Programm Photovoltaik Ausgabe 2009 ... - Bundesamt für Energie BFE
Programm Photovoltaik Ausgabe 2009 ... - Bundesamt für Energie BFE Programm Photovoltaik Ausgabe 2009 ... - Bundesamt für Energie BFE
5/7 Fig. 3: Raman spectra recorded from as-deposited IGS (A); Cu-treated IGS (B); a precursor layer heated to 250°C with Se (C); and layers annealed at 575°C with Se supplied throughout the entire annealing process (D); and only once substrate temperature reached �400°C (E). The peaks in spectra D and E are identified with CIGS vibrational modes. Scanning electron microscopy (SEM) The Scanning Electron Microscope (SEM) micrographs displayed in Figure 4 show the surface and cross-section of layers annealed at 575°C with Se supplied continuously throughout annealing (left) and only once the substrate temperature reached �400°C (right). In the latter case CuSey formation and the accompanying expansion and contraction of the layer is avoided and it is clear that this results in a much smoother layer. Whilst a large affect on grain size is observed in these images, other layers that exhibit the same trend in surface roughness have shown different trends in grain growth and so conclusions cannot be drawn without further investigation. Fig. 4: Surface (top) and cross-section (bottom) SEM micrographs of layers annealed at 575°C with Se supplied throughout the entire annealing process (left); and only once substrate temperature reached �400°C (right). 91/290 Thin Film CIGS Solar Cells with a Novel Low Cost Process, A. N. Tiwari, ETH Zürich
Secondary-ion mass spectroscopy (SIMS) Figure 5 shows SIMS depth profiles of layers at various stages of processing. The IGS films used to make these samples were not quite of the same thickness, due to their positions in the deposition chamber, hence conclusions cannot be drawn from apparent changes in thickness. The composition of the as-deposited IGS layer (A) is homogeneous throughout its depth, however a regular oscillation in Ga/In signal strength ratio is observed. Since the number of oscillations corresponds to the number of passes that the substrates made back and forth across the sources, they are attributed to incomplete mixing of the In and Ga during deposition. The layer analyzed following Cu treatment (B) indicates that Cu is incorporated from the surface and that loss of In occurs in preference to loss of Ga, explaining the higher than expected Ga content in the annealed CIGS layers. That Ga-Se compounds have greater enthalpies of formation than their In-Se analogues is a possible explanation for Cu ions exchanging more rapidly for In ions than Ga ions. Another explanation involves the fact that the atomic radii of Cu and In are similar, whilst the ionic radius of Ga is significantly smaller. As a result, the energy of a Cu ion occupying a Ga site in the IGS layer is likely to be higher than that of a Cu ion occupying an In site, again making the exchange reaction likely to occur more rapidly for In than for Ga. The Cu distribution data indicate that some grading of Cu into the underlying IGS layer occurs during immersion in the solution, however a component of the decaying Cu signal will have arisen from forward sputtering effects. The depth profiles measured from the annealed layers, both with preheated Se source (C) and delayed Se supply (D) indicate broadly homogenised depth profiles. However, in both cases there is a decrease in Ga signal towards the front of the layer which is slightly more pronounced for the layer annealed with delayed Se supply. Fig. 5: SIMS depth profiles of as-deposited IGS (A), Cu-treated IGS (B) and layers annealed at 575°C with Se supplied throughout the entire annealing process (C) and only once substrate temperature reached �400°C (D). Oscillation in the In and Ga signals in A and B result from substrate movement during deposition. 92/290 Thin Film CIGS Solar Cells with a Novel Low Cost Process, A. N. Tiwari, ETH Zürich 6/7
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Secondary-ion mass spectroscopy (SIMS)<br />
Figure 5 shows SIMS depth profiles of layers at various stages of processing. The IGS films used to<br />
make these samples were not quite of the same thickness, due to their positions in the deposition<br />
chamber, hence conclusions cannot be drawn from apparent changes in thickness. The composition<br />
of the as-deposited IGS layer (A) is homogeneous throughout its depth, however a regular oscillation<br />
in Ga/In signal strength ratio is observed. Since the number of oscillations corresponds to the number<br />
of passes that the substrates made back and forth across the sources, they are attributed to incomplete<br />
mixing of the In and Ga during deposition. The layer analyzed following Cu treatment (B) indicates<br />
that Cu is incorporated from the surface and that loss of In occurs in preference to loss of Ga,<br />
explaining the higher than expected Ga content in the annealed CIGS layers. That Ga-Se compounds<br />
have greater enthalpies of formation than their In-Se analogues is a possible explanation for Cu ions<br />
exchanging more rapidly for In ions than Ga ions. Another explanation involves the fact that the<br />
atomic radii of Cu and In are similar, whilst the ionic radius of Ga is significantly smaller. As a result,<br />
the energy of a Cu ion occupying a Ga site in the IGS layer is likely to be higher than that of a Cu ion<br />
occupying an In site, again making the exchange reaction likely to occur more rapidly for In than for<br />
Ga. The Cu distribution data indicate that some grading of Cu into the underlying IGS layer occurs<br />
during immersion in the solution, however a component of the decaying Cu signal will have arisen<br />
from forward sputtering effects. The depth profiles measured from the annealed layers, both with preheated<br />
Se source (C) and delayed Se supply (D) indicate broadly homogenised depth profiles. However,<br />
in both cases there is a decrease in Ga signal towards the front of the layer which is slightly<br />
more pronounced for the layer annealed with delayed Se supply.<br />
Fig. 5: SIMS depth profiles of as-deposited IGS (A), Cu-treated IGS (B) and layers annealed at 575°C<br />
with Se supplied throughout the entire annealing process (C) and only once substrate temperature<br />
reached �400°C (D). Oscillation in the In and Ga signals in A and B result from substrate<br />
movement during deposition.<br />
92/290<br />
Thin Film CIGS Solar Cells with a Novel Low Cost Process, A. N. Tiwari, ETH Zürich<br />
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