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Advances in Condensed Matter Physics
Volume 2018, Article ID 8297918, 7 pages
https://doi.org/10.1155/2018/8297918
Research Article

Surface Dynamics Transition of Vacuum Vapor Deposited CH3NH3PbI3 Perovskite Thin Films

1School of Science, Shandong University of Technology, Zibo, Shandong 255049, China
2School of Science, Shandong Jianzhu University, Jinan, Shandong 250101, China
3State Key Laboratory of Luminescence and Applications, Changchun Institute of Optics, Fine Mechanics and Physics, Chinese Academy of Sciences, Changchun, Jilin 130033, China

Correspondence should be addressed to Zisheng Su; nc.ca.pmoic@szus and Gongxiang Wei; nc.ude.tuds@xgiew

Received 30 August 2017; Accepted 4 December 2017; Published 22 February 2018

Academic Editor: Shicai Xu

Copyright © 2018 Yunyan Liu et al. This is an open access article distributed under the Creative Commons Attribution License, which permits unrestricted use, distribution, and reproduction in any medium, provided the original work is properly cited.

Abstract

The growth dynamics of CH3NH3PbI3 perovskite thin films on ITO covered glass substrate were investigated. The evolution of the film could be divided into two stages. A mound-like surface was obvious at the first stage. Stable dynamic scaling was observed for thicker films at the second stage. Through analyzing the scaling exponent, growth exponent , and 2D fast Fourier transform, it is concluded that, at the second stage, the growth mechanism of mound formation does not play a major role, and the film growth mechanism can be described by Mullins diffusion equation.

1. Introduction

In the past few years, organic–inorganic halide perovskites materials have been intensively investigated for their excellent combination of optoelectronic properties and low cost. Perovskites have found applications in many fields including photovoltaics, lasing, and lighting [13] and also potential application in sensitive devices such as photoelectric sensors and gas sensors [4, 5]. The power conversion efficiency (PCE) of perovskite solar cells has increased rapidly from 3.8% to 22.1% in merely 5 years [69]. However, the devices’ performance and stability are impacted by problems associated with uniformity morphology, coverage, and roughness of the perovskite films. In addition, there is still limited knowledge of the morphology evolution and basic growth dynamics of the halide perovskite thin films.

For inorganic and organic thin films, scaling concepts have been developed to quantify the statistical properties of the morphology evolution of the growth front in order to study the growth dynamics of thin films. Various surface growth mechanisms have been supported by different growth models with different sets of scaling exponents [10]. Within this framework, the growth-induced surface morphology information is described by the equal-time height-height correlation function . is defined as a function of lateral position and deposition time by , where represents the relative surface height at position r and time t with respect to the average surface height .

We have reported the scaling behavior and related physical growth dynamics of MAPbI3 perovskite thin films on smooth Si substrates [11]. However, practical applications of devices require the perovskite thin films to be deposited on a wide variety of substrates. The nucleation and growth of the deposited perovskite thin films are strongly affected by the surface properties of the substrates underneath the growing films. In this article, the morphology evolution and growth kinetics of CH3NH3PbI3 (MAPbI3) perovskite thin films by vacuum vapor deposition onto rough ITO covered glass substrates were investigated by analyzing the height-height correlation function , scaling exponents , , and , and 2D fast Fourier transform. The transition in the growth process of thermally evaporated MAPbI3 thin films from mound to Mullins growth is found, and this transition could be resulting from the competition between step-edge bias (SEB) and surface diffusion. This result is quite different from that of Si substrates, which indicates that the perovskite thin films’ performance is strongly dependent on the surface properties of the substrates.

2. Materials and Methods

The MAPbI3 perovskite thin films were fabricated by thermal evaporation on ITO (indium tin oxide) covered glass substrates. The substrates were routinely cleaned, followed by UV-ozone treatment for 10 min. The substrates were not intentionally heated during deposition and all the films were not post-heat-treated. The background pressure of the vacuum chamber for thermal evaporation is  Pa. The MAPbI3 film was grown by thermally coevaporating CH3NH3I and PbI2 with a mass ratio of CH3NH3I to PbI2 of 4 : 1. The growth rate was kept at 0.5 Å/s for MAPbI3 films. The perovskite layer thicknesses from 6.5 to 300 nm were controlled by the deposition time between 130 s and 600 s, respectively. The deposition rate and layer thickness were monitored in situ using oscillating quartz monitors.

The surface topographies were imaged with a Bruker Multimode 8 atomic force microscope (AFM) in tapping mode under ambient air. The scanning area for AFM imaging is 3 m 3 m with a resolution of . In order to get better statistical properties, repeated measurements were carried out to obtain the average .

3. Results and Discussion

Figures 1(a)1(d) describe AFM images of the ITO substrate and different MAPbI3 perovskite thin films of growth time of 130 s, 200 s, and 500 s, respectively. The corresponding 1D cross-sectional scans of surface profile are also shown, where denotes the relative surface height at coordinate on the cross section line. The MAPbI3 film with a deposition time of 130 s shows a dramatically different surface morphology (Figure 1(b)) from that of the ITO substrate (Figure 1(a)). The ITO grooves surface is covered by isolated spherical grains, suggesting the island film growth of perovskite thin films. When growth time  s (Figures 1(c) and 1(d)), the topography of the substrate is invisible and a continuous grainy surface of MAPbI3 film develops. From the beginning of deposition, as shown in 1D cross-sectional scans of the surface profile, the relative surface height decreases with the increasing deposition time. After a continuous film is formed, the transition of morphology is accompanied by the height increase as more materials are deposited. This indicates that the surface formation evolves from a dynamic smoothening process to a roughening growth, as will be further discussed in the following sections.

Figure 1: Representative AFM images (3 m × 3 m) and one-dimensional cross-sectional scan of the surface profile of (a) ITO coated glass and MAPbI3 thin film on ITO coated glass substrates for deposition time of (b) 130, (c) 200, and (d) 500 seconds.

For the calculated results of and and scaling exponents , , and , refer to [11].

Figure 2 shows the roughness exponent as a function of growth time . It can be seen that the changes of the variables and can be divided into two stages. At the first stage ( s), values decrease from about 0.9 to 0.84 with increasing time . This implies a strong interaction between the incoming flux and the substrates at the initial coverage stage, and the surface experiences an unstable scaling behavior [12]. At the second stage ( s), values are almost invariant and the average value is about 0.83. This indicates the stable kinetic roughening corresponding to continuous film growth at this stage [13].

Figure 2: The roughness exponent as a function of growth time for MAPbI3 thin films; the short dashed line shows the average value of when  s.

The calculated scaling exponent at the first stage is quite close to the one predicted by the model of mound formation or Mullins model where, in both cases, . However, it may be smaller than that predicted by the theoretical model practically, for example, SnCl2Pc on glass [14]. The mound growth mechanism can usually occur in thin film growth in the presence of nonlocal roughening effects such as shadowing or step-edge barrier (Schwoebel barrier), which is associated with reduced interlayer transport [15, 16]. Mullins growth refers to a linear model of a self-affine growth mechanism, in which the growth is dominated by the surface diffusion, and in turn the latter is due to the curvature induced chemical potential gradient. The ring structure is the main feature of SEB induced mound growth [17]. We have plotted 2D fast Fourier transform (FFT) of the surface from the AFM images (Figures 3(a)3(d)), and the formation of the mound at the initial film growth stage is supported by the ring-like behavior in the 2D FFT of the film for growth time of less than 200 s (Figure 3(a)). Furthermore, the mound surface is supported by the curves displaying an overshoot in the crossover [15] and by the oscillation in larger as shown in the curves of  s in [11]. Hence, the growth of MAPbI3 film at the first stage is more likely to be governed by SEB induced mound growth model.

Figure 3: 2D FFT of the surface from MAPbI3 thin film AFM images of deposition time of (a) 130 s, (b) 160 s, (c) 500 s, and (d) 600 s.

For the SEB induced surface, the mound growth model can be described by the following equation:Here, and terms refer to SEB effect and surface diffusion, respectively. Small ratio means that the SEB dominates the growth and the ring structure would be obvious. On the other hand, when is much larger than 1, either SEB is small or surface diffusion is fast, and the ring structure would be beyond recognition [18].

Figure 4(a) shows the - plot. It is clearly shown that decreases and then increases with time , indicating a shift from smoothing to roughening of film surface. This is consistent with the fluctuation of height as revealed in Figure 1. The solid line in Figure 4(a) is the linear fit to the data for the second growth stage , when continuous film growth and stable scaling behavior occur, and is obtained.

Figure 4: The log-log plot of (a) and (b) as a function of growth time for MAPbI3 thin films. The solid lines are linear fits to the data for growth time  s which give and .

is close to the reported results of vapor deposited oligomer films on silicon substrate [19] and recent reports of vapor phase deposition of poly(ethylene) ( varying from 0.20 to 0.33 in postaggregation and aggregation regime, resp.) [20]. Previous theoretical or experimental studies have revealed that, in the step-edge barrier or shadowing effect governing film growth, the value of will be equal to or greater than 0.5 [21, 22]. Our value of about 0.28 indicates that both step-edge barrier and shadowing effects are weak during the growth of perovskite films at the second stage, and this may lead to the situation of as discussed in (1). In this case, the satellite ring structure should not be observed for the films of the second stage. To confirm this, we investigated the ring structure for the MAPbI3 films. Results show that the ring structure gradually disappears and could not be definitely determined for s as expected, as shown in Figures 3(b)3(d). This information reveals that the surface diffusion induced growth, instead of mound growth, might be the dominant mechanism at the second stage. It should be noted that the value of growth exponent is close to the predictions of the surface diffusion induced Mullins scenario or Kardar–Parisi–Zhang (KPZ) model [23]. However, KPZ type of growth develops the scaling exponent , and it is well below as obtained at the second growth stage in our work; thus, KPZ growth is excluded. In fact, is in the range of the prediction of the surface diffusion mechanism [24]. These results strongly support the fact that surface diffusion dominated growth offers a more plausible scenario than others at the second growth stage of MAPbI3 thin films. In this case, the terms could be neglected from (1), and the growth at the second stage would be governed by Mullins diffusion described by the following [25]:The dominant growth mechanism might shift from SEB induced mound growth at the first growth stage to surface diffusion induced Mullins growth at the second stage.

The correlation length at each growth time could be determined by fitting the curve of to the phenomenological function for self-affine proposition by Sinha et al. [26]:

Figure 4(b) displays the log-log plot of versus . The solid line in Figure 4(b) is the linear fit to the data for the second growth stage , and is obtained. is a little lower than . This may indicate weak anomalous scaling, where the local slope is no longer time-independent for short range of and corresponding growth is not stationary. This supports the nonstationary growth behavior of short range as revealed in [11].

We note that the interface width decreases with time at early growth time. This phenomenon is in contrast to the results obtained in theoretical prediction and most experiments show that the surface roughness evolves with time in the form of power law as at the initial film growth stage, where ideal smooth substrate surfaces are applied. However, smoothening may occur at the initial film growth due to the complicated growth conditions in real systems [27], which have drawn little attention in the past few years. Previously, studies revealed some smoothening mechanisms of various films, including rough substrate, surface diffusion, step-edge barrier effect, nonlinearity, or reemission [2730]. The surface smoothing in the initial growth of ZrO2 thin films deposited on glass, because of the interaction of substrate and diffusion of deposited atoms, has been reported [28]. Ballestad et al. [29] explained the mounded surface smoothening using nonlinear Kardar–Parisi–Zhang (KPZ) equation . Liu et al. [30] observed linear surface smoothening which could be explained by noise driven Mullins diffusion equation . Also, an example can be found in [27], from kinetic Monte Carlo (KMC) simulations, where the initial smoothening effect of InAs films on InAs substrates is attributed to the presence of an asymmetric step-edge barrier induced linear instability.

Due to the step-edge barrier at the early growth stage of the MAPbI3 film, which prevents atoms from hopping from the top of the island to the substrate, the adatoms are more apt to combine with each other than with the substrate, and this leads to the initial mound growth. The isolated island has not completely covered the substrate and the height difference between the island and the substrate was explained as a possible origin for the initial larger roughness of the surface. At the same time, deposited atoms prefer to move downward by overcoming the island edge barrier to minimize the surface energy. As more islands grow and merge with each other, the surface of the substrates is gradually covered by more and more film. The height difference between the newly formed islands, merged islands, and the ITO substrates gradually decreases. This decrease will continue until the roughness fluctuation of homogeneous film morphology becomes evident, due to growth behaviors of the continuous MAPbI3 thin films, and evolves with time in the form of power law as . On the other hand, the introduction of newly built grain boundary and in-plane tensile stress in merged islands and continuous film grains could change the behavior during film growth [31]. In such case, the film growth evolves into a different evolution mechanism which should be dominated by a weak step-edge barrier and large surface diffusion at the second stage. The variations of the growth mechanism may also be considered to be related to thickness dependent structural changes or molecular reorientation [21, 32], ultimately leading to the morphology evolution of thin films.

4. Conclusions

In conclusion, the growth dynamics of MAPbI3 thin films by thermal evaporation on rough ITO substrates were investigated. Two growth stages can be found before and after the formation of continuous films. By analyzing the scaling behavior of the films and 2D fast Fourier transform, we conclude that step-edge barriers governing growth result in the morphology evolution of MAPbI3 thin films following obvious mound-like formation at the initial growth stage. At the second stage, stable kinetic roughening corresponds to a continuous film growth, with , growth exponent , and a dynamic exponent . The mound feature disappeared and the film growth at the second stage was shown to belong to a Mullins diffusion model, and the dominant roughening mechanism would be diffusion induced dynamic growth. The shift of the interface width from a decrease to an increase also suggests different evolution mechanisms at different growth stages. The nonstationary growth behavior of short range and the relation of indicate the anomalous scaling behavior of MAPbI3 surface evolution.

Conflicts of Interest

The authors declare that they have no conflicts of interest.

Acknowledgments

The authors acknowledge the support of the National Natural Science Foundation of China (11404191, 61604149, and 11574185) and Shandong Provincial Natural Science Foundation (ZR2016AQ22). This work is also supported by the Program for the Top Young of SDUT, China.

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