Abstract
In this paper, we demonstrate via Finite-difference time-domain (FDTD) simulations that the performance of indium-rich InxGa1-xN (x = 0.6) p-n junction thin-film solar cells is improved by incorporating an integrated structure of a 2-dimensional (2D) array of ITO nanodiscs on the top surface and a 2D array of Ag nanodiscs in the active layer above the Ag back reflector of the solar cell. The bottom Ag nanodiscs primarily enhance the absorption of longer wavelengths by coupling incident light into surface plasmon resonance (SPR) and waveguide modes. The top ITO nanodiscs enhance the middle wavelengths (400 nm to 800 nm) by coupling the incident light to photonic modes in the active layer. Thus, the integrated structure of nanodisc arrays leads to a very high absorption in the active region in broad spectral range (> 0.85 for wavelengths lying between 350 nm and 800 nm), significantly increasing the short circuit current density (Jsc) and power conversion efficiency (PCE) of the solar cell. In the proposed solar cells, the geometries of the silver and ITO nanodiscs were optimized to obtain the maximum possible values of the Jsc. The highest enhancements in Jsc and PCE of ∼25% and ∼26%, respectively, were obtained in a solar cell containing the integrated structure of ITO and Ag nanodisc arrays. Moreover, the performance of these cells was examined under oblique light incidence and it was observed that the solar cells containing the integrated structure of nanodisc arrays have a significantly larger value of Jsc when compared to the cells having no nanostructures or having only the top ITO nanodisc array or only the bottom Ag nanodisc array.
© 2020 Optical Society of America under the terms of the OSA Open Access Publishing Agreement
1. Introduction
Among crystalline semiconductor materials, indium gallium nitride (InGaN) ternary alloys are of great interest in the field of photovoltaics due to their superior photovoltaic properties, especially the tunable direct band gap covering most of the solar spectrum ranging from ultraviolet to the near-infrared region [1,2], high absorption coefficient (∼105 cm−1) [3], and high carrier mobility [1]. InGaN alloys also exhibit high thermal and chemical stabilities and superior radiation resistance [1,4]. Hence, these alloys have become a potential candidate for photovoltaic device applications in harsh environments. Many previous reports have proposed the fabrication of InGaN-based solar cells with low indium content [5–8]. But, a low indium content in InGaN results in a large band gap of the InGaN alloy. This leads to the absorption of sunlight only for shorter wavelengths, which in turn leads to lower efficiency of the solar cells. Thus, for the realization of a high efficiency InGaN-based solar cell, the indium content in the InGaN active layer must be increased to cover most of the solar spectrum.
Previous studies have reported phase separation in indium-rich InGaN alloy due to solid phase immiscibility between GaN and InN [3,9–12]. Nevertheless, recent reports have shown the growth of high quality, single crystalline InGaN with high indium content can be carried out by controlling the growth temperature and pressure [13–16]. However, with higher indium content, the crystalline quality of the InGaN thin films degrades significantly with increasing layer thickness [17]. Therefore, for high efficiency indium-rich InGaN solar cells, the thickness of the active layer needs to be in the order of a few hundred nanometers. But, decreasing the layer thickness results in poor light absorption in the active region, which then leads to a low-efficiency cell.
To increase the absorption of sunlight in the thin active layer, researchers have proposed several light trapping methods such as surface texturing [8,18], anti-reflection coating [19], and anti-reflection sub-wavelength structures on the top surface of the solar cell [20–23]. Some plasmonic nanostructures have also been demonstrated to confine the sunlight in the thin active layer through surface plasmon resonance (SPR)-based scattering and coupling of incident light into SPR modes or waveguide modes in the active layer [24–27]. Recent studies have shown the use of dual interface nanostructures in silicon and organic solar cells for enhanced performance [28–32]. Although several plasmonic-enhanced silicon and organic solar cells have been proposed in the last few years, there are very few reports of a plasmonic-enhanced InGaN p-n junction solar cell with indium-rich InGaN layers.
In this paper, we present an indium-rich InGaN (with 60% indium content) p-n junction thin-film solar cell with an integrated structure of a 2-dimensional (2D) array of ITO nanodiscs on the top surface and a 2D array of Ag nanodisc in the active layer above the Ag back reflector of the solar cell. A detailed theoretical study of InGaN p-n junction solar cells with varying indium composition from 0 to 100% in the InGaN active region was presented by Feng et al. [33]. They reported that the indium composition of 60% in the InGaN active region leads to maximum power conversion efficiency. Moreover, Pantha et al. [15] have succesfully demonstrated epitaxial growth of InGaN thin films with indium concentrations upto 63% with no phase separation. Hence, an indium composition of 60% in the InGaN active region is chosen for the solar cell structures being proposed here. It is demonstrated that the absorption in the proposed solar cell structure is significantly enhanced across a broad spectral range, thus obtaining significantly larger short circuit current density (Jsc) and power conversion efficiency (PCE) as compared to a solar cell having either no nanostructures or having only the top ITO nanodisc array or only the bottom Ag nanodisc array. The change in Jsc of the solar cell due to the oblique incidence of light was also examined.
However, embedding such metallic or dielectric nanoparticles in the absorbing InGaN epitaxial layers reduces the crystalline quality of these layers because the epitaxial layers have to be grown continuously as high-quality crystalline films. A fabrication process, addressing this, has been proposed to develop the indium-rich InGaN solar cells containing plasmonic nanostructures (Appendix A).
2. Solar cell structure and numerical calculation method
The device structures of InGaN p-n junction solar cells containing plasmonic or photonic nanostructures are shown in Fig. 1 — a planar solar cell without nanodiscs (Fig. 1(a)), a cell with only Ag nanodiscs on the back electrode (Fig. 1(b)), a cell with only ITO nanodiscs on top (Fig. 1(c)), and finally, a cell with the integrated structure of vertically aligned ITO nanodiscs on top and Ag nanodiscs in the back (Fig. 1(d)). In all these InGaN solar cell configurations, the thicknesses of the Ag, n-InGaN, and p-InGaN layers were taken to be 100 nm, while the thickness of the top ITO electrode was taken to be 20 nm. The Ag bottom layer serves both as a back reflector and the cathode in these solar cells. In the proposed solar cell structures, the radius (Rb) of the bottom Ag nanodiscs, as well as the height (Ht) and radius (Rt) of the top ITO nanodiscs were optimized to maximize the Jsc of the cells. The height (Hb) of the bottom Ag nanodiscs in the back side of the n-InGaN layer was fixed at 50 nm.
The finite-difference time-domain (FDTD) method was employed to calculate the absorption in the solar cells using a commercial FDTD simulation software (Lumerical FDTD Solutions). Plane waves with free space wavelengths varying from 300 nm to 900 nm were incident on the top surface of the solar cells. While optimizing the nanodiscs parameters, the incident plane waves were taken to be TM polarized (polarization along x-direction) and were normally incident along the z-direction. After optimizing the nanodiscs parameters, the solar cell performances of the various cells (as shown in Figs. 1(a)–1(d)) were studied under oblique incidence of light for both TM and TE polarizations. As the solar radiation consists of un-polarized light, we obtained an average of the absorptions calculated for the TE and TM polarizations for the calculation of the short circuit current density. Periodic boundary conditions were used in the x- and y-directions, and perfectly matched layer (PML) boundary conditions were used in the z-direction.
In the FDTD simulations, non-uniform grid sizes were taken — 1 nm for the simulation region of the nanostructures (i.e. the region of the Ag and ITO nanodiscs), and 2 nm for the remaining regions of the solar cell. The simulation window had a dimension of 250 nm in both x- and y- directions i.e. the periodicity of the nanodiscs in the x- and y- directions was fixed at 250 nm. The wavelength dependent refractive indices for Ag and ITO were taken from the literature [34] and [35], respectively. Methodology for calculation of the wavelength-dependent refractive indices of the InGaN alloy is described in Appendix B.
FDTD simulations were carried out to obtain the E- and H- fields in the solar cells. Then, the time-averaged power absorbed in the active medium (InGaN) was calculated by the following relation [27]:
3. Results and discussion
The performance enhancement of the solar cells due to the addition of the bottom Ag nanodisc array and the top ITO nanodisc array was demonstrated by a comparative study of the absorption and short circuit current density (Jsc) for the four different device structures shown in Figs. 1(a) − 1(d). The Jsc of the solar cell was maximized by an optimization procedure involving the bottom Ag nanodisc radius (Rb), the top ITO nanodisc height (Ht) and the top ITO nanodisc radius (Rt). The bottom Ag nanodisc height (Hb) was kept constant at 50 nm.
3.1 Bottom Ag nanodisc array
Firstly, the bottom Ag nanodisc parameters were optimized — for normal incidence of solar radiation — to maximize the Jsc of the solar cell. Figure 2(a) shows the absorption in the active medium as a function of wavelength in solar cells containing only 2D bottom Ag nanodisc arrays — for different values of the radii (Rb) of the Ag nanodiscs. For comparison, the absorption spectrum of the planar solar cell is also shown. Figure 2(a) demonstrates that the absorption is higher for wavelengths longer than 450 nm due to the introduction of the bottom Ag nanodisc array. Figure 2(b) shows the enhancement in the Jsc as a function of bottom Ag nanodisc radius (Rb). The Jsc was calculated by integrating the product of the wavelength-dependent absorption and the solar spectrum AM1.5G from wavelength 300 nm to 900 nm as given by Eq. (3). With an increase of the Ag nanodisc radius, the enhancement in Jsc increases to a maximum of ∼19% for Rb = 90 nm and then, decreases. Figure 2(b) also shows that the enhancement in Jsc is more than 14% for the specified range (60 nm-120 nm) of Ag nanodisc radii.
In order to study the enhancement in absorption due to the addition of the bottom Ag nanodisc array, the absorption enhancement in the solar cell containing the optimized bottom Ag nanodiscs was plotted against wavelength, as shown in Fig. 3(a). It can be observed from Fig. 3(a) that the absorption in the active layer is significantly enhanced for longer wavelengths — with ∼ 60% enhancement at a wavelength of 820 nm. Figures 3(b) and 3(c) show the magnetic field distribution in the x-z plane at a wavelength of 820 nm for a solar cell containing the optimized bottom Ag nanodiscs and for a planar solar cell, respectively. Due to the periodic arrangement, the Ag nanodisc array on the Ag back electrode behaves like a 2D plasmonic nano-grating. Figure 3(b) demonstrates significant magnetic field confinement in the active region due to the presence of the bottom Ag nanodisc array. This can be ascribed to two processes. Firstly, the incident light couples into surface plasmon resonance (SPR) modes present at the interface between the Ag nanodiscs (which are present on the Ag back electrode) and the InGaN active layer. This leads to the localization of fields near Ag nanodiscs in the normal direction and scattering of incident light at different angles in the plane of the active medium. Secondly, the scattered light is reflected back from the interface between the InGaN and the ITO layer. Hence, the scattered light couples into waveguide modes for the wavelengths around the band edge of InGaN active material (∼ 835 nm). Thus, the enhancement of absorption in the active region can be attributed to the field confinement in the active region due to the presence of bottom Ag nanodiscs (as shown in Fig. 3(b)). On the other hand, in a planar solar cell, normally incident light is reflected normally from the flat Ag back reflector (Fig. 3(c)), and reflected back into the air, leading to lower absorption in the thin active layer.
An optimization of the parameters of a solar cell containing only the top ITO nanodisc array was also performed, and the results are presented in Appendix C. A maximum Jsc enhancement of 15.71% was obtained by employing only top ITO nanodiscs in the solar cell — for Rt = 110 nm and Ht = 120 nm. However, combining these individually optimized top ITO nanodisc parameters with those of the individually optimized bottom Ag nanodisc parameters leads to a solar cell with a Jsc enhancement of only 16.90%. This is significantly less than the enhancement obtained in the solar cell containing only bottom Ag nanodisc array, which was 19%. Thus, to obtain further enhancement in the Jsc, the top ITO nanodisc parameters were optimized in the solar cell containing the optimized bottom Ag nanodisc array.
3.2 Top ITO nanodisc array integrated with bottom Ag nanodisc array
Figure 4 shows the absorption in the active medium as a function of the wavelength for the solar cell with the integrated structure of a 2D array of ITO nanodiscs on the top surface and a 2D array of Ag nanodiscs at the bottom of the solar cell. For comparison, the absorption spectrum for the planar solar cell and the solar cell with only the bottom Ag nanodisc array are also shown. The optimization of the top ITO nanodisc parameters was carried out by taking the optimized values of the bottom Ag nanodisc parameters i.e. height Hb = 50 nm and radius Rb = 90 nm, and varying only the top ITO nanodisc parameters. The height (Ht) and radius (Rt) of ITO nanodiscs were varied from 60 nm to 140 nm and from 50 nm to 100 nm, respectively — Figs. 4(a), 4(b), 4(c), 4(d), and 4(e) correspond to Ht = 60 nm, 80 nm, 100 nm, 120 nm, and 140 nm, respectively. Figures 4(a) − 4(e) show that the addition of the top ITO nanodisc array to the solar cell containing bottom Ag nanodiscs primarily enhances the absorption for the middle wavelengths from 400 nm to 750 nm. However, as the radius and the height of the ITO nanodiscs increase, the absorption in the active region decreases for wavelengths smaller than 430 nm and for wavelengths greater than 700 nm.
Figure 5 shows the enhancement in the Jsc of the solar cell containing the integrated structure of nanodisc arrays (i.e. containing the top ITO nanodisc array and the bottom Ag nanodisc array). The Jsc was calculated by integrating the product of the wavelength-dependent absorption (shown in Fig. 4) and the solar spectrum AM1.5G as given by Eq. (3). Figure 5 shows the enhancement in Jsc with respect to the Jsc of a planar solar cell as a function of ITO nanodisc radius Rt — for varying heights of the ITO nanodiscs. A maximum Jsc enhancement of ∼ 25% was obtained for radius Rt = 75 nm and height Ht = 100 nm. Thus, the optimized integrated structure consists of a bottom Ag nanodisc array having height Hb = 50 nm and radius Rb = 90 nm, with a top ITO nanodisc array having height Ht = 100 nm and radius Rt of 75 nm. Comparing with the planar solar cell, the addition of only bottom Ag nanodisc array enhances the Jsc by 19%, while the addition of the integrated structure of vertically aligned top ITO nanodisc array and bottom Ag nanodisc array enhances the Jsc by 25%.
For a comparative study of the various solar cell structures, the absorption and absorption enhancement in the active medium of the solar cells are plotted in Figs. 6(a) and 6(b), respectively. These results demonstrate that a bottom Ag nanodisc array primarily enhances at the longer wavelengths, while the top ITO nanodisc array primarily enhances at the middle wavelengths – from 400 nm to 800 nm. Hence, the integrated structure of the bottom Ag nanodisc array and the top ITO nanodisc array enhances the absorption in a broad spectral range. The solar cell containing the integrated structure has an absorption greater than 0.85 for the wavelength range from 350 nm to 800 nm.
The enhancement in absorption can be attributed to the high electromagnetic field intensities in the active region due to the coupling of incident light to the plasmonic modes and photonic modes by the bottom Ag nanodisc array and the top ITO nanodisc array, respectively [31]. The absorption enhancement due to the introduction of the bottom Ag nanodisc array has been attributed to the coupling of incident light into plasmonic modes near the Ag nanodiscs and into waveguide modes in the active region. The addition of the ITO nanodisc array on the top surface of the solar cell leads to the coupling of the incident light into photonic Bloch-modes (as shown in Appendix D, Fig. 10) in the active layer [31,37], which results in reduced top-surface reflection from the solar cell. Thus, a greater enhancement in absorption and Jsc is observed due to the addition of the ITO nanodisc array on the top surface of the solar cells containing the bottom Ag nanodisc array.
3.3 Oblique angle incidence on optimized solar cells
We studied the performance of the various solar cell structures under the oblique incidence of light on the top surface. A BFAST source was used as the incident light source for the FDTD simulations with oblique light incidence in the Lumerical software. More than 75% of sunlight incident around midday is at angles smaller than 40° [31]. Therefore, we calculated the absorption of the solar cells for incident angles varying from 0° to 50°. Figure 7(a) shows the short circuit current density (Jsc) as a function of incident angle θ for the solar cells containing optimized plasmonic and dielectric nanostructures – bottom Ag nanodisc array, top ITO nanodisc array, and an integrated structure of these nanodisc arrays, under both TM- and TE-polarized illumination. The results of a planar solar cell are also plotted for comparison. The Jsc of a planar solar cell decreases with an increasing angle of incidence under the TE-polarized light. But for TM-polarized light, the Jsc increases with increasing angle of incidence. This can be explained by the Fresnel’s equations of reflection and transmission at an interface [38]. According to the Fresnel’s equations, transmission through an interface of low refractive index medium to high refractive index medium (examples air/ITO or ITO/In0.6Ga0.4N interface) decreases with increasing angle of incidence for TE polarization. On the other hand, under TM polarization, the transmission first increases for increasing angle of incidence up to a certain angle (given by Brewster’s angle) and then decreases beyond that [38]. It is observed from Fig. 7(a) that the Jsc of a solar cell with a bottom Ag nanodisc array and/or a top ITO nanodisc array is greater than the Jsc of a planar solar cell for incident angles 0° to 37° under both TM- and TE-polarized light. Many recent reports have shown the increased solar cell performance due to plasmonic or dielectric gratings as a function of incident light angle [39–43]. When a bottom Ag nanodisc array and/or a top ITO nanodisc array are present in the solar cell, the absorption in the active region is increased due to the excitation of various SPR and photonic modes. This leads to the increment in the Jsc of these solar cells. Figure 7(a) shows that the Jsc of the solar cell containing bottom Ag nanodisc array or top ITO nanodisc array increases with an increasing angle of incidence under the TM-polarized light while decreases with an increasing angle of incidence under the TE-polarized light. This effect of the incident angle on the Jsc is similar to the planar solar cell. But the rate of changing the Jsc with incident angle is different from the rate of changing the Jsc of the planar solar cell (see Fig. 7(a)). This can be attributed to the shifting of the spectral position of SPR and photonic modes with the angle of incidence. The spectral position of these SPR modes and photonic modes depends on the angle of incidence [44,45]. Thus the incident angle of light influences the absorption enhancement in the active layer and hence the Jsc of the solar cells.
It is observed from Fig. 7(a) that the Jsc of the solar cell containing integrated structure of top ITO and bottom Ag nanodiscs is larger than that of the other solar cell structures for incident angles from 0° to 43° under both TM and TE polarized incident light. The Jsc of the solar cell containing integrated structure slightly decreases with an increasing angle of incidence under the TM-polarized light while under TE polarization the Jsc increases initially with the angle of incidence up to ∼ 30° and then starts decreasing. When both the layers of nanostructures — the bottom Ag nanodisc array and the top ITO nanodisc array are present in the solar cell, then the plasmonic and photonic modes (excited in the active region of the solar cell) interact with each other [45]. This mode-interaction is affected by the angle of incidence of light [45]. Therefore the overall effect of the angle of incidence on the absorption as well as on the Jsc depends on the modes excited in the active layer and on the interaction between these modes.
Figure 7(b) shows the Jsc as a function of incident angle θ of these solar cells, under un-polarized illumination — evaluated as the average of Jsc under TM- and TE-polarization. It is observed that the addition of the integrated structure of top ITO and bottom Ag nanodiscs into the solar cell leads to significant enhancement in the Jsc for incident angles of 0° to 50°, as compared to cells having either no nanostructures or having only the top ITO nanodisc array or only the bottom Ag nanodisc array. More importantly, the solar cell containing the integrated structure exhibits a substantially large Jsc for a range of incident angles from 0° to 40°, as shown in Fig. 7(b). This result reveals a significant advantage of the integrated structure of top ITO and bottom Ag nanodiscs in these solar cells.
3.4 Efficiency characteristics
The J-V characteristics of the various solar cell structures shown in Fig. 1 were evaluated by employing the procedure described in Appendix E and plotted in Fig. 8. A summary of the photovoltaic characteristics of these solar cells is presented in Table 1. It was observed that the optimized integrated structure can enhance the Jsc and the power conversion efficiency (PCE) of the solar cell by ∼25% and ∼26%, respectively, which are significantly large as compared to cells having either only the top ITO nanodisc array or only the bottom Ag nanodisc array. Since it was assumed that the presence of the Ag nanostructures and the ITO nanostructures do not make a difference in the InGaN semiconductor properties or in the contact quality, the open circuit voltage and the fill factor do not change significantly.
4. Conclusions
In this paper, the improved photovoltaic characteristics of various configurations of In0.6Ga0.4N thin-film solar cells — containing either only top ITO nanodisc arrays or only bottom Ag nanodisc arrays or both top ITO and bottom Ag nanodisc arrays — were discussed. It was determined that the introduction of an integrated structure consisting of both the top ITO nanodisc array and the bottom Ag nanodisc array leads to a greater enhancement in the solar cell performance as compared to either of the individual nanodisc arrays. The Ag nanodisc array at the bottom of the solar cell enhances absorption primarily for longer wavelengths of light (with ∼ 60% absorption enhancement at a wavelength of 820 nm). This was attributed to the excitation of surface plasmon-based scattering and coupling of incident light into waveguide modes. The ITO nanodisc array on the top surface leads to an enhanced absorption primarily for the middle wavelengths from 400 nm to 800 nm. This was associated with the coupling of incident light to photonic modes. Hence, a broadband absorption enhancement was obtained by employing the integrated structure of the nanodisc arrays. The optimized integrated structure of the nanodisc arrays enhances the Jsc and PCE of the InGaN solar cell by 25% and 26%, respectively. Moreover, the study of oblique light incidence demonstrates significantly larger Jsc of the solar cell containing the integrated structure of nanodisc arrays as compared to the cells having no nanostructures or having only the top ITO nanodisc array or only the bottom Ag nanodisc array.
Appendix A. Fabrication processes for indium-rich InGaN solar cells
In order to develop the proposed InGaN solar cell containing bottom Ag nanodisc array and top ITO nanodisc array, a multi-step fabrication process can be followed. In this process, the indium-rich InxGa1-xN (x = 0.6) layer can be grown on GaN/Al2O3 epitemplates by metal organic chemical vapor deposition (MOCVD) or by molecular beam epitaxy (MBE) with the required doping levels for the n-InGaN and p-InGaN regions [14,15]. The indium content can be controlled by the growth temperature and pressure. To develop the Ag- and ITO- nanodisc arrays into the solar cell, first, a 2-dimensional array of nano-circles (radius Rb and period P) can be etched in n-InGaN up to height Hb using deep UV lithography or electron beam lithography and inductively coupled plasma reactive-ion etching. This can be followed by Ag deposition, mechanical polishing, and planarization, such that the required Ag layer thickness is obtained. Subsequently, this structure can be transferred onto a suitable substrate. The Al2O3 layer, now on top, can be removed using laser lift-off. A uniform ITO layer of the required thickness can be deposited on top. Finally, the 2D array of ITO nanodiscs can be developed on the ITO layer by using deep UV lithography or electron beam lithography and inductively coupled plasma reactive-ion etching.
Appendix B. Calculation of real and imaginary parts of the refractive indices for InGaN alloy
The refractive indices of InGaN alloy depend on its band gap (Eg), which is a function of indium composition (x) of InxGa1-xN and given by [2]:
The real part of the refractive index of InxGa1-xN is given by the following relation [46]:The imaginary part of the refractive index of InxGa1-xN is evaluated as:
where λ0 is the free space wavelength of incident light.Appendix C. Optimization of height and radius of ITO nanodiscs present on top of the solar cells
To obtain the maximum enhancement in Jsc due to the presence of a top ITO nanodisc array, the height and radius of the ITO nanodiscs were varied from 60 nm to 160 nm and from 70 nm to 120 nm, respectively. Figure 9(a) shows the Jsc enhancement as a function of ITO nanodisc radius Rt, when the ITO nanodisc height (Ht) was varied from 60 nm to 160 nm. A maximum Jsc enhancement of 15.71% was obtained for Ht = 120 nm and Rt = 110 nm. Figure 9(b) shows the absorption in the active region of the solar cell containing top ITO nanodiscs of height 120 nm, with the nanodisc radius varying from 80 nm to 120 nm.
Appendix D. Cross-sectional view of magnetic field distributions in the solar cells containing top ITO nanodisc arrays and/or bottom Ag nanodisc arrays
Figure 10 shows the distributions of the magnetic field enhancement in the different configurations of the In0.6Ga0.4N thin-film solar cells, when the wavelength of the incident optical radiation was taken to be 600 nm. The addition of the ITO nanodisc array on the top surface of the In0.6Ga0.4N solar cells leads to the coupling of the incident light into photonic Bloch-modes in the active layer (as shown in Figs. 10(c) and 10(d)), which results in reduced top-surface reflection from the solar cells as compared to solar cells without any nanostructures (as shown in Fig. 10(a)). Figure 10(d) shows that there is a greater magnetic field enhancement in presence of the integrated structure consisting of a top ITO ND array and a bottom Ag ND array, thereby leading to greater absorption in the active layer.
Appendix E. Calculation of J-V characteristics of the solar cells
The open circuit voltage (${V_{oc}}$) was calculated using the Jsc of the solar cells obtained from Eq. (3) in the following relationship [36]:
where k is the Boltzmann constant, T is the absolute temperature, and $\;{J_0}$ is the reverse saturation current for the p-n diode given by [36]:Here, me is the electronic rest mass i.e. me = 9.109 × 10−31 Kg.
Funding
Ministry of Human Resource Development (RP03246G: UAY program, RP03417G: IMPRINT program); Science and Engineering Research Board (RP03055G); Department of Biotechnology , Ministry of Science and Technology (RP02829G, RP03150G); Defence Research and Development Organisation (RP03356G, RP03436G).
Acknowledgments
We would also like to thank the Digital India Corporation. This publication is an outcome of the R&D work undertaken in the project under the Visvesvaraya PhD Scheme of Ministry of Electronics & Information Technology, Government of India, being implemented by Digital India Corporation (formerly Media Lab Asia).
Disclosures
The authors declare no conflicts of interest.
References
1. J. Wu, W. Walukiewicz, K. M. Yu, W. Shan, J. W. Ager, E. E. Haller, H. Lu, W. J. Schaff, W. K. Metzger, and S. Kurtz, “Superior radiation resistance of In1− xGaxN alloys: Full-solar-spectrum photovoltaic material system,” J. Appl. Phys. 94(10), 6477–6482 (2003). [CrossRef]
2. J. Wu, W. Walukiewicz, K. M. Yu, J. W. Ager III, E. E. Haller, H. Lu, and W. J. Schaff, “Small band gap bowing in In1-xGaxN alloys,” Appl. Phys. Lett. 80(25), 4741–4743 (2002). [CrossRef]
3. R. Singh, D. Doppalapudi, T. D. Moustakas, and L. T. Romano, “Phase separation in InGaN thick films and formation of InGaN / GaN double heterostructures in the entire alloy composition,” Appl. Phys. Lett. 70(9), 1089–1091 (1997). [CrossRef]
4. X. Huang, H. Fu, H. Chen, Z. Lu, I. Baranowski, J. Montes, T.-H. Yang, B. P. Gunning, D. Koleske, and Y. Zhao, “Reliability analysis of InGaN/GaN multi-quantum-well solar cells under thermal stress,” Appl. Phys. Lett. 111(23), 233511 (2017). [CrossRef]
5. Y. Kuwahara, T. Fujii, Y. Fujiyama, T. Sugiyama, M. Iwaya, T. Takeuchi, S. Kamiyama, I. Akasaki, and H. Amano, “Realization of Nitride-Based Solar Cell on Freestanding GaN Substrate,” Appl. Phys. Express 3(11), 111001 (2010). [CrossRef]
6. N. G. Young, R. M. Farrell, Y. L. Hu, Y. Terao, M. Iza, S. Keller, S. P. DenBaars, S. Nakamura, and J. S. Speck, “High performance thin quantum barrier InGaN / GaN solar cells on sapphire and bulk (0001) GaN substrates,” Appl. Phys. Lett. 103(17), 173903 (2013). [CrossRef]
7. C. J. Neufeld, S. C. Cruz, R. M. Farrell, M. Iza, J. R. Lang, S. Keller, S. Nakamura, S. P. DenBaars, J. S. Speck, and U. K. Mishra, “Effect of doping and polarization on carrier collection in InGaN quantum well solar cells,” Appl. Phys. Lett. 98(24), 243507 (2011). [CrossRef]
8. S. Bae, J. Shim, D.-S. Lee, S. Jeon, and G. Namkoong, “Improved Photovoltaic Effects of a Vertical-Type InGaN / GaN Multiple Quantum Well Solar Cell,” Jpn. J. Appl. Phys. 50(9), 092301 (2011). [CrossRef]
9. D. Doppalapudi, S. N. Basu, K. F. Ludwig Jr, and T. D. Moustakas, “Phase separation and ordering in InGaN alloys grown by molecular beam epitaxy,” J. Appl. Phys. 84(3), 1389–1395 (1998). [CrossRef]
10. N. A. El-Masry, E. L. Piner, S. X. Liu, and S. M. Bedair, “Phase separation in InGaN grown by metalorganic chemical vapor deposition,” Appl. Phys. Lett. 72(1), 40–42 (1998). [CrossRef]
11. I. Ho and G. B. Stringfellow, “Solid phase immiscibility in GaInN,” Appl. Phys. Lett. 69(18), 2701–2703 (1996). [CrossRef]
12. J. Adhikari and D. A. Kofke, “Molecular simulation study of miscibility of ternary and quaternary InGaAlN alloys,” J. Appl. Phys. 95(11), 6129–6137 (2004). [CrossRef]
13. S. Mukundan, L. Mohan, G. Chandan, B. Roul, S. B. Krupanidhi, S. Shinde, K. K. Nanda, R. Maiti, and S. K. Ray, “High indium non-polar InGaN clusters with infrared sensitivity grown by PAMBE,” AIP Adv. 5(3), 037112 (2015). [CrossRef]
14. J. J. Xue, D. J. Chen, B. Liu, H. Lu, R. Zhang, Y. D. Zheng, B. Cui, A. M. Wowchak, A. M. Dabiran, K. Xu, and J. P. Zhang, “Indium-rich InGaN epitaxial layers grown pseudomorphically on a nano-sculpted InGaN template,” Opt. Express 20(7), 8093–8099 (2012). [CrossRef]
15. B. N. Pantha, J. Li, J. Y. Lin, and H. X. Jiang, “Single phase InxGa1− xN (0.25 ≤ x ≤ 0.63) alloys synthesized by metal organic chemical vapor deposition,” Appl. Phys. Lett. 93(18), 182107 (2008). [CrossRef]
16. T. Kuykendall, P. Ulrich, S. Aloni, and P. Yang, “Complete composition tunability of InGaN nanowires using a combinatorial approach,” Nat. Mater. 6(12), 951–956 (2007). [CrossRef]
17. C. A. Parker, J. C. Roberts, S. M. Bedair, M. J. Reed, S. X. Liu, and N. A. El-Masry, “Determination of the critical layer thickness in the InGaN/GaN heterostructures,” Appl. Phys. Lett. 75(18), 2776–2778 (1999). [CrossRef]
18. J. Bai, M. Athanasiou, and T. Wang, “Influence of the ITO current spreading layer on efficiencies of InGaN-based solar cells,” Sol. Energy Mater. Sol. Cells 145(3), 226–230 (2016). [CrossRef]
19. N. G. Young, E. E. Perl, R. M. Farrell, M. Iza, S. Keller, J. E. Bowers, S. Nakamura, S. P. DenBaars, and J. S. Speck, “High-performance broadband optical coatings on InGaN / GaN solar cells for multijunction device integration,” Appl. Phys. Lett. 104(16), 163902 (2014). [CrossRef]
20. P. H. Fu, G. J. Lin, C. H. Ho, C. A. Lin, C. F. Kang, Y. L. Lai, K. Y. Lai, and J. H. He, “Efficiency enhancement of InGaN multi-quantum-well solar cells via light-harvesting SiO2 nano-honeycombs,” Appl. Phys. Lett. 100(1), 013105 (2012). [CrossRef]
21. D.-J. Seo, J. Shim, S. Choi, T. H. Seo, E. Suh, and D. Lee, “Efficiency improvement in InGaN-based solar cells by indium tin oxide nano dots covered with ITO films,” Opt. Express 20(S6), A991–A996 (2012). [CrossRef]
22. T. H. Seo, J. P. Shim, S. J. Chae, G. Shin, B. K. Kim, D. S. Lee, Y. H. Lee, and E. K. Suh, “Improved photovoltaic effects in InGaN-based multiple quantum well solar cell with graphene on indium tin oxide nanodot nodes for transparent and current spreading electrode,” Appl. Phys. Lett. 102(3), 031116 (2013). [CrossRef]
23. Z. Bi, D. Bacon-Brown, F. Du, J. Zhang, S. Xu, P. Li, J. Zhang, Y. Zhan, and Y. Hao, “An InGaN/GaN MQWs Solar Cell Improved By a Surficial GaN Nanostructure as Light Traps,” IEEE Photonics Technol. Lett. 30(1), 83–86 (2018). [CrossRef]
24. V. E. Ferry, M. A. Verschuuren, H. B. T. Li, E. Verhagen, R. J. Walters, R. E. I. Schropp, H. A. Atwater, and A. Polman, “Light trapping in ultrathin plasmonic solar cells,” Opt. Express 18(S2), A237–A245 (2010). [CrossRef]
25. H. A. Atwater and A. Polman, “Plasmonics for improved photovoltaic devices,” Nat. Mater. 9(3), 205–213 (2010). [CrossRef]
26. I. M. Pryce, D. D. Koleske, A. J. Fischer, and H. A. Atwater, “Plasmonic nanoparticle enhanced photocurrent in GaN/InGaN/GaN quantum well solar cells,” Appl. Phys. Lett. 96(15), 153501 (2010). [CrossRef]
27. J. Wang, F. Tsai, J. Huang, C. Chen, N. Li, Y. Kiang, and C. C. Yang, “Enhancing InGaN-based solar cell efficiency through localized surface plasmon interaction by embedding Ag nanoparticles in the absorbing layer,” Opt. Express 18(3), 2682–2694 (2010). [CrossRef]
28. W. C. Hsu, J. K. Tong, M. S. Branham, Y. Huang, S. Yerci, S. V. Boriskina, and G. Chen, “Mismatched front and back gratings for optimum light trapping in ultra-thin crystalline silicon solar cells,” Opt. Commun. 377, 52–58 (2016). [CrossRef]
29. O. Isabella, R. Vismara, A. Ingenito, N. Rezaei, and M. Zeman, “Decoupled front/back dielectric textures for flat ultra-thin c-Si solar cells,” Opt. Express 24(6), A708–A719 (2016). [CrossRef]
30. K. X. Wang, Z. Yu, V. Liu, Y. Cui, and S. Fan, “Absorption enhancement in ultrathin crystalline silicon solar cells with antireflection and light-trapping nanocone gratings,” Nano lett. 12(3), 1616–1619 (2012). [CrossRef]
31. R. Chriki, A. Yanai, J. Shappir, and U. Levy, “Enhanced efficiency of thin film solar cells using a shifted dual grating plasmonic structure,” Opt. Express 21(S3), A382–A391 (2013). [CrossRef]
32. H. Shen and B. Maes, “Combined plasmonic gratings in organic solar cells,” Opt. Express 19(S6), A1202–A1210 (2011). [CrossRef]
33. S. Feng, C. Lai, C. Tsai, Y. Su, and L. Tu, “Modeling of InGaN p-n junction solar cells,” Opt. Mater. Express 3(10), 1777–1788 (2013). [CrossRef]
34. E. Palik, Handbook of Optical Constants of Solids, Elsevier Inc., (1998).
35. R. J. Moerland and J. P. Hoogenboom, “Subnanometer-accuracy optical distance ruler based on fluorescence quenching by transparent conductors : supplementary material,” Optica 3(2), 112–117 (2016). [CrossRef]
36. S. M. Sze and K. K. Ng, “Physics of semiconductor devices,” John Wiley & Sons, 2006. [CrossRef]
37. Y. Tanaka, K. Ishizaki, M. De Zoysa, T. Umeda, Y. Kawamoto, S. Fujita, and S. Noda, “Photonic crystal microcrystalline silicon solar cells,” Prog. Photovoltaics 23(11), 1475–1483 (2015). [CrossRef]
38. B. E. A. Saleh and M. C. Teich, “Fundamentals of photonics,” John Wiley & Sons, 1991.
39. H. Heidarzadeh, A. Rostami, M. Dolatyari, and G. Rostami, “Plasmon-enhanced performance of an ultrathin silicon solar cell using metal-semiconductor core-shell hemispherical nanoparticles and metallic back grating,” Appl. Opt. 55(7), 1779–1785 (2016). [CrossRef]
40. K. Q. Le, J. Bai, and P.-Y. Chen, “Dielectric antireflection fiber arrays for absorption enhancement in thin-film organic tandem solar cells,” IEEE J. Sel. Top. Quantum Electron. 22(1), 1–6 (2016). [CrossRef]
41. H. Heidarzadeh, A. Rostami, S. Matloub, M. Dolatyari, and G. Rostami, “Analysis of the light trapping effect on the performance of silicon-based solar cells: absorption enhancement,” Appl. Opt. 54(12), 3591–3601 (2015). [CrossRef]
42. H. Heidarzadeh, “Incident light management in a thin silicon solar cell using a two-dimensional grating according a Gaussian distribution,” Sol. Energy 189, 457–463 (2019). [CrossRef]
43. H. Heidarzadeh and A. Tavousi, “Performance enhancement methods of an ultra-thin silicon solar cell using different shapes of back grating and angle of incidence light,” Mater. Sci. Eng., B 240, 1–6 (2019). [CrossRef]
44. M. Yang, Z. Fu, F. Lin, and X. Zhu, “Incident angle dependence of absorption enhancement in plasmonic solar cells,” Opt. Express 19(S4), A763–A771 (2011). [CrossRef]
45. A. Yanai and U. Levy, “Tunability of reflection and transmission spectra of two periodically corrugated metallic plates, obtained by control of the interactions between plasmonic and photonic modes,” J. Opt. Soc. Am. B 27(8), 1523–1529 (2010). [CrossRef]
46. G. M. Laws, E. C. Larkins, I. Harrison, C. Molloy, and D. Somerford, “Improved refractive index formulas for the AlxGa1−xN and InyGa1−yN alloys,” J. Appl. Phys. 89(2), 1108–1115 (2001). [CrossRef]
47. G. F. Brown, J. W. Ager III, W. Walukiewicz, and J. Wu, “Finite element simulations of compositionally graded InGaN solar cells,” Sol. Energy Mater. Sol. Cells 94(3), 478–483 (2010). [CrossRef]