Samrat Das Adhikari
Narayan Pradhan- School of Materials Sciences, Indian Association for the Cultivation of Science, Kolkata, India
Two-dimensional (2D) layered perovskites recently emerged as one of the most promising materials for optoelectronics. These not only behave like a quantum well structures, but also on doping Mn(II) ions at the Pb site result as a highly emissive doped material. These structures can also be used as a starting material for obtaining 3D perovskites. Thermal treatment of Mn(II)-incorporated layered perovskites in presence of Cs(I) ions led to Mn(II)-doped 2D platelet–shaped perovskites, which also tune their dimensions with varying dopant ion concentrations. Keeping the importance of the 2D-layered perovskites, this review focused on the basic structures to the recently developed synthetic strategies and their optical properties of layered structured perovskites, Mn(II)-doped layered perovskites, and Mn(II)-doped 2D platelet–shaped perovskites.
Introduction
Lead halide perovskite nanostructures recently emerged as the most promising materials for photovoltaic and optoelectronic applications (Kojima et al., 2009; Kovalenko et al., 2017; Jena et al., 2019; Li and Yang, 2019; Smith et al., 2019), which possess very high absorption coefficient, can achieve near unity photoluminescence quantum efficiency in different colors, and also can be efficiently doped for enhancing carrier transportation ability (Snaith, 2013; Kim et al., 2016; Di Stasio et al., 2017; Yong et al., 2018; Das Adhikari et al., 2019b; Dutta A. et al., 2019; Mondal et al., 2019; Park et al., 2019; Zhang et al., 2019). Significant achievements have been obtained in designing different all-inorganic and hybrid nanostructures, and their photophysical properties were also largely studied. Among these, two-dimensional (2D) layered perovskites and also 2D platelets of all inorganic perovskites remained promising for obtaining films with efficient activity and also confining the exciton within a limited boundary (Li et al., 2018; Mauck and Tisdale, 2019). Before discussing more on these 2D perovskites, details of the compositions and their possible structural variations are briefly discussed.
Lead halide perovskite is typically known in the formula APbX3, where ‘A’ is a monovalent cation (Cs+/Rb+/methylammonium, formadinium, etc.), and ‘X’ is the halide ions. Generally, APbX3 absorbs and emits visible light and is highly tunable with the composition of halide ions. In a report by Kovalenko et al., the emission of FAPbI3 is further red tuned to the NIR region (780 nm) (Protesescu et al., 2017). These ‘A’ cations are placed at the octahedral cavity of eight corner-shared [PbX6]4– octahedra moiety (Nedelcu et al., 2015; Protesescu et al., 2015; Leijtens et al., 2017; Beck et al., 2019). Varying ‘A’ cations in APbX3 typically retain their physical properties, irrespective to their nature, either inorganic Cs+ or organic methylammonium or formadinium ions (Protesescu et al., 2016; Chen et al., 2018; Kanwat et al., 2018; Kato et al., 2018). But, in case of hybrid organic–inorganic–based perovskites, when the chain length of the ‘A’ cation becomes too large to fit within the octahedral cavity, each layer of the corner shared [PbX6]4– separates and conjugated by two flipped large organic ammonium cations, which are mentioned as “spacer ligands” and form Ruddlesden–Popper phase perovskite, simply known as layered perovskite. The spacer ligands are basically large organic ammonium cations (RNH3+), and the halides are bonded through hydrogen bonding with the ammonium ion (Smith et al., 2014; Dou et al., 2015; Kumar et al., 2016; Mao et al., 2016; Pedesseau et al., 2016; Weidman et al., 2016; Lermer et al., 2018; Sheikh et al., 2018; Yin et al., 2018). Because the spacer ligands are insulating, these structures behave as multiple quantum wells. In this case, the inorganic layers act as the wells, where the spacer ligands serve as the potential barriers (Lan et al., 2019; Sichert et al., 2019; Soe et al., 2019).
Apart from the 3D APbX3 perovskites, recent reports are strongly focused on these 2D-layered perovskites because of their high degree of structural flexibility and tunable optoelectronic properties (Even et al., 2014; Pedesseau et al., 2016; Stoumpos et al., 2016a, b; Tsai et al., 2016; Blancon et al., 2017). The optical bandgap of these layered perovskites is highly tunable by exchanging the halides accordingly (Weidman et al., 2016; Smith et al., 2017). Apart from this, a recent report also depicts the optical bandgap tunability as a function of chain length of the spacer ligand, where the blue shift with increasing the chain length is observed because of the change in octahedral tilting (Sichert et al., 2019). So, the synthetic development of these layered perovskites is necessary, which can prepare a set of visible light absorbing and emitting 2D-layered perovskites (Koutselas et al., 2011; Liang et al., 2016; Vassilakopoulou et al., 2016; Yuan et al., 2016; Cortecchia et al., 2017; Sun et al., 2019). Mn doping in these 2D-layered perovskite nanocrystals facilitate a dual emission window, one is from the host nanocrystal, and the secondary emission is from the Mn(II) dopant, which possess very high quantum yield, and to date reported as 97%, to the best of our knowledge (Biswas et al., 2017; Ba et al., 2019; Bakthavatsalam et al., 2019; Dutta S. K. et al., 2019; Luo et al., 2019; Sheikh and Nag, 2019; Sun et al., 2019). The optical emission generated from the dopant state is highly dependent on the dopant concentration. Apart from this, the doped layered perovskites are also used as the template for the preparation of 3D-doped perovskite nanocrystals, by the thermal treatment of layered perovskite and Cs+ precursor (Das Adhikari et al., 2018; Parobek et al., 2018). Keeping all these issues in mind, this review focuses on the recent synthetic development and the structural and optical properties of these doped and undoped layered perovskites and also their use as a template for the preparation of 2D platelet perovskites.
Structure of 2D-Layered Perovskites
The general structural formula of Ruddlesden–Popper phase perovskite is L2(APbX3)n–1PbnX4. The integer, n, is the number of corner-shared [PbX6]4– layers, separated by the two large organic ammonium ions. The simplest structure of this kind of perovskite is L2PbX4, when the value of n is 1 (Weidman et al., 2016). Figure 1A shows the typical structure of corner-shared octahedra separate by the spacer ligands (L), and form the layered perovskite, L2PbX4. The transmission electron microscopic (TEM) images are presented in Figures 1B,C for L2PbCl4 and L2PbBr4, respectively. The lateral dimension of these layered structures is generally several hundred nanometers to micron. This highly oriented stacked layered structure has a repetitive powder x-ray diffraction (XRD) pattern at (00n) peaks. From this XRD pattern, the distance between two successive layers can be calculated from the difference in diffraction angle of two repetitive (00n) peaks. Figure 1D represents such XRD patterns of three different-layered structures composed of butylammonium (BA), octylammonium (OA), and their equimolar mixture as the spacer ligand (L). In this case, the OA ligands occupy 2.1-nm distances between two inorganic layers, whereas BA ligands occupy 1.3-nm distances, which has a good agreement with their corresponding chain lengths.
Figure 1. (A) Schematic presentation of L2PbX4, where two successive corner-shared [PbX6]4– are separated by two flipped organic ammonium ions. (B,C) TEM images of L2PbCl4 and L2PbBr4, respectively. (D) Powder x-ray diffraction patterns of (OA)2PbBr4 (red), (OA/BA)2PbBr4 (green), and (BA)2PbBr4 (blue) layered perovskites. Here, OA and BA stand for octylammonium and butylammonium, respectively. (E) Absorption spectra of L2PbX4 showing continuous tunability with the pure and mixed composition of halides. All figures are adapted from Weidman et al. (2016), with permission from the American Chemical Society.
The layered perovskite, L2PbX4, has halide ions–dependent bandgap tunability, which is a well-known fact for their 3D counterpart (APbX3). The anion exchange in layered perovskites, L2PbX4, is first reported by Weidman et al. (2016), by mixing the pure L2PbX4 with 10% proportion and controlled further to study the successive red shift of bandgap energy going from chloride to iodide. Figure 1E shows a set of absorption spectra of pure and mixed halide-based layered perovskite. The absorption band edge shifts at the lower wavelength, when the Cl– ions were replaced by Br– and followed by I– ions from partially to completely. L2PbCl4 has the absorption band edge near 334 nm (∼3.7 eV), which shows no optical emission because of its very high bandgap. L2PbBr4 has an absorption band edge near 400 nm, which has similar optical properties to 3D CsPbCl3. For this reason, Mn2+ doping is found to be more feasible in L2PbBr4 in comparison to the L2PbCl4 or L2PbI4 to study their optical properties, which is discussed in the later section. L2PbI4 is green emitting in nature and has an optical absorption near 500 nm.
Mn(II) Doping in 2D-Layered Perovskite
The mostly studied optical property of Mn(II) doping in 3D lead halide perovskite is CsPbCl3, which has the ideal bandgap to transfer an efficient amount of excitonic energy to the Mn dopant state, to get a characteristic spin flipped emission of Mn dopant that originated from Mn d-d states 4T1 to 6A1 transition (Liu et al., 2016; Parobek et al., 2016; Guria et al., 2017; Mir et al., 2017; Dutta and Pradhan, 2019). L2PbBr4 is the alternative to the CsPbCl3 because of their nearly identical bandgap differences. Similar to CsPbCl3, the Mn(II)-doped L2PbBr4 has the excitonic emission near 400 nm, while highly intense Mn d-d emission near 600 nm. Figure 2 presents a series of photoluminescence spectra, composed of different spacer ligands (L). The absorption and emission spectra of Mn2+-doped (oleylammonium)2PbBr4 are presented in Figures 2A,B, respectively. The synthesis of this layered perovskite was carried out by mixing PbBr2, MnBr2, oleylamine, and oleic acid in 1-octadecene (ODE) in the presence of HBr. It was found that the presence of HBr played an important role for the formation of the layered perovskites, which helped dissolve the MnBr2, and took part in the layered structures (Parobek et al., 2018). The highly emissive orange emission is known to be originated from the energy transfer of host exciton to dopant state. The inset of Figure 2B shows the illuminated digital image of a flask having the doped layered perovskites. The similar type of PL spectra originates when the spacer ligand is 1-napthylmethylammonium ion (NMA+). Using these ligands, Mn(II)-doped (NMA)2PbBr4 film was prepared by spin coating the solution of (NMA)Br, PbBr2, and MnBr2 in DMF, previously annealed at 100°C for 2 h (Cortecchia et al., 2019). Figure 2C shows the PL spectra of undoped and 0.38% Mn(II)-doped butylammonium lead bromide single crystals. Herein, only 0.38% Mn(II) dopant incorporation leads to the highly intense dopant emission along with the minimized excitonic emission (Sheikh and Nag, 2019).
Figure 2. (A) Absorbance, PLE, and (B) PL spectra of (oleylammonium)2PbBr4; inset is showing the illuminated three-necked flask having orange emission. (C) The PL spectra of undoped (black) and Mn(II)-doped (red) butylammonium lead bromide single crystals. Mn concentration–dependent PL spectra of Mn-doped L2PbBr4, when the corresponding spacer ligand (L) is (D) phenylethylammonium, (E) ethylammonium, (F,G) butylammonium and (H) 2,2’-(ethylenedioxy)-bis(ethylammonium). (A,B) are adapted from Parobek et al. (2018), with permission from the American Chemical Society. (C) is adapted from Sheikh and Nag (2019), with permission from the American Chemical Society. (D–H) are reproduced from Biswas et al., 2017; Dutta S. K. et al., 2019; Luo et al., 2019; Sun et al., 2019; Zhou et al., 2019, with permission from the American Chemical Society.
Figure 2D presents another set of Mn dopant concentration-dependent PL spectra of (phenylethylammonium)2PbBr4, where a minimum PL red shifting of approximately only 6 nm was observed with increasing the Mn dopant concentration in the layered structure. Here, the synthesis was carried out by mixing Pb(II)-acetate, Mn(II)-acetate, oleic acid, and phenylethylamine in ODE solvent. Then raising the temperature at 140°C, the required amount of trimethylsilyl bromide was injected, which acted as the bromide source. This doped layered perovskite that formed showed the highest PLQY (97%) of among the reported doped layered perovskite (Sun et al., 2019). The Mn dopant concentration was increased from 1 to 33%, and there was also a blue shift in the excitonic emission, and the Mn d-d emission that originates from the 4T1-6A1 transition has a red shifting at the higher dopant concentration. The red shifting of Mn d-d emission due to the Mn–Mn interaction has a larger shift (approximately 25- to 40-nm red shift) is reported for Mn-doped CsPbCl3 also (De et al., 2017; Das Adhikari et al., 2019a).
Mn(II) d-d Emission Tunability
Apart from the PL red shifting, Mn concentration increment into the layered structure also enhanced the Mn d-d emission successively. Figures 2E–H present such kind of Mn concentration–dependent PL spectra with different spacer ligands that were used. Figure 2E presents the PL spectra of different percentages of Mn-substituted EA2PbBr4. This was prepared by following the ligand-assisted reprecipitation method, by dissolving ethylammonium bromide, PbBr2 and different amounts of MnBr2 in a polar solvent (DMF), followed by the addition of this dissolved precursor solution into the vigorously stirring toluene. Here, the quantum yield of Mn dopant emission was increased with increasing the Mn dopant concentrations, and the quantum yield obtained 78%, at the dopant level of 40% with respect to Pb (Luo et al., 2019). Figures 2F–G present Mn concentration–dependent PL spectra for the Mn-doped butylammonium lead bromide powder samples and single crystals, respectively, where the Mn d-d emission was increased with increasing the dopant concentration (Biswas et al., 2017; Dutta S. K. et al., 2019). Synthetic procedures of these products are discussed in later section Effect of thermal annealing of Mn(II)-doped 2D-Layered perovskite.
Figure 2H presents a set of PL spectra of undoped and doped (C6H18N2O2)PbBr4 at different Mn concentrations. The synthesis was carried out by mixing PbBr2 and C6H16N2O2 in HBr under vigorous stirring at 60°C and washed in ethanol. The supernatant was discarded, and the polycrystalline powder product was collected. For doping, different amounts of MnBr2⋅5H2O were taken along with PbBr2. The undoped (C6H18N2O2)PbBr4 has a broad emission at 403 and 555 nm (Figure 2H, bottom line spectrum) with the 365-nm excitation. The peak position at 403 nm is attributed to excitonic emission, and the broad peak position at 555 nm with a large Stokes shift is assigned as the self-trapped exciton (STE) emission due to the strong electron–lattice coupling at this deformable structure. When Mn was doped into this layered structure, an Mn dopant characteristic peak arises at 640 nm and produces highly intense white light emission due to covering the entire visible range. Similar to previous observations, the PL emission peak position at 640 nm was increased with increasing the dopant concentration (Zhou et al., 2019).
Effect of Thermal Annealing of Mn(II)-Doped 2D-Layered Perovskite
Biswas et al. (2017) have followed the mechanochemical approach for the preparation of host BA2PbBr4, followed by the thermal annealing with MnBr2 at the desired temperature for the preparation of Mn-doped BA2PbBr4. They have reported that the thermal annealing has an important role for controlling the incorporation of Mn dopants into the layered perovskite. The corresponding annealing temperature varied PL spectra are presented in Figure 3A. With increasing the annealing temperature starting from room temperature to 125°C, the Mn d-d emission intensity was found to be increased. When the sample is annealed at room temperature, there is a strong band-edge emission along with the weak Mn dopant emission. When the sample was annealed at 125°C, the band-edge emission is heavily suppressed and the dopant emission highly intensified. The main reason is only for increasing the thermal diffusion of dopant ions at a higher annealing temperature (here, 125°C).
Figure 3. (A) PL spectra of Mn2+-doped (butylammonium)2PbBr4 annealed at different temperature. (B) PL spectra of Mn-doped (butylammonium)2PbBr4 microcrystals after (top, red) and before (bottom, blue) annealing at 200°C for 1 h, (C,D) optical microscopic images under UV irradiation (λ = 340-380 nm), and (E) corresponding powder XRD patterns. (A,B–E) are adapted from Biswas et al. (2017) and Dutta S. K. et al. (2019), respectively, with permission from the American Chemical Society.
Another report of our previous work on Mn-doped (BA)2PbBr4 microcrystals also predicts a similar effect on thermal annealing at 200°C (Dutta S. K. et al., 2019). This was synthesized by loading all precursors (PbBr2, MnBr2, butylammonium bromide, and HBr) in ODE and heated at 120°C. First, the as-prepared samples were drop-casted onto a glass slide; the structural and optical characterizations were carried out. After this, the same slide was heated at 200°C for 1 h in an inert atmosphere, followed by the structural and optical measurements that were carried out. The corresponding PL spectra of 1-h annealed samples and the as-prepared samples are presented in Figure 3B. The intensity of the excitonic and the dopant emission was more or less similar for the as-prepared sample, but the dopant emission was enhanced, and the excitonic emission was suppressed surprisingly after the thermal annealing at 200°C for 1 h. The optical microscopic images under the UV irradiation (λ = 340-380 nm) of these samples after and before thermal treatment are presented in Figures 3C,D, which shows the bigger and smaller microcrystals for the thermally annealed and as-prepared samples, respectively. The smaller microcrystals are the mixture of blue- and orange-emitting in nature, which reflect the equal intensity ratio of excitonic and dopant emission in the PL spectra. When the samples were heated for 1 h at 200°C, the smaller blue- and orange-emitting microcrystals are merged and form the only orange-emitting bigger microcrystals, which reflect the minimized excitonic emission along with the enhanced Mn d-d emission at the PL spectrum. This observation strongly supports the solid-state ripening of microcrystals, where the smaller undoped microcrystals are merged, and forms the bigger doped microcrystals. The powder XRD patterns of 1-h annealed sample and the as-prepared samples are presented in Figure 3E, where the peak intensities corresponding to (n00) planes have the multifold enhancement (∼100 fold) for the 1-h annealed microcrystals due to the increased grain size of post-annealed microcrystals.
2D-Layered Perovskite to Doped Perovskite
In a report by Parobek et al. (2018), the Mn-doped oleylammonium lead bromide layered perovskites are used as the template for the synthesis of 3D Mn-doped CsPbBr3 nanocubes and nanoplatelets. In such typical case, the Mn-doped–layered lead bromide perovskites are first prepared, followed by the treatment with Cs precursor to prepare a mixture of Mn-doped CsPbBr3 nanocubes and nanoplatelets. Figure 4A presents the schematic presentation of the stepwise preparation of layered perovskite followed by Mn2+-doped CsPbBr3 nanocubes and nanoplatelets. The supernatant of the product solution contains the smaller nanocubes, which has a mild Mn dopant emission and a strong excitonic emission presented in Figure 4B. There is a strong dependence of HBr used during the synthesis on the Mn dopant emission of Mn-doped CsPbBr3 nanocubes, due to the dissolution of MnBr2 during the synthesis, which helps in the incorporation of Mn dopant at the Pb site. The precipitate of the product solution contains the Mn-doped CsPbBr3 platelets, which has the dominated Mn d-d emission, and the minimized excitonic emission arises from the nanoplatelets, which is presented in Figure 4C.
Figure 4. (A) Schematic presentation of the stepwise formation of Mn-doped CsPbBr3 nanocubes and nanoplatelets via the formation of Mn-doped L2PbBr4 at 120°C. The PL spectra of (B) Mn-doped CsPbBr3 nanocubes, at different amounts of HBr used during the reaction, and (C) Mn-doped CsPbBr3 nanoplatelets. (D) Schematic presentation of the formation of layered perovskite to Mn-doped CsPbCl3 nanoplatelets upon the thermal treatment of layered perovskites with Cs+ precursor. (E) Absorbance spectrum and (F) corresponding PL spectrum of Mn-doped CsPbCl3 nanoplatelets. (A–C) adapted from Parobek et al. (2018) and (D–F) adapted from Das Adhikari et al. (2018), with permission from the American Chemical Society.
In one of our previous report, we have also used L2(Pb1–xMnx)Cl4 layered perovskite, as the template for the preparation of Mn-doped CsPbCl3 nanoplatelets, when these layered structures were thermally treated with Cs+ precursor (Das Adhikari et al., 2018). The schematic presentation of such typical process is presented in Figure 4D. There was a fine control over the platelet dimension as a function of Mn2 + ions present into the layered structure. The platelet dimension was found to be decreased with increasing the Mn content into the layered structure. Figure 4E presents the sharp absorbance spectrum of Mn-doped CsPbCl3 nanoplatelets, obtained by the thermal treatment of Cs-oleate with the highly Mn2+-incorporated layered lead chloride perovskite. The sharp absorbance indicates the fine control of nanoplatelets size uniformity. The Mn-doped CsPbCl3 nanoplatelets have dominated Mn d-d emission along with the negligible excitonic emission, which is presented in Figure 4F.
Conclusion and Future Prospects
The advanced synthetic strategies for 2D-layered perovskites, Mn(II)-doped–layered perovskites, and the all-inorganic 2D platelet–shaped Mn(II)-doped CsPbBr3 and CsPbCl3 perovskite nanostructures are reported. The review discussed from the basic concepts of layered perovskites, their formation, Mn(II) doping, and appearance of Mn d-d emission and finally presented layered to doped 2D platelets of 3D perovskite nanostructures. It also covered all reports that appeared in and accepted by the community. Methodology and findings reported here are timely and would help the community for the future progress on developing more on the layered and 2D perovskites, and the future prospects for further development are as follows:
One pot generic synthesis could be implemented by the incorporation of different chain lengths of alkylammonium ions and to tune their respective bandgaps, by controlling the chain length of spacer cations, as well as the halide ions.
Thermal annealing causes fusion of small single crystalline-layered perovskite to a comparative bigger structure. The application of such single crystalline-layered perovskite with large dimension would be more fantastic.
Unlike Mn(II)-doped CsPbCl3, low-temperature optical properties of Mn(II)-doped L2PbBr4 are still elusive and need to be explored. The exciton to dopant energy transfer mechanism also needs to be explored, which is well understood for Mn(II)-doped CsPbCl3.
Mn(II) doping in CsPbI3 results enhanced stability. Thermal treatment of Cs(I) with Mn(II)-doped–layered lead iodide perovskite would prepare more stable Mn(II)-doped CsPbI3 perovskites.
Author Contributions
SD and NP designed the concept and wrote the manuscript. Both authors contributed to the article and approved the submitted version.
Conflict of Interest
The authors declare that the research was conducted in the absence of any commercial or financial relationships that could be construed as a potential conflict of interest.
Acknowledgments
DST of India is acknowledged for funding.
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Keywords: lead halide perovskite, Ruddlesden–Popper perovskites, Mn doping, structure of layered perovskites, CsPbCl3 2D nanoplatelets
Citation: Das Adhikari S and Pradhan N (2020) Recent Developments of Mn(II)-Doped 2D-Layered and 2D Platelet Perovskite Nanostructures. Front. Mater. 7:206. doi: 10.3389/fmats.2020.00206
Received: 19 November 2019; Accepted: 05 June 2020;
Published: 05 August 2020.
Edited by:
Jiatao Zhang, Beijing Institute of Technology, ChinaReviewed by:
Way Foong Lim, Universiti Sains Malaysia (USM), MalaysiaHongbo Li, Beijing Institute of Technology, China
Copyright © 2020 Das Adhikari and Pradhan. This is an open-access article distributed under the terms of the Creative Commons Attribution License (CC BY). The use, distribution or reproduction in other forums is permitted, provided the original author(s) and the copyright owner(s) are credited and that the original publication in this journal is cited, in accordance with accepted academic practice. No use, distribution or reproduction is permitted which does not comply with these terms.
*Correspondence: Samrat Das Adhikari, c2RhLmNoZW1pc3RAZ21haWwuY29t; Narayan Pradhan, Y2FtbnBAaWFjcy5yZXMuaW4=