it is not THE precipitation

diff --git a/posic/thesis/sic.tex b/posic/thesis/sic.tex
index f5e5b841d328d44b8f324a8017262763fca6084d..5389ce1c80f5e5d57a3540e53a40d047e16a0f5b 100644 (file)
--- a/posic/thesis/sic.tex
+++ b/posic/thesis/sic.tex
@@ -409,7 +409,7 @@ The precipitation mechanism based on a preceding dumbbell agglomeration as indic
 \subfigure[]{\label{fig:sic:db_agglom:seq03}\includegraphics[width=0.30\columnwidth]{sic_prec_seq_03.eps}}
 %SiC formation and release of excess Si atoms
 \end{center}
-\caption[Two dimensional schematic of the assumed SiC precipitation mechanism based on an initial C-Si dumbbell agglomeration.]{Two dimensional schematic of the assumed SiC precipitation mechanism based on an initial C-Si dumbbell agglomeration. C atoms (red dots) incorporated into the Si (black dots) host form C-Si dumbbells (a), which agglomerate into clusters (b) followed by the precipitation of SiC and the emission of a few excess Si atoms (black circles), which are located in the interstitial Si lattice (c). The dotted lines mark the atomic spacing of c-Si in \hkl[1 0 0] direction indicating the $4/5$ ratio of the lattice constants of c-Si and 3C-SiC.}
+\caption[Two dimensional schematic of the assumed SiC precipitation mechanism based on an initial C-Si dumbbell agglomeration.]{Two dimensional schematic of the assumed SiC precipitation mechanism based on an initial C-Si dumbbell agglomeration. C atoms (red dots) incorporated into the Si (black dots) host form C-Si dumbbells (a), which agglomerate into clusters (b) followed by precipitation of SiC and the emission of a few excess Si atoms (black circles), which are located in the interstitial Si lattice (c). The dotted lines mark the atomic spacing of c-Si in \hkl[1 0 0] direction indicating the $4/5$ ratio of the lattice constants of c-Si and 3C-SiC.}
 \label{fig:sic:db_agglom}
 \end{figure}
 The incorporated C atoms form C-Si dumbbells on regular Si lattice sites.
@@ -436,7 +436,7 @@ Furthermore, IBS studies of Reeson~et~al.~\cite{reeson87}, in which implantation
 The results support a mechanism of an initial coherent precipitation based on substitutional C that is likewise valid for the IBS of 3C-SiC by C implantation into Si at elevated temperatures.
 The fact that the metastable cubic phase instead of the thermodynamically more favorable hexagonal $\alpha$-SiC structure is formed and the alignment of these cubic precipitates within the Si matrix, which can be explained straightforward by considering a topotactic transformation by C atoms occupying substitutionally Si lattice sites of one of the two fcc lattices that make up the Si crystal, reinforce the proposed mechanism.
 
-To conclude, a controversy with respect to the precipitation of SiC in Si exists in literature.
+To conclude, a controversy with respect to the precipitation model of SiC in Si exists in literature.
 Next to the pure scientific interest, solving this controversy and gaining new insight in the SiC conversion mechanism might enable significant progress in the heteroepitaxial growth of thin films featuring non-coherent interfaces in the C/Si system.
 On the other hand, processes relying upon prevention of precipitation in order to produce strained heterostructures will likewise benefit.