Home  ›  Easy Insight Into Spacecharge Effects on Steadystate Transport in Oxide Films

Easy Insight Into Spacecharge Effects on Steadystate Transport in Oxide Films

Written By Wednesday, August 31, 2022 Add Comment Edit

Abstract

Hybrid organic-inorganic perovskites are promising materials for the application in solar cells and light-emitting diodes. However, the basic current-voltage behavior for electrons and holes is still poorly understood in these semiconductors due to their mixed electronic-ionic character. Here, we present the analysis of space-charge-limited electron and hole currents in the archetypical perovskite methyl ammonium lead iodide (MAPbI3). We demonstrate that the frequency dependence of the permittivity plays a crucial role in the analysis of space-charge-limited currents and their dependence on voltage scan rate and temperature. Using a mixed electronic-ionic device model based on experimentally determined parameters, the current-voltage characteristics of single-carrier devices are accurately reproduced. Our results reveal that in our solution processed MAPbI3 thin films transport of electrons dominates over holes. Furthermore, we show that the direction of the hysteresis in the current-voltage characteristics provides a fingerprint for the sign of the dominant moving ionic species.

Introduction

Hybrid organic–inorganic perovskites have emerged as promising semiconducting materials over recent years1,2. Especially in optoelectronic devices, such as solar cells1,2, light-emitting diodes3,4, lasers5,6, and photodetectors7,8,9, perovskites show great potential. However, understanding the device physics of perovskite-based devices has proven not to be straightforward, which can mainly be traced back to the mixed ionic–electronic conduction behavior of these materials10,11,12,13,14,15,16,17,18. One particularly important aspect in understanding the behavior of perovskite-based electronic devices is the characterization of the transport of electronic charges. Over recent years, many techniques have been employed to measure the charge-carrier mobility in perovskites19,20,21,22,23,24,25,26,27,28,29,30, giving a vast range of different numbers31,32. The large differences observed in the measured charge-carrier mobility may, in part, be the result of different perovskite formulations and processing conditions, resulting in different film morphologies. However, also experimental techniques to measure the mobility can give rise to different values31,32. For instance, time-resolved techniques may only probe fast charge carriers within crystal grains, whereas the slower transport of charges across grain boundaries and those affected by defect sites may be disregarded in the measurements. Such slower charge carriers may considerably impact the device performance.

A powerful technique that has proven its value in determining the time-averaged steady-state mobility of organic semiconductors is the measurement of space-charge-limited currents (SCLCs)33,34. SCLCs are observed in so-called electron- and hole-only devices, in which, by careful choice of the electrodes, either only electrons or holes are injected into the semiconductor. The maximum electrostatically allowed current in such a device is limited by the buildup of space charge. The space-charge density depends on the permittivity of the semiconductor, similar to a parallel-plate capacitor. The current will then be determined by the conductivity, being a product of the space-charge density and the charge-carrier mobility. In perovskites, classical SCLC theory has been used previously to estimate the density of defects, or trapping sites, from measured current–voltage characteristics19. An important feature in the SCLC model is that the electric field resulting from the injected space charge exhibits a square-root dependence on distance from the injecting contact. However, it is well established that ion movement plays an important role in the shape, magnitude, and hysteresis of the current–voltage characteristics of perovskite solar cells14,17,35,36,37. As slow-moving ions modify the electric-field distribution in the device as a function of time, it is evident that classical SCLC models are not applicable to mixed ionic–electronic semiconductors, such as perovskites. The ion dynamics and resulting field distributions will strongly affect the current–voltage characteristics in single-carrier devices, greatly complicating their analysis. Application of the SCLC model disregarding the effects of ions on permittivity and field distribution then leads to erroneous results regarding charge-carrier mobility and trapping sites. Although there are numerous publications on SCLC measurements of perovskite single crystals and thin films, the effect of mobile ions, permittivity, and temperature on the current–voltage behavior are missing7,19,38,39,40,41,42,43,44,45,46,47,48,49,50,51,52,53,54. To date, an accurate description of SCLCs in perovskite thin films does not exist. In this study, we investigate SCLCs in single-carrier devices of methylammonium lead iodide (MAPbI3), the work-horse material in perovskite solar-cell research. As a central result, it is demonstrated that the frequency and temperature dependence of the apparent dielectric constant is of paramount importance in understanding the magnitude, the scan-rate dependence, and temperature dependence of SCLCs in perovskites. We develop a drift-diffusion model, including experimentally validated ion dynamics that can consistently reproduce the scan-rate dependence and temperature dependence of the current–voltage characteristics of electron-only and hole-only devices. The quantitative agreement allows for reliable determination of the electron and hole mobility from SCLC measurements on MAPbI3 thin films. It is also demonstrated that the direction of the hysteresis in the electron and hole currents reveals the sign of the dominant mobile ionic species.

Results

Analysis of the relative permittivity

In the analysis of the current–voltage characteristics of MAPbI3 perovskite solar cells in literature thus far, the dielectric constant (ε) was assumed to be frequency independent, having constant values typically ranging from 6 to 1177,19,35,37,38,39,40,41,42,43,44,46,48,49,50,51,53,54,55,56,57,58,59. Also for other perovskites, the relative permittivity in the SCLC analysis was taken to be constant7,19,38,39,40,42,43,44,46,48,49,50,51,53,54,58,59. In Fig. 1, the frequency dependence of the dielectric constant is displayed, as obtained by impedance spectroscopy on MAPbI3 capacitors. The relative permittivity is observed to be rather constant for frequencies above 100 Hz, having a value of 65, much higher than that used in most device-modeling studies but consistent with earlier results60. However, at lower frequencies, the dielectric constant increases considerably, up to two orders of magnitude higher. This apparent high dielectric constant at low frequencies is the result of slow-moving ions18. As stated above, the dielectric constant has a direct influence on the magnitude of the SCLC, as it determines the amount of space charge that builds up in the semiconductor layer.

Fig. 1: The apparent dielectric constant of a MAPbI3 thin film.
figure 1

a As a function of frequency, obtained by impedance spectroscopy (black solid line). The red stars correspond to the apparent dielectric constant at the voltage scan rates used in the simulations (Sim values) in Fig. 3. b Temperature dependence of the apparent dielectric constant (red filled stars) at 0.0575 Hz (dashed line in Supplementary Fig. 1), corresponding to the scan rate of the temperature-dependent J–V measurements in Figs. 2 and 4. c Ion diffusion coefficient as a function of temperature, obtained from impedance spectroscopy (red circles). The measurements are fitted with an Arrhenius law with an activation energy of 0.42 eV (black line). The blue stars represent the ion diffusion coefficients used in the simulations.

Full size image

Characterization of electron- and hole-only devices

To measure space-charge-limited electron and hole currents, we have fabricated electron- and hole-only devices, as displayed in Fig. 2. To optimize electron injection, a thin (5 nm) C60 layer was used, capped with a 5 nm 1,3,5-tris(1-phenyl-1H-benzimidazol-2-yl)benzene (TPBi) buffer layer61,62. The corresponding current density–voltage characteristics are displayed in Fig. 2c, d. The electron-only device shows asymmetric current–voltage characteristics, which is due to the electron-injection barrier at the Ag bottom electrode (see also Supplementary Fig. 4), resulting in a lower, injection-limited current in reverse bias. The hole-only device displays almost symmetric J–V characteristics. The hole current is observed to be lower than the electron current. We note that we observed this behavior for many similarly prepared samples over the course of several years.

Fig. 2: Schematic device structure and current density–voltage characteristics.
figure 2

a Electron-only device, using a C60(5 nm)/TPBi(5 nm)/Al electron-injection layer. Due to the barrier at the Ag bottom electrode, the current in reverse bias is injection limited. The dark cyan symbols represent the electron current measured at room temperature, with a scan rate of 0.46 V s−1. The red solid line shows the simulated electron current using the electronic-ionic drift-diffusion model with an apparent dielectric constant of 5700. b Schematic of the hole-only device, using Au bottom and top electrodes. The symbols and solid line represent the measured and simulated hole current, respectively, under the same conditions as the electron current (a).

Full size image

When measuring a SCLC in a single-carrier device, the scan rate is typically low (0.1 V s−1 to 1 V s−1). As a result, slow-moving ions can follow the changes in applied voltage, leading to small hysteresis in the measured current–voltage characteristics. This is shown for electron- and hole-only devices of MAPbI3 in Fig. 2. Considering the slow scan rate of 0.46 V s−1, the question arises which value should be taken for the dielectric constant in the SCLC analysis. Another important factor in the analysis is the influence of the moving ions on the electric-field distribution in the device, and thus the current. In many device-modeling studies, the ion diffusivity and concentration are not known, and literature values are taken, compromising the analysis. The situation is even more complicated when modeling complete solar cells including charge-transport layers, as the electron and hole mobility of all materials, the recombination rate, and possible charge-trapping effects are also not known accurately. By using all of these quantities as fit parameters, a reasonable agreement with experiment may be obtained, although a reliable analysis is near impossible without experimentally validating the input parameters in the model. Therefore, we have recently determined the ion diffusion coefficient (1 × 10−15 m2 s−1; Fig. 1) and ion concentration (2 × 1025 m−3) in similarly prepared MAPbI3 films, verified by using two independent techniques18. These techniques involved the analysis of impedance spectroscopy with a simple equivalent circuit for ionic conductors and measurement of the electric displacement as a function of frequency, which could be reproduced with a mixed ionic–electronic drift-diffusion model. It was demonstrated that the movement of ions completely dominates the displacement characteristics. Furthermore, it was observed that the drift-diffusion model could only reproduce the displacement characteristics when a frequency-dependent permittivity was used, as displayed in Fig. 1a. In the analysis, it was assumed that positive ions are mobile and negative ions are fixed18, based on previous studies. Likely candidates for the mobile positive ions are methylammonium ions or iodine vacancies15,37,63.

As we have characterized the dielectric constant, ion diffusivity, and ion concentration experimentally, we can now fit the current–voltage characteristics of our single-carrier devices by tuning only the charge-carrier mobility. In this case, we have used an apparent relative dielectric constant of 5700, as measured at a frequency of 0.0575 Hz. This frequency corresponds to the voltage scan rate of the J–V measurements, \(f = \frac{{\mathrm{{Scan}}\,{\mathrm{{rate}}}}}{{4 \times V_{\mathrm{m}}}}\), where V m is the amplitude of the applied voltage (see Supplementary Fig. 2). We obtain a mobility of 1.2 × 10−6 m2 V−1 s−1 for electrons and 3.5 × 10−10 m2 V−1 s−1 for holes. We note that our extracted mobilities are comparable to values obtained by electrode-based mobility measurement techniques31,40,43,64,65 and lower than the ones obtained by electrode-free techniques27,28,31. We note that the large variation in reported mobilities is likely the result of differences in sample morphologies, measurement techniques (e.g., different timescales), and their interpretation. For instance, as demonstrated here, classical SCLC analysis is not applicable to semiconductors with mobile ions. We further note that similarly low hole mobilities have been reported in MAPbI3 field-effect transistors, also being a steady-state technique66,67. As demonstrated in Supplementary Fig. 7, the solar-cell characteristics are excellently reproduced by the drift-diffusion model, using the above-determined mobilities. More extensive solar-cell simulations are the topic of a future study.

Although our electron and hole mobilities are in a range similar to earlier reported values for MAPbI3 thin films of ~\(4 \times 10^{ - 8 }\;{\mathrm{m}}^2{\mathrm{V}}^{ - 1}{\mathrm{s}}^{ - 1}\) obtained from time-of-flight measurements64, we do not find ambipolar transport, but a clearly higher mobility for electrons as compared with holes. We verified that our hole currents are not limited by a contact barrier by comparing the hole injection from Au, poly(3,4-ethylenedioxythiophene) polystyrene sulfonate (PEDOT : PSS), and polytriarylamine (PTAA) into MAPbI3 (Supplementary Fig. 5). We note that the MAPbI3 morphology and grain size is independent of the bottom electrode used (Supplementary Fig. 3). Furthermore, with the inclusion of an injection barrier in the device model the shape of the J–V characteristics cannot be reproduced. We note that we cannot fully exclude that the low hole mobility originates from the presence of shallow hole traps68, which in the classical model would give rise to an SCLC in which the mobility is replaced by an "effective mobility" defined by the product µθ. Here, µ is the mobility without shallow traps, which is reduced by a factor θ, being the fraction of free carriers with regard to the total amount of injected carriers. The effective mobility µθ can thus be considerably lower than the free charge-carrier mobility µ. In this case, the measured current has all the features of an SCLC, except that the obtained mobility represents an effective mobility. However, this does not change our conclusion that the charge transport is highly unbalanced and electron dominated. Furthermore, it should be noted that the high current in forward bias in the electron-only device is limited by the series resistance of the electrodes, despite our attempts to reduce this resistance as much as possible in the fabricated devices. Therefore, the determined electron mobility should be viewed as a lower limit.

As an SCLC is essentially determined by the product of the permittivity and the (effective) mobility, a question is whether a fit could also be obtained when assuming a lower value for the permittivity, as obtained at higher frequencies (Fig. 1). As shown in Supplementary Fig. 6, by assuming a lower value of the permittivity the shape of the J–V characteristics cannot be reproduced, irrespective of the chosen mobility.

Scan-rate dependence of the SCLC

To further confirm whether the frequency-dependent permittivity should be used in the SCLC analysis, we have performed current–voltage measurements as a function of scan rate, as displayed in Fig. 3a, c. As shown in Fig. 3b, d the scan-rate dependence of the current–voltage characteristics can only be completely reproduced by considering the frequency dependence of the permittivity for every scan rate (red stars in Fig. 1a). Although the electron current in forward bias is limited by the electrode series resistance at higher applied voltages, it is observed that the hole current in the hole-only device increases with decreasing scan rate, in accordance with the higher permittivity measured at lower frequencies. This increase cannot be reproduced by assuming a constant, scan-rate independent permittivity.

Fig. 3: Current density–voltage characteristics of single-carrier devices for different voltage scan rates.
figure 3

The measurements (symbols) for the electron-only (a) and hole-only (c) device are reproduced by the corresponding simulations (solid lines) in panel (b) and (d), respectively. The hole-only device in an Au/MAPbI3/PTAA/Au configuration shows slightly asymmetric characteristics. The simulations incorporate a scan rate-dependent dielectric constant, resulting in a correct description of both the magnitude of the current and the hysteresis behavior.

Full size image

Temperature dependence of the SCLC

The relative permittivity also controls the temperature dependence of the electron and hole currents. As displayed in Fig. 1b, the quasi-static dielectric constant at a frequency of 0.0575 Hz decreases with decreasing temperature, which is associated with a decrease in ion diffusivity, as shown in Fig. 1c. Both these quantities are determined by impedance spectroscopy on MAPbI3 capacitors. The temperature-dependent dielectric constant directly results in a temperature dependence of the SCLCs, as displayed in Fig. 4. The device simulations correctly reproduce the temperature dependence, using the measured temperature-dependent permittivity (Fig. 1b) as input, while keeping the charge-carrier mobility constant. In addition, the hysteresis behavior is also correctly reproduced by the model, using the temperature-dependent diffusivity as shown in Fig. 1c. With regard to the hole-only current at low temperatures the ions are so slow that they cannot follow the voltage scan, resulting in the absence of hysteresis. With increasing temperature the ions become more mobile and the hysteresis increases. At room temperature, the further increased ion mobility reduces the hysteresis again, since the ions are sufficiently fast to follow the applied voltage signal. The hysteresis behavior of the electron-only is more complex due to the presence of a built-in voltage. The built-in voltage leads to diffusion of ions, in this case positive ions to the exiting contact, already at zero applied bias. At low temperatures, the immobile ions stay at this contact, independent of the applied voltage, which can give rise to negative electric fields in the device and large hysteresis. The effect of ion movement on the hysteresis will be discussed in more detail below. We note that a sharp increase is present in the experimental injection-limited current in high reverse bias, especially noticeable in the electron-only devices at higher temperatures. This might be associated with field-assisted charge injection, which will be enhanced by the accumulation of ions at the contact.

Fig. 4: Temperature-dependent current density–voltage characteristics of single-carrier devices.
figure 4

The electron (a) and hole (c) currents (symbols) were measured from 295 K to 215 K at a scan rate of 0.46 V s−1. The simulations (solid lines) of the electron-only (b) and hole-only (d) device reproduce the experiments by using a temperature-dependent dielectric constant and ion diffusion coefficient, using the values as displayed in Fig. 1b, c.

Full size image

The accurate agreement between our experiments and simulations, based on experimentally determined parameters, demonstrates that the SCLC behavior in perovskites is completely governed by the temperature dependence of ion dynamics and the associated temperature and frequency-dependent permittivity. We note that temperature-dependent mobilities have been reported using different techniques, but in all cases the frequency and temperature dependence of permittivity due to ion dynamics were not taken into account in the interpretation of the data24,28,29,53,64,65,69,70,71,72. We cannot fully exclude a very small temperature dependence of the charge-carrier mobility but, if present, is fully overwhelmed by the temperature dependence of the permittivity and therefore of no relevance for the description of the SCLC.

Influence of ion motion on SCLCs

Thus far, we have assumed that only positive ions are mobile in the simulations, which excellently reproduces the direction of hysteresis in the experimental data, as displayed in Fig. 5a. Here, the arrows and numbers represent the voltage scan direction. A question is whether this assumption also has an effect on the analysis of the SCLCs. For this reason, we have also performed simulations by assuming negative ions to be mobile, but keeping all other parameters the same. As a first case, we consider the hole transport at 275 K, where the hysteresis is maximal. Strikingly, as shown in Fig. 5b, the direction of the hysteresis is reversed when assuming mobile negative ions. A similar observation is obtained for electron-only devices (Supplementary Fig. 8). Also here, only mobile positive carriers provide the correct direction of the hysteresis. We note that for the electron-only devices, we modeled experiments at higher scan rate, as the hysteresis is more pronounced in that case.

Fig. 5: Current density–voltage characteristics of a hole-only device at 275 K.
figure 5

The current density–voltage characteristics (solid lines) are simulated with the same set of parameters under two different conditions for ionic charges: mobile positive ions and a uniform density of immobile negative ions (a) and mobile negative ions and immobile positive ions (b). The corresponding energy band diagrams and ion distributions for mobile positive ions (c, e) as well as mobile negative ions (d, f) are displayed at a forward bias of 0.5 V for the up scan (blue solid lines) and down scan (red solid lines). The dashed lines in e and f indicate the average ion densities.

Full size image

To explain this behavior in more detail, the energy band diagrams of the hole-only device at an applied voltage of 0.5 V are displayed in Fig. 5c, d. Consider the example of a hole-only device with positive ions. On the up scan (from 0 to 2 V, forward bias), the positive ions will migrate in the direction of the negatively biased (right) electrode, at which the holes are extracted. As these ions move slowly, the accumulation of ions at the extracting electrode at a bias voltage of 0.5 V is still rather limited (Figs. 5a (1)), having a minor influence on the electric-field distribution across the device (Fig. 5c). However, on the down scan (Figs. 5a (2)), the positive ions have migrated further away from the positively biased electrode (Fig. 5c), resulting in positive ion depletion and an associated positive field near the hole injection electrode, enhancing the injection of holes. This results in a higher current in the down scan (Figs. 5a (2). In the case of negative ions, the ions migrate toward the positively biased, hole injecting electrode, where they screen the applied field (Fig. 5b (1)). Also in this case, the ions are distributed relatively uniformly on the up scan (Fig. 5d), whereas the field screening limits hole injection on the down scan and, in turn, a decreased hole current is observed (Fig. 5b (2)). The corresponding electric field, hole, and ion concentration profiles for both cases are shown in Supplementary Figs. 9 and 10, respectively. As a result, the direction of the hysteresis in MAPbI3 single-carrier devices directly reveals the sign of the moving ionic species.

Discussion

In conclusion, we have demonstrated the importance of temperature-dependent ion dynamics and a temperature- and frequency-dependent apparent dielectric constant on the analysis of SCLCs in hybrid organic–inorganic perovskites. We have developed a device model that can reproduce the scan-rate and temperature-dependent current–voltage characteristics with only experimentally validated parameters as input. The sign of the dominant mobile ionic species can be determined from the direction of the hysteresis in electron- and hole-only devices. The basic understanding of electron and hole currents in perovskite layers is an important step in the direction of unraveling the device physics of perovskite solar cells and light-emitting diodes, in which charge recombination is an additional factor that needs to be taken into account. Only by successive experimental validation of separate factors, such as ion dynamics and charge transport, perovskite device models can be built up with increasing complexity, containing a large body of input variables.

Methods

Device fabrication

For fabricating electron-only (hole-only) devices, layers of Cr/Ag (Cr/Au) (1 nm/60 nm) was deposited as the bottom contact on a glass substrate by thermal evaporation in high vacuum. For Au/PTAA/MAPbI3/Au hole-only devices, a thin layer (10 nm) of PTAA was spin coated from a solution of PTAA in toluene (2 mg/mL) on the bottom Au electrode. A 30 wt.% solution of Methylammonium iodide and lead acetate trigydrate (PbAc2) with a molar ratio of 3:1 in N,N-dimethylformamide was prepared and spin coated on the substrate inside a nitrogen-filled glovebox12. The MAPbI3 films were annealed at 100 °C for 30 min on a hot plate. The hole-only devices were finished by thermally evaporating a layer of Au (60 nm) as top electrode. For electron-only devices, 5 nm of C60 and 5 nm of TPBi were thermally evaporated to achieve efficient electron injection into the MAPbI3 layer. On top of that, a capping layer of Al (100 nm) was deposited by thermal evaporation. The area of the devices was 1 mm2.

Characterization

Impedance measurements were performed using a computer-controlled Solartron impedance analyzer. The current–voltage measurements were carried out using a Keithley 2400 source meter. The scan-rate-dependent measurements were conducted using a Paios system from Fluxim. All the measurements were performed inside a nitrogen-filled glovebox.

Simulation

Device simulations were performed using an experimentally validated electronic-ionic drift-diffusion model. For solving the drift-diffusion equations coupled with Poisson's equation, a code was programmed in MATLAB. The model includes both electronic and ionic conduction. The program numerically solves the one-dimensional drift-diffusion equations for electrons, holes, and ions by forward integration over time and space. The ions are confined inside the perovskite layer by the ion-blocking contacts. The input ionic properties were experimentally quantified by impedance spectroscopy and electric displacement measurements18. For modeling the single-carrier devices, the injection barrier for the majority carriers is taken to be zero and the injection of the minority carriers was minimized by applying large injection barriers. Current–voltage calculations were conducted with the same protocol as the experimental measurements, including the voltage scan range and scan rate, as well as the temperature. The effects of the electrode series resistance on the electron-only data were included in the simulation results.

Data availability

Experimental data and simulation code are available from the corresponding author upon reasonable request.

References

  1. Kojima, A., Teshima, K., Shirai, Y. & Miyasaka, T. Organometal halide perovskites as visible-light sensitizers for photovoltaic cells. J. Am. Chem. Soc. 131, 6050–6051 (2009).

    CAS  PubMed  Google Scholar

  2. Green, M., Ho-Baillie, A. & Snaith, H. The emergence of perovskite solar cells. Nat. Photonics 8, 506–514 (2014).

    ADS  CAS  Google Scholar

  3. Tan, Z. et al. Bright light-emitting diodes based on organometal halide perovskite. Nat. Nanotechnol. 9, 687–692 (2014).

    ADS  CAS  PubMed  Google Scholar

  4. Lin, K. et al. Perovskite light-emitting diodes with external quantum efficiency exceeding 20 per cent. Nature 562, 245–248 (2018).

    ADS  CAS  PubMed  Google Scholar

  5. Zhu, H. et al. Lead halide perovskite nanowire lasers with low lasing thresholds and high quality factors. Nat. Mater. 14, 636–642 (2015).

    ADS  CAS  PubMed  Google Scholar

  6. Xing, G. et al. Low-temperature solution-processed wavelength-tunable perovskites for lasing. Nat. Mater. 13, 476–480 (2014).

    ADS  CAS  PubMed  Google Scholar

  7. Liu, Y. et al. 20‐mm‐Large single‐crystalline formamidinium‐perovskite wafer for mass production of integrated photodetectors. Adv. Opt. Mater. 4, 1829–1837 (2016).

    ADS  CAS  Google Scholar

  8. Dong, R. et al. High‐gain and low‐driving‐voltage photodetectors based on organolead triiodide perovskites. Adv. Mater. 27, 1912–1918 (2015).

    CAS  PubMed  Google Scholar

  9. Li, D., Dong, G., Li, W. & Wang, L. High performance organic-inorganic perovskite-optocoupler based on low-voltage and fast response perovskite compound photodetector. Sci. Rep. 5, 7902 (2015).

    ADS  CAS  PubMed  PubMed Central  Google Scholar

  10. Snaith, H. et al. Anomalous hysteresis in perovskite solar cells. J. Phys. Chem. Lett. 5, 1511–1515 (2014).

    CAS  PubMed  Google Scholar

  11. Frost, J. & Walsh, A. What is moving in hybrid halide perovskite solar cells? Acc. Chem. Res. 49, 528–535 (2016).

    CAS  PubMed  PubMed Central  Google Scholar

  12. Sajedi Alvar, M., Kumar, M., Blom, P., Wetzelaer, G. & Asadi, K. Absence of ferroelectricity in methylammonium lead iodide perovskite. AIP Adv. 7, 095110 (2017).

    ADS  Google Scholar

  13. Belisle, R. et al. Interpretation of inverted photocurrent transients in organic lead halide perovskite solar cells: proof of the field screening by mobile ions and determination of the space charge layer widths. Energy Environ. Sci. 10, 192–204 (2017).

    CAS  Google Scholar

  14. Tress, W. et al. Understanding the rate-dependent J–V hysteresis, slow time component, and aging in CH3NH3PbI3 perovskite solar cells: the role of a compensated electric field. Energy Environ. Sci. 8, 995–1004 (2015).

    CAS  Google Scholar

  15. Eames, C. et al. Ionic transport in hybrid lead iodide perovskite solar cells. Nat. Commun. 6, 7497 (2015).

    ADS  CAS  PubMed  PubMed Central  Google Scholar

  16. Calado, P. et al. Evidence for ion migration in hybrid perovskite solar cells with minimal hysteresis. Nat. Commun. 7, 13831 (2016).

    ADS  CAS  PubMed  PubMed Central  Google Scholar

  17. Weber, S. et al. How the formation of interfacial charge causes hysteresis in perovskite solar cells. Energy Environ. Sci. 11, 2404–2413 (2018).

    CAS  Google Scholar

  18. Sajedi Alvar, M., Blom, P. W. M., & Wetzelaer, G. ‐J. A. H. Device model for methylammonium lead iodide perovskite with experimentally validated ion dynamics. Adv. Electron. Mater. 6, 1900935 (2020).

  19. Shi, D. et al. Low trap-state density and long carrier diffusion in organolead trihalide perovskite single crystals. Science 347, 519–522 (2015).

    ADS  CAS  PubMed  Google Scholar

  20. DeQuilettes, D. et al. Photo-induced halide redistribution in organic–inorganic perovskite films. Nat. Commun. 7, 11683 (2016).

    ADS  CAS  PubMed  PubMed Central  Google Scholar

  21. Wang, K. et al. P-type mesoscopic nickel oxide/organometallic perovskite heterojunction solar cells. Sci. Rep. 4, 4756 (2015).

    Google Scholar

  22. Stranks, S. et al. Electron-hole diffusion lengths exceeding 1 micrometer in an organometal trihalide perovskite absorber. Science 342, 341–344 (2013).

    ADS  CAS  PubMed  Google Scholar

  23. Labram, J. et al. Charge transport in a two-dimensional hybrid metal halide thiocyanate compound. J. Mater. Chem. C. 5, 5930–5938 (2017).

    CAS  Google Scholar

  24. Milot, R., Eperon, G., Snaith, H., Johnston, M. & Herz, L. Temperature‐dependent charge‐carrier dynamics in CH3NH3PbI3 perovskite thin films. Adv. Funct. Mater. 25, 6218–6227 (2015).

    CAS  Google Scholar

  25. Leijtens, T. et al. Mapping electric field‐induced switchable poling and structural degradation in hybrid lead halide perovskite. Thin Films. Adv. Energy Mater. 5, 1500962 (2015).

    Google Scholar

  26. Takahashi, Y., Hasegawa, H., Takahashi, Y. & Inabe, T. Hall mobility in tin iodide perovskite CH3NH3SnI3: evidence for a doped semiconductor. J. Solid State Chem. 205, 39–43 (2013).

    ADS  CAS  Google Scholar

  27. Lim, J. et al. Elucidating the long-range charge carrier mobility in metal halide perovskite thin films. Energy Environ. Sci. 12, 169–176 (2019).

    CAS  Google Scholar

  28. Biewald, A. et al. Temperature-dependent ambipolar charge carrier mobility in large-crystal hybrid halide perovskite thin films. ACS Appl. Mater. interfaces 11, 20838–20844 (2019).

    CAS  PubMed  Google Scholar

  29. Yi, H. T., Wu, X., Zhu, X. & Podzorov, V. Intrinsic charge transport across phase transitions in hybrid organo‐inorganic perovskites. Adv. Mater. 28, 6509–6514 (2016).

    CAS  PubMed  Google Scholar

  30. Shrestha, S. et al. High-performance direct conversion X-ray detectors based on sintered hybrid lead triiodide perovskite wafers. Nat. Photon 11, 436–440 (2017).

    ADS  CAS  Google Scholar

  31. Peng, J., Chen, Y., Zheng, K., Pullerits, T. & Liang, Z. Insights into charge carrier dynamics in organo-metal halide perovskites: from neat films to solar cells. Chem. Soc. Rev. 46, 5714–5729 (2017).

    CAS  PubMed  Google Scholar

  32. Herz, L. Charge-carrier mobilities in metal halide perovskites: fundamental mechanisms and limits. ACS Energy Lett. 2, 1539–1548 (2017).

    CAS  Google Scholar

  33. Lampert, M. Simplified theory of space-charge-limited currents in an insulator with traps. Phys. Rev. 103, 1648 (1956).

    ADS  CAS  Google Scholar

  34. Mott, N. F. & Gurney, R. W.Electronic Processes in Ionic Crystals (Oxford University Press: Oxford, 1940).

  35. van Reenen, S., Kemerink, M. & Snaith, H. Modeling anomalous hysteresis in perovskite solar cells. J. Phys. Chem. Lett. 6, 3808–3814 (2015).

    PubMed  Google Scholar

  36. Chen, B., Yang, M., Priya, S. & Zhu, K. Origin of J–V hysteresis in perovskite solar cells. J. Phys. Chem. Lett. 7, 905–917 (2016).

    CAS  PubMed  Google Scholar

  37. Richardson, G. et al. Can slow-moving ions explain hysteresis in the current–voltage curves of perovskite solar cells? Energy Environ. Sci. 9, 1476–1485 (2016).

    CAS  Google Scholar

  38. Pospisil, J. et al. Density of bulk trap states of hybrid lead halide perovskite single crystals: temperature modulated space-charge-limited-currents. Sci. Rep. 9, 3332 (2019).

    ADS  PubMed  PubMed Central  Google Scholar

  39. Duijnstee, E. A. et al. Towards space-charge limited current measurements on metal halide perovskites. ACS Energy Lett. 5, 376–384 (2020).

    CAS  Google Scholar

  40. Lin, Y. et al. Unveiling the operation mechanism of layered perovskite solar cells. Nat. Commun. 10, 1008 (2019).

    ADS  PubMed  PubMed Central  Google Scholar

  41. Gu, Z., Huang, Z., Li, C., Li, M. & Song, Y. A general printing approach for scalable growth of perovskite single-crystal films. Sci. Adv. 4, eaat2390 (2018).

    ADS  PubMed  PubMed Central  Google Scholar

  42. Ju, D. et al. Tunable band gap and long carrier recombination lifetime of stable mixed CH3NH3PbxSn1–xBr3 single crystals. Chem. Mater. 30, 1556–1565 (2018).

    CAS  Google Scholar

  43. Zheng, G. et al. Manipulation of facet orientation in hybrid perovskite polycrystalline films by cation cascade. Nat. Commun. 9, 2793 (2018).

    ADS  PubMed  PubMed Central  Google Scholar

  44. Wu, X., Li, H., Wang, K., Sun, X. & Wang, L. CH3NH3Pb1−xEuxI3 mixed halide perovskite for hybrid solar cells: the impact of divalent europium doping on efficiency and stability. RSC Adv. 8, 11095–11101 (2018).

    CAS  Google Scholar

  45. Rao, H. S., Li, W. G., Chen, B. X., Kuang, D. B. & Su, C. Y. In situ growth of 120 cm2 CH3NH3PbBr3 perovskite crystal film on FTO glass for narrowband‐photodetectors. Adv. Mater. 29, 1602639 (2017).

    Google Scholar

  46. Huang, Y. et al. The intrinsic properties of FA(1−x)MAxPbI3 perovskite single crystals. J. Mater. Chem. A 5, 8537–8544 (2017).

    CAS  Google Scholar

  47. Röhr, J., Kirchartz, T. & Nelson, J. On the correct interpretation of the low voltage regime in intrinsic single-carrier devices. J. Phys. Condens Matter 29, 205901 (2017).

    ADS  PubMed  Google Scholar

  48. Murali, B. et al. The surface of hybrid perovskite crystals: a boon or bane. ACS Energy Lett. 2, 846–856 (2017).

    CAS  Google Scholar

  49. Zhumekenov, A. et al. Formamidinium lead halide perovskite crystals with unprecedented long carrier dynamics and diffusion length. ACS Energy Lett. 1, 32–37 (2016).

    CAS  Google Scholar

  50. Han, Q. et al. Single crystal formamidinium lead iodide (FAPbI3): insight into the structural, optical, and electrical properties. Adv. Mater. 28, 2253–2258 (2016).

    CAS  PubMed  Google Scholar

  51. Liu, Y. et al. Thinness‐and shape‐controlled growth for ultrathin single‐crystalline perovskite wafers for mass production of superior photoelectronic devices. Adv. Mater. 28, 9204–9209 (2016).

    ADS  CAS  PubMed  Google Scholar

  52. Liu, Y. et al. Two‐inch‐sized perovskite CH3NH3PbX3 (X=Cl, Br, I) crystals: growth and characterization. Adv. Mater. 27, 5176–5183 (2016).

    ADS  Google Scholar

  53. Saidaminov, M. et al. Planar-integrated single-crystalline perovskite photodetectors. Nat. Commun. 6, 8724 (2015).

    ADS  CAS  PubMed  PubMed Central  Google Scholar

  54. Saidaminov, M. et al. High-quality bulk hybrid perovskite single crystals within minutes by inverse temperature crystallization. Nat. Commun. 6, 7586 (2015).

    ADS  PubMed  PubMed Central  Google Scholar

  55. Courtier, N., Cave, J., Foster, J., Walker, A. & Richardson, G. How transport layer properties affect perovskite solar cell performance: insights from a coupled charge transport/ion migration model. Energy Environ. Sci. 12, 396–409 (2019).

    CAS  Google Scholar

  56. Neukom, M. et al. Consistent device simulation model describing perovskite solar cells in steady-state, transient and frequency domain. ACS Appl. Mater. Interfaces 11, 23320–23328 (2019).

    CAS  PubMed  Google Scholar

  57. O'Kane, S. et al. Measurement and modelling of dark current decay transients in perovskite solar cells. J. Mater. Chem. C. 5, 452–462 (2017).

    Google Scholar

  58. Lian, Z. et al. Perovskite CH3NH3PbI3 (Cl) single crystals: rapid solution growth, unparalleled crystalline quality, and low trap density toward 108 cm–3. J. Am. Chem. Soc. 138, 9409–9412 (2016).

    CAS  PubMed  Google Scholar

  59. Yang, D. et al. High efficiency planar-type perovskite solar cells with negligible hysteresis using EDTA-complexed SnO2. Nat. Commun. 9, 3239 (2018).

    ADS  PubMed  PubMed Central  Google Scholar

  60. Onoda-Yamamuro, N., Matsuo, T. & Suga, H. Dielectric study of CH3NH3PbX3 (X=Cl, Br, I). J. Phys. Chem. Solids 53, 935–939 (1992).

    ADS  CAS  Google Scholar

  61. Liu, D. et al. Impact of ultrathin C60 on perovskite photovoltaic devices. ACS nano 12, 876–883 (2018).

    CAS  PubMed  Google Scholar

  62. Schulz, P. et al. Electronic level alignment in inverted organometal perovskite solar cells. Adv. Mater. Interfaces 2, 1400532 (2015).

    Google Scholar

  63. Futscher, M. H. et al. Quantification of ion migration in CH3NH3PbI3 perovskite solar cells by transient capacitance measurements. Mater. Horiz. 6, 1497–1503 (2019).

    CAS  Google Scholar

  64. Chen, Y., Peng, J., Su, D., Chen, X. & Liang, Z. Efficient and balanced charge transport revealed in planar perovskite solar cells. ACS Appl. Mater. Interfaces 7, 4471–4475 (2015).

    CAS  PubMed  Google Scholar

  65. Petrovic, M., Ye, T., Chellappan, V. & Ramakrishna, S. Effect of low temperature on charge transport in operational planar and mesoporous perovskite solar cells. ACS Appl. Mater. Interfaces 9, 42769–42778 (2017).

    CAS  PubMed  Google Scholar

  66. Chin, X. Y., Cortecchia, D., Yin, J., Bruno, A. & Soci, C. Lead iodide perovskite light-emitting field-effect transistor. Nat. Commun. 6, 7383 (2015).

    ADS  CAS  PubMed  PubMed Central  Google Scholar

  67. Li, D. et al. Size-dependent phase transition in methylammonium lead iodide perovskite microplate crystals. Nat. Commun. 7, 1–8 (2016).

    ADS  Google Scholar

  68. Meggiolaro, D. et al. Iodine chemistry determines the defect tolerance of lead-halide perovskites. Energy Environ. Sci. 11, 702–713 (2018).

    CAS  Google Scholar

  69. Gélvez-Rueda, M., Renaud, N. & Grozema, F. Temperature dependent charge carrier dynamics in formamidinium lead iodide perovskite. J. Phys. Chem. C. 121, 23392–23397 (2017).

    Google Scholar

  70. Shrestha, S. et al. Assessing temperature dependence of drift mobility in methylammonium lead iodide perovskite single crystals. J. Phys. Chem. C. 122, 5935–5939 (2018).

    CAS  Google Scholar

  71. Ma, J. & Wang, L.-W. The nature of electron mobility in hybrid perovskite CH3NH3PbI3. Nano Lett. 17, 3646–3654 (2017).

    ADS  CAS  PubMed  Google Scholar

  72. Zhao, T., Shi, W., Xi, J., Wang, D. & Shuai, Z. Intrinsic and extrinsic charge transport in CH3NH3PbI3 perovskites predicted from first-principles. Sci. Rep. 6, 19968 (2016).

    ADS  Google Scholar

Download references

Acknowledgements

We thank Christian Bauer, Michelle Beuchel, Hans-Jürgen Guttmann, Frank Keller, and Verona Maus for technical support. Open access funding provided by Projekt DEAL.

Author information

Authors and Affiliations

  1. Max Planck Institute for Polymer Research, Ackermannweg 10, 55128, Mainz, Germany

    Mohammad Sajedi Alvar, Paul W. M. Blom & Gert-Jan A. H. Wetzelaer

Contributions

G.A.H.W. and P.W.M.B. proposed the project. M.S.A. fabricated the devices and performed all measurements. M.S.A. programmed the drift-diffusion model and performed the simulations. All authors contributed to the experimental and theoretical analysis. P.W.M.B. and G.A.H.W. supervised the project and all authors contributed to preparing and writing of the manuscript.

Corresponding authors

Correspondence to Mohammad Sajedi Alvar, Paul W. M. Blom or Gert-Jan A. H. Wetzelaer.

Ethics declarations

Competing interests

The authors declare no competing interests.

Additional information

Peer review information Nature Communications thanks Jongchul Lim and the other, anonymous, reviewer(s) for their contribution to the peer review of this work. Peer reviewer reports are available.

Publisher's note Springer Nature remains neutral with regard to jurisdictional claims in published maps and institutional affiliations.

Supplementary information

Rights and permissions

Open Access This article is licensed under a Creative Commons Attribution 4.0 International License, which permits use, sharing, adaptation, distribution and reproduction in any medium or format, as long as you give appropriate credit to the original author(s) and the source, provide a link to the Creative Commons license, and indicate if changes were made. The images or other third party material in this article are included in the article's Creative Commons license, unless indicated otherwise in a credit line to the material. If material is not included in the article's Creative Commons license and your intended use is not permitted by statutory regulation or exceeds the permitted use, you will need to obtain permission directly from the copyright holder. To view a copy of this license, visit http://creativecommons.org/licenses/by/4.0/.

Reprints and Permissions

About this article

Verify currency and authenticity via CrossMark

Cite this article

Sajedi Alvar, M., Blom, P.W.M. & Wetzelaer, GJ.A.H. Space-charge-limited electron and hole currents in hybrid organic-inorganic perovskites. Nat Commun 11, 4023 (2020). https://doi.org/10.1038/s41467-020-17868-0

Download citation

  • Received:

  • Accepted:

  • Published:

  • DOI : https://doi.org/10.1038/s41467-020-17868-0

Further reading

Comments

By submitting a comment you agree to abide by our Terms and Community Guidelines. If you find something abusive or that does not comply with our terms or guidelines please flag it as inappropriate.

flaniganyouret.blogspot.com

Source: https://www.nature.com/articles/s41467-020-17868-0

0 Response to "Easy Insight Into Spacecharge Effects on Steadystate Transport in Oxide Films"

Post a Comment

Subscribe to: Post Comments (Atom)

Iklan Atas Artikel

Iklan Tengah Artikel 1

Iklan Tengah Artikel 2

Iklan Bawah Artikel