Research Article | Open Access

T. F. Gundogdu, M. Gökkavas, E. Ozbay, "Improving the Efficiency Enhancement of Photonic Crystal Based InGaN Solar Cell by Using a GaN Cap Layer", *Advances in Materials Science and Engineering*, vol. 2014, Article ID 605204, 9 pages, 2014. https://doi.org/10.1155/2014/605204

# Improving the Efficiency Enhancement of Photonic Crystal Based InGaN Solar Cell by Using a GaN Cap Layer

**Academic Editor:**Sefer Bora Lisesivdin

#### Abstract

We studied a high indium content (0.8) InGaN based solar cell design where the active InGaN layer is sandwiched between a GaN cap layer and a GaN spacer layer. The incorporation of the sacrificial cap layer allows for the etching of the front surface without removing the active InGaN resulting in a 50% enhancement of the short-circuit current density for a 15 nm-thick InGaN layer.

#### 1. Introduction

One of the promising alternatives for the solution of the renewable energy problem is the development of solar cell technologies, where high energy-conversion efficiency is a key requirement [1]. To date, silicon has been the solar cell material of choice owing to its mature technology and comparably better availability. However, silicon, with a relatively small band-gap, has limited efficiency due to excess carrier energy generation and surface absorption. Alternative materials, mainly semiconductor compounds, have also been used in single or higher efficiency multijunction forms. Conventional high efficiency solar cell design relies on multiple junctions, each with differing band-gaps optimized in order to harvest energy from different portions of the solar irradiation. Theoretical studies show that increasing the number of junctions in a solar cell is an effective way of increasing efficiency. The practical number of junctions, on the other hand, is limited to a few due to the difficulty of growing and stacking dissimilar materials on top of each other without compromising material quality. Another limitation is the problem of current extraction from these heterostructures, where barriers between dissimilar materials have to be overcome for efficient current flow.

Following the development of the MOCVD (metal organic chemical vapor deposition) material growth technology, the III-nitride material system has been utilized in a number of key applications, such as lasers and LEDs (light emitting diode), UV (ultraviolet) photodetectors, and HEMTs (high electron mobility transistor). Historically, the material system incorporated only wide band-gap materials (AlN, GaN, and InN) limiting photonic device applications to the blue, UV, and deep-UV portions of the spectrum. When the band-gap of InN was recently revised to 0.7 eV [2, 3], allowing for band-gap tunable InGaN compounds, the spectral range covered by InGaN-based heterostructures was effectively extended to include the photon energies between 3.7 eV and 0.7 eV, which coincides extremely well with desired optical absorption spectrum of multijunction terrestrial solar cells. Additional desirable properties of InGaN material are well-established growth and fabrication processes [4], the possibility of multiple-junctions within a single alloy system, and high carrier mobility [5]. Together with the wide absorption range and possibility of using thinner active layers allowed by a large absorption coefficient, InGaN has captured interest as an emerging candidate for next generation high efficiency cells. Furthermore, InGaN-based solar cells are particularly desirable for space applications because of their superior radiation resistance [6]. Successfully demonstrated cases of InGaN solar cells incorporate low concentration indium alloys, which results in absorption of a small spectral portion of the solar irradiation, ultimately limiting cell conversion efficiency [7]. An increase in indium concentration (e.g., to >25%) to capture a wider spectrum results in the detoriation of crystalline material quality. Epitaxial layers with >25% In concentration have a critical InGaN thickness on the order of a few tens of nanometers [8].

One method to increase the efficiency obtained from thin active layers of absorbing material is to excite guided mode resonances within these thin layers using nanophotonic methods [9]. Solar cell structures incorporating subwavelength modifications such as nanopatterned surfaces [10, 11] and backside gratings [12, 13], plasmonic nanostructures [14, 15], embedded nanoparticles [16], and nanowires [17–19] have been extensively reported. Similarly, there have been a few reports in the literature on InGaN-based solar cells utilizing nanophotonic methods to increase efficiency. Embedded plasmonic nanoparticles were proposed in one study where calculations indicated 27% efficiency enhancement [20]. Although it is possible to study such embedded-type nanoparticles theoretically, in terms of experimental demonstration, nanostructures that are limited to material surface are more practical. An experimental work was presented where metallic nanoparticles were deposited on an InGaN/GaN quantum well solar cell resulting in a 54% increase in external quantum efficiency [21].

Another relatively easy to fabricate subwavelength surface modifications are photonic crystals. Photonic crystal enhanced solar cells aiming to enhance the efficiency of thin film solar cells by the mechanisms of optical path increase, light trapping, and optical impedance matching have been proposed and studied in the literature mostly for silicon and germanium materials [22, 23]. Our group has been working on the growth of InGaN heterostructures [24–26]. Previously, we proposed a solar cell design, where the optical absorption from a thin InGaN active layer was enhanced by a photonic crystal etched into the top surface [27]. It was observed that the etching away of the active InGaN material to fabricate the photonic crystal limited the achievable efficiency. In this work, we employ a GaN cap layer that serves to increase the enhancement achieved by the photonic crystal pattern. In the literature such capping layers have been proposed and demonstrated for a variety of device structures. The function of the cap layer is to improve either the electrical and/or the optical performance of the proposed device. In HEMTs, for example, the cap layer has multiple functions, to planarize/homogenize the surface, to increase the Schottky barrier height due to piezo polarization effects, to improve Ohmic contacts, and to passivate surface states. In LEDs and lasers incorporating InGaN quantum wells, GaN caps serve to homogenize and passivate the surface. To achieve pin structures, p-type GaN cap layers are employed in LEDs, lasers, and photodetectors. From an optical point of view, the GaN cap serves to displace the active layer from the surface. In the literature, the sandwiching of an absorbing material in nonabsorbing material is employed either to improve the absorption spectrum of photodetectors or to localize absorption within high E-field regions to improve bandwidth. Similarly, in lasers, nonabsorbing cap layers are employed as lossless waveguiding regions surrounding the high current areas. In this paper, the GaN cap layer is employed as a sacrificial layer that hosts the photonic crystal lattice structure, effectively displacing the active InGaN layer to high optical field areas. Although the structure is not analysed electrically in this work, it is worth noting that the GaN cap layer can serve as a possible p-GaN contact layer as well.

#### 2. Structure and Method

An initial design of layer structures studied in [27] is shown in Figure 1(a). The thickness of the In_{0.8}Ga_{0.2}N active layer is denoted by , and the thickness of a GaN layer beneath the active layer is denoted by . The epitaxial layers are modeled to be grown on sapphire. Figure 1(c) depicts the cross section of the proposed photonic crystal structure. The 1D photonic crystal structure is formed by etching trenches that have depth and lattice constant . The parameter denotes the width of the photonic crystal grating, where the width of the trenches is equal to -. The graphic in Figure 1(e) illustrates the perspective view of the proposed design. In [27], we have shown that an optimized design of the photonic crystal structure, in Figure 1(a), yields a short-circuit current density increase of 17.5% for a case where = 200 nm and = 150 nm. However, it was also observed that the enhancement is limited since the etching of the photonic crystal pattern effectively removed a significant portion of the active absorber material InGaN. To alleviate this problem, we propose the modified layer structure as shown in Figure 1(b). Here, the InGaN layer is displaced from the surface and sandwiched between two GaN layers to facilitate the etching of the top GaN layer instead of the active InGaN layer. The thickness of the top GaN layer is denoted by the parameter and the thickness of the bottom GaN layer is denoted by the parameter . To achieve a fair comparison among results of different structures, the total thickness of the structure + = + + = 350 nm for all results reported in this paper. When the modified layer structure in Figure 1(b) is etched as shown in the cross section in Figure 1(d), the resulting 3D geometry is as shown in Figure 1(f).

**(a)**

**(b)**

**(c)**

**(d)**

**(e)**

**(f)**

As discussed in [27],* I-V* (current-voltage) curve can be used to express the electrical behavior of solar cells and the efficiency can be extracted by analyzing the* I-V* characteristics. By using the* I-V* curve descriptions for an ideal diode as detailed in [28], it is possible to show that there is an approximate linear relation between the solar cell conversion efficiency and short-circuit current density . As a consequence, one can employ the short-circuit current density as a figure of merit without further elaborating the electrical behavior. If it is assumed that each carrier pair is transported to the circuit and the influence of the photonic crystal structure is neglected, can be written as
In the equation, is the spectral absorption and is the photon flux density [27]. For terrestrial solar cells, the integration starts at 280 nm as a result of the filtering in the ozone layer. The upper limit is determined by the absorbing material. For an In_{0.8}Ga_{0.2}N layer, the absorption is cut-off beyond 860 nm. For any studied structure type, the specific spectral absorption pertaining to each structure was calculated and weighted by the photon flux density to find the short-circuit current density. As the incoming radiation, the spectrum of a blackbody at 5800 K with a power density equal to 1000 W/m^{2} was used as a smooth replacement for the AM 1.5 G irradiation. To calculate the spectral absorption, finite-difference time-domain (FDTD) method was employed with periodic boundary conditions. The spectral dependency of the GaN refractive index was modeled after [29, 30], while the InGaN refractive index was modeled using data from [31, 32] as described in [27].

#### 3. Results

Parametric simulations were performed to maximize the short-circuit current density for the initial structure in Figure 1(a) and the improved structure including the GaN cap layer in Figure 1(b). The effect of the three parameters (lattice constant), (etch depth), and (fill factor) (=*/*) were investigated. As an example, Figure 2 shows the absorption spectra for a 20 nm-thick InGaN layer sandwiched between a 130 nm-thick GaN cap layer and a 200 nm-thick GaN spacer layer, with the photonic crystal parameters of nm, %, and nm, for the two orthogonal polarizations, as well as for unpolarized light. It is immediately observed that there are two peaks located close to 550 nm and 650 nm for both polarizations. The positions of the absorption peaks are slightly offset for the two polarizations and they shift towards larger wavelengths for longer periods, and their absolute value (height) depends on the two parameters and (see [27]). The highest was observed when nm. An increase or decrease from nm resulted in a slow decrease in . To find the optimum geometry, the short-circuit current density was calculated for the parameter space spanned by and . Figure 3 shows the result of this span for the 130 nm GaN-capped and 20-nm thick InGaN layer. Figures 3(a) and 3(b) show the case for light polarized parallel and perpendicular to the photonic crystal trenches, respectively whereas Figure 3(c) illustrates the case when the incoming light is unpolarized. It is observed that the short-circuit current density is maximized at ( nm and %) for light polarized perpendicular to the photonic crystal, at ( nm and %) for light polarized parallel to the photonic crystal, and at ( nm and %) for unpolarized light. It is seen that a reference structure without the photonic pattern (when the fill factor is equal to 100%) results in a = 5.9 mA/cm^{2}. The calculated short-circuit current density for the optimum structure is 8.38 mA/cm^{2}, corresponding to a 42% increase over a reference structure. The dependency of the parametric results around the optimum can be observed by inspecting Figure 3. First, the maximum enhancement occurs at a larger fill factor (but at the same etch depth) value for the perpendicular polarization in comparison with the parallel polarization. Second, as expected, for both polarizations, the short-circuit current density drops quickly as the etch depth increases from the optimum value and the InGaN layer is removed.

**(a)**

**(b)**

**(c)**

Figure 4 shows the calculated absorption spectra and the associated optical field distribution for a solar cell structure with 130 nm GaN cap layer, 20 nm InGaN layer, 300 nm period, 50% fill factor, and 120 nm etch depth. In part (a) of Figure 4, the absorption spectrum of the PC-etched solar cell (120 nm etch depth) and the absorption spectrum of the reference structure (no etch) are compared. It is observed that the PC pattern improves the absorption at two peaks located around 555 nm and 650 nm, while it does not significantly affect the absorption outside the peak regions. Parts (b), (c), and (d) of Figure 4 show the optical field intensity inside the photonic crystal etched solar cell structure for the three different wavelengths of 555 nm, 610 nm, and 650 nm, respectively. These wavelengths correspond to the points marked as 1, 2, and 3 in part (a) of Figure 4. The outline of the etched structure, as well as the boundaries between different layers, is shown for clarity purposes. The top surface of the structure is located at , while the active InGaN layer is placed between nm and nm. Parts (b) and (d) of Figure 4 show significant enhancement for the optical field within the InGaN layer at the absorption peaks, while it is observed in Figure 4(c) that the field is not enhanced at all within the InGaN layer for this wavelength between the peaks. In the literature, the photonic crystal in this work is explained by relating it to a diffraction grating, where normally incident light is diffracted in oblique directions, resulting in a longer path and associated higher absorption. A wave optics explanation would be that the grating couples light into and excites guided slab modes. The existence of diffracted light and resulting Fabry-Pérot resonances in the structure shapes the absorption spectrum. Deeper trenches modify the slab waveguide modes to photonic crystal modes and the resulting absorption peaks are more pronounced.

**(a)**

**(b)**

**(c)**

**(d)**

Figure 5 shows the calculated absorption spectra of the modified GaN-capped structure in Figure 1(d) for different values of the InGaN layer thickness. The etch depth and fill factor are chosen to maximize the absorption of the unpolarized light. For all four curves in Figure 5, the shape of the spectral absorption is qualitatively similar with two distinct high absorption regions that are located between 500 to 600 nm and 600 to 700 nm. As the InGaN thickness increases, the absorption peaks broaden and their height above the baseline decreases in contrast to an increase in total absorption outside the peak regions. This result indicates that the enhancement by the photonic crystal pattern is more prononunced in the wavelength region of the two peaks and the absolute value of the enhancement is higher for thinner InGaN layers.

To compare the short-circuit current densities obtained from the initial design shown in Figure 1(c) and the modified design shown in Figure 1(d), calculations were performed for a range of InGaN layer thickness values. For all calculations, the period nm was chosen, and the etch depth and fill factor were optimized to maximize the short-circuit current density for unpolarized light. In the case of the GaN-capped structure of Figure 1(d), the thickness of the top GaN layer was chosen as another free parameter and optimized separately for each InGaN layer thickness. Figure 6 shows the calculated versus InGaN layer thickness for the initial design without the GaN cap (as shown in Figure 1(c)), the modified design with the GaN cap (as shown in Figure 1(d)), and a reference structure (unetched as shown in Figure 1(b)). It can be seen that for all InGaN layer thicknesses, the incorporation of the GaN-cap layer, i.e., the placement of the InGaN active layer away from the surface resulted in higher current densities. This is expected; since in order to form the photonic crystal pattern, the active InGaN layer is being etched away for the conventional design, whereas, in comparison, only GaN sacrificial cap layer is being etched away for the case of the improved design with the GaN cap layer. Therefore, it is possible to obtain higher current densities with thinner InGaN layers by using the improved design with the GaN cap layer shown in Figure 1(d).

As discussed earlier, it is desirable to design solar cells incorporating InGaN layers thinner than the critical thickness for any given InGaN composition. Figure 7 shows the maximum attainable enhancement over a reference structure without any photonic crystal pattern for both the initial design where the thin InGaN layer is placed at the top surface and the improved design where the thin InGaN layer is sandwiched between two GaN layers. It can be seen that the enhancement is higher for the modified design with the sacrificial GaN cap layer compared to the design where the active InGaN layer is placed at the surface without the GaN cap. In the case with the GaN cap, the enhancement is as high as 50% for InGaN layers thinner than 15 nm and gradually drops as the InGaN layer thickness is increased. In the case of the design without the GaN cap, the maximum attainable enhancement is around 20%, achieved by very thin and thick (150 nm) InGaN layers. For thin layers, this result is readily understood, since the current density of the reference structure is lower for thinner layers. As the InGaN layer thickness gets higher, for equal amount of InGaN being etched away, the unetched portion of InGaN increases, resulting in the enhancement increase between 70 nm and 150 nm. Of course, such a problem does not exist for the GaN-capped design, where only GaN material is etched away and, as a result, the maximum attainable enhancement is always higher than the enhancement attainable without the GaN cap, regardless of the InGaN layer thickness.

In conclusion, the spectral absorption and the short-circuit current density for an InGaN-based solar cell layer structure was calculated, the effect of a photonic crystal surface pattern was investigated, and a sacrificial GaN cap layer was proposed to improve the enhancement of short-circuit current, and it was demonstrated that it is possible to increase the current as much as 50%. This enhancement was obtained by the inclusion of the GaN cap layer which was removed during the surface patterning instead of the absorbing InGaN layer being etched in earlier designs. As an improvement to the current design, antireflective coatings and backside reflectors would further increase the enhancement. As the InGaN growth and fabrication technologies continue to mature, the proposed surface pattern designs can be employed to demonstrate practical solar cells with higher conversion efficiency.

#### Conflict of Interests

The authors declare that there is no conflict of interests regarding the publication of this paper.

#### Acknowledgments

This work is supported by the projects DPT-HAMIT, ESF-EPIGRAT, NATO-SET-181, and TUBITAK under the Project nos. 107A004, 107A012, and 109E301. One of the authors (E. Ozbay) also acknowledges partial support from the Turkish Academy of Sciences.

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#### Copyright

Copyright © 2014 T. F. Gundogdu 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.