MAPbI3 Microrods-Based Photo Resistor Switches: Fabrication and Electrical Characterization

The current work proposed the application of methylammonium lead iodide (MAPbI3) perovskite microrods toward photo resistor switches. A metal-semiconductor-metal (MSM) configuration with a structure of silver-MAPbI3(rods)-silver (Ag/MAPbI3/Ag) based photo-resistor was fabricated. The MAPbI3 microrods were prepared by adopting a facile low-temperature solution process, and then an independent MAPbI3 microrod was employed to the two-terminal device. The morphological and elemental compositional studies of the fabricated MAPbI3 microrods were performed using FESEM and EDS, respectively. The voltage-dependent electrical behavior and electronic conduction mechanisms of the fabricated photo-resistors were studied using current–voltage (I–V) characteristics. Different conduction mechanisms were observed at different voltage ranges in dark and under illumination. In dark conditions, the conduction behavior was dominated by typical trap-controlled charge transport mechanisms within the investigated voltage range. However, under illumination, the carrier transport is dominated by the current photogenerated mechanism. This study could extend the promising application of perovskite microrods in photo-induced resistor switches and beyond.


Introduction
During the last decade, hybrid organic-inorganic perovskites (HOIPs) have been extensively studied for the emerging perovskite solar cell technology and other optoelectronic applications. Among various types of HOIPs, methylammonium lead iodide (MAPbI 3 ) has been commonly employed in artificial synapses, photodetectors, light-emitting diodes (LEDs), field-effect transistors, and photo-resistors beyond the photovoltaics (PV) [1,2]. Besides the use of MAPbI 3 -based thin films in PV applications, other low dimensional perovskite structures, including zero-dimensional (0D) quantum dots (QDs), one dimensional (1D) nanowires (NWs) and nano/microrods, and two dimensional (2D) nanoplates, have been widely employed in optoelectronic applications [3][4][5]. Since perovskite crystals offer better performance relative to thin films in terms of effective light absorption, large surface-to-volume ratio, mechanical flexibility, and better charge separation and conductivity, they have been effectively incorporated in optoelectronic devices [6][7][8]. Among different sub-classes of low-dimensional materials, 1D microrods with a well-defined configuration offer superiority in terms of a 3-4-millimeter length range, confined excitons in one-dimension, effective photon coupling, less heterostructure defects, direct charge carriers transport routes, and simple solution-based technique growth [9][10][11][12]. In addition, a relatively higher and long carrier diffusion length (≈41 µm) is also a beneficial key point in 1D structures [10].
Recent research has shown that I − (0.1-0.6 eV) and MA + (0.5-0.8 eV) have low migration activation energies and several types of point defects in MAPbI 3 have low formation energies, including vacancies (V Pb , V MA , V I ), interstitials (MA i , I i ), and antisubstitutions (Pb I , MA Pb ) [13]. These point defects can cause shallow defect levels and then trap charges at these energy levels, revealing that in HOIPs, a strong potential application of photo-resistors can be predicted. The current flowing across a two-terminal perovskite/semiconductor-based capacitor-like structure is preferentially confined in areas localized at defects [14].
Photo-resistors can be employed in a variety of applications such as fire sensing [15], motion sensing, and radiation detection-based devices [16]. Many reports have been made on the photo-resistor applications using CdS [17], CdSe [18], PbS [19], PbSe [20], and ZnO [21]. In contrast, owing to the advantages of low dimensional perovskite crystals, such as fast photosensitivity over a broad absorption spectrum range, we successfully employed facile solution-grown MAPbI 3 microrods in the photo-resistors. Usually, MSM capacitor-like devices have been fabricated by sandwiching a thin film of a semiconductor between two metals. However, here, a MAPbI 3 microrod connected between two metal electrodes has been exploited to form a MSM device.

Preparation of Microrods
In Dimethylformamide (DMF, anhydrous, 99.8%, Agros chemicals, Broendby, Denmark) and isopropanol (IPA, VWR Prolab chemicals, Laval, QC, Canada), 1 M solutions of each Lead (II) iodide (PbI 2 , Sigma-Aldrich, Darmstadt, Germany) and methylammonium iodide (MAI, TCI Chemicals, Tokyo, Japan), respectively, were prepared separately. To form the solution of MAPbI 3 , already prepared solutions of PbI 2 and MAI were combined in the volumetric ratio of 2:1. At the initial stage, the thick precipitates of perovskite in the solution were developed. Over time, a crystal-clear yellow solution of the MAPbI 3 was formed after concurrent heating at 70 • C and stirring at 400 rpm. At a very slow rate of 10 • C/HR, the prepared solution of the MAPbI 3 was set to cool down to room temperature for 24 h. After passing 24 h, the growth of the microrods was observed. In the vibration-free environment, the length of microrods seems to increase within the solution over time.
Step-by-step preparation of MAPbI 3 microrods is demonstrated in Figure 1a. The microrods were kept for 1000 h in an ambient environment to let them degrade and stabilize after the fabrication of the devices. All the materials were used as received without any purification. Recent research has shown that I − (0.1-0.6 eV) and MA + (0.5-0.8 eV) have low migration activation energies and several types of point defects in MAPbI3 have low formation energies, including vacancies (VPb, VMA, VI), interstitials (MAi, Ii), and antisubstitutions (PbI, MAPb) [13]. These point defects can cause shallow defect levels and then trap charges at these energy levels, revealing that in HOIPs, a strong potential application of photoresistors can be predicted. The current flowing across a two-terminal perovskite/semiconductor-based capacitor-like structure is preferentially confined in areas localized at defects [14].
Photo-resistors can be employed in a variety of applications such as fire sensing [15], motion sensing, and radiation detection-based devices [16]. Many reports have been made on the photo-resistor applications using CdS [17], CdSe [18], PbS [19], PbSe [20], and ZnO [21]. In contrast, owing to the advantages of low dimensional perovskite crystals, such as fast photosensitivity over a broad absorption spectrum range, we successfully employed facile solution-grown MAPbI3 microrods in the photo-resistors. Usually, MSM capacitorlike devices have been fabricated by sandwiching a thin film of a semiconductor between two metals. However, here, a MAPbI3 microrod connected between two metal electrodes has been exploited to form a MSM device.

Preparation of Microrods
In Dimethylformamide (DMF, anhydrous, 99.8%, Agros chemicals, Broendby, Denmark) and isopropanol (IPA, VWR Prolab chemicals, Laval, QC, Canada), 1 M solutions of each Lead (II) iodide (PbI2, Sigma-Aldrich, Darmstadt, Germany) and methylammonium iodide (MAI, TCI Chemicals, Tokyo, Japan), respectively, were prepared separately. To form the solution of MAPbI3, already prepared solutions of PbI2 and MAI were combined in the volumetric ratio of 2:1. At the initial stage, the thick precipitates of perovskite in the solution were developed. Over time, a crystal-clear yellow solution of the MAPbI3 was formed after concurrent heating at 70 °C and stirring at 400 rpm. At a very slow rate of 10 °C/HR, the prepared solution of the MAPbI3 was set to cool down to room temperature for 24 h. After passing 24 h, the growth of the microrods was observed. In the vibration-free environment, the length of microrods seems to increase within the solution over time.
Step-by-step preparation of MAPbI3 microrods is demonstrated in Figure 1a. The microrods were kept for 1000 h in an ambient environment to let them degrade and stabilize after the fabrication of the devices. All the materials were used as received without any purification.

Device Preparation
Commercially available ITO glass substrates (S161, Ossila Ltd, Sheffield, UK) were cleaned as per a well-established cleaning procedure, i.e., ultrasonication in hot DI water mixed with 1% Hellmanex III liquid (for 5 min), followed by rinsing in hot DI water without Hellmanex III liquid. The substrates were then dumped and sonicated in Isopropyl alcohol (for 5 min) and finally rinsed in normal DI water. Later on, the substrates were dried using a stream of dry nitrogen. An individual MAPbI 3 rod was placed over the pre-patterned ITO electrodes on S161 glass substrates. Then, the silver (Ag) paste was placed at both ends of the rod to form an Ag/MAPbI 3 /Ag-based photo-resistor. We prepared two devices with the diameter of the rods as 50 µm each and lengths of 3.5 and 4 mm (Supplementary Materials Figure S1). The calculated areas are 1.25 and 1.5 µm 2 for rods with 3.5-and 4-millimeter lengths. The device structure of the Ag/MAPbI 3 /Ag-based photo-resistor is depicted in Figure 1b.

Characterization
To study the surface morphology of the microrods, a field emission scanning electron microscope (FESEM) study was performed. The microrods' elemental compositional analysis was carried out using Energy-dispersive X-ray spectroscopy (EDS) and X-ray photoelectron spectroscopy (XPS). The monochromatic radiation was used in XPS measurement. In addition, the crystallinity measurement of the microrods was performed using X-ray diffraction (XRD) analysis with a step size of 0.013 • of 2θ. Current-voltage (I-V) characterization of the Ag/MAPbI 3 /Ag-based device was measured under dark and 1 Sun illumination (with a scan rate of 10 mV/s) using an Oriel AAA solar simulator (Newport) and Keithley 2400 source measuring unit (SMU). The I-V measurements were conducted under the periodic dc voltage supply considering that one Ag electrode was provided with the voltage while the other was grounded. Figure 2 illustrates the FESEM analysis of MAPbI 3 microrods under various magnifications. The micrographs reveal the porous structure of MAPbI 3 microrods. A well-aligned parallel arrangement of the submicron level perovskite crystals in the longitudinal direction is demonstrated. The perovskite microrods display a diameter in the range of~10-50 µm; however, the length of microrods was up to several millimeters (~3-5 mm), as reported previously [9]. During the growth process, crystals are combined in such a way that hollow regions are created between the adjacent crystals. Nevertheless, no adjacent cracks are observed at the magnification level given in Figure 2. EDS data presented in Figure 3 demonstrate a well-defined stoichiometry of MAPbI 3, indicating lead (Pb) and iodine (I) presence as the main ingredients. Two prominent peaks exist at 2.32 and 10.5 keV correlated to Pb, while the peaks at 3.98 and 4.2 keV correspond to the I element in the MAPbI 3 crystals. Furthermore, the atomic composition of microcrystals reveals the presence of Pb with I in the ratio of 1:2.3, which is consistent with PbI 2 , conforming to the formation of pure phases. In addition, the full EDS data of MAPbI 3 rods is provided in Supplementary Materials Figure S2. The carbon (C) peak is clearly visible in the full spectrum. The formation of C peak could be attributed to the preparation of MAPbI 3 rods in DMF solution.  The XRD results are demonstrated in Figure 4. The results showed the hexagonal structure with a P3m1(164) space group for the MAPbI3 crystals. The high-intensity diffraction peaks are prominent at low angles, such as 9.0, 9.5, 18.1, and 24.5°, and they strongly dominate the diffraction pattern. The high crystalline nature of the MAPbI3 phase formation is verified by the highly intense diffraction peaks assigned to (110), (202), (004), and (220). Additionally, few low-intensity peaks of MAPbI3 also exist at (310), (314), and (404) [22]. At room temperature, the unidentified peaks reflecting the stable phase did not match either the pure PbI2 or the MAI phase. This implies a new intermediate phase, which could be a PbI2-DMF or PbI2-MAI-DMF complex [23]. In addition, we have performed XRD analysis for as-synthesis and fresh samples (over 10,000 h). Interestingly, the  The XRD results are demonstrated in Figure 4. The results showed the hexagonal structure with a P3m1(164) space group for the MAPbI3 crystals. The high-intensity diffraction peaks are prominent at low angles, such as 9.0, 9.5, 18.1, and 24.5°, and they strongly dominate the diffraction pattern. The high crystalline nature of the MAPbI3 phase formation is verified by the highly intense diffraction peaks assigned to (110), (202), (004), and (220). Additionally, few low-intensity peaks of MAPbI3 also exist at (310), (314), and (404) [22]. At room temperature, the unidentified peaks reflecting the stable phase did not match either the pure PbI2 or the MAI phase. This implies a new intermediate phase, which could be a PbI2-DMF or PbI2-MAI-DMF complex [23]. In addition, we have performed XRD analysis for as-synthesis and fresh samples (over 10,000 h). Interestingly, the The XRD results are demonstrated in Figure 4. The results showed the hexagonal structure with a P3m1(164) space group for the MAPbI 3 crystals. The high-intensity diffraction peaks are prominent at low angles, such as 9.0, 9.5, 18.1, and 24.5 • , and they strongly dominate the diffraction pattern. The high crystalline nature of the MAPbI 3 phase formation is verified by the highly intense diffraction peaks assigned to (110), (202), (004), and (220). Additionally, few low-intensity peaks of MAPbI 3 also exist at (310), (314), and (404) [22]. At room temperature, the unidentified peaks reflecting the stable phase did not match either the pure PbI 2 or the MAI phase. This implies a new intermediate phase, which could be a PbI 2 -DMF or PbI 2 -MAI-DMF complex [23]. In addition, we have performed XRD analysis for as-synthesis and fresh samples (over 10,000 h). Interestingly, the results demonstrate no significant change. The peaks are prominent in both results. However, the intensities of the peaks have been reduced in fresh samples. These results indicate the crystallinity nature in the MAPbI 3 rods with no elemental change.  The elementary composition analysis of the MAPbI3 crystals was performed using XPS. Figure 5a shows the survey spectrum was recorded in the binding energy range between 0 and 800 eV, with the identified elements comprising lead (Pb), iodine (I), oxygen (O), and carbon (C). The existence of O and C shows exposure of crystals to the atmosphere after synthesis. The elemental concentration data are derived from the XPS survey spectrum shown in Table S1. The atomic concentrations of lead (26.95%), iodine (47.57%), and carbon (C) are found as 25.47% in MAPbI3 crystals. In addition, the calculated ratio of Pb and I is found as 1:1.765121. This confirms the existence of intermediate phases due to the addition of the MAI. In addition, XPS core spectra were obtained to explain the changes in crystal growth chemical bonding. To precisely explain features, Shirley background subtraction has been The elementary composition analysis of the MAPbI 3 crystals was performed using XPS. Figure 5a shows the survey spectrum was recorded in the binding energy range between 0 and 800 eV, with the identified elements comprising lead (Pb), iodine (I), oxygen (O), and carbon (C). The existence of O and C shows exposure of crystals to the atmosphere after synthesis. The elemental concentration data are derived from the XPS survey spectrum shown in Table S1. The atomic concentrations of lead (26.95%), iodine (47.57%), and carbon (C) are found as 25.47% in MAPbI 3 crystals. In addition, the calculated ratio of Pb and I is found as 1:1.765121. This confirms the existence of intermediate phases due to the addition of the MAI.  The elementary composition analysis of the MAPbI3 crystals was performed using XPS. Figure 5a shows the survey spectrum was recorded in the binding energy range between 0 and 800 eV, with the identified elements comprising lead (Pb), iodine (I), oxygen (O), and carbon (C). The existence of O and C shows exposure of crystals to the atmosphere after synthesis. The elemental concentration data are derived from the XPS survey spectrum shown in Table S1. The atomic concentrations of lead (26.95%), iodine (47.57%), and carbon (C) are found as 25.47% in MAPbI3 crystals. In addition, the calculated ratio of Pb and I is found as 1:1.765121. This confirms the existence of intermediate phases due to the addition of the MAI. In addition, XPS core spectra were obtained to explain the changes in crystal growth chemical bonding. To precisely explain features, Shirley background subtraction has been In addition, XPS core spectra were obtained to explain the changes in crystal growth chemical bonding. To precisely explain features, Shirley background subtraction has been performed before Gaussian curve fitting. The spectra in C 1 s on the surface of the crystals  Figure 5b. The C 1 s spectrum of the MAPbI 3 crystals shows elements at 284.6, 286.3, and 288.3 eV. This refers to the C-C, C-O-C, and O-C=O bonds, respectively. The core level iodine range has been shown in Figure 5c with two different (P1 and P3) iodine peaks at about 619.20 eV, I(3d 5/2 ) and 630.51 eV, I(3d 3/2 ) associated with iodine anions from CH 3 NH 3 I and peaks (P2 and P4) at about 619.77 eV, I(3d 5/2 ) and 63.31 eV, I(3d 3/2 ) for Pb-I bonding. As shown in the core level spectrum of Pb (Figure 5d), four different peaks (P1, P2, P3, P4) have been associated to obtain a perfect fit, the first, P1 at 136.86 eV and the other, P3 at 141.77 eV, represent the Pb(4f 7/2 ) and Pb(4f 5/2 ) cations associated with PbI 6 . Furthermore, P3 at 137.43 eV and the additional P4 at 142.28 eV represent the Pb 2+ cation associated with PbO. However, it must be noted that the intensity of P1 and P3 is much more than the P2 and P3. Furthermore, energy separation between peaks P1 and P3 is 4.91 eV, while P2 and P3 maintain 4.85 eV, hence suggesting that crystals mainly have PbI 6 with strong binding [24,25].

Results and Discussion
The I-V characteristics of the Ag/MAPbI 3 /Ag-based photo-resistor are recorded in the voltage ranging from −1 to +1 V, as shown in Figure 6a. The MAPbI 3 microrod attached with the Ag contacts exhibit nonlinear features and demonstrates metal/semiconductor/metal (M/S/M) junction behavior. The typical I-V characteristics of the Ag/MAPbI 3 /Ag-based photo-resistor on the semi-log scale are plotted in Figure 6b. As shown by the red curve in Figure 6c, the photovoltaic current is generated under illumination. The turn-on voltage was found to be 0.55 V. The series and shunt resistances, R s and R sh , resistances are shown in Figure 6d. The values obtained for the R s and R sh are 130 kΩ and 3 MΩ, respectively. For the fabricated photo-resistor, the value of the ideality factor "n" was calculated as 1.85 ± 0.4. The ideality factor for an ideal diode must be close to one, but in most of the metal/semiconductor interfaces, this value is deviated from unity and is observed to be greater than one. This larger value implies secondary conduction mechanisms at the interface. The I-V curves under dark and light conditions with scan directions (−V to 0) for an Ag/MAPbI 3 /Ag-based photo-resistor are demonstrated in Figure 6e,f, respectively. A significant hysteresis effect can be observed in both cases.
To study the possible conduction mechanism in the dark and under light, the I-V characteristics of microrod-based Ag/MAPbI 3 /Ag photo-resistor are plotted in a log V-log I scale as shown in Figure 7a,b, respectively. There are three major regions with distinct slopes, namely, the region I, II, and III, observed in Figure 7a. The slope of the fitting line in region I (between −1.4 and −0.75 V) is estimated as 2.2 (close to 2) that obeys I ∝ V 2 (child's law), demonstrating a space charge limited current (SCLC) transport mechanism. In regions II and III, the slope takes the values of 7.4 and 6.3, respectively, indicating a trapped charge limited current (TCLC) in a voltage range greater than 0.75 V. Among the proposed models, the SCLC and the TCLC mechanism can be employed to elucidate the conduction mechanism of our device under dark. Region I is dominated by the SCLC conduction mechanism in which the injected electrons participate in the current flow and govern the conduction mechanism. The trapping of injected carriers by the inherent defects in the perovskite layer (MAPbI 3 ) causes the current to flow proportional to the applied bias square. The electrons and traps in the perovskite layer play an essential role in the charge transport mechanism. It has been broadly argued that the SCLC is strongly correlated to the switching layer's charge trapping and dielectric quality. In Figure 7b, there are three distinct regions, e.g., regions I, II, and III. Region I demonstrates a slope of 0.02, region II shows a slope of 0.06, and Region III represents a slope of 0.009. Typically, the slope with a value of one represents the ohmic state. However, in our case, all the slopes are <1 and close to 0. This indicates that the density of the photogenerated carriers dominates the electrical transport within the Ag/MAPbI 3 /Ag device. In region I, the photogenerated carrier concentration exceeds the injected carriers, while in region II, a rapid increase in the current is observed. This could be attributed to the fact that few trapped electrons absorbed the incident photons and became excited [26]. Moreover, it can be assumed that the charged ions trap some of the photo-excited carriers at the perovskite interface, reducing the current To study the possible conduction mechanism in the dark and under light, the I-V characteristics of microrod-based Ag/MAPbI3/Ag photo-resistor are plotted in a log V-log I scale as shown in Figure 7a,b, respectively. There are three major regions with distinct slopes, namely, the region I, II, and III, observed in Figure 7a. The slope of the fitting line in region I (between −1.4 and −0.75 V) is estimated as 2.2 (close to 2) that obeys I ∝ V 2 (child's law), demonstrating a space charge limited current (SCLC) transport mechanism. In regions II and III, the slope takes the values of 7.4 and 6.3, respectively, indicating a togenerated carrier concentration exceeds the injected carriers, while in region II, a rapid increase in the current is observed. This could be attributed to the fact that few trapped electrons absorbed the incident photons and became excited [26]. Moreover, it can be assumed that the charged ions trap some of the photo-excited carriers at the perovskite interface, reducing the current flow in region III. The accumulated charges are beneficial for the application of hybrid organic-inorganic perovskites-based photo-resistors [27] . A possible elucidation of the transport mechanism in the Ag/MAPbI3/Ag photo resistor could be the presence of interface traps generated due to vacancies and interstitials defects of MAPbI3. Inherently, when the potential is applied at the Ag electrode, the injected carriers rapidly increase at the interface and become entrapped by the traps at the Ag-MAPbI3 interface induced by the intrinsic defects of MAPbI3. The trap filling up process is demonstrated in Figure 8. These filled traps provide a smooth pathway for the conduction of electrons leading to the increased current value. Accordingly, the entrapped carriers (electrons in our case) in this region account for limiting the current flow. A possible elucidation of the transport mechanism in the Ag/MAPbI 3 /Ag photo resistor could be the presence of interface traps generated due to vacancies and interstitials defects of MAPbI 3 . Inherently, when the potential is applied at the Ag electrode, the injected carriers rapidly increase at the interface and become entrapped by the traps at the Ag-MAPbI 3 interface induced by the intrinsic defects of MAPbI 3 . The trap filling up process is demonstrated in Figure 8. These filled traps provide a smooth pathway for the conduction of electrons leading to the increased current value. Accordingly, the entrapped carriers (electrons in our case) in this region account for limiting the current flow. The photo-sensitivity characteristics of the Ag/MAPbI3/Ag-based device were performed, whereas noticeable differences in high and low currents and resistances are presented in Figure 9a,b, respectively. Moreover, under an illumination intensity of 100 mWcm −2 with an external bias voltage of 0.4 V, the device was set to a low resistance state (LRS), and during the absence of light illumination, the device exhibited a high resistance The photo-sensitivity characteristics of the Ag/MAPbI 3 /Ag-based device were performed, whereas noticeable differences in high and low currents and resistances are presented in Figure 9a,b, respectively. Moreover, under an illumination intensity of 100 mWcm −2 with an external bias voltage of 0.4 V, the device was set to a low resistance state (LRS), and during the absence of light illumination, the device exhibited a high resistance state (HRS). The applied initial electric field was weakened by the reverse electric field caused by space charges; this prevents the injection of charge carriers. Therefore, the device changes from ON to OFF. The light illumination intensity releases the trapped space charges, which disappear due to the internal electric field; hence, it switches OFF state to ON.
A comparison of the photosensitivity of an MAPbI 3 -based thin film and a 1D microrod is presented in Table 1. Here, the results of the 1D microrod indicate a superior performance in terms of photosensitivity compared to the MAPbI 3 -based thin films and even with nanowires. The photosensitivity (S) is defined in (1) as follows [29,30]: where I p and P in represent photo-current and incident light power, respectively. The I p is further defined as I p = I light − I dark .

Conclusions
In summary, we have demonstrated the possible application of MAPbI3 microrodsbased Ag/MAPbI3/Ag devices for photo-resistors. FESEM images exhibit the porous structure of microrods. An EDS study demonstrates the Pb and I as main components. In addition, the structural analysis was carried out using XRD, and the results revealed the pure formation of MAPbI3 microrods. Different conduction mechanisms were observed at different voltage ranges in the dark and under illumination. In dark conditions, the conduction behavior was dominated by typical trap-controlled charge transport mechanisms within the investigated voltage range. However, under illumination, the carrier transport is dominated by the current photogenerated mechanism. The device parameters such as average rectified current (0.11 nA), ideality factor (1.4), and barrier height (0.6 eV) were extracted using the current-voltage (I-V) characteristics of the photo-resistor. The obtained values for the Rs and Rsh are found as 130 kΩ and 3 MΩ, respectively. The results

Conclusions
In summary, we have demonstrated the possible application of MAPbI 3 microrodsbased Ag/MAPbI 3 /Ag devices for photo-resistors. FESEM images exhibit the porous structure of microrods. An EDS study demonstrates the Pb and I as main components. In addition, the structural analysis was carried out using XRD, and the results revealed the pure formation of MAPbI 3 microrods. Different conduction mechanisms were observed at different voltage ranges in the dark and under illumination. In dark conditions, the conduction behavior was dominated by typical trap-controlled charge transport mecha-nisms within the investigated voltage range. However, under illumination, the carrier transport is dominated by the current photogenerated mechanism. The device parameters such as average rectified current (0.11 nA), ideality factor (1.4), and barrier height (0.6 eV) were extracted using the current-voltage (I-V) characteristics of the photo-resistor. The obtained values for the R s and R sh are found as 130 kΩ and 3 MΩ, respectively. The results show that the perovskite microrods can potentially fabricate sensitive and fast photoelectric photo-resistor devices.
Supplementary Materials: The following are available online at https://www.mdpi.com/article/ 10.3390/ma14164385/s1, Figure S1: The image of the developed MAPbI 3 based device on ITO substrates. The image is zoomed-in and shown in right side of the image, Figure S2: Energy-dispersive X-ray spectroscopy (EDS) spectra of MAPbI3 based micro-rods showing peaks of lead (Pb) & iodine (I) as prominent components. The carbon (C) peak is also visible at low voltage values, Figure S3: XRD analysis of as-synthesis and fresh crystals of MAPbI 3 based micro-rods, Figure S4: XPS analysis survey spectra of MAPbI 3 crystals with full binding energy (0-1200 eV) and without any background subtraction and baseline correction, Table S1: Elemental composition data extracted from XPS analysis.