Semiconductor sensitized solar cells (SSCs) are promising as one of the next generation photovoltaics (PVs) due to the attractive optoelectronic properties of semiconductor light harvesters. In addition to the high absorption coefficient, bandgap and band edge positions can be tuned by the quantum confinement effect and composition1,2,3,4,5,6. There is also the possibility of multiple exciton generation, which may lead to the PVs overcoming Shockley-Queisser limit7,8,9. Two main approaches exist for assembling light-harvesting semiconductor sensitizers on mesoporous metal oxide electrodes such as TiO2 (mp-TiO2). One approach is the in situ route, where the semiconductor sensitizers are grown directly on the surface of mp-TiO2 electrodes10,11. Successive ionic layer adsorption and reaction (SILAR) and chemical bath deposition (CBD) are typical methods belonging to this category12,13,14,15. The in situ route benefits from the intimate contact between the sensitizer and the TiO2, but often suffers from the complication of sensitizer size/shape control and relatively poor crystallinity of the assembled sensitizers16,17. On the other hand, in the ex situ route, semiconductor sensitizers are synthesized prior to the assembly onto the mp-TiO2 electrode and sensitization is carried out thereafter via direct adsorption, linker-assisted adsorption, electrophoretic deposition (EPD), or similar approaches18,19,20,21. In the ex situ assembly route, pre-synthesized sensitizers bear insulating ligand molecules on their surfaces, making the contact between the sensitizers and the mp-TiO2 electrode less intimate22,23. However, SSCs derived from an ex situ assembly route can benefit from high-quality sensitizers with well-defined size/shape and high crystallinity and over 8% certified power conversion efficiency (PCE) has been achieved recently with quantum dots (QDs)24,25.

Despite the versatility of the ex situ assembly route allowing separately prepared sensitizers with various shapes, sizes and compositions, most efforts have been focused solely on the 0-D semiconductor QDs as sensitizer materials18,19,20,21,22,23,24,25. One-dimensional nanorods have been known to have fascinating optoelectronic properties different from QDs, which are potentially conducive to realizing better-performance SSCs. Compared to the QDs in which photogenerated electron-hole pairs are strongly bound by electrostatic forces26, 1-D nanorods are expected to have weaker binding for the electron-hole pairs in their elongated structure27. This implies that the electron-hole recombination, one of the major factors deteriorating the performance of SSCs, will be less significant in the 1-D sensitizers than QDs. Therefore, 1-D nanorods can be a decent alternative or complement for the conventional SSCs utilizing QD sensitizers. However, 1-D nanostructures and their multi-composition variants have been given only a limited attention in this field up to now28,29. This is because of two major complications of integrating those nanostructures into SSCs: one is the difficulty of synthesizing well-defined 1-D sensitizer itself with proper composition and nanoscale morphology guaranteeing the optimal photovoltaic performance and the other is the spatial incompatibility of the long 1-D sensitizers with the conventionally available nanoporous photoelectrodes derived from metal-oxide nanoparticles, by which the full penetration of 1-D sensitizers through the photoelectrode is impeded. Various strategies to improve PCE are also remaining unexplored in the case of 1-D nanostructure-sensitized PVs, such as ligand-exchange, transition-metal doping, formation of core-shell structures and other surface-passivation technologies30,31,32,33.

Herein, we report for the first time the CdSe/CdSexTe1−x type-II heterojunction nanorods (HNRs) as light harvesting sensitizers for SSCs. About 33% enhancement of the PCE is achieved using HNRs compared to the PCE using CdSe nanorods (NRs), which can be attributed to the inherent efficient charge separation across the type-II heterointerface and favorable effects of 1-octanethiol (OT) surface ligands on the TiO2-HNR interfacial charge transfer. Furthermore, to circumvent the spatial incompatibility of long 1-D sensitizers with conventional mp-TiO2 electrodes, polystyrene (PS) microbeads are added as sacrificial additives to render large percolating pores in the mp-TiO2 and thereby facilitate the infiltration of HNRs throughout the entire electrode depth. The CdSe/CdSexTe1−x HNR-SSC with pore-engineered electrode is shown to reach 3.02% PCE, which is one of the highest values among SSCs using the 1-D sensitizers.


Optical Properties of NRs and HNRs

Absorption and photoluminescence (PL) spectra of NRs and HNRs used in this study are shown in Fig. 1. Each sample is synthesized from CdSe NR seeds, with the second components grown at the tips. TEM images of NRs and HNRs are presented in Fig. 2, showing that HNRs synthesized from ~15 nm long CdSe NR seeds are ~25 nm long in average. The absorption spectrum for CdSe-only NRs shows a peak near 600 nm with a sharp PL peak at 615 nm. When CdTe is introduced as the second component, an absorption shoulder appears at 650 nm due to the smaller bandgap of CdTe. The absorption tail extends beyond 700 nm as a result of the charge transfer transition from the CdTe valence band to the CdSe conduction band. Recombination across the CdSe/CdTe interface occurs at energies lower than the bandgap of either component, shifting the PL peak to ~800 nm and broadening it considerably. Alloyed CdSe0.4Te0.6 also forms a type-II junction with CdSe, therefore many of the absorption and PL features for these HNRs are similar. The difference between the PL peak position of the HNRs and that of the CdSe seeds, measured to be 0.37 eV, was used to determine the concentration of Te in the alloy following the calibration introduced in our previous work34,35. The CdSe/CdSe0.4Te0.6 HNRs recapped with 1-octanethiol retain the absorption features seen with the native ligands, but have higher PL intensity and better stability in air, similar to the 1-octanethiol capped CdSe/CdTe HNRs we reported recently36. For every heterostructured sample, the absorption spectrum extends beyond 700 nm and should allow a greater portion of the incident solar spectrum to be collected in a photovoltaic device compared to single-component CdSe.

Figure 1
figure 1

(a) Absorption and photoluminescence (PL) spectra of CdSe NRs, CdSe/CdTe HNRs and CdSe/CdSe0.4Te0.6 HNRs with both native ligands (TOPO) and 1-octanethiol ligands (OT). The PL spectra for CdSe NRs and 1-octanethiol-capped CdSe/CdSe0.4Te0.6 HNRs are normalized to the absorbance at the CdSe first exciton peak. The PL spectra for native ligand capped CdSe/CdSe0.4Te0.6 and CdSe/CdTe HNRs are normalized to the absorbance at the excitation then scaled relative to the PL spectrum of the 1-octanethiol capped CdSe/CdSe0.4Te0.6 HNRs. (b) Schematic illustration of different 1-D sensitizers and energy-level diagram of each component consisting of type-II HNRs based on previous reports34,35.

Figure 2
figure 2

Transmission electron micrographs of (a) the seed CdSe NRs, (b) TOPO-CdSe NRs, (c) TOPO-CdSe/CdTe HNRs, (d) TOPO-CdSe/CdSe0.4Te0.6 HNRs, (e) OT-CdSe/CdSe0.4Te0.6 HNRs and (f) OT-CdSe/CdSe0.4Te0.6 HNRs anchored to the TiO2 nanoparticles.

Photovoltaic Properties of NR- and HNR-Sensitized PV Devices

Photocurrent-voltage (J-V) characteristics, absorbance spectra of sensitized films, incident photon-to-current efficiency (IPCE) and absorbed photon-to-current efficiency (APCE) spectra for various NR- and HNR-sensitized PV devices are presented in Fig. 3. Photovoltaic parameters of the devices are given in Table 1. Every device exhibits similar open-circuit voltages (Voc) and fill factors (FF), but short-circuit current density (Jsc) values show remarkable differences. As the time constant of the electron transfer from CdTe (or CdSe0.4Te0.6) tips to CdSe in HNRs (<400 fs) is much shorter than that of the electron transfer from CdTe to TiO2 (~1 ns)34,36,37, we believe that most of the photocurrent would come from the electron transfer at the CdSe-TiO2 interface (for CdSe NRs and HNRs). If a major portion of HNRs are anchored to TiO2 only by their tips, electron extraction at the CdTe/TiO2 interface should compete with more efficient electron transfer to CdSe. Moreover, electron transfer from CdSe to CdTe is not favored considering the band diagram in Fig. 1b, leading to poor fill factor as we previously reported in the case of organic-inorganic hybrid solar-cell structure utilizing curved CdSe/CdTe HNRs as inorganic light harvesters38. Such a loss of fill factor was not observed in HNR-sensitized PV devices and therefore we believe that most of HNRs incorporated in the mp-TiO2 frame have some portion of CdSe directly anchored to the TiO2 nanoparticles. The TEM images of HNRs anchored on mp-TiO2 in Fig. 2f partially support this argument.

Table 1 Photovoltaic parameters of nanorod (NR)- and heterojunction nanorod (HNR)- sensitized solar cells with different sensitizer structures, compositions and surface ligands.
Figure 3
figure 3

(a) Photocurrent-voltage curves (averaged line from two sets of samples prepared in parallel), (b) absorption spectra of the sensitized films, (c) incident photon-to-current conversion efficiency (IPCE) and (d) absorbed photon-to-current conversion efficiency (APCE) of NR- and HNR-sensitized solar cells with different sensitizer structures, compositions and surface ligands (native ligands (TOPO) or 1-octanethiol (OT)).

The TOPO-CdSe/CdTe HNR device delivers slightly higher Jsc compared to the TOPO-CdSe device. Considering that the photocurrent generated from single-component CdTe sensitizers is generally far lower than the single-component CdSe sensitizers presumably due to the recombination loss from the charge-carrier trapping38,39,40,41, higher Jsc of the TOPO-CdSe/CdTe HNRs than that of the TOPO-CdSe NRs (with the same dimension of ~25 nm) cannot be explained simply by summing up the photocurrent generated from individual CdSe and CdTe components in HNRs. Due to the unique feature of type-II band offset in HNRs, where photoexcited electron-hole pairs are innately separated, the electron extraction process at the TiO2-sensitizer interface becomes more efficient with HNRs than with the single-component NRs39. This explains the increase of IPCE over the entire wavelength region for the TOPO-CdSe/CdTe HNR-SSCs compared to the case of TOPO-CdSe single-component NRs working as light harvesters. Furthermore, the type-II interface of TOPO-CdSe/CdTe HNR leads to a charge-separated state (CSS) absorption39, enabling the utilization of less energetic photons close to the near-infrared region. The effect of CSS absorption inherent for the HNR sensitizers is reflected in the extended absorption tail of the sensitized films (Fig. 3b) compared to that of the TOPO-CdSe NR device.

In terms of the performance of TOPO-CdSe/CdTe HNR device, the stability of CdTe component in polysulfide electrolyte is a major concern and therefore should be discussed. It has been well known that in the case of CdTe-sensitized SSCs using polysulfide electrolyte, anodic corrosion due to the ineffective hole scavenging from CdTe leads to the degradation of CdTe and low photovoltaic performance42,43. This degradation can be lessened by forming a semiconductor shell preventing CdTe cores from directly facing the polysulfide electrolyte25. Even though the CdTe component of the CdSe/CdTe HNRs does not have such a core-shell structure, our devices are finally treated to have ZnS passivation layer and therefore CdSe/CdTe HNR devices are not much affected by the anodic corrosion and exhibit reasonable performance.

In the case of TOPO-CdSe/CdSe0.4Te0.6 HNR device, ~11% extra enhancement of Jsc compared to that of the TOPO-CdSe/CdTe NR device is observed. CdSe/CdSe0.4Te0.6 HNRs allow faster charge separation compared to the CdSe/CdTe HNRs and have lower valence band position in the alloyed tip34, which might lead to the Jsc improvement by aiding facile charge extraction to TiO2. Furthermore, in the case of HNRs with alloyed tips, enhanced chemical stability of alloyed tips is also thought to contribute to achieve the improved photocurrent39.

A noticeable further enhancement in the photocurrent density is observed by exchanging the surface ligands on the CdSe/CdSe0.4Te0.6 HNRs, from native TOPO, ODPA and TOP (simply referred to here as TOPO) ligands to 1-octanethiol (OT). As the absorption spectra obtained from mp-TiO2 films sensitized with TOPO-CdSe/CdSe0.4Te0.6 and OT-CdSe/CdSe0.4Te0.6 are quite similar (Fig. 3b), the Jsc upsurge may be attributed to the enhancement of electron injection/collection efficiency rather than the difference in the light harvesting from both sensitizers. Such an interpretation is further supported by the trend shown in the APCE spectra (Fig. 3d): APCE is represented as the product of charge collection efficiency (ηcol) and charge injection efficiency (ηinj), which can be calculated from the following relation (equation (1))44:

where the term LHE represents light harvesting efficiency. By comparing Fig. 3c,d, it is found that the APCE onset of the OT-CdSe/CdSe0.4Te0.6 device is extended to ~760 nm compared to that of the TOPO-capped HNR devices. This result is in line with the previous report of the photocurrent spectra extended over ~700 nm for the 1-octanethiol capped CdSe/CdTe HNRs36. Moreover, the difference of IPCE among the TOPO-capped sensitizer devices almost vanishes from the ~580-nm wavelength in the APCE spectra, showing that the charge collection and injection efficiency of the TOPO-capped samples are quite similar in this wavelength region. However, APCE near ~480 nm corresponding to the X2 excitonic band of CdSe still shows composition dependence, which we might attribute to the aforementioned effect from the faster charge-separation kinetics of type-II band offset and higher photocurrent obtainable from alloyed tips than CdTe tips. However, clear interpretation for this phenomenon is not established yet and further study is needed.

It is readily deduced that ηcol can be improved from the 1-octanethiol capping, as it has been well known that the thiol recapping of CdTe reduces the surface defect sites responsible for any unwanted recombination of photo-generated charge carriers36,40,41. This feature is also found in Fig. 1a showing higher PL intensity of OT-CdSe/CdSe0.4Te0.6 than TOPO-CdSe/CdSe0.4Te0.6, which is presumably resulted from the suppressed recombination by 1-octanethiol capping. Improvement of carrier collection from enhanced electric-field throughout the HNR absorber layer is another possible factor leading to the improved Jsc, but it may hardly be the case in our devices considering photocurrent saturation under the reverse-biased condition in the J-V curve (Fig. 3a) and our sensitized solar cell structure utilizing monolayer HNRs as light absorber layer45.

However, the difference of ηinj from 1-octanethiol recapping is not self-evident and further investigation on the TiO2-OT-HNR interface is needed. To elucidate the interface properties, electrochemical impedance spectroscopy (EIS) was carried out46,47. The mp-TiO2 electrodes sensitized with TOPO-capped CdSe/CdSe0.4Te0.6 HNR and OT-capped CdSe/CdSe0.4Te0.6 HNR sensitizers were chosen for the EIS measurement, to examine the capping ligand effect by excluding any side effects from the HNR composition and different loading amount of HNRs on mp-TiO2 electrodes. Figure 4 presents the chemical capacitance (Cμ) and recombination resistance (Rrec) extracted from the measured impedance spectra for both electrodes, exhibiting that the electrode sensitized with OT-CdSe/CdSe0.4Te0.6 HNR shows higher chemical capacitance in the measured voltage range and higher recombination resistance in average. Higher chemical capacitance is generally interpreted as evidence for the downshift of the TiO2 conduction-band minimum (CBM)48,49. However, in our case, we believe it is the upshift of the CdSe CBM of CdSe/CdSe0.4Te0.6 HNR with OT, as reported for CdSe nanocrystals50,51, that may be responsible for the increased chemical capacitance. Furthermore, TiO2 in both devices have been treated with 3-MPA and therefore the effects of 3-MPA on the CBM of TiO2 is not likely to be very different. Whether it is the downshift of the TiO2 CBM or the upshift of the CdSe CBM, both cases lead to a larger offset between TiO2 CBM and CdSe CBM of CdSe/CdSe0.4Te0.6 HNR. From the many-state Marcus model describing the electron transfer rate at the metal-oxide and semiconductor-nanoparticle interface52, faster electron injection is predicted for this case as the CBM offset serves as the driving force for the electron transfer at the TiO2-CdSe interface53,54,55. Less energetic electrons generated in the HNRs may become extractable by this larger injection driving force, which also explains the origin of red-shifted APCE onset for the OT-CdSe/CdSe0.4Te0.6 device. The higher recombination resistance is believed to result from the reduced recombination by thiol-capping, as explained in the previous section.

Figure 4
figure 4

(a) Chemical capacitance (Cμ) and (b) recombination resistance (Rrec) of TiO2 photoelectrodes sensitized with CdSe/CdSe0.4Te0.6 HNRs having different passivation ligands, measured by electrochemical impedance spectroscopy (EIS) under dark conditions. Each point is the average value from two sets of samples prepared in parallel.

Therefore, it is concluded that both ηcol and ηinj (equation (1)) are improved through the 1-octanethiol recapping and the Jsc increase from the OT-CdSe/CdSe0.4Te0.6 device with the red-shifted IPCE onset compared to the TOPO-CdSe/CdSe0.4Te0.6 can happen without remarkable increase of the light absorption. The OT-CdSe/CdSe0.4Te0.6 HNR-SSC shows Jsc of 6.238 ± 0.212 mA cm−2 with 2.202 ± 0.131 overall PCE, approximately 33% improvement over the single-component CdSe NR devices with native ligands.

The Effect of Polystyrene Bead-Induced Percolating Pores on the PV Performance

Even though the power conversion efficiency of the HNR device is much enhanced by utilizing both the type-II HNR sensitizers and ligand exchange, utilization of such 1-D long nanostructures as light harvesters for SSCs is still limited by their spatial incompatibility with the TiO2 nanoparticle-based porous photoelectrodes. This type of electrode commonly provides ~20-nm sized pores (BET scale)56, which is smaller than the length of these 1-D nanostructures (~25 nm long). However, strategies to circumvent such limitations have been investigated only by a few researchers28,57.

To render the internal pore structures of mp-TiO2 electrode more suitable for the infiltration of 1-D sensitizers, we utilized polystyrene (PS) microbeads as sacrificial additives for the conventional TiO2 paste. Figures 5 and 6b show cross-sectional SEM images and EDS profiles of mp-TiO2 electrodes derived from the pastes of different TiO2:PS weight ratios. For the electrode without PS beads, Cd/Ti ratio is not homogeneous throughout the electrode cross-section and abruptly decreases at the ~2-μm depth, suggesting that ~20-nm sized pores in mp-TiO2 electrodes are easily clogged by the NR or HNR sensitizers. However, when the PS beads are incorporated into the TiO2 pastes and calcined to leave large pores (Fig. 7a), the Cd/Ti ratio at every given depth of the electrode cross-section is highly increased and the distribution of Cd/Ti values becomes much more homogeneous throughout the entire electrode depth.

Figure 5
figure 5

Cross-sectional SEM images of mp-TiO2 electrodes derived from the pastes with various PS contents.

Figure 6
figure 6

(a) Photocurrent-voltage curves (averaged line from two sets of samples prepared in parallel, except for the curve of champion cell) and (b) Cd/Ti atomic ratio determined by cross-sectional EDS of OT-CdSe/CdSe0.4Te0.6 HNR-sensitized electrodes derived from the pastes of various PS contents.

Figure 7
figure 7

(a) Schematic illustration for the formation of percolating large pore channels in mp-TiO2 electrode. (b,c) Monte-Carlo simulation results. (b) Differential surface area at the given depth in 8 × 8 × 8 μm3 sized continuous cube, calculated from the percolated pores (200 nm in diameter). Each line is averaged from 4 different simulations. (c) Visual illustration of typical simulation results for different contents of spherical pores, showing the percolated 200-nm spheres.

Figure 6a shows the J-V characteristics of HNR devices with different TiO2 to PS ratios, the photovoltaic parameters of which are presented in Table 2. Incorporation of PS beads leads to a significant increase in both Jsc and PCE. From these results, we presume that the incorporation of PS beads leads to a more open pore structures, possibly by the percolation of beads to yield large pore channels through which infiltration of HNRs is facilitated. To support this idea, a Monte-Carlo simulation was conducted: 200-nm sized spheres representing PS beads are randomly distributed in an 8 × 8 × 8 μm3 space and the condition of the bead-to-bead percolation allowing the passage of NRHs through the pores induced from adjoining PS beads was estimated from the average length of HNRs (including the capping ligands) and average diameter of TiO2 (P25) nanoparticles. The Monte-Carlo simulation results are presented for various volume fraction of PS beads: Fig. 7b exhibits the differential value of internal surface area (dS/dz) along the depth direction, while Fig. 7c shows 3-D construction of typical simulation results, revealing the percolated 200-nm spheres in the simulation volume.

Table 2 Photovoltaic parameters of 1-octanethiol (OT) capped CdSe/CdSe0.4Te0.6 HNR-sensitized solar cells with mesoporous-TiO2 (mp-TiO2) electrodes derived from the pastes with various polystyrene (PS) microbead contents.

It is predicted that with ~32.5% volumetric occupation of 200-nm sized PS beads in the TiO2 nanoparticle electrode, percolation of beads extends throughout the entire electrode depth (8 μm). Assuming the porosity of mp-TiO2 films to be in the range of 0.5–0.656, the PS beads account for the 27.5–32.1% of the total volume in the electrodes with TiO2:PS = 4:1 after calcination, which is close to 32.5%. Therefore, the homogeneous Cd/Ti ratio throughout the electrode depth and the improvement of PV performances from the PS-derived hierarchically porous TiO2 electrodes can be explained by the percolation of large pores and subsequently facilitated infiltration of HNRs. Furthermore, dS/dz values increase even further after the formation of electrode-penetrating percolation channel, as seen in Fig. 7b, meaning that the infiltration of HNRs would be more promoted by the addition of more PS beads. Therefore, the Cd/Ti ratio exhibits a further increase for the TiO2:PS = 2:1 electrode and the optimal PV performance is obtained at this ratio. We also believe that this strategy can benefit from the Mie-type light-scattering effects produced by spherical pores filled with electrolytes, as previously explored theoretically (in the case of dye-sensitized solar cells) and experimentally58,59. However, with a larger amount of PS beads the electrode structure collapses from the aggregation of PS beads forming large voids (Fig. 5d), leading to inferior Jsc and FF due to the loss of active mp-TiO2 volume to accommodate HNRs and deteriorated recombination at the direct electrolyte-FTO contact.

Our simple approach utilizing sacrificial spherical additives results in ~34% additional enhancement in Jsc compared to the OT-CdSe/CdSe0.4Te0.6 HNR-SSC from the mp-TiO2 electrode without polystyrene microbead-induced percolating pores, yielding a 3.02% efficient PV device. This is one of the highest values among the SSCs with 1-D sensitizers and a promising result proving that multi-composition variants of 1-D nanostructures can be fully utilized for this type of photovoltaic device with sensible engineering.


In this work, CdSe/CdSexTe1−x HNRs were effectively utilized as a light absorber material for semiconductor-sensitized solar cells. Tailored nano-heterostructures and surface passivation with suitable ligand proved to be crucial factors to achieve the enhanced photocurrent density, by utilizing the superior optoelectronic properties of type-II heterostructures and modifying the conduction band level with surface ligands. Furthermore, to circumvent the spatial incompatibility of 1-D sensitizers with the conventional mp-TiO2 electrodes, spherical PS bead additives were incorporated to render a hierarchical pore structure in the mp-TiO2 electrode. Electrodes with PS-modified pore structures showed highly enhanced PV performance by the formation of large percolating pores inside the electrode, which was also supported by a Monte-Carlo simulation. Consequently, 3.02% efficient HNR-SSC was achieved by integrating the aforementioned approaches, exhibiting that 1- or higher-dimensional nanostructures and their multi-composition variants can potentially be fascinating alternatives as light harvesters for sensitized PVs.


Nanorod Synthesis and Recapping

Trioctylphosphine oxide (TOPO) (90%), trioctylphosphine (TOP) (90%), 1-octanethiol (98.5%), CdO (99.5%), Se powder (99.99%), Te powder (99.997%) and anhydrous toluene were obtained from Sigma-Aldrich. N-octadecylphosphonic acid (ODPA) was obtained from PCI Synthesis. ACS grade chloroform, hexanes and methanol were obtained from Fisher Scientific. All chemicals were used as received. CdSe NRs, CdSe/CdTe HNRs and CdSe/CdSexTe1−x HNRs were synthesized following our previous work with minor differences34. In brief, 0.19 g CdO, 1 g ODPA and 3 g TOPO were added to a 3-neck round-bottom flask and degassed at 150 °C, then heated and stirred at 350 °C for 2 h under argon atmosphere to form the Cd-ODPA complex. The reaction mixture was then cooled to 150 °C and degassed for 10 min. Precursor solutions of 1 M TOP-Se and 1 M TOP-Te were prepared separately in an N2-filled glovebox by dissolving elemental Se or Te powder in TOP. Injection solutions were made by diluting the concentrated precursors to the appropriate concentrations with TOP and 3 mL of 0.33 M TOP-Se was swiftly injected at 320 °C, quenching the reaction mixture to 260 °C. The growth of CdSe nanorods continued for 15 min. Then, the temperature was decreased to 250 °C and 2 mL of the second component was added dropwise over 15 min. Solutions of 0.5 M TOP-Se, 0.25 M TOP-Te and 0.1 M TOP-Te mixed with 0.4 M TOP-Se were used to make CdSe NRs, CdSe/CdTe HNRs and CdSe/CdSexTe1−x HNRs, respectively. Approximately 2/3 of the Cd in the solution was consumed during the growth of seeds, limiting the average overall length of the HNRs to ~25 nm. After 5 additional minutes of growth, the reaction mixture was cooled by removing the heating mantle. The NR/HNR suspensions were cleaned once by precipitation with chloroform and methanol and redissolved in hexanes. Any insoluble precipitates were discarded and the NR/HNRs were precipitated again by the addition of chloroform and methanol, dissolved in anhydrous toluene and stored under N2. Recapping with 1-octanethiol followed our previous work on the CdSe/CdTe HNRs36. Briefly, 12 mL of 1-octanethiol was added to the flask containing approximately 4 mL of reaction mixture under Ar atmosphere. The reaction vessel was heated to 110 °C and allowed to cool slowly to 60 °C. After stirring overnight, the HNRs were purified and stored as above.

Preparation of Polystyrene Microbead-Incorporated TiO2 Pastes

Polystyrene (PS) microbead-incorporated TiO2 nanoparticle pastes were prepared with P25 nanoparticles (Degussa), ethyl cellulose (EC) as binder and terpineol as solvent60. First, 3 g of P25 powder was added with 0.5 mL of acetic acid and ground for 5 min. Additional grinding for 25 min followed, during which 0.5 mL of ethanol (EtOH) was added every 1 min. Ground P25 powders were dispersed in an excess amount of EtOH. To prepare ethanolic suspension of 200-nm polystyrene beads, aqueous suspensions of PS beads (Alfa Aesar) were dried at 45 °C for 24 h in an oven and obtained solid beads were redispersed in EtOH and sonicated for 1 h. To prepare PS bead-incorporated TiO2 pastes, a mixture of ethanolic suspension of P25, ethanolic suspension of PS beads, 10wt.% ethanolic solution of EC and terpineol was concentrated by evaporating the excess solvents in a 45 °C oil bath with mild stirring. The final composition of the pastes was controlled to be (P25 + PS):EC:solvent = 1.5:1:8 in weight ratio.

Solar Cell Fabrication

A fluorine-doped tin oxide (FTO) substrate was cleaned and treated by 0.04 M aqueous solution of TiCl4 (Sigma-Aldrich, 99.9%) for 30 min at 70 °C, rinsed with deionized water (DIW) and annealed at 450 °C for 30 min to form TiO2 blocking layers on the surface61. On the TiCl4 pre-treated FTO substrate, TiO2 paste was spread by the doctor-blade method and annealed for 30 min at 450 °C. Another TiCl4 treatment was carried out on the sintered mp-TiO2 film using the same conditions as above. The mp-TiO2 film was then immersed in a mixture of 3-mercaptopropionic acid (3-MPA, Sigma-Aldrich, ≥99%), acetonitrile (Daejung, Extra Pure) and sulphuric acid (Duksan, Extra Pure) with the volume ratio of 1:9:0.05 for 24 h. The mp-TiO2 film functionalized with 3-MPA was then cleaned with acetonitrile and immersed in 3 mM (by Cd content) NR or HNR solution in toluene for 96 h. A ZnS passivation layer was formed on the sensitized film by SILAR, alternately immersing the NR- or HNR-sensitized electrode into a 0.1 M aqueous solution of zinc acetate dihydrate (Zn(CH3COOH)2 ∙ 2H2O, Sigma-Aldrich, ≥98%) and 0.1 M aqueous solution of sodium sulfide nonahydrate (Na2S ∙ 9H2O, Sigma-Aldrich, ≥98%). Each immersion took 1 min and the films were rinsed with DIW after each immersion to remove any remaining ions. This cycle was repeated twice to complete the ZnS passivation. To fabricate cuprous sulfide counter electrodes, thoroughly polished brass foil was first etched by hydrochloric acid for 20 min in an 80 °C oven. Etched foil was then sulfurized by adding a polysulfide solution (2 M Na2S and 2 M S in DIW) droplet, immediately after which the foil turned black62. The NR- or HNR-sensitized mp-TiO2 electrode and cuprous sulfide counter electrode were finally assembled into a sandwich-type cell using a binder clip and 60 μm thick scotch tape as a spacer. A solution of 1 M Na2S, 1 M S and 0.2 M KCl in MeOH:DIW = 7:3 solvent was used as the working electrolyte.


Transmission electron microscopy (TEM) was carried out on a JEOL 2100 TEM operating at 200 kV with samples that were prepared by drop-drying a dilute solution of NRs or HNRs in chloroform onto a Cu grid with a thin carbon film (Electron Microscopy Sciences). The UV-vis absorption spectra were collected with an Agilent 8453 photodiode array spectrometer and photoluminescence spectra were collected with a Horiba Jobin Yvon FluoroMax-3 fluorometer. The morphologies of mp-TiO2 electrodes were analysed using a scanning electron microscope (JSM-6360: Hitachi). The photocurrent-voltage (J-V) curves of SSCs were obtained with a potentiostat (CHI 608C: CH Instrumental Inc., Austin, USA) under AM 1.5 illumination (K3000: McScience, Korea, intensity at 100 mW cm−2). An incident photon-to-current conversion efficiency (IPCE) measurement system (K3100: McScience, Korea) was used to obtain IPCE spectra. Electrochemical impedance spectra (EIS) were obtained by a potentiostat with 20 mV sinusoidal perturbation and frequencies ranging from 10−1 to 105 Hz.

Additional Information

How to cite this article: Lee, S. et al. Integration of CdSe/CdSexTe1–x Type-II Heterojunction Nanorods into Hierarchically Porous TiO2 Electrode for Efficient Solar Energy Conversion. Sci. Rep. 5, 17472; doi: 10.1038/srep17472 (2015).