Colloidal semiconductor nanocrystals have attracted significant interest for applications in solution-processable devices such as light-emitting diodes and solar cells. However, a poor understanding of charge transport in nanocrystal assemblies, specifically the relation between electrical conductance in dark and under light illumination, hinders their technological applicability. Here we simultaneously address the issues of 'dark' transport and photoconductivity in films of PbS nanocrystals, by incorporating them into optical field-effect transistors in which the channel conductance is controlled by both gate voltage and incident radiation. Spectrally resolved photoresponses of these devices reveal a weakly conductive mid-gap band that is responsible for charge transport in dark. The mechanism for conductance, however, changes under illumination when it becomes dominated by band-edge quantized states. In this case, the mid-gap band still has an important role as its occupancy (tuned by the gate voltage) controls the dynamics of band-edge charges.
Semiconductor nanocrystals (NCs) fabricated by chemical1 and physical2 methods have been considered promising materials for applications in solution-processable devices including light-emitting diodes3,4,5, field-effect transistors (FETs)6,7,8,9,10,11 ,photodetectors12, and solar cells13,14,15,16,17,18. In addition to processability from solutions, NCs are attractive because of a variety of novel physical properties that can be controlled by NC dimensions, shapes, and internal structure19. Several recent examples have also demonstrated a large promise of NCs for the realization of generation-III photovoltaics by employing concepts such as multiexciton generation through carrier multiplication20,21,22,23,24, and hot-electron extraction25,26.
A significant problem in realizing practical NC-based devices is poor understanding of charge transport in NC films. Traditional assumption is that electrical conductance in NC-based structures is mediated by a network of overlapping band-edge quantized states20,27. However, recent demonstrations of a dramatic effect of surface treatments on 'dark' conductivity (σ0) of NC films9, combined with observations of relatively weak sensitivity of σ0 to NC size polydispersity10, suggest the involvement of intra-gap states (probably of surface origin) in charge transport. Furthermore, previous FET studies have indicated that changes in the occupancy of surface traps might be responsible for observed changes in apparent levels of doping of NC films11.
Whereas it is typically difficult to assess the nature of states involved in 'dark' charge transport, a photoresponse should involve quantized states, as these states get populated as a result of light absorption. The relative contribution of quantized states to photoconductivity compared with the states that dominate 'dark' charge transport is unclear. For example, the studies of NC photovoltaics indicate that although the open circuit voltage (Voc) does scale with NC band-gap energy (Eg), it is always appreciably lower than the ideal Voc calculated for a given Eg (refs 14,15,17,27) (see Supplementary Information for discussion on semiconductor bandgap and open-circuit voltage). This might be considered as an indication of a mixed character of photoconductivity, which could involve both quantized and surface-related states. One hurdle in elucidating the nature of electronic states responsible for conduction in dark and under illumination arises from the fact that the data on 'dark' transport and photoconductivity are normally obtained using different types of devices that are, respectively, three-terminal FETs, and two-terminal photodetectors or photovoltaic cells.
Here we investigate the roles of quantized band-edge and intra-gap states in NC-film conductance by using three-terminal PbS–NC-based optical FETs (OFETs). We simultaneously address the problems of 'dark' transport and photoconductance, and elucidate the roles of equilibrium charges injected by applying gate voltage versus non-equilibrium carriers generated by photoexcitation. Spectrally resolved studies of a gate-voltage-dependent photocurrent reveal the existence of mid-gap states in NC films that form a weakly conducting band (mid-gap band or MGB), which serves as a charge conduit in dark. We also observe that the nature of charge transport changes under illumination when it becomes dominated by carrier migration through the network of band-edge quantized states, which is characterized by much higher mobility than the MGB. The MGB still has an important role in the photoresponse as its occupancy controls the photoconduction by controlling recombination dynamics of band-edge charges. The analysis of the gate-voltage dependence of photoresponses indicates that lifetimes of band-edge electrons are much shorter than those of holes indicating a much greater probability of electron capture at MGB states compared with holes. This suggest that photoconductivity in our films is dominated by photogenerated holes.
'Dark' charge transport in NC films
The layout of the OFET devices used in the present study is shown schematically in Figure 1a (fabrication details in Methods). Its channel is fabricated from PbS NCs with a mean diameter of 3.3 nm (Fig. 1b inset). The corresponding band-gap energy Eg=1.3 eV. First, we characterize these structures in dark (black curve in Fig. 1c) by monitoring the source–drain current (Isd) as a function of gate bias (Vg). When Vg=0 (flat-band condition in our devices in dark), the OFET channel is only weakly conductive. However, Isd quickly increases under negative gate bias, which corresponds to injection of holes into the NC film. At Vg=−25 V, Isd becomes ca. three orders of magnitude higher than at Vg=0. From gate-source capacitance measurements (Fig. 1d), we estimate that that the average number of holes injected per NC (n0) at Vg=−25 V is n0≈0.1 (Methods).
Although Isd also appears to increase considerably on applying the positive gate-source voltage, this growth is an artefact of our measurements, in which we switch the sign of Vg without changing the sign of the source–drain voltage. As a result, the gate-drain voltage for Vg>0 is considerably higher (varies from +25 V to +35 V) than in the case of Vg<0 (varies from +25 V to 0), which might lead to a significant gate leakage current for positive gate voltages. This effect is likely responsible for the increase of Isd when Vg>0, but not electron injection. The reason for performing the measurements without changing the sign of Vsd is that the exposure of OFETs to light leads to changes in the flat-band voltage. Because of this effect, an extra positive gate voltage is required to achieve the flat-band condition on illumination.
From the data in Figure 1c, however, it is still possible to evaluate the relative efficiencies of electron and hole injection into the NC channel. Specifically, because of symmetry between the gate and source electrodes (both are fabricated from gold), the conditions for hole injection at Vg=−25 V are equivalent to conditions for electron injection at Vg=0 V. A significantly smaller dark current measured in the latter case indicates that electron injection in our devices is much less efficient (likely negligible) than hole injection. The capacitance measurements (Fig. 1d) also do not show any detectable electron injection in our structures in the range of Vg>0.
Spectrally resolved photoresponses of OFETs
Illumination of these devices with monochromatic light leads to a dramatic increase in Isd even at low light intensities, as illustrated by the three-dimensional plot in Figure 1c, for incident fluxes from 120 nW cm−2 to 30 μW cm−2 (2.25 eV illumination). The respective densities of photogenerated charges can be estimated from the product of the generation rate (G) and the carrier lifetime (τ), which yields ca 10−4 to 10−6 per NC for the maximum photon flux (Methods). This density is orders of magnitude lower than the number of charges injected into the film by applying a gate voltage (for example, n0≈0.1 for Vg=−25 V). Therefore, the fact that exposure to light leads to a dramatic increase in conductivity implies that photogenerated charges are characterized by much higher mobilities than equilibrium background charges. This strongly suggests that the natures of electronic states involved in charge transport in dark and under illumination are different.
Light illumination also results in the apparent, intensity-dependent shift of the flat-band voltage traced by the black line in the contour plot at the bottom of Figure 1c. This is a reflection of the photovoltaic effect due to accumulation of photogenerated carriers under the source/drain electrode, which changes the total gate bias and hence the source–drain current (light acts as the 'fourth terminal' in our OFETs). As a result, under illumination an extra positive voltage is required to achieve the flat-band condition and the magnitude of this excess bias can serve as a measure of the photovoltaic effect.
To gain further insights into the origin of charge-transporting states, we investigate the Vg-dependence of photocurrent spectra that are derived from the Isd-versus-Vg characteristics measured for different excitation wavelengths (Figs 2a and b). Under zero gate bias, the photocurrent spectrum (blue curve in Fig. 2c) reproduces a general behaviour of a linear absorption spectrum (Fig. 1b) and specifically exhibits a similar spectral onset at ~1.3 eV. Application of negative Vg leads to an overall increase in the photocurrent across the entire spectrum. The most striking effect of gate voltage, however, is the development of new spectral features at ~0.9 eV (M1S) and ~1.5 eV (MX). The fact that the M1S-band is located in the region of nominal transparency of the NC films (~0.4 eV below the 1S band-edge peak) points towards the involvement of MGB states. Further, as MGB states only manifest under negative bias, this suggests that at Vg≥0 they are fully occupied with electrons. However, some of these states become depopulated under negative Vg, when the Fermi level shifts below the MGB edge. The introduction of holes into the mid-gap states unblocks optical transitions from the valence-band to the MGB levels (solid arrows in Fig. 3a). The M1S feature is likely associated with the transition involving the 1Sh valence-band state, whereas the MX peak is probably due to some lower-lying level (labelled Xh in Fig. 3a). Because of mirror symmetry between the valence and the conduction bands in PbS28,29, the band-to-band Xh–Xe optical transition is expected to be located ~1.2 eV to the blue from the 1S peak, which is twice the M1S–MX separation (~0.6 eV). Indeed, the second derivative of the absorption spectrum of the solution sample (inset of Fig. 2b) shows a pronounced feature at ~2.5 eV, which is ~1.2 eV higher than the band-edge peak. More examples that illustrate the development of extra MGB-related spectral features in the photocurrent under negative Vg are given in Supplementary Figure S1.
In the case of a fully or partially occupied MGB, one might also expect to see the transitions that promote the MGB electrons into the unoccupied conduction-band states (red-dashed arrows in Fig. 3a). Although such transitions may indeed exist, their relative contribution to the photocurrent is much smaller than that due to the M1S and MX features because, as discussed in detail below, the electron lifetimes in these structures are much shorter than the hole lifetimes due to a higher probability of electron capture at the MGB states.
The observed spectral features due to the MGB are wider (~0.5 eV) than the 1S absorption peak (~0.2 eV). This difference is likely due to the fact that in addition to NC size-polydispersity, random NC-to-NC differences in the positions of the mid-gap levels and a systematic variation in the local Fermi level in the NC channel along the source–drain direction also contribute to the linewidths of the M1S and MX bands.
An interesting feature of the photocurrent spectra recorded under negative gate bias is the large amplitude of the MGB-related bands, which is comparable to that of the features due to intrinsic band-edge transitions. This is somewhat surprising given that the oscillator strength of the intrinsic NC transitions is expected to be stronger than for transitions involving surface-related MGB states that have a reduced spatial overlap with the wave functions of the quantized levels. However, in addition to the oscillator strength, the contribution of a given optical transition to photocurrent depends on the relative fraction of photogenerated electron-hole pairs that experience spatial separation (characteristic time τsep) before recombination compared with the fraction of charges that recombines geminately at or near the photogeneration site (characteristic time τeh). This contribution can be characterized in quantitative terms by the ratio χ=τeh/τsep, assuming that it is smaller than unity. It is natural to expect that the electron-hole pairs generated in intrinsic NC states have a shorter geminate recombination time and a longer charge-separation time compared with the electron-hole pairs produced through the MGB-related transitions, because the latter are characterized by a certain degree of spatial separation immediately following photogeneration. As a result, the transitions involving the MGB, although, perhaps, not as pronounced in optical absorption spectra, can still provide a significant contribution to photocurrent due to the enhanced value of χ compared with transitions involving the quantized states.
The films fabricated from as-prepared NCs do not show any gating effect. This implies that the mid-gap states are likely introduced by ligand-exchange procedures, which further suggests that these states are possibly of surface origin. The MGB has a role of charge conduit under dark and its conductivity is controlled by gate bias. The MGB can be either insulating (if it is completely filled or empty) or conductive (if filled partially). In the latter case, transport through MGB can be explained in terms of either electron or hole conductivity depending on whether the Fermi level is near the bottom or the top of the MGB, respectively. This might explain the possibility of facile switching the conductivity of NC films between n- and p-type through relatively simple chemical or heat treatments7,8,9,10,11,30. In our films, under the flat-band condition, the Fermi level is located near the top of the MGB, and therefore, at Vg=0 this band is essentially nonconductive. Application of negative gate bias shifts Fermi level deeper inside the MGB, which generates an increasing amount of MGB holes and results in a sharp increase of dark conductivity observed in Figure 1c.
While in dark, MGB serves as a charge conduit, its role is different in the case of photoconduction. Specifically, our observation of a dramatic enhancement of Isd under illumination suggests that transport of photogenerated charges is mediated by intrinsic quantum-confined NC states that form a more conductive network, because of a greater extent of overlapping electronic wave functions compared with surface-related MGB states. The fact that, even in this case, channel conductance is sensitive to changes in gate voltage can be explained by the effect of MGB occupancy on recombination dynamics of band-edge carriers, as elaborated in the Discussion section.
According to our earlier estimations, the densities of photogenerated charges (n and p for electrons and holes, respectively) are much smaller than 1 per NC, while the density of mid-gap states (N0) is at least on the order of 1 because they form a percolated conductive network. Because p, n≪N0, the relaxation of photogenerated carriers is dominated not by band-to-band recombination but trapping at the mid-gap levels. From charge neutrality, the density of non-equilibrium electrons in the MGB under photoexcitation is nm=p−n. Alternatively, the effect of photoexcitation on occupancy of MGB states can be characterized in terms of photogenerated holes with density pm=n−p. Under steady state, the trapping rates are equal to the photogeneration rate:
where α and β are electron- and hole-capture coefficients, respectively.
When MGB is completely empty (n0=0), equations (1) and (2) yield n~G/(αN0) and βp2~G(1+βα−1p/N0); these expressions are obtained assuming that p, n≪N0. As we show below, in our structures β≪α, therefore, p~(G/β)1/2, and consequently, n can be expressed as n~p(p/N0)(β/α). The latter relationship suggests that n≪p, and therefore, nm~p. In this case, photoconduction is dominated by holes and the photoconductivity can be expressed as σph,h=eμhnNCp=eμhnNC(G/β)1/2, where μh is hole mobility and nNC is the density of NCs in the film. As MGB gets filled, the contribution from holes to photoconduction decreases whereas the contribution from electrons increases until the latter reaches the value of σph,e=eμenNCn=eμenNC(G/α)1/2 (μe is electron mobility) when the MGB is completely full (n0=N0). The above two limits describe the situations of, respectively, large negative and flat-band gate biases, when the Fermi level is either below or above the MGB (Fig. 3a).
Because of symmetry between the conduction and valence bands in PbS28,29, μe and μh in our films are likely similar (μh~μe=μ). Therefore, if the electron- and hole-capture probabilities were the same, the filling of the MGB would not lead to changes in total photoconductivity, σph=σph,e+σph,h, as the decrease in σph,h would be compensated by the increase in σph,e. However, our experimental data (Figs 1c and 3b) indicate a decrease in the photoconductivity by a factor (ξ) of ca 20 to 50 as Vg changes from large negative values to the flat-band voltage. This implies that the electrons provide a smaller contribution to photoconduction than holes and, further, suggests that α is much greater than β. Specifically, in the limits of empty and full MGB, the total photoconductivity can be expressed as σph(empty)~σph,h=eμnNC(G/β)1/2 and σph(full)=e μ nNC(G/α)1/2+σph,h(full), respectively, which yields the ratio ξ=eμnNC(G/β)1/2/[eμnNC(G/α)1/2+σph,h(full)]. From this expression, we obtain (α/β)1/2=ξ[1+σph,h(full) (eμnNC)−1(α/G)−1/2], which suggests that (α/β)1/2>ξ. On the basis of the measured ratio of the photocurrents (Fig. 3b), we can conclude that α is at least 400 times greater than β. This result indicates that band-edge electrons in our films are much shorter lived than holes (α ≫β) and therefore provide a smaller contribution to the photocurrent. This is probably because of close proximity of the MGB to the conduction band (~0.4 eV versus ~0.9 eV separation from the valence band), which makes trapping through multiphonon emission easier for electrons than for holes31.
To quantify the relative contributions of band-edge electrons and holes to photoconduction, we solve equations (1) and (2) for the situation when the density of MGB equilibrium charges is much greater than the density of photogenerated carriers (n0≫nm and N0–n0≫nm), and hence, the dynamics of both electrons and holes are controlled by the equilibrium occupancy of the MGB. In this case, σph is
where u=β/α ≪ 1 and x=n0/N0. Equation (3) indicates a linear dependence of σph on G and it approximates the behaviour of σph between the limits of almost complete filling and almost complete depletion of the MGB. The first and the second terms in the right-hand side of equation (3) correspond, respectively, to electron and hole contributions. In Figure 3c, we compare them for β/α=0.002 (black dashed and red dashed-and-dotted lines for holes and electrons, respectively). Interestingly, up to near-unity values of x, the photoconductivity is dominated by valence-band holes and even for x=0.95, the hole contribution to σph is more than 20 times greater than that of electrons. This is a direct result of a high capture probability for electrons that quickly relax from the band-edge states into the low-mobility MGB. The short electron lifetime also explains why optical transitions, where MGB electrons are promoted to the conduction band (M'1S and M'X transitions in Fig. 3a; red dashed arrows), are not prominent in the photocurrent. The dominant role of hole photoconduction in our devices helps also to rationalize the overall Vg-dependent trends observed in the photocurrent spectra (Fig. 2c), namely the increase in Isd when Vg changes from positive to progressively more negative values. This behaviour reflects the change in the lifetime of photogenerated holes, which becomes progressively longer as MGB gets more depleted of electrons under increasing negative gate bias.
Assuming hole-dominated photoconductance, from equations (1) and (2), we can obtain the following expression for σph, which in addition to the regime described by equation (3) also allows us to treat the transition to a completely depleted MGB, that is, the range of x from 1 – ɛ to 0 (ɛ is a small quantity defined by the condition N0–n0≫nm or ɛ≫nm/N0):
We further use this expression (the corresponding dependence is shown by the blue solid line in Fig. 3c) to model the measured Vg-dependence of photocurrent for different excitation intensities (lines in Fig. 3b). In our modelling, we relate n0 to N0 and Vg by
where kB is the Boltzmann constant, T is the temperature, and EF=γ(Vg−V0) is the Fermi energy (γ is the dimensionless constant and V0 is the flat-band voltage). Equation (5) correctly predicts that under the flat-band condition (Vg=V0), n0=N0, which corresponds to a fully occupied MGB, and n0 exponentially decreases for progressively more negative gate voltages. Using equations (4) and (5), we can accurately describe both the gate-voltage and the illumination-intensity dependence of the measured photocurrent (Fig. 3b; compare calculations shown by lines with measurements shown by symbols). This confirms the validity of our model and provides an extra piece of evidence that photoconduction in our structures is dominated by valence-band holes.
An interesting prediction of equation (4) is that in addition to the magnitude of photoconductivity, the type of light-intensity-dependence of photoconduction can also be controlled by n0, and, hence, gate voltage. For example, in the regime of a depleted MGB, when n0≪2(G/β)1/2, which realized in our devices for large negative Vg, the band-edge electrons quickly relax into the mid-gap states and hole dynamics are dominated by bimolecular recombination with these non-equilibrium MGB electrons. This results in a square-root dependence of σph on G: σph,h=eμhnNC(G/β)1/2. However, as MGB becomes occupied with even a moderate number of electrons (n0≫2(G/β)1/2), the hole dynamics are dominated by recombination with 'pre-existing' MGB electrons, which leads to a linear dependence of σph on G: σph,h=eμhnNCG/(βn0).
Our data indeed indicate an approximately square-root scaling of the photocurrent with G for large negative Vg (Fig. 3d; open red circles). We also observe that the σph versus G dependence becomes progressively steeper as Vg gets less negative, and the number of MGB electrons increases (compare data shown by solid black squares and open green triangles in Figure 3d; see also Supplementary Fig. S2 for a different device, which shows a similar change in the scaling of photocurrent with light intensity). This behaviour is consistent with the predicted transition to the linear scaling described by equation (4).
The demonstrated control of recombination dynamics by gate voltage is useful in photodetection, where it can be employed for controlling both device sensitivity and its dynamic range. A significant increase in device sensitivity can be obtained by combining contributions from photoconductive and photovoltaic effects. This is illustrated in Figure 4 (inset) where we compare a purely photoconductive response measured at Vg=Vgmin (the photocurrent minimum) with one obtained for Vg=0; the latter signal exhibits a much faster growth with G due to a photovoltaic contribution. The enhancement in sensitivity arising from the photovoltaic effect is also pronounced in the spectral dependence of a photoresponse (main panel of Fig. 4; compare traces shown by solid and dashed lines).
The observed difference in hole and electron relaxation times results in a peculiar, mixed character of photoconduction, when holes are transported through quantized states whereas electrons through the MGB. One implication of this transport mechanism is that the photovoltage, which can be derived from such a structure, is determined by the energy difference between the valence-band edge and the MGB. As a result, while displaying correlation with the band-gap energy it should be always lower than the ideal Voc calculated for a given Eg. This trend has indeed been observed in NC solar cells13,14,15,17,27,32,33 (Supplementary Fig. S3).
To summarize, we have investigated OFETs fabricated from PbS NCs. Spectrally resolved studies of Vg-dependent photocurrent reveal the existence of mid-gap states in NCs films that form a weakly conducting MGB. This band serves as a charge conduit in dark, however, the mechanism of charge transport changes under illumination when it becomes dominated by a more conductive network of quantized band-edge states. In this case, the MGB still has an important role as its occupancy controls photoconduction by controlling recombination dynamics of band-edge charges. The mechanisms for 'dark' and 'light' transport are schematically illustrated in Figure 5. The results of our studies together with the developed model should help one to predictably engineer both charge transport properties of NC films in dark as well as under illumination. Interesting opportunities could also be opened by engineered placement of MGB states within the NC energy gap. This could allow, for example, switching between electron- and hole-dominated photoconductivity and, perhaps, help in practical realization of advanced photovoltaic concepts such as intermediate-band solar cells34.
PbS NCs with a mean diameter of ca 3.3 nm, were synthesized according to ref. 35 (see transmission electron micrograph in the inset of Fig. 1b). The NC dispersion was cleaned by repeatedly precipitating and re-dispersing in toluene to remove excess reactants. PbS NCs were then ligand exchanged with oleylamine33, and after removal of excess oleylamine, were re-dispersed in octane. The purified NC colloidal suspension in octane was spin-coated onto a doped silicon/silicon-oxide substrate (the oxide layer thickness was ca 100 nm), which served as a gate electrode. This was followed by film treatment with 0.1 M of 1,2-ethanedithiol solution in acetonitrile14, and a new spin coating step with the PbS NC suspension and the treatment with 1,2-ethanedithiol. The final thickness of the NC film was ~40 nm, as evaluated from atomic force microscopy measurements. Interdigitated source and drain gold electrodes (50 μm separation) were deposited directly on top of the NC film using a shadow mask.
Three-terminal device measurements were conducted using a semiconductor device analyser (B1500A, Agilent Technologies). A constant bias of −25 V was applied between the source and the drain electrodes, while the gate-source bias was varied from 10 to −25 V. In the measurements of the Isd versus Vg dependences, we ramped the gate voltage in 1 V increments using three different integration times: tint=640 μs, 16.6 ms, and 267 ms. The measured photocurrent did not vary by more than 5–10% between different values of tint. We also did not detect any difference in traces recorded by ramping the gate either up or down.
The light from xenon or tungsten lamps, filtered through a monochromator (~10 nm bandwidth) was used to illuminate the OFET from the top, whereas the photocurrent was monitored as a function of either monochromatic light intensity or incident radiation wavelength. The maximum light intensity incident onto the device was 50 μW cm−2.
Density of charges injected by applying gate voltage
We derive the density of charges injected into the channel of the NC–OFET from 'dark' capacitance measurements. The total charge injected for a given gate voltage was calculated from , which yields Q=1.82 μC cm−2 for Vg=−25 V. Assuming that, in our devices, NCs form a random close-packed solid, we estimate that the NC surface density per monolayer is ~1013 cm−2, which indicates that the average number of charges injected per NC for Vg=−25 is ~0.1, assuming that the NC film is ~10-monolayers thick.
Density of photogenerated charges
Using absorption cross section (σabs) of 10−15 cm−2 (ref. 36) and fluxes (W) from 5 to 50 μW cm−2, we calculate the photogeneration rate, G=(W/ħω)σabs, from 10−4 to 10−6 ms−1 (ħω is photon energy). The lifetime of carriers in our devices (τ) is 0.01–1 ms. On the basis of these values, an upper limit of the density of photogenerated charges, n=p=Gτ, is 10−4 per NC.
How to cite this article: Nagpal, P. & Klimov, V.I. Role of mid-gap states in charge transport and photoconductivity in semiconductor nanocrystal films. Nat. Commun. 2:486 doi: 10.1038/ncomms1492 (2011).
Murray, C. B., Norris, D. J. & Bawendi, M. G. Synthesis and characterization of nearly monodisperse CdE (E=S, Se, Te) semiconductor nanocrystallites. J. Am. Chem. Soc. 115, 8706–8715 (1993).
Mangolini, L., Thimsen, E. & Kortshagen, U. High-yield plasma synthesis of luminescent silicon nanocrystals. Nano Lett. 5, 655–659 (2005).
Coe, S., Woo, W. K., Bawendi, M. & Bulovic, V. Electroluminescence from single monolayers of nanocrystals in molecular organic devices. Nature 420, 800–803 (2002).
Mueller, A. H. et al. Multicolor light-emitting diodes based on semiconductor nanocrystals encapsulated in GaN charge injection layers. Nano Lett. 5, 1039–1044 (2005).
Cho, K. S. et al. High-performance crosslinked colloidal quantum-dot light-emitting diodes. Nat. Photon. 3, 341–345 (2009).
Holman, Z. C., Liu, C. Y. & Kortshagen, U. R. Germanium and silicon nanocrystal thin-film field-effect transistors from solution. Nano Lett. 10, 2661–2666 (2010).
Kang, M. S., Lee, J., Norris, D. J. & Frisbie, C. D. High carrier densities achieved at low voltages in ambipolar PbSe nanocrystal thin-film transistors. Nano Lett. 9, 3848–3852 (2009).
Mentzel, T. S. et al. Charge transport in PbSe nanocrystal arrays. Phys. Rev. B 77, 075316 (2008).
Talapin, D. V. & Murray, C. B. PbSe nanocrystal solids for n- and p-channel thin film field-effect transistors. Science 310, 86–89 (2005).
Liu, Y. et al. Dependence of carrier mobility on nanocrystal size and ligand length in PbSe nanocrystal solids. Nano Lett. 10, 1960–1969 (2010).
Luther, J. M. et al. Structural, optical and electrical properties of self-assembled films of PbSe nanocrystals treated with 1,2-ethanedithiol. ACS Nano 2, 271–280 (2008).
Konstantatos, G. et al. Ultrasensitive solution-cast quantum dot photodetectors. Nature 442, 180–183 (2006).
Gur, I., Fromer, N. A., Geier, M. L. & Alivisatos, A. P. Air-stable all-inorganic nanocrystal solar cells processed from solution. Science 310, 462–465 (2005).
Luther, J. M. et al. Schottky solar cells based on colloidal nanocrystal films. Nano Lett. 8, 3488–3492 (2008).
Pattantyus-Abraham, A. G. et al. Depleted-heterojunction colloidal quantum dot solar cells. ACS Nano 4, 3374–3380 (2010).
Kamat, P. V. Quantum dot solar cells. semiconductor nanocrystals as light harvesters. J. Phys. Chem. C 112, 18737–18753 (2008).
Sun, B., Findikoglu, A. T., Sykora, M., Werder, D. J. & Klimov, V. I. Hybrid photovoltaics based on semiconductor nanocrystals and amorphous silicon. Nano Lett. 9, 1235–1241 (2009).
Sun, B. Q., Marx, E. & Greenham, N. C. Photovoltaic devices using blends of branched CdSe nanoparticles and conjugated polymers. Nano Lett. 3, 961–963 (2003).
Nanocrystal Quantum Dots 2nd edn (ed. Klimov, V. I.) (CRC Press, Taylor & Francis Group, Boca Raton, 2010).
Nozik, A. J. Quantum dot solar cells. Physica E 14, 115–120 (2002).
Schaller, R. D. & Klimov, V. I. High efficiency carrier multiplication in PbSe nanocrystals: Implications for solar energy conversion. Phys. Rev. Lett. 92, 186601 (2004).
Ellingson, R. J. et al. Highly efficient multiple exciton generation in colloidal PbSe and PbS quantum dots. Nano Lett. 5, 865–871 (2005).
Sukhovatkin, V., Hinds, S., Brzozowski, L. & Sargent, E. H. Colloidal quantum-dot photodetectors exploiting multiexciton generation. Science 324, 1542–1544 (2009).
Sambur, J. B., Novet, T. & Parkinson, B. A. Multiple exciton collection in a sensitized photovoltaic system. Science 330, 63–66 (2010).
Ross, R. T. & Nozik, A. J. Efficiency of hot-carrier solar-energy converters. J. Appl. Phys. 53, 3813–3818 (1982).
Tisdale, W. A. et al. Hot-electron transfer from semiconductor nanocrystals. Science 328, 1543–1547 (2010).
Talapin, D. V., Lee, J. S., Kovalenko, M. V. & Shevchenko, E. V. Prospects of colloidal nanocrystals for electronic and optoelectronic applications. Chem. Rev. 110, 389–458 (2010).
Kang, I. & Wise, F. W. Electronic structure and optical properties of PbS and PbSe quantum dots. J. Opt. Soc. Am. B Opt. Phys. 14, 1632–1646 (1997).
Bartnik, A. C., Efros, A. L., Koh, W. K., Murray, C. B. & Wise, F. W. Electronic states and optical properties of PbSe nanorods and nanowires. Phys. Rev. B 82, 195313 (2010).
Law, M. et al. Structural, optical, and electrical properties of PbSe nanocrystal solids treated thermally or with simple amines. J. Am. Chem. Soc. 130,5974–5985 (2008).
Ridley, B. K. Quantum Processes in Semiconductors Second edn, (Oxford Science Publications, 1988).
Luther, J. M. et al. Stability assessment on a 3% bilayer PbS/ZnO quantum dot heterojunction solar cell. Adv. Mater. 22, 3704–3707 (2010).
Tang, J. et al. Quantum dot photovoltaics in the extreme quantum confinement regime: the surface-chemical origins of exceptional air- and light-stability. ACS Nano 4, 869–878 (2010).
Marti, A. & Luque, A. Next Generation Photovoltaics: High Efficiency through Full Spectrum Utilization (Institute of Physics, 2003).
Hines, M. A. & Scholes, G. D. Colloidal PbS nanocrystals with size-tunable near-infrared emission: Observation of post-synthesis self-narrowing of the particle size distribution. Adv. Mater. 15, 1844–1849 (2003).
Moreels, I. et al. Size-dependent optical properties of colloidal PbS quantum dots. ACS Nano 3, 3023–3030 (2009).
We thank Don Werder for assistance with transmission electron microscopy, Bhola Pal for help with transient photocurrent data, and Jeff Pietryga and Lazaro Padilha for insightful comments regarding the manuscript. This material is based on work within the Center for Advanced Solar Photophysics, an Energy Frontier Research Center funded by the U.S. Department of Energy, Office of Science, Office of Basic Energy Sciences.
The authors declare no competing financial interests.
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Nagpal, P., Klimov, V. Role of mid-gap states in charge transport and photoconductivity in semiconductor nanocrystal films. Nat Commun 2, 486 (2011). https://doi.org/10.1038/ncomms1492
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