Impact of Pre-Annealing on Industrially LPCVD Deposited PolySi Hole-selective Contacts-solarbe文库

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Impact of Pre-Annealing on Industrially LPCVD Deposited PolySi Hole-selective Contacts Josua Stuckelberger1, Di Yan1, Sieu Pheng Phang1, Chris Samundsett1, Luca Antognini2, Franz- Josef Haug2, Zhao Wang3, Jie Yang3, Peiting Zheng3, Xinyu Zhang3, Daniel Macdonald1 1Research School of Electrical, Energy and Material Engineering, The Australian National University, Canberra 2601, Australia 2École Polytechnique Fédérale de Lausanne EPFL, Institute of Microengineering IMT, Photovoltaics and Thin-Film Electronics Laboratory, Rue dela Maladière 71b, 2002 Neuchâtel, Switzerland 3Jinko Solar, 58 Yuanxi Road, Yuanhua Industrial Park, Haining Zhejiang 314400, China Abstract We present the beneficial effect on passivation of industrially LPCVD deposited polySi/SiOX hole-selective contacts by the introduction of a pre-annealing step prior to the boron diffusion. We investigate the influence of the pre-anneal temperature on passivation quality and crystallinity. A clear increase in passivation quality is observed on planar and textured surfaces as well as for various polySi thicknesses 100 – 230nm and thermal SiOX growth temperatures 600 – 800°C. On planar surfaces and without the use of atomic hydrogenation, we report an increase in iVOC of around 5mV with every additional increase of pre-annealing temperature by 50°C 900°C leading to an iVOC of 720mV J0 9.3fA/cm2. After atomic hydrogenation, the effect of pre-annealing is less pronounced nevertheless a gain in iVOC reduction in J0 of 5-10mV 2-5fA/cm2 is achieved comparing samples without pre-anneal with samples after a pre-anneal at 1050°C. On textured surfaces on the other hand, the beneficial effect is more pronounced after the atomic hydrogenation and a preannealing at 1050°C leads to an iVOC J0 of 705mV 16.8fA/cm2, which is a gain reduction by 24mV 21.7fA/cm2 compared to samples without a pre-annealing step. Introduction Carrier-selective passivating contacts based on a thin silicon oxide SiOX layer capped by a highly doped polycrystalline silicon polySi have achieved impressive results over the last years [1]–[9], including word-record efficiencies in laboratory devices [10], [11], and are currently adopted by manufacturers as next generation for crystalline silicon solar cells [12], [13]. In recent years, the gap between electron-selective n-type contacts and the more challenging hole-selective p-type contacts is closing thanks to the introduction of more sophisticated multilayer systems [9] to control the boron diffusion or by the incorporation of C atoms [6], [14], [15]. In this work, we present another way to achieve high performing hole-selective contacts using a pre- annealing of the intrinsic SiOX/polySi structures before the boron diffusion takes place. On industrially fabricated symmetrical SiOX/polySi structures, we present the beneficial effect for a wide range of pre-anneal temperatures. Experimental This study was performed on symmetrical test structures using chemically polished and industrially textured 1-5 ohmcm phosphorus doped n-type Cz c-S wafers with a thickness of 180 μm textured 170 μm. Thermal oxidation at three different temperatures 600°C, 700°C, 800°C is followed by intrinsic polySi deposition via low-pressure chemical vapour deposition LPCVD fabricating three different thicknesses 100nm, 175nm, 230nm. Up to here, the sample fabrication was performed in Jinko Solar in industrial mass-production tools. A pre-annealing was performed using five different temperatures 850°C, 900°C, 950°C, 1000°C, 1050°C for 60min followed by the same boron diffusion for all samples. After a forming gas anneal FGA at 425°C for 30min one sample of each condition went on for atomic hydrogenation via an Al2OXH/SiNX stack with subsequent annealing at 500°C in FGA, whereas a sister sample was kept for contact resistance measurements. Results Figure 1 and Figure 2 depict the passivation quality on planar and textured samples, respectively, as a function of the pre-annealing temperature. In Figure 1a and b, we observe a clear increase in iVOC decrease in J0 with increasing pre-annealing temperature independently of the SiOX growth temperature or the polySi thickness. For pre-annealing temperatures above 900°C, we observe an increase of 5mV with every additional increase of pre-annealing temperature by 50°C leading to an iVOC of 720mV J0 9.3fA/cm2 after FGA. After atomic hydrogenation, a gain in iVOC reduction in J0 of 5-10mV 2-5fA/cm2 is observed comparing samples without pre-anneal and samples after a pre-anneal at 1050°C leading to an excellent passivation with an iVOC of 729mV and a J0 of 3.1fA/cm2 using a pre-annealing at 1050°C. 30 November – 2 December 2020 Melbourne, Australia Figure 1 iVOC top and J0 bottom for planar samples as a function of pre-annealing temperature measured after FGA filled symbols and after atomic hydrogenation via an AlOx/SiNx stack open symbols. In a the thermal SiOX growth temperature is varied between 600°C green, 700°C red and 800°C blue keeping the polySi thickness constant at 175nm. In b the polySi thickness is varied between 100nm orange squares, 175nm red circles and 230nm dark red triangles for 700°C thermal SiOX. As for the planar surfaces, on textured surfaces Figure 2 an increase in passivation quality is observed with increasing pre-annealing temperature. In general the iVOC J0 on textured surfaces is 20-30mV lower 20-30fA/cm2 higher than on planar surfaces which is attributed to a poorer passivation ability of the SiOX layer on 111 surfaces compared to 100 surfaces [16]. An interesting point is that on textured surfaces the beneficial effect of the pre-anneal is more pronounced after the atomic hydrogenation than directly after FGA, which is different than observed on planar surfaces. The optimum with a pre-annealing at 1050°C leads to an iVOC J0 of 705mV 16.8fA/cm2, which is a gain reduction by 24mV 21.7fA/cm2 compared to the 681mV 38.5fA/cm2 without a pre- annealing step. 30 November – 2 December 2020 Melbourne, Australia Figure 2 iVOC top and J0 bottom for textured samples as a function of pre-annealing temperature measured after FGA filled symbols and after atomic hydrogenation via an AlOX/SiNX stack open symbols. In a the thermal SiOX growth temperature is varied between 600°C green, 700°C red and 800°C blue keeping the polySi thickness constant at 175nm. In b the polySi thickness is varied between 100nm light blue squares, 175nm blue circles and 230nm dark blue triangles for 800°C thermal SiOX. Contact resistivity measurements were performed using the TLM method [17]. Values for the contact resistivity ρC are found between 0.1 – 1 mΩcm2 with no clear trend regarding the SiOX growth temperature, polySi thickness or pre-annealing temperature and are therefore not plotted here. Electrically active boron profiles are assessed using electrochemical capacitance voltage measurements ECV on planar surfaces Figure 3a. No clear difference is observed for a variation in pre-anneal temperature for the in-diffused profile within the wafer, but a slightly lower boron concentration within the polySi is detected for higher pre-annealing temperature. Figure 3 In a the active boron doping profiles measured by ECV shown in the region around the interface of polySi/SiOX/c-Si. The pre-annealing temperature is varied between 0°C no pre-annealing, dark green and 1050°C orange. In b normalized Raman spectra before dotted lines and after boron diffusion solid lines are plotted varying pre-annealing 30 November – 2 December 2020 Melbourne, Australia temperature from 0°C dark green up to 1050°C red for the case of 175nm thick polySi on 700°C grown SiOX. The inset in b shows the estimated crystallinity. The crystallization of the polySi layer is assessed using Raman spectroscopy on the planar samples with an excitation wavelength of 442nm Figure 3b. In the LPCVD grown state 0°C a broad peak around 480cm-1 suggests a completely amorphous film. After pre-anneal, the appearance of a strong peak at 520cm-1 indicates crystallisation of the film, and we note that the presence of a small shoulder at 515cm-1 decreases with increasing pre-anneal temperature. The crystallinity increases from 96 to 98.3 after pre-anneal at 1050°C inset Figure 3b. After boron diffusion, the peaks widen and the shoulder gets clearly enhanced as boron atoms cause damage to the crystal structure during the diffusion [18]. This results in a drop in the estimated crystallinity by 3 ending up at values between 93.0 no pre-anneal and 95.4 1050°C. Conclusion We have presented the beneficial effect on passivation of industrially LPCVD deposited polySi/SiOX hole-selective contacts by the introduction of a pre-annealing step prior to the boron diffusion. Increasing the pre-anneal temperature lead to a higher crystallization of the boron doped polySi layer, while the in-diffusion of dopants to the wafer is not affected. A clear increase in iVOC decrease in J0 is observed with increasing pre-annealing temperature independently of the SiOX growth temperature or polySi thickness. On planar surfaces and after atomic hydrogenation, we observed a gain in iVOC reduction in J0 of 5-10mV 2-5fA/cm2 after a pre-anneal at 1050°C leading to an excellent iVOC 729mV and J0 3.1fA/cm2. On textured surfaces after atomic hydrogenation and a pre-annealing at 1050°C an iVOC J0 of 705mV 16.8fA/cm2 is found, which is a gain reduction by 24mV 21.7fA/cm2 compared to samples without a pre-annealing. Acknowledgement This work has been supported by the Australian Renewable Energy Agency ARENA through project RND016. JS acknowledges support through an Australian Centre for Advanced Photovoltaics ACAP postdoctoral fellowship. We owe thanks to the Australian National Fabrication Facility ANFF for providing access to some of the facilities used in this work. References [1] F. Feldmann et al., Sol. Energy Mater. Sol. 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