Can interface charge enhance selectivity in tunnel layer passivated contacts? Using negatively charged aluminium oxide capped with dopant free PEDOT or boron doped polysilicon
Graphical abstract
Introduction
Tunnel layer passivating contacts have proven to enable high energy conversion efficiencies for crystalline silicon (c-Si) solar cells at low processing complexity. Sandwiching an ultrathin dielectric tunnel layer (passivating the c-Si wafer interface) and a highly p-/n-doped or a high/low work function capping layer between the metal contact and the c-Si wafer results in reduced contact recombination and thus in improved solar cell efficiencies [[1], [2], [3], [4], [5], [6], [7]]. The tunnel oxide is the core element of a tunnel layer passivated contact. It must decrease minority carrier recombination near the contact (for instance, electron recombination in case of a hole extracting contact as studied here, Fig. 1.), leading to lower recombination current density Jcontact, and simultaneously allow majority carriers (holes in our case) to pass through it, resulting in a low effective contact resistivity ρcontact (corresponding to a high hole current Jholes in our case studied), see Fig. 1. In order to form ‘conventional’ SiOx tunnel layers, different oxidation technologies like applying a standard RCA oxide [8,9], wet-chemical HNO3 [1,[10], [11], [12]], a dry-grown UV/O3 oxide [13], thermal oxides [10,11], etc., were studied. Using ultra-thin atomic layer deposited (ALD) aluminium oxide (Al2O3) tunnel layers, exhibiting a high negative charge density (~1012 cm−2), as opposed to SiOx tunnel layers, which exhibit only a moderate positive fixed charge density (~1010 cm−2), might enhance the excess hole extraction (selectivity) of the passivated contact formed as shown in Fig. 1 (as the negative tunnel layer charge in Al2O3 films leads to an enhanced accumulation of holes nearby the contact). ALD Al2O3 layers not only provide the benefit of high field effect passivation, but also improved chemical passivation by decreasing the interface defect density, thereby making it a promising candidate for tunnelling passivation layer for solar cell contacts in MIS structure [14] or when coupled with separate carrier selective material like doped polysilicon [[15], [16], [17]], molybdenum oxide [18], zinc oxide [19] or even high work function materials [20]. But does high negative interface charge of AlOx actually improve hole selectivity and subsequently solar cell efficiency?
In order to test this, we compared two different capping layers suited for selective hole extraction: dopant-free poly (3,4-ethylenedioxythiophene) polystyrene sulphonate (PEDOT:PSS, an organic, low-cost, high work function material) and the conventionally used capping layer, i.e. boron doped polycrystalline silicon (p+-poly-Si). Please note, PEDOT:PSS is processed at low temperature (spin coating at room temperature, followed by an anneal at ~140 °C), whereas p+-poly-Si deposition is a high temperature process (we used low pressure chemical vapour deposition (LPCVD) at ~570 °C and subsequent boron diffusion at ~800–850 °C). As low temperature capping layer processing would likely not alter the tunnel layer properties, this will allow us to better understand the effect of tunnel layer variation without facing additional problems of high temperature processing as encountered for polysilicon based contacts. ‘Conventional’ SiOx/p+-poly-Si [21,22] and SiOx/PEDOT:PSS [23,24] passivated contacts, as well as ‘negatively charged’ AlOx/p+-poly-Si [15,17] and AlOx/PEDOT:PSS [20,25] passivated contacts are already realized and have resulted in cell efficiencies above 20%. In this work, we systematically investigate whether the presence of a high negative fixed charge density at the c-Si/AlOx interface helps to selectively extract holes in the above mentioned hole selective passivated contact configurations.
Xin et al. [15] replaced the SiOx tunnel layer beneath the p+ poly-Si by AlOx tunnel layer to achieve improved hole selectivity for thicknesses < 1 nm [15]. However, the negative charge in AlOx films is typically located within the first 1 nm of the c-Si/AlOx interface [26] and thickness of the AlOx tunnel layers plays a crucial role here. Since, it is important to grow tunnel layers with precise thickness control therefore, we used industrially relevant, high throughput spatial ALD tool to deposit AlOx films. The passivation properties of ALD AlOx tunnel layers with varying thicknesses were studied before and after annealing at 425 °C in air ambient (as charge formation in AlOx layers takes place upon annealing). After a subsequent PEDOT:PSS or p+-poly-Si capping, the resulting hole extracting passivated contacts were further characterized, i.e. the contact recombination parameter (J0,contact) and the effective contact resistivity (ρcontact) were measured. Finally, the selectivity of the processed passivated contacts and their efficiency potential if deployed rear-side within a solar cell were calculated according to Brendel's model [27]. Overall, two hole-selective passivated contacts, AlOx/PEDOT:PSS and AlOx/p+-poly-Si deploying negative charge at interface were optimized as a function of ALD AlOx thickness (0.13–2 nm) and compared to their ‘conventional’ reference system SiOx/PEDOT:PSS and SiOx/p+-poly-Si.
Section snippets
Experimental details
6 inch, saw damage cut, N-type, CZ wafers (ρ:2–7 Ωcm) were subjected to the standard RCA cleaning treatments (RCA1 – HF - RCA2) after a saw damage etch for 10 min. These wafers were then dipped in 1% HF solution for 2 min to form hydrophobic surfaces (H termination). AlOx films, 0.13–2 nm thick (1–15 ALD cycles) were then symmetrically deposited on these wafers using the industrial, high throughput thermal ALD deposition tool SoLayTec at 200 °C, see Fig. 2(a). Trimethylaluminium (TMA) and water
Impact of AlOx thickness and annealing on passivation properties
The effective minority carrier lifetime (τeff) of test-samples, being symmetrically passivated by ultra-thin AlOx tunnel layers only, as sketched in Fig. 2(a), are plotted as a function of AlOx thickness in the as-deposited and the post-annealed states in Fig. 4(a). It can be clearly seen that annealing results in improvement of τeff. Annealing at 425 °C of thicker samples (beyond 1 nm) lead to a steep improvement in lifetime (up to 12–35 times). Surface passivation results from the combined
Conclusion
From above observations and discussion, we conclude that an ALD-AlOx tunnel layer with its high negative fixed charged density (forming upon thickness > 1 nm) can indeed increase selective hole extraction (as compared to using a ‘conventional’ SiOx tunnel layer). For PEDOT:PSS capped passivated contacts, the efficiency potential deploying optimized negatively charged AlOx tunnel layers was measured to be 1.1% absolute higher as compared to using a conventional (moderately charged) SiOx tunnel
CRediT authorship contribution statement
Gurleen Kaur: Conceptualization, Investigation, Formal analysis, Visualization, Writing - original draft, preparation, Writing - review & editing. Tanmay Dutta: Formal analysis, Writing - review & editing. Ranjani Sridharan: Investigation, Validation. Xin Zheng: Software, Methodology. Aaron Danner: Supervision, Resources, Project administration, Writing - review & editing, Funding acquisition. Rolf Stangl: Supervision, Conceptualization, Funding acquisition, Resources, Project administration,
Declaration of competing interest
The authors declare that they have no known competing financial interests or personal relationships that could have appeared to influence the work reported in this paper.
Acknowledgements
This research is supported by the National Research Foundation, Prime Minister's Office, Singapore, under its Energy Innovation Research Programme (EIRP Award No. NRF2014EWT-EIRP001-006 titled “Passivated contacts for high efficiency solar cells“). The authors gratefully acknowledge the support of Department of Electrical and Computer Engineering, National University of Singapore (NUS), and Solar Energy Research Institute of Singapore (SERIS) for their resources.
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Now at Empa-Swiss Federal Laboratories for Material Science and Technology, Dübendorf, Switzerland.