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Improvement of Photophysical Properties of CsPbBr3 and Mn2+:CsPb(Br,Cl)3 Perovskite Nanocrystals by Sr2+ Doping for White Light-Emitting Diodes
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C: Physical Properties of Materials and Interfaces

Improvement of Photophysical Properties of CsPbBr3 and Mn2+:CsPb(Br,Cl)3 Perovskite Nanocrystals by Sr2+ Doping for White Light-Emitting Diodes
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The Journal of Physical Chemistry C

Cite this: J. Phys. Chem. C 2022, 126, 27, 11277–11284
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https://doi.org/10.1021/acs.jpcc.2c01244
Published June 28, 2022

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Abstract

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All-inorganic metal halide perovskite nanocrystals (NCs) having the general formula ABX3, where A is a monovalent cation, for example, Cs+, B is a divalent cation, typically Pb2+, and X is Cl, Br, I, or their binary mixture, show potential in optoelectronic devices. In this work, we explore the effect of B-site doping on the optoelectronic properties of CsPbX3 NCs (X = Br, Cl). First, the Pb2+ ions in the pristine CsPbBr3 NC are partially substituted by Mn2+ ions. The alkaline earth metal strontium is then doped on both pristine and the Mn2+-substituted NCs. We found that a small percentage of Sr2+ doping remarkably improves the photoluminescence quantum yield of CsPbBr3 and Mn2+-state emission in Mn2+:CsPb(Br,Cl)3 NCs. Perovskite NC film/poly(methyl methacrylate) composites with all four NC variants were used in a white light-emitting diode (WLED), where Sr2+ doping increased the luminous efficiency of the WLED by ∼4.7%. We attribute this performance enhancement to a reduced defect density and an attenuated microstrain in the local NC structure.

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Introduction

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All-inorganic lead halide perovskite nanocrystals (NCs), for example, CsPbX3 (X = Cl, Br, I), have attracted remarkable attention owing to their high photoluminescence quantum yield (PLQY), defect tolerance, adjustable band gaps, narrow PL linewidth, and low-cost fabrication. (1−3) These features make perovskite NCs a good candidate for optoelectronic applications, such as light-emitting diodes (LEDs), (4−6) solar cells, (7,8) lasers, (9,10) and photodetectors. (11,12) In perovskite-based white LEDs (WLEDs), CsPbX3 perovskite NCs can be used as PL converters either by using a combination of red-/green-/blue-emitting perovskites and exciting them using a UV LED (13) or by using the combinations of red-/green-emitting perovskites excited using a blue LED. (14) Conveniently, in CsPbX3 perovskite NCs, the halogen content X can be tuned to alter the emission color, for example, the CsPbI3, CsPbBr3, and CsPbCl3 NCs can be deployed as the red (∼1.7 eV), green (∼2.4 eV), and blue (∼3.0 eV) emitters, respectively. (1) However, these perovskite NCs under ambient conditions often suffer from low stability, while the presence of surface defects promotes non-radiative recombinations and deteriorates optical properties. (15,16)
Compositional engineering is a promising method to counter these problems. Homovalent M2+ ions (M = Zn, (17,18) Cd, (17,19) Sr, (20,21) Mn, (22,23) and Sn (17,24)) or heterovalent N3+ dopants (N = Ce, (25) Bi, (26) Sb, (27) and Al (28)) can increase stability and reduce defect density in perovskite NCs. (16,29,30) Among these dopants, Mn2+ incorporation into the CsPbX3 (X = Br, Cl) perovskite lattice gives rise to a characteristic emission around ∼2.1 eV (31) due to the d–d transition between the 4T1 and 6A1 configurations. (32,33) Therefore, Mn2+:CsPbX3 (X = Br,Cl) perovskite NCs can serve as a viable alternative to CsPbI3 NCs for harnessing emission in the red region in perovskite-based WLEDs, (34−36) given that Mn2+:CsPbX3 (X = Br, Cl) NCs have better phase stability than CsPbI3 NCs. (37) Nevertheless, low PLQY of the Mn state emission is still an issue, which can be improved by co-doping Mn2+:CsPbX3 NCs with bivalent Co2+, (38) Ni2+, (39) and Cu2+ (40) or trivalent Bi3+ (41) and Yb3+ (42) ions.
In this work, we present improved photophysical properties of CsPbBr3 and Mn2+:CsPb(Br,Cl)3 perovskite NCs achieved by Sr2+ doping. We utilized scanning transmission electron microscopy (STEM) to show that Sr2+ doping leads to a more uniform size distribution of the perovskite NCs. Microstrain calculations were performed by using the Williamson–Hall (W–H) method extracted from X-ray diffraction (XRD) analyses, which revealed that Sr2+ doping decreases defect density in the perovskite NCs. Consequently, a remarkable increase in the PLQY with longer PL lifetimes was observed for both Sr2+-doped NCs, Sr2+:CsPbBr3 and Sr2+:Mn2+:CsPb(Br,Cl)3.
Finally, perovskite-based WLEDs were constructed by using CsPbBr3/PMMA [PMMA = poly(methyl methacrylate)] and Mn2+:CsPb(Br,Cl)3/PMMA NCs as PL converters excited using a UV LED. WLEDs fabricated with Sr2+-doped perovskite NCs, that is, Sr2+:CsPbBr3 and Sr2+:Mn2+:CsPb(Br,Cl)3, exhibit a higher PL intensity, higher luminescence efficiency, and slightly higher color rendering index (CRI) than those fabricated with pristine CsPbBr3 and Mn2+:CsPb(Br,Cl)3 perovskite NCs. The results presented here provide a good platform to enhance the photophysical properties of CsPbBr3 and Mn2+:CsPb(Br,Cl)3 perovskite NCs using the Sr2+ doping strategy.

Experimental Procedure

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Materials

Lead(II) bromide (PbBr2, ≥98%), strontium bromide (SrBr2, 99.99% trace metal basis), manganese(II) chloride tetrahydrate (MnCl2·4H2O, ≥98%), cesium carbonate (Cs2CO3, 99.9%, Sigma-Aldrich), 1-octadecene (ODE, 90%), oleylamine (OLAM, 70%), and oleic acid (OA, 90%) were purchased from Sigma-Aldrich. Toluene (≥99%, Merck) was purchased and used without any further purification. PMMA with an average Mw of 15,000 (GPC) was purchased from Aldrich Chemical Company, Inc.

Synthesis of Cs-Oleate for CsPbBr3 NCs

203.5 mg (266.67 mg) of Cs2CO3, 625 μL (1,167 μL) of OA, and 10 mL of ODE were put into a round bottom flask and dried under vacuum at 120 °C while stirring for 1 h. After drying, the temperature was increased to 150 °C under a nitrogen atmosphere. The solution was kept at 150 °C overnight to make sure that all Cs2CO3 reacted with OA. The values given in parentheses are for Cs-oleate synthesis of pristine and Sr2+:Mn2+:CsPb(Br,Cl)3 NCs.

Synthesis of Pristine and Sr2+:CsPbBr3 NCs

For the synthesis of pristine CsPbBr3 NCs, first, 17.2 mg of PbBr2 was put into a glass tube along with 1.25 mL of ODE, 125 μL of OA, and 125 μL of OLAM and dissolved/degassed at 120 °C for 30 min under vacuum. After degassing, the temperature was increased to 180 °C under nitrogen, and then, 100 μL of Cs-oleate was injected. After injection, the solution was immediately cooled down using an ice bath and then centrifuged for 15 min at 6000 rpm. Later, the supernatant was discarded, and the NCs were dispersed in toluene. For the synthesis of Sr2+:CsPbBr3 NCs, the same procedure was followed except that 1, 2, 5, and 10% SrBr2 was added to the solution, while the same molar amount of PbBr2 was excluded.

Synthesis of Mn2+:CsPb(Br,Cl)3 and Sr2+:Mn2+:CsPb(Br,Cl)3 NCs

For the synthesis of Mn2+:CsPb(Br,Cl)3 NCs, first, 9.175 mg of PbBr2 and 4.95 mg of MnCl2·4H2O were put into a glass tube along with 1.25 mL of ODE, 125 μL of OA, and 125 μL of OLAM and dissolved/degassed at 120 °C for 30 min under vacuum. After degassing, the temperature was increased to 180 °C where 100 μL of Cs-oleate was injected under nitrogen. After injection, the solution was immediately cooled down using an ice bath and then centrifuged for 15 min at 6000 rpm. The supernatant was then discarded, and the perovskite NCs were dispersed in toluene. For the synthesis of Sr2+:Mn2+:CsPb(Br,Cl)3 NCs, the same process was followed except that 2% SrBr2 was added to the solution, while the same molar amount of PbBr2 was excluded.

Fabrication of the WLED

0.5 g of PMMA was dissolved in 10 mL of toluene. For each film of CsPbBr3, drop-cast films were prepared with the mixture of 40 μL of PMMA and 120 μL of the perovskite, while Mn2+:CsPb(Br,Cl)3 drop-cast films were prepared with the mixture of 40 μL of PMMA and 240 μL of perovskite dispersion on 1.5 cm × 1.5 cm glass substrates. Then, these CsPbBr3 and Mn2+:CsPb(Br,Cl)3 (for 0 and 2% Sr2+ series, respectively) were placed on the LED laterally. The emission spectra were taken from the perovskite layers excited with UV light (366 nm of wavelength, 12 V, and 8 W power), and the International Commission on Illumination (CIE) chromaticity diagram was extracted from the OSRAM ColorCalculator program.

Characterization

STEM images for all perovskite NCs were taken by using scanning electron microscopy (SEM) with STEM mode: Quanta 250, FEI, Hillsboro, OR. Perovskite dispersions were dropped onto 300 mesh holey carbon-Cu (50 μm) for STEM images. XRD analyses were done by using X’Pert Pro, Philips, Eindhoven, the Netherlands. Optical measurements including absorption, PL, PL lifetime, and PLQY were carried out on an FS5 spectrofluorometer (Edinburgh Instruments, U.K.). For PL and PLQY measurements, excitation wavelengths of CsPbBr3 and Mn2+:CsPb(Br,Cl)3 samples were 400 nm and 390 nm, respectively. For lifetime measurements, CsPbBr3 and Mn2+:CsPb(Br,Cl)3 samples were excited with 442 nm and 307 nm lasers, respectively. Trace metal analysis was carried out using an inductively coupled plasma-mass spectrometer on an Agilent 7500ce Octopole Reaction System.

Results and Discussion

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Inductively coupled plasma mass spectrometry (ICP–MS) measurements were carried out to determine the actual doping ratios of Sr2+/Pb2+ in Sr2+-doped Sr2+:CsPbBr3 (Table 1 and Figure S1) and Sr2+:Mn2+:CsPb(Br,Cl)3 NCs (Table S1). The ICP–MS analysis shows that Sr2+ was successfully doped into perovskite NCs. The Sr2+/Pb2+ ratio was systematically increased by increasing the SrBr2 concentration in the perovskite solution. The Sr2+ doping concentrations measured against their addition amounts agreed with the report by Chen et al. on Sr2+:CsPbI3 NCs. (20) Since MnCl2 was used for incorporating Mn2+ ions into the pristine CsPbBr3 particle, a fraction of bromide ions were replaced by chloride ions. Ion chromatography (IC) analysis revealed Br/Cl ratios in Mn2+:CsPb(Br,Cl)3 and 2%Sr2+:Mn2+:CsPb(Br,Cl)3 samples to be 72.34 and 75.26%, respectively (Table S1).
Table 1. Actual Sr2+/Pb2+ mol Ratio, NC Size, PLQY, and PL Lifetime of Various CsPbBr3 NC Samples Having Different %Sr2+ Dopings
% Sr2+ amount in Sr2+:CsPbBr3Actual Sr2+/Pb2+ mol ratio (%)Average NC Size (nm)PLQY (%)PL lifetime (ns)
0% Sr2+ 20.384.77.62
1% Sr2+0.04716.888.88.42
2% Sr2+0.09917.392.610.39
5% Sr2+0.23816.083.07.30
10% Sr2+1.05117.070.06.84
The relative propensity for the formation of a given NC was explored computationally employing density functional theory (DFT). We first constructed three cubic NCs of size ∼3 nm (Figure S10). Their cohesive energy (Ecohesive), which quantifies the energy required to dissociate the atoms constituting the NC into a collection of neutral free atoms, was calculated using eq S5 (see the Supporting Information). For the pristine CsPbBr3, Sr2+-doped Sr2+:CsPbBr3, and Sr2+/Mn2+ co-doped Sr2+:Mn2+:CsPb(Br,Cl)3 NCs, Ecohesive was computed to be 3.04, 3.05, and 3.17 eV/atom, respectively. Hence, the Sr2+ doping replacing two Pb2+ ions is marginally favorable (ΔEcohesive ∼ 0.01 eV/atom), whereas the Cl anions from MnCl2 drive the formation of Sr2+:Mn2+:CsPb(Br,Cl)3, which has ΔEcohesive ∼ 0.13 eV/atom when compared with the pristine NC.
Perovskites doped with Mn2+ have been reported in the literature to have a marginally increased Ecohesive (43) and a generally improved robustness. (16,44) Consequently, two additional models were examined to investigate the effects of Mn doping on Ecohesive, Mn2+:CsPbBr3 and Sr2+:CsPb(Br,Cl)3. In our simulations, however, the calculated Ecohesive was not affected by Mn doping. Ecohesive was maintained at 3.04 eV/atom in the Mn2+:CsPbBr3 model, which substitutes two Mn2+ ions for two Pb2+ ions in the pristine NC. Ecohesive was again unchanged at 3.17 eV/atom for the Sr2+:CsPb(Br,Cl)3 model, where two Mn2+ dopants from the Sr2+:Mn2+:CsPb(Br,Cl)3 particle have been replaced with the original Pb2+ ions. Accordingly, Mn2+ doping seems to have a less pronounced effect on Ecohesive, and hence on stability, for bromide nanoparticles than it does for the iodide nanoparticles, for which it is hypothesized that the smaller Mn2+ ion partially releases the strain imposed by the larger iodide ions. (16)
The morphology and size distribution of CsPbBr3 NCs upon Sr2+ doping were monitored via the STEM mode in SEM. The incorporation of Sr2+ ions into the perovskite lattice does not significantly affect the structure and morphology (Figure S2). The reason for the decrease in NC size upon Sr2+ doping (Figure S2) could be the effect of the impurity (i.e., the dopant) on crystallization dynamics. (45) We argue that the Sr2+ impurities lead to a reduction of the energy threshold for nucleation and cause more nuclei to form, resulting in a smaller NC size. The uniformity of NC size distribution is improved upon Sr2+ doping until the 2% Sr2+ concentration; however, higher Sr2+ concentrations beyond 2% adversely affect NC homogeneity (Figure S2a–e insets).
Figure 1a shows the XRD patterns of pristine and Sr2+:CsPbBr3 NC samples having various Sr2+ concentrations. XRD reflections of all samples confirm the orthorhombic Pnma crystal structure of CsPbBr3. (46) The incorporation of Sr2+ ions into the perovskite lattice does not cause any additional XRD reflection, confirming no phase transition upon doping. Furthermore, due to the similar ionic radii of Pb2+ (119 pm) and Sr2+ (118 pm) ions, (47) no systematic shift in XRD reflections was observed upon Sr2+ doping.

Figure 1

Figure 1. (a) XRD patterns, (b) microstrain values, (c) lattice parameters obtained by the W–H plot, (d) PL spectra, (e) time-resolved PL (TRPL) plot, and (f) PLQY distribution of pristine and Sr2+:CsPbBr3 NCs.

The absence of a systematic shift in the XRD patterns (Figure 1a) motivated us to investigate the influence of the Sr2+-doping concentration on microstrain, which describes local distortions of a crystal lattice. (48,49) Microstrain in the studied NCs was calculated from the slope of the WH plot (Figure S4 and Table S3). Figure 1b shows that microstrain decreases upon Sr2+ additive until the 2% concentration and then systematically increases at higher concentrations. This suggests that until the 2% Sr2+ concentration, the defect density in the NCs and concomitantly defect-related lattice distortions are reduced, resulting in a smaller microstrain in the crystal structure.
Variation of three cell-length lattice constants (a0, b0, and c0) as a function of the Sr2+concentration is summarized in Table S2, and their trend is shown in Figure 1c. We observe that the b0 parameter reaches a minimum at the 2% Sr2+ concentration and then increases as the Sr2+ concentration exceeds 2%, whereas the a0 and c0 parameters follow the opposite trend. These results indicate that the octahedral tilt angle changes upon Sr2+ doping. Recalling the trend in microstrain with the Sr2+-doping concentration, which reaches a minimum for the 2% Sr2+ sample, we argue that the reduced defect-related lattice distortions in the perovskite NCs are the reason for the change in lattice parameters, peaking at 2% Sr2+.
To understand the doping effect further, we have carried out optical measurements as shown in Figure 1d–f. The PL spectra of pristine and Sr2+:CsPbBr3 NCs are shown in Figure 1d. Despite the changes in the NC size upon doping (Table 1), the PL emission energy (Figure 1d) and absorption edges (Figure S5) of all samples are strikingly similar. We rationalize this by considering that the studied CsPbBr3 NCs are within the intermediate-to-weak quantum confinement regime, (50) and the incorporation of Sr2+ ions into the lattice does not affect the band gap energy of CsPbBr3.
From Tauc’s plot (Figure S5), the band gap energies of both pristine CsPbBr3 and Sr2+:CsPbBr3 NC samples are calculated to be ∼2.39 eV. PL signals were centered at 2.41 eV. Furthermore, the full width half-maxima of PL peaks were reduced upon Sr2+ doping, in line with the NC size distribution (Figure S2).
To better understand the effect of Sr2+ doping on the optoelectronic properties of the NCs, 2D periodic slab models were constructed for the pristine CsPbBr3 and 5% Sr2+-doped Sr2+:CsPbBr3 NCs (Figure 2a, top) and analyzed using DFT. Inspection of the projected densities of states (pDOS; Figure 2b, top) and the band structures (Figure S11) of the pristine and Sr2+-doped models suggests that both NCs are a direct-bandgap material, with the valence band maximum (VBM) and conduction band minimum (CBM) located at the Γ-point. In line with the experimental observations, Figure 2b shows that Sr2+ inclusion into CsPbBr3 NCs had no significant effect on the DOS, where the VBM consists mainly of filled Br(p) orbitals, while the CBM is made up mainly of empty Pb(p) orbitals.

Figure 2

Figure 2. (a) Four periodic slab models considered for the computational study: pristine CsPbBr3, Sr2+-doped Sr2+:CsPbBr3, Mn2+-doped Mn2+:CsPb(Br,Cl)3, and Sr2+/Mn2+ co-doped Sr2+:Mn2+:CsPb(Br,Cl)3 and (b) their corresponding pDOS.

Figure 1e shows time-resolved PL (TRPL) results for CsPbBr3 NCs with varied Sr2+ contents. The average PL lifetimes (τavg) of the samples, calculated using eq S4, systematically increase upon the incorporation of Sr2+ ions into the perovskite NCs until the 2% concentration. At higher Sr2+ concentrations (>2%), however, the PL lifetime gradually decreases (Table 1). Considering that PL lifetimes are inversely proportional to the defect concentration, (51,52) the trend in PL lifetimes agrees with that of the calculated microstrain data. The PLQY results in Figure 1f demonstrate a trend analogous to that of the PL lifetime and microstrain. The PLQY of the pristine CsPbBr3 NC was found to be 84.7%. Sr2+ doping increased the PLQY to 88.8% for 1% Sr2+ and 92.6% for 2% Sr2+. As Sr2+ concentrations increased, PLQY dropped to 83% for 5% Sr2+ and then to 70% for 10% Sr2+.
According to the microstrain calculations (Figure 1b), defect-related distortions are reduced when Sr2+ ions are incorporated into the CsPbBr3 lattice until the 2% concentration. The minimum microstrain originating from fewer defects was also determined for the same 2% Sr2+ sample. Since defect sites serve as potential non-radiative recombination centers for this class of material, the reduced defect density at low Sr2+-doping concentrations should eliminate non-radiative recombination pathways, resulting in a higher PLQY and longer PL lifetime. (53) Beyond 2% Sr2+ addition, we argue that the added dopants may trigger the formation of new defects, (21) which would cause an increased microstrain and may lead to a reduction in PL lifetimes and PLQY.
The STEM images of Mn2+:CsPb(Br,Cl)3 and 2%Sr2+:Mn2+:CsPb(Br,Cl)3 NCs are given in Figure S3. 2% Sr2+ incorporation into the Mn2+:CsPb(Br,Cl)3 lattice does not change the shape of NCs but decreases the particle size and improves monodispersity, similar to the Sr2+:CsPbBr3 case (Figure S2).
To quantify the impact of the 2% Sr2+ additive on the NCs, XRD of Mn2+:CsPb(Br,Cl)3 NCs was carried out. The XRD patterns shown in Figure 3a correspond to the orthorhombic perovskite phase. (54) Since Mn2+ ions have a smaller radius (67 pm) than Pb2+ ions (119 pm), (47) the XRD signal for Mn2+-doped perovskite NCs shifts to higher angles, indicating that Mn2+ ions were successfully incorporated into the perovskite lattice. (55) However, this shift in the XRD signal in Mn2+:CsPb(Br,Cl)3 is not exclusively due to Mn2+ ions substituting for Pb2+ ions. The overall lattice shrinking can also be attributed to Cl/Br substitutions (Figure 3b). (37) Subsequent doping of the Sr2+ ions into the Mn2+:CsPb(Br,Cl)3 NCs does not cause any peak shift, indicating that the Sr2+ ions are substituted with the Pb2+ ions instead of the Mn2+ ions. Microstrain calculations of both Mn2+:CsPb(Br,Cl)3 and 2%Sr2+:Mn2+:CsPb(Br,Cl)3 samples again confirmed that Sr2+ doping reduces microstrain (Figure 3c). Regarding variations in the cell-length lattice constants of the Sr2+/Mn2+ co-doped samples, we found that the lattice parameter b0 increases, while c0 decreases, and a0 stays constant at 8.13 Å, as shown in Figure 3c and Table S2.

Figure 3

Figure 3. (a) XRD patterns: NCs show reflections at 15.4, 22.0, 31.1, 35.0, 38.4, and 44.6°, (b) comparisons of XRD signal positions for CsPbBr3, Mn2+:CsPb(Br,Cl)3, and Sr2+:Mn2+:CsPb(Br,Cl)3 perovskite NCs, (c) microstrain and lattice constant parameters, (d) PL/absorption spectra, (e) TRPL plot, and (f) PLQY comparisons of Mn2+:CsPb(Br,Cl)3 and 2%Sr2:Mn2+:CsPb(Br,Cl)3 NCs.

The UV–vis and PL spectra of the Mn2+:CsPb(Br,Cl)3 and 2%Sr2+:Mn2+:CsPb(Br,Cl)3 samples are shown in Figure 3d, both of which demonstrate very similar absorption behavior. Comparison of these spectra (Figure S6) reveals the appearance of the characteristic PL peak at around 2.1 eV due to the Mn state. Indeed, DFT calculations on both Mn-doped systems reveal (Figure 2b, bottom) Mn d-states just below the empty Pb(p) states resulting in a midgap state. Tauc’s plots (Figure S7) yield band gaps of 2.70 and 2.69 eV for these two samples, respectively. This slight change in the band gap energies between the samples was also observed in PL peak positions, with the Mn2+:CsPb(Br,Cl)3 and 2%Sr2+:Mn2+:CsPb(Br,Cl)3 NCs exhibiting exciton PL signals at 2.72 and 2.71 eV, respectively (Figure 3d). Considering that Sr2+ doping at low concentrations (≤1% actual doping) does not affect the band gap energy (Figure S5), the slight change in band gap and PL emission energies observed herein can be attributed to small differences in Br/Cl ratios in the perovskite structures; see Table S1.
Interestingly, PL emission due to the Mn state in Mn2+:CsPb(Br,Cl)3 perovskite NCs increases upon Sr2+ doping. TRPL measurements of these samples (Figure 3e) reveal that the average PL lifetime of the Mn2+:CsPb(Br,Cl)3 NCs increases from 9.39 to 10.10 ns as a result of the 2% Sr2+ additive, attributable to a lower defect density in the 2% Sr2+ sample.
PLQY measurements were performed on the Mn2+:CsPb(Br,Cl)3 and 2%Sr2+:Mn2+:CsPb(Br,Cl)3 NCs in the 2.38–1.59 eV (521–780 nm) and 3.02–2.38 eV (410–521 nm) ranges, relevant for the Mn state and perovskite emission, respectively. The PLQY of the Mn-state emission increases from 7.6% in Mn2+:CsPb(Br,Cl)3 to 14.2% in 2%Sr2+:Mn2+:CsPb(Br,Cl)3, as can be seen in Figure 3f, highlighting the beneficial effect of Sr2+ co-doping along with Mn2+. In addition, the perovskite PLQY increases from 43.4 to 49.1% due to Sr2+ doping. These optical improvements with better exciton-to-Mn2+ energy transfer upon Sr2+ incorporation are a direct consequence of a lowered defect density.
Finally, two sets of UV-pumped tricolor WLEDs were fabricated using perovskite/PMMA composite films via the drop-casting method (Figures S8 and S9). Under UV light, CsPbBr3/PMMA works as a green emitter, while Mn2+:CsPb(Br,Cl)3/PMMA is a red–blue emitter, and these two combinations were used together to construct the 0%Sr2+:WLED. The 2%Sr2+:WLED, on the other hand, was fabricated using 2%Sr2+:CsPbBr3/PMMA (green emitter) and 2%Sr2+:Mn2+:CsPb(Br,Cl)3/PMMA (red–blue emitter) layers.
The PL spectra (Figure 4a) and the CIE coordinates (Figure 4b) of both the 0% and 2%Sr2+:WLED show that the 2%Sr2+:WLED has a higher luminescence efficiency (290 lm/W under a UV light) than the pristine WLED (277 lm/W). Sr2+ doping is observed to decrease the computed work function for both pristine and Mn-doped particles (Table 2), which may improve device efficiency and enhance charge extraction in heterojunction-layered devices. (56) Furthermore, the CRI increases from 80 in the pristine 0% Sr2+:WLED system to 83 in the 2% Sr2+:WLED system. We surmise that the deficiency of red emission for the pristine 0% Sr2+:WLED system is partly compensated by the increased PL emission of the Mn state in the Sr2+:WLED system.

Figure 4

Figure 4. (a) PL spectra of the pristine WLED and 2%Sr2+:WLED and (b) corresponding CIE coordinates.

Table 2. Computed Work Function and Band Gapsa of Four Slab Models (Figure 2a) Considered in This Studyb
NC particlework function (eV)band gap (eV)
CsPbBr34.431.89 (2.39)
Sr2+:CsPbBr34.381.98 (2.39)
Mn2+:CsPb(Br,Cl)34.282.06 (2.70)
Sr2+:Mn2+:CsPb(Br,Cl)34.192.11 (2.69)
a

The overestimation of the computed band gap widening upon Sr2+ doping can be attributed to possible structural changes when Sr2+ is doped since ca 5% Sr2+ concentration is used in simulations rather than <1% in experiments.

b

Experimentally obtained band gaps are added in the parenthesis for comparison. The systematic underestimation of the calculated band gaps (with respect to the experiment) can be attributed to the presence of (57) (i) the unphysical electron self-Coulomb repulsion, (ii) derivative discontinuity of the energy with respect to the number of electrons, and (iii) the nonlinear dependence of energy on the number of electrons in the Perdew–Burke–Ernzerhof functional. (58,59)

Conclusions

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We have presented a detailed study on the effect of Sr2+ doping into CsPbBr3 and Mn2+:CsPb(Br,Cl)3 perovskite NCs. The STEM images showed a decrease in perovskite NC size after Sr2+ doping. The changes in the lattice parameters and microstrains were calculated from XRD signals; microstrain decreased and reached a minimum at the 2% Sr2+ concentration, possibly due to the elimination of defects. In addition, the optical properties of the NCs improved, with the PLQY of the CsPbBr3 NCs increasing from 84.7% in the pristine sample to 92.6% in the Sr2+:CsPbBr3 NCs, caused by reduced non-radiative recombination pathways with fewer defects in the sample. Inspired by the optical property enhancements of CsPbBr3 NCs due to Sr2+ doping, we have applied the same doping strategy to enhance the optical properties of Mn2+:CsPb(Br,Cl)3 NCs. As a result of 2% Sr2+ addition, the PLQY of the Mn2+-state emission increased from 7.6 to 14.2%. Finally, the 2%Sr2+:CsPbBr3 and 2%Sr2+:Mn2+:CsPb(Br,Cl)3 NCs were used to construct a WLED that provided improved white light compared to WLEDs constructed with their undoped counterparts. Our study shows that adding Sr2+ to pristine perovskite materials can be a successful strategy for improving their optical properties.

Supporting Information

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The Supporting Information is available free of charge at https://pubs.acs.org/doi/10.1021/acs.jpcc.2c01244.

  • STEM images, WH plot calculations, Tauc plots, ICP–MS and IC analysis results, TRPL parameters, and DFT computational details (PDF)

  • DFT-computed structures: slab models and non-periodic clusters (ZIP)

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Author Information

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  • Corresponding Author
  • Authors
    • Hurriyet Yuce - Department of Materials Science and Engineering, Izmir Institute of Technology, Urla, 35430 Izmir, Turkey
    • Mukunda Mandal - Max Planck Institute for Polymer Research, Ackermannweg 10, 55128 Mainz, GermanyOrcidhttps://orcid.org/0000-0002-5984-465X
    • Yenal Yalcinkaya - Max Planck Institute for Polymer Research, Ackermannweg 10, 55128 Mainz, Germany
    • Denis Andrienko - Max Planck Institute for Polymer Research, Ackermannweg 10, 55128 Mainz, GermanyOrcidhttps://orcid.org/0000-0002-1541-1377
  • Notes
    The authors declare no competing financial interest.

Acknowledgments

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This work was partially supported by the IZTECH Scientific Research Project with the number 2021IYTE-1-0036. D.A. acknowledges support from the Deutsche Forschungsgemeinschaft (DFG) within the Priority Program SPP2196 (“Perovskite Semiconductors: From Fundamental Properties to Devices”) under project no. 424708673. Y.Y. acknowledges the SPP2196 project (Deutsche Forschungsgemeinschaft) for funding. M.M. acknowledges postdoctoral support from the Alexander von Humboldt Foundation.

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  • Abstract

    Figure 1

    Figure 1. (a) XRD patterns, (b) microstrain values, (c) lattice parameters obtained by the W–H plot, (d) PL spectra, (e) time-resolved PL (TRPL) plot, and (f) PLQY distribution of pristine and Sr2+:CsPbBr3 NCs.

    Figure 2

    Figure 2. (a) Four periodic slab models considered for the computational study: pristine CsPbBr3, Sr2+-doped Sr2+:CsPbBr3, Mn2+-doped Mn2+:CsPb(Br,Cl)3, and Sr2+/Mn2+ co-doped Sr2+:Mn2+:CsPb(Br,Cl)3 and (b) their corresponding pDOS.

    Figure 3

    Figure 3. (a) XRD patterns: NCs show reflections at 15.4, 22.0, 31.1, 35.0, 38.4, and 44.6°, (b) comparisons of XRD signal positions for CsPbBr3, Mn2+:CsPb(Br,Cl)3, and Sr2+:Mn2+:CsPb(Br,Cl)3 perovskite NCs, (c) microstrain and lattice constant parameters, (d) PL/absorption spectra, (e) TRPL plot, and (f) PLQY comparisons of Mn2+:CsPb(Br,Cl)3 and 2%Sr2:Mn2+:CsPb(Br,Cl)3 NCs.

    Figure 4

    Figure 4. (a) PL spectra of the pristine WLED and 2%Sr2+:WLED and (b) corresponding CIE coordinates.

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