Reducing the transmission loss for below-gap photons is a straightforward way to break the limit of the energy-conversion efficiency of solar cells (SCs). The up-conversion of below-gap photons is very promising for generating additional photocurrent. Here we propose a two-step photon up-conversion SC with a hetero-interface comprising different bandgaps of Al0.3Ga0.7As and GaAs. The below-gap photons for Al0.3Ga0.7As excite GaAs and generate electrons at the hetero-interface. The accumulated electrons at the hetero-interface are pumped upwards into the Al0.3Ga0.7As barrier by below-gap photons for GaAs. Efficient two-step photon up-conversion is achieved by introducing InAs quantum dots at the hetero-interface. We observe not only a dramatic increase in the additional photocurrent, which exceeds the reported values by approximately two orders of magnitude, but also an increase in the photovoltage. These results suggest that the two-step photon up-conversion SC has a high potential for implementation in the next-generation high-efficiency SCs.
High-efficiency photovoltaics using n-i-p semiconductor solar cells (SCs) are very promising for generating electrical power by utilizing solar radiation. The conversion efficiency of single-junction SCs is limited to ∼30% of the so-called Shockley–Queisser limit owing to unavoidable losses, such as transmission loss, thermalization loss, Carnot loss, Boltzmann loss and emission loss1,2. In particular, the main factors influencing this efficiency limitation are the transmission loss of below-gap photons and the thermalization of photogenerated carriers towards the band edge2. Below-bandgap photons with energy smaller than the bandgap of SC are not absorbed and do not contribute to create carriers. Many efforts have been made to realize high-efficiency SCs by breaking the conversion limit and several concepts have been proposed to improve the efficiency3,4,5,6,7,8,9. One promising SC is the intermediate-band SC (IBSC) containing an additional parallel diode connection, which can reduce the transmission loss5,6. The IBSC includes intermediate states in the bandgap. By absorbing a below-gap photon, an electron transits from the valence band (VB) to the intermediate band (IB). Upon absorbing another below-gap photon, the electron is further excited into the conduction band (CB). This two-step photon up-conversion (TPU) process following the absorption of two below-gap photons produces additional photocurrent without degrading the photovoltage. According to ideal theoretical predictions, the IBSC is expected to exhibit extremely high conversion efficiency, >60%, under the maximum concentration and 48.2% under one-sun irradiation5. Substantial progress has been made in this field10,11,12,13,14,15,16,17,18,19,20,21,22,23,24,25,26,27 since Luque and Martí have proposed this concept of IBSC in 1997 (ref. 5). Generally, the absorption strength of the intraband transition from the IB to the CB is very weak14,15,16 and the energy relaxation of the excited electrons into the IB is fast17,18. Therefore, improving the second-excitation efficiency in the TPU process strongly influences the conversion efficiency. The optical selection rule for light irradiating the SC surface is relaxed by designing the electronic properties of the quantized states in low-dimensional structures, such as quantum dots (QDs)19 and impurities20. Obviously, carriers in the IB that have long lifetimes have a greater capacity to improve the TPU efficiency because the absorption coefficient between the CB and IB is proportional to the electron density in the initial state of the intraband transition. However, the application of an additional infrared (IR) light corresponding to 40 suns has been observed to improve the external quantum efficiency (EQE) by <0.5% (refs 21, 22). The further enhancement of TPU is essential to accomplish high conversion efficiency above 50% under sunlight concentration.
TPU has been known to occur at the hetero-interfaces between III and V semiconductors. Extensive studies have been conducted on photoluminescence up-conversion phenomena28,29,30,31,32,33,34. Recently, Sellers et al. have proposed a SC structure which attempts optical up-conversion in electrically isolated up-conversion layers35,36, where high-energy photons emitted by radiative recombination of up-converted electron and hole in the up-conversion layers are absorbed in a SC stacked on it.
Here, we propose a TPU-SC with a hetero-interface, where up-converted electrons are directly collected by the top electrode. We demonstrate an enhancement of the photovoltage as well as a dramatic increase in the photocurrent. This enhancement indicates that the quasi-Fermi gap widens according to the electron excitation into Al0.3Ga0.7As.
Concept of two-step photon up-conversion solar cell
We propose a simple structure with a hetero-interface that demonstrates the concept of the TPU-SC. Here, the TPU is effectively realized at a hetero-interface comprising different bandgaps of III-V semiconductors instead of one IB in the bandgap. Figure 1a,b illustrate the schematic band diagram of the proposed TPU-SC with a diode structure of n-Al0.3Ga0.7As/Al0.3Ga0.7As/GaAs/p-GaAs on a p+-GaAs(001) substrate. A single InAs QD layer capped by 10 nm GaAs was inserted just below the Al0.3Ga0.7As layer to improve the TPU efficiency. Detailed device structure is described in the Methods section. Here, sunlight irradiates the n-Al0.3Ga0.7As side (left-hand side of Fig. 1a). High-energy photons are absorbed in the Al0.3Ga0.7As layer, and excited electrons and holes drift in opposite directions towards n-Al0.3Ga0.7As and p-GaAs, respectively. The excited electrons reach the n-Al0.3Ga0.7As layer without being captured. The VB discontinuity of ∼170 meV (ref. 37) between Al0.3Ga0.7As and GaAs corresponds to the energy loss that occurs at the hetero-interface. This loss must be carefully designed when optimizing the SC structure. Below-gap photons passing through Al0.3Ga0.7As excite the InAs QDs and GaAs. The excited electrons and holes in GaAs drift in opposite directions in the internal electric field. Although the excited holes can reach the p-GaAs contact layer, the electrons are accumulated at the Al0.3Ga0.7As/GaAs interface. Besides, similar spatial carrier separation occurs for photoexcited carriers in the InAs QDs. Electrons accumulated at the hetero-interface are separated from the holes and are expected to exhibit extended lifetimes, which can be in the order of milliseconds in some cases38. Long-lived electrons improve the absorption strength for below-gap photons for GaAs and are efficiently pumped upwards into the Al0.3Ga0.7As barrier. As shown in Fig. 1b, the output voltage of TPU-SC corresponds to the gap of the quasi-Fermi levels for electrons in Al0.3Ga0.7As and holes in GaAs at an operating condition.
Measurement of external quantum efficiency
To demonstrate the TPU effect, we measured the EQE and its change (ΔEQE) that were produced by irradiating SC with IR light with photon energy lower than the fundamental edge of InAs QDs. All the measurements were performed at room temperature (290 K). Fig. 2a,b show the EQE and ΔEQE spectra for TPU-SC with InAs QDs, respectively. Without the IR illumination, two clear absorption edges appear at 685 and 875 nm in the EQE spectrum (black colour in Fig. 2a); these edges correspond to the bandgaps of Al0.3Ga0.7As and GaAs, respectively. The EQE signal for high-energy photons (above the bandgap of Al0.3Ga0.7As) decreases because of the shallow penetration of the incident light and significant carrier recombination at the surface, which are suppressed by introducing a wider-gap window layer39. When excited above the bandgap of Al0.3Ga0.7As, the excited electrons and holes are collected at the corresponding electrodes. However, the behaviour of carriers generated by below-gap photons in Al0.3Ga0.7As is different. Below-gap photons are predominantly absorbed in i-GaAs and generate electrons and holes. The excited holes drift towards the p-layer of GaAs. On the other hand, the drift current of excited electrons is partially obstructed at the Al0.3Ga0.7As/GaAs interface, resulting in a significant drop of the EQE signal below the bandgap of Al0.3Ga0.7As. The observed photocurrent in the wavelength region between the bandgaps of Al0.3Ga0.7As and GaAs is caused by the thermal and tunnelling escape of the accumulated electrons at room temperature. In this wavelength region, the EQE signal also shows a gradual decrease with increasing wavelength because the optical absorption coefficient becomes small with increasing wavelength. In the near-IR wavelength region below the bandgap of GaAs, the EQE signal decreases drastically and shows a small structure at 912 nm that can be attributed to thermally excited carriers from the deep quantized states of the InAs wetting layer21,40.
Figure 3a shows the temperature dependent EQE spectra. At low temperature, the absorption edges of Al0.3Ga0.7As and GaAs are relatively steep owing to the excitonic feature. With increasing the temperature, the absorption edges shift and the below-gap state attributed to the InAs-wetting layer appears gradually. The EQE signal from QDs was very weak and below the detection limit because of the deeper quantized state. Figure 3b shows the temperature dependence of the current density at 780 nm excited by a laser diode (LD). 780 nm photons directly excite i-GaAs. The excitation power density was 47 mW cm–2. The current density increases with increasing the temperature. The inset of Fig. 3b indicates the applied bias voltage dependence of the estimated thermal activation energy EA. EA monotonically decreases with increasing the electric field because of lowering the effective barrier height at the hetero-interface. EA shows the maximum of 221±3 meV at 0.02 V. Conversely, applying higher positive bias voltage weakens the internal electric field significantly and makes flatter the band. As the forward current increases even at the same bias condition with increasing the temperature, the detected photocurrent decreases rapidly with flatten the band. Thereby, EA decreases and finally becomes negative with increasing the bias voltage. The maximum EA excellently coincides with the estimated CB discontinuity between Al0.3Ga0.7As and GaAs37. Figure 3c shows the temperature dependence of the current density at 912 nm corresponding to the wetting layer state. We recorded the current at the bias of 0.02 V. Here, the excitation light was produced by a supercontinuum laser, passed through a 270 mm single monochromator. The monochromatic excitation-laser line width was 9.6 nm. The EQE line width of the wetting layer state is ∼15 nm and the temperature drift of the wetting layer state is ∼2.9 nm, so that we fixed the excitation wavelength in this experiment. The evaluated thermal activation energy was 254±5 meV. Photo-excited electrons are thermally excited from the GaAs edge to the Al0.3Ga0.7As one, from the InAs wetting layer state to the Al0.3Ga0.7As edge, and from the ground state of the QD transition to the GaAs edge. We did not confirm an obvious change caused by thermal excitation of holes, suggesting photo-excited holes reach the p-GaAs contact without captured at the hetero-interface. These optical responses are linear with the excitation density, and we did not observe any obvious nonlinear two-photon absorptions, as discussed later.
The temperature dependence of the photoluminescence (PL) intensity reflects the change in the recombining carrier density in QDs. That change is caused by the thermal carrier escape from the confined state. Figure 4a,b show PL spectra for TPU-SC with InAs QDs measured at various temperatures and the temperature dependence of the integrated PL intensity, respectively. The wavelength and power density of the excitation laser were 784 nm and 2.1 mW cm–2, respectively. The PL represents the ground state transition of InAs QDs. The PL peak shifts with temperature and obeys a well-known Varshni’s relationship. The integrated PL intensity decreases with increasing the temperature. The thermal activation energy evaluated from the Arrhenius plot is 244±4 meV, which coincides with the CB discontinuity between the ground state of InAs QD and the GaAs band edge41. Figure 5 summarizes these results we obtained. This clear picture clarifies available energy states for confined carriers at the hetero-interface of TPU-SC with InAs QDs.
Next, we discuss the EQE spectrum measured under illumination by an IR-LD. The wavelength of the IR-LD was 1,300 nm, which is sufficiently long to prevent interband transitions and can only induce intraband transitions, as shown in Fig. 4a. In this case, the spectrum was dramatically changed. It must be noted that the EQE signal (drawn by magenta colour in Fig. 2a) increases remarkably in the wavelength region between the bandgaps of Al0.3Ga0.7As and GaAs and seems to eliminate the loss caused by the electron accumulation at the hetero-interface. We defined ΔEQE (blue colour in Fig. 2b) as the difference between the EQE obtained with and without the 1,300 nm LD illumination. The ΔEQE enhancement was ∼30%. We also observed an increase in the EQE signal attributed to the quantized states of the InAs wetting layer. However, ΔEQE at the InAs QD ground state of 1,186 nm was very weak, suggesting that optical absorption in the single InAs QD layer with the in-plane QD density of ∼1.0 × 1010 cm–3 is not enough to contribute to the change in the current generation at the QD ground state. Most of the excited electrons in GaAs were separated from the holes and accumulated at the Al0.3Ga0.7As/GaAs interface. Such densely accumulated long-lived electrons are easily pumped into the Al0.3Ga0.7As barrier by the 1,300 nm LD light, which accomplishes efficient TPU at the hetero-interface. Additionally, we fabricated a reference TPU-SC without InAs QDs. The EQE and ΔEQE spectra for the reference TPU-SC are shown in Fig. 2c,d, respectively. The same absorption edges of Al0.3Ga0.7As and GaAs appear in the EQE spectrum. As shown in Fig. 2a,c, the EQE drop observed below the bandgap of Al0.3Ga0.7As was significant for TPU-SC with InAs QDs, which is caused by extra carrier recombination in QDs. As shown in Fig. 2d, ΔEQE is obviously generated even in TPU-SC with the hetero-interface of Al0.3Ga0.7As/GaAs without InAs QDs. Comparison between the ΔEQE spectra suggests that the hetero-interface containing InAs QDs improves the TPU efficiency for the accumulated electrons. The optical selection rule of the intersubband transition of electrons in an ideal two-dimensional structure is forbidden for light irradiating the two-dimensional plane perpendicularly42. The finite thickness of the accumulation layer relaxes the selection rule, and, moreover, InAs QDs play a role enhancing the TPU efficiency. Generally, it is well known that the electronic wavefunctions in QDs are quantized on all three dimensions, and light of all polarization directions induces intersubband transitions43. Thus, electrons at the hetero-interface obey the selection rule modified by QDs and are efficiently pumped into the CB of Al0.3Ga0.7As by the 1,300 nm LD illumination.
Short-circuit current generated by 780 nm photo-excitation
Figure 6 shows the short-circuit current density of TPU-SC with InAs QDs as a function of the excitation power density of a single-colour excitation light source. We used a 780 nm LD for excitation. The 780 nm photons traversed Al0.3Ga0.7As and directly excited the intrinsic layer of GaAs. The excited electrons drifted towards the n-layer and were obstructed at the hetero-interface; subsequently, they were partially extracted by thermal and tunnelling processes at the interface and finally reached the n-side electrode, generating a photocurrent. The short-circuit current density clearly exhibits a linear dependence on the excitation power density, indicating that no nonlinear two-photon absorption occurs in Al0.3Ga0.7As.
TPU at biased conditions
Next, we studied TPU phenomena at biased conditions using two-colour photo-excitations. Figure 7a shows typical current–voltage curves obtained for the TPU-SC with InAs QDs with illumination from the 780 nm LD and the additional 1,300 nm LD. The excitation power density of the 780 nm LD was 110 mW cm–2. When only the 1,300 nm LD was used for the excitation, no changes were observed in the photocurrent and photovoltage, indicating that the below-gap photons for GaAs do not cause non-linear two-photon absorption in GaAs. When irradiated by the 780 nm LD, the TPU-SC produces both photocurrent and photovoltage and the 780 nm photons traverse Al0.3Ga0.7As and excite GaAs. The excited electrons drift towards n-Al0.3Ga0.7As and are obstructed at the hetero-interface. The accumulated electrons at the hetero-interface are partially extracted by thermal and tunnelling processes and thus generate electric power. By adding the 1,300 nm LD illumination, we observed an obvious enhancement in the photocurrent; for a density of 320 mW cm–2, the photocurrent increased by 0.6 mA cm–2. This value is rather high and approximately two orders of magnitude greater than previously reported values, as described in the Discussion section. Generally, the intraband excitation strength is proportional to the electron density in the initial state. Because of the carrier separation in the internal electric field, extremely long-lived electrons are densely accumulated at the hetero-interface and fill all the confinement states of the InAs QDs and the wetting layer. Here, it must be noted that we confirmed an increase in the photovoltage by adding the 1,300 nm LD illumination. This demonstrates that TPU enhances quasi-Fermi level splitting, which is a key feature that characterizes the operation of the TPU-SC. When irradiated by the 780 nm LD, the SC operates only in the GaAs region, and the open-circuit voltage is predominantly limited by GaAs. TPU populates electrons in Al0.3Ga0.7As and consequently, the quasi-Fermi levels split further.
Figure 7b,c summarize the 1,300 nm excitation power dependence of the change in the short-circuit current density, ΔJsc, and the open-circuit voltage, ΔVoc. ΔJsc and ΔVoc exhibit different behaviours according to a model proposed in the Methods section. ΔJsc is proportional to Pex0.73, where Pex is the 1,300 nm excitation power density. Generally, the short-circuit current has a linear relationship with the excitation density. The measured ΔJsc shows a sub-linear response. Figure 7d indicates the dependence of the evaluated n value on the reverse-bias voltage in the relationship Jsc ∝ Pexn. As the reverse-bias voltage increases, n increases and approaches unity. The dense space charge accumulated at the hetero-interface weakens the electric field, resulting in a sub-linear response to the excitation density because a stronger electric field improves the carrier collection efficiency of the TPU. Conversely, ΔVoc increases non-linearly with the 1,300 nm -excitation power density. A detailed model that reproduces ΔJsc and ΔVoc is proposed and discussed in the Methods section. As given in equation (4), ΔVoc is an increase against Voc,single which is the open-circuit voltage measured at the single-colour excitation without the 1,300 nm LD illumination. The increase in ΔVoc includes effect of the voltage boost effect at the hetero-interface, which follows an increase in the extra photocurrent ΔJsc created by the additional 1,300 nm LD illumination. Next, we demonstrated a difference between the TPU effect caused by the optical process and the thermal excitation effect. To confirm the contribution of 1,300 nm LD illumination to ΔVoc, we carefully measured ΔVoc as a function of Jsc controlled by the 1,300 nm LD illumination or temperature. The results are summarized in Fig. 7e. The blue circles indicate ΔVoc recorded by changing Jsc controlled by temperature. Here, the 1,300 nm LD does not shine the device. With increasing the temperature, Jsc increases because of increasing thermal carrier excitation, and, resultantly, ΔVoc reduces. This is a well-known phenomenon. As the bandgap change in this temperature variation is ∼4.5 meV which is given by 5 × 10−4 eV K−1 of the temperature dependence of the bandgap of GaAs, the observed change in ΔVoc was almost caused by the thermal carrier excitation effect. Conversely, when the 1,300 nm LD with the excitation power density of 300 mW cm−2 illuminates the device at 290 K, ΔVoc slightly increases, despite increasing Jsc similarly. The clear difference between the thermal effect and the TPU by the second-photon flux proves the concept of the proposed TPU-SC.
Theoretical prediction of the conversion efficiency
Here, we estimate the expected conversion efficiency of the TPU-SC, using the detailed balance framework which considers a steady state between carrier generation and recombination at the optimum operation point of SC1,25. We ignore nonradiative processes in SC for predicting the ideal limit of the conversion efficiency. As shown in Fig. 2d, TPU itself occurs at the Al0.3Ga0.7As/GaAs hetero-interface, and InAs QDs play a role enhancing the TPU efficiency. Here, we neglected QD states enhancing the TPU efficiency in our calculation, and we simply assumed a perfect TPU at the hetero-interface. In this calculation, we consider that solar radiation is a black body with a temperature of 6,000 K and the temperature of the TPU-SC is 300 K. The calculation model assumes an absorptivity of 1 and good photon selectivity25. We maintained the bandgap energy (1.80 eV) of Al0.3Ga0.7As fixed and varied the CB offset (E2) and the VB offset (ΔE). The TPU of electrons occurs at the potential discontinuity of E2. Figure 8 shows the calculated results as a function of E2 at a solar concentration of 1 and 1,000 suns. Increasing the E2 with a fixed ΔE results in a decreasing E1 (see inset of Fig. 8). When E2 and ΔE are zero, the conversion efficiency coincides with that of a single-junction Al0.3Ga0.7As SC. Regardless of ΔE, the conversion efficiency increases as E2 increases because the contribution of the TPU increases, namely, the transmission loss decreases. Finally, the efficiency reaches a peak; under the one-sun irradiation, the maximum conversion efficiency is 44% at E2=0.63 eV when ΔE=0. This value coincides with the efficiency calculated for the well-known ideal IBSC5. Furthermore, under 1,000-sun irradiation, the conversion efficiency exceeds 50%, even at ΔE=0.2 eV. The E2 at which the conversion efficiency exhibits a peak shifts with varying ΔE. Increasing the ΔE leads to a monotonic decrease in the conversion efficiency, which is caused by a voltage loss at the hetero-interface. These results suggest that a zero VB discontinuity (ΔE=0) achieves maximum conversion efficiency. To reduce ΔE, the use of other material systems showing a type-II band alignment would accentuate the intrinsic nature of the TPU-SC.
Intraband transition is recognized as a very weak phenomenon that depends on the carrier density in the initial state. Here, we observed a strong TPU when using a hetero-structure that included InAs QDs. Considering the results of ΔJsc shown in Fig. 7b, we estimated the intraband absorption coefficients for the TPU at the hetero-structure. We assumed that ΔJsc and the absorption coefficient obey the following relationship that is based on the Beer–Lambert law:
where q is the elementary charge, Nin is the incident 1,300 nm photon flux, α is the absorption coefficient and d is the thickness of absorber. When calculating Nin, we considered a reflectivity of 29.8% at the SC surface. The maximum value of αd estimated from equation (1) was 9 × 10−3, depending on the 1,300 nm excitation power density. d corresponds to the thickness of the electrons gas forming around the hetero-interface. Roughly assuming that the electron gas concentrates in the InAs QDs layer, d is considered to be the InAs-QD height of 3 nm; consequently, the maximum α becomes 30,000 cm−1. This value is rather high compared to coefficients previously reported in the literature, which were in the range 400–2,000 cm−1 (refs 18,26,27). The developed TPU-SC presents extremely long-lived electrons accumulated at the hetero-interface that fill all the confinement states of the InAs QDs and wetting layer, leading to this strong intraband excitation. The additional 1,300 nm LD produces not only a dramatic increase in the photocurrent, which is two orders of magnitude greater than ever observed, but also an increase in the photovoltage. The typical illumination power density used in the experiment corresponded to approximately 17 suns. This concentration ratio is relatively low, demonstrating the efficient TPU effect, and is expected to be easily realized.
Next, we compare ΔJsc with results reported in several references. As shown in Fig. 7a, the maximum ΔJsc of our TPU-SC was 0.6 mA cm–2 at the additional 1,300 nm IR-LD power density of 320 mW cm–2. In ref. 14, two-step photon absorption in GaSb/GaAs type-II QD-IBSC has been reported, where the maximum ΔJsc obtained by irradiating additional IR light with the intensity of 750 W cm–2 was estimated ∼10 nA cm–2 at 200 K and became smaller than 1 nA cm–2 at the temperature above 250 K. In ref. 38, we reported a saturable behaviour of ΔJsc in IBSC including InAs QDs embedded in Al0.3Ga0.7As/GaAs quantum well. In that study, the maximum ΔJsc was 0.15 μA cm–2 when excited by the additional IR light with the power density of 56 mW cm–2. As the saturated ΔJsc is proportional to the IR power density, ΔJsc can be estimated to be 0.86 μA cm–2 at the IR power density of 320 mW cm–2 used in our experiment. Elborg et al. investigated the voltage dependence of extra photocurent for the GaAs/Al0.28Ga0.72As QD-IBSC23. In that literature, ΔJsc was 0.44 μA cm–2 when excited at the additional IR power density of 1,400 mW cm–2. Sellers et al.24 investigated InAs/GaAs QD-IBSC inserting GaP strain-balancing layer between each QD layer. Here, the maximum ΔJsc was 3 μA cm–2 at the additional IR power density of 300 mW cm–2. Thus, ΔJsc of our TPU-SC exceeded all the reported values by greater than two orders of magnitude.
The SC device used in this study was designed and fabricated to demonstrate a strong TPU phenomenon. However, the SC structure presented in this paper is not the final version of this device. A detailed optimized design considering the theoretical predictions shown in Fig. 8 is necessary to achieve the best performance of the TPU-SC. For example, the position of the hetero-interface becomes important. Furthermore, as the cause for TPU reduces when the electric field is strongly reduced, we need to perform detailed simulations of the band profile at the operating point in order to maintain a moderate internal electric field even at the operating point by controlling the doping profile near the hetero-interface. In any case, the obtained results suggest that the SC structure proposed in this paper has a high potential for implementation in the next-generation high-efficiency SCs.
Solar cell fabrication
The TPU-SC was fabricated on a p+-GaAs (001) substrate using solid-source molecular beam epitaxy. The detailed structure is illustrated in Fig. 9. A 150-nm-thick p-GaAs (Be: 2 × 1018 cm−3) layer was grown over a 400-nm-thick p+-GaAs (Be: 1 × 1019 cm−3) buffer layer at a substrate temperature of 550 °C. The substrate temperature was monitored during the growth using an infrared pyrometer. Subsequently, an i layer with the structure Al0.3Ga0.7As (250 nm)/GaAs (10 nm)/InAs QDs/GaAs (1,140 nm) was deposited. The nominal thickness of InAs was 0.64 nm (2.1 monolayers). The typical height and width of the QDs was 3 and 20 nm, respectively, and the QD density was approximately 1.0 × 1010 cm−3. The substrate temperature before the deposition of the InAs QDs was 550 °C. The InAs QDs and the subsequent 10-nm-thick GaAs capping layer were grown at 490 °C. The thin GaAs capping layer maintained the optical quality of the InAs QDs, even if Al0.3Ga0.7As is grown at 490 °C, which is lower than the optimum growth temperature. Finally, n+-GaAs (Si: 2.5 × 1018 cm−3), n+-Al0.3Ga0.7As (Si: 2.5 × 1017 cm−3), and n-Al0.3Ga0.7As (Si: 1 × 1017 cm−3) layers were grown on the SC structure at a substrate temperature of 500 °C. The beam-equivalent pressure of the As2 flux was 1.15 × 10−3 Pa. Then, metal Au/Au-Ge and Au/Au-Zn contacts were created on the top and the bottom surfaces, respectively. The dimensions of the SC were 4 × 4 mm2. Note that the SC structure used in this study was not optimized for obtaining a high conversion efficiency according to the theoretical work shown in Fig. 8 but was fabricated to demonstrate the fundamental TPU effects on the SC characteristics. Further development, such as the optimization of the thickness and doping concentration of each layer as well as introduction of a window layer and anti-reflection coating, is required to obtain the best performance.
EQE and ΔEQE measurement
The EQE and ΔEQE measurement was conducted at various temperatures. The excitation light was produced by a tungsten halogen lamp, passed through a 140 mm single monochromator, and chopped by an optical chopper with a frequency of 800 Hz. The excitation power density depended on the wavelength and the integrated power density was approximately 2 mW cm−2, much lower than that of the 1 sun solar irradiance of 100 mW cm−2. The beam diameter of the monochromatic light was 1.2 mm on the SC surface. The photocurrent was detected by a lock-in amplifier synchronized with the optical chopper. The photocurrent was measured under short-circuit conditions without external bias voltage. Here, the EQE was defined as the efficiency of the photocurrent generation under monochromatic excitation, namely, the number of electrons collected as the photocurrent normalized by the incident photon flux at each wavelength. The TPU was demonstrated by measuring the change in the EQE signal amplitude under two-colour excitation using two types of light sources. The first interband-excitation light source was a monochromated tungsten halogen lamp. The second intraband light source was a continuous-wave LD with the 1,300 nm emission, which was used for pumping electrons accumulated at the Al0.3Ga0.7As/GaAs interface into the Al0.3Ga0.7As barrier. The 1,300 nm LD wavelength was sufficiently long to prevent interband transitions. The beam diameter of the 1,300 nm LD was 1.2 mm on the SC surface. The excitation power density of the 1,300 nm LD was 360 mW cm−2. ΔEQE was defined as the difference between the EQE obtained with and without the 1,300 nm LD illumination.
In this measurement, we used two LDs. The first interband excitation was obtained using a 780 nm LD; the 780 nm photons traversed Al0.3Ga0.7As and directly excited the i-GaAs layer. The second intraband-excitation light source was a 1,300 nm LD. Both excitation sources operated in the continuous-wave mode. The excitation density was varied by using a reflective neutral density filter. The beam diameter of the both LD was 1.2 mm on the SC surface. When the bias voltage was applied on the SC, the photocurrent was obtained using a Keithley 2400 source meter. The measurements were performed at 297 K without a temperature controller.
Modelling of ΔJsc and ΔVoc
Generally, the short-circuit current has a linear relationship with the excitation density. However, as described in the Results section, ΔJsc exhibited a clear sub-linear response to the excitation density; this is because dense space charge accumulated at the hetero-interface weakens the electric field and the carrier collection efficiency of the TPU decreases. Therefore, we modified equation (1) as follows to interpret the results phenomenologically:
where n is a fitting parameter. The result of the reverse-bias-voltage dependence of the evaluated n value shown in Fig. 7d indicates that our hypothesis is realistic.
On the other hand, when modelling ΔVoc, we used the equation describing the Voc of a single-junction SC:
where kB is the Boltzmann constant, T is the temperature, and J0 is the saturation current. For two-colour photo-excitation measurements, Voc can be divided into Voc,single and ΔVoc, where Voc,single is the open-circuit voltage at the single-colour excitation. Likewise, Jsc can be divided into Jsc,single and ΔJsc, where Jsc,single is the short-circuit current at the single-colour excitation. By substituting Voc and Jsc with Voc,single + ΔVoc and Jsc,single +ΔJsc, ΔVoc is written as
Equation (4) was used to fit the results of Fig. 7b,c.
The data that support the findings of this study are available from the corresponding author upon request.
How to cite this article: Asahi, S. et al. Two-step photon up-conversion solar cells. Nat. Commun. 8, 14962 doi: 10.1038/ncomms14962 (2017).
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Shockley, W. & Queisser, H. J. Detailed balance limit of efficiency of p-n junction solar cells. J. Appl. Phys. 32, 510–519 (1961).
Hirst, L. C. & Ekins-Daukes, N. J. Fundamental losses in solar cells. Prog. Photovolt. Res. Appl. 19, 286–293 (2011).
De Vos, A. Detailed balance limit of the efficiency of tandem solar cells. J. Phys. D Appl. Phys. 13, 839–846 (1980).
Henry, C. H. Limiting efficiencies of ideal single and multiple energy gap terrestrial solar cells. J. Appl. Phys. 51, 4494–4500 (1980).
Luque, A. & Martí, A. Increasing the efficiency of ideal solar cells by photon induced transitions at intermediate levels. Phys. Rev. Lett. 78, 5014–5017 (1997).
Okada, Y. et al. Intermediate band solar cells: recent progress and future directions. Appl. Phys. Rev. 2, 021302 (2015).
Ross, R. T. & Nozik, A. J. Efficiency of hot-carrier solar energy converters. J. Appl. Phys. 53, 3813–3818 (1982).
Hirst, L. C., Walters, R. J., Führer, M. F. & Ekins-Daukes, N. J. Experimental demonstration of hot-carrier photo-current in an InGaAs quantum well solar cell. Appl. Phys. Lett. 104, 231115 (2014).
Farrell, D. J., Sodabanlu, H., Wang, Y., Sugiyama, M. & Okada, Y. A hot-electron thermophotonic solar cell demonstrated by thermal up-conversion of sub-bandgap photons. Nat. Commun. 6, 8685 (2015).
Huang, S., Semichaevsky, A. V., Webster, L., Johnson, H. T. & Goldman, R. S. Influence of wetting layers and quantum dot size distribution on intermediate band formation in InAs/GaAs superlattices. J. Appl. Phys. 110, 073105 (2011).
Gioannini, M., Cédola, A. P., Santo, N. D., Bertazzi, F. & Cappelluti, F. Simulation of quantum dot solar cells including carrier intersubband dynamics and transport. IEEE J. Photovolt. 3, 1271–1278 (2013).
Creti, A. et al. Role of charge separation on two-step two photon absorption in InAs/GaAs quantum dot intermediate band solar cells. Appl. Phys. Lett. 108, 063901 (2016).
Varghese, A. et al. Complete voltage recovery in quantum dot solar cells due to suppression of electron capture. Nanoscale 8, 7248–7256 (2016).
Hwang, J. et al. Multiphoton sub-band-gap photoconductivity and critical transition temperature in type-II GaSb quantum-dot intermediate-band solar cells. Phys. Rev. Appl. 1, 051003 (2014).
Okada, Y. et al. Increase in photocurrent by optical transitions via intermediate quantum states in direct-doped InAs/GaNAs strain-compensated quantum dot solar cell. J. Appl. Phys. 109, 024301 (2011).
Martí, A. et al. Production of photocurrent due to intermediate-to-conduction-band transitions: a demonstration of a key operating principle of the intermediate-band solar cell. Phys. Rev. Lett. 97, 247701 (2006).
Kita, T., Maeda, T. & Harada, Y. Carrier dynamics of the intermediate state in InAs/GaAs quantum dots coupled in a photonic cavity under two-photon excitation. Phys. Rev. B 86, 035301 (2012).
Harada, Y., Maeda, T. & Kita, T. Intraband carrier dynamics in InAs/GaAs quantum dots stimulated by bound-to-continuum excitation. J. Appl. Phys. 113, 223511 (2013).
Martí, A., Cuadra, L. & Luque, A. in Conference Record of the 28th IEEE Photovoltaic Specialists Conference 940–943IEEE (2000).
López, N., Reichertz, L. A., Yu, K. M., Campman, K. & Walukiewicz, W. Engineering the electronic band structure for multiband solar cells. Phys. Rev. Lett. 106, 028701 (2011).
Asahi, S. et al. Suppression of thermal carrier escape and efficient photo-carrier generation by two-step photon absorption in InAs quantum dot intermediate-band solar cells using a dot- in-well structure. J. Appl. Phys. 116, 063510 (2014).
Tamaki, R., Shoji, Y., Okada, Y. & Miyano, K. Spectrally resolved intraband transitions on two-step photon absorption in InGaAs/GaAs quantum dot solar cell. Appl. Phys. Lett. 105, 073118 (2014).
Elborg, M. et al. Voltage dependence of two-step photocurrent generation in quantum dot intermediate band solar cells. Solar Energy Mater. Solar Cells 134, 108–113 (2015).
Sellers, D. G., Polly, S., Hubbard, S. M. & Doty, M. F. Analyzing carrier escape mechanisms in InAs/GaAs quantum dot p-i-n junction photovoltaic cells. Appl. Phys. Lett. 104, 223903 (2014).
Yoshida, M., Ekins-Daukes, N. J., Farrell, D. J. & Phillips, C. C. Photon ratchet intermediate band solar cells. Appl. Phys. Lett. 100, 263902 (2012).
Luque, A. et al. Absorption coefficient for the intraband transitions in quantum dot materials. Prog. Photovolt: Res. Appl. 21, 658–667 (2013).
Mehdipour, A., Sasaoka, K., Ogawa, M. & Souma, S. Proposal of simplified model for absorption coefficients in quantum dot array based intermediate band solar cell structure. IEICE Electron. Exp. 11, 1–11 (2014).
Driessen, F. A. J. M. High-efficiency energy up-conversion at GaAs-GaInP2 interfaces. Appl. Phys. Lett. 67, 2813–2815 (1995).
Yamashita, K., Kita, & Nishino, T. Carrier localization effects in energy up conversion at ordered (Al0.5Ga0.5)0.5In0.5P/GaAs heterointerface. J. Appl. Phys. 84, 359–363 (1998).
Kita, T., Nishino, T., Geng, C., Scholz, F. & Schweizer, H. Dynamic process of anti-stokes photoluminescence at a long-range-ordered Ga0.5In0.5P / GaAs heterointerface. Phys. Rev. B 59, 15358–15362 (1999).
Yamashita, K., Kita, T., Nishino, T. & Oestreich, M. Carrier-relaxation process in time-resolved up-converted photoluminescence at ordered (Al0.5Ga0.5)0.5In0.5P and GaAs heterointerface. Jpn J. Appl. Phys. 38, 1001–1003 (1999).
Kita, T., Nishino, T., Geng, C., Scholz, F. & Schweizer, H. Time-resolved observation of anti-stokes photoluminescence at ordered Ga0.5In0.5P and GaAs interfaces. J. Lumin. 87-89, 269–271 (2000).
Kojima, O., Okumura, S., Kita, T. & Akahane, K. Effect of exciton oscillator strength on upconversion photoluminescence in GaAs/AlAs multiple quantum wells. Appl. Phys. Lett. 105, 181901 (2014).
Hylton, N. P. et al. Photoluminescence upconversion at GaAs/InGaP2 interfaces driven by a sequential two-photon absorption mechanism. Phys. Rev. B 93, 235303 (2016).
Sellers, D. G. et al. New nanostructured materials for efficient photon upconversion. IEEE J. Photovolt. 5, 224–228 (2015).
Sellers, D. G. et al. Novel nanostructures for efficient photon upconversion and high-efficiency photovoltaics. Solar Energy Mater. Solar Cells 155, 446–453 (2016).
Wang, Y. et al. Band offset of GaAs/AlxGa1−xAs heterojunctions from atomistic first principles. Appl. Phys. Lett. 102, 132109 (2013).
Asahi, S. et al. Saturable Two-step photocurrent generation in intermediate-band solar cells including InAs quantum dots embedded in Al0.3Ga0.7As/GaAs quantum wells. IEEE J. Photovolt. 6, 465–472 (2016).
Plá, J., Barrera, M. & Rubinelli, F. The influence of the InGaP window layer on the optical and electrical performance of GaAs solar cells. Semicond. Sci. Technol. 22, 1122–1130 (2007).
Kada, T. et al. Two-step photon absorption in InAs/GaAs quantum-dot superlattice solar cells. Phys. Rev. B 91, 201303 (2015).
Yang, X.-F., Chen, X.-S., Lu, W. & Fu, Y. Effects of shape and strain distribution of quantum dots on optical transition in the quantum dot infrared photodetectors. Nanoscale Res. Lett. 3, 534–539 (2008).
Harrison, P. in Quantum Wells, Wires and Dots 3 edn, 328–334John Wiley & Sons (2005).
Bimberg, D., Grundmann, M. & Ledentsov, N. N. Inter-sublevel transitions. In Quantum Dot Heterostructures 154–155John Wiley & Sons (1999).
This work was partially supported by the Incorporated Administrative Agency New Energy and Industrial Technology Development Organization (NEDO) and the Japan Society for the Promotion of Science (JSPS) KAKENHI Grant Number JP15K13953. One of the authors (T. Kita) thanks Prof. Masakazu Sugiyama of the University of Tokyo for fruitful discussions.
The authors declare no competing financial interests.
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Asahi, S., Teranishi, H., Kusaki, K. et al. Two-step photon up-conversion solar cells. Nat Commun 8, 14962 (2017) doi:10.1038/ncomms14962
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