A long standing question in organic electronics concerns the effects of molecular orientation at donor/acceptor heterojunctions. Given a well-controlled donor/acceptor bilayer system, we uncover the genuine effects of molecular orientation on charge generation and recombination. These effects are studied through the point of view of photovoltaics—however, the results have important implications on the operation of all optoelectronic devices with donor/acceptor interfaces, such as light emitting diodes and photodetectors. Our findings can be summarized by two points. First, devices with donor molecules face-on to the acceptor interface have a higher charge transfer state energy and less non-radiative recombination, resulting in larger open-circuit voltages and higher radiative efficiencies. Second, devices with donor molecules edge-on to the acceptor interface are more efficient at charge generation, attributed to smaller electronic coupling between the charge transfer states and the ground state, and lower activation energy for charge generation.
The efficiencies of charge generation and recombination at a donor acceptor heterojunction depend on parameters, such as distance and molecular orientation of the donor and acceptor molecules at the interface. These processes dictate the performance of electronic devices such as light emitting diodes (LEDs), photodetectors, and photovoltaics. It is therefore critical to understand the properties of the donor/acceptor interface which affect the efficiencies of charge generation and recombination. The properties of the donor/acceptor interface can be studied from the point of view of photovoltaics, with implications on the performance of other devices which depend on donor/acceptor interfaces.
A fundamental issue under much debate in the organic photovoltaic (OPV) literature involves the geometry of the donor/acceptor interface: whether a face-on geometry (one where the π-faces of the donor and acceptor π-conjugated molecules or polymer chains are parallel) is favorable compared to an edge-on geometry (where the π-faces are orthogonal). Theoretical calculations have long suggested that the nature of the donor–acceptor interface will have a large effect on the rates of charge transfer and recombination1,2,3, as well as charge delocalization3, 4. Other calculations have found that molecular orientation affects interfacial quadrupoles and consequently the ease of charge separation5, 6. A number of researchers have attempted to resolve this question experimentally with the use of controlled donor and/or acceptor orientations in planar heterojunction solar cells1, 7,8,9,10,11,12,13,14. In general, most studies have found that within the same material system, face-on solar cells have a superior power conversion efficiency (PCE) when compared to the edge-on orientation7, 15. This has been attributed primarily to changes in the donor ionization potential (IP) (or, to a first approximation, highest occupied molecular orbital energy level), which directly affects the open circuit voltage (V OC)7,8,9, 11, 15,16,17, but has also been explained by differences in recombination rates1, 7, 12, 15.
Despite significant efforts, it has remained very challenging to fabricate high-quality planar heterojunctions with identical active layers and contacts, but opposite molecular orientations. Most studies settle for comparisons between one orientation and a mixed orientation, or modified contacts to induce changes in orientation. Furthermore, it was demonstrated that molecular diffusion in planar heterojunctions can happen spontaneously18, and to varying extents for different orientations19. Interfacial mixing will lead to unfair comparisons and erroneous conclusions if not properly taken into account. Furthermore, differences due to interfacial and/or bulk disorder have also been shown to influence device performance20, 21. To date, experimental studies in which the effects of molecular orientation have truly been isolated—a single materials system in which the two extremes of face-on and edge-on orientations can be accessed while maintaining abrupt donor/acceptor interfaces and identical contacts—have not been reported.
From the point of view of molecular orientation, our study addresses two topics that have been gaining significant attention in the OPV literature: non-radiative recombination losses to the V OC 3, 22,23,24,25,26,27, and the driving force for charge generation28,29,30. It is thought that non-radiative recombination plays a significant role in efficiency losses in photovoltaics and LEDs, and it is only when non-radiative pathways have been eliminated that organic solar cells become competitive with high performance inorganic materials23, 25, 31, 32. A recent theoretical study by Chen et al. on pentacene/C60 interfaces predicts that face-on interactions result in less non-radiative recombination, due to reduced vibronic coupling between the charge transfer (CT) state and the ground state (GS)3. To date, little is understood about the origin of non-radiative recombination in organic solar cells, how it relates to molecular orientation, or how to curtail this recombination pathway. Furthermore, the driving force for charge generation has remained a disputed topic in the literature, with researchers quoting the need for energetic offsets33, 34, hot charges35, 36, delocalization37, 38, low reorganization energies39, electric fields40, 41, energetic cascades and disorder42, 43, and entropy29, 44, to achieve efficient charge generation.
In this work, we begin by establishing that we are able to precisely control the molecular orientation of p-SIDT(FBTTh2)2 45 (structure and orientations shown in Fig. 1a) in neat films, and fabricate bilayer heterojunctions with sharp, well-defined interfaces of known molecular orientations. We then analyze the photovoltaic performance, which reveals that molecular orientation has a profound effect on the V OC and short-circuit current (J SC) (Fig. 1b). The higher V OC of the solar cells with face-on p-SIDT(FBTTh2)2 is attributed to a higher CT state energy (E CT) and lower non-radiative recombination losses. However, the edge-on solar cells are more efficient at charge generation, illustrated by a higher internal quantum efficiency (IQE). Electronic-structure calculations predict that the face-on bilayers have a larger electronic coupling between the CT state and GS, suggesting that they suffer from greater geminate recombination. In addition, charge generation in face-on bilayers is significantly more temperature-dependent than edge-on bilayers, which may be a consequence of a larger barrier to charge generation or favorable polarization at the edge-on donor/acceptor interface. Our study presents important experimental evidence pertaining to the effect of molecular orientation on non-radiative recombination and the efficiency of charge generation.
To begin, films of neat p-SIDT(FBTTh2)2 were characterized to quantify bulk and interfacial molecular orientation. Preferential orientation can be measured using grazing incidence wide-angle X-ray scattering (GIWAXS), by comparing intensities of in-plane and out-of-plane π-stacking peaks (at q ~ 1.7 Å−1). More detail on the methodology is available in the Supplementary Fig. 1. When cast from chlorobenzene (CB), films of p-SIDT(FBTTh2)2 show a ratio of 99.5:0.5 face-on:edge-on orientation. When cast from CB with 0.4% v/v diiodooctane (DIO), films of p-SIDT(FBTTh2)2 show a ratio of 94:6 edge-on:face-on orientation. The two orientations also have distinctly different structures seen by high-resolution transmission electron microscope (HR-TEM) images. Figure 2a–d show HR-TEM and GIWAXS images of p-SIDT(FBTTh2)2 films cast from CB (face-on) and CB+DIO (edge-on).
In addition to providing information about the molecular orientation, the GIWAXS images in Figs. 2c, d also show that the edge-on p-SIDT(FBTTh2)2 films are more ordered than the face-on films. We do not believe that this difference in ordering has a large impact on the results discussed further in this study; we refer the reader to further data and discussion on this topic in Supplementary Fig. 2 and Supplementary Notes 1, 2.
The quality of the p-SIDT(FBTTh2)2 interface was verified by cross-section HR-TEM and GIWAXS. The miscibility of C60 into p-SIDT(FBTTh2)2 was determined by monitoring the GIWAXS signal of varying thicknesses of C60 evaporated on p-SIDT(FBTTh2)2 (Supplementary Fig. 3). A linear increase in C60 scattering intensity with C60 thickness indicates that C60 molecules are not diffusing into the p-SIDT(BFTTh2)2 layer beneath. Figure 2g shows a linear signal growth with C60 thickness for the face-on device, confirming that the interface is sharp. The trace for the edge-on device, Fig. 2h, shows a slight deviation from linearity at small thicknesses of C60. However, this can be explained by deposition of C60 into pinholes in the edge-on p-SIDT(FBTTh2)2 film which are not present in the face-on film (Supplementary Fig. 4). In addition to reducing the actual film thickness from the nominal predicted film thickness, the surface topography presented by pinholes may have an unpredictable effect on the X-ray scattering. Cross-section TEM (Figs. 2e, f) shows no evidence of interdiffusion for either face-on or edge-on bilayers. In fact, lattice planes can be well resolved in the cross-section TEM of the edge-on sample for the entire thickness of the p-SIDT(FBTTh2)2 layer (Fig. 2f). The lattice planes further confirm that the donor layers retain their orientation through the bulk of the film to the interface with C60, and that deposition of the C60 layer does not disrupt the packing of p-SIDT(FBTTh2)2. Thus, it can be concluded that the donor/acceptor interface is abrupt for edge-on and face-on p-SIDT(FBTTh2)2.
Solar cell characteristics
The J–V characteristics of the edge-on and face-on bilayers, using identical contacts (ITO/PEDOT:PSS/active layer/BCP/Al, see Methods for full material names), under 1 sun illumination, are presented in Fig. 1b and Table 1. The J SC and the fill factor (FF) are very similar for both molecular orientations of the donor layer. The V OC, on the other hand, is a substantial 150 mV larger when the donor molecules are face-on compared to edge-on.
The solar cell characteristics here are averages of over 150 devices of each orientation; histograms for each parameter are available in Supplementary Fig. 5.
Open circuit voltage
There are several factors that can account for the change in the V OC, and we will explore each in turn: IP and E CT, radiative recombination, and non-radiative recombination.
A number of studies have demonstrated that changing molecular orientation in a film can lead to differences in the material energy levels7,8,9, 11, 16, 17, which can have a direct effect on the V OC. Indeed, ultraviolet photoelectron spectroscopy (UPS) measurements of neat p-SIDT(FBTTh2)2 films show an increase on the order of 60 meV in the IP of p-SIDT(FBTTh2)2 when it is face-on (Supplementary Fig. 6). In good agreement, electronic-structure calculations performed on p-SIDT(FBTTh2)2 also found that the face-on orientation has a deeper ionization potential (Supplementary Fig. 7). However, as the V OC varies by 150 mV, changing the molecular orientation has altered more than just the IP value.
It has been demonstrated numerous times that E CT and V OC tend to correlate according to: E CT−qV OC = 0.6 ± 0.1 eV23, 46. The CT state is routinely studied with highly sensitive absorption techniques (here, we use external quantum efficiency, EQE), where it is identified as a shoulder at sub-bandgap energies46. The CT state can also be studied by emission spectra (here we use electroluminescence, EL), where it is identified as a featureless emission spectrum at low energies47. The E CT, located at the midpoint between the absorption and emission of the CT state, can be determined by a simultaneous fit to the measured absorption (Eq. 1) and emission spectra (Eq. 2)48:
In these equations, k denotes Boltzmann’s constant; T, temperature; and E, photon energy. The fit parameters are E CT (energy of the CT state), λ (reorganization energy), and f (a parameter proportional to the number of CT states and the square of their coupling matrix element with the GS). Eqs. 1 and 2 are called the reduced absorption and emission spectra, due to the multiplication and division of the spectra by E, respectively.
Using Eqs. 1 and 2, fit simultaneously to the EQE and EL spectra, we obtain that E CT is 1.38 ± 0.02 eV when p-SIDT(FBTTh2)2 is face-on vs. 1.32 ± 0.03 eV for the edge-on orientation. The EQE, EL and their corresponding fits are shown in Fig. 3a–b. The 60 meV higher E CT is in excellent agreement with the higher ionization energy of the face-on p-SIDT(FBTTh2)2 layer, implying vacuum alignment at the interface to C60. However, it does not explain the full difference in V OC upon changing molecular orientation.
Another estimate for the E CT can be obtained by temperature-dependent V OC measurements extrapolated to 0 K48, 49, where the deviation from E CT to V OC at room temperature (RT) should correlate with losses in the solar cell. One model that has been demonstrated on a number of systems separates the losses from E CT into radiative and non-radiative recombination, shown in Eq. 3 48:
In these equations, J SC represents the short circuit current; h, Planck’s constant; c, speed of light; E CT, f, λ are fit parameters from Eqs. 1 and 2 (Fig. 3a, b); and EQEEL is the total external quantum efficiency of electroluminescence.
The V OC values of each bilayer were measured at different light intensities and temperatures ranging from 190 to 310 K, and extrapolated to 0 K, as shown in Fig. 3c. For all light intensities the V OC extrapolated to 0 K is 1.40 ± 0.02 V for the face-on compared to 1.31 ± 0.02 V for the edge-on solar cells, which is in close agreement to the E CT values obtained from the fits of the EQE and EL spectra. This confirms our interpretation from above that the difference in V OC is not solely due to energetics. In fact, from the temperature-dependent slopes in Fig. 3c, it is evident that the overall V OC loss is smaller in face-on than in edge-on bilayers.
As shown by Eq. 3, the voltage loss can be quantified into radiative and non-radiative recombination contributions, as has been outlined by Rau31 and Vandewal et al.48 Radiative recombination can be estimated according to Eq. 4. We find that at room temperature ΔV rad is very similar, 199 ± 2 mV and 197 ± 4 mV for the face-on and edge-on bilayers, respectively, leading to the conclusion that losses due to radiative recombination are not a function of molecular orientation.
Non-radiative recombination remains poorly understood, yet it is considered to be among the primary reasons that the overall V OC loss has not decreased significantly in recent years25. Most organic blends reported in the literature lose 300–400 mV to non-radiative recombination, constituting 60% or more of the lost potential25, 48. To estimate the effect of orientation on non-radiative recombination, we refer to EQEEL, defined as photons emitted per electrons injected into the device. The lower the radiative efficiency, the more non-radiative decay channels contribute to the overall recombination. Equation 5 relates EQEEL to the voltage loss.
Importantly, the measured EQEEL values differ by more than an order of magnitude between the two samples, with 3.2 × 10−6 ± 1.4 × 10−6 for the face-on and 2.3 × 10−7 ± 3.5 × 10−7 for the edge-on bilayers. Using Eq. 5, we find that voltage losses due to non-radiative recombination are 316 ± 10 mV and 382 ± 28 mV for the face-on and edge-on solar cells, respectively.
Table 2 summarizes the energetic and recombination differences between the bilayers with the two orientations. The estimated difference in V OC between the two orientations, V OC,calc, calculated from the measured E CT and the estimated losses due to radiative and non-radiative recombinations (Eq. 3) is in very good agreement with the measured ΔV OC, determined experimentally from the J–V characteristics.
The significance of these findings lies in the differences in non-radiative recombination: on average, the edge-on solar cells lose 66 mV more voltage than face-on cells due to non-radiative recombination. Using the same system but flipping the donor molecular orientation, the non-radiative recombination pathway has been altered, implying it is sensitive to the molecular alignment at the donor/acceptor interface. Interestingly, these experimental results are fully consistent with a recent theoretical study: Chen et al.3 found that the higher E CT value and greater hole delocalization and migration away from a face-on pentacene/C60 interface caused a decrease in vibronic coupling of the CT state to the GS, thus reducing the non-radiative recombination rate. While the results by Chen et al.3 refer to model molecular packings of pentacene, the similarity to our findings on p-SIDT(FBTTh2)2/C60, namely a smaller E CT and more non-radiative recombination in the edge-on bilayers, is striking.
Short circuit current
In contrast to the V OC, the J SC appears independent of molecular orientation (Fig. 1). However, due to alignment of the molecular transition dipoles, the absorption strength of the two bilayers toward normal incident light is significantly different: face-on p-SIDT(FBTTh2)2 films have a two times higher absorbance as edge-on films (Supplementary Fig. 8). Using a combination of Monte Carlo (MC) and molecular dynamics (MD) simulations, we find that p-SIDT(FBTTh2)2 has a unique unit cell, shown in Supplementary Fig. 9, true for both molecular orientations. As a consequence, half the p-SIDT(FBTTh2)2 molecules in the edge-on orientation are lying down with their long edge parallel to the substrate, and half the molecules are standing up on their end, with their sides perpendicular to the substrate (as depicted in Fig. 1a). In the face-on orientation, all the p-SIDT(FBTTh2)2 molecules are parallel to the substrate. This model for the packing of p-SIDT(FBTTh2)2 is in good agreement with the two-times higher absorbance of the face-on films. Furthermore, to verify that the results we have reported thus far are not a consequence of the different geometry of molecular transition dipoles with respect to light, we measured the current-voltage (J-V) curves for the bilayer solar cells as a function of illumination angle. The V OC remains unchanged, while the J SC increases by a small amount (Supplementary Fig. 10).
The similar J SC values are in agreement with the EQE (quantum efficiency per incident photon) of the bilayers, both peaking at about 25% on average. However, when the EQE spectra are corrected for absorption of the active layer (device absorption corrected for parasitic absorption, more detail in Supplementary Fig. 11), we obtain quantum efficiency spectra per absorbed photons, i.e., IQE. EQE and IQE spectra of the bilayers are shown in Fig. 4a. For reference, the unitless absorption spectra of p-SIDT(FBTTh2)2 and C60 are shown in the background.
IQE of the edge-on bilayers is higher than the face-on bilayers (Fig. 4a). A higher IQE indicates that in edge-on bilayers fewer excitons and charges recombine at short circuit. In other words, the edge-on solar cells have more efficient charge generation. Charge generation depends on exciton quenching efficiency and geminate recombination. Photoluminescence (PL) quenching measurements comparing neat edge-on and face-on films with their respective bilayer structure show that both molecular orientations have the same quenching efficiency (Supplementary Fig. 12). Therefore, the difference in the IQE values must originate from geminate recombination after charge transfer across the heterojunction. This finding is consistent with the results of our electronic-structure calculations, which indicate that electronic coupling between CT state and GS is weaker in the edge-on configuration than in the face-on configuration (Supplementary Fig. 13). A smaller electronic coupling is expected to decrease the rate of geminate recombination as the CT state tends to dissociate, shifting the generation-recombination balance towards free charge formation, as seen here2.
For a deeper understanding of the differences in IQE, we measured the EQE under varying electric fields and temperatures. These measurements are complex, since they reflect the combination of many processes such as exciton diffusion, charge transfer, charge generation, bimolecular recombination, and charge transport. However, with the appropriate conditions and analysis, EQE measurements can be used to gain insight into charge generation/geminate recombination. Specifically, to eliminate effects of exciton diffusion and charge transfer, EQE spectra can be analyzed at energies corresponding to CT state absorption. Also, since these devices are bilayers and the measurements are carried out at low light intensities and under an internal field (J SC conditions, unless otherwise stated), bimolecular recombination and the effect of differences in of charge transport are expected to be negligible. Under these conditions, our EQE measurements should reflect the dependence of charge generation/geminate recombination on electric field and temperature.
First, we asked if changing interfacial molecular orientation has an impact on the Coulomb binding energy of the CT state. The binding energy, a consequence of the electrostatic attraction between opposite charge carriers, depends on the electron-hole separation and the dielectric constant50. The binding energy can be overcome with the assistance of a field40, 51, and thus it may follow that the field-dependence of generation would be different for the two bilayers52. Figure 4b shows the effect of an electric field on the EQE of the devices: both have a very similar dependence on the electric field. The EQE values in Fig. 4b are normalized to the efficiency at the strongest applied bias, and the field across the device is corrected by the built-in voltage, analogous to photocurrent analysis (for bias-dependent EQE spectra, see Supplementary Fig. 14). Time delayed collection field (TDCF) measurements confirm no significant differences in the field dependence of generation between the two orientations (Supplementary Fig. 15). Furthermore, by TDCF there is no difference in field-dependence of generation for excitations at 350 nm, 600 nm, or 650 nm, ruling out any effects of hot-exciton generation. All these results indicate that the binding energy of the CT state is not a function of molecular orientation.
Next, we turned our attention to the temperature-dependence of charge generation. Figure 4c shows EQE values normalized to the EQE at RT, as a function of temperature (for temperature-dependent EQE spectra, see Supplementary Fig. 16). The temperature dependence is shown for absorption over all energies, as well as absorption corresponding only to the CT state (~1.2–1.5 eV). Overall, while charge generation in both bilayers is temperature-dependent, the temperature-dependence in the face-on bilayers is much stronger, indicating a larger activation energy for charge generation. To illustrate this point, if we make crude simplifications and extrapolate the EQE values to the limit of temperature→0 K, we find that generation in the face-on bilayer becomes negligible, while the edge-on bilayer can still generate about 10–40% carriers (as compared to carrier generation at RT). Charge generation resulting from bulk and direct CT state excitations follows similar temperature dependences, as a function of p-SIDT(FBTTh2)2 orientation. The contrast in temperature dependence is therefore not due to differences in exciton diffusion or electron transfer, but is instead a result of difference in charge generation with interfacial molecular orientation. This can be explained by a larger barrier to charge generation in the face-on bilayer due to elements such as electronic coupling between the CT states and separated states or polarization at the donor/acceptor interface.
In conclusion, we have been able to fabricate donor-acceptor bilayers with sharp interfaces and well-defined p-SIDT(FBTTh2)2 molecular orientations: either face-on or edge-on with respect to the substrate. These orientations are preserved through the donor film to the interface with C60, with none-to-minimal diffusion at the donor/acceptor interface. This unprecedented precise morphological control reveals the genuine effects of molecular orientation on photovoltaic performance. Edge-on p-SIDT(FBTTh2)2 bilayers suffer from greater non-radiative recombination and a reduced E CT, which result in a substantial V OC loss of 150 mV. However, charge generation is more efficient when the donor/acceptor interface is edge-on, evidenced by a higher IQE. This is attributed to reduced CT state-GS electronic coupling as well as smaller activation energy for charge generation in the edge-on bilayer, which may be a consequence of a reduced barrier between CT state and charge-separated states or favorable polarization at the donor/acceptor interface.
The lessons learned from p-SIDT(FBTTh2)2/C60 bilayers can be summarized into two major points: First, in applications which benefit from high radiative efficiency (such as LEDs and OPVs), interfacial molecular orientation should reduce non-radiative recombination (by reducing charge recombination through triplet states or through vibronic coupling of the CT state to the GS). Our results establish that face-on molecular orientations would achieve higher radiative efficiency. Second, In applications where charge separation is important (such as photodetectors and OPVs), the electronic couplings between the CT state and the GS, as well as the activation energy for charge generation should both be minimized. This can perhaps be accomplished by beneficial polarization effects. Thus, our results determine that interfacial molecular orientation should be edge-on for intrinsic, efficient charge generation.
Overall, in the case of OPV, these two lessons go in opposite directions. These results highlight that to achieve high performance in OPV, the electronic coupling for face-on donor/acceptor interactions must be reduced to eliminate geminate recombination. Conversely, more research on non-radiative recombination is necessary in order to curtail the resulting losses and benefit from the improved charge generation in an edge-on donor/acceptor interaction. It may be possible to tackle both problems from the perspectives of molecular design and clever device engineering.
p-SIDT(FBTTh2)2 (benzo[1,2-b:4,5-b]bis(4,4′-dihexyl-4H-silolo[3,2-b]thiophene-2,2′-diyl)bis(6-fluoro-4-(5′-hexyl-[2,2′-bithiophene]-5-yl)benzo[c][1,2,5]thiadiazole) was synthesized according to the previously reported scheme45. p-SIDT(FBTTh2)2 was dissolved at a concentration of 15 mg ml−1 in pristine CB, or CB with 0.4% DIO v/v. In the CB+DIO solution, the conditions correspond to a ratio of two molecules DIO for every one molecule of p-SIDT(FBTTh2)2 53. The face-on films used in this study were achieved by spin-casting p-SIDT(FBTTh2)2 from pristine CB solutions, and the edge-on films were achieved by casting from CB+DIO solutions, at 2000 round per minute (RPM). Bilayer devices were fabricated on glass substrates sputtered with ITO, and coated with 35 nm poly(3,4-ehtylenedioxythiophene):poly(styrenesulfonate) (PEDOT:PSS). A C60 layer was thermally evaporated on p-SIDT(FBTTh2)2, followed by bathocuproine (BCP) and aluminum (Al). The final device structure for nearly all measurements reported herein is as follows: ITO/PEDOT (35 nm)/p-SIDT(FBTTh2)2 (45 nm)/C60 (45 nm)/BCP (4 nm)/Al (80 nm).
GIWAXS was performed at Stanford Synchrotron Radiation Lightsource beamline 11-3 with a MAR345 image plate. The data was calibrated and reduced using WxDiff software package54. To characterize the amount of edge-on vs. face-on material, a cake slice around the π-stacking peak, between Q = 1.8 Å−1 and 2.0 Å−1, was reduced to a pole figure. An adjacent cake slice between Q = 1.7 Å−1 and 1.8 Å−1 was subtracted from the data to account for background scattering (see Supplementary Fig. 1). The data was fit to two in-plane π-stacking peaks at about −90° and +90°, one out-of-plane π-stacking peak at 0°, and four peaks around ±30° and ±55° representing the SiO2 substrate background. The out-of-plane peak area was compared to the average of the two in-plane peak areas to arrive at the face-on to edge-on ratio for each sample. Samples for GIWAXS were prepared on cleaned SiO2 substrates, coated with PEDOT:PSS and p-SIDT(FBTTh2)2 cast from 15 mg ml−1 CB or CB+DIO.
The C60 scattering as a function of C60 thickness was tracked by reducing cake slices shown in Supplementary Fig. 3 to I vs. Q. We selected these specific cake slices for analysis because they contain non-overlapping peaks from both the small molecule and the C60, allowing a simultaneous comparison of contributions from both materials. This data was fit to a linear combination of neat p-SIDT(FBTTh2)2 and neat C60 data, and the fit coefficient for C60 was reported. Fits are shown in Supplementary Fig. 3 along with the neat data. Fits have some discrepancy due to small changes in peak shape but are reasonably accurate in depicting overall trends. Samples for these measurements were prepared on cleaned SiO2 substrates, coated with PEDOT:PSS and p-SIDT(FBTTh2)2 cast from 15 mg ml−1 CB or CB+DIO, with C60 evaporated for thicknesses of 0–30 nm.
Ultraviolet photoelectron spectroscopy
UPS samples were prepared on ITO-sputtered glass substrates cleaned by sonication in water, acetone, and isopropyl alcohol for 15 min, followed by UVO treatment for 1 h. ITO pieces were immediately transferred to the glove box. Solutions of 7 mg ml−1 p-SIDT(FBTTh2)2 in CB or CB+0.4% DIO were prepared ahead of time, and allowed to stir on the hot plate at 110 °C. Prior to casting the films, the solutions were brought to room temperature. Films were cast at 4000 RPM for film thicknesses of about 10 nm; thicker films of p-SIDT(FBTTh2)2 led to distortion of the UPS signal due to charging in the film. The UPS samples were transferred to an ultrahigh vacuum chamber from the nitrogen glove box in an airtight chamber to avoid any surface degradation or contamination with air. The UPS was measured with a HeI source (21.2 eV), at pressures of low 10−7 Pa, a constant pass of 5 eV, current of 10 mA, and the anode set to 6 kV. The ionization potential was calculated according to I p = 21.2 eV−(E cutoff −E g)55, where the E cutoff and E g were determined by the onset at high and low binding energies, respectively. The energy resolution of the UPS measurements is below 10 meV.
Solar-cell device properties were measured under illumination by a simulated 100 mW cm−2 AM1.5 G light source using a 300 W Xe arc lamp with an AM 1.5 global filter. The irradiance was adjusted to one sun with a standard silicon photovoltaic calibrated by the National Renewable Energy Laboratory. Temperature dependent V OC in the range of 275–300 K was collected using a custom Peltier cooled sample holder under illumination from the above described light source in combination with optical density filters to reduce the intensity. In the range of temperatures below 275 K, a helium cryostat was used for temperature control and illumination was achieved with a high power 1 W, 445 nm laser diode (fluence was tuned with the DC bias applied to the laser diode to match light intensity used in the solar simulator). Bias dependent J–V spectra were measured by changing the angle of the light source, while keeping the device constant. Before each J–V measurement light intensity was calibrated to 1-sun using the calibrated silicon photovoltaic.
TEM and cross-sectional TEM
TEM samples were prepared by casting a layer of p-SIDT(FBTTh2)2 from CB or CB+DIO on PEDOT:PSS, and floating pieces of the film on deionized (DI) water. Film pieces were transferred to TEM grids and allowed to dry overnight. High-resolution images were taken with an FEI Titan FEG High Resolution microscope. The TEM images were collected using a low-dose electron beam (spot size 6) to avoid beam damage, and a small defocus to enhance the contrast in the images.
Using an FEI focused ion-beam (FIB) microscope, a 20 µm long slice with a thickness of about 200 nm was cut from a bilayer device (prepared as described above), and mounted on a TEM grid. The donor/acceptor interface in the bilayers was then imaged by HR-TEM. The procedure followed has been described in detail previously56, 57. Careful attention was devoted to minimize exposure of the sample to high-energy electron and ion beams, thereby reducing damage as much as possible.
Atomic force microscopy
Atomic force microscopy (AFM) images were collected in air, using a Si tip, and an Innova AFM operated under tapping mode.
UV-visible absorption spectroscopy
Absorption spectra of neat face-on and edge-on p-SIDT(FBTTh2)2 and C60 films were collected using a Perkin Elmer Lambda 750 spectrophotometer. Samples for absorption measurements were prepared on clean glass slides, following the same procedure used to prepare the respective layer in the bilayer solar cell devices: face-on and edge-on p-SIDT(FBTTh2)2 films were solution cast from their respective solutions, and C60 films were thermally evaporated. The film thickness for all samples was 45 nm.
External and internal quantum efficiency
EQE characteristics were measured in a nitrogen-filled glovebox using a setup at UCSB and in Potsdam University. At UCSB, the EQE setup consisted of a 75 W Xe light source, monochromator, optical chopper, lock-in amplifier, and a National Institute of Standards and Technology calibrated silicon photodiode for power-density calibration. At Potsdam University, the EQE setup is similar, but used a 200 W halogen lamp (Philips), and a UV enhanced silicon photodiode to calibrate the visible spectra, or a germanium photodiode to calibrate the near infrared spectra. Both photodiodes were calibrated by Newport. For the sub-bandgap EQE, higher sensitivity settings were used with a longer time delay between measurement points. Bias-dependent EQE was collected on the setup in Potsdam University, coupled to a Keithley source-measure-unit used to apply a bias while the EQE spectra were recorded. Temperature-dependent EQE measurements were collected with a setup at UCSB, following a similar procedure, using a nitrogen-cooled cryostat.
Total absorption of solar cell devices was measured with an integrating sphere, and corrected for parasitic absorption as determined for the bilayers using a transfer matrix model58. Subtracting the parasitic absorption from the total device absorption then gives the active layer absorption, and dividing EQE spectra by the corresponding active layer absorption gives the IQE spectra of the device.
EL and its efficiency
EL spectra for the bilayers were collected directly from the solar cell devices, by applying a bias that is close to the turn-on voltage of the devices. The resulting emission was collected with an Andor SR393i-B spectrometer provided with a cooled silicon detector DU420ABR-DD and a cooled InGaAs DU491A-1.7 detector. The spectra were corrected for detector response using a blackbody spectrum.
The EL efficiency was collected by applying a small bias to the bilayer devices, and placing a calibrated silicon photodiode directly in front of the device to collect the resulting emission. The angle between the calibrated silicon photodiode and the device was varied to account for anisotropy in emission intensity.
PL quenching measurements
PL samples were prepared by spin-coating p-SIDT(FBTTh2)2 films (face-on or edge-on) on clean glass slides, and evaporating C60 on half the slides, analogous to the preparation of the active layer in the bilayer devices. The samples were encapsulated inside the glovebox by applying epoxy around the edges of the glass slide and putting another glass slide on top, to create an air-tight, nitrogen environment. The samples were excited by a laser excitation at 455 nm, and the PL collected using a silicon CCD camera, cooled to −70 °C. A series of lenses were used to collect the PL and focus it on the CCD camera slit. The resulting spectra were corrected for instrument response by using a reference blackbody spectrum.
Time-delayed collection field measurements
Excitation is realized by a laser system consisting of a Libra USP-1K-HE with a pulse energy of ~4.0 mJ at 1 kHz and an OPerA Solo for wavelength selection. The pre- and collection voltage is applied via an Agilent 81150A pulse generator in combination with a home-built amplifier. Currents through the devices are measured via a 50 Ω resistor and recorded with an Yokogawa DL9140 oscilloscope.
The p-SIDT(FBTTh2)2 bulk structure and C60/p-SIDT(FBTTh2)2 bilayer structure were generated by a combination of MC and MD simulations. The MD simulations were run for 200 ps at 300 K with under the NVT ensemble using the Verlet integrator with a time step of 1 fs. The temperature was maintained by the Nose-Hoover thermostat. A spherical cutoff of 1.25 nm for the summation of van der Waals interactions and the Ewald solver for long-range Coulomb interactions was used throughout. The COMPASS force field as implemented in the Forcite program of Materials Studio was used for the MD simulations59. Density-functional theory calculations using the range-separated HSE functional were then carried out for face-on and edge-on p-SIDT(FBTTh2)2 slabs under periodic boundary conditions using the plane-wave based Vienna Ab-initio Simulation Package60,61,62,63.
The electron couplings between diabatic CT state and the GS of the p-SIDT(FBTTh2)2/C60 complexes were evaluated by means of the generalized Mulliken-Hush approach at the MD generated geometry. These calculations were performed with the B3LYP functional and 6–31G(d,p) basis set, using the Q-Chem package64.
Data and materials necessary to replicate this work are available upon request from the authors.
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This collaborative project was supported by the Department of the Navy, Office of Naval Research (Award No. N00014-14-1-0580). Synthesis of p-SIDT(FBTTh2)2 was supported by the Office of Naval Research (N-00014-04-0411). HR-TEM and FIB analysis were conducted in the MRL Shared Experimental Facilities at UCSB. The MRL Shared Experimental Facilities are supported by the MRSEC Program of the NSF under Award No. DMR 1121053; a member of the NSF-funded Materials Research Facilities Network (www.mrfn.org). S.R. and D.N. acknowledge financial support by the German Ministry of Science and Education (Project UNVEIL, FKZ 13N13719). The high resolution TDCF setup was funded by the Deutsche Forschungsgesellschaft (INST 336/94-1 FUGG).
The authors declare no competing financial interests.
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