Single crystalline perovskites exhibit high optical absorption, long carrier lifetime, large carrier mobility, low trap-state-density and high defect tolerance. Unfortunately, all single crystalline perovskites attained so far are limited to bulk single crystals and small area wafers. As such, it is impossible to design highly demanded flexible single-crystalline electronics and wearable devices including displays, touch sensing devices, transistors, etc. Herein we report a method of induced peripheral crystallization to prepare large area flexible single-crystalline membrane (SCM) of phenylethylamine lead iodide (C6H5C2H4NH3)2PbI4 with area exceeding 2500 mm2 and thinness as little as 0.6 μm. The ultrathin flexible SCM exhibits ultralow defect density, superior uniformity and long-term stability. Using the superior ultrathin membrane, a series of flexible photosensors were designed and fabricated to exhibit very high external quantum efficiency of 26530%, responsivity of 98.17 A W−1 and detectivity as much as 1.62 × 1015 cm Hz1/2 W−1 (Jones).
Single-crystalline organic–halide-based perovskites have attracted tremendous research in the past few years due to their superior optoelectronic properties, including high optical absorption1,2,3, long carrier lifetime as much as >260 μs4, large carrier mobility (approximately 25–100 cm2 V−1 s−1) comparing to other organic semiconductors3,5,6,7, trap-state-density measured as low as 109–1010 cm−33,5,6,7, and high-exciton diffusion length reported as long as 1 mm7,8. To date, perovskite single crystals reported9 have included MAPbX3 (MA = CH3NH3, X = Cl, Br, I)3,5,6,7,10, MACaI311, MASnX312,13, FAPbX3 (FA = HC(NH2)2, X = Cl, Br, I)2,14,15,16, FASnX312,17, NH(CH3)3SnX317, Cs2PdBr618, Cs2AgBiBX619,20, CsPbX321,22,23,24, and mixed ion halide perovskites25,26,27,28,29. Unfortunately, all crystalline perovskite materials available at present are limited to bulk single crystals and wafers with thickness much larger than sub-millimeters while their lateral dimensions limited to only sub-centimeter beyond a few large crystals reported by our group1,2,3,30. As such, it is impossible to use the bulk single crystals to design highly demanded flexible electronics and wearable devices, such as displays, touch sensing devices, transistors, photosensors, and solar cells. Even though the microcrystalline perovskite thin films may be used in flexible electronic devices, their efficiencies are fairly low31,32,33. Beyond efforts in our group with limited success1,2,30, only a couple of papers reported on thin perovskite single crystals. Specifically, a cavitation-triggered asymmetric crystallization strategy has been developed to form approximately 2.3 × 1.8 mm2 sized MAPbBr3 single-crystalline sheets34. The space confined condition has been introduced to grow 6 × 8 mm2, 5 × 4 mm2, and approximately 2.8 × 3.9 mm2 perovskite crystalline thin films35,36,37. However, they are too small to be usable for real device applications. Most recently, a 120 cm2 (approximately 18.5 × 6.5 cm2) films MAPbBr3 was grown, but it is too thick (0.4 mm) to be flexible38. It appears to be indeed intrinsically challenged to grow flexible perovskite single-crystalline membrane (SCM).
Recently, two-dimensional (2D) layered lead halide perovskite has come to the spotlight for its superior environmental stability. In fact, it is recognized as a promising candidate for potential commercial applications in solar cells, light-emitting diodes, and other optoelectronics39,40,41,42,43,44,45,46,47,48,49,50. More recently, 2D layered lead halide perovskite, particularly (C6H5C2H4NH3)2PbX4 ((PEA)2PbX4, X = Cl, Br, I) compounds, have been rediscovered for their astonishing stability and potential high solar cell efficiency42,51,52. However, up to now all research has been limited to the microcrystalline thin films (MCTFs) and nanocrystalline materials. To take full advantage of its structural, optical, and electronic properties, it is imperative to prepare single crystals. Even though a few limited 2D layered (PEA)2PbI4 single-crystalline perovskites have already been prepared, unfortunately, none of them is large enough for large-area device applications. Moreover, large-area SCM is needed in order to develop larger-scale integrated optoelectronic devices. In fact, so far there are only three reports on the (PEA)2PbI4 single crystals, with dimensions limited to approximately 0.2 × 0.2, 2 × 1, and 8.7 × 3.1 mm2, respectively53,54,55. It is apparent that the inherent nature of random growth to all directions makes it challenging to control membrane thickness while at the meantime large lateral size is demanded.
In this paper, we report a “induced peripheral crystallization” (IPC) method to grow large-area SCM of (C6H5C2H4NH3)2PbI4 ((PEA)2PbI4 SCM) with well-controlled thinness to approximately 0.6 µm, while its area expanded to >2500 mm2 (73 × 35 mm2), much larger than what is reported in literature to the best of our knowledge54,55. It is found that the ultrathin single-crystalline perovskite membrane displays ultralow defect density, long-term stability, and excellent flexibility. Meanwhile, we have designed and fabricated flexible photosensors using the ultrathin large (PEA)2PbI4 SCM. It is found that the present photosensor shows very high external quantum efficiency (EQE) as much as 26,530%, responsivity (R) as high as 98.17 A W−1, and detectivity (D*) as large as 1.62 × 1015 cm Hz1/2 W−1 (Jones). It should be noted that this detectivity value is not only among the highest detectivity reported to date for all single-crystalline and thin-film perovskite photosensors56, it is even higher than devices based on the state-of-the-art material including single-crystalline silicon56, InGaAs57, GaAs58, CdTe59, and GaN60. Moreover, the flexible membrane photosensor shows excellent mechanical stability.
There have been two typical methods developed to grow the hybrid lead halide perovskite CH3NH3PbI3 single crystals. The first uses hydrogen iodide acid as the solvent in which the solubility of perovskite increases as temperature rises. By slowly lowering the temperature of the saturated solution, the crystals are harvested7,61. In comparison, the second one uses γ-butyrolactone (GBL) as the solvent in which solubility of the perovskite decreases as temperature rises. The crystals were collected by first preparing a saturated solution and then slowly increases its temperature to enter into the oversaturation zone1,2,3.
There are a few key parameters that are known to affect crystal quality and its growth process. In general, the lower the growth rate, the higher the crystalline quality is. The crystal growth is directly controlled by two processes: the first is solute diffusion from the solution to the crystallite surface, and the second is the solute deposition onto the crystallite. The former can be well controlled by regulating solution temperature for the diffusion rate that is well known to change exponentially with the temperature62. However, it is difficult to control the solute deposition process. We therefore maintain the process well under the diffusion-controlled region and use relatively low temperature to regulate the diffusion rate, hence the crystal growth rate and quality. On the other hand, it is key to control the growth along the solubility curve for, when it is in the well-oversaturated region, small crystallites form instantly with plenty of defects. When it goes into the unsaturated region, the crystal formed may start to be dissolved into the solution. Only when the solute concentration is controlled just over the solubility curve or slightly oversaturated, the crystallization kinetics allows high-quality crystal growth on the already formed crystallite or seed with no extraneous nucleation63.
More quantitatively, crystal growth rate is directly proportional to the first-order derivative of solubility and the temperature ramp rate according to the oversaturation model64:
where m is the mass of the crystal, C the solution concentration, and V the solution volume that changes very little during the entire crystallization process, hence can be treated as a constant. Figure 1a shows the solubility of (PEA)2PbI4 perovskite in the GBL solvent measured as a function of temperature. It is clear that, in the temperature range of 27–106 °C, the solubility of (PEA)2PbI4 increases with temperature. Based on the solubility data measured in Fig. 1a, its first-order derivative with respect to temperature is calculated and plotted in Fig. 1b. As the solution temperature can be well controlled over time, so is the temperature ramp rate. Once the temperature is set, the solubility derivative is defined based on the curve in Fig. 1b.
To grow single crystals along lateral dimensions while limiting its growth in thickness, it is critical to selectively control its growth rate along different directions. It is found that the best temperature range is 25–80 °C in which the solubility derivative is about 3.45 × 10−4, apparently lower comparing to its value 8.47 × 10−4 at higher temperature beyond 80 °C, as shown in Fig. 1b. For the best quality at acceptable growth rate, we further regulated the temperature ramp rate to 1 °C h−1.
Figure 2a illustrates the IPC growth procedure. Briefly, PbI2 and C6H5C2H4NH3I (1:2 molar ratio) were dissolved in γ-butyrolactone (GBL) at 80 °C under active mixing for 24 h to generate the (PEA)2PbI4 precursor solution (2.12 M). The solution was then filtered prior to crystal growth. For the growth of the (PEA)2PbI4 SCM, a drop of the prepared precursor solution was pipetted onto a glass slide substrate (or flexible plastic substrate, polyethylene terephthalate (PET) substrate) preheated to 80 °C as shown in step 1. Then, a second glass slide with smaller lateral dimensions was placed onto the precursor solution drop. The solution was squeezed to spread evenly between two slides (step 2). It should be noted that part of the precursor solution was squeezed out to the edge of the top slide. Step 3 is to maintain the temperature at 80 °C in an enclosed oven. In such case, the evaporation of the precursor solution along the edge of the top slide was well controlled at a consistent rate. In about 2 h, nucleation and crystallization occurred at the edge of the top slide, as evidenced by some shinny crystallites. Further gradient decrease of the temperature from 80 to 30 °C at a rate of 1 °C h−1 led to the growth of the (PEA)2PbI4 SCM between slides (step 4). In order to avoid crystallite growth in solution, the precursor was prepared at 80 °C with concentration controlled at 2.12 M (PEA)2PbI4 in GBA to warrant an unsaturated solution free of particulates that may serve as nucleation seeds. Everything used in the process, including glass slides and pipet, were preheated to 80 °C to avoid local temperature change and associated crystallization during the entire operation of steps 1–3. At this temperature, the solution (2.12 M) is unsaturated, therefore there is no possibility of crystallite formation anywhere. As the solvent around edges of the second glass slide was evaporated, the local solution concentration was slowly increased. When it surpasses the solubility curve, small crystallites start to form and grow larger. In step 4, temperature of the set-up was gradually lowered. When it was dropped to below 75 °C, the solution became oversaturated, leading to crystal growth surrounding the nucleation seeds. As the process continues, the crystals grow into the slit until they filled the entire space. It is of vital importance for the edges of the second plate to provide nucleation sites to direct the crystals to grow inwards into the slit, rather than to form nanocrystalline powder from the solution. Figure 2b shows five photographs of the (PEA)2PbI4 SCMs completed at different stages of the growth process. It shows that, without any seed crystal in the slit, there was no crystal formed when the temperature was kept at 80 °C. This is expected for, at the 80 °C, the solution is unsaturated. As the temperature was dropped to 72 °C, small crystallites were formed along the edge of the glass slide. When the temperature was dropped to 64 °C, the small crystallite grew larger and eventually forming 5 × 3 mm2 SCM in the slit. When the temperature was further lowered to 53 °C, the SCM grew larger to a 26 × 15 mm2 SCM. Apparently, the perovskite crystallites are formed from the edge of the second slide, they then grow larger into the slit until the space is filled. However, when the identical procedure was carried out in a closed petri dish without using any slide from 80 to 30 °C, there formed a few well-shaped single crystals with habitant rectangular parallelepiped, as shown in Fig. 2c.
Thickness control and flexibility
Figure 3a, b and Supplementary Fig. 1a, b present three-dimensional (3D) atomic force microscopy (AFM) images, with the height profiles clearly revealing successful fabrication of (PEA)2PbI4 SCM in thickness of 1.56 and 1.21 μm, respectively. It is found that the thickness of the (PEA)2PbI4 SCMs can be controlled by adjusting the cooling rate. The thickness distribution of the (PEA)2PbI4 SCMs obtained with various cooling rates are as shown in Supplementary Fig. 2. Figure 3c provides cross-sectional scanning electron microscopic (SEM) images of a few typical (PEA)2PbI4 SCMs prepared using the IPC method with thickness ranging from 0.6 to 50 μm, with detailed characterizations and analyses shown in Supplementary Fig. 3. Supplementary Fig. 3a, b presents photos and SEM images of a representative (PEA)2PbI4 SCM, there is no cracking found in the area of 4.1 × 1.8 mm2 inspected. Careful examination at higher resolution (Supplementary Fig. 3c) further confirms that the SCM is indeed single crystalline without observable grain boundaries. Supplementary Fig. 3d, e provides analysis using the energy-dispersive X-ray spectroscopy (EDS). It shows that the atomic ratio: C:Pb:I is approximately 18:1:4, consistent with the stoichiometry of (C6H5C2H4NH3)2PbI4. In addition, EDS mapping analysis (Supplementary Fig. 3f–i) over area 0.56 × 0.88 mm2 shows very uniform atomic distribution. Moreover, there are some terraces observed along the edge of the (PEA)2PbI4 SCMs (Supplementary Fig. 4), demonstrating that the (PEA)2PbI4 SCM is indeed a layered (2D) material. It is worthwhile to note that the 2D layered perovskite (PEA)2PbI4 SCMs are flexible. As shown in Fig. 3d, the (PEA)2PbI4 SCM with thickness of 3.5 μm can be wrapped around on a small tube (1.6 cm in diameter) without any deformation, demonstrating that the (PEA)2PbI4 SCM is of very good flexibility. In fact, the (PEA)2PbI4 SCM can be flexed in a wide range without observable fracture. Figure 3e illustrates the measurement procedure for the flexing angle, the maximum bending angle tolerated before fracture, and Supplementary Fig. 5 shows a test for a 7.14-μm-thick membrane in the range of flexing angle from 45° to 195°. Figure 3f shows the flexing angle as a function of the (PEA)2PbI4 SCM thicknesses. It is found that, the thinner the membrane, the larger the flexing angle, the more flexible it is. Moreover, the curve showed a biexponential feature, consistent with the calculated result from elastic flexing deformation model for the layered materials (details described in Supplementary Fig. 6)65.
where L is the maximum stretching length, α is the flexing angle, and d is half the thickness of the (PEA)2PbI4 SCM.
The above results demonstrate that the IPC is indeed a highly effective method to fabricate large-area flexible (PEA)2PbI4 SCM. More importantly, flexible PET substrate has also been successfully tested to grow the (PEA)2PbI4 SCM, as the samples shown in Supplementary Fig. 7. Compared to the brittle 3D perovskite single crystals, e.g., MAPbX3 and FAPbI3 as we reported earlier1,2,3,30, the 2D flexible layered (PEA)2PbI4 SCM is of obvious advantages in flexible electronic devices, including flexible displays, wearable electronics, portable devices, ultrathin transistors, and special sensors.
X-ray diffraction (XRD), grazing-incidence wide-angle X-ray scattering (GIWAXS), and transmission electron microscopy (TEM) have been used to characterize the (PEA)2PbI4 SCM samples. Figure 4a shows a photo of a typical (PEA)2PbI4 SCM (73 × 35 mm2) on glass substrate used for the XRD measurement. The XRD in Fig. 4b shows a series of sharp, intense, and well-defined diffraction peaks repeating periodically, signature of the (00h) (h = 1, 2, 3…) planes in layered (PEA)2PbI4 crystalline structure54,55 as shown in Fig. 4c. As it was previously observed, the 2D plane of the (PEA)2PbI4 SCM are preferentially parallel to the substrate45,55. Supplementary Fig. 8 shows the rocking curve corresponding to the (005) plane with the full-width at half maximum (FWHM) only 0.1055°, demonstrating respectable crystalline quality. To gain more insights into the orientation, GIWAXS were performed on both the (PEA)2PbI4 SCM and a sample of corresponding MCTF. The GIWAXS image and the intensity versus q for the scattering features of the (PEA)2PbI4 SCM are shown in Fig. 4d and Supplementary Fig. 9, respectively. We observed sharp, discrete Bragg spots at q values of 10.14, 14.40, 16.16, 20.13, and 22.66 nm−1, corresponding to the (00h) (h = 1, 2, 3…) planes in layered (PEA)2PbI4 crystalline structure. This indicates perfect ordering and closed packing between each crystalline slab. Meanwhile, the synchrotron diffraction data indicate that the major perovskite growth is confined within the (00h) plane that is perpendicular to the qz direction66. In contrast, strong diffraction rings at q = 18.8 nm−1 and q = 23.8 nm−1 are observed for the microcrystalline counterpart (Supplementary Fig. 10), indicating considerable randomness in the orientation of the crystal grains due to the discontinued/misaligned stacking. The (PEA)2PbI4 SCM was further studied using high-resolution TEM analysis (HRTEM). Figure 4e shows the TEM image and Fig. 4f shows the crystal lattice image of the (PEA)2PbI4 SCM with a lattice spacing of 0.27 nm, corresponding to the perovskite (006) plane, consistent with the XRD result.
Optical and transport properties
Optical properties of the (PEA)2PbI4 SCM were thoroughly studied, with the absorption spectrum showing a sharp absorption edge at 550 nm, corresponding to the bandgap of 2.28 eV (Fig. 5a). This phenomenon is consistent with the absorption curve reported independently by other group on bulk crystals54. The optical band gaps estimated from the corresponding Tauc plots show values of 2.28 and 2.35 eV for the (PEA)2PbI4 SCM and MCTF (Supplementary Fig. 11), respectively, in good agreement with previous report53,54. From ultraviolet photoelectron spectroscopy (UPS) results, we estimated the valence band edge position of (PEA)2PbI4 SCM to be −5.90 eV and for MCTF at −5.44 eV, relative to the vacuum level (Fig. 5b and Supplementary Fig. 12). The (PEA)2PbI4 SCM and MCTF samples were further characterized by photoluminescence (PL) spectra with a 375 nm laser excitation, as shown in Fig. 5c. The sharp and narrow peak at 525 nm (FWHM = 15.1 nm) demonstrates the high color purity (narrow emission bandwidth) of the (PEA)2PbI4 SCM, an attractive feature for light-emitting applications. The PL peak centered at 521 nm for the MCTF (PEA)2PbI4 is slightly blue-shifted compared to that in the (PEA)2PbI4 SCM located at 525 nm, indicating that the latter is indeed the SCM with lower defect density67. In addition, the PL intensity of the (PEA)2PbI4 SCM is much higher than that of the (PEA)2PbI4 MCTF under same test condition, as shown in the inset photograph. Figure 5d, e shows photos of the (PEA)2PbI4 SCM taken under weak room light and ultraviolet (UV) lamp, respectively. It shows that, under the weak white light, the membrane appears to be yellowish in color and very uniform across the surface area. When it is exposed to strong UV irradiation, it becomes bright green with very uniform appearance. Apparently, the UV lamp has effectively excited the PL peaked at 525 nm. The PL lifetimes of the (PEA)2PbI4 SCM and MCTF were measured using time-resolved PL. As shown in Fig. 5f, the decay curves show a biexponential feature with average lifetime of 1.3 and 0.6 ns, respectively. More interestingly, we found that the (PEA)2PbI4 SCM shows characteristic excitation-dependent fluorescence behavior, with the observed emission peaks shifting from 525 to 530 nm and to 520 nm with excitation wavelengths as shown in Fig. 5g. Specifically, when the excitation wavelength is <400 nm, the emission peak position is at 525 nm. When the excitation wavelength is changed from 400 to 480 nm, the emission peak shifts from 525 to 530 nm. Further increasing the excitation wavelength, the emission peak is shifted from 530 to 520 nm. This characteristic feature can also be observed on the MCTFs (Supplementary Fig. 13).
The PL is also used to study uniformity of the (PEA)2PbI4 SCM sample. Surprisingly, the PL emission peak from 44 different points taken across the SCM is sharply centered at 525 nm, with FWHM distributed within 14.8 ± 0.14 nm. More surprisingly, their peak intensity is maintained essentially the same at 3.87 ± 0.02 × 104 counts (Fig. 5h and Supplementary Table 1). The standard deviation for these 44 tests is as low as 0.53% of their average intensity and only 0.95% for the FWHM, demonstrating good uniformity over large area for the high quality (PEA)2PbI4 SCM. The automated PL intensity and lifetime mapping performed over surface area of 1 cm2 also exhibits far superior uniformity comparing to the corresponding MCTF (PEA)2PbI4 sample (Supplementary Fig. 14). The excellent optical uniformity makes it a promising candidate for large-area optoelectronic applications.
Trap-state density is another key figure-of-merit for optoelectronic and photovoltaic applications. Both electron-only and hole-only devices were therefore designed and fabricated for the measurement using the space-charge-limited current (SCLC) method3. The dielectric constants (ε) was determined to be 5.8 ± 0.1 from the capacitance–frequency measurement in the range of 100 kHz to 30 MHz by impedance analyzer (Supplementary Fig. 15). Supplementary Fig. 16 presents the dark current–voltage (I–V) curves for the single-carrier devices using the (PEA)2PbI4 SCM. Based on 8 measurements, the hole-trap density (ntrap) was calculated as (8.18 ± 2.67) × 1010 cm-3 (Supplementary Table 2), and the electron-trap density was calculated as (1.66 ± 0.88) × 1011 cm−3 (Supplementary Table 3). With low defect density and uniformity, the (PEA)2PbI4 SCM should be ideal for optoelectronic applications. For real-world usage, stability becomes a critical factor for consideration. The thermal stability of the (PEA)2PbI4 SCM was evaluated using thermogravimetric analysis (TGA), as shown in Supplementary Fig. 17. It shows that the (PEA)2PbI4 SCM does not exhibit any observable degradation until 230 °C. We also tested its stability in high humidity environment by subjecting it to approximately 65% relative humidity at 25 °C for 32 days. For the stability measurement, XRD was collected on a daily basis during the test period. As shown in Supplementary Fig. 18, there is no detectable decomposition in the XRD patterns after the long-term exposure, which suggests that the (PEA)2PbI4 SCM is highly stable in humid condition. As its MCTF counterpart decomposes after 24 h in the same test, it is believed that the better stability of SCM is attributed to essentially eliminated solvent residues, grain boundaries, inclusions, and voids within the crystal. Supplementary Fig. 19 shows water contact angle tests to compare SCM with MCTF. While the contact angle for the reference MCTF sample measured is only 76°, it is increased to as much as 94° for the (PEA)2PbI4 SCM sample, demonstrating that the (PEA)2PbI4 SCM is significantly poorer in wettability or better in water/moisture resistance.
Device performance of flexible photosensor
With all above superior properties including low defect density, good uniformity, long-term stability and adequate flexibility, we are inspired to expand its application into flexible photosensors, as designed with the architecture schematically illustrated in Supplementary Fig. 20 and the working mechanism is described in Fig. 6a, b. Please note that the devices in this manuscript are designed using the metal–semiconductor–metal structure with interdigitated electrodes. As the photogenerated electrons may be trapped by shallow defects, holes may traverse between the electrodes for multiple times before recombination, in other words, holes drift along the electric field until they reach the electrode while electrons remain trapped in “doping centers.” To maintain charge neutrality, mobile holes are continuously recirculated between electrodes (majority carrier recirculation)68,69. Consequently, for each electron–hole pair created, holes may bounce between two electrodes repeatedly for multiple times, resulting in recirculation for abnormally high photoconductive gain.
The effectively illuminated device area is measured to be 4.54 × 10−2 mm2. In order to study its response as a function of bias and light intensity, the I–V curves were measured in dark and under 460 nm light illumination with intensity ranging from 8 × 10−5 to 310 mW cm−2 (Fig. 6c). The dark current is measured as low as 1.62 × 10−3 nA or 3.57 × 10−6 mA cm−2 at 2 V bias; the light current of the same device increases to 1068 nA or 2.35 mA cm−2 under illumination intensity of 10 mW cm−2, exceeding 5 orders of magnitude enhancement comparing to its dark current. It should be noted that, the dark current of the present (PEA)2PbI4 SCM device is strikingly lower than the control device made of 3D perovskite single-crystal wafer (Supplementary Table 4). In general, the dark current decreases as the material quality increases. In other words, devices with fewer defects are expected to show lower dark current. To compare the optoelectronic performance between the (PEA)2PbI4 SCM and MCTF, the I–V curves of their corresponding devices were measured under illumination, as shown in Supplementary Fig. 21. Under the same illumination condition, photocurrent of the (PEA)2PbI4 MCTF device measured only 0.12 nA or 2.64 × 10−4 mA cm−2, about 8900 times smaller.
The key sensor parameters such as R, EQE, and D* are calculated and provided in Supplementary Information. Figure 6d shows the photoresponse as a function of the incident light intensity. Both the photocurrent density and R show good linear correlation with high correlation coefficients (0.999). It can be seen that the photocurrent of the SCM devices show a linear response from 8 × 10−5 to 310 mW cm−2, with an linear dynamic range (LDR) of 124 dB. Figure 6f shows the EQE for the flexible photosensor based on the (PEA)2PbI4 SCM within the illumination intensity ranging from 8 × 10−5 to 310 mW cm−2 at wavelength of 460 nm under a 4 V bias. To obtain the detectivity (D*), we first directly recorded the noise current by a dynamic signal analyzer, a method that has been well established by Tang et al. and Huang et al.69,70. As shown in Fig. 6e, the measured average noise current of the (PEA)2PbI4 SCM photosensor is approximately 1.29 × 10−15 A Hz−1/2. It can be seen that the noise current is independent of the frequency, indicating that the noise of the present devices is not dominated by the 1/f noise due to the minimized trap density and the absence of grain boundaries in the (PEA)2PbI4 SCMs69,70. The two main noise sources are the shot noise (in,s) and the thermal noise (in,t), respectively. The shot noise (in,s) can be calculated from the dark current using the following equation:
where id is the dark current, e the elementary charge, and B the electrical bandwidth. Based on dark current of the device at 4 V bias, the shot noise is calculated to be 9.12 × 10−16 A Hz−1/2. Besides the shot noise, the thermal noise (in,t) is determined by the following equation:
where kB is the Boltzmann constant, T the temperature, and R the resistance of the (PEA)2PbI4 SCM photosensor. Based on the dark current curve, the resistance at 4 V is obtained and so that the thermal noise is calculated to be 1.03 × 10−16 A Hz−1/2. Undoubtedly, large resistivity of the photosensor resulted in low dark current, small shot noise, and low thermal noise. The total noise (in,T) can be calculated according to the expression below:
As a result, the calculated total noise limit 9.18 × 10−16 A Hz−1/2 by only considering the shot noise and thermal noise is very close to the measured noise 1.29 × 10−15 A Hz−1/2. Based on the measured dark current noise (in) and the responsivity (R) of the photosensor, the noise equivalent power (NEP) can be calculated by the following equation:
Accordingly, the specific detectivity (D*) of the photosensor is deduced by the following equation:
where A is the active area of the device and B the electrical bandwidth. Finally, D* is calculated and shown in Fig. 6f as a function of the illumination intensity ranging from 8 × 10−5 to 310 mW cm−2 at wavelength of 460 nm with a fixed 4 V bias. Because of more charge recombination occurred under higher illumination intensity, all values of R, EQE, and D* decrease as the incident light intensity increases. Figure 6g shows its spectral photocurrent response. As expected, the photosensor shows high response in the wavelength region of 350–550 nm, consistent with its optical absorption. R, EQE, and D* against various wavelength under a fixed 4 V bias are calculated and shown in Supplementary Fig. 22. Under the lowest measured incident light, power density achieves 8 × 10−5 mW cm−2, and the highest R, EQE, and D* are calculated to be 98.17 A W−1, 2.65 × 104% and 1.62 × 1015 cm Hz1/2 W−1 (Jones), respectively. Note that the extraordinarily high D* value of the present device (exceeding 1015 cm Hz1/2 W−1) is among the record high reported for the perovskite photosensors so far, and it is even higher than that of devices based on single-crystalline silicon56, InGaAs57, GaAs58, CdTe59, and GaN60, demonstrating much superior quality of the 2D layered (PEA)2PbI4 single-crystalline perovskite membrane material.
Supplementary Fig. 23a presents the time-dependent on/off cycle test. Clearly, the device is very stable during the test process under multiple repeated on/off cycles with the bias at 0.5, 1, 2, 3, and 4 V. The photocurrent response as a function of bias voltage of the photosensors is provided in Supplementary Fig. 23b. It is found that there is a good linear correlation with high correlation coefficients (approximately 1). Furthermore, we measured the response time of the (PEA)2PbI4 SCM photosensors. The rise time (trise) is generally defined in literature as time needed for the photocurrent to rise from 10% peak value to 90% and inverse for the decay time (tdecay). As shown in Fig. 6h, the photosensor shows the response speed with the photocurrent rise and fall times as 64 and 52 µs, respectively. Figure 6i depicts the plot of the frequency responses of the photosensor, showing a −3 dB cutoff frequency up to 10.72 KHz. Undoubtedly, the fast photocurrent response of these photosensors can be attributed to very low defect density of the SCM. More detailed comparison is provided in Supplementary Table 5.
Apart from the stability and detectivity, the mechanical flexibility is also an important parameter for the photosensors. To assess the flexibility of the present (PEA)2PbI4 SCM photosensor, the optoelectronic performance of the device has been measured precisely at various bending angles under constant incident light intensity. The corresponding photocurrents are shown in Supplementary Fig. 24a–f. When compared with the original data given in Supplementary Fig. 24a, the responsivities decrease slightly, and the reduction is calculated to be approximately 8%, even when the sensor is bent to 155° of flexing angle (Supplementary Fig. 24f), thus demonstrating the superior flexibility of the photosensor.
In summary, we have developed an effective process to grow high-quality flexible 2D layered (PEA)2PbI4 SCM. Under optimal temperature ramp rate, the size of these SCMs is >73 × 35 mm2, with thickness as thin as 0.6 μm. As far as we know, this is the first time to grow flexible perovskite SCM with thickness thinner than 10 μm and area exceeding 2500 mm2. XRD, GIWAXS, and TEM analyses confirm that the SCMs are of layered structure. In addition, the SCM displays very low defect density, long-term stability, and excellent flexibility. It is also found that the as-synthesized (PEA)2PbI4 SCM shows excitation-dependent fluorescence behavior. Finally, the flexible perovskite SCM with large surface area opens a way for its application in high-performance flexible planar photosensors. The successful growth and further utilization of the flexible 2D layered (PEA)2PbI4 SCM not only provide a new material system but also open up an avenue to applications in optoelectronics.
GBL (99%) and Lead iodide (PbI2, 99%) were purchased from Aladdin Reagent Ltd. Phenylethylammonium iodide (PEAI, 99%) was purchased from Xi’an Polymer Light Technology Corp. All the chemicals were used as received without further purification.
Fabrication of the (PEA)2PbI4 single-crystal membranes (SCMs)
Induced peripheral crystallization procedure is schematically illustrated in Fig. 2a. Briefly, PbI2 and PEAI (1:2 molar ratio) were dissolved in GBL at 80 °C under active mixing for 24 h to generate the (PEA)2PbI4 precursor solution (2.12 M). The solution was then filtered prior to crystal growth. For the growth of the (PEA)2PbI4 SCM, a drop of the prepared precursor solution was pipetted onto a glass slide substrate (or flexible plastic substrate, PET substrate) preheated to 80 °C as shown in step 1. Then a second glass slide with smaller lateral dimensions was placed onto the precursor solution drop. The solution was squeezed to spread evenly between two glass slides (step 2). It should be noted that part of the precursor solution was squeezed out to the edge of the top slide. Step 3 is to maintain the temperature of the entire assembly at 80 °C in an enclosed oven. In such case, the evaporation the precursor solution along the edge of the top slide was well controlled at a consistent rate. In about 2h, nucleation and crystallization occurred at the edge of the top slide, as evidenced by some shinny crystallites formed along the edges of the second slide. Further gradient decrease of the temperature from 80 to 30 °C at a rate of 1 °C h−1 led to the growth of the (PEA)2PbI4 SCM between the slides (step 4).
Fabrication of the (PEA)2PbI4 MCTFs
The glass substrate was cleaned by successive sonication with acetone, isopropanol, and ethanol for 30 min and then dried with N2 flow. The clean substrate was then treated with UV-Ozone for 15 min before solution casting. Precursor solution (70 μL) was dropped on the fresh-prepared glass substrate followed by spin-coating at 5000 r.p.m. for 20 s without delay. The as-cast films were then annealed at 100 °C for 10 min. The spin-coating was accomplished under inert atmosphere inside a nitrogen-filled glove box.
Fabrication of devices for relative dielectric constant (ε) measurements
Seven devices were fabricated by depositing Au electrodes (100-nm thickness) on two opposite surfaces of the (PEA)2PbI4 SCMs.
Fabrication of devices for SCLC measurements
The devices were fabricated by depositing the Au electrodes (approximately 100-nm thickness) with the architecture of Au/(PEA)2PbI4 SCM/Au for hole-only devices and Au/PCBM/(PEA)2PbI4 SCM/PCBM/Au for electron-only devices.
Fabrication of the (PEA)2PbI4 SCM planar photodetectors
Planar photodetectors were fabricated by depositing interdigital Au electrodes (200-nm thickness) via vacuum evaporation method on the (PEA)2PbI4 SCMs and (PEA)2PbI4 MCTFs. The bridging gap of electrode width is 20 μm, while the effective illuminated area of each device was about 4.54 × 10−2 mm2.
Powder XRD and high-resolution XRD on SC wafer: XRD patterns were collected using a Bruker D8 Advance X-ray diffractometer equipped with a Cu tube (λ = 1.5406 Å) operated at 40 kV and 20 mA. High-resolution XRD measurement was taken using X’Pert MRD, with Cu Kα1 line (λ = 1.5406 Å) with V = 40 KV and I = 20 mA.
Grazing-incidence wide angle X-ray scattering: GIWAXS measurements were performed at D line at the Cornell High Energy Synchrotron Source. The wavelength of the X-rays was 1.157 Å with a bandwidth Δλ/λ of 1.5%. The scattering signal was collected by Pilatus 200 K detector, with a pixel size of 172 × 172 µm2 placed at 191 mm away from the sample position. The incident angle of the X-ray beam was at 0.30° and the integration time was 1 s.
Thermal analysis: TGA was performed on a TA SDT-Q600 V20.9 (Build 20). The sample was placed in an Al2O3 crucible and heated in an interval from room temperature to 800 °C at a ramp rate 5 °C min−1 under flowing nitrogen gas with a flow rate 100 mL min−1. About 3 mg of (PEA)2PbI4 SCM powder was used for the TGA measurements.
UV-Vis-near infrared (NIR) absorbance spectra measurements: UV-Vis absorbance spectrum of (PEA)2PbI4 SCMs and (PEA)2PbI4 MCTFs were measured using a Perkin-Elmer Lambda 950 UV-Vis-NIR spectrophotometer equipped with an integrating sphere attachment operating in the 300–800 nm region at room temperature.
UPS measurements: UPS was performed on a photoelectron spectrometer (ESCALAB 250Xi, Thermo Fisher Scientific) to study the working function of the (PEA)2PbI4 SCMs and (PEA)2PbI4 MCTFs.
Steady-state and time-resolved PL measurements: Steady-state and time-resolved PL measurements of (PEA)2PbI4 SCMs and (PEA)2PbI4 MCTFs were taken using a PicoQuant FT-300 and FT-100, with 375 nm excitation wavelength. All PL spectra were measured in air without encapsulation.
Relative dielectric constant measurements: Capacitance of the (PEA)2PbI4 SCMs were determined using the impedance analyzer (Agilent 4294 A Precision LCR Meter) over a wide frequency range from 100 kHz up to 30 MHz (Figure S10a). The relative dielectric constant of the prepared samples was calculated using the capacitance.
SCLC measurements: The single carrier devices were fabricated and used to measure the trap-state density by using the SCLC method for the (PEA)2PbI4 SCMs. The structure is Au/(PEA)2PbI4 SCM/Au for hole-only devices and Au/PCBM/(PEA)2PbI4 SCM/PCBM/Au for electron-only devices. The dark I–V curve was measured using the Keithley 4200 semiconductor characterization system and was used to calculate the trap-state density.
Photosensor performance measurements: All device performance characterizations were done in a dark box with optical and electrical shielding to minimize electromagnetic and ambient light disturbance. The photoresponse characteristics were measured using the Keithley 4200 semiconductor characterization system and a manual probe station under various bias voltages. To measure the response speed, a 462 nm semiconductor laser driven by a signal generator (Tektronix, AFG3252C) was used as the light source to generate pulsed laser beam, and the temporal response of the device was measured by using a Low-Noise Current Preamplifier (Stanford Research System, SR570) with a Mixed Domain Oscilloscope (Tektronix, MDO3104). For wavelength-dependent photocurrent measurement, the spectrum was generated by modulating a xenon lamp equipped with a monochromator. Noise currents were measured by using a spectrum analyzer (Keysight 35670 A). A resistor (10 MΩ) was connected in series with the device and the frequency analyzer was connected in parallel with the device. The signal can be read out as V Hz−1/2 from the frequency analyzer in the range of ~10–1000 Hz, and the corresponding current was calculated by dividing the resistance of the perovskite SCM. The incident intensity was measured using an Optical Power Meter (VEGA OPHIR PD300-UV) and calibrated with a silicon photodetector. All measurements were taken at room temperature.
Electron microscopy: SEM imaging was performed on a field-emission SEM (SU-8020, Hitachi). TEM and HRTEM imaging was conducted on a FEI Tecnai G2 F20.
Atomic force microscopy (AFM): AFM images were acquired on a Bruker Dimension ICON instrument.
Photography: Photographs in this manuscript were taken by using an eight-mega-pixel digital camera.
The data that support the plots within this Article and other findings of this study are available from the corresponding authors upon reasonable request.
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).
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).
Liu, Y. et al. Two-inch-sized perovskite CH3NH3PbX3 (X = Cl, Br, I) crystals: growth and characterization. Adv. Mater. 27, 5176–5183 (2015).
Zhang, F. et al. Perovskite CH3NH3PbI3-xBrx single crystals with charge-carrier lifetimes exceeding 260 μs. ACS Appl. Mater. Interfaces 9, 14827–14832 (2017).
Shi, D. et al. Low trap-state density and long carrier diffusion in organolead trihalide perovskite single crystals. Science 347, 519–522 (2015).
Saidaminov, M. I. et al. High-quality bulk hybrid perovskite single crystals within minutes by inverse temperature crystallization. Nat. Commun. 6, 7586 (2015).
Dong, Q. et al. Electron-hole diffusion lengths >175 mum in solution-grown CH3NH3PbI3 single crystals. Science 347, 967–970 (2015).
Zhang, F., Yang, B., Li, Y., Deng, W. & He, R. Extra long electron–hole diffusion lengths in CH3NH3PbI3−xClx perovskite single crystals. J. Mater. Chem. C 5, 8431–8435 (2017).
Liu, Y., Yang, Z. & Liu, S. Z. Recent progress in single-crystalline perovskite research including crystal preparation, property evaluation, and applications. Adv. Sci. 5, 1700471 (2018).
Nayak, P. K. et al. Mechanism for rapid growth of organic-inorganic halide perovskite crystals. Nat. Commun. 7, 13303 (2016).
Uribe, J. I., Ramirez, D., Osorio-Guillén, J. M., Osorio, J. & Jaramillo, F. CH3NH3CaI3 perovskite: synthesis, characterization, and first-principles studies. J. Phys. Chem. C 120, 16393–16398 (2016).
Dang, Y. et al. Formation of hybrid perovskite tin iodide single crystals by top-seeded solution growth. Angew. Chem. Int. Ed. 55, 3447–3450 (2016).
Yao, Z. et al. Local temperature reduction induced crystallization of MASnI3 and achieving a direct wafer production. RSC Adv. 7, 38155–38159 (2017).
Zhumekenov, A. A. et al. Formamidinium lead halide perovskite crystals with unprecedented long carrier dynamics and diffusion length. Acs Energy Lett. 1, 32–37 (2016).
Han, Q. et al. Single crystal formamidinium lead iodide (FAPbI3): insight into the structural, optical, and electrical properties. Adv. Mater. 28, 2253–2258 (2016).
Saidaminov, M. I., Abdelhady, A. L., Maculan, G. & Bakr, O. M. Retrograde solubility of formamidinium and methylammonium lead halide perovskites enabling rapid single crystal growth. Chem. Commun. 51, 17658–17661 (2015).
Dang, Y. et al. Crystallographic investigations into properties of acentric hybrid perovskite single crystals NH(CH3)3SnX3 (X = Cl, Br). Chem. Mater. 28, 6968–6974 (2016).
Sakai, N. et al. Solution-processed cesium hexabromopalladate(IV), Cs2PdBr6, for optoelectronic applications. J. Am. Chem. Soc. 139, 6030–6033 (2017).
Slavney, A. H., Hu, T., Lindenberg, A. M. & Karunadasa, H. I. A bismuth-halide double perovskite with long carrier recombination lifetime for photovoltaic applications. J. Am. Chem. Soc. 138, 2138–2141 (2016).
McClure, E. T., Ball, M. R., Windl, W. & Woodward, P. M. Cs2AgBiX6(X = Br, Cl): new visible light absorbing, lead-free halide perovskite semiconductors. Chem. Mater. 28, 1348–1354 (2016).
Dirin, D. N., Cherniukh, I., Yakunin, S., Shynkarenko, Y. & Kovalenko, M. V. Solution-grown CsPbBr3 perovskite single crystals for photon detection. Chem. Mater. 28, 8470–8474 (2016).
Song, J. et al. Ultralarge all-inorganic perovskite bulk single crystal for high-performance visible-infrared dual-modal photodetectors. Adv. Opt. Mater. 5, 1700157 (2017).
Stoumpos, C. C. et al. Crystal growth of the perovskite semiconductor CsPbBr3: a new material for high-energy radiation detection. Cryst. Growth Des. 13, 2722–2727 (2013).
Saidaminov, M. I. et al. Inorganic lead halide perovskite single crystals: phase-selective low-temperature growth, carrier transport properties, and self-powered photodetection. Adv. Opt. Mater. 5, 1600704 (2017).
Zhang, Y., Liu, Y., Li, Y., Yang, Z. & Liu, S. Z. Perovskite CH3NH3Pb(BrxI1−x)3 single crystals with controlled composition for fine-tuned bandgap towards optimized optoelectronic applications. J. Mater. Chem. C 4, 9172–9178 (2016).
Wei, H. et al. Dopant compensation in alloyed CH3NH3PbBr3-xClx perovskite single crystals for gamma-ray spectroscopy. Nat. Mater. 16, 826–833 (2017).
Miao, X. et al. Air-stable CsPb1−xBixBr3 (0 ≤ x≪1) perovskite crystals: optoelectronic and photostriction properties. J. Mater. Chem. C 5, 4931–4939 (2017).
Huang, Y. et al. The intrinsic properties of FA(1−x)MAxPbI3 perovskite single crystals. J. Mater. Chem. A 5, 8537–8544 (2017).
Zhang, T. et al. A facile solvothermal growth of single crystal mixed halide perovskite CH3NH3Pb(Br1-xClx)3. Chem. Commun. 51, 7820–7823 (2015).
Liu, Y. et al. 120 mm Single-crystalline perovskite and wafers: towards viable applications. Sci. China Chem. 60, 1367–1376 (2017).
Cao, F. et al. Novel perovskite/TiO2/Si trilayer heterojunctions for high-performance self-powered ultraviolet-visible-near infrared (UV-Vis-NIR) photodetectors. Nano Res. 11, 1722–1730 (2018).
Sun, H. et al. Self-powered, flexible, and solution-processable perovskite photodetector based on low-cost carbon cloth. Small 13, 1701042 (2017).
Lu, H. et al. A self-powered and stable all-perovskite photodetector-solar cell nanosystem. Adv. Funct. Mater. 26, 1296–1302 (2016).
Peng, W. et al. Solution-grown monocrystalline hybrid perovskite films for hole-transporter-free solar cells. Adv. Mater. 28, 3383–3390 (2016).
Rao, H. S., Chen, B. X., Wang, X. D., Kuang, D. B. & Su, C. Y. A micron-scale laminar MAPbBr3 single crystal for an efficient and stable perovskite solar cell. Chem. Commun. 53, 5163–5166 (2017).
Bao, C. et al. Low-noise and large-linear-dynamic-range photodetectors based on hybrid-perovskite thin-single-crystals. Adv. Mater. 29, 1703209 (2017).
Chen, Z. et al. Thin single crystal perovskite solar cells to harvest below-bandgap light absorption. Nat. Commun. 8, 1890 (2017).
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).
Zhang, X. et al. Stable high efficiency two-dimensional perovskite solar cells via cesium doping. Energy Environ. Sci. 10, 2095–2102 (2017).
Thirumal, K. et al. Morphology-independent stable white-light emission from self-assembled two-dimensional perovskites driven by strong exciton–phonon coupling to the organic framework. Chem. Mater. 29, 3947–3953 (2017).
Ha, S. T., Shen, C., Zhang, J. & Xiong, Q. Laser cooling of organic-inorganic lead halide perovskites. Nat. Photon. 10, 115–121 (2015).
Gauthron, K. et al. Optical spectroscopy of two-dimensional layered (C6H5C2H4NH3)2PbI4 perovskite. Opt. Express 18, 5912–5919 (2010).
Mitzi, D. B. A layered solution crystal growth technique and the crystal structure of (C6H5C2H4NH3)2PbCl4. J. Solid State Chem. 145, 694–704 (1999).
Kagan, C. R. Organic-inorganic hybrid materials as semiconducting channels in thin-film field-effect transistors. Science 286, 945–947 (1999).
Liang, K., Mitzi, D. B. & Prikas, M. T. Synthesis and characterization of organic−inorganic perovskite thin films prepared using a versatile two-step dipping technique. Chem. Mater. 10, 403–411 (1998).
Era, M., Morimoto, S., Tsutsui, T. & Saito, S. Organic‐inorganic heterostructure electroluminescent device using a layered perovskite semiconductor (C6H5C2H4NH3)2PbI4. Appl. Phys. Lett. 65, 676–678 (1994).
Dammak, T. et al. Two-dimensional excitons and photoluminescence properties of the organic/inorganic (4-FC6H4C2H4NH3)2[PbI4] nanomaterial. J. Phys. Chem. C 113, 19305–19309 (2009).
Kitazawa, N. Optical absorption and photoluminescence properties of Pb(I, Br)-based two-dimensional layered perovskite. Jpn. J. Appl. Phys. 36, 2272–2276 (1997).
Kitazawa, N. Excitons in two-dimensional layered perovskite compounds: (C6H5C2NH3)2H4 Pb(Br,I)4 and (C6H5C2NH3Pb(Cl,Br)4. Mater. Sci. Eng. B 49, 233–238 (1997).
Kikuchi, K., Takeoka, Y., Rikukawa, M. & Sanui, K. Structure and optical properties of lead iodide based two-dimensional perovskite compounds containing fluorophenethylamines. Curr. Appl. Phys. 4, 599–602 (2004).
Saidaminov, M. I., Mohammed, O. F. & Bakr, O. M. Low-dimensional-networked metal halide perovskites: the next big thing. ACS Energy Lett. 2, 889–896 (2017).
Shimizu, M., Fujisawa, Ji & Ishihara, T. Photoluminescence of the inorganic-organic layered semiconductor(C6H5C2H4NH3)2PbI4: observation of triexciton formation. Phys. Rev. B 74, 155206 (2006).
Peng, W. et al. Ultralow self-doping in two-dimensional hybrid perovskite single crystals. Nano. Lett. 17, 4759–4767 (2017).
Liu, W. et al. Giant two-photon absorption and its saturation in 2D organic-inorganic perovskite. Adv. Opt. Mater. 5, 1601045 (2017).
Lédée, F. et al. Fast growth of monocrystalline thin films of 2D layered hybrid perovskite. CrystEngComm 19, 2598–2602 (2017).
Dou, L. et al. Solution-processed hybrid perovskite photodetectors with high detectivity. Nat. Commun. 5, 5404 (2014).
Gong, X. et al. High-detectivity polymer photodetectors with spectral response from 300 nm to 1450 nm. Science 325, 1665–1667 (2009).
Ghadi, H. et al. Enhancement in peak detectivity and operating temperature of strain-coupled InAs/GaAs quantum dot infrared photodetectors by rapid thermal annealing. IEEE Trans. Nanotechnol. 14, 668–672 (2015).
Wei, H., Fang, Y., Yuan, Y., Shen, L. & Huang, J. Trap engineering of CdTe nanoparticle for high gain, fast response, and low noise P3HT:CdTe nanocomposite photodetectors. Adv. Mater. 27, 4975–4981 (2015).
Gundimeda, A. et al. Fabrication of non-polar GaN based highly responsive and fast UV photodetector. Appl. Phys. Lett. 110, 103507 (2017).
Dang, Y. Y. et al. Bulk crystal growth of hybrid perovskite material CH3NH3PbI3. CrystEngComm 17, 665–670 (2015).
Nernst, W. Theorie der reaktionsgeschwindigkeit in heterogenen systemen. Z. Phys. Chem. 47, 52–55 (1904).
Dash, J. G. Clustering and percolation transitions in helium and other thin films. Phys. Rev. B 15, 3136–3146 (1977).
Sung, M. H., Kim, J. S., Kim, W. S., Hirasawa, I. & Kim, W. S. Modification of crystal growth mechanism of yttrium oxalate in metastable solution. J. Cryst. Growth 235, 529–540 (2002).
Zhang, N. H. & Xing, J. J. An alternative model for elastic bending deformation of multilayered beams. J. Appl. Phys. 100, 103519 (2006).
Li, J. B. et al. Solution coating of superior large-area flexible perovskite thin films with controlled crystal packing. Adv. Opt. Mater. 5, 1700102 (2017).
Edri, E. Elucidating the charge carrier separation mechanism in CH3NH3PbI3-xClx perovskite solar cells. Nat. Commun. 5, 3461 (2014).
Konstantatos, G., Clifford, J., Levina, L. & Sargent, E. H. Sensitive solution-processed visible-wavelength photodetectors. Nat. Photon. 1, 531–534 (2007).
Pan, W. et al. Cs2AgBiBr6 single-crystal X-ray detectors with a low detection limit. Nat. Photon. 11, 726–732 (2017).
Fang, Y. J., Dong, Q. F., Shao, Y. C., Yuan, Y. B. & Huang, J. S. Highly narrowband perovskite single-crystal photodetectors enabled by surface-charge recombination. Nat. Photon. 9, 679–687 (2015).
This work was funded by the National Key Research and Development Program of China (2017YFA0204800), the Fundamental Research Funds for the Central Universities (2018CBLZ006), National Natural Science Foundation of China (91733301, 61604092 and 61674098), the 111 Project (B14041), the Changjiang Scholar and Innovative Research Team (IRT_14R33), the Natural Science Basic Research Plan in Shaanxi Province of China (2018JM5132), and the Fundamental Research Funds for the Central Universities (GK201803012).
The authors declare no competing interests.
Publisher’s note: Springer Nature remains neutral with regard to jurisdictional claims in published maps and institutional affiliations.
Electronic supplementary material
About this article
Cite this article
Liu, Y., Zhang, Y., Yang, Z. et al. Multi-inch single-crystalline perovskite membrane for high-detectivity flexible photosensors. Nat Commun 9, 5302 (2018). https://doi.org/10.1038/s41467-018-07440-2
Overcoming the Anisotropic Growth Limitations of Free‐Standing Single‐Crystal Halide Perovskite Films
Angewandte Chemie (2021)
Synergistically Enhanced Amplified Spontaneous Emission by Cd Doping and Cl‐Assisted Crystallization
Advanced Optical Materials (2021)
A high performance CsPbBr3 microwire based photodetector boosted by coupling plasmonic and piezo-phototronic effects
Nano Energy (2021)
Advanced Energy Materials (2021)
Low-Dimensional Hybrid Lead Iodide Perovskites Single Crystals via Bifunctional Amino Acid Cross-Linkage: Structural Diversity and Properties Controllability
ACS Applied Materials & Interfaces (2021)