g <strong>the</strong> collision phase and a<br />
high-energy density dur<strong>in</strong>g <strong>the</strong> <strong>the</strong>rmal spike. They attributed this to <strong>the</strong> light masses<br />
<strong>of</strong> <strong>the</strong> <strong>SiC</strong> system and small scatter<strong>in</strong>g cross-sections <strong>of</strong> <strong>the</strong> Si and C atoms.<br />
Fur<strong>the</strong>rmore <strong>the</strong> high melt<strong>in</strong>g temperature <strong>of</strong> <strong>the</strong> <strong>SiC</strong> also <strong>in</strong>hibits <strong>the</strong> development <strong>of</strong><br />
a liquid like cascade which results <strong>in</strong> a very short lifetime <strong>of</strong> <strong>the</strong> <strong>the</strong>rmal spike. This<br />
along with <strong>the</strong> formation energies <strong>of</strong> <strong>defects</strong> provide a physical basis for defect<br />
production and cluster<strong>in</strong>g <strong>in</strong> <strong>the</strong> material. They found that at <strong>the</strong> peak <strong>of</strong> <strong>the</strong> <strong>the</strong>rmal<br />
spikes <strong>the</strong> number <strong>of</strong> displaced Si and C atoms are essentially <strong>the</strong> same but that <strong>the</strong> Si<br />
sublattice partially recovers as <strong>the</strong> energy <strong>of</strong> <strong>the</strong> cascades dissipate <strong>in</strong>to <strong>the</strong> lattice,<br />
while <strong>the</strong> damage <strong>in</strong> <strong>the</strong> C sublattice does not. The number <strong>of</strong> Si <strong>in</strong>terstitials surviv<strong>in</strong>g<br />
after <strong>the</strong> cascade was on average three times smaller than for C. This is possible s<strong>in</strong>ce<br />
most silicon atoms are only displaced a short distance from <strong>the</strong>ir lattice positions and<br />
recomb<strong>in</strong>e dur<strong>in</strong>g <strong>the</strong> <strong>the</strong>rmal spike phase. They expla<strong>in</strong> that as a consequence <strong>of</strong> <strong>the</strong><br />
above facts, <strong>the</strong> formation <strong>of</strong> a dispersed cascade is seen with <strong>defects</strong> spread over <strong>the</strong><br />
simulation box, and most <strong>in</strong>terstitials rema<strong>in</strong> as s<strong>in</strong>gle <strong>defects</strong>. Only a small fraction<br />
<strong>of</strong> <strong>in</strong>terstitials form clusters, <strong>the</strong> biggest be<strong>in</strong>g four atoms. Fur<strong>the</strong>rmore Perlado et al.