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The area of thin-film photovoltaics has been overwhelmed by organometal halide perovskites. Unfortunately, serious stability concerns arise with perovskite solar cells. For example, methyl-ammonium lead iodide is known to decompose in the presence of water and, more severely, even under inert conditions at elevated temperatures. Here, we demonstrate inverted perovskite solar cells, in which the decomposition of the perovskite is significantly mitigated even at elevated temperatures. Specifically, we introduce a bilayered electron-extraction interlayer consisting of aluminium-doped zinc oxide and tin oxide. We evidence tin oxide grown by atomic layer deposition does form an outstandingly dense gas permeation barrier that effectively hinders the ingress of moisture towards the perovskite and—more importantly—it prevents the egress of decomposition products of the perovskite. Thereby, the overall decomposition of the perovskite is significantly suppressed, leading to an outstanding device stability.
Solar cells based on organolead halide perovskites have seen tremendous progress over the past 5 years1. Although their power conversion efficiency (PCE) has skyrocketed to reach a level of >20% (ref. 2), concerns about their stability are still intimately linked to this technology3,4,5.
Generally, there is consensus that perovskites like CH3NH3PbI3 decompose to their constituents, that is, HI, CH3NH2 and PbI2, in the presence of water6. Moreover, the intrinsic decomposition of CH3NH3PbI3 to CH3NH3I and PbI2, which is thermally activated and which occurs even under inert conditions, states a more fundamental problem7,8. At the same time, there are secondary effects of perovskite decomposition such as the degradation of functional building blocks in the solar cell because of the corrosive effect of the perovskite decomposition products9. Specifically, the corrosion of metal electrodes like Ag or Al has been identified to be a critical issue10. Overall, without proper concepts to overcome these reliability issues, the prospects of wide-spread application and commercialization of organolead halide perovskite technology may be significantly compromised.
Among the various device architectures for perovskite solar cells, the inverted planar geometry has been shown to yield devices essentially free of hysteresis11,12. Here, the photogenerated holes are extracted via the bottom electrode using a hole-extraction interlayer (for example, poly(3,4-ethylenedioxythiophene) polystyrene sulfonate (PEDOT:PSS)), while the electron extraction proceeds via the top electrode. The energetic alignment of CH3NH3PbI3 and [6,6′]-phenyl-C61-butyric acid methyl ester (PCBM) has been shown to be especially favourable for the extraction of electrons from the conduction band of the perovskite13. To overcome the stability issues discussed above, several groups have introduced inverted planar perovskite cells based on metal oxides as electron- and hole-extraction interfacial layers adjacent to the cathode and anode, respectively14,15. Chen et al.15 employed a sol-gel Ti(Nb)Ox electron-extraction layer that was aimed to protect the perovskite against moisture from ambient atmosphere. Because of its poor electrical conductivity of 10−5Scm–1, the authors had to limit the thickness of the sol-gel Ti(Nb)Ox to 10nm. Moreover, it is known that sol-gel-derived layers state only relatively poor permeation barriers16. As a result, the device stability tests that afforded a lifetime of 1,000h were done with additional encapsulation. Kaltenbrunner et al.17 have used Cr2O3/Cr at the cathode side to protect the metal cathode and thereby to improve the stability under ambient conditions, but still the efficiency was found to drop to 80% of its initial value after only 28h. Very recently, Guerrero et al.18 confirmed the protective effect of the Cr2O3/Cr interlayer but still found some severe degradation after only a few hours. You et al.14 have shown that devices based on indium tin oxide (ITO)/NiO/perovskite/ZnO/Al were stable for tens of days in ambient conditions, whereas a reference device based on ITO/PEDOT:PSS/perovskite/PCBM/Al showed severe degradation within half a day. Especially, the ZnO layer, which has been spin coated from a nanoparticle dispersion on top of the perovskite, has been claimed to protect the Al electrode against corrosion. Very recently, Bush et al.19 have found that in their devices a similar nanoparticle-based ZnO layer next to the cathode did not provide any sufficient protection at elevated temperatures. As solar cells in outdoor conditions may reach a temperature significantly above 25°C, the latter result appears to be extremely relevant. Other reports have evidenced rapid decomposition of CH3NH3PbI3 when in direct contact with ZnO20.
Here we propose an inverted cell architecture, where a bilayered aluminium-doped ZnO (AZO)/tin oxide (SnOx) electron-extraction layer (EEL) affords perovskite solar cells with a remarkable resilience against moisture and heat. AZO is excellently suited to extract electrons from the lowest unoccupied molecular orbital of fullerenes21. However, the nanoparticle-based AZO layer does not provide sufficient protection against the ingress of moisture or the egress of perovskite decomposition products. Thus, we add a thin SnOx layer to form a bilayered AZO/SnOx EEL assembly. The SnOx is grown by low-temperature atomic layer deposition (ALD) at 80°C that affords extremely dense, conformal and pinhole-free layers. Please note that there are reports where ALD layers have been directly deposited on top of perovskites to improve their resilience against ambient atmosphere and heat22. However, these ALD layers were not a functional part of a device, and therefore most of the experiments were based on electrical insulators like Al2O3. SnOx layers grown by ALD are optically highly transparent, electrically conductive and provide outstanding gas permeation barrier properties with a water vapour transmission rate as low as 7 × 10−5g (m−2day−1), even when grown at a low temperature23. Their water vapour transmission rate is orders of magnitude better than that of sputtered ITO thin films or that of solution processed metal oxide layers. The electrical conductivity of the SnOx layer on the order of 5 × 10−3Scm−1 allows us to place it between the sensitive electrode and the photoactive layers without adding any noticeable series resistance. Thereby, the SnOx provides outstanding protection of the perovskite against the ingress of moisture and, more importantly, at the same time it serves as permeation barrier against the out-diffusion of decomposition products of the perovskite. We will show that the sealing property of the SnOx layer contains the decomposition products inside the cell and, thereby, the overall decomposition of the perovskite is significantly suppressed. Although cells based on LiF/Al or AZO degrade within tens of hours in ambient air (23°C and 50% relative humidity (rH)), devices based on AZO/SnOx show superior stability of their solar cell characteristics even on a timescale of >350h. More strikingly, at 60°C under inert atmosphere, AZO-based devices degrade within 100h because of thermally induced decomposition of the perovskite. On the contrary, the suppressed out-diffusion of decomposition products because of the diffusion-barrier properties of the AZO/SnOx EEL affords cells that are essentially unchanged even after >1,000h under the same conditions. Our paper reports a general strategy to achieve a substantially improved device lifetime in the case of photoactive materials that may come with concerns about their intrinsic compositional stability.
The devices used in this study are based on a planar inverted cell layout, where the holes are extracted via the bottom electrode (substrate electrode). The layer sequence is shown in Fig. 1. As hole-extraction layer, PEDOT:PSS is used, whereas for electron extraction a 100nm thick PCBM layer is deposited on top of the typically 180nm thick CH3NH3PbI3 perovskite layer. Directly adjacent to the PCBM we have used a 100nm thick AZO layer prepared from a nanoparticle dispersion in isopropylalcohol. In some cells, a SnOx layer is deposited on top of the AZO layer by ALD at 80°C to form the bilayered electron-extraction assembly (AZO/SnOx). The nominal thickness of the SnOx layer is 20nm. As the AZO layer is derived from a nanoparticle dispersion, it contains pores that are partially coated with SnOx because of the conformal nature of the ALD process. A more detailed discussion of the SnOx growth on top of the AZO layer is provided in the Supplementary Fig. 1. Please note that we have also prepared devices with SnOx deposited directly on top of PCBM, but the stability of the resulting devices was inferior to that of the AZO/SnOx cells (see discussion below). Reference devices based on ITO/PEDOT:PSS/Perovskite/PCBM/LiF/Al have also been included in our study.
The external quantum efficiency (EQE) spectrum of a typical AZO/SnOx-based perovskite solar cell is shown in Fig. 1b. The J/V characteristics of the device measured in forward and reverse direction (scan speed: 500mVs−1) are presented in Fig. 1c. No substantial hysteresis is found in the J/V data. The extracted characteristics Voc=0.95V, FF=74% and a Jsc=18mAcm−2 result in a PCE of 12.8%. We want to note that the perovskite precursor used in this study was commercially obtained from Ossila Ltd with a typically specified efficiency in the range of 11–13% (see Methods for details).
Significantly higher PCEs can be achieved by using, for example, optimized precursor inks or mixed-cation/mixed-halide perovskite absorbers24. As the EEL is in the core of this report, further optimization of the perovskite system itself was considered to be beyond the scope here.
A very striking advantage of the bilayered AZO/SnOx EEL in direct comparison with AZO is displayed in Fig. 2. Here, the stability of the cell characteristics is shown for devices that were continuously exposed to ambient air at 23°C and 50% relative humidity. The devices that were based on a single layer of AZO as EEL degrade swiftly within ~50h. A severe decay of the FF from ~70% to <25% and a concomitant drop of the Jsc from ~17 to 8.2mAcm−2 is found. Opposed to that, the characteristics of the corresponding cells with the bilayered EEL of AZO/SnOx do not show any degradation even after >300h in air. Note that the thickness of the SnOx layer is only 20nm in these devices. There is a slight increase of the Voc in the AZO/SnOx samples that happens on a timescale of several tens of hours. This increase is only observed in the AZO/SnOx samples, as the LiF/Al and the AZO cells already undergo strong degradation on the same timescale. A similar increase of Voc on such a long timescale has been seen by other authors and it has been explained by an ageing effect that reduces the density of trap states in the perovskite25. As a reference, the cells based on LiF/Al are essentially degraded within ~1 day.
In order to analyse the reasons underlying the strikingly different degradation phenomena shown in Fig. 2, we have performed X-ray diffraction (XRD) and X-ray photoelectron spectroscopy (XPS) studies of the respective device structures. Note that in case of the XPS measurements, a thinner top Ag electrode was chosen (10nm) compared with the actual solar cells (100nm) because of the small probing depth of the technique. Looking first at the AZO-based device, the XRD spectrum shows the (110) and (220) reflections of tetragonal MAPbI3 at angles of 14.11° and 28.14, respectively. As this XRD measurement has been made on a full device stack, further signals related to the Ag and ITO electrodes are visible. A detailed assignment of these peaks is shown in the Supplementary Fig. 3. Only a very weak signal due to PbI2 was found that did not significantly increase even after 7 days in air (Fig. 3a). Thus, no severe decomposition of the perovskite to PbI2 upon storage in air can be inferred from the XRD data. On the other hand, when XPS was used to look for degradation products on the surface, a notable amount of iodine was evidenced on the AZO sample (Fig. 3b) after exposure to air for 2 days, whereas on identical samples kept in nitrogen no such iodine signal is found. Please note that the peak of ~622eV in the XPS spectrum of the aged AZO cell does not represent another bonding state of the iodine, but it is rather a so-called shake-up peak. Such shake-up peaks are commonly observed in strong XPS signals. The survey XPS spectra can be found in the Supplementary Fig. 4. Plan-view scanning electron microscopy (SEM) images of the AZO samples aged in air show the formation of spot-like degradation motifs (Fig. 3c,d). These spots point to the local ingress of moisture and out-diffusion of decomposition products of the perovskite, supported by the appearance of the iodine signal in XPS. In the degraded spots, needle-like features occur. Similar features have been reported for Ag electrodes corroded by the decomposition products of MAPbI3 (ref. 26). Our findings are also in line with the results of Kato et al.10 who unveiled a moisture promoted corrosion mechanism of Ag which resulted in the formation of products like AgI. The role of water in the electrode corrosion is further clarified below in cells aged under inert conditions.
To explain the spot-like degradation, we can assume that structural defects, such as pinholes, in the AZO NP layer would give rise to locally enhanced water permeation. Opposed to that, the sample with the bilayered EEL of AZO/SnOx does not show any sign of degradation in SEM (Fig. 3e) under identical conditions. In XPS, only a negligible amount of iodine at the surface of the AZO/SnOx samples can be detected. For comparison, we have also studied layer stacks where only SnOx, that is, without AZO between the PCBM and the SnOx, has been used as EEL. We have recently shown that SnOx with a work function of 4.1eV forms an excellent EEL layer in inverted organic solar cells27. Here, the resulting perovskite solar cells based on SnOx were more stable than the devices based on AZO. However, they showed a statistical failure on a timescale of 100h (Supplementary Fig. 5). This finding could be explained by a nonideal ALD growth of the SnOx directly on top of the organic PCBM layer. ALD as a chemical deposition technique relies on self-limiting chemical reactions on the sample surface28. For the ALD deposition of oxide layers, –OH surface groups form the nucleation sites for layer growth. In this sense, on organic surfaces like PCBM the nucleation of an ALD layer may deviate significantly from the growth on a surface rich of –OH groups29. Therefore, we can assume that the SnOx layer grown on PCBM is not free of some pin-hole defects that compromise its functionality as diffusion barrier. Consequently, substantially more iodine is detected on the surface after exposure to air compared with the AZO/SnOx device (Fig. 3b). Thus, we conclude that the AZO serves two purposes in the bilayered AZO/SnOx EEL: (1) its electronic structure has been shown to facilitate electron extraction from the PCBM (ref. 21) and (2) the AZO layer provides an improved (oxide-) surface for the nucleation of the subsequent SnOx ALD layer that can thus from a dense, pin-hole-free permeation barrier. Figure 3f,g shows schemes portraying the specific differences between AZO and AZO/SnOx as EEL in devices exposed to air.
As indicated before, the AZO layer prepared from the NP dispersion does not provide a significant diffusion barrier against the local ingress of moisture from the ambient air. As a result, decomposition of the MAPbI3 perovskite occurs and yields iodine-based products that migrate to the surface. In the case of AZO/SnOx, substantially better moisture barrier properties prevent the penetration of water. The claim of superior moisture barrier properties of the bilayered AZO/SnOx EEL compared with that of the AZO NP layer is also supported by Ca-corrosion tests (Supplementary Fig. 6).
It has to be noted that the detrimental effects of ambient air could in principle be avoided by using a proper encapsulation of the entire solar cell. However, the out-diffusion of decomposition products from the perovskite and the degradation of the metal electrode (Fig. 3c,d) may impose a more fundamental issue. This is even more important, as earlier reports evidenced the thermally activated decomposition of the MAPbI3 perovskite even under inert atmosphere7.
To study the long-term stability of our solar cells under inert conditions, we have stored a set of devices in a glove box under N2 atmosphere. All the devices were placed on a hot plate at 60°C and their characteristics were measured repeatedly. Most remarkably, the characteristics of devices based on AZO EELs degraded on a timescale of 100h (Fig. 4). Although the Jsc and Voc of these devices remain fairly stable, the decay of the FF results in the severe drop of PCE to ~2% after 360h. The degradation motif in the AZO-based cells is essentially different from that found in ambient air, where all cell characteristics decayed within a day (Fig. 2). Again in striking contrast, the characteristics of devices based on the bilayered AZO/SnOx EEL remain almost unchanged even after 1,032h. Note that the hysteresis did not increase in the course of ageing.
To unravel the mechanisms behind these results, we have again performed XRD and XPS studies of the respective device structures. After heating the device stacks for 6 days under inert atmosphere, the XRD spectrum of the AZO samples reveals a significant signal due to PbI2 that is absent in pristine stacks (Fig. 5a). The formation of PbI2 indicates the thermally activated decomposition of the perovskite upon heating, in agreement with earlier reports7. Opposed to that, the devices based on the bilayered AZO/SnOx EEL do not show any signature of a PbI2 phase after identical ageing conditions (Fig. 5b).
The formation of PbI2 in the AZO samples is in contrast to the degradation experiments in air, where no PbI2 phase in the AZO samples was found in XRD (Fig. 3a). At the same time, the I3d5/2 XPS spectra (Fig. 5c) do not reveal any significant increase of the amount of iodine at the surface of any of the samples aged in N2. Please note that the noise in the XPS spectra indicates that the concentration of I3d5/2 at the surface of all the samples is close to the detection limit and variations between the samples are within the measurement error. A plan-view SEM image of the aged AZO samples does not reveal any degradation of the Ag electrode, in contrast to the experiment where the ageing took place in air (Fig. 3c,d). Thus, we conclude that in the case of AZO, volatile decomposition products of the MAPbI3 perovskite evaporate from the cell stack without degradation of the Ag electrode. In air, other than in N2, the presence of water would promote the corrosion of Ag because of CH3NH3I and other halide compounds10. However, the loss of CH3NH3I etc. drives the further decomposition of the perovskite.
Taken together, the device characteristics (Fig. 4) and the XRD and XPS spectroscopy point to a scheme of degradation as shown in Fig. 5e,f. Under inert atmosphere, the thermally activated degradation of the perovskite leads to decomposition products that can easily diffuse through the PCBM/AZO/Ag layers on top of the perovskite. The less volatile PbI2 phase remains in the active layer leading to a substantial decay of the FF of the corresponding devices (Fig. 4c). Moreover, it has been shown earlier that a change in film stoichiometry (Pb poor to Pb rich) may substantially alter the electronic properties of the perovskite and especially the position of the conduction and valence band with respect to the vacuum level30. Towards increasingly Pb-rich conditions, the ionization energy of the perovskite has been shown to increase significantly to values in excess of 6eV that would render the extraction of holes more and more challenging.
Opposed to the case of the AZO cells, the AZO/SnOx-based cells do not show any formation of PbI2 under otherwise identical conditions. We therefore conclude that the decomposition products are contained inside the cell stack because of the dense SnOx layer forming a permeation barrier. Thereby, the equilibrium of the decomposition/formation reaction would be shifted to stabilize the perovskite. Thus, the decomposition of the MAPbI3 obviously is significantly slowed down, and the cells do not show significant degradation even after heating for >1,000h (Fig. 4). It has to be noted that it is favourable to position the permeation barrier between the perovskite and the Ag electrode, as thereby the known long-term corrosive effect of residual halide components on the Ag electrode31 and on the interface EEL/Ag can be efficiently suppressed. In further work, this concept could even be extended to a setup, in which the perovskite layer is sandwiched between diffusion barriers at the cathode and anode side, in case permeable substrates like polymer foils are used. For example, there are reports on using ALD to prepare V2O5 layers32. V2O5 is a high work function transition metal oxide that has successfully been used for hole extraction in organic and perovskite solar cells33,34,35,36. ALD prepared V2O5 would presumably provide similar gas permeation barrier properties as those shown for the SnOx. Thereby, the intrinsic decomposition of the perovskite active layers would be substantially delayed or even prevented as volatile decomposition products would be hindered from evaporating.
Aside from the so-called mono-stress conditions like elevated temperature, multi-stressing can be considered. To this end, we conducted set of long-term light soaking tests at 60°C under N2, in which the devices were simultaneously illuminated with a white light-emitting diode (LED) to achieve the same Jsc as upon AM1.5G solar irradiation (for details see the Methods section). The results of this multi-stress experiment are shown in the Supplementary Fig. 8. Briefly, again the AZO/SnOx cells are substantially more stable than the AZO cells under concomitant heat and illumination. This difference is in part because of the suppressed decomposition of the perovskite owing to heat in case of the AZO/SnOx (in agreement with the discussion of Fig. 4). However, there is a clear degradation even of the AZO/SnOx samples where the PCE decays to roughly 60% of its initial value after 300h. This is in contrast to the case where only thermal stress has been used. Earlier work has unravelled the photo-induced degradation of solar cells based on MAPbI3. Whereas Misra et al.37 identified a photoactivated decomposition mechanism, more recently Nie et al.38 reported that continuous illumination of MAPbI3 caused the formation of trap states that spoiled the solar cell performance, especially Jsc. Although our sealing approach based on the impermeable AZO/SnOx electron extraction layer has been shown to efficiently suppress the decomposition of the perovskite, it cannot suppress the formation of trap states in the perovskite. Similar to the report of Nie et al.38 the cell characteristics recover after stressing, if the cells are kept in darkness (Supplementary Fig. 8f). This is why we conclude that photo-induced trap-state formation occurs in our cells. However, there have been recent reports confirming that photo-induced degradation is not a general problem of organolead halide perovskites, and some optimized mixed cation/mixed halide perovskite active materials were shown to be far less prone to light soaking degradation24,39. Heat was found to be a dominating source of degradation in these mixed cation perovskite cells40. Note that our inverted device structure based on the impermeable AZO/SnOx electron extraction layer is generally applicable and can also accommodate these next-generation perovskite photoactive systems with enhanced stability and efficiency41.
In summary, we have shown an ultra-stable inverted cell architecture, where a bilayered AZO/SnOx EEL has been demonstrated to afford perovskite solar cells with a remarkable resilience. The 20nm thin ALD grown SnOx has been evidenced to form an outstandingly dense gas permeation barrier that effectively hinders the ingress of moisture towards the perovskite and—more importantly—it prevents the egress of decomposition products like CH3NH3I, HI out of the perovskite.
Although the efficiency of cells based on LiF/Al or AZO degraded to <50% of the initial value within less than a day in ambient air, devices based on AZO/SnOx showed superior stability of their solar cell characteristics even on a timescale of >350h. Under inert atmosphere, AZO-based devices degraded to roughly 50% of its initial efficiency within 100h because of thermally induced decomposition of the perovskite. On the contrary, the suppressed out-diffusion of decomposition products because of the diffusion-barrier properties of the AZO/SnOx EEL has been shown to significantly slow down the thermally activated decomposition of the perovskite. This afforded cells that did not change even after >1,000h. The concept of impermeable EELs is generally applicable and therefore is expected to provide an avenue to achieve a substantially improved device lifetime of solar cells based on organometal halide perovskites even beyond MAPbI3.
The inverted perovskite solar cells studied in this work are based on the following layer sequence: glass/ITO/PEDOT:PSS/perovskite/PCBM/EEL/Ag (see Fig. 1a). The PEDOT layer (AI4083) has been spin coated in ambient air and dried on a hot plate at 120°C for 20min in air and for another 20min in a glove box under N2 atmosphere. The perovskite layer has been spin coated under inert atmosphere from a commercially available precursor solution (Ossila) and the resulting layers were thermally annealed at 100°C for 80min. The typical layer thickness was 180nm.
On top of the perovskite, PCBM (American Dye Sorce Inc., ADS61BFA) was spin coated from a solution in chlorobenzene (concentration: 100mgml−1). AZO has been deposited from a commercial nanoparticle dispersion (2.5wt% in isopropanol, Prod. No. 8045, Nanograde AG, Switzerland). Tin oxide has been prepared by atomic layer deposition in a Beneq TFS 200 system (base pressure 1.5mbar). As precursors, tetrakis(dimethylamino)tin(IV) (TDMASn), kept at 45°C and water, kept at room temperature, were used. At a substrate temperature of 80°C the growth rate per cycle was 1.1Å. Further details on the materials properties of the SnOx can be found in our earlier work23,27. Ag (100 or 10nm) layers were thermally evaporated in high vacuum (10−7mbar). In some reference devices, LiF (1nm) and Al (100nm) have been thermally evaporated as cathode.
The electrical conductivity was measured with the Van der Pauw method.
The SEM studies were conducted using Neon 40 (Zeiss).
XRD was measured using a monochromatic Cu-Kα1,2 source (Philips X'Pert Pro MPD). XPS has been performed using a non-monochromatic Mg Kα X-ray source (VG) and a Phoibos 100 (Specs) electron analyser.
Rutherford backscattering was measured at RUBION (University of Bochum, Germany) using a dynamitron tandem accelerator with 2MeV 4He+ beam (beam current of 20–40nA). A silicon surface barrier detector was placed at an angle of 160° with respect to the beam axis. The solid angle of the detector was 1.91msrad.
The solar cells were characterized in ambient air without encapsulation using a Keithley 2400-C source meter and a solar simulator (300W Newport, model 91160, AM1.5G, 100mWcm−2). We used a commercial Si reference cell (Rera Systems) that is IEC 60904–9 compliant and certified. Short circuit current was obtained from the EQE data. EQE has been measured with a home-built tunable light source, calibrated with a power meter (Thorlabs). The spectral mismatch factor was 1.163.
Some of the devices have been kept in a glovebox under N2 atmosphere on a hot plate at 60°C. The J/V characteristics were measured in forward and reverse direction at a scanning speed of 500mVs−1. Cells were measured using a mask with round aperture of 1.5mm diameter. Stabilized current was measured in the same J/V setup using a voltage source.
Long-term light soaking tests at 60°C under N2 were conducted by simultaneously illuminating the cells with a white LED to achieve the same Jsc as upon AM1.5G solar irradiation. The LED spectrum is shown in the Supplementary Fig. 8e. The cells were mounted in a home-built oven inside a glove box. They were kept in short circuit conditions during the ageing experiment.
The data that support the findings of this study are available from the corresponding author on request.
How to cite this article: Brinkmann, K. O. et al. Suppressed decomposition of organometal halide perovskites by impermeable electron-extraction layers in inverted solar cells. Nat. Commun. 8, 13938 doi: 10.1038/ncomms13938 (2017).
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Supplementary Figures 1-8 and Supplementary References
We acknowledge the German Federal Ministry for Education and Research (Grant No. 03EK3529E) and the Deutsche Forschungsgemeinschaft (DFG) (Grants: RI1551/4-2) for financial support. We acknowledge the Ministry of Science of the state of NRW for funding within the PeroBOOST (EFRE) project. The research leading to these results has received partial funding from the European Unions 7th Framework Programme under Grant Agreement no. 604148 (MUJULIMA).
The authors declare no competing financial interests.
Author contributions T.R. and K.O.B. conceived and designed the experiments. S.O. and K.M. contributed the XPS and plan-view SEM analysis. N.P. did the XRD study. D.R. contributed the Rutherford backscattering (RBS) analysis. K.O.B., T.B., T.H. and J.Z. performed the experimental work on the perovskite cell devices. L.H. and T.G. contributed the tin oxide ALD layers as well as electrical and permeation barrier studies. R.H. did the cross-section SEM measurements. M.F.O. and N.A.L. provided the AZO dispersions along with the expertise of their processing. All authors discussed the results and were involved in the writing.