Solution-processed organometal halide perovskites (formulated as ABX3, where A is the methylammonium (CH3NH3+) (MA) or metal cesium cation (Cs+), B is the lead cation (Pb2+) and X is the halide anion (Br−, I−, Cl−)) are promising candidates for next generation light-emitting materials owing to their unique optoelectronic properties. These properties mainly include extremely high photoluminescence quantum yield (PLQY), easily tunable band gap and narrow emission characteristics. During the past two years, impressive progresses have been made in perovskite light-emitting diodes (PeLED) with hybrid organic–inorganic perovskite materials (i.e., CH3NH3PbBr3). So far, the best external quantum efficiency (EQE) of CH3NH3PbBr3-based PeLED was reaching up to ~8.53% which was close to the results of organic light-emitting diodes (OLED). Despite the remarkable performance of the devices demonstrated, the stability of organic–inorganic hybrid perovskites remains a major concern. To circumvent this problem, all-inorganic halide perovskites exhibiting higher thermal and chemical stability, such as cesium lead bromide (CsPbBr3), have been used as alternative emitters in PeLED. Despite the advantages described above, both the brightness and the EQE of CsPbBr3-based PeLED remain limited. One important reason for low efficiency of CsPbBr3-based PeLED is the facile dissociation of excitons in 3D perovskites due to their small exciton binding energy. One promising way to enhance the exciton binding energy is reducing the grain size of perovskites. Herein, we report a solution process to form highly uniform and ultra-flat perovskite films with nanometre-sized grains that allow us to demonstrate efficient PeLED. By mixing long-chain ammonium halides of CH3CH2CH2NH3Br (PABr) with the 3D CsPbBr3 perovskite precursor solution, the growth of 3D perovskite grains are dramatically impeded and the PA2(CsPbBr3) n −1PbBr4 quantum dots with grain size of ~100 nm were achieved. This is because the long-chain ammonium ions cannot fill the corner of PbBr4 octahedral layers and therefore impedes the 3D perovskite formation. Moreover, the nanometre-sized grains feature reduced dimensionality, starting a transition from 3D to 2D layered (so-called Ruddlesden-Popper phase) perovskite structures. The SEM image show the morphology of PA2(CsPbBr3) n −1PbBr4 layer was dense and uniform, which is very important to suppress the leaking current in the PeLED. We found that PA2(CsPbBr3) n −1PbBr4 film mainly consists of two different 2D structures, namely PA2PbBr4 ( n =1) and PA2(CsPbBr3)PbBr4 ( n =2), according to the analysis of XRD pattern. Compared to the single UVs absorption peak of CsPbBr3 at ~520 nm, PA2(CsPbBr3) n −1PbBr4 film show multiple absorption peaks, indicating several extonic states are formed upon light excitation. Although several extonic states exist, photoluminescence (PL) with only one peak of 506 nm was observed in PA2(CsPbBr3) n −1PbBr4 film. We suspect that the energy transfer occurs from the excitons with larger bandgap to those with smaller bandgap, making recombination occurs only in the excitons with the smallest bandgap. For the PeLED with structure of ITO/PEDOT:PSS/PA2- (CsPbBr3) n −1PbBr4/TPBi/Cs2CO3/Al, the turn-on voltage is ~4.2 V, the maximum luminance is ~2370 cd/m2, the maximum current efficiency is ~1.06 cd/A, and maximum EQE is ~0.57%. Compared to the traditional method achieving blue PeLED by substituting halide anions, obvious improvements can be seem not only in the material processing and the perovskites film quality, but also in the PeLED′s performance. Our studies may provide an alternative way to explore low-cost and high- efficiency blue PeLED.
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