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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5.4 Self-Assembled InAs QDs Embedded in Si Matrix<br />
negligible strain relaxation (Eq. 5.10) and negligible crystal rotation. However,<br />
by direct substitution <strong>of</strong> the approximation in Eq. 5.10 into Eq. 5.11, the relation<br />
between material strain and GPA strain is obtained and expressed by Eq. 5.12:<br />
d bulk<br />
Si<br />
d measured<br />
Si<br />
= 1 (approximation) (5.10)<br />
ε GP A − f<br />
1 + f<br />
=<br />
d measured<br />
InAs (<br />
d bulk<br />
Si<br />
d measured<br />
Si<br />
d bulk<br />
InAs<br />
) − d bulk<br />
Si<br />
(5.11)<br />
ε InAs = εGP A − f<br />
1 + f<br />
(5.12)<br />
The material strain analysis <strong>of</strong> dierent shape and size InAs QDs is shown in<br />
Fig. 5.27. The direction and magnitude <strong>of</strong> tensile and compressive strain is clearly<br />
shown with the color map. The color scale indicates the type and magnitude <strong>of</strong><br />
the strain.<br />
The tensile strain has positive sign values (marked in red to yellow colors<br />
in Fig. 5.27) and is pointing to outward directions (highlighted by red arrows).<br />
Fig. 5.27(a) shows an example <strong>of</strong> tensile strain in y direction (ε yy ). On the other<br />
hand, the compressive strain has negative sign values and marked in green to<br />
dark blue colors with direction (highlighted by red arrows) pointing to inward<br />
direction as illustrated in Fig. 5.27(b). The structure <strong>of</strong> 4 MLs InAs embedded in<br />
Si matrix proved to have high degree <strong>of</strong> relaxation and low residual strain values.<br />
The bulk lattice mismatch <strong>of</strong> 11.55 % is relieved by dislocation loops along the<br />
interface consisting <strong>of</strong> perfect 60 ◦ -type dislocations and partial dislocation with<br />
stacking faults inside the InAs clusters, which is in agreement with the literature<br />
[1]. By two-dimensional strain mapping derived from high-resolution TEM<br />
structure images, no strain gradients in the Si matrix around InAs clusters are<br />
detectable (Fig. 5.26). Therefore, it has been observed that the strain relaxation<br />
eects is mostly relieved by defects formation inside InAs QDs such as (SFs and<br />
MTs) and mist dislocation (MD) array at the InAs/Si interface, as it was shown<br />
in Fig. 5.27. On the other hand, anisotropic distortion <strong>of</strong> InAs lattice constant<br />
is another indication <strong>of</strong> strain relaxation. The residual strain is discussed based<br />
on the thermal mismatch between InAs and Si. However, the deformation force<br />
93