Article | Open | Published:

Near-infrared-triggered photon upconversion tuning in all-inorganic cesium lead halide perovskite quantum dots

Nature Communicationsvolume 9, Article number: 3462 (2018) | Download Citation

Abstract

All-inorganic CsPbX3 (X = Cl, Br, and I) perovskite quantum dots (PeQDs) have shown great promise in optoelectronics and photovoltaics owing to their outstanding linear optical properties; however, nonlinear upconversion is limited by the small cross-section of multiphoton absorption, necessitating high power density excitation. Herein, we report a convenient and versatile strategy to fine tuning the upconversion luminescence in CsPbX3 PeQDs through sensitization by lanthanide-doped nanoparticles. Full-color emission with wavelengths beyond the availability of lanthanides is achieved through tailoring of the PeQDs bandgap, in parallel with the inherent high conversion efficiency of energy transfer upconversion under low power density excitation. Importantly, the luminescent lifetimes of the excitons can be enormously lengthened from the intrinsic nanosecond scale to milliseconds depending on the lifetimes of lanthanide ions. These findings provide a general approach to stimulate photon upconversion in PeQDs, thereby opening up a new avenue for exploring novel and versatile applications of PeQDs.

Introduction

All-inorganic cesium lead halide (CsPbX3, X = Cl, Br, and I) perovskite quantum dots (PeQDs) have recently attracted intensive attention in a wide array of research fields, owing to their outstanding physicochemical properties such as large absorption coefficients, high photoluminescence (PL) quantum yields (QYs), narrow emission bands, and tunable bandgap and PL emissions by varying the halide composition1,2,3,4. These elegant characteristics make CsPbX3 PeQDs ideal candidates as light-harvesting or light-emitting materials for diverse optoelectronic and photovoltaic applications5,6,7,8,9,10,11,12. Although PeQDs exhibit excellent linear optical properties under ultraviolet (UV) or visible light excitation, their nonlinear optical properties such as near-infrared (NIR)-triggered photon upconversion are limited by low efficiency ( < 10−8) of multiphoton absorption and the requirement of expensive pulsed lasers for excitation13,14,15,16,17,18. In contrast to linear absorption and emission, the nonlinear upconversion analogs feature a series of advantages including a large penetration depth, high spatial resolution, minimal background interference, and little damage to the targeted samples, which hold great promise in areas as diverse as multiplexed optical encoding, three-dimensional displays, super-resolution bioimaging, and effective solar spectrum conversion19,20,21,22,23,24,25,26.

As compared with PeQDs, lanthanide-doped nanoparticles (NPs) are much more efficient (10−1–10−3) in photon upconversion through successive photon absorption and energy transfer processes within lanthanide ions, and thus can be excited by using a low-cost continuous-wave (CW) diode laser27,28,29,30. By controlling the energy transfer processes based on core/shell engineering, these NPs can produce efficient upconversion luminescence (UCL) with wavelengths spanning from UV to NIR and lifetimes ranging from microseconds to milliseconds31,32,33,34,35,36. Nevertheless, upconversion tuning in lanthanide-doped NPs requires cumbersome experimentation involving repeated trials to optimize the dopant concentration37. Moreover, there are inherent limitations on wavelength tunability in lanthanide-doped NPs due to the defined and discrete energy levels of lanthanide ions.

To circumvent these limitations, it is essential to bring together both advantages of lanthanide-doped NPs and PeQDs, whereby lanthanide-doped NPs may serve as an effective sensitizer for PeQDs to boost their upconversion efficiency, whereas PeQDs with continuously tunable emission bands could extend the emission wavelengths of lanthanide-doped NPs. Unfortunately, previous endeavors on this aspect through non-radiative Förster resonance energy transfer (FRET) from lanthanide-doped NPs to quantum dots usually resulted in serious quenching of overall UCL intensity and negligibly weak quantum dots emissions, because it is notoriously difficult to control the number of energy acceptors in close proximity of the donors within an effective FRET distance38,39,40.

Herein, we report a convenient and versatile approach to fine tuning the UCL in CsPbX3 PeQDs through sensitization by lanthanide-doped NPs. We demonstrate that the sensitization is governed by a radiative energy transfer upconversion (RETU) process. In our design (Fig. 1), lanthanide-doped NPs function as the energy donor to convert the NIR excitation light into the UV and visible emission light through successive photon absorption and energy transfer upconversion processes within lanthanides. The emission light from the NPs is then reabsorbed by PeQDs to create electron–hole pairs (excitons) in the conduction band and valence band, followed by photon emission through exciton recombination. A key feature of RETU is that the PeQDs possess large absorption coefficient and high PLQY. As a result, tunable upconversion emission with wavelengths beyond the availability of lanthanide-doped NPs is likely to be realized via bandgap tailoring of PeQDs, in parallel with the benefits of lifetime tunability by lanthanide ions and the inherent high conversion efficiency of energy transfer upconversion under low power density excitation.

Fig. 1
Fig. 1

Schematic representation of the radiative energy transfer upconversion (RETU) processes in all-inorganic CsPbX3 perovskite quantum dots (PeQDs) through sensitization by lanthanide-doped nanoparticles (NPs). Lanthanide-doped NPs function as the energy donor to convert the NIR excitation light into the ultraviolet (UV) and visible emission light through successive photon absorption and energy transfer upconversion (ETU) processes within lanthanides. The emission light from the NPs is then reabsorbed by PeQDs to create electron–hole pairs (excitons) in the conduction band (CB) and valence band (VB), followed by photon emission through exciton recombination. The solid and dash lines represent the electronic transitions

Results

Synthesis and characterization

High-quality CsPbX3 PeQDs were synthesized through a facile and novel method by injecting HX (X = Cl, Br, and I) to the precursor solution of Cs-oleate and Pb(II)-oleate at an elevated temperature (Methods). Structure and morphology characterizations through transmission electron microscopy (TEM), X-ray powder diffraction, energy dispersive X-ray spectra, and selected area electron diffraction revealed cubic phase and high crystallinity of the PeQDs with particle sizes of 11.0–13.3 nm (Fig. 2a, b and Supplementary Figs. 1 and 2). Optical absorption spectra showed that the PeQDs had large absorbance in the UV and visible spectral region with band edges shifting from 410 nm to 700 nm as the halide composition changed from Cl to I (Fig. 2c), indicating bandgap tailoring of PeQDs by adjusting the halide composition41. Upon UV excitation at 365 nm, these PeQDs displayed remarkably bright PL with full-gamut color tuning from violet to green and deep red (Fig. 2d). PL spectra of the PeQDs exhibited tunable emission band, which can be ascribed to the band-edge exciton recombination over the entire visible spectral region42, with bandwidths of 11.7–37.0 nm (Fig. 2e and Supplementary Table 1). PL decays indicated effective PL lifetimes of the band-edge excitons in the range of 1.8–81.1 ns with faster decay for wider-bandgap PeQDs (Fig. 2f and Supplementary Table 2). The absolute PLQYs, defined as the ratio of the number of emitted photons to the number of absorbed photons, were determined to be 26.0–79.8% with the highest value of 79.8% for CsPbBr3 PeQDs (Supplementary Table 1).

Fig. 2
Fig. 2

Synthesis and characterization of CsPbX3 perovskite quantum dots (PeQDs). a Transmission electron microscopy (TEM) and b high-resolution TEM images of the as-synthesized CsPbBr3 PeQDs. The scale bars in (a) and (b) represent 100 nm and 5 nm, respectively. c Optical absorption spectra, d photoluminescence (PL) photograph (λ = 365 nm), e PL spectra (λ = 360 nm) and f PL decays of the as-synthesized CsPbX3 PeQDs with varying halide compositions

We synthesized LiYbF4:Tm3+@LiYF4 core/shell NPs through a high-temperature co-precipitation method (Supplementary Note 1) and selected them as the energy donors in view of their intense upconversion emission at 362 nm that can potentially excite the whole series of CsPbX3 PeQDs43. The as-synthesized NPs were rhombohedral and highly crystallized with a mean size of (26.7 ± 1.2) × (33.3 ± 1.8) nm and a shell thickness of 5.5 ± 0.6 nm (Supplementary Fig. 3). Under 980 nm excitation, the NPs displayed intense UCL with a set of sharp and typical emission peaks from Tm3+, which were divided into four regions: the UV region with peaks at 347 nm (1I6 → 3F4) and 362 nm (1D2 → 3H6), the blue region with peaks at 450 nm (1D2 → 3F4) and 483 nm (1G4 → 3H6), the red region with single peak at 648 nm (1G4 → 3F4), and the NIR region with a peak at 792 nm (3H4 → 3H6) (see Fig. 3a for a simplified diagram of transitions in the Yb3+–Tm3+ system and Supplementary Fig. 4)43. Power dependence investigations revealed that at least four pump photons are needed to populate the 1D2 level of Tm3+ to yield the UV emissions and three pump photons are required to feed the 1G4 level to produce the blue and red emissions (Supplementary Fig. 5)44. The UCL lifetimes were determined to be 217, 253, 447, and 601 μs for the decays from 1I6, 1D2, 1G4, and 3H4 of Tm3+, respectively (Supplementary Fig. 6).

Fig. 3
Fig. 3

Full-color upconversion tuning in CsPbX3 perovskite quantum dots (PeQDs) through sensitization by lanthanide-doped nanoparticles (NPs). a Simplified energy-level scheme of LiYbF4:0.5%Tm3+@LiYF4 core/shell NPs indicating major upconversion processes, and schematic illustration of full-color upconversion tuning in CsPbX3 PeQDs through sensitization by the NPs. Black lines represent non-radiative energy transfer and the curved arrows denote internal conversion. b Upconversion luminescence (UCL) spectra for LiYbF4:0.5%Tm3+@LiYF4 core/shell NPs and the NP-sensitized CsPbX3 PeQDs (NPs: 1 mg mL−1; PeQDs: 2 mg mL−1) with varying halide compositions under 980 nm continuous-wave (CW) diode laser excitation at a power density of 50 W cm−2. c Photographs of samples (1–9) under 980 nm illumination, showing color tuning through bandgap tailoring of PeQDs. d Corresponding color gamut of the emission colors (solid white triangle) from the samples shown in (c), compared with the color gamut (dashed white triangle) defined in the NTSC television color standard. e Double logarithmic plots of intensity vs. excitation power for the upconverted exciton emissions from CsPbCl3, CsPbBr3, and CsPbI3 PeQDs at 410, 520, and 700 nm, respectively. f Calculated energy transfer efficiency in NP-sensitized PeQDs, as obtained from (b)

Full-color upconversion tuning in NP-sensitized CsPbX3 PeQDs

To sensitize photon upconversion in CsPbX3 PeQDs, we dispersed the PeQDs with LiYbF4:0.5%Tm3+@LiYF4 core/shell NPs in a homogeneous colloidal cyclohexane solution with a weight ratio of 2:1, in which the NPs can function as an internal UV or blue lamp to illuminate the PeQDs by utilizing the intense UCL of Tm3+ (Fig. 3a). Figure 3b shows the NP-sensitized UCL spectra for CsPbX3 PeQDs under 980 nm CW diode laser excitation. Intriguingly, we observed that the characteristic band-edge exciton emissions from the PeQDs were dominant in the UCL spectra, whereas the emissions of Tm3+ from the NPs were selectively quenched in accordance with the PeQDs absorption, which indicates an efficient energy transfer from the NPs to PeQDs as CW laser cannot trigger photon upconversion in pure PeQDs (Supplementary Fig. 7)17. As a result, multicolor emission with color gamut beyond the three primary colors can be easily achieved by varying the halide composition in PeQDs (Fig. 3c). Moreover, because of the narrow bandwidths of the PeQDs emissions, highly saturated Red-Green-Blue colors can be generated, leading to a wide color gamut with a triangle in the Commission Internationale de l'Eclairage chromaticity diagram encompassing 140% of that defined in the National Television System Committee (NTSC) color standard (Fig. 3d and Supplementary Table 3)45. Such a wide color gamut tuned by NP-sensitized PeQDs is inaccessible by either lanthanide-doped NPs or PeQDs alone and is highly desired for optical coding and three-dimensional displays46,47,48.

Power dependence investigations reveal that the slope of the double logarithmic plots of intensity vs. excitation power is larger than 3 for the upconverted exciton emission from CsPbCl3 and larger than 2 for the emissions from CsPbBr3, CsPbI3, and mixed CsPb(Cl/Br)3 and CsPb(Br/I)3 (Fig. 3e and Supplementary Fig. 8). According to Pollnau et al.34, this may be interpreted as reflecting four-photon and three-photon processes, respectively, whereby energy transfer upconversion appears to be the dominant mechanism. It implies that, at least four pump photons are required to generate the UV emissions of Tm3+ to excite CsPbCl3, whereas only three pump photons are necessary to produce the blue or red emissions of Tm3+, which, in turn, sensitize CsPbBr3, CsPbI3, CsPb(Cl/Br)3, or CsPb(Br/I)3 PeQDs. These results show unambiguously that the upconverted exciton emissions in NP-sensitized PeQDs originate from the NPs-to-PeQDs energy transfer. As shown in Fig. 3f, the energy transfer efficiency was calculated to increase from 65.5 to 96.6 and 99.9% as the halide composition changed from Cl to Br and I (see Supplementary Note 2 and Supplementary Table 4 for details in definition and calculation). The lower efficiency of energy transfer from the NPs to CsPbCl3 can be attributed to the smaller absorbance of CsPbCl3 in UV than the other CsPbX3 PeQDs, as evidenced by their absorption spectra. The absolute upconversion QYs, upon excitation at 980 nm with a power density of 100 W cm−2, were determined to be 0.06 ± 0.01%, 0.39 ± 0.08%, and 0.36 ± 0.09% for exciton emissions in NP-sensitized CsPbCl3, CsPbBr3, and CsPbI3 PeQDs, respectively (Supplementary Note 3 and Supplementary Table 5). The overall upconversion QYs of the NP-sensitized PeQDs are in the range of 0.33–0.45% ( ±0.07−0.13%), which are comparable to that (0.49 ± 0.13%) of pure LiYbF4:0.5%Tm3+@LiYF4 core/shell NPs (Supplementary Table 5). We can estimate the expected partial QYs of the excitons in NP-sensitized PeQDs as being the product of the upconversion QYs of pure NPs by the efficiency of energy transfer and by the PLQYs of PeQDs; in this way, we attained 0.08, 0.38, and 0.28% for the chloride, bromide, and iodide perovskites, respectively, in good agreement with the experimental values mentioned above. This confirms the high photon conversion efficiency in NP-sensitized PeQDs. Note that higher upconversion QYs for CsPbX3 PeQDs could be achieved by improving both upconversion QYs of the NPs and PLQYs of PeQDs.

Mechanistic investigation of the RETU process

In view of the core/shell structure of the NPs that imposed a distance of 5.5 nm between the energy donor and acceptor, we deduced that the energy transfer from the NPs to PeQDs is dominated by a radiative reabsorption process instead of a non-radiative FRET process, because the core/shell structure is unfavorable for distance-dependent FRET49,50. To gain more insights into the energy transfer process, we investigated PeQDs concentration-dependent steady-state and transient UCL in NP-sensitized PeQDs. As shown in Fig. 4a, under 980 nm CW diode laser excitation, the CsPbBr3 emission at 520 nm increased gradually at the expense of the UV and blue emissions of Tm3+ with increasing CsPbBr3 concentration, as a result of energy transfer from the NPs to CsPbBr3 PeQDs. Coincidentally, the UV emission intensities of Tm3+ at 347 nm (1I6 → 3F4) and 362 nm (1D2 → 3H6) dropped much faster than the blue emissions at 450 nm (1D2 → 3F4) and 483 nm (1G4 → 3H6) with increasing CsPbBr3 concentration, whereas the red emissions at 648 nm (1G4 → 3F4) remained nearly unchanged (Fig. 4b). This can be attributed to the much larger absorbance of CsPbBr3 in UV than in blue and no absorption in red (Supplementary Fig. 9). One should keep in mind that the depopulation of 1D2 or 1G4 of Tm3+ through non-radiative FRET would lead to simultaneous quenching of all emissions from 1D2 or 1G432. Thus, the observed distinct UCL evolutions between the emissions from identical 1D2 or 1G4 level reveal that the NPs-to-PeQDs energy transfer may be a radiative reabsorption process rather than a non-radiative FRET process. Such radiative energy transfer was further evidenced by the essentially unchanged UCL lifetimes of 1I6, 1D2, and 1G4 of Tm3+ in NP-sensitized CsPbBr3 PeQDs in comparison with those in NPs alone (Fig. 4c, d and Supplementary Fig. 10), because non-radiative FRET always results in a decrease in lifetime of energy donor by imposing additional relaxation channel on the donor51. The drastically distinct evolutions in PeQDs concentration-dependent UCL between the emissions from 1D2 or 1G4 level and the nearly unchanged UCL lifetimes of Tm3+ were also observed for PeQDs with different halide compositions (Supplementary Figs. 1118), thus demonstrating that the upconverted exciton emission from the NP-sensitized CsPbX3 PeQDs is governed by a RETU process.

Fig. 4
Fig. 4

Mechanistic investigation of the radiative energy transfer upconversion (RETU) process in nanoparticle (NP)-sensitized CsPbX3 perovskite quantum dots (PeQDs). a CsPbBr3 concentration-dependent upconversion luminescence (UCL) spectra for LiYbF4:0.5%Tm3+@LiYF4 core/shell NP-sensitized CsPbBr3 PeQDs with NPs concentration of 1 mg mL−1 under 980 nm excitation at a power density of 50 W cm−2. b Integrated intensities of the Tm3+ emissions at 347, 362, 450, 483, and 648 nm and the CsPbBr3 emission at 520 nm vs. the CsPbBr3 concentration, as obtained from (a). c UCL decays from 1D2 of Tm3+ by monitoring the Tm3+ emission at 362 nm in NP-sensitized CsPbBr3 PeQDs with varying CsPbBr3 concentrations under 980 nm excitation. d UCL lifetimes of 1I6, 1D2, and 1G4 of Tm3+ in NP-sensitized CsPbBr3 PeQDs vs. the CsPbBr3 concentration

Upconversion lifetime tuning in NP-sensitized CsPbX3 PeQDs

More importantly, we discovered that the UCL lifetimes of exciton emissions in NP-sensitized PeQDs were abnormally much longer (hundreds of μs vs. ns) than their PL lifetimes in pure PeQDs. Figure 5a compares the UCL decays from the exciton emissions in NP-sensitized CsPbCl3, CsPbBr3, and CsPbI3 PeQDs, respectively, under 980 nm excitation. It was observed that all the decays displayed similar temporal profiles to that of Tm3+, namely, a rising edge in the initial stage followed by single-exponential decay, as a result of RETU process52. By single-exponential fitting to the decay curves, the UCL lifetimes of CsPbCl3, CsPbBr3, and CsPbI3 PeQDs were determined to be 229, 389, and 416 μs, respectively, in marked contrast to their original PL lifetimes of 1.8, 21.1, and 81.1 ns under UV excitation (Supplementary Table 2). It is worth mentioning that the exciton lifetimes of PeQDs were intrinsically unchanged, but were apparently lengthened due to the slow population of the PeQDs excited state from the long-lived Tm3+ excited state during the radiative energy transfer from the NPs to PeQDs53,54. Therefore, through lifetime tuning of Tm3+ in the NPs, the apparent UCL lifetimes of PeQDs can be modulated. By controlling the Tm3+ concentration from 3 mol% to 0.1 mol% in the NPs, the lifetimes of 1I6, 1D2, 1G4, and 3H4 of Tm3+ increased from 60, 61, 119, and 154 μs to 473, 553, 803, and 1205 μs, respectively (Fig. 5b and Supplementary Fig. 19). Accordingly, the UCL lifetimes of CsPbCl3, CsPbBr3, and CsPbI3 PeQDs sensitized by the NPs were tuned from 61, 81, and 80 μs to 494, 794, and 1053 μs, respectively (Fig. 5c, d). Similar strategy was employed for manipulating the UCL lifetime of exciton in hybrid CsPb(Cl/Br)3 and CsPb(Br/I)3 PeQDs (Supplementary Figs. 2027 and Supplementary Table 6), thus validating the general lifetime tunability in various PeQDs. The ability of ultralong lifetime tuning (61 μs–1.053 ms) along with wide color gamut modulation (140% of the NTSC television color standard) via engineering the composition and concentration of PeQDs, offers us an unparalleled opportunity for constructing a huge library of discernable upconversion identities, which are of vital importance in optical encoding and multiplexing for applications in diverse areas such as complex data storage and multilevel anticounterfeiting55,56.

Fig. 5
Fig. 5

Upconversion lifetime tuning in nanoparticle (NP)-sensitized CsPbX3 perovskite quantum dots (PeQDs). a Upconversion luminescence (UCL) decays from the upconverted excitons in NP-sensitized CsPbCl3, CsPbBr3, and CsPbI3 PeQDs (0.5 mol% Tm3+) by monitoring their emissions at 410, 520, and 700 nm, respectively, under 980 nm excitation. b UCL lifetimes of 1I6, 1D2, 1G4, and 3H4 of Tm3+ in LiYbF4:x%Tm3+@LiYF4 core/shell NPs as a function of the Tm3+ concentration. c UCL decays from the upconverted excitons in NP-sensitized CsPbBr3 PeQDs with varying Tm3+ concentration in the NPs. d UCL lifetimes of CsPbCl3, CsPbBr3, and CsPbI3 PeQDs as a function of the Tm3+ concentration

Generality of the proposed RETU

Furthermore, we demonstrated that the NP-sensitized PeQDs can be fabricated as films by casting them onto glass substrate, from which intense and tunable upconversion emissions were realized under CW diode laser excitation (Fig. 6a). The proposed RETU nanosystem can also be extended to the sensitization of different kinds of quantum dots by employing different lanthanide-doped NPs as energy donors. For example, through sensitization by NaYF4:Yb3+, Er3+ NPs, tunable upconverted exciton emissions were detected in CsPbX3 PeQDs (Fig. 6b). Similarly, upconverted exciton emissions from CdSe and InP@ZnS quantum dots were explicitly observed through radiative energy transfer from LiYbF4:Tm3+@LiYF4 (Supplementary Figs. 28 and 29). These results show the generality of RETU for sensitizing photon upconversion in various quantum dots.

Fig. 6
Fig. 6

Generality of the proposed radiative energy transfer upconversion (RETU) for sensitizing photon upconversion in CsPbX3 perovskite quantum dots (PeQDs). a Upconversion luminescence (UCL) spectra for LiYbF4:0.5%Tm3+@LiYF4 core/shell nanoparticles (NPs) and the NP-sensitized CsPbX3 PeQDs (NPs: 1 mg mL−1; PeQDs: 2 mg mL−1) with varying halide compositions by casting them onto glass substrate under 980 nm CW diode laser excitation at a power density of 50 W cm−2. The insets show the corresponding UCL photographs for the NP-sensitized PeQDs, and the scale bar represents 1 cm. b UCL spectra for NaYF4:18%Yb3+, 2%Er3+ NPs (approximately 23 nm) and the NP-sensitized CsPbX3 PeQDs (NPs: 1 mg mL−1; PeQDs: 2 mg mL−1) with varying halide composition under 980 nm CW diode laser excitation at a power density of 20 W cm−2. The insets show the corresponding UCL photographs for the colloidal cyclohexane solution of the NP-sensitized PeQDs

Discussion

In contrast to multiphoton absorption, the proposed RETU in NP-sensitized CsPbX3 PeQDs is made much more efficient through the use of physically existing intermediate energy levels of lanthanide ions and thus can be triggered by using a low-cost NIR laser diode. In comparison with non-radiative FRET, the RETU nanosystem breaks the distance restriction on energy transfer efficiency, and therefore is much more robust and convenient through simple mixing of lanthanide-doped NPs and PeQDs. Most importantly, as a merit of RETU, the PL lifetime of the exciton in PeQDs inheriting from the excited-state lifetime of lanthanides can be lengthened tremendously from the original nanosecond scale to milliseconds. Such a unique PL lifetime of the exciton is beneficial for electron and hole separation in photovoltaics by distributing the large number of excitons in a much longer time window, and is also highly desirable for time-gated PL biosensing to eliminate the interference of short-lived background noise. Nevertheless, there remain many technical challenges to be overcome toward their practical applications, including the concerns about the stability and toxicity of PeQDs, as well as their upconversion efficiency. We envision that these concerns can be addressed by overall optimization involving the controlled synthesis and surface modification of the NP-sensitized PeQDs. For example, we can encapsulate lanthanide-doped NPs and PeQDs into SiO2 or polystyrene NPs to improve the chemical stability, and employ dye-sensitized lanthanide-doped NPs as an antenna to broaden the excitation wavelengths and boost the upconversion efficiency. Finally, it is urgent to develop lead-free PeQDs with desirable physicochemical properties for optoelectronics and photovoltaics.

To conclude, the optical properties observed in lanthanide-doped NP-sensitized CsPbX3 PeQDs are striking because they have presented the first panorama of photon upconversion with high efficiency and multicolor and lifetime tunability in PeQDs under low power density excitation. These findings offer a general approach for fine tuning NIR-triggered photon upconversion in PeQDs, which may open up a new avenue for the exploration of PeQDs toward versatile applications, such as ultrasensitive bioassay, high-resolution bioimaging, and full-spectrum conversion in solar cells.

Methods

Chemicals and materials

Pb(CH3COO)2·3H2O (99.99%), CH3COOLi·2H2O (99.99%), Cs2CO3 (99.99%), HBr (48%), HI (55.0–58.0%) were purchased from Aladdin (Shanghai, China). Oleic acid (OA, 90%), oleylamine (OAm, 90%), 1-octadecene (ODE, 90%), trioctylamine (98%), Yb(CH3COO)3·4H2O (99.999%), Tm(CH3COO)3·4H2O (99.99%), and Y(CH3COO)3·4H2O (99.99%) were purchased from Sigma-Aldrich (Shanghai, China). NH4F, HCl, cyclohexane, acetone, and ethanol were of analytical grade and purchased from Sinopharm Chemical Reagent Co. (Shanghai, China). All the chemical reagents were used as received without further purification.

Synthesis of CsPbX3 PeQDs

Monodisperse CsPbX3 (X = Cl, Br, and I) PeQDs were synthesized through a modified hot-injection method by using HX as the halide source to precipitate the PeQDs45. As a result, the halide composition of the PeQDs can be precisely adjusted on demand by changing the ratio of HX during the synthesis. In a typical synthesis of CsPbBr3 PeQDs, 0.5 mmol of Pb(CH3COO)3·3H2O and 0.1 mmol of Cs2CO3 were mixed with 2 mL of OA, 2 mL of OAm, and 6 mL of ODE in a 50 mL three-neck round-bottom flask. The resulting mixture was heated to 120 °C under a N2 flow with constant stirring for 40 min to form a clear solution. The temperature was then raised up to 180 °C and stabilized for 10 min, and 1.5 mmol of HBr was quickly injected. After 20 s, the reaction mixture was cooled down to room temperature by ice-water bath. For the synthesis of CsPbCl3 and CsPbI3 PeQDs, 1.5 mmol of HCl and HI instead of HBr was injected, respectively, under otherwise identical conditions. For the synthesis of mixed-halide CsPb(Cl/Br)3 and CsPb(Br/I)3 PeQDs, 1.5 mmol of total amount of mixed HCl/HBr and HBr/HI was injected, respectively. The final halide composition of the PeQDs was designated by the ratio of HCl/HBr/HI used in the synthesis.

Isolation and purification of CsPbX3 PeQDs

The crude solution was cooled down to room temperature with ice-water bath and the PeQDs were collected by centrifuging at 12,000 rpm for 5 min. The precipitate was then dispersed in 1 mL of cyclohexane and centrifuged again at 12,000 rpm for 5 min. After centrifugation, the supernatant was discarded and the PeQDs were redispersed in 30 mL of cyclohexane. Finally, 100 μL of OAm was added and ultrasonicated for 1 min to stabilize the PeQDs for long-term storage.

Structural and optical characterization

Powder X-ray powder diffraction patterns of the samples were collected with an X-ray diffractometer (MiniFlex2, Rigaku) with Cu Kα1 radiation (λ = 0.154187 nm). Both the low- and high-resolution TEM measurements were performed by using a TECNAI G2 F20 TEM equipped with the energy dispersive X-ray spectrum. Optical absorption spectra of CsPbX3 PeQDs were collected with a Perkin-Elmer Lambda365 UV/Vis spectrometer in transmission mode. PL excitation and emission spectra and PL decays were recorded on the FLS980 spectrometer (Edinburgh) equipped with both continuous xenon (450 W) and pulsed flash lamps. UCL emission spectra were acquired under 980 nm excitation with a CW diode laser (2 W). UCL lifetimes were measured with a customized UV to mid-infrared steady-state and phosphorescence lifetime spectrometer (FSP920-C, Edinburgh) equipped with a digital oscilloscope (TDS3052B, Tektronix) and a tunable mid-band Optical Parametric Oscillator pulsed laser as the excitation source (410–2400 nm, 10 Hz, pulse width ≤ 5 ns, Vibrant 355II, OPOTEK). PL photographs of the NPs and PeQDs were taken by using a Canon 70D digital camera without using any filter. The absolute PLQYs of CsPbX3 PeQDs were measured by employing a standard barium sulfate coated integrating sphere (150 mm in diameter, Edinburgh) as the sample chamber that was mounted on the FLS920 spectrometer with the entry and output port of the sphere located in 90° geometry from each other in the plane of the spectrometer. A standard tungsten lamp was used to correct the optical response of the instrument. All the spectral data were recorded at room temperature and corrected for the spectral response of both the spectrometer and the integrating sphere.

Data availability

The authors declare that all data supporting the findings of this study are available within the paper and its supplementary information files.

Additional information

Publisher's note: Springer Nature remains neutral with regard to jurisdictional claims in published maps and institutional affiliations.

References

  1. 1.

    Swarnkar, A. et al. Colloidal CsPbBr3 perovskite nanocrystals: luminescence beyond traditional quantum dots. Angew. Chem. Int. Ed. 54, 15424–15428 (2015).

  2. 2.

    Bekenstein, Y., Koscher, B. A., Eaton, S. W., Yang, P. & Alivisatos, A. P. Highly luminescent colloidal nanoplates of perovskite cesium lead halide and their oriented assemblies. J. Am. Chem. Soc. 137, 16008–16011 (2015).

  3. 3.

    De Roo, J. et al. Highly dynamic ligand binding and light absorption coefficient of cesium lead bromide perovskite nanocrystals. ACS Nano 10, 2071–2081 (2016).

  4. 4.

    Kovalenko, M. V., Protesescu, L. & Bodnarchuk, M. I. Properties and potential optoelectronic applications of lead halide perovskite nanocrystals. Science 358, 745–750 (2017).

  5. 5.

    Song, J. et al. Quantum dot light-emitting diodes based on inorganic perovskite cesium lead halides (CsPbX3). Adv. Mater. 27, 7162–7167 (2015).

  6. 6.

    Wang, Y. et al. All-inorganic colloidal perovskite quantum dots: a new class of lasing materials with favorable characteristics. Adv. Mater. 27, 7101–7108 (2015).

  7. 7.

    Saliba, M. et al. Incorporation of rubidium cations into perovskite solar cells improves photovoltaic performance. Science 354, 206–209 (2016).

  8. 8.

    Swarnkar, A. et al. Quantum dot–induced phase stabilization of α-CsPbI3 perovskite for high-efficiency photovoltaics. Science 354, 92–95 (2016).

  9. 9.

    Huang, H. et al. Water resistant CsPbX3 nanocrystals coated with polyhedral oligomeric silsesquioxane and their use as solid state luminophores in all-perovskite white light-emitting devices. Chem. Sci. 7, 5699–5703 (2016).

  10. 10.

    He, X., Qiu, Y. & Yang, S. Fully-inorganic trihalide perovskite nanocrystals: a new research frontier of optoelectronic materials. Adv. Mater. 29, 1700775 (2017).

  11. 11.

    Zhou, D. L. et al. Cerium and ytterbium codoped halide perovskite quantum dots: a novel and efficient downconverter for improving the performance of silicon solar cells. Adv. Mater. 29, 1704149 (2017).

  12. 12.

    Pan, G. et al. Doping lanthanide into perovskite nanocrystals: highly improved and expanded optical properties. Nano. Lett. 17, 8005–8011 (2017).

  13. 13.

    Deutsch, Z., Neeman, L. & Oron, D. Luminescence upconversion in colloidal double quantum dots. Nat. Nanotechnol. 8, 649–653 (2013).

  14. 14.

    Pan, J. et al. Air-stable surface-passivated perovskite quantum dots for ultra-robust, single- and two-photon-induced amplified spontaneous emission. J. Phys. Chem. Lett. 6, 5027–5033 (2015).

  15. 15.

    Wang, Y. et al. Nonlinear absorption and low-threshold multiphoton pumped stimulated emission from all-inorganic perovskite nanocrystals. Nano. Lett. 16, 448–453 (2016).

  16. 16.

    Xu, Y. et al. Two-photon-pumped perovskite semiconductor nanocrystal lasers. J. Am. Chem. Soc. 138, 3761–3768 (2016).

  17. 17.

    Chen, W. et al. Giant five-photon absorption from multidimensional core-shell halide perovskite colloidal nanocrystals. Nat. Commun. 8, 15198 (2017).

  18. 18.

    Chen, J. S. et al. Size- and wavelength-dependent two-photon absorption cross-section of CsPbBr3 perovskite quantum dots. J. Phys. Chem. Lett. 8, 2316–2321 (2017).

  19. 19.

    Zou, W. Q., Visser, C., Maduro, J. A., Pshenichnikov, M. S. & Hummelen, J. C. Broadband dye-sensitized upconversion of near-infrared light. Nat. Photon. 6, 560–564 (2012).

  20. 20.

    Wang, J. et al. Photon energy upconversion through thermal radiation with the power efficiency reaching 16%. Nat. Commun. 5, 5669 (2014).

  21. 21.

    Lee, J. et al. Universal process-inert encoding architecture for polymer microparticles. Nat. Mater. 13, 524–529 (2014).

  22. 22.

    Zhou, B., Shi, B. Y., Jin, D. Y. & Liu, X. G. Controlling upconversion nanocrystals for emerging applications. Nat. Nanotechnol. 10, 924–936 (2015).

  23. 23.

    Wu, M. et al. Solid-state infrared-to-visible upconversion sensitized by colloidal nanocrystals. Nat. Photon. 10, 31–34 (2015).

  24. 24.

    Jalani, G. et al. Photocleavable hydrogel-coated upconverting nanoparticles: a multifunctional theranostic platform for nir imaging and on-demand macromolecular delivery. J. Am. Chem. Soc. 138, 1078–1083 (2016).

  25. 25.

    Kakavelakis, G., Petridis, K. & Kymakis, E. Recent advances in plasmonic metal and rare-earth-element upconversion nanoparticle doped perovskite solar cells. J. Mater. Chem. A 5, 21604–21624 (2017).

  26. 26.

    Li, J. et al. Stable high-performance flexible photodetector based on upconversion nanoparticles/perovskite microarrays composite. ACS Appl. Mater. Interfaces 9, 19176–19183 (2017).

  27. 27.

    Auzel, F. Upconversion and anti-stokes processes with f and d ions in solids. Chem. Rev. 104, 139–173 (2004).

  28. 28.

    Venkataramanan, M., Fiorenzo, V., Rafik, N., Adolfo, S. & A., C. J. Colloidal Tm3+/Yb3+-doped LiYF4 nanocrystals: multiple luminescence spanning the UV to NIR regions via low-energy excitation. Adv. Mater. 21, 4025–4028 (2009).

  29. 29.

    Haase, M. & Schafer, H. Upconverting nanoparticles. Angew. Chem. Int. Ed. 50, 5808–5829 (2011).

  30. 30.

    Zheng, W. et al. Lanthanide-doped upconversion nano-bioprobes: electronic structures, optical properties, and biodetection. Chem. Soc. Rev. 44, 1379–1415 (2015).

  31. 31.

    Bunzli, J.-C. G. & Piguet, C. Taking advantage of luminescent lanthanide ions. Chem. Soc. Rev. 34, 1048–1077 (2005).

  32. 32.

    Wang, F. et al. Tuning upconversion through energy migration in core-shell nanoparticles. Nat. Mater. 10, 968–973 (2011).

  33. 33.

    Gargas, D. J. et al. Engineering bright sub-10-nm upconverting nanocrystals for single-molecule imaging. Nat. Nanotechnol. 9, 300–305 (2014).

  34. 34.

    Quintanilla, M., Ren, F., Ma, D. & Vetrone, F. Light management in upconverting nanoparticles: ultrasmall core/shell architectures to tune the emission color. ACS Photonics 1, 662–669 (2014).

  35. 35.

    Han, S. Y. et al. Multicolour synthesis in lanthanide-doped nanocrystals through cation exchange in water. Nat. Commun. 7, 13059 (2016).

  36. 36.

    Yan, C. L., Zhao, H. G., Perepichka, D. F. & Rosei, F. Lanthanide ion doped upconverting nanoparticles: synthesis, structure and properties. Small 12, 3888–3907 (2016).

  37. 37.

    Gnach, A. & Bednarkiewicz, A. Lanthanide-doped up-converting nanoparticles: merits and challenges. Nano Today 7, 532–563 (2012).

  38. 38.

    Yan, C., Dadvand, A., Rosei, F. & Perepichka, D. F. Near-IR photoresponse in new up-converting CdSe/NaYF4:Yb,Er nanoheterostructures. J. Am. Chem. Soc. 132, 8868–8869 (2010).

  39. 39.

    Bednarkiewicz, A., Nyk, M., Samoc, M. & Strek, W. Up-conversion FRET from Er3+/Yb3+:NaYF4 nanophosphor to CdSe quantum dots. J. Phys. Chem. C. 114, 17535–17541 (2010).

  40. 40.

    Marin, R. et al. Upconverting nanoparticle to quantum dot Förster resonance energy transfer: increasing the efficiency through donor design. ACS Photonics 5, 2261–2270 (2018).

  41. 41.

    Akkerman, Q. A. et al. Tuning the optical properties of cesium lead halide perovskite nanocrystals by anion exchange reactions. J. Am. Chem. Soc. 137, 10276–10281 (2015).

  42. 42.

    Ravi, V. K., Markad, G. B. & Nag, A. Band edge energies and excitonic transition probabilities of colloidal CsPbX3 (X = Cl, Br, I) perovskite nanocrystals. ACS Energy Lett. 1, 665–671 (2016).

  43. 43.

    Zou, Q. et al. Cooperative and non-cooperative sensitization upconversion in lanthanide-doped LiYbF4 nanoparticles. Nanoscale 9, 6521–6528 (2017).

  44. 44.

    Pollnau, M., Gamelin, D. R., Luthi, S. R., Güdel, H. U. & Hehlen, M. P. Power dependence of upconversion luminescence in lanthanide and transition-metal-ion systems. Phys. Rev. B 61, 3337–3346 (2000).

  45. 45.

    Protesescu, L. et al. Nanocrystals of cesium lead halide perovskites (CsPbX3, X = Cl, Br, and I): novel optoelectronic materials showing bright emission with wide color gamut. Nano Lett. 15, 3692–3696 (2015).

  46. 46.

    Gorris, H. H. & Wolfbeis, O. S. Photon-upconverting nanoparticles for optical encoding and multiplexing of cells, biomolecules, and microspheres. Angew. Chem. Int. Ed. 52, 3584–3600 (2013).

  47. 47.

    Dai, X. et al. Solution-processed, high-performance light-emitting diodes based on quantum dots. Nature 515, 96–99 (2014).

  48. 48.

    Deng, R. R. et al. Temporal full-colour tuning through non-steady-state upconversion. Nat. Nanotechnol. 10, 237–242 (2015).

  49. 49.

    Zhang, J., Fu, Y., Chowdhury, M. H. & Lakowicz, J. R. Enhanced Förster resonance energy transfer on single metal particle. 2. Dependence on donor-acceptor separation distance, particle size, and distance from metal surface. J. Phys. Chem. C. 111, 11784–11792 (2007).

  50. 50.

    Su, Q. Q., Feng, W., Yang, D. P. & Li, F. Y. Resonance energy transfer in upconversion nanoplatforms for selective biodetection. Acc. Chem. Res. 50, 32–40 (2017).

  51. 51.

    Tu, D. T. et al. Time-resolved FRET biosensor based on amine-functionalized lanthanide-doped NaYF4 nanocrystals. Angew. Chem. Int. Ed. 50, 6306–6310 (2011).

  52. 52.

    Luo, W. Q. et al. Er3+-doped anatase TiO2 nanocrystals: crystal-field levels, excited-state dynamics, upconversion, and defect luminescence. Small 7, 3046–3056 (2011).

  53. 53.

    Cardoso Dos Santos, M. & Hildebrandt, N. Recent developments in lanthanide-to-quantum dot FRET using time-gated fluorescence detection and photon upconversion. TrAC-Trend Anal. Chem. 84, 60–71 (2016).

  54. 54.

    Díaz, S. A. et al. Bridging lanthanide to quantum dot energy transfer with a short-lifetime organic dye. J. Phys. Chem. Lett. 8, 2182–2188 (2017).

  55. 55.

    Zhang, F. et al. Fluorescence upconversion microbarcodes for multiplexed biological detection: nucleic acid encoding. Adv. Mater. 23, 3775–3779 (2011).

  56. 56.

    Lu, Y. Q. et al. Tunable lifetime multiplexing using luminescent nanocrystals. Nat. Photon. 8, 33–37 (2014).

Download references

Acknowledgements

This work is supported by the 973 program of MOST (no. 2014CB845605), the Strategic Priority Research Program of the Chinese Academy of Sciences (XDB20000000), the NSFC (nos. 21325104, 21771185, 11774345, U1305244, 21501180, and 11704380), the CAS/SAFEA International Partnership Program for Creative Research Teams, the CAS Youth Innovation Promotion Association (no. 2016277), the Chunmiao Project of Haixi Institutes of the CAS (no. CMZX-2016–002), and Natural Science Foundation of Fujian Province (no. 2017I0018).

Author information

Affiliations

  1. CAS Key Laboratory of Design and Assembly of Functional Nanostructures, and Fujian Key Laboratory of Nanomaterials, Fujian Institute of Research on the Structure of Matter, Chinese Academy of Sciences, Fuzhou, 350002, Fujian, China

    • Wei Zheng
    • , Ping Huang
    • , Zhongliang Gong
    • , Datao Tu
    • , Jin Xu
    • , Qilin Zou
    • , Renfu Li
    • , Wenwu You
    •  & Xueyuan Chen
  2. University of Chinese Academy of Sciences, 100049, Beijing, China

    • Zhongliang Gong
    •  & Xueyuan Chen
  3. Institute of Chemical Sciences and Engineering, Swiss Federal Institute of Technology, Lausanne (EPFL), CH-1015, Lausanne, Switzerland

    • Jean-Claude G. Bünzli

Authors

  1. Search for Wei Zheng in:

  2. Search for Ping Huang in:

  3. Search for Zhongliang Gong in:

  4. Search for Datao Tu in:

  5. Search for Jin Xu in:

  6. Search for Qilin Zou in:

  7. Search for Renfu Li in:

  8. Search for Wenwu You in:

  9. Search for Jean-Claude G. Bünzli in:

  10. Search for Xueyuan Chen in:

Contributions

W.Z. and X.C. conceived the projects, wrote the paper, and were primarily responsible for the experiments. P.H., D.T., J.X., and J.-C.G.B. provided input into the design of the experiments. Z.G. and Q.Z. synthesized and characterized the NPs and PeQDs. R.L. and W.Y. carried out the QY measurement and calculation. All authors contributed to the analysis of the manuscript.

Competing interests

The authors declare no competing interests.

Corresponding author

Correspondence to Xueyuan Chen.

Electronic supplementary material

About this article

Publication history

Received

Accepted

Published

DOI

https://doi.org/10.1038/s41467-018-05947-2

Comments

By submitting a comment you agree to abide by our Terms and Community Guidelines. If you find something abusive or that does not comply with our terms or guidelines please flag it as inappropriate.