Molecular beam epitaxial growth of III-V semiconductor ... - KOBRA
Molecular beam epitaxial growth of III-V semiconductor ... - KOBRA
Molecular beam epitaxial growth of III-V semiconductor ... - KOBRA
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Hetero<strong>epitaxial</strong> Growth <strong>of</strong> <strong>III</strong>-V Semiconductor on Silicon Substrates<br />
hand, epi-layers with lattices constant larger than the substrate lattice constant<br />
(f< 0) will undergo compressive strain. In hetero<strong>epitaxial</strong> systems with a low<br />
amount <strong>of</strong> mismatch (|f|< 1), the initial <strong>growth</strong> tends to be coherent, or pseudomorphic<br />
as illustrated in Fig. 3.5(a). Therefore, a pseudomorphic (full strained)<br />
layer exhibits an in-plane strain (ɛ || ) equal to the lattice mismatch (f) as described<br />
in Eq. 3.9 [31].<br />
ɛ || = f (P seudomorphic) (3.9)<br />
The residual strain in highly strained materials is generally a function <strong>of</strong> the<br />
mismatch and layer thickness. However, the strain can be calculated based on a<br />
thermodynamic model, as long as the <strong>growth</strong> occurs near thermal equilibrium.<br />
However, there are kinetic barriers to the lattice relaxation. These are associated<br />
with the generation and movement <strong>of</strong> dislocations. Kinetic models have been<br />
devised to explain and predict the lattice relaxation behavior in these situations<br />
[31]. These models predict that the residual strain in the layer will depend on<br />
the <strong>growth</strong> conditions and post <strong>growth</strong> thermal annealing (PGA) applied after<br />
the <strong>growth</strong>, as well as the mismatch and layer thickness. However, with higher<br />
amount <strong>of</strong> mismatch, or thicker <strong>epitaxial</strong> layers, the mist strain will increase until<br />
it exceeds the elastic strength <strong>of</strong> the coherent <strong>semiconductor</strong>-substrate bonds. At<br />
this point, the lm will undergo a plastic deformation resulting in the formation<br />
<strong>of</strong> broken bonds and non-coherent <strong>growth</strong> fashion with mist dislocations at the<br />
<strong>epitaxial</strong> lm-substrate interface as shown in Fig. 3.5(b). This mist dislocation<br />
is associated with an extra half-plane <strong>of</strong> atoms in the substrate.<br />
The pseudomorphic layer matches the substrate lattice constant in the plane<br />
<strong>of</strong> the interface and therefore experiences in-plane biaxial compression. Beyond<br />
the critical layer thickness, therefore, part <strong>of</strong> the mismatch is accommodated by<br />
mist dislocations (plastic strain) and the balance by elastic strain. In this case,<br />
using the denition for the mismatch adopted here, the in-plane strain (ɛ || ) is<br />
expressed as in Eq. 3.10.<br />
ɛ || = f − δ (P artially relaxed layer) (3.10)<br />
Where δ is the lattice relaxation. In the pseudomorphic layer, for which no lattice<br />
relaxation has occurred (δ=0), the result will be a fully strained system as<br />
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