Performance analysis of WSe2-based bifacial solar cells with different electron transport and hole transport materials by SCAPS-1D.

In recent years, solar cells made of tungsten diselenide (WSe2) have received comprehensive consideration because of their good photoelectric properties. The planar WSe2-based heterojunction solar cell with a preliminary device structure of Au/WSe2/electron transport layer (ETL)/FTO/Al was designed and investigated numerically by SCAPS-1D. CdS ETL is widely used in thin film solar cells (TFSCs). Due to environmental issues and the low band gap (2.42 eV) of CdS ETL, an alternative to CdS ETL was being explored for WSe2 solar cells. In this work, the photovoltaic (PV) performance of the WSe2-based TFSCs with different ETLs were simulated, analyzed and compared, in an attempt to track down a suitable substitute for the CdS ETL. In addition to CdS ETL, ZnO, TiO2 and SnO2 ETLs were independently used to simulate the PV performance of WSe2-based TCSCs. In the wake of analyzing the J-V curves of different cell configurations, SnO2 ETL yielded the best results with PCE of 27.14 % for the single-junction WSe2/SnO2 TFSC. Then, our simulation predicted that the PV performance of the WSe2 device can be improved significantly by using N doped Cu2O as a hole transport layer (HTL). The optimized WSe2 device with SnO2 ETL and Cu2O:N HTL showed an improved PCE of 33.84 % with very good performance stability at higher temperature. Furthermore, this article proposes to use the Au/Cu2O:N/WSe2/SnO2/FTO/Al heterojunction solar cell in bifacial mode and PV performance of the proposed bifacial device have been also studied using SCAPS-1D. Bifacial WSe2 device leads to enhanced PV performance with bifaciality factor for PCE is 83.64 %. Bifacial gain of the proposed device under simultaneous irradiation of 1 sun from the front and 20 % of 1 sun from back side is found to be 13.95 %. Our simulation predicts that the proposed WSe2 bifacial solar cell is capable of converting solar energy into electricity with an efficiency of about 38.38 %.

Introduction

The fast growth of world energy demand and the increasing global pollution as well as the decreasing conventional energy resources clearly demonstrate the need to provide affordable and sustainable clean energy supplies. There are not many resources that can meet the power demand of the tera-watts (TW) scale by 2050. Solar energy is considered as the main compelling alternatives that can meet the demand of 15 TW with a huge amount of solar energy to spare [1], and solve the world energy crisis and reduce the environmental problems. A potentially effective way to harness solar energy is to use photovoltaic (PV) devices called solar cells (SCs) to convert it directly into electricity. The PV technology is relatively simple, with no moving parts or necessary subsystems, which makes it relatively easy to expand to the TW level. The first SC made of Si was reported in the 1950s [2], and recently, its efficiency reached a record 26.1% in 2020 [3]. In the 1970s, many inorganic solar energy absorbing materials were considered to be able to produce high-efficiency SCs. However, in practice, few of them such as CdTe and CIGS SCs have their power conversion efficiency (PCE) exceeding 20% [4]. However, the environmental impact of Cd and the inadequacy of Te, In, and Ga are major issues for the widespread commercialization of these devices. Since then, the number of suitable absorbers has been increasing [5] and in 1988, CZTS/CZTSe stood out from the ongoing investigation of absorber materials for being composed of low-cost, earth-abundant, and nontoxic elements. At present, the PCE of CZTS/CZTSSe devices has advanced to 13.0 % in 2021 [3], which is far behind the CdTe and CIGS-based devices. Very recent theoretical studies predict that 31 % PCE of CZTS/CTSe-based SCs can be achieved by engineering the conduction band edges between the buffer and the absorber layer to reduce non-radiative recombination at the interfaces and utilizing the back surface field layer between the back-electrode and absorber layer [6, 7]. In recent years, the emergence of hybrid perovskite SCs is noticeable because of their suitable optoelectrical properties, low fabrication costs, and its efficiency cross-over the commercialization demarcation line and ramped up to 25.5 % level in just a few years [3]. However, there are many challenges such as hysteresis, long-term stability and sensitivity to moisture, and toxicity associated with perovskite SCs which degrade its performance [8, 9, 10].

Tungsten diselenide (WSe2) has a three-layers microstructure of selenium (Se)-tungsten (W)–Se, in which the interlayer is bonded by a weak van der Waals force, which allows to effectively tune their electrical and optical properties by suitable doping. It was first identified as a possible PV absorber material in the 1970s [11, 12, 13]. It has the optimal band gap of 1.35–1.58 eV [14] for single and double junction SCs, very high optical absorption in the near infra-red and visible region [12, 15, 16], high carrier mobility [12], tunable carrier concentration, and low thermal conductivity [17]. More importantly, it has eminently high chemical phase purity with only one stable phase at room temperature [18] and is very stable in acidic solutions [19]. Recently, TMDCs have attracted enormous consideration owing to their low-cost and superior electrochemical [20, 21], optical [22], mechanical [23], and thermal properties [17]. Hence, it is of a great scientific interest as an active layer for thin film SCs. TMDCs have also been investigated as electrodes for photoelectrochemical SCs [24]. A special feature of layered-type materials is the low surface defect density of the van der Waals planes [25], which is a potential advantage for the use of such materials to prepare heterojunctions for optoelectronic and PV applications [26].

Different methods such as soft selenization [15, 27], high temperature selenization [28], physical vapor transport [29], chemical bath deposition [30], electrodeposition [31], pulsed laser deposition [32], Se–oxygen ion exchange [33], and atmospheric pressure chemical vapor deposition [34], have been used successfully to synthesize high quality WSe2 thin films. Recently, Hongchao Li et al. have demonstrated an environmentally friendly method to prepare WSe2 films with different orientations on the non-conductive quartz glass [35, 36]. Although WSe2 thin films have many applications, such as p-n diodes [37], field-effect transistors [38], and logic devices [39, 40], there are only a few reports that have proven its application in PV SCs so far [41, 42, 43].

In view of all of these aforementioned favorable properties of WSe2 thin films as absorber materials of TFSCs, we adopt crystalline-WSe2-based heterojunction PV devices with different junction partners using SCAPS-1D SC simulator to simulate its PV performance. In this work, several ETL materials namely CdS, ZnO, TiO2, and SnO2 were studied and four WSe2-based TFSCs with the preliminary structure of SLG/Au/WSe2/ETL/FTO/Al were implemented in the SCAPS-1D environment to analyze their PV performances. The J-V characteristics of the SCs have been calculated for different ETLs to compare their PV performance and select suitable ETL for WSe2-based SCs.

The PV performance of WSe2 SCs is hindered by many reasons. For instance, the PV performance of the SCs is limited by the high recombination of minority carriers at the back contact. The passivation of the back contact can improve the PV performance of the device. This can be achieved by the back surface field (BSF) concept of introducing a highly doped p+-type semiconductor between the back contact and the WSe2 absorber layer. Therefore, the electric field at the p-p junction acts as a potential barrier for the photogenerated electrons and repels back toward the p-n junction, which leads to a reduction in recombination of minority carriers at the back contact. Nitrogen-doped Cu2O (Cu2O:N) has high acceptor density, earth-abundant elements, low-cost, and low-temperature synthesis process, making it a suitable candidate as BSF/HTL layer for WSe2 based SCs. In this simulation, with the aim to reduce minority carrier recombination and enhance photogenerated holes collection at the back contact, the effect of introducing Cu2O:N HTL into the WSe2 SCs with the configuration of SLG/Au/

Cu2O:N/WSe2/ETL/FTO/Al has been studied. The impact of the thickness and carrier concentration of different layers of the proposed WSe2-based device with Cu2O:N HTL and without Cu2O:N HTL are also studied. At last, we examine the viability of the proposed WSe2-based device with Cu2O:N HTL to use as a bifacial SC with further improved PV performance.

Numerical modeling and simulation parameters

The simulation can reproduce the outcomes of physical device which can be investigated by varying input conditions. The study of the proposed physical model or device by numerical simulation is a basic method to understand the operation of the device, and predicts how the device parameters immediately affect the physical operation and performance of the device without spending a lot of money and wait a long time. Planar WSe2-based heterojunction TFSCs with a preliminary structure of SLG/back contact (Au)/WSe2/ETL/FTO/front-contact (Al) was adopted in SCAPS-1D environment and analyzed the PV performance of devices. SCAPS-1D is based upon the solution of three governing transport equations in semiconductor; Poisson's equation, continuity equations for free electrons, and holes [44]. SCAPS simulator firstly solves these three coupled differential equations at one-dimensional steady-state conditions, and then calculates quasi-Fermi levels and electrostatic potential of carriers (free electrons and holes) at all points in the SC, and finally calculates the carrier concentration, electric field and other device performance parameters. The relative accuracy of results acquired by simulation depends on precise selection of parameters of materials used in each layer of the device. In this simulation, the material parameters of each layer of the device are selected precisely from authentic literature. In some circumstances, the input parameters are taken from reasonable assumptions to reflect the possible results under actual experimental conditions. The parameters for each layer of the device and the baseline value of each parameter which is used to carry out the simulation are tabulated in Table 1. In the bulk region of each semiconductor layer of the device, a single-level defect (donor/acceptor) with Gaussian energetic distribution is introduced and bulk defect density of each layer of the device is listed in Table 1. The hole and electron capture cross-section for defects in the WSe2 layer are computed as: cm2; where n is the defect density in the WSe2 layer (1014 cm−3), v is the thermal velocity of electron (1.7 × 107 cm/s) and hole (1.4 × 107 cm/s) [56], and τ is carrier lifetime in the WSe2 absorber layer.

Table 1

Baseline simulation parameters of different layers, used for simulating WSe2-based dualjunction bifacial thin film solar cells [45, 46, 47].

Parameters	FTO	TiO2	CdS	ZnO	SnO2	c-WSe2	Cu2O:N
Layer type	Window	ETL	ETL	ETL	ETL	Absorber	BSF
Conductivity type	n	n	n	n	n	p	p+
Thickness (nm)	50	100	100	100	100	1000	100
Bandgap Eg (eV)	3.72	3.26 [48]	2.42	3.31	3.6 [49]	1.55 [50]	2.6 [51, 52, 53]
Electron affinity, χ (eV)	4.0	4.20 [48]	4.30	4.35	3.93 [49]	4.03 [54]	3.2
Relative permittivity εr	9.0	10.0	9.35	9.0	8.0	13.8	6.6
Effective DOS at CB NC (cm−3)	2.2×1019	2.2×1018	2.2×1018	2.2×1018	3.16×1018 [55]	8.3×1018 [56]	2.5×1020
Effective DOS at VB NV (cm−3)	1.8×1018	1.8×1019	1.8×1019	1.8×1019	2.5×1019 [55]	1.4×1019 [56]	2.5×1020
Electron thermal velocity (cms−1)	107	107	107	107	107	1.7×107 [56]	107
Hole thermal velocity (cms−1)	107	107	107	107	107	1.4×107 [56]	107
Electron mobility, μn (cm2V−1s−1)	20	0.1 [57]	100	100	15 [58]	30 [50]	0.1 [53]
Hole mobility, μp (cm2V−1s−1)	10	0.1 [57]	25	25	0.1 [58]	30 [50]	0.1 [53]
Donor concentration, ND (cm−3)	1019	1018	1.15×1017	1018	1019 [58]	0.0	0.0
Acceptor concentration, NA (cm−3)	0.0	0.0	0.0	0.0	0.0	1016	1019
Defect type	Acceptor	Acceptor	Acceptor	Acceptor	Acceptor	Donor	Donor
Energetic distribution	Gaussian	Gaussian	Gaussian	Gaussian	Gaussian	Gaussian	Gaussian
Peak defect density, Nt (eV−1cm−3)	1015	1016	2.5×1017	1016	1016	1014	1015
Characteristic energy (eV)	0.1	0.1	0.1	0.19	0.1	0.1	0.1
Reference energy (eV)	0.6	0.6	0.6	0.6	0.6	0.6	0.6
σn for acceptor defect (cm2)	10–15	10–15	10–15	10–15	10–15	–	–
σp for acceptor defect (cm2)	10–15	10–15	10–15	10–15	10–15	–	–
σn for donor defect (cm2)	–	–	–	–	–	3.67 × 10−14	10–15
σp for donor defect (cm2)	–	–	–	–	–	4.46 × 10−14	10–15
nt at WSe2/ETL interface (cm−2)	1.0×1016	1.0×1016	1.0×1016	1.0×1016	1.0×1016	–	–
nt at HTL/WSe2 interface (cm−2)	–	–	–	–	–	–	1.0×1016a

N.B.: DOS = Density of states, CB = Conduction band, VB = Valance band, σ = Electron capture cross-section of defects, σ = Hole capture cross-section of defects, n = Defect density.

Early reports shows that the value of the carrier lifetime in c-WSe2 thin films is in the range of 6–30 ns [60, 61]. As a first approximation, we used an average value of approximately 16 ns for the carrier lifetime in the WSe2 thin films. Therefore, the calculated values of electron and hole capture cross-section for defects in the WSe2 layer are 3.67 × 10−14 cm2 and 4.46 × 10−14 cm2 respectively. Losses due to recombination at each interface are accounted for by introducing reasonable neutral interface defects, shown in Table 1. The characteristic features of the front and back-contact materials are work function, reflectivity, and surface recombination velocity, etc. The reflectivity at the front and back contact are considered to be 10 % and 90 % respectively, while other properties of the front-contact, back-contact, and working temperature are provided in Table 2. In this simulation, the experimental optical absorption coefficient of the WSe2, Cu2O:N, and different ETLs are taken from the literature [50, 62, 63, 64, 65, 66]. The device is irradiated with a standard AM 1.5G solar spectrum at the power of 100 mW/cm2. In the simulation process, as the shunt and series resistances allow to consider the recombination or leakages losses in solar cells, the reasonable values of 1000 Ω.cm2 and 2.5 Ω.cm2 for the shunt and series resistances, respectively, are considered to realize the real device. In this work, 300 K is assumed to the normal operating temperature of the device.

Table 2

Front and back contact parameters used in simulation.

Parameters	Back-contact	Front-contact
Surface recombination velocity of electrons (cms−1)	1.0×105	1.0×107
Surface recombination velocity of holes (cms−1)	1.0×107	1.0×105
Work function (eV)	5.47; Au (100) [59]	4.06; Al [59]
Cell temperature (K)	298–368

Results and discussion

Effect of different ETLs on the performance of WSe2 solar cells

In order to generate an adequate field at the absorber/ETL junction, the role of the ETL is very important. More importantly, the energy band edges of ETL affect the band offset at the interface, thereby affecting carrier transport. In addition, the ETL can prevent shunting between the TCO and the absorber layer. Kessler J. et al. reported that SCs without ETL provide lower PCE compared to SCs with ETL [67]. Therefore, to implement the TFSC under high PCE conditions, the selection of the ETL is crucial. This section is devoted to a comprehensive study of the influence of different ETLs (namely CdS, ZnO, TiO2, and SnO2) and HTL on the PV performance of the WSe2 SCs. Initially, the thickness of the WSe2 layer and ETLs of all devices are fixed to 1000 nm and 100 nm, respectively. The other simulation parameters remain at the baseline values listed in Table 1.

Figure 1 exhibits the J-V characteristics curves of four WSe2 devices having different ETLs. Simulation shows that the PCE produced by the WSe2 device using CdS ETL is only 20.72%, which is far below the theoretical PCE limit for the WSe2 SC with the absorption layer band gap of around 1.5 eV. Although the overall efficiency of the WSe2/CdS device is not very high, it is expected to be the starting point for the WSe2 SC to further enhance the device's performance. The device is then modified by replacing the CdS ETL with ZnO ETL. It is noteworthy that the performance of WSe2 device with ZnO ETL is slightly improved. Compared with the device using CdS ETL, its PCE has increased by only about 8.6 % (the actual PCE is 22.68 %, which is within close range of the previously reported results [43, 50]). The results are very promising, but due to carrier recombination, improper band structure, incomplete absorption, low carrier collection efficiency, etc., there are still losses, so it is very likely to further enrich the device's performance. For instance, the energy band structure at the WSe2/ETL interface (see Figure 2) is still not optimal, which unfavorably affects the (V) of the device. Therefore, other modifications will now be studied to help us get the efficiency of the device as close as possible to the Shockley-Queisser limit. TiO2 is another commonly used ETL, which has been successfully employed in dye synthesis and perovskite SCs [68, 69]. Using TiO2 as the ETL in the WSe2 device, the V of the WSe2 SC is 1.011 V, which is 177 mV higher than that of the CdS device, and the PCE is 26.43 %. However, deposition of TiO2 is a high temperature (500 °C) process and it also suffers from intrinsic low electron mobility [70]. Alternatively, tin-oxide (SnO2) with its earth-abundant compositions is a low-cost environment friendly, wide band gap n-type semiconductor with high and tunable carrier concentration [71], high electron mobility [72], low-temperature deposition process [73], high thermal and chemical stability, making them favourable ETL candidate for WSe2 SCs. With SnO2 as ETL, WSe2 device has the best performance among other devices (V = 1.051 V, J = 33.30 mA/cm2, FF = 77.56 % and PCE = 27.14 %).

Figure 1

J-V characteristics under front-illumination for the WSe2-based heterojunction TFSCs with different ETLs and with Cu2O:N HTL.

Figure 2

Energy levels of the WSe2-based heterojunction TFSCs with different ETLs.

Now we analyze the PV performance of the WSe2/SnO2 device with the incorporation of HTL. The specific HTL material to be studied in this work is Cu2O:N. Wide band gap Cu2O:N is a highly doped p-type semiconductor with the ability to allow the tuning of its acceptor density [53], making it an appropriate HTL material for WSe2 SCs. Figure 3 shows the device structure and energy band diagram of our proposed SLG/Au/Cu2O:N/WSe2/SnO2/FTO/Al heterojunction TFSCs and its JV characteristics curve is also shown in Figure 1. When using Cu2O:N as the HTL, the performance of the WSe2/SnO2 device is further improved: PCE = 29.46 %, V = 1.125 V, J = 33.60 mA/cm2 and FF = 77.92%. The PV parameters of all WSe2 devices are extracted from JV curves of the representative devices and listed in Table 3. The external quantum efficiency spectra of the WSe2 SC with Cu2O:N HTL and different ETLs are presented in Figure 4. A suitable quantum efficiency for all devices is obtained in the visible range and is related to the good current density (≈33 mA/cm2). For TiO2 ETL, a drop in EQE at wavelength <400 nm is observed. However, the impact of Cu2O:N HTL is clearly observed with improved EQE in the long-wavelength region, indicating that light-induced carrier generation and collection are improved. This drives to a further raise in the J (≈34.0 mA/cm2) of the device.

Figure 3

(a) Schematic of the proposed bifacial dual-junction WSe2 solar cell and (b) it's energy band diagram.

Table 3

PV performance parameters of WSe2 solar cells with HTL and different ETLs.

ETL	HTL	VOC(Volt)	JSC(mA/cm2)	FF (%)	PCE (%)	∗KT	Cell Configuration
CdS	–	0.847	33.41	73.21	20.72	2.89	Au/WSe2/CdS/FTO/Al
ZnO	–	0.894	33.47	75.75	22.68	2.25	Au/WSe2/ZnO/FTO/Al
TiO2	–	1.024	33.40	77.28	26.43	2.29	Au/WSe2/TiO2/FTO/Al
SnO2	–	1.051	33.30	77.56	27.14	2.30	Au/WSe2/SnO2/FTO/Al
SnO2	Cu2O:N	1.125	33.60	77.92	29.46	1.64	Au/Cu2O:N/WSe2/SnO2/FTO/Al
SnO2	Cu2O:N	1.25	33.92	79.88	33.84	1.64	Au/Cu2O:N/WSe2/SnO2/FTO/Al∗∗

∗K is the temperature coefficient of P and expressed in parts per thousand and Kelvin.

∗∗After optimization of thickness and carrier concentration of different layers.

Figure 4

EQE spectra of the WSe2-based heterojunction TFSCs with HTL and different ETLs.

Defect states at the interface are formed due to large lattice mismatch, energy band misalignment, dangling bonds, surface defects, etc. Photo-generated carriers tend to occupy and then recombine with these defect states, thereby hindering the PV performance of the SCs. There are two types of energy band structures at the absorber/ETL interface, namely cliff-like (E < E) and spike-like (E > E) [74]. The activation energy (E) of carrier recombination at the interface depends on the energy band structure at the absorber/ETL interface. The higher the E, the lower the interface recombination, and vice-versa [75, 76]. For the cliff-like band structure, the E (E = E - CBO) is smaller than the band gap of the absorber layer, which leads to an increase in interface recombination of minority carriers, thereby reducing the V of the SC. The opposite is true for the spike-like band structure at the absorber/ETL interface.

T. Minemoto et. al showed that the spike-like band structure at the absorber/ETL interface with CBO of 0 to - 0.4 eV is beneficial for high-performance SCs [77]. The energy band structure of WSe2 SCs with different ETLs is shown in Figure 2. It is observed that a cliff-like band structure with CBO = 0.27 eV is developed at the WSe2/CdS interface, which enhances the minority carrier recombination, as shown by Figure 5, and thereby reducing the V of the device, as shown by the JV curve in Figure 1 and in Table 3. Another important attribute of the band structure at the WSe2/CdS interface is that the band bending also occurs in the CdS region, which indicates that most of the interface defect states are occupied by acceptor defects [78]. Therefore, the Fermi level is pinned at the intermediate gap area and restricts the quasi-Fermi levels splitting under illumination and results in a poor V at the cell output. In addition, the very high lattice mismatch (24.5 %, see Table 4) at the WSe2/CdS interface would further deteriorate the device performance. Therefore, we conclude that CdS ETL is not suitable for high-performance WSe2 SCs.

Figure 5

Recombination rate of the WSe2-based heterojunction TFSCs with HTL and different ETLs.

Table 4

Lattice mismatch∗ at WSe2/ETL interface with different ETLs.

Layer	Lattice Parameters			Lattice Mismatch
	a (Å)	b (Å)	c (Å)
WSe2	3.25	3.25	12.97	–
CdS	4.16	4.16	6.756	24.56 %
ZnO	3.249	3.249	5.205	0.03 %
TiO2	4.594	4.594	2.958	9.40 %
SnO2	4.737	4.737	3.186	2.0 %

Although the cliff-like CBO at the WSe2/ZnO interface is somewhat higher than that at the WSe2/CdS interface, the slight improvement of the PCE of the WSe2 device with ZnO ETL (see Table 3) may be associated with the reduction in carrier recombination due to nearly perfect lattice matching at the WSe2/ZnO interface (see ​Table 4) ​[79] as compared to the WSe2/CdS interface, low absorption of light below 500 nm by the ZnO layer and reduced series resistance of WSe2/ZnO device (as the FF increased). The band structure at the WSe2/TiO2 interface shows a cliff-like CBO of 0.17 eV, which is significantly lower than the first two devices. As a matter of fact, due to the reduction of minority carrier recombination, as witnessed in Figure 5, the PCE of the WSe2/TiO2 device further increased to 26.43 %, see Table 3.

According to our simulated results, the SnO2 ETL produces the highest PCE compared to other ETLs. When SnO2 is used as ETL, the conduction band (- 3.93 eV) of SnO2 is higher in potential than WSe2 layer (- 4.03 eV), resulting in the set-up of a small spike-like CBO of - 0.1 eV at the WSe2/SnO2 interface, which helps to prevent minority carriers from recombining at this interface. Therefore, this improved performance of the WSe2/SnO2 device is due to favourable band alignment at the WSe2/SnO2 interface, extended depletion layer width (see Figure 6), high carrier mobility of SnO2 ETL; this significantly improve carrier collection, and good lattice matching (only 2.0 % lattice mismatch, see Table 4), at the WSe2/SnO2 interface. Another important parameter is the field generated at the WSe2/ETL interface, which affects the injection of photogenerated electrons from the absorber layer to the ETL. Figure 6 shows the electric field at the WSe2/ETL interface for different ETLs. It can be seen that the field generated by CdS, ZnO, and TiO2 TELs at the WSe2/ETL interface is relatively poor. However, SnO2 ETL exhibits an improved field at the interface, which forces to separate photogenerated electron-hole pairs and effectively collects electrons from the absorber layer. With the understanding of device performance improvement, we chose SnO2 as ETL for the WSe2 SC to carry on further study.

Figure 6

Electric field at the WSe2/ETL interface with HTL and different ETLs.

By using Cu2O:N HTL, the field at the Cu2O:N/WSe2 interface enhances the potential distribution along the absorber layer, as it is noticed in Figure 6, which reduces carrier recombination in the bulk absorber layer as well as at the interfaces, as viewed in Figure 5, and improved the V. This field also enhances the separation and collection of photo-induced carriers at the electrode, thereby also increasing J.

Device optimization

Effect of absorber layer thickness and carrier concentration

In this section, the final device structure of SLG/Au/Cu2O:N/WSe2/SnO2/FTO/Al is optimized for the highest PCE in terms of thickness and carrier concentration of all layers. In TFSCs, most of carrier generation by incident photons occurs in the absorber layer. Minority carrier recombination also occurs in the absorber layer. Therefore, thickness of the active layer of SC is an influential parameter to obtain the best performance, as the diffusion length of free carriers represents a constraint with the thickness. To study the influence of the absorber's thickness, simulation was executed by changing it from 300 nm to 2000 nm and putting up all other input parameters at the baseline values summarized in Table 1. Figure 7 illustrates the effect of absorber layer thickness on the PV performance of the WSe2 SC. Because of less carrier recombination in the bulk region of the absorber layer, the photogenerated current (J) is lower and the charge extraction rate is higher for the thin absorber layer, as evidenced by the high V, shown in Figure 7(a). As the thickness increases from 300 nm to 1100 nm, the J sharply increases from ≈30.45 mA/cm2 to ≈33.8 mA/cm2 and then slowly increases until all photons are absorbed, and finally saturated to ≈34.40 mA/cm2. In contrast to J, V of the device decreases from 1.16 to 1.12 V as the thickness increases from 300 to 1100 nm, and the V decreases at a slower rate exceeding this thickness. PCE and FF follow the same trend of J up to the thickness of 1650 nm and then reduce at a diminishing rate as the thickness further increases.

Figure 7

Influence of the WSe2 layer thickness on PV performance parameters: (a) V and J and (b) FF and PCE.

The J is lower for the thinner absorber layer (<1000 nm), which is due to the lower absorption of light by the absorber layer [80]. Nevertheless, the effective band gap of semiconductor thin films decreases as its thickness increases [81] and thereby increases J. However, carrier recombination in the bulk region of the WSe2 layer increases when its thickness is comparable with the diffusion length of the free carriers, and as a result, V decreases. Therefore, in order to operate SCs under high-performance conditions, tuning of absorber layer thickness is essential to maximize current density and minimize bulk recombination. At this point, the best performance was found at the absorber layer thickness of 1650 nm for the monofacial WSe2 SC.

Figure 8 shows the variation of key PV parameters of the WSe2 SC for various acceptor densities of the WSe2 layer ranging from 1015 to 1019 cm−3. It can be seen that, except for J, all PV parameters show a similar trend of exponential growth with the acceptor density up to 2 × 1018 cm−3 and then severely reduced with further increase of acceptor density. When the acceptor density in the absorber layer increases, the built-in potential at the junction of the SC also increases, which forces the charge carriers to move to the corresponding electrodes and enhances the collection of photoinduced carriers and thus, the cell efficiency. FF also increases with the increase of the acceptor level, up to 2 × 1018 cm−3, which is because of increasing in the conductivity of the WSe2 layer. Beyond this value of acceptor concentration, a negative effect on FF is observed. On the contrary, J decreases with increasing the acceptor concentration. When the acceptor concentration in active layer of SC increases, it incompatibly affects the carrier mobility and enhances the inter-band recombination of photo-induced carriers, resulting in the insufficient carrier collection. In addition, Auger recombination and impurity scattering in the absorber layer may play a significant role under high carrier density, resulting in a decrease in J. The best performance is obtained when the acceptor concentration is around 2 × 1018 cm−3. This optimized carrier density for the absorber layer enhanced the PCE to 33.6 % from an unoptimized PCE of 29.8 % for the WSe2 SC.

Figure 8

Key PV parameters of the WSe2 solar cell as a function of acceptor concentration of the absorber layer.

Effect of carrier concentration of SnO2 ETL and Cu2O:N HTL on the device performance

In this section, the carrier concentrations of ETL and HTL are optimized for the highest PCE, using the previously obtained optimized values of absorber layer thickness and acceptor density. Our results show that within the thickness of around 50–150 nm for both HTL and ETL layers, the device performance does not change too much. Therefore, considering simulated results and the fabrication cost, the optimal thickness of 100 nm was chosen for both layers. It has become obvious that this thickness is adequate for the high efficiency of the WSe2 SC. To study the effect of HTL carrier concentration, it was changed from 1017 cm−3–1021 cm−3 and the results are displayed in Figure 9(a). As shown in Figure 9(a), V is constant and independent of carrier concentration, which indicates that there are very few minority carriers in the HTL as photogenerated electrons in the absorber layer are effectively blocked by the sufficiently high potential formed by the high CBO at the HTL/WSe2 interface, see Figure 3(b). This finding also confirms that due to favorable band alignment at the HTL/absorber interface, Cu2O:N HTL effectively blocks electrons and only accepts holes from the absorber [82] (see Figure 3(b)). Between lightly-doped and highly-doped HTL, the main differences in cell performance are the J and FF. As the carrier density of HTL increases, the FF improves initially, which is due to an improvement in conductivity and sheet resistance of HTL [83]. Our results show that when the carrier density of HTL is 3.5 × 1019 cm−3, the V, J, and FF of the device are 1.244 V, 33.92 mA/cm2, and 79.8 % respectively and an eminent PCE of 33.67 % is obtained. The response of the proposed WSe2 SC is also analyzed based on changing the ETL donor density from 1017 to 1020 cm−3. The influence of ETL donor density on cell performance parameters is shown in Figure 9(b). It is evident that J maintains nearly identical value with the variation of ETL donor density. On the other hand, the values of V, FF, and PCE begin to increase at a slow rate between 1017 cm−3 to 2 × 1018 cm−3 and increase sharply from 2 × 1018 cm−3 to 1019 cm−3 and finally saturate beyond that donor level. The optimum value chosen for ETL donor density is 3.75 × 1019 cm−3 on which the PCE of SC reached a value of 33.84 % with V, J, and FF of 1.25 V, 33.92 mA/cm2, and 79.88 % respectively.

Figure 9

Variation of cell performance as a function of (a) HTL (b) ETL carrier concentration.

Effect of cell temperature on the performance of WSe2 solar cells

Environmental parameters strongly affect the overall PV performance of TFSCs. The cell temperature is recognized to be a key environmental parameter that determines SC performance and quality. Since the typical operating temperature of the SC is about 45 °C ± 2 °C, observations are made in the range of 298 K–368 K with a step of 10 K. The temperature coefficient of P (K) is an indicator of performance of PV devices, shows how higher operating temperature affects the device's performance. It can be expressed as follows [84]:where, P = V × J under standard test conditions (298 K); V and J are the voltage and current density at the maximum power point of the JV curve, respectively. Using Eq. (1), K, the temperature coefficient of P for all WSe2 devices studied herein are calculated and tabulated in Table 3. From the data in Table 3, it can be seen that the WSe2 device with SnO2 ETL and Cu2O: N HTL exhibits K = - 1.64 (parts per thousand and Kelvin), indicating the best thermal stability among all WSe2 devices studied herein and is better than previously reported results [84]. It is because of low temperature coefficient of energy bandgap (E) of WSe2 thin films [12].

The J-V characteristics of the optimized WSe2 SC with SnO2 ETL and Cu2O:N HTL at different cell temperature are presented in Figure 10(a). The cell temperature was varied from 25 °C to 95 °C with a step of 10 °C. It is clearly seen in Figure 10(a) that the cell temperature has a significant impact on the J-V characteristics of the WSe2 SC. Normalized PV parameters (V, J, FF, and PCE) extracted from J-V curves as function of cell temperature are illustrated in Figure 10(b). As seen in Figure 10(b) that the FF and V decrease while the J increases slightly with cell temperature. It is also noticed that the V strongly depends on cell temperature, whereas, the J shows only slight variation. The observed impact of cell temperature on V can be interpreted by the temperature-dependent built-in potential at the pn junction of the SC. The intrinsic carrier concentration in the semiconductor increases, as the cell temperature increases. Therefore, when cell temperature increases, the built-in potential of the pn junction decreases, which lead to a decrease in V of the device. On the other side, the carrier generation rate in semiconductors increases with increase in the cell temperature, which causes the J to increase [85]. A similar result is also observed in earlier reported works [86, 87].

Figure 10

(a) The J–V characteristics (b) Variation of normalized values of PV parameters of the WSe2 solar cell with different cell temperature.

Bifacial WSe2 solar cells

Compared with traditional monofacial SCs, the energy harvest per unit area of SCs can be increased without significantly increasing the manufacturing complexity and cost by utilizing bifacial concept. Recent studies have shown that, compared with monofacial SCs, the bifacial SCs installed under high albedo surface can increase the energy at the output to 20–30% [88, 89]. Based on these advantages, the International Photovoltaic Technology Roadmap (ITRPV) predicts that by 2028, bifacial SCs will account for about 40% of the world PV market share [90].

The key parameters that govern the back side contribution of bifacial SCs are the back surface absorption loss, diffusion length of minority carrier, minority carrier lifetime, absorber layer thickness, albedo coefficient of background surface, etc. In a conventional monofacial SC, the front surface with a metallic grid pattern is transparent to allow maximum light to enter the absorber layer. However, an opaque metal film is coated on the back side of the monofacial SC. In contrast, the metallic grid pattern is deposited on both surfaces of the bifacial SC, as demonstrated in Figure 3(a), to reduce surface recombination velocity and material costs, and HTL material with high acceptor density and optical transparency is used to admit maximum photons from back surfaces. In our proposed WSe2 SC, the advantage of using Cu2O:N HTL is the possibility of designing bifacial SCs by allowing maximum collection of albedo components. The use of Cu2O:N HTL at the rare side of the WSe2 SCs can be justified by their high acceptor density and high optical transparency in the visible region [91, 92]. The relation between the diffusion length and the lifetime of free carriers is as follows:where, KT/q is the thermal voltage (0.02586 V at 300 K), μ is the mobility of the carrier in the c-WSe2 thin films (30 cm2 V−1s−1 [50]). According to earlier reports, the lifetime (τ) of minority carriers in the c-WSe2 film is around 30 ns [60, 61]. Using this Eq. (2), the diffusion length of free carriers in the c-WSe2 thin-film is estimated to be greater than 1200 nm. Therefore, due to the elongated diffusion length and carrier lifetime in the c-WSe2 film, if the thickness of the WSe2 layer is less than 1200 nm, regardless of the direction of the incident light, the photogenerated carriers can reach the corresponding electrode before recombination.

For bifacial SCs, the simulation is quite complicated due to the additional illumination from the back side. For bifacial SCs, PV parameters are usually calculated using independent measurements for both back and front side illumination under one sun conditions [93]. Therefore, we present a simulation method for the bifacial SCs, which divides our computations into two independent simulations of the rare and front side illumination of the device. Herein, we use the terms bifacial factor (BF) and bifacial gain (BG) to understand the asymmetric photoelectric behaviour of bifacial devices. The BF is defined by Eq. (3) and allows to estimate the relative response of each side of the device when illuminated individually.where, X is any PV parameter (V, J, FF or PCE) of the device under front, and back illumination condition.

The value of the albedo coefficient depends on the reflection characteristics of the surface. In the range of 300 nm–1300 nm, the integrated average of the spectral albedo coefficients of different surfaces varies from 15.0 % to 88 % [94]. In this simulation, in order to provide some insights, we considered that the WSe2 device was running on a background surface with a 20 % albedo coefficient, and added the relative efficiencies of front and back illumination to calculate the bifacial efficiency: η = η (at 1 sun) + η (at 20% of 1 sun). The additional contribution of the back side illumination to the PCE of the device is represented by BG and defined by Eq. (4) as follows:

The bifacial SC allows photons to enter into the absorber layer from either side of the device. Therefore, the absorber layer thickness is an important parameter to achieve the best performance of bifacial SCs. The WSe2 absorber thickness was varied between 300 nm and 2000 nm in order to find the optimum PCE condition for the bifacial SCs. The dependence of the PV parameters on the thickness of WSe2 layer for both back and front illumination conditions (1 sun) is presented in Figure 11. For the front and back illumination conditions, as the WSe2 layer thickness increases, the V of the device gradually decreases, as viewed in Figure 11(a) and the FF slightly increases (FF not shown). However, as the WSe2 layer thickness increases, J as well as PCE exhibit the same behaviour under both illumination conditions. In particular, J and PCE increase sharply with the thickness of the WSe2 layer up to 800 nm under both back and front illumination condition and then, on further increasing WSe2 layer thickness, both of these PV parameters start decreasing gradually for back-illuminated device and continue increasing at a slow rate and finally saturate for the front-illuminated device, as manifested in Figures 11(b) and 11(c).

Figure 11

Dependence of PV parameters (a) V (b) J and (c) PCE of the WSe2 solar cell on the absorber layer thickness for front- and back-side illumination (1 sun).

Under back-illuminated conditions, when the thickness of the WSe2 layer is comparable with the diffusion length of the minority carriers, the bulk and back contact recombination will be higher, because more minority carriers reach the back contact and recombine. Therefore, we have optimized the thickness of the WSe2 layer for the best efficiency condition in bifacial mode. The optimal WSe2 layer thickness for this particular WSe2 bifacial device is 1100 nm. Note that as mentioned earlier, the optimized WSe2 layer thickness of the monofacial WSe2 is 1650 nm. Therefore, relatively thin WSe2 bifacial devices perform better than thicker devices. These findings are in agreement with previously reported results [95].

J-V characteristics curves of the WSe2 SC with this optimized absorber layer thickness under front illumination at 1 sun, back-illumination at 1 sun, and back-illumination at 20 % of 1 sun conditions are shown in Figure 12. The overall PV performance of the WSe2 SC is lower at the back illumination condition than that at the front-illumination condition.

Figure 12

JV characteristics curves of the WSe2 solar cell under front illumination at 1 sun, back-illumination at 1 sun, back-illumination at 20 % of 1 sun conditions, and net JV curve for bifacial WSe2 solar cells.

Using Eq. (3), We observe that the BF of V and FF maintain values of 99.59 % and 100 %, respectively, indicating that there are no additional losses that may be involved when the device is illuminated from the back. The BF for J is around 84 %, which is due to significant absorption loss at the back surface of the WSe2 device. As a result, it is found that the BF of the PCE of the WSe2 device is 83.64 %. According to the JV characteristics in Figure 12, the WSe2 device provides a PCE of 33.68 % and 4.70 % under front illumination at 1 sun and back illumination at 20% of 1 sun, respectively. Hence our simulation predicts that the bifacial PCE (η) of the WSe2 device is 38.38 %. Using Eq. (4), the bifacial gain (BG) of the WSe2 device is estimated to be 13.95 %. The findings of this investigations are in agreement with previously reported results [88, 89].

Conclusions

In this work, SCAPS-1D was used to model a low-cost, environmentally friendly, earth-abundant tungsten diselenide (WSe2)-based TFSC with Cu2O:N HTL and various ETLs, namely CdS, ZnO, TiO2 and SnO2. First, the best ETL material for the WSe2 SC (in terms of device performance) was determined from various ETLs, which was identified to be SnO2. The suitability of SnO2 ETL for the WSe2 SC was demonstrated by proper lattice matching at the WSe2/SnO2 interface and appropriate band alignment between the conduction bands of SnO2 and WSe2. This study showed that the minority carrier recombination in the bulk region of the absorber layer and at the back-contact reduced significantly when the device was pulled off by adding a heavily doped thin (100 nm) Cu2O:N layer between absorber and back electrode as HTL, which led to further improving the PV performance of the WSe2/SnO2 device. Several factors such as the thickness and carrier density of each layer of the device, the operating temperature etc. affecting the device's performance were investigated. At optimized condition, the highest PCE of the monofacial WSe2 SC was 33.84 % at the WSe2, SnO2 and Cu2O:N layer thicknesses of 1650, 100 and 100 nm with the carrier concentrations of 2.0 × 1018, 3.75 × 1019, and 3.50 × 1019 cm−3, respectively. The effect of temperature on the PV performance of WSe2-based SCs was also reported. The simulation was performed under the cell temperature range of 25–95 °C. The proposed WSe2 device showed very good performance stability at high temperature, with a temperature coefficient of P, K = - 1.64 (parts per thousand and Kelvin). In the present article, the proposed SLG/Ag/Cu2O:N/WSe2/SnO2/FTO/Al device structure of the WSe2 SC was also brought to use for the bifacial WSe2 solar cell. We found that the performance of the WSe2 device under the back-illuminated condition was slightly lower than that of the front-illuminated condition, and the BF of the PCE was about 84.0%. The bifacial WSe2 device with a relatively thin absorber layer performed better than the thick WSe2 device. This investigation has revealed that the optimal thickness of the absorber layer for this particular bifacial WSe2 device is 1100 nm. The bifacial WSe2 device under simultaneous irradiation of 1 sun from the front side and 20.0 % of 1 sun from the back side provides improved PCE of 38.38 % with the BG of PCE is around 14 %. Therefore, this work could provide an insightful approach for designing and fabricating cost-effective, earth-abundant, environment friendly, efficient, and thermally stable bifacial WSe2-based TFSCs.

Declarations

Author contribution statement

M. Atowar Rahman: Conceived and designed the experiments; Performed the experiments; Analyzed and interpreted the data; Contributed reagents, materials, analysis tools or data; Wrote the paper.

Funding statement

This research did not receive any specific grant from funding agencies in the public, commercial, or not-for-profit sectors.

Data availability statement

Data will be made available on request.

Declaration of interests statement

The authors declare no conflict of interest.

Additional information

No additional information is available for this paper.