Patent Description:
Photovoltaic cells with passivation layers are known from e.g. <CIT>. A photovoltaic cell according to the pre-characterizing portion of claim <NUM> is known from <CIT>.

A limiting factor in the performance of silicon based photovoltaic cells, also called solar cells hereafter, is recombination of charge carriers at the surface, due to the presence of surface states which facilitate this recombination. Such surface recombination is an issue for solar cells, since charge carriers which recombine at the surface are lost and cannot contribute to the collected current, thereby reducing energy conversion efficiency. In order to reduce surface recombination, the surface must be passivated such that the recombination activity of the surface states is suppressed. This is commonly achieved by deposition or growth of a thin film layer or stack of dielectric or other materials on the semiconductor surface, such that the density of surface states at the interface between the semiconductor and this layer or stack is reduced. Commonly, this layer or stack also induces band bending at the semiconductor surface, such that the surface concentration of one type of charge carrier (either electrons or holes) is reduced. This also reduces surface recombination because recombination requires the presence of both carrier types.

Currently, a large number of materials are known to be effective for semiconductor surface passivation. These include silicon oxide, silicon nitride, amorphous silicon, aluminium oxide, aluminium nitride, hafnium oxide, gallium oxide, titanium oxide, and tantalum oxide. Sometimes these materials are combined in stacks.

Most of these materials result in upward band-bending (accumulation of holes) at the semiconductor surface, due to the fact that they contain negative charge states either in the bulk material or near the semiconductor interface (see <FIG>). This is advantageous for passivation of p-type semiconductor surfaces, but disadvantageous for passivation of n-type semiconductor surfaces. This is because on n-type surfaces such upward band-bending results in the formation of an inversion layer at the surface which facilitates lateral transport of minority carriers to areas of high recombination such as edges, which may lead to shunting. On heavily doped n-type surfaces upward band-bending may even increase rather than reduce surface recombination because the induced band-bending is insufficient to produce full inversion of the surface charge, but only results in depletion or weak inversion of the semiconductor surface.

Known passivation materials which induce downward band-bending (accumulation of electrons) at the semiconductor surface, and are therefore advantageous for passivation of n-type surfaces, include silicon oxide, and silicon nitride, due to the fact that both contain positive charge states. The former however only contains a rather low concentration of charge states (typically < <NUM>×<NUM><NUM> cm-<NUM>), such that the contribution of this induced band-bending to reducing surface recombination is rather small. Silicon nitride can have a much larger charge concentration (> <NUM>×<NUM><NUM> cm-<NUM> [Hezel <NUM>]), however, the charge concentration in passivating silicon nitride films (those which also feature a low density of interface states) is typically somewhat smaller, ranging between about <NUM>×<NUM><NUM> and <NUM>×<NUM><NUM> cm-<NUM> [Hezel <NUM>, Schuurmans <NUM>, Aberle <NUM>, Dauwe <NUM>, Wan <NUM>].

This is significantly smaller than the charge concentrations observed for the best-passivating negatively charged material, aluminium oxide, which typically possesses negative charge concentrations in the range of <NUM>-<NUM> × <NUM><NUM> cm-<NUM>. There is therefore a gap between the availability of passivation materials with a strong negative charge and those with a strong positive charge.

A second important functionality of thin film materials in semiconductor device fabrication is as dopant sources for the formation of highly doped surface regions in a semiconductor substrate. This has for example been demonstrated using deposited phosphorus- and boron-doped silicon oxides, as well as for phosphosilicate and borosilicate glass grown during standard diffusion processes on silicon. Diffusion of dopant species into the semiconductor substrate may be induced by heating the sample surface to high temperatures, either across the whole surface as in a firing furnace, or only locally using for example laser-induced heating (<FIG>). A particularly advantageous case occurs when such thin film dopant sources also function as surface passivation layers. This is the case for aluminium oxide, which both provides effective passivation of p-type surfaces due to its large negative charge, and has been shown to function as a dopant source for aluminium doping of silicon via laser doping. This situation is advantageous because it allows the formation of local diffused contact regions which are self-aligned with the surrounding passivation layers, thereby simplifying processing.

Aluminium and phosphorus sit on either side of silicon in the periodic table. Aluminium is a p-type dopant, and phosphorus an n-type dopant in silicon. Aluminium oxide (Al<NUM>O<NUM>) films are known to possess a large concentration of negative fixed charge when deposited on silicon. Stoichiometric aluminium phosphate (AlPO<NUM>) can be considered to be isoelectronic with silicon oxide (SiO<NUM>), which features a small concentration of positive charge at its interface with silicon.

The present invention relates to a photovoltaic cell comprising a silicon substrate having two opposite main surfaces, wherein a first main surface of the two main surfaces is covered with a passivation layer stack. The passivation layer stack is characterized by:.

The POx- and Al-comprising-layer is a layer comprising phosphorus, aluminium and oxygen, more particularly a layer comprising a mixture of phosporus, aluminium and oxide. Such a passivation layer stack can be tailored to obtain an optimal balance between the effective excess carrier lifetime τeff (s), the fixed charge density Qf (cm-<NUM>) and the interface state density Dit (eV-<NUM>cm-<NUM>). Preferably, the effective excess carrier lifetime τeff is relatively long and the and the interface state density Dit is relatively low. The desired fixed charge density Qε depends on the type of doping, i.e. n- or p-silicon, of the main surface onto which the POx- and Al-comprising-layer is applied.

For example, the POx- and Al-comprising-layer may possess a large positive fixed charge, and may provide an excellent passivation of crystalline silicon surfaces. The silicon at the first main surface of the silicon substrate may be doped by the phosphorus in the POx- and Al-comprising-layer. By this means local, heavily doped regions may be formed which facilitate the formation of electrical contacts to the silicon substrate. The capping layer structure acts as a moisture barrier and provide chemical stability to the POx- and Al-comprising-layer which, dependent on its content, may be instable relative to the environment.

In a first embodiment, the POx- and Al-comprising-layer is a mixed AlPxOy-film. The ratio between the atomic percentage of phosphorus and phosphorus + aluminium (P / (P + Al)) in the POx- and Al-comprising layer is thereby tailored to obtain an optimal balance between the effective excess carrier lifetime τeff(s), the fixed charge density Qf (cm-<NUM>) and the interface state density Dit (eV-<NUM>cm-<NUM>).

As is clear from <FIG>, the atomic percentage of phosphorus and phosphorus + aluminium (P / (P + Al)) in the layer has an impact on the fixed charge density (Qf). By tailoring this ratio, the fixed charge density can be varied from negative to positive charge, in the example from -<NUM>*<NUM><NUM> cm-<NUM> to +<NUM>*<NUM><NUM> cm-<NUM>. The effective excess carrier lifetime τeff is preferably long and this can also be obtained by tailoring the ratio between the atomic percentage of phosphorus and phosphorus + aluminium (P / (P + Al)) as is clear from <FIG>. The effective excess carrier lifetime τeff can even be improved by forming gas annealing and by applying a capping layer of Al<NUM>O<NUM> and optionally subsequent annealing. The interface state density (Dit) is preferably relatively low and this can also be achieved by tailoring the atomic percentage of phosphorus and phosphorus + aluminium (P / (P + Al)) in the POx- and Al-comprising layer.

In an embodiment, the ratio between the atomic percentage of phosphorus and phosphorus + aluminium (P / (P + Al)) in the layer is in the range of <NUM> to <NUM>. In this range, the effective excess carrier lifetime τeff is relatively large, the fixed charge density Qf is positive and the interface state density Dit varies and may be relatively small. This will result in a PV-cell with a good efficiency.

In an embodiment, the ratio between the atomic percentage of phosphorus and phosphorus + aluminium (P / (P + Al)) in the layer is at least <NUM>.

In an embodiment, the POx- and Al-comprising-layer additionally comprises at least one of H, Si, C.

For example H, may be beneficial for reducing the interface state density with the silicon substrate.

Si and additional Al may diffuse in the POx- and Al-comprising layer in the contact region between the POx- and Al-comprising layer and the silicon substrate on the one hand and in the contact region between the POx- and Al-comprising layer and a capping layer structure that comprises Al<NUM>O<NUM> on the other hand.

In an embodiment, a thin SiO<NUM> layer (formed either intentionally or as a by-product of the deposition process) may be present between the Si substrate and the POx film so as to minimize the concentration of electrical interface states (Dit).

In an embodiment, this thin SiO<NUM> layer may have a thickness of <NUM>-<NUM>.

In an embodiment, the capping layer structure may be an aluminium oxide (Al<NUM>O<NUM>) layer. However, note that other materials could possibly be used in this role, especially other oxides or nitrides (e.g. silicon nitride, titanium oxide, silicon oxide etc.). The capping layer structure may also be embodied as a stack of layers, for example a stack of an Al<NUM>O<NUM>-layer and SiNx-layer.

In an embodiment, the POx- and Al-comprising-layer covering the first main surface may have a thickness of less than <NUM>.

In an embodiment, the capping layer structure on top comprises an aluminium oxide (Al<NUM>O<NUM>) layer having a thickness in the range of <NUM>-<NUM>, more preferably in the range of <NUM>-<NUM>.

In an embodiment, a second main surface of the two main surfaces of the silicon substrate may be covered with an Al<NUM>O<NUM> layer.

The Al<NUM>O<NUM> layer provides an excellent passivation of crystalline silicon surface and possesses a negative fixed charge.

In an embodiment the photovoltaic cell having an Al<NUM>O<NUM> layer on the second main surface may comprise a SiO<NUM> layer between the second main surface and the aluminium oxide (Al<NUM>O<NUM>) layer covering the second main surface.

In an embodiment this SiO<NUM> layer may have a thickness in the range of <NUM>-<NUM>.

In a further elaboration of the embodiment with the aluminium oxide (Al<NUM>O<NUM>) layer covering the second main surface, the Al<NUM>O<NUM> layer may be part of a stack which comprises subsequently from the second main surface to the top, the Al<NUM>O<NUM> layer, optionally a SiO<NUM>-layer on top of the Al<NUM>O<NUM> layer, and a SiNx capping layer on top of that.

The present invention also relates to a method for manufacturing a photovoltaic cell, the method comprising:.

The POx- and Al-comprising-layer passivates the silicon and may be tailored to obtain an optimal balance between the effective excess carrier lifetime τeff (s), the fixed charge density Qf (cm-<NUM>) and the interface state density Dit (eV-<NUM>cm-<NUM>). Preferably, the effective excess carrier lifetime τeff is relatively long and the and the interface state density Dit is relatively low. The desired fixed charge density Qε depends on the type of doping, i.e. n- or p-silicon, of the main surface onto which the POx- and Al-comprising-layer is applied.

In an embodiment, the POx- and Al-comprising-layer is a mixed AlPxOy-film which is formed by:
by applying a number of POx-layers and a number of Al-containing layers, wherein the ratio between the atomic percentage of phosphorus and phosphorus + aluminium (P / (P + Al)) in the POx- and Al-comprising-layer is tailored to obtain an optimal balance between the effective excess carrier lifetime τeff (s), the fixed charge density Qf (cm-<NUM>) and the interface state density Dit (eV-<NUM>cm-<NUM>), wherein the tailoring is effected by applying a desired number of POx-layers and a desired number of Al-comprising layers for forming the mixed AlPxOy-film.

By applying a desired number of POx-layers and a desired number of Al-comprising layers, e.g. Al<NUM>O<NUM>-layers, the ratio P / (P + Al) within the POx- and Al-comprising-layer can be exactly obtained as desired. Especially when the layers are formed by ALD, for example in a spatial atmospheric system as the one marketed under the brand name Levitrack, the POx-layers and the Al<NUM>O<NUM>-layers are monolayers and the ratio P / (P + Al) within the POx- and Al-comprising-layer can be defined exactly.

In an embodiment, the ratio between the atomic percentage of phosphorus and phosphorus + aluminium (P / (P + Al)) in the layer is in the range of <NUM> to <NUM>.

In an embodiment, the POx- and Al-comprising-layer may formed by applying at least one POx-layer and by applying at least one Al-containing layer and subsequently anneal the stack of the at least one POx-layer and the at least one Al-containing layer so as to mix the Al and P to obtain a mixed AlPxOy film.

In an embodiment, the POx-layers and Al-comprising layers are alternately applied so as to form a stack of layers. Such an alternating stack of POx-layers and Al-containing layers leads to a very well mixed AlPxOy film after annealing.

In an embodiment, the application of at least one POx-layer and at least one Al-containing layer and a subsequent POx-layer and a subsequent Al-comprising layer an intermediate anneal step is performed so as to mix the Al and P in the previously applied at least one POx-layer and at least one Al-containing layer to obtain a mixed AlPxOy film on top of which the subsequent POx-layer and a subsequent Al-containing layer are applied.

When annealing is done several times during the formation of the AlPxOy film, a very homogeneous content of the mixed AlPxOy film will be obtained.

In an embodiment, first the POx-layers and Al-comprising-layers are alternately applied so as to form the stack of layers and subsequently the stack of layers is annealed so as to mix the Al and P to obtain a mixed AlPxOy film. In this embodiment, the annealing is done after all the layers of the POx- and Al-comprising-layer are applied. It may depend on the type of layer application process whether intermediate annealing is preferred or whether annealing after application of the entire stack of POx-layers and Al-comprising-layers is preferred. In a spatial atmospheric system as the one marketed under the brand name Levitrack, the intermediate annealing is feasible without almost any delay in the formation of the PV-cell.

In an embodiment, the applying of the POx- and Al-comprising-layer on the first main surface may be effected by means of pulsed, spatial or batch atomic layer deposition (ALD) or pulsed, spatial or batch chemical vapour deposition (CVD).

In a further elaboration of this embodiment, the pulsed, spatial or batch chemical vapour deposition (CVD) may be pulsed, spatial or batch plasma enhanced chemical vapour deposition (PECVD).

In an embodiment, the pulsed, spatial or batch atomic layer deposition (ALD) or pulsed, spatial or batch chemical vapour deposition (CVD) for the applying of the POx-and Al-comprising-layer on the first main surface may be done by alternately exposing the surface to trimethyl phosphate (TMP) and an O-containing reactant, chosen from the group comprising O2 plasma, H<NUM>O, O<NUM> and H<NUM>O<NUM> and alternately exposing the surface to trimethyl aluminium (TMA) and an O-containing reactant, chosen from the group comprising O<NUM> plasma, H<NUM>O, O<NUM> and H<NUM>O<NUM>.

In an embodiment, the first main surface may be exposed to a purge gas, such as N<NUM>, between each exposure to trimethyl phosphate and exposure to the O-containing reactant. Thereby, the first main surface may also be exposed to a purge gas, such as N<NUM>, between each exposure to trimethyl aluminium and exposure to the O-containing reactant. In an embodiment, the pulsed, spatial or batch atomic layer deposition (ALD) or pulsed, spatial or batch chemical vapour deposition (CVD) may performed in an atmospheric ALD or CVD systems, such as the spatial atmospheric system marketed under the brand name Levitrack.

In an embodiment, the pulsed, spatial or batch atomic layer deposition (ALD) or pulsed, spatial or batch chemical vapour deposition (CVD) may be performed in a low-pressure deposition system.

With a low-pressure deposition system, a system is meant in which the pressure is subatmospheric.

In an embodiment, the applying of the POx- and Al-comprising-layer on the first main surface of the silicon substrate may effected at a temperature in the range of <NUM>-<NUM>, more preferably <NUM>-<NUM>.

In an embodiment, the applying of the capping layer structure may comprise the applying of an Al<NUM>O<NUM> layer.

In an embodiment, the applying of the Al<NUM>O<NUM> layer may effected in the same atmospheric spatial ALD system as the applying of the POx- and Al-comprising-layer and immediately follows the applying of the POx- and Al-comprising-layer without removing the substrate from the atmospheric spatial ALD system so that the POx- and Al-comprising-layer is not exposed to air or moisture before the capping layer structure of Al<NUM>O<NUM> is applied onto the POx- and Al-comprising-layer.

In an embodiment, the applying of the POx- and Al-comprising-layer and the applying of the Al<NUM>O<NUM> layer may be effected in different modules of an ALD, CVD and/or PECVD system, in which air exposure of the POx- and Al-comprising-layer is avoided by transferring the substrates from a module in which the POx- and Al-comprising-layer is applied to a module in which the Al<NUM>O<NUM> layer is applied in an inert ambient or in vacuum.

In an embodiment, the applying of the Al<NUM>O<NUM> capping layer is effected at a temperature in the range of <NUM>-<NUM>, more preferably <NUM>-<NUM> and even more preferably <NUM>-<NUM>.

The invention is further elucidated in the detailed description with reference to the following figures.

POx films were deposited on a main surface of a silicon substrate in an atomic layer deposition (ALD) reactor at temperatures between <NUM> and <NUM> by exposing samples alternately to trimethyl phosphate (TMP) and an O<NUM> plasma reactant in a cyclic fashion, with separating N<NUM> purges. This process resulted in linear thin film growth following an initial nucleation delay, with a growth-per-cycle (GPC) of between <NUM> and <NUM>Å depending on the temperature and TMP exposure time (saturation of the GPC with respect to the precursor dose was not observed, at least at a deposition temperature of <NUM>, so that this process should be considered a pulsed chemical vapour deposition process rather than true ALD). Note that other phosphorus-containing precursors, and other reactants (e.g. H<NUM>O, O<NUM>, H<NUM>O<NUM>), could potentially be used in place of TMP and O2 plasma to deposit the POx layer in a similar manner. It may also be possible to use other deposition methods to deposit the POx layer in place of ALD, for example chemical vapour deposition, evaporation, sputtering, or solution-based methods.

Al<NUM>O<NUM> capping layers were deposited in-situ immediately following POx deposition at the same temperature using trimethyl aluminium (TMA) and O<NUM> plasma. The Al<NUM>O<NUM> films could in principle also be deposited using other precursors or reactants, or by other deposition methods. The Al<NUM>O<NUM> capping layer could also possibly be replaced by another material with suitable moisture barrier properties, for example silicon nitride or titanium oxide.

Deposition of the passivation stacks was performed in a low-pressure (base pressure of ~<NUM>-<NUM> Torr) deposition system with a low concentration of water vapour. Alternatively, the stacks could also be deposited in atmospheric ALD or CVD systems, such as in e.g. the Levitrack tool that is currently marketed for Al<NUM>O<NUM> deposition. Uncapped POx films were observed to visibly degrade within minutes on exposure to atmosphere, with the formation of fractal cracking patterns and blisters, presumably due to atmospheric moisture. In contrast, POx films capped by Al<NUM>O<NUM> appeared to be stable over weeks and months of atmospheric exposure. Gradual blister formation was observed for thicker POx films (∼<NUM>-<NUM>) capped by Al<NUM>O<NUM> in an as-deposited state. Annealing such stacks at a temperature of <NUM> in N<NUM> for <NUM> minute immediately following deposition resulted in improved stability and blister-free films. POx films thicker than <NUM> and capped by Al<NUM>O<NUM> exhibited significant cracking within minutes of exposure to atmosphere and significant blistering on annealing. Therefore, POx film thickness is preferably kept below <NUM>.

To avoid air exposure of the rather reactive POx film, the deposition of the POx/Al<NUM>O<NUM> stack could be carried out in one integrated process flow in a spatial ALD system such as the Levitrack tool. In such a system different precursors can be injected at different segments along the track that are heated to different temperatures. In that way it is possible to carry out the two processes at different temperature, e.g. POx at <NUM>, and AlOx at <NUM>, without exposure to air in between.

X-ray photoelectron spectroscopy (XPS) compositional depth profiling (using sputtering) of POx/Al<NUM>O<NUM> stacks (<FIG>) showed the existence of a POx- and Al-comprising-layer below the Al<NUM>O<NUM> capping layer, i.e. AlPxOy layer. There is also a thin silicon oxide (SiOx) layer likely formed by O<NUM> plasma exposure during the initial deposition cycles when the POx is still nucleating. Carbon concentrations were below the detection limit (<<NUM>%) through the whole stack.

To investigate the passivation properties of these layers, <NUM>-<NUM> thick POx films were deposited in an atomic layer deposition (ALD) reactor from trimethyl phosphate (TMP) using an O<NUM> plasma reactant at temperatures of <NUM> and <NUM>. ~<NUM> thick Al<NUM>O<NUM> capping layers were deposited in-situ at the same temperature using trimethyl aluminium (TMA) and O<NUM> plasma. Control samples featuring Al<NUM>O<NUM> only (without POx) were deposited in the same way. Symmetric carrier lifetime test structures were fabricated on <NUM> pm thick double-side-polished float-zone (<NUM>) <NUM>-<NUM>Ω cm n-type Si wafers, which received a standard RCA clean and HF dip immediately prior to POx/Al<NUM>O<NUM> or Al<NUM>O<NUM> deposition. Following deposition, samples were annealed consecutively at a series of increasing temperatures for <NUM> minutes in N<NUM>. Carrier lifetime measurements were performed using a Sinton WCT-120TS photoconductance lifetime tester.

<FIG> shows the measured effective excess carrier lifetime τeff as a function of post-deposition annealing temperature for samples passivated by POx/Al<NUM>O<NUM> or by Al<NUM>O<NUM> only. Two points are immediately clear. Firstly, POx/Al<NUM>O<NUM> is capable of providing excellent levels of surface passivation, comparable or better than that of plasma ALD Al<NUM>O<NUM> films deposited at the same temperature, with peak lifetimes of <NUM> and <NUM> for stacks deposited at <NUM> and <NUM> respectively (it should be noted that these temperatures are not optimal for Al<NUM>O<NUM> passivation). Secondly, the dependence of passivation quality on annealing temperature is fundamentally different for POx/Al<NUM>O<NUM> stacks compared to Al<NUM>O<NUM> alone. In particular, a significant increase in lifetime is observed at significantly lower annealing temperatures, with lifetimes on the order of <NUM> observed already after annealing for <NUM> minutes at <NUM>. The latter point shows clearly that the passivation provided by the POx/Al<NUM>O<NUM> stacks is not simply due to the Al<NUM>O<NUM> capping layer, and that the interfaces formed by these two materials with c-Si are fundamentally dissimilar. The passivation of films deposited at <NUM> was observed to degrade already on annealing at <NUM>, but the lifetime of films deposited at <NUM> degraded only at <NUM>.

Closer examination of the injection-dependent lifetime data (<FIG>) reveals some further differences between films deposited at <NUM> and <NUM>. The lifetime of samples passivated at <NUM> after annealing at <NUM> is well-described by a single-diode model, with a saturation current density J<NUM> of <NUM> fA/cm<NUM> per side, suggesting that the surface is strongly accumulated or inverted due to charge in the dielectric stack. Following annealing at higher temperatures the lifetime simultaneously increases in high injection, while decreasing in low injection, such that the surface recombination can no longer be adequately parameterized by J<NUM>. In contrast, the stacks deposited at <NUM> exhibit single diode behaviour over a much wider temperature range, with an exceptionally low J<NUM> of ~<NUM> fA/cm<NUM> per side observed after annealing at <NUM>. A deposition temperature of <NUM> therefore appears preferable. These differences in injection dependence may relate to differences in the magnitude of fixed charge. Interestingly, stacks deposited at both temperatures exhibit similarly high lifetimes in high injection, with corresponding <NUM>-Sun implied open-circuit voltages of ~<NUM> mV. These represent exceptionally high values and show the outstanding passivation potential of such stacks.

The fixed charge concentration Qf of the POx/Al<NUM>O<NUM> stacks was determined using high-frequency (<NUM>) capacitance-voltage measurements (<FIG>). A positive fixed charge of between <NUM> and <NUM>×<NUM><NUM> cm-<NUM> was found for POx/Al<NUM>O<NUM> stacks deposited at <NUM> and annealed at temperatures of <NUM>-<NUM>, compared to a negative fixed charge of around <NUM>×<NUM><NUM> cm-<NUM> for the same Al<NUM>O<NUM> films without POx. This charge is significantly larger than that of standard silicon nitride (SiNx) films commonly used to passivate n-type silicon surfaces. The capacitance-voltage measurements also indicate that the investigated POx/Al<NUM>O<NUM> stacks feature a very low density of interface states (Dit), comparable or lower than that of Al<NUM>O<NUM>, and significantly lower than that of SiNx, which along with the large fixed charge accounts for the excellent passivation of these stacks. This is likely due to the formation of a well-controlled SiOx interface and effective hydrogenation by the capping Al<NUM>O<NUM>.

<FIG> shows the effective excess carrier lifetime τeff vs the ratio between the atomic percentage of phosphorus and phosphorus + aluminium (P / (P + Al)) in the layer. From this figure it is clear that the effective excess carrier lifetime is high when the ratio P / (P + Al) is between <NUM> - <NUM> and between <NUM> - <NUM>. Forming gas annealing and the application of a capping layer of Al<NUM>O<NUM> improve the excess carrier lifetime so that even in along the entire ratio range good values for the effective excess carrier lifetime may be obtained.

<FIG> shows the fixed charge density Qf (cm-<NUM>) vs the ratio between the atomic percentage of phosphorus and phosphorus + aluminium (P / (P + Al)) in the layer. From diagram it is clear that the fixed charge density can be tailored from negative to positive as desired by changing the ratio between the atomic percentage of phosphorus and phosphorus + aluminium (P / (P + Al)) in the layer. In the range between <NUM> - <NUM> the fixed charge density is between <NUM> and <NUM>. In this range of <NUM> - <NUM> a good value of the fixed charge density may be obtained and at the same time a very low interface state density may be obtained as well, which is advantageous.

<FIG> shows the interface state density Dit (eV-<NUM>cm-<NUM>) vs the ratio between the atomic percentage of phosphorus and (phosphorus + aluminium) (P / (P + Al)) in the layer. A low interface state density and a relatively high positive fixed charge density may be obtained when the ratio between the atomic percentage of phosphorus and phosphorus + aluminium (P / (P + Al)) in the layer is between <NUM> - <NUM>.

The invention is not limited to the examples described in the detailed description.

Claim 1:
A photovoltaic cell comprising a silicon substrate having two opposite main surfaces, wherein a first main surface of the two main surfaces is covered with a passivation layer stack,
characterized in that
the passivation layer stack comprises:
- a POx- and Al-comprising-layer covering the first main surface, and
- a capping layer structure which covers the POx- and Al-comprising-layer.