Materials Sciences and Applications
Vol.07 No.12(2016), Article ID:72698,13 pages

A Novel Thin-Film, Single-Junction Solar Cell Design1 to Achieve Power Conversion Efficiency above 30 Percent

Joseph Edward O’Connor, Sherif Michael

Department of Electrical and Computer Engineering/Space Systems Academic Group, Naval Postgraduate School, Monterey, USA

Copyright © 2016 by authors and Scientific Research Publishing Inc.

This work is licensed under the Creative Commons Attribution International License (CC BY 4.0).

Received: October 5, 2016; Accepted: December 10, 2016; Published: December 13, 2016


The record efficiency for a thin-film, single-junction solar cell has remained static at 28.8% since 2012. This research presents a unique design that demonstrates potential to exceed record efficiency and approach the theoretical efficiency limit of ~33.5%. The findings of this study are significant, from an efficiency standpoint, and also because the cell design can be realized using existing fabrication methods that do not require complex, post-processing steps. In this study, a benchmark simulation is developed that closely resembles a high-efficiency, front-and-back contact cell. Intrinsic performance limiters are overcome by moving the emitter and front-contact to the back of the cell to eliminate electrical grid shading and improve optical performance. To further improve performance, the P-N junction formed by the emitter layer is removed from the model to allow selective Ohmic contacts to accept (reject) minority (majority) carriers as required. The design modifications improve open-circuit voltage, short-circuit current, and fill-factor which collectively boost efficiency above 30%-primarily due to a 2% gain of incident irradiance and improved optical performance.


Solar Cell, Back-Contacts, Gallium-Arsenide, Thin-Film

1. Introduction

The Shockley-Queisser (SQ) limit, proposed by W. Shockley and H. Queisser in 1961, is the upper theoretical efficiency of a single-junction solar cell (hereafter “cell”) converter operating at 300 K under an incident spectrum approximated by a 6000 K blackbody [1] . For a planar Gallium-Arsenide (GaAs) cell (band gap ~1.42 electron-volts) the SQ limit is about 33.5%. SQ limit research has expanded over the years to incorporate the AM1.5G spectrum, non-radiative recombination, and other variables; yet the limit has remained unchanged [2] . Given claims that manufacturing a >30% efficient cell is possible, it seems improbable that record efficiency would stall at ~25% from 1990-2007 and remain at 28.8% since 2012 [2] - [8] . In this paper, we present a novel design to exceed 30% efficiency by addressing intrinsic performance limitations of the high-efficiency (HE), thin-film, single-junction GaAs cell (hereafter “HE GaAs cell”) presented in [3] [7] [8] . We begin by eliminating an estimated ~2% front-grid shading loss [9] by employing all-back-contact (hereafter “back-contact”) technology that has achieved success with silicon cells [10] [11] . Then we remove the P-N junction formed by the emitter layer to enhance carrier mobility and allow a selective Ohmic contact to accept (reject) minority (majority) carriers as required [6] . These design improvements boost model efficiency above 30% and suggest that record efficiency for HE GaAs cells can be improved.

2. Modeling Semiconductor Devices in Silvaco® AtlasTM

Silvaco is an industry leader for modeling semiconductor devices, and Atlas is the preferred simulator for predicting electrical characteristics of cell structures under bias conditions. Atlas constructs two-dimensional (2D) or 3D structures with internal grids that generate intersections called nodes. Continuity equations, current-density JSC equations, and Poisson’s equation are solved at each node to achieve convergence and simulate the transport of charge carriers in a cell. Device modeling provides insight into the physical phenomena of a cell and displays data in a visual platform [12] .

Since it is not cost-effective to design cells by trial and error, modeling can be useful to investigate ideas before investing time and money to build a prototype. The down-side of modeling is the uncertainty involved in accounting for all physical processes that occur in a cell. Simplifications, numerical methods, and other factors guarantee that a model will never exactly simulate the physical behavior of a cell. Nevertheless, we show that a high-level of confidence can be attained for a given model by carefully accounting for key design parameters, benchmarking model behavior to experimental results, and making single-variable adjustments to predict the behaviors of a new design.

2.1. Modeling a High-Efficiency, Thin-Film, Single-Junction, Gallium-Arsenide Solar Cell with Front and Back Contacts

We begin by assembling design characteristics from [2] - [8] to develop a model that closely resembles the performance of the HE GaAs cell from [3] [8] . We make no assertion that the structure shown in Figure 1 is an exact representation of the cell; however, careful consideration was given to matching design variables with experimental data as we show in this section. It is the opinion of the authors that the cell structure shown in Figure 1 is the product of an industry that focuses on the optimization of front-contact

(a) (b)

Figure 1. (a) 2D model representation of the front-contact HE GaAs cell presented in [3] [8] ; (b) 3D model representation of the HE GaAs cell presented in [3] [8].

grid dimensions to balance trade-offs associated with shading and series resistance. We note that most researchers utilize front-contact technology to achieve record efficiency; however, we believe the benefits derived from back-contact technology can outweigh the drawbacks as with the current record for large-area crystalline silicon cells and Sun Power® Corporation’s industry-leading commercial cell [3] . Both back-contact designs make the case for exploring the technology as a suitable structure for thin-film GaAs cells.

The HE GaAs cell’s foundation is high-quality GaAs manufactured via a metal-or- ganic chemical vapor deposition (MOCVD) and an epitaxial-lift-off (ELO) process. Since the cell is only ~1 μm thick and material quality is excellent, efficient electron transport and minimal bulk recombination is achieved. Additionally, passivation of the cell’s front and back surfaces yields very low surface-recombination velocity which, among other factors, contributes to the highest open-circuit voltage VOC recorded for a single-junction cell. The back-contact is >90% reflective, which enhances photon recycling through radiative recombination and band-edge absorption. A broadband anti-reflection coating (ARC) encompasses the spectral response of the cell (0.3 - 0.9 μm) with some room for improvement at shorter wavelengths as noted in [8] . A front-sur- face electrical grid with estimated 2% coverage is derived from [8] , which corresponds with the coverage of a similar HE cell reported in [9] . Grid shading loss is combined with 4.5% ARC reflectivity/window layer absorption losses to yield a total JSC reduction of ~6.5%, which corresponds with [5] . We assume a minority carrier lifetime of ~50 nanoseconds for an absorption layer doped to ~1017 cm−3, which is compounded by photon recycling [i.e., the process whereby photons are emitted through radiative recombination and subsequently produce another electron-hole-pair (EHP)] to produce “effective” lifetimes of 10x or greater [8] and corresponds to values reported in [13] [14] [15] .

Auger recombination is the process whereby an electron-hole-pair (EHP) transfers energy and momentum to a third carrier via non-radiative recombination [16] . Auger recombination is modeled as


where Cn (Cp) is the auger coefficient for electrons (holes), and ni is the intrinsic electron concentration. Coefficient values ranging from 7 × 10−30 cm6∙s−1 to 1.6 × 10−29 cm6∙s−1 are reported in literature which often distinguishes between direct and indirect auger recombination [16] . This work combines direct and indirect auger recombination effects and sets Cn and Cp to 7 × 10−30 cm6∙s−1 to match HE GaAs cell performance parameters. Reference [5] uses the same value and reports auger recombination as ~6% of total recombination in a HE GaAs cell simulation, which suggests that the mechanism should not be ignored.

Radiative or optical recombination is the process whereby an electron from the conduction band combines with a hole in the valence band to release a photon. This type of recombination is dominant in direct band gap semiconductors (e.g., GaAs) and is essentially the inverse of optical generation. Radiative recombination is modeled as


where B is the intrinsic radiative recombination coefficient, is the energy difference between EHP quasi-Fermi levels, k is Boltzmann’s constant, and T is the operating temperature. Radiative recombination contributes to photon recycling in the HE GaAs cell, which determines the effective minority carrier lifetime. Experimental measurements of B range from~10−11 cm3∙s−1 to ~10−10 cm3∙s−1 in literature [15] [16] [17] [18] [19] , and we adopt 10−11 cm3∙s−1 to match HE GaAs cell performance.

Shockley-Read-Hall (SRH) or “trap-assisted” recombination is a two-step process whereby an electron (hole) occupies an energy level in the band gap and then recombines with a hole (electron). The energy traps may be intentional (i.e. due to doping) or unintentional (i.e., due to defects). If SRH recombination occurs at a surface or interface due to intermediate energy levels caused by dangling bonds or lattice mismatch, it is often referred to as “surface” or “interface” recombination. SRH recombination is modeled as


where τnp) is the electron (hole) minority carrier lifetime, and Etrap is the energy difference between the impurity “trap” located in the band gap and the intrinsic Fermi levels. In this work, we assume a single trap level which corresponds to the most efficiency recombination center. Distributed trap states may be modeled; however, separate SRH statistics are required.

Carrier mobility is dependent upon doping concentration. We set electron and hole mobility for intrinsic GaAs (at 300 K) to 8500 and 400 cm2∙V−1∙s−1, respectively [17] , and employ a concentration-mobility (CONMOB) dependent model to account for reduced mobility due to doping. Fermi statistics are implemented to account for reduced carrier concentrations in the heavily doped emitter and cap layers adjacent to Ohmic contacts; however, we note that model output did not change significantly when using Boltzmann statistics. Surface recombination velocities are modeled at 45 cm-s−1 and 10 cm-s−1 for external surfaces and internal interfaces, respectively, which corresponds with velocities given in [5] [17] [20] .

Experimentally derived refractive index values (real and imaginary) are critical for accurate model performance, and extinction coefficients near the band edge are especially important since they determine the extent that photons are absorbed and “recycled” after radiative recombination events―a primary design consideration for HE cell performance. We found that a widely referenced optical database [18] contained few reference points at the band edge; thus, we compiled information from [21] [22] [23] [24] to cross-check measurements, identify outliers, and assemble a dense measurement sequence. The resulting collection of refractive indices instilled confidence that photon absorption and reflection were accurately accounted for in the model.

The authors of [5] and [17] modeled lumped resistance to match HE GaAs cell fill-factors; however, we opted to model resistivity since the parameter characterizes resistance independently of contact area and improves model accuracy. Ohmic contacts are often used to achieve very low resistivity required for HE operation, typically <10−3 Ω-cm2 for the back-contact (full-coverage) and <10−5 Ω-cm2 for the front-contact (partial coverage). References [25] and [26] assert that semiconductor doping on the order of 1019 cm−3 enables Ohmic contact where tunneling is the dominant transport mechanism. Reference [26] surveys experimental data from n-type GaAs/metal contacts and p-type GaAs/metal contacts to conclude that 1019 cm−3 doping for p-type GaAs is typical, whereas 4 × 1018 cm−3 is more realistic for n-type GaAs. However, [27] reports n-type GaAs doped to 1019 cm−3 on Au/Pt/Ti to achieve 1.1 × 10−6 Ω-cm2 resistivity, and [9] reports n-type GaAs doped to 6.5 × 1018 cm−3 on Pd/Ge/Au to achieve 3.6 × 10−6 Ω-cm2 resistivity. We adopt conservative doping concentrations of 5 × 1018 cm−3 for the n-type, front-contact cap layer with a corresponding resistivity of ~10−5 Ω-cm2, and 1019 cm−3 for the p-type, back-contact cap layer with a corresponding resistivity of ~10−3 Ω-cm2. Incidentally, the low contact resistivities of the cell described in [9] produced an excellent fill-factor FF which contributed to record efficiency in 2009. We note the technological challenges and high cost associated with manufacturing a front-contact with low-resistivity and point out that the problem is avoided entirely when using back- contact technology.

Various works cited in this paper employ models to modify key design parameters in order to determine the impact on cell performance. Authors compare model output parameters with experimental measurements (Jsc, Voc, FF, and efficiency η) to instill confidence in their simulations; however, model output is not compared with experimentally measured external quantum efficiency (EQE). We assert that matching VOC, JSC, FF, and η of a physical cell is not sufficient and that models should also reproduce the EQE curve to ensure that key variables such as window layer absorption and ARC performance are accounted for in the model. To this end, we compare cell performance parameters and EQE traces from [8] and [18] to our model output as shown in Figure 2(a) and Figure 2(b), respectively.

(a) (b)

Figure 2. (a) Comparison of HE GaAs cell model output parameters and J-V curve to measurements presented in [8] [28] ; (b) Comparison of HE GaAs cell model EQE curve to measurements presented in [8] [28] . Referenced EQE curves were traced and scaled to fit the plot.

2.2. Modeling a High-Efficiency, Thin-Film, Single-Junction Gallium-Arsenide Solar Cell with Back-Contacts

Figure 2 establishes confidence that the model sufficiently resembles HE GaAs cell performance as presented in [3] [8] . To maintain the integrity of the model as we experiment with a new design, we alter a single variable and move the emitter (and associated front-contact) to the back of the device. To this end, we reduce the coverage of the back-contact and back-surface-field (BSF) to 40% to make room for the emitter- contact which occupies the remaining 60%. All other variables are held constant except for emitter-contact resistivity which is increased from 10−5 Ω-cm2 to 10−3 Ω-cm2 since ultra-low front-grid resistivity is not required in a back-contact design. 2D and 3D structures of the GaAs, Back-surface Alternating-Contact (GaAs-BAC) cell design are shown in Figure 3(a) and Figure 3(b), respectively. Note that the BSF is split to occupy each side of the back-surface in order to establish symmetry and enable 2D simulation, which decreases model run-time.

The GaAs-BAC cell model exceeded the HE GaAs Cell model for performance categories shown in Figure 4(a). VOC improved 1.0%, JSC improved 1.4%, FF improved 2.7%, and η improved 5.2%. If we categorize the GaAs-BAC cell structure as a ~1 μm thick, planar, untextured cell with good back-surface reflectivity (~90%), [2] indicates that FF and VOC are close to their theoretical limits of 89.1% and 1.15 V, respectively. Conversely, JSC has room to improve to its theoretical limit of 31.6 mA/cm2. We focus on improving JSC and identifying the possible causes of ~1.5 mA/cm2 loss by setting front-surface reflectivity to 0% and changing refractive index values in the window layer to make it completely transparent. The adjustments improve JSC to 31.53 mA/cm2, which suggests that ARC reflection and window layer absorption are the main contributors to current-density loss. An examination of the EQE curve in Figure 4(b) further suggests that most of the loss occurs in the 0.3-0.5μmrange of the solar spectrum which is almost entirely absorbed near the front-surface of the cell. We test the hypothesis by evaluating optical generation G from the front-to-back surface of the cell and spectral generation g at various depths as shown in Figure 5(a) and Figure 5(b). Analysis of the

(a) (b)

Figure 3. (a) GaAs-BAC cell model 2D structure. Note that the BSF occupies both sides of the structure to achieve symmetry and enable accurate 2D modeling; (b) GaAs-BAC cell model 3D structure with key parts labeled. Front-surface and back-surface heterojunctions reduce surface recombination. A “thin” insulating layer occupies space between the emitter and BSF contacts to prevent electrical shorting. Both 2D and 3D modeling were used in this work, and results were very similar; therefore, 2D modeling was adopted to decrease simulation time.

(a) (b)

Figure 4. (a) J-V curves and output parameters of the HE GaAs cell model vs. the GaAs-BAC cell model; (b) EQE curves of the HE GaAs cell model vs. the GaAs-BAC cell model. Ideal EQE response shown in red. The space (gap) between black and red lines indicates loss due to recombination. Higher loss is noted in the 0.3 - 0.5 μm range. Lower loss is noted above 0.5 μm.

(a) (b)

Figure 5. (a) GaAs-BAC cell model optical generation measured from the front-to-back surface of the cell;2 (b) GaAs-BAC cell model spectral generation measured at various depths d within the cell.

plots confirm that 0.3 - 0.5 μm wavelengths are indeed absorbed in the front ~10% of the cell; hence, JSC may be improved by reducing reflection and improving window layer transparency in that spectral range. Further examination of Figure 4(b) reveals less severe losses above 0.5 μm that can be attributed to external luminescence loss and non-radiative recombination loss during carrier transport [8] . We estimate external luminescence loss at <2%, which is indicative of a “good” HE cell [4] ; however, we note that carrier transport could be enhanced by improving carrier mobility?a topic addressed in the next section.

2.3. Modeling an “Emitter-Less” High-Efficiency, Thin-Film, Single-Junction, Gallium-Arsenide Solar Cell with Back-Contacts

Examination of the GaAs-BAC cell model structure shown in Figure 3 identified two regions of high doping concentration and low carrier mobility―the emitter layer and contact-cap layers. Contact-cap layers are constrained to high doping concentration to achieve Ohmic contact with metal; however, the emitter layer is thicker than contact layers and has a greater impact on carrier mobility. At 300K, electron and hole mobility in the GaAs-BAC cell model is reduced to ~3500 cm2∙V−1∙s−1 and ~350 cm2∙V−1∙s−1, respectively, for an emitter-layer doping concentration of ~1017 cm−3 [29] . The band diagrams in Figure 6(a) and Figure 6(b) represent an “n-on-p” GaAs-BAC cell design (i.e. an n-type absorption layer interfaced with a p-type emitter layer).3 The built-in voltage at cell depth d = 1.2 μm shown in Figure 6(a) is designed to separate EHPs; however, the electrostatic potential also reduces VOC Reference [6] asserts that the built-in voltage (P-N junction) is not required for certain cell designs. In the case of the GaAs-BAC cell, minority carrier lifetime is relatively high compared to the distance

(a) (b) (c) (d)

Figure 6. (a) GaAs-BAC cell model band diagram traced from the front-surface through the emitter. The characteristic P-N junction is shown at depth d = 1.2 μm; (b) GaAs-BAC cell model band diagram traced from the front-surface through the BSF; (c) Emitter-less GaAs-BAC cell model band diagram traced from the front-surface through the p-type hetero-contact that accepts minority carriers (holes) and rejects majority carriers (electrons); note the absence of a P-N junction; (d) Emitter-less GaAs-BAC cell model band diagram traced from the front-surface through the n-type hetero-contact that accepts majority carriers (electrons) and rejects minority carriers (holes).

that carriers must diffuse to reach the back-contact; hence, the cell may not require a P-N junction to keep EHPs separated. Furthermore, the p-type hetero-contact at the back-surface is specifically designed to accept (reject) minority (majority) carriers, which implies that the purpose of the emitter may be redundant, or even unnecessary. Therefore, we remove the emitter from the GaAs-BAC cell model and note the results on the band diagrams shown in Figure 6(c) and Figure 6(d).

The “emitter-less” GaAs-BAC cell allows minority carriers (holes) to diffuse freely in the cell with a high probability of capture at the p-type hetero-contact (for an “n-on-p” cell). Note that the diffusion gradient required to drive carriers to a contact is very small (~1 millivolt) and reduces VOC only slightly. In fact, the model shows that VOC (measured to the nearest millivolt) is not reduced, whereas JSC and FF improve slightly as shown in Figure 7(a). Another benefit of removing the emitter is the elimination of the GaAs-BAC cell’s structural “offset” as shown in Figure 7(b). This is an important attribute because a “flat” back-surface is easier to manufacture via the MOCVD/ELO process.

3. Conclusion and Future Work

This research demonstrates the advantage of modeling a novel solar cell design to investigate performance impacts prior to investing time and money to build a prototype. We developed a benchmark model of a thin-film, GaAs solar cell from [3] [8] and changed the model structure to investigate how the cell would perform with back-sur- face contacts. The design alternation significantly improved VOC, JSC, FF, and η―mainly due to a 2% incident irradiance gain from the removal of the front-contact. Analysis of the GaAs-BAC cell simulation identified an area of reduced carrier mobility in the heavily-doped emitter region, which was subsequently removed to analyze whether a “selective” hetero-contact would maintain or even improve performance. We found that JSC, FF, and η improved slightly, which supports the hypothesis proposed in [6] that certain cell designs do not require a P-N junction if hetero-contacts are implemented. We conclude that the relatively long lifetime and comparatively short diffusion length of minority carriers in the GaAs-BAC cell enable efficient operation without a

(a) (b)

Figure 7. (a) J-V curves and output parameters of the GaAs-BAC cell model vs. the emitter-less GaAs-BAC cell model; (b) 2D structure of the emitter-less GaAs-BAC cell model.

P-N junction.

Future research will concentrate on design parameter optimization to further improve cell efficiency. Specifically, the benefits of random texturing on the front-and- back surfaces to promote internal reflection and photon recycling will be investigated. Additionally, high-temperature operation and “radiation-hardness” will be examined to evaluate the cell’s potential for employment aboard spacecraft.

Patents are pending for designs presented in this paper [30] [31] .

Cite this paper

O’Connor, J.E. and Michael, S. (2016) A Novel Thin-Film, Sin- gle-Junction Solar Cell Design to Achieve Power Conversion Efficiency above 30 Percent. Materials Sciences and Applications, 7, 823-835.


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We confirmed that the solar cell simulation was working correctly by calculating spectral generation at an arbitrary wavelength and optical generation (for all wavelengths in the spectral response) at particular depths using experimentally-derived extinction coefficients. The calculations were then compared to model output to verify performance as shown below.

The absorption coefficient α as a function of energy for direct band gap materials is defined as


where A is a material-dependent constant, h is Planck’s constant, is the frequency, and EG is the material band gap. For solar cell analysis, it is convenient to define α as a function of wavelength λ as in


where k is the extinction coefficient and the imaginary portion of the index of refraction. Equation (5) is calculated at an arbitrary wavelength λ = 600 nm (where k = 0.214) to give 4.5 × 106 m−1.

Photon flux ϕ at the cell’s front-surface is defined as


where P is the spectral power density and c is the speed of light. Integrating the AM1.5G solar spectrum yields P = 1000 W∙m−2; hence, (5) gives ϕ = 3 × 1021m−2∙s−1 at the front-surface of the cell.

The spectral generation rate g is defined as


where R is the front-surface reflectivity, η is the internal quantum efficiency, and d is the depth (of interest) in the cell. Equation (7) calculated at λ = 600 nm and d = 1.2 μm gives 7 × 1019 cm−3∙s−1. Now the optical generation rate G may be defined as


which gives 3.6 × 1020 cm−3∙s−1 at d = 1.2 μm, measured over the spectral response of the cell (λ1 = 300 nm and λ2 = 900 nm). Comparing calculations to the model output shown in Figure A1, we conclude that the simulation accurately predicts carrier generation.

(a) (b)

Figure A1. (a) GaAs-BAC cell model spectral generation at cell depth d = 1.2 μm; the red asterisk plots spectral generation g at λ = 0.6 μm (600 nm); the spectral generation curve is integrated to yield optical generation G over the spectral response range (300 nm - 900 nm); (b) GaAs-BAC cell model optical generation G plotted from the front-surface to the back-surface of the cell. The red asterisk plots optical generation G at cell depth d = 1.2 μm. Spectral and optical generation values plotted in the figures correspond with hand calculations and confirm that the model accurately predicts carrier generation.

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1Patents Pending.

2Reference Appendix for more information on Figure 5.

3Both “n-on-p” and “p-on-n” models were developed for this work and performance varied only slightly.