International Journal of Photoenergy

International Journal of Photoenergy / 2017 / Article
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Nanostructured Solar Cells

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Research Article | Open Access

Volume 2017 |Article ID 7153640 | https://doi.org/10.1155/2017/7153640

Yusi Chen, Yangsen Kang, Jieyang Jia, Yijie Huo, Muyu Xue, Zheng Lyu, Dong Liang, Li Zhao, James S. Harris, "Nanostructured Dielectric Layer for Ultrathin Crystalline Silicon Solar Cells", International Journal of Photoenergy, vol. 2017, Article ID 7153640, 6 pages, 2017. https://doi.org/10.1155/2017/7153640

Nanostructured Dielectric Layer for Ultrathin Crystalline Silicon Solar Cells

Academic Editor: Sanjay K. Srivastava
Received18 Nov 2016
Revised05 Mar 2017
Accepted22 Mar 2017
Published16 May 2017

Abstract

Nanostructures have been widely used in solar cells due to their extraordinary photon management properties. However, due to poor pn junction quality and high surface recombination velocity, typical nanostructured solar cells are not efficient compared with the traditional commercial solar cells. Here, we demonstrate a new approach to design, simulate, and fabricate whole-wafer nanostructures on dielectric layer on thin c-Si for solar cell light trapping. The optical simulation results show that the periodic nanostructure arrays on dielectric materials could suppress the reflection loss over a wide spectral range. In addition, by applying the nanostructured dielectric layer on 40 μm thin c-Si, the reflection loss is suppressed to below 5% over a wide spectra and angular range. Moreover, a c-Si solar cell with 2.9 μm ultrathin absorber layer demonstrates 32% improvement in short circuit current and 44% relative improvement in energy conversion efficiency. Our results suggest that nanostructured dielectric layer has the potential to significantly improve solar cell performance and avoid typical problems of defects and surface recombination for nanostructured solar cells, thus providing a new pathway towards realizing high-efficiency and low-cost c-Si solar cells.

1. Introduction

Nanostructures have been widely applied onto solar cells, as they demonstrate promising features for future high-efficiency and low-cost solar cells, such as antireflection and light trapping [17]. However, how to effectively realize the potential of nanostructured solar cells still remain a challenge. Compared with traditional commercial counterparts, nanostructured solar cells have lower energy conversion efficiency [8].

On the other hand, ultrathin crystalline silicon (c-Si) solar cells have attracted much interest, as they could potentially achieve high efficiency with low-cost manufacturing [9, 10]. However, due to the intrinsic optical properties of Si as an indirect bandgap material, light trapping using nanostructures is necessary for ultrathin c-Si solar cells to achieve competitive efficiencies [1114]. In order to get high efficiency, reducing recombination, especially surface recombination, is critical for ultrathin c-Si solar cells [11, 12]. However, typical nanostructured c-Si solar cells suffer from nanostructured pn junction with poor junction quality and high surface damage due the fabrication process, which result in a low Voc, despite a relatively high short circuit current Jsc [1114]. Consequently, the efficiencies of ultrathin c-Si cells are low.

Such problems can be solved in III-V solar cells by nanostructuring the semiconductor window layer with higher energy bandgap instead of nanostructuring the solar cell absorber. The nanostructured window layer could produce antireflection and light-trapping effect, while at the same time maintaining the pn junction quality and blocking the minority carriers from being recombined at the surface [6]. Similarly, this concept could be applied to c-Si solar cells as well. Particularly, low-cost dielectric materials with large bandgap (above 3 eV) have already been widely used in c-Si solar cells, such as silicon nitride (SiNx), aluminum oxide (Al2O3), and silicon dioxide (SiO2) [15]. In addition, these dielectric materials have been reported to provide excellent surface passivation for c-Si solar cells [16, 17]. Therefore, by nanostructuring those dielectric materials, antireflection and light trapping could be achieved without sacrificing the junction quality and surface passivation.

In this work, we present the design of nanostructured dielectric layer (NDL) of SiNx on c-Si thin films for antireflection and light trapping. Simulation and experiment results are also provided and discussed. First, simulation results demonstrate the design robustness and the photon management performance of the NDL over a wide spectra and angular range. Second, NDL is applied onto a 40 μm c-Si thin film, which suppresses the overall reflection to below 5%. In the final part, the NDL is integrated with a c-Si solar cell with 2.9 μm ultrathin absorber layer, demonstrating 32% improvement in Jsc and 30 mV enhancement in Voc.

2. Design and Simulation of Nanostructured Dielectric Layer

To study the antireflection effect of nanostructured dielectric layers, optical simulations were performed by finite-difference time-domain (FDTD) method in FDTD Solutions from Lumerical Inc. The simulated nanostructures were an array of nanocones with a 600 nm diameter at the base and 600 nm height, as illustrated in Figure 1. In this simulation, the light source was located above the nanostructures, which is incident normally into the nanostructures. The reflectance of each wavelength was calculated based on the ratio of reflected power and the total incident power. As we are only studying the antireflection effect, the c-Si layer under the NDL is assumed to be infinite. A 10 nm thick SiO2 (index of 1.6) passivation layer is also included beneath the SiNx region. When the light comes through the NDL and into the solar cell, reflection occurs at the air/NDL and NDL/c-Si interfaces. The tapper-shaped nanocones provide a gradually changing refractive index and eliminate the reflection at the air/NDL interface. On the other hand, although the index mismatch between dielectric and c-Si exists, SiNx with refractive can suppress the reflectance to below 8%.

Figure 2(a) shows the simulated spectral reflectance of SiNx NDL with refractive index ranging from 1.9 to 2.2. The predicted reflectance is below 10% over a wide portion of the solar spectrum. Another benefit of nanostructures is their wide acceptance angle. Figure 2(b) shows the comparison of simulated spectral averaged reflectance, which is the integrated reflectance weighted by the number of incident photons per wavelength over AM 1.5G, between the SiNx NDL, single-layer antireflective coating (SLARC, 80 nm thick SiNx), and double-layer antireflective coating (DLARC). In the simulation, the SLARC was set to be single 80 nm thick SiNx layer, and the DLARC was 140 nm thick SiO2 on top of 80 nm thick SiNx. The SiNx NDL with refractive index of 2.1 shows below 10% overall reflectance up to 60-degree incidence, which is better than any single-layer antireflective coating (SLARC) at all angles and outperforms double-layer antireflective coating (DLARC) when the incident angle is greater than 20 degrees. On the other hand, the antireflection performance does not change much for NDL with different refractive index from 1.9 to 2.2, which provides a good design robustness as SiNx might have a variation in refractive index.

3. Fabrication of Nanostructured Dielectric Layer

The SiNx NDL was fabricated using a nanosphere lithography method [18] as shown in Figure 3. First, 700 nm of SiNx with 10 nm of SiOx on top was deposited on the c-Si layer using plasma-enhanced chemical vapor deposition (PECVD) at 350°C. It should be noted that the 10 nm of SiOx is crucial here for the etching uniformity during the nanosphere lithography process. Next, 600 nm silica nanospheres were assembled into monolayer closed-pack film on top of the SiOx via Langmuir–Blodgett (LB) coating method [19]. Later, with the silica nanospheres as etch masks, electron cyclotron resonance plasma etching with CF4 and O2 gas (CF4 : O2 = 10 : 1) is used to etch down the SiNx and produce the nanocone arrays. To achieve isotropic etching for the nanostructures, a high chamber pressure of 40 to 50 mTorr was used [20, 21]. Finally, silica nanosphere residues were removed in 50 : 1 hydrofluoric acid. The shape of nanostructures can be controlled by the ratio between etchant gas and the bias applied during plasma etching. Scanning electron microscope (SEM) images in Figure 4 shows the fabricated nanocone array with different shapes.

4. Nanostructured Dielectric Layer on 40 μm c-Si Layer

To evaluate the antireflection and light-trapping effect, a SiNx NDL layer was applied onto a 40 μm c-Si thin layer that was prepared using the epi-lift-off (ELO) kerfless Si technique. The NDL layer was fabricated using the method described in Section 3 and has the nanodome shape as in Figure 4(a). The reflectance measurements were performed using a standard integrating sphere system, and the characterization results are shown in Figure 5. Figure 5(a) shows the FDTD simulation and experimental measurement results of reflectance on top of the 40 μm c-Si thin layer with NDL. The incident light is under normal direction with wavelength ranging from 400 nm to 1000 nm. From Figure 5(a), the reflectance loss has been suppressed to below 5% over a wide portion of the solar spectrum, from 400 nm up to 850 nm. Above 850 nm, the reflectance increases for both simulation and measurement results. This is because the optical absorption in c-Si is weak in this wavelength range [22]. The difference between simulation and experiment results at 900 nm to 1000 nm mainly comes from the different bottom interface configuration. In simulation, the 40 μm c-Si thin layer is a free-standing thin film and the bottom surface is expose to air with large refractive index mismatch. Therefore, the unabsorbed light gets partially reflected at the bottom surface of c-Si. Such reflected light is reflected again at the front SiNx/c-Si interface and the SiNx/air interface. The 40 μm thin Si acts like a resonant cavity in this case, generating the resonant peaks between 900 nm to 1000 nm in Figure 5(a). On the other hand, in experiment, the sample was placed on a thick polymer layer (~1 mm) for handling. Therefore, the reflection from the back surface is not strong enough to generate such resonant peaks as in the simulation results. Figure 5(b) shows the measured integrated reflection at different incident angles. The spectral averaged reflection has been suppressed from ~30% to below 10% up to 60-degree incident angle, demonstrating a wide-angle antireflection effect.

5. Nanostructured Dielectric Layer on Ultrathin c-Si Solar Cells

To better assess the performance of NDL, a c-Si solar cell with 2.9 μm ultrathin absorber was fabricated and integrated with NDL [23]. The fabrication process is shown in Figure 6. For comparison, a control sample was fabricated using similar process but without the NDL on top.

First, the ultrathin c-Si solar cell was deposited on top of a ~100 Ω·cm semi-insulating p CZ substrate using reduced pressure chemical vapor deposition (RPCVD) in an Applied Materials Epi2 system (Figure 6(a)). The deposition was at 1000°C using dichlorosilane (DCS), and phosphine (PH3) and diborane (B2H6) were used as the dopants. The solar cell contains three layers: a 1.7 μm 1.5 × 1018 cm−3 boron-doped p-type base layer, a 0.9 μm 1016 cm−3 p intrinsic layer, and a 0.3 μm 1.5 × 1019 cm−3 phosphorus-doped n+-type emitter layer.

Second, the NDL was fabricated over the whole sample using the method described in Section 3. 700 nm SiNx layer was deposited at 350°C using PECVD with 10 nm SiOx layer on top (Figure 6(b)). Later, a monolayer of compact silica nanospheres was assembled on top of the SiOx thin film using LB method (Figure 6(c)). Next, a combination of CF4 and O2 was used to dry etch the SiNx with silica nanopheres as etching masks and followed by 50 : 1 HF dip to remove the remaining SiOx and silica (Figure 6(d)). The fabricated NDL has the nanodome shape as in Figure 4(a).

Standard 5X projection system optical lithography was used to define the contact region. The top contact region is formed by removing the PECVD SiNx with 6 : 1 buffered oxide etchant (BOE) (Figure 6(e)) and followed by evaporation of 200 nm thick aluminum for the contact. The front contact region is finally formed by lift-off process in acetone. The back contact was formed by directly aluminum evaporation on the back side of the wafer. The schematic of the fabricated solar cell with NDL is shown in Figure 6(f). To evaluate the performance of the NDL, control samples were also fabricated. The control samples have the similar cell structure and fabrication process, but without NDL on top.

The current density-voltage (J-V) characteristics of the fabricated 2.9 μm cells were performed under AM 1.5G 1-sun illumination (1000 W/cm2) at room temperature. A calibrated solar simulator was used to provide the illumination, and the light intensity was monitored using a NREL certificated solar cell. The J-V measurement results of the cells with and without the SiNx NDL structures are shown in Figure 7(a), and the key solar cell parameters including short-circuit current density, open-circuit voltage, efficiency, and fill factor are summarized in Table 1.


Jsc
(mA/cm2)
Voc (mV)Fill factor (%)Efficiency
(%)

w/ NDL28.1557071.311.44
w/o NDL21.3254069.48.08
Relative
improvement
25%6.5%2.7%44%

First of all, the solar cell with NDL achieved a Jsc of 28.15 mA/cm2, which is 32% higher than the Jsc of the control cell without NDL. This is due to the antireflection and light-trapping effect of the NDL. Such effect could also be seen from the results of the external quantum efficiency (EQE) measurement in Figure 7(b), which was conducted using mechanically chopped monochromatic light with the photocurrent measured using a lock-in amplifier. With NDL, the EQE is improved from below 60% to ~80% over a wide range of solar spectrum (500 nm to 800 nm). However, EQE decreases at wavelength above 800 nm due to the weak absorption of c-Si at such wavelength range, and the improvement with NDL is also smaller there. The Jsc and EQE could be further improved by making a stand-alone ultrathin c-Si solar cell with integrated back reflector [24].

Second, the solar cell with NDL also achieved a Voc of 570 mV, which is 30 mV higher than the Voc of the control cell without NDL. As Voc is related to the overall minority carrier recombination inside the solar cells, a higher Voc indicates that the cell with NDL has a better surface passivation effect while still maintaining the same pn junction quality. Such a surface passivation effect could also be seen from the EQE enhancement at short wavelength (400 nm to 500 nm) in Figure 7(b). With NDL, the EQE is improved from below 20% to above 40% at 400 nm, which is more than 100% relative improvement. For photons at 400 nm wavelength, the absorption depth is only 82 nm [22], which means that most of the photons at 400 nm are absorbed near the surface and are highly affected by the surface recombination. Therefore, such a huge improvement at 400 nm EQE not only exhibits the antireflection effect but also demonstrates the surface passivation effect of NDL.

Overall, the solar cell with NDL has an energy conversion efficiency of 11.44%, which is 44% relatively higher than the efficiency of the control cell without NDL.

6. Summary

To summarize, we have demonstrated a systematical analysis of SiNx NDL for antireflection and light trapping in ultrathin c-Si solar cells. A complete large-area and whole-wafer process to form NDL on thin c-Si is also presented. Also, the NDL has been successfully integrated onto a 40 μm thin c-Si layer and an ultrathin c-Si solar cell with 2.9 μm absorber. From the simulation and experiment results, a wide-spectrum and wide-angle antireflection and light-trapping effect has been achieved using NDL. Together with the good surface passivation effect of SiNx, NDL exhibits great potential to produce high-efficiency and low-cost ultrathin c-Si solar cells.

Conflicts of Interest

The authors declare that they have no conflicts of interest.

Acknowledgments

This work was supported by the Bay Area Photovoltaic Consortium (BAPVC) and the Global Climate and Energy Project (GCEP) at Stanford University. The authors acknowledge the Stanford Nanofabrication Facility (SNF) for the use of the processing facilities, Center on Nanostructuring for Efficient Energy Conversion (CNEEC) for the use of characterization facilities, and Solexel Inc. for providing the 40 μm c-Si layer. Yusi Chen would like to acknowledge the funding support from Applied Materials Inc. through the SystemX FMA program. Jieyang Jia would like to acknowledge the funding support from the Stanford Graduate Fellowship (SGF).

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Copyright © 2017 Yusi Chen et al. This is an open access article distributed under the Creative Commons Attribution License, which permits unrestricted use, distribution, and reproduction in any medium, provided the original work is properly cited.


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