Simulation of nanostructure-based and ultra-thin film solar cell devices beyond the classical picture

Urs Aeberhard

doi:10.1117/1.JPE.4.042099

21 August 2014 Simulation of nanostructure-based and ultra-thin film solar cell devices beyond the classical picture

Urs Aeberhard

Author Affiliations +

Journal of Photonics for Energy, Vol. 4, Issue 1, 042099 (August 2014). https://doi.org/10.1117/1.JPE.4.042099

Abstract

An optoelectronic device simulation framework valid for arbitrary spatial variation of electronic potentials and optical modes, and for transport regimes ranging from ballistic to diffusive, is used to study the nonlocal photon absorption, photocurrent generation and carrier extraction in ultra-thin film, and nanostructure-based solar cell devices at the radiative limit. Among the effects that are revealed by the microscopic approach and which are inaccessible to macroscopic models is the impact of structure, doping- or bias-induced nanoscale potential variations on the local photogeneration rate and the photocarrier transport regime.

1. Introduction

Since the introduction of novel light-trapping schemes reaching beyond the ray-optics limit, high-efficiency solar cells with an active absorber thickness of only a fraction of the typical irradiation wavelength are becoming interesting alternatives to expensive wafer-based architecture. In the case where these ultra-thin film solar cells are made of high-mobility semiconductors, the classical picture of local charge carrier generation and diffusive transport in thermalized distributions may no longer be appropriate, especially in the presence of strong doping-induced internal fields. The same applies to a wide range of nanostructure-based photovoltaic device components, such as quantum well and quantum dot structures or highly doped tunnel junctions, in which the local electronic structure deviates strongly from the flat band bulk picture conventionally assumed in photovoltaic device simulations.

In this situation, microscopic theories on the quantum kinetic level allow for the step beyond the local and macroscopic description by enabling the consideration of arbitrary potential variations and general nonequilibrium carrier distributions at the nanoscale. For the specific case of photovoltaic devices, where optical transitions and charge carrier transport are equally important, such a theory has recently been formulated based on the nonequilibrium Green’s function formalism (NEGF) and has been successfully applied to the investigation of a number of nanostructure-based solar cell architectures. ¹ ^– ⁵

In the present study, the focus is on the impact of structure, doping- or bias-induced nanoscale potential variations on the local photogeneration rate and the photocarrier transport regime, as these features are not accessible in macroscopic approaches. ⁶

2. Theory Framework

The general NEGF theory of nanostructure-based solar cell devices is described in detail in Ref. 7. Here, only the elements relevant for the current investigation will be presented. In consideration of the high computational cost associated with the NEGF simulation approach, the current application of the formalism is restricted to the technologically most relevant class of thin-film devices containing planar nanostructures.

2.1.

Green’s Functions and Self-Energies for Planar Systems

In the case of planar device architectures, the charge carriers are described by a slab representation for the steady-state Green’s functions (GFs),

Eq. (1)

G (r, r^{'}, E) = A^{- 1} \sum_{k_{∥}} G (k_{∥}, z, z^{'}, E) e^{i k_{∥} \cdot (r_{∥} - r_{∥}^{'})},

where

A

is the slab cross-sectional area. The classical electromagnetic field is expressed via the vector potential

Eq. (2)

A (r, t) = A^{- \frac{1}{2}} \sum_{q_{∥}} A (q_{∥}, z, t) e^{i q_{∥} \cdot r_{∥}} .

The steady-state charge carrier GF is obtained from the integro-differential equations

Eq. (3)

G^{R} (k_{∥}, z, z^{'}, E) = G_{0}^{R} (k_{∥}, z, z^{'}, E) + \int d z_{1} \int d z_{2} G_{0}^{R} (k_{∥}, z, z_{1}, E) Σ^{R} (k_{∥}, z_{1}, z_{2}, E) G^{R} (k_{∥}, z_{2}, z^{'}, E),

Eq. (4)

G^{≶} (k_{∥}, z, z^{'}, E) = \int d z_{1} \int d z_{2} G^{R} (k_{∥}, z, z_{1}, E) Σ^{≶} (k_{∥}, z_{1}, z_{2}, E) G^{A} (k_{∥}, z_{2}, z^{'}, E),

with

Eq. (5)

[E - H_{0} (k_{∥}, z)] G_{0}^{R} (k_{∥}, z, z^{'}, E) = δ (z - z^{'}) .

The noninteracting part ${\hat{H}}_{0}$ of the Hamiltonian contains the electronic structure (at this stage, a simple two-band effective mass model) and the electrostatic mean-field potential from coupling to the Poisson equation via the nonequilibrium carrier densities,

Eq. (6)

n (z) = A^{- 1} \sum_{k_{∥}} \int \frac{d E}{2 π} [- i G_{cc}^{<} (k_{∥}, z, z, E)], p (z) = A^{- 1} \sum_{k_{∥}} \int \frac{d E}{2 π} [i G_{vv}^{>} (k_{∥}, z, z, E)] .

The term ${\hat{H}}_{e γ} = - (e / m_{0}) \hat{A} (r, t) \cdot \hat{p}$ is used to describe the interaction of charge carriers with photons that are required for radiative generation and recombination processes via corresponding nonlocal self-energies, e.g., for electrons in the conduction band,

Eq. (7)

Σ_{cc}^{< (gen)} (k_{∥}, z, z^{'}, E) = {(\frac{e}{m_{0}})}^{2} \sum_{μ} p_{cv}^{μ} (z) p_{cv}^{μ *} (z^{'}) \int d E_{γ} G_{vv}^{<} (k_{∥}, z, z^{'}, E - E_{γ}) A^{- 1} \sum_{q_{∥}} A_{μ} (q_{∥}, z, E_{γ}) A_{μ}^{*} (q_{∥}, z^{'}, E_{γ}),

Eq. (8)

Σ_{cc}^{> (rec)} (k_{∥}, z, z^{'}, E) = {(\frac{e}{m_{0}})}^{2} \sum_{μ, ν} p_{cv}^{μ} (z) p_{cv}^{ν *} (z^{'}) \int \frac{d E_{γ}}{2 π ℏ} G_{vv}^{>} (k_{∥}, z, z^{'}, E - E_{γ}) A^{- 1} \sum_{q_{∥}} i ℏ μ_{0} D_{μ ν}^{>} (q_{∥}, z, z^{'}, E_{γ}),

Eq. (9)

\approx \frac{n_{0}^{3}}{{6 π}^{2} ℏ c_{0}^{3} ε_{0}} {(\frac{e}{m_{0}})}^{2} \sum_{μ} p_{cv}^{μ} (z) p_{cv}^{μ *} (z^{'}) \int d E_{γ} E_{γ} G_{vv}^{>} (k_{∥}, z, z^{'}, E - E_{γ}),

where the local approximation of the momentum-averaged GF of free field photon modes,

Eq. (10)

A^{- 1} \sum_{q_{∥}} D_{μ ν, 0}^{>} (q_{∥}, z, z^{'}, E_{γ}) \approx - \frac{{in}_{0}^{3} E_{γ}}{3 π ℏ c_{0}} δ_{μ ν}, (z \approx z^{'}),

was used in the last line. This corresponds to emission into an optically homogeneous medium. The classical electromagnetic vector potential

A

in the multilayer device is obtained from the conventional transfer matrix method (TMM). The local extinction coefficient used in the TMM is related to the local absorption coefficient as obtained from the microscopic interband polarization in terms of the charge carrier GFs. ⁸ At this point, it should be noted that for detailed balance to hold, both self-energies should be expressed in terms of the same photon GF, which can be obtained from an additional set of Dyson and Keldysh equations similar to Eqs. (3) and (4). ⁹

In addition to the electron–photon interaction, the coupling of charge carriers to phonons also needs to be considered for the description of relaxation effects and phonon-mediated transport processes. Here, it is included via the standard self-energy on the level of the self-consistent Born approximation based on the noninteracting equilibrium GFs of bulk phonon modes. ¹⁰

2.2.

Absorption, Generation Rate, and Photocurrent

The local and spectral photogeneration rate $g$ at fixed photon energy ( $\sim E_{γ}$ ), polarization ( $\sim μ$ ), and incident angle ( $\sim q_{∥}$ , $E_{γ}$ ), where $q_{∥}$ is the transverse photon momentum, is related to the corresponding local absorption coefficient $α$ and local photon flux $Φ$ via

Eq. (11)

g^{μ} (q_{∥}, z, E_{γ}) = Φ_{μ} (q_{∥}, z, E_{γ}) α_{μ} (q_{∥}, z, E_{γ}) .

In the NEGF formalism, the spectral photogeneration rate can be obtained from the expression for the local integral radiative interband generation rate $G$ in terms of electronic GFs and self-energies, ⁸ which for charge carriers in the conduction band reads

Eq. (12)

G_{c} (z) = A^{- 1} \sum_{k_{∥}} \int d z^{'} \int \frac{d E}{2 π ℏ} Σ_{cc}^{< (gen)} (k_{∥}, z, z^{'}, E) G_{cc}^{>} (k_{∥}, z^{'}, z, E) \equiv A^{- 1} \sum_{μ} \sum_{q_{∥}} \int d E_{γ} g_{c}^{μ} (q_{∥}, z, E_{γ}) .

At the radiative limit, the short-circuit current density $J_{sc}$ is directly given by the incident photon flux and the total absorptance of the slab,

Eq. (13)

J_{sc} = \frac{e}{A} \sum_{q_{∥}} \int d E_{γ} Φ (q_{∥}, z_{0}, E_{γ}) \cdot a (q_{∥}, z_{\max}, E_{γ}) .

On the other hand, the recombination-free limit of the short-circuit current derives from the quantities computed within the NEGF formalism as follows: ⁸

Eq. (14)

J_{sc} = j_{c} (z_{\max}) - j_{c} (z_{0}) = \int_{z_{0}}^{z_{\max}} d z \partial_{z} j (z) \equiv e \int_{z_{0}}^{z_{\max}} d z G_{c} (z),

where

j_{c}

denotes the electron current in the conduction band, which is given in terms of the charge carrier GFs via

Eq. (15)

j_{c} (z) = \lim_{z^{'} \to z} \frac{e ℏ}{m_{0}} (\partial_{z} - \partial_{z^{'}}) A^{- 1} \sum_{k_{∥}} \int \frac{d E}{2 π} G_{cc}^{<} (k_{∥}, z, z^{'}, E) .

Together, Eqs. (12)–(14) yield the following expression of the absorptance in terms of the local generation spectrum:

Eq. (16)

a_{μ} (q_{∥}, z_{\max}, E_{γ}) = Φ_{μ}^{- 1} (q_{∥}, z_{0}, E_{γ}) \int_{z_{0}}^{z_{\max}} d z g^{μ} (q_{∥}, z, E_{γ}) .

Using the electron–photon self-energy (7) in Eq. (12) for $G$ , the local spectral photogeneration acquires the following form:

Eq. (17)

g^{μ} (q_{∥}, z, E_{γ}) = \frac{i}{ℏ μ_{0}} A_{μ} (q_{∥}, z, E_{γ}) \int d z^{'} A_{μ}^{*} (q_{∥}, z^{'}, E_{γ}) Π_{μ μ}^{>} (q_{∥}, z^{'}, z, E_{γ}),

where

Π

is the photon self-energy related to the nonequilibrium polarization function

P

and the momentum matrix elements

p_{cv}

,

Eq. (18)

Π_{μ ν}^{>} (q_{∥}, z, z^{'}, E_{γ}) = - i ℏ μ_{0} {(\frac{e}{m_{0}})}^{2} p_{cv}^{μ *} (z) P_{cv}^{>} (q_{∥}, z, z^{'}, E_{γ}) p_{cv}^{ν} (z^{'}),

with the random-phase approximation of the interband polarization function given in terms of the charge carrier GFs as follows:

Eq. (19)

P_{cv}^{>} (q_{∥}, z, z^{'}, E_{γ}) = A^{- 1} \sum_{k_{∥}} \int \frac{d E}{2 π ℏ} G_{cc}^{>} (k_{∥}, z, z^{'}, E) G_{vv}^{<} (k_{∥} - q_{∥}, z^{'}, z, E - E_{γ}) .

Using Eq. (17) in Eq. (16), the final expression for the absorptance of a slab of thickness $d = z_{\max} - z_{0}$ acquires the form

Eq. (20)

a_{μ} (q_{∥}, z_{\max}, E_{γ}) = \frac{i}{ℏ μ_{0}} Φ_{μ}^{- 1} (q_{∥}, z_{0}, E_{γ}) \int_{z_{0}}^{z_{\max}} d z \int_{z_{0}}^{z_{\max}} d z^{'} A_{μ} (q_{∥}, z, E_{γ}) A_{μ}^{*} (q_{∥}, z^{'}, E_{γ}) Π_{μ μ}^{>} (q_{∥}, z^{'}, z, E_{γ}) .

The local absorption coefficient $α$ that is required to provide the extinction coefficient

Eq. (21)

κ_{μ} (q_{∥}, z, E_{γ}) = α_{μ} (q_{∥}, z, E_{γ}) \cdot \frac{ℏ c_{0}}{2 E_{γ}}

used in the TMM is formally defined by Eq. (11) in terms of the local values of photon flux and photogeneration. If the local variation of the electromagnetic field is neglected, an expression can be found that contains solely the local electronic properties,

Eq. (22)

α_{μ} (q_{∥}, z, E_{γ}) = \frac{ℏ c_{0}}{2 n_{r} (q_{∥}, z, E_{γ}) E_{γ}} \int d z^{'} Re [i Π_{μ μ}^{>} (q_{∥}, z^{'}, z, E_{γ})] .

2.3.

Recombination and Radiative Dark Current

In analogy to the photogeneration process, a local rate of radiative recombination can be expressed in terms of the emission self-energy and carrier GF,

Eq. (23)

R_{c} (z) = A^{- 1} \sum_{k_{∥}} \int d z^{'} \int \frac{d E}{2 π ℏ} Σ_{cc}^{> (rec)} (k_{∥}, z, z^{'}, E) G_{cc}^{<} (k_{∥}, z^{'}, z, E) \equiv A^{- 1} \sum_{μ} \sum_{q_{∥}} \int d E_{γ} r_{c}^{μ} (q_{∥}, z, E_{γ}),

which defines the transverse momentum average of the local and spectral radiative emission rate

\bar{r}

,

Eq. (24)

{\bar{r}}_{c}^{μ} (z, E_{γ}) \equiv A^{- 1} \sum_{q_{∥}} r_{c}^{μ} (q_{∥}, z, E_{γ}) \approx \frac{n_{0}^{3} E_{γ}}{6 π^{2} ℏ^{2} c_{0}} \int d z^{'} Re [i Π_{μ μ}^{<} (0, z^{'}, z, E_{γ})],

where the photon self-energy component

Π^{<}

is given by Eq. (18) with “

>

” replaced by “

<

”. The radiative dark current is obtained as the spatial integral of the local recombination rate,

Eq. (25)

J_{dark, rad} = e \int_{z_{0}}^{z_{\max}} d z R_{c} (z) .

3. Numerical Simulation Results for Showcase Structures

In the following, deviations from the bulk or flat-band picture are revealed by applying the above formalism to specific structures encountered as components of advanced nanostructure-based solar cell architectures, such as ultra-thin films, superlattices, and heterostructure tunnel junctions. In all cases, the electronic structure is described by a simple two- band model of a direct semiconductor, using either the effective mass approximation (EMA) or an $s p_{z}$ tight-binding (TB) approach, with parameters given in Table 1 (EMA) or in Ref. 5 (TB). Intraband relaxation and energy dissipation are considered via inclusion of inelastic coupling of charge carriers to a single polar optical phonon mode as well as elastic coupling to acoustic phonons, and the extinction coefficient used for the light propagation is computed according to the local approximation in Eq. (22).

Table 1

Material parameters for the two-band effective mass model used for the simulation of the ultra-thin film and quantum well superlattice absorbers.

	GaAs	In0.53Ga0.47As	In0.52Al0.33Ga0.15As
$m_{el}^{*} / m_{0}$	0.063	0.041	0.065	Electron effective mass
$m_{hl}^{*} / m_{0}$	0.22	0.052	0.087	Hole effective mass
$E_{gap}$ (eV)	1.42	0.74	1.18	Bandgap
$E_{aff}$ (eV)	4.07	4.54	4.24	Electron affinity
$P_{cv}$ (eV)	28.8	18	18	Optical matrix element
$ε_{r}$	13.18	14.24	13.18	Relative dielectric constant
$ε_{\infty}$	10.89	8.16	10.72	High frequency dielectric constant
$D_{AC, el}$ (eV)	8.93	8.93	8.93	Acoustic deformation potential (el)
$D_{AC, hl}$ (eV)	5	5	5	Acoustic deformation potential (hl)
$ρ$ ( $m^{- 3}$ )	2329	2329	2329	Material density
$c_{s}$ ( $m s^{- 1}$ )	9040	9040	9040	Sound velocity
$ℏ Ω_{LO}$ (eV)	0.036	0.033	0.038	Optical phonon energy

3.1.

Field-Dependent Generation and Recombination in Ultra-Thin Film Absorber Solar Cells

Recently, plasmonic concepts were presented for strong confinement of the incident light in absorber layers with thickness of only a few nm. ¹¹ ^, ¹² If such ultra-thin film solar cells remain based on bipolar junctions, such as the 40 nm GaAs $p - i - n$ diode with doping density of $3 \times 10^{18} {cm}^{- 3}$ investigated here using the EMA with parameters given in Table 1, the doping-induced built-in potential is dropped over a very short distance (Fig. 1), which results in strong doping- and bias-dependent band tailing (Franz–Keldysh) effects on the absorptance (Fig. 2), and consequently on the shape of the monochromatic current–voltage characteristics (Fig. 3). The bias-dependent band tail leads not only to subgap absorption, but also to a red shifting of the emission spectra under electrical injection at forward bias (Fig. 4). The decrease of the field with increasing bias causes the ideality factor of the radiative dark current to shrink toward unity as the field-induced tunnel enhancement of the recombination process is reduced (Fig. 5).

Fig. 1

Band profile and local density of states of a 40-nm GaAs pin junction solar cell. The doped layers extend over 10 nm and provide a charge carrier density of $3 \times 10^{18} {cm}^{- 3}$ .

Fig. 2

The strong built-in potential present in the ultra-thin junction leads to a Franz–Keldysh tailing of the band edge, inducing the absorption of sub-bandgap energy photons. Following the strength of the built-in field, the tailing (a) increases with doping density and (b) decreases with forward bias. The effect on the absorptance depends on the photon energy, whereas the absorption is increased at sub-bandgap energies, it is reduced above the band edge.

Fig. 3

The bias dependence of the absorptance at different photon energies as displayed in Fig. 2 is reflected in the monochromatic current–voltage characteristics (@ $0.1 kW / {cm}^{2}$ ).

Fig. 4

With the field-induced extension of the band edge to lower energies, the emission is also redshifted.

Fig. 5

The characteristics of the radiative dark current show a tunnel enhancement of the ideality factor, which decreases as the field is reduced.

3.2.

Photocarrier Transport in Quantum Well Superlattice Solar Cells

Quantum well superlattice solar cells were proposed some time ago as tunable bandgap absorber components in multijunction solar cells. ¹³ Recently, absorber structures with strongly coupled quantum wells have shown enhanced carrier extraction efficiency as compared with multiquantum well structures with decoupled wells. ¹⁴ Conventional approaches to the simulation of quantum well superlattice solar cells assume either an infinite superlattice at flat band conditions and band-like semiclassical transport ¹⁵ or ballistic transport via the transfer matrix formalism. ¹⁶

Here, we use again the two-band EMA-NEGF approach. Figure 6 shows the local density of states of a 20 period, selectively contacted ${In}_{0.52} {Al}_{0.33} {Ga}_{0.15} As - {In}_{0.53} {Ga}_{0.47} As$ quantum well superlattice with barrier and well thicknesses of 1.5 and 2.5 nm, respectively, for (a) the flat band situation, corresponding to an intrinsic system and (b) a pin structure with strong built-in field induced by a doping density of $2 \times 10^{18} {cm}^{- 3}$ . The strong coupling of the quantum wells results in a bulk-like density of states, however, exhibiting an confinement-induced increase in the effective bandgap as compared with bulk InGaAs. Both features are preserved in the presence of the large built-in field.

Fig. 6

Local density of states of a 20-period quantum well superlattice at vanishing bias voltage and (a) flat band conditions, corresponding to an intrinsic system, and (b) for a doping density of $2 \times 10^{18} {cm}^{- 3}$ . Although the effective bandgap is increased as compared with bulk InGaAs because of confinement, the strong coupling results in a pronounced carrier delocalization and associated quasi-3D DOS.

The (radiative) current–voltage characteristics of the 20-period superlattice structure are displayed in Fig. 7 for applied forward bias voltage in the dark and under monochromatic illumination with photons of an energy of 0.95 eV and at an intensity of $0.1 kW / {cm}^{2}$ . The current–voltage characteristics $J (V)$ under illumination are perfectly reproduced by the superposition of the bias-dependent photocurrent $J_{abs} (V)$ as computed from the absorptance and the radiative dark current $J_{dark} (V)$ . Therefore, the charge carrier collection probability is close to unity even at large bias voltages in the vicinity of the maximum power point.

Fig. 7

Current voltage characteristics of the 20-period superlattice in the dark and under monochromatic illumination with photons of 0.95 eV and at $0.1 kW / {cm}^{2}$ . Because of the high degree of delocalization, the carrier escape probability is unity, i.e., the light JV-curve is the exact superposition of the bias-dependent photocurrent from the absorptance and the radiative dark current.

The charge carrier extraction can be investigated in more detail by considering the (spectral) current flow at different bias voltages. Figure 8 shows the current–voltage characteristics together with spectral and integral current flow, for (a) short-circuit conditions (0 V), (b) close to the maximum power point (0.45 V), (c) at open-circuit conditions (0.52 V), and (d) at open-circuit voltage in the dark. The sum of integral electron and hole currents is conserved at all bias voltages. As can be inferred from the current spectra, the minibands break up under realistic built-in fields, but at strong coupling, i.e., for thin barriers, carrier extraction proceeds almost ballistically. However, as shown in Fig. 9 for the structures of coupled 2.5-nm wide InGaAs with InAlGaAs barriers of thickness increasing from 1.5 to 3.5 nm, for thick barriers, the character of carrier transport changes from ballistic to sequential tunneling assisted by phonon-mediated relaxation. Thus, a rigorous assessment of carrier extraction in a given superlattice structure under realistic operating conditions is only provided at the quantum kinetic level.

Fig. 8

JV characteristics, integral and spectral current flow at (a) short-circuit conditions (0 V), (b) close to the maximum power point (0.45 V), (c) at open-circuit conditions (0.52 V), and (d) at open-circuit voltage in the dark. Although the minibands break up under realistic built-in fields, carrier extraction proceeds almost ballistically for thin barriers.

Fig. 9

Photocurrent spectrum ( $0.1 kW / {cm}^{2}$ @0.95 eV) of coupled quantum well absorber structures with fixed InGaAs QW size of 2.5 nm and InAlGaAs layer thicknesses ranging from 1.5 to 3.5 nm. With increasing barrier width, the character of carrier transport gradually changes from quasi-ballistic to phonon-assisted sequential tunneling.

3.3.

Absorption Losses in Double Quantum Well Tunnel Junctions for Multijunction Solar Cells

In high-efficiency multijunction solar cells, double quantum well structures have been proposed as tunnel junctions with high peak currents as well as low optical transmission losses. ¹⁷ In the junction region, the pronounced spatial variation of the doping profile gives rise to extreme band bending effects. As shown by recent NEGF simulations employing a $s p_{z}$ tight-binding basis, ⁵ the strong fields result in large deviations of the local density of states from the situation at flat band conditions, apparent in both bulk injection and quantum well tunnel zones [Fig. 10(a)]. The local structure of bound and quasibound states in the junction region not only affects the tunneling transport of charge carriers, but also affects the local absorption coefficient [Fig. 10(b)]. The associated absorptance no longer reflects the joint density of states of either the bulk injection regions or a regular square well potential [Fig. 10(c)].

Fig. 10

(a) Local density of states in a double quantum well tunnel junction, (b) associated local absorption coefficient, and (c) the overall absorptance of the structure, revealing pronounced deviations from the flat band situation of a square well potential and bulk injection regions.

4. Conclusions

The strong local potential variations that are present in ultra-thin or nanostructure-based solar cell devices have a large impact on the photogeneration, photocarrier extraction, and radiative recombination processes, which is fully captured by the proposed NEGF-based simulation framework. Notable examples are strong field-induced band tailing effects in ultra-thin junction solar cells, with associated red shift in the absorption and emission spectra. It is further shown that the deviations from the flat band bulk picture are of special relevance for the assessment of carrier transport in superlattice solar cells and of the absorption losses in novel tunnel junction architectures for multijunction devices.

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Biography

Urs Aeberhard is a senior researcher at the Institute of Energy and Climate Research 5: Photovoltaics, Research Centre Jülich, Germany. He received a diploma degree in theoretical physics and PhD degree in condensed matter theory from the Swiss Federal Institute of Technology in Zurich (ETHZ) in 2004 and 2008, respectively. His current research interests include the theory and simulation of nanostructure-based solar cell devices.

CC BY: © The Authors. Published by SPIE under a Creative Commons Attribution 4.0 Unported License. Distribution or reproduction of this work in whole or in part requires full attribution of the original publication, including its DOI.

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Urs Aeberhard "Simulation of nanostructure-based and ultra-thin film solar cell devices beyond the classical picture," Journal of Photonics for Energy 4(1), 042099 (21 August 2014). https://doi.org/10.1117/1.JPE.4.042099

Published: 21 August 2014

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Cited by 24 scholarly publications.

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KEYWORDS

Solar cells

Quantum wells

Absorption

Superlattices

Electrons

Doping

Phonons

1.

Introduction

2.

Theory Framework

2.1.

Green’s Functions and Self-Energies for Planar Systems

Eq. (1)

Eq. (2)

Eq. (3)

Eq. (4)

Eq. (5)

Eq. (6)

Eq. (7)

Eq. (8)

Eq. (9)

Eq. (10)

2.2.

Absorption, Generation Rate, and Photocurrent

Eq. (11)

Eq. (12)

Eq. (13)

Eq. (14)

Eq. (15)

Eq. (16)

Eq. (17)

Eq. (18)

Eq. (19)

Eq. (20)

Eq. (21)

Eq. (22)

2.3.

Recombination and Radiative Dark Current

Eq. (23)

Eq. (24)

Eq. (25)

3.

Numerical Simulation Results for Showcase Structures

Table 1

3.1.

Field-Dependent Generation and Recombination in Ultra-Thin Film Absorber Solar Cells

Fig. 1

Fig. 2

Fig. 3

Fig. 4

Fig. 5

3.2.

Photocarrier Transport in Quantum Well Superlattice Solar Cells

Fig. 6

Fig. 7

Fig. 8

Fig. 9

3.3.

Absorption Losses in Double Quantum Well Tunnel Junctions for Multijunction Solar Cells

Fig. 10

4.

Conclusions

References

Biography

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