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Chaotong Zhou, Yu Ma, Fan Jiang, Guoying Zhao, Jingshan Hou, Yufeng Liu, Xin Qiao, Zhongzhi Wang, [Ji-Guang Li](https://orcid.org/0000-0002-5625-7361), Yongzheng Fang

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[Enhanced the luminescent performance of CsPbI3 quantum dot-embedded borosilicate glass by controlling crystallization using Dy3+ ions as nucleating agent for remote color-tunable LEDs](https://mdr.nims.go.jp/datasets/5f3a837c-1015-4d9a-8db1-ae9669beab2b)

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1  Enhanced the luminescent performance of CsPbI3 quantum 1 dot-embedded borosilicate glass by controlling 2 crystallization using Dy3+ ions as nucleating agent for remote 3 color-tunable LEDs  4 Chaotong Zhou1, Yu Ma1, Fan Jiang1, Guoying Zhao1*, Jingshan Hou1, Yufeng Liu1, Xin Qiao2*, 5 Zhongzhi Wang2, Ji-Guang Li3, Yongzheng Fang1* 6 1 School of Materials Science and Engineering, Shanghai Institute of Technology, Shanghai 201418, 7 PR China 8 2Baotou Research Institute of Rare Earths, Baotou, 014030, China 9 3Research Center for Functional Materials, National Institute for Materials Science, Tsukuba, 10 Ibaraki 305-0044, Japan 11 *Corresponding author, E-mail addresses: zhaogy135@126.com; qiaoxinbt@163.com; 12 fyz1003@sina.com. 13 Abstract：Different concentrations of Dy3+ and perovskite quantum dots (PQDs) 14 were simultaneously embedded in the B-Si-Zn glasses by melt-quenching and 15 heat-treatment subsequently. A battery of experimental results including TEM, 16 distribution of different elements, and photoluminescence prove that partial Dy ions 17 are successfully doped into CsPbI3 and played different roles depending on the doping 18 concentration. When the Dy3+ concentration is circa 0.1mol%, Dy3+ as a nucleation 19 agent reduces the energy required for the precipitation and growth of perovskite 20 quantum dots, obtaining outstanding quantum efficiency of 31.82%. The excess Dy3+ 21 supplement will prevent the mobility of PQDs elements. Based on the as-made glass 22 sample, the remote fluorescent films have been successfully prepared. A kind of 23 prototype lighting device was assembled, which demonstrated a high color rendering 24 index of 96.5 under the current of 20mA. Interestingly, by adjusting the concentration 25 of Dy3+, color regulation can be achieved from orange-red light to yellow-white light.  26 Keywords: CsPbI3; Dy3+; Boron-silicate glass; Remote fluorescent films; High 27 quantum efficiency 28  29  30 Revised manuscript Click here to access/download;Manuscript;revised manuscript.docxClick here to view linked Referenceshttps://www.editorialmanager.com/noc/download.aspx?id=787691&guid=cfbb5a92-110b-4fb2-880d-1b4bb5e4054a&scheme=1https://www.editorialmanager.com/noc/download.aspx?id=787691&guid=cfbb5a92-110b-4fb2-880d-1b4bb5e4054a&scheme=1https://www.editorialmanager.com/noc/viewRCResults.aspx?pdf=1&docID=37992&rev=1&fileID=787691&msid=558ca5b5-ae63-4b4e-a1f5-de8ac1a58cbc2  1. Introduction 1 In recent years, inorganic cesium lead halide (CsPbX3, X=Cl, Br, I) perovskite 2 quantum dots (PQDs) have attracted a lot of attention because of their excellent 3 optical properties such as narrow full width at half maxima (FWHM), precisely 4 tunable bandgap, large absorption intensity and high photoluminescence quantum 5 yield (PLQY), which suggests great potential applications in optoelectronic fields 6 including lighting, display as well as lasing[1-4]. Unfortunately, colloidal CsPbX3 7 PQDs generally suffer from poor long-term stability upon the impact of moisture, heat 8 and light irradiation of their low formation energy and ionic crystal features[5-7]. In 9 previous studies, glass has become a well-regarded host for protecting perovskite 10 quantum dots. The transparent glass matrix can cover the quantum dots, achieving 11 good stability and maintaining the quantum dots excellent optical properties[8-10].  12 Different to the wet-chemical synthesis route to fabricate colloidal CsPbX3 PQDs,   13 the nucleation mechanism and growth behavior of quantum dots are greatly restricted 14 by the properties of mother glass melt, though it protects them from environmental 15 induced degradation[1,11,12]. During the heat treatment processing, the viscosity and 16 rigidity of glass melt will hinder the mobility of Cs+, Pb2+ and X- ions, which make it 17 difficult to obtain the whole-family precipitation of CsPbX3 PQDs[13]. Consequently, 18 how to realize controlled crystallization of quantum dots in glass remains challenging. 19 Moreover, PLQYs of glass-stabilized CsPbX3 PQDs are relatively lower than that of 20 corresponding colloidal counterparts, especially CsPbI3, which becomes a major issue 21 to obstruct the practical application in solid-state lighting. To address this problem, 22 Chen et al introduced F- ions into borosilicate glass, obtaining PLQY of 50% from 23 CsPbI3[13]. Recently, the CsPbI3 PQDs@glass has been prepared in our groups, and 24 the highest PLQY value of glass stabilized CsPbI3 reaches 17.1% by virtue of the 25 regulation of glass grid structure[1]. It is reported that the PLQY of pure CsPbI3 26 PQDs@glass is only 4.2%[14]. 27 Another critical disadvantage of PQDs@glass is reabsorption between excitation 28 and emission energy. In the current LEDs based on CsPbX3 PQDs glass, it is 29 necessary to mix different halogen synthesis glass powder to obtain a variety of 30 multi-color converters by careful regulation[15]. In view of wide absorption band of 31 CsPbX3 PQDs, the energy transfer of excitation photons among different color glass 32 powder is inevitable. In addition, it is difficult to obtain an appropriate proportion of 33 CsPbX3 PQDs in glass powder and ultimately get a white light via excitation by 34 blue-chip, leading to a completely complicated and inefficient process[16,17]. The 35 javascript:;javascript:;javascript:;3  existing technology is still not rid of the shortcomings of the dispensing LED package, 1 such as complex operation and low efficiency[18]. Therefore, we need to synthesize a 2 CsPbX3 PQDs glass that can both effectively improve the operability and also enable 3 better application in light-emitting diodes (LEDs). In this work, the remote 4 fluorescent film of a single system has been successfully prepared for effectively 5 solving the above problems. 6 From the above consideration, the rare earth ions, Dy3+ ions, were introduced 7 into CsPbI3 PQDs embedded borosilicate glasses in present work. The reasons for 8 selecting Dy3+ ion are two-fold. Firstly, Dy3+ ion is a kind of glass network modifier, 9 which can break the tightness of glass network, improving the mobility of extrusive 10 Cs+, Pb2+ and I- ions during precipitation processing[1,19,20]. The homogeneous 11 distribution of Dy3+ ion is beneficial to the finely controlled nucleation and growth of 12 PQDs in glass host. Secondly, the yellow and blue color attributed to the f-f electronic 13 transitions of Dy3+ ion will compensate colorimetric absence of CsPbI3 PQDs, for the 14 purpose of enhancing the luminescent performance[21,22]. By adjusting the 15 concentration of Dy3+ dopants in glass matrix, the influence of Dy3+ dopants on 16 structure and optical properties of CsPbI3 PQDs has been systematically studied to 17 explore its potential application in white LEDs. All the experimental results 18 demonstrate that this Dy3+ doped glass-stabilized CsPbI3 PQD characterized with high 19 quantum efficiency, excellent physical/chemical stability and color tunability is a 20 promising converter candidate for remote white LEDs.  21 2. Experimental Section 22 Glass  specimens  with  the  nominal composition  of  23 38SiO2-29B2O3-16ZnO-9Cs2CO3-5.4PbI2-10.8KI-xDy2O3 (x=0，0.1，0.3，0.5，0.7，24 0.8，1.0 mol%) were prepared by conventional melt-quenching. The raw materials 25 were prepared from high-purity SiO2，B2O3，ZnO，Cs2CO3，PbI2，KI and Dy2O3 26 powder. Well-mixed raw materials (15 g) were dissolved in a capped alumina crucible 27 and melted at 1200℃ for 15 min under an ambient atmosphere. Then the molten glass 28 liquid was poured into a preheated copper plate to obtain precursor glass. Furthermore, 29 the CsPbI3 PQDs@glass was successfully prepared through controllable in-situ glass 30 crystallization via heating at 480℃ for 10 h. Finally，the as-prepared glass samples 31 were ground or polished to obtain a shape of 20×15×1.5 mm3 for subsequent 32 characterization. 33 The XRD patterns of the samples were recorded by X-ray diffraction (XRD) 34 system (Rigaku, Ultima IV, Japan) through a Cu Kα radiation source with a scan range 35 javascript:;4  covered from 10 to 80o and a scan rate of 8o/min and 0.02o/step. The microstructure of 1 the sample was studied by TEM (JEM-2100F). The optical absorption spectra were 2 recorded at room temperature using a UV–visible–NIR spectrophotometer (Hitachi, 3 UH4150), working at 400–1800 nm. The photoluminescence properties (excitation 4 spectra, emission spectra, and temperature dependent photoluminescence spectra) 5 were measured by F-7000 spectrofluorometer equipped from Hitachi Instruments. 6 PLQY and fluorescent lifetime for the CsPbI3 PQDs@glass samples were recorded on 7 an Edinburgh Instruments FS5 spectrofluorometer. All measurements were carried out 8 at room temperature. The color of emission light was determined by CIE 1931 (x, y) 9 chromaticity diagram. 10 Absolute photoluminescence Quantum yield (PLQY), defined as the ratio of 11 emitted photons to absorbed ones, was measured by a spectrofluoremeter (FS5). An 12 integrating sphere was mounted on the spectrofluoremeter with the entrance and exit 13 ports located in 90o geometry. The PQD sample was located in the center of the 14 integrating sphere. All the recorded spectroscopic data were corrected for the spectral 15 responses of both the spectrofluoremeter and the integrating sphere. The responses of 16 the detecting systems (integrating sphere, monochromators and detectors) in photon 17 flux were determined using a calibrated tungsten lamp. Based on this setup, PLQY is 18 calculated based on the following equitation 19 samplereference sampleL number of photons emitted number of photons absorbed E E       (2-1) 20 where η represents QY, Lsample the emission intensity, Ereference and Esample the 21 intensities of the excitation light not absorbed by the reference and the sample 22 respectively. The difference in integrated areas between the sample and the reference 23 represents the number of the absorbed photons. The emitted photons were determined 24 by integrating the related emission band. 25  26  27  28  29  30  31  32  33  34 5  3. Result and Discussion 1 3.1 Crystal structure identification  2  3 Figure 1. (a) XRD patterns of CsPbI3 PQD@glasses with different Dy3+ ion doping 4 concentrations; (b) crystal structure of CsPbI3 PQD typical unit cell and the substitution of Dy3+; 5 (c) photographs of CsPbI3 PQDs@glass plates with different Dy3+ ion doping 6 concentrations under daylight and (d) irradiation of a UV lamp. 7 XRD patterns of a series of CsPbI3 embedded glass with different concentrations of 8 Dy3+ are shown in Figure 1a. Evidently, the patterns exhibit a broad hump in the 9 diffraction angle of 26°, indicating that the typical amorphous feature of glass samples 10 [23,24]. No obvious diffraction peaks attributed to CsPbI3 PQDs are observed in XRD 11 patterns, which might be due to the trace amount of quantum dots embedded within 12 glasses[1,25,26]. Fortunately, the bright red color of glass flakes under an ultraviolet 13 lamp confirms the successful precipitation of CsPbI3 PQDs in glass (Figure 1c). In 14 fact, there is a faint yellow light under the naked eye, but due to the low doping 15 concentration of Dy, the luminous efficiency is hardly high. By contrast，the light 16 from quantum dots is more concentrated and sharper, therefore，it appears red in the 17 glass eventually.  Figure.1b demonstrates the unit-cell structure of the CsPbI3 PQD. 18 It consists of 12-coordinated Cs+ ions and 6-fold coordinated Pb2+ ions. With the 19 increasing doping concentration of Dy3+ ions, the color of glass samples changed 20 remarkably as shown in Figure 1c and d. It is indicated that the ligand surrounding 21 Dy3+ ions has an important impact on the growth and photoluminescent behavior of 22 6  CsPbI3 PQD. 1  2  3 Figure 2. HRTEM spectra of CsPbI3 QDs glass without Dy3+ (a, b) and with 0.5 mol% Dy3+ 4 doping (c, d); the inset of (a) and (c): the particle size distribution for CsPbI3 PQDs in the 5 glass without Dy3+ and with 0.5 mol% Dy3+ doping, respectively; (e-h) Cs, Pb, I, Dy 6 elemental mappings. 7 In order to further explore the existential state of Dy3+ ions in glass, 8 high-resolution TEM (HRTEM) images of CsPbI3 QDs glass without and with 0.5 mol% 9 Dy3+ doped samples are depicted in Figure 2. The clear lattice fringes with an 10 inter-planar distance of 2.78 Å evidence the successful precipitation of CsPbI3 PQDs 11 with high-crystallinity, which corresponds to the (112) crystal facet. This value of 12 CsPbI3 PQDs is decreased to 2.75 Å since the introduction of 0.5 mol% Dy3+ into 13 glass matrix. The ionic radius of Dy3+ in 6-fold coordination is 0.912 Å  suggesting 14 substitution at Pb2+ (1.19 Å ) sites in CsPbI3 PQD[27]. The much big size difference 15 between Dy3+ and Pb2+ in octahedral coordination gives reasonable evidence for the 16 reduced inter-planar distance of (112) crystal facet. Notably, Figure 2a demonstrates 17 the homogeneous distribution of PQDs with an average diameter of 3.8 nm. After the 18 introduction of Dy3+, the average diameter of PQDs was decreased to 3.4 nm in 19 Figure 2c. By comparison, the spot size in Figure 2c exhibits the relatively regular 20 distribution in Dy3+ ions doped glass sample.  21 The EDS mapping that includes Cs, Pb, I and Dy elements were carried out to 22 7  check the possible reaction between quantum dots and rare earth ions, as shown in 1 Figure 2e-h. It is clearly seen that these elements are homogeneously dispersed in host 2 glass. Nevertheless, the evidence that the overlap of the element distribution between 3 Dy and I is comparatively small manifests that partial Dy3+ ions are involved in 4 CsPbI3 PQDs synthesis inevitably. As a result, there are two kinds of quantum dots in 5 glass host, that is, CsPbI3 and CsDyI3. Dy2O3 as raw material is a glass network 6 modifier, which can break the chemical bonds of bridging oxygens during the glass 7 network forming processing. Therefore, the destruction of the ligand surrounding 8 around reduces the energy required for the precipitation of all elements, promoting the 9 formation of quantum dots [13,28]. Notably, the introduction of excessive Dy3+ 10 supplements in raw material will limit the growth of PQDs in glass. Dy3+ ions seem to 11 be an obstacle in the transmitting tunnel of all PQD elements. This can be explained 12 by the adverse impact of Dy3+ for the surrounding elements polymerization, leading to 13 hindering the mobility of extrusive Cs+, Pb2+ and I- ions from grid. Besides, the 14 homogeneous distribution of Dy3+ in glass host is beneficial to guide to regular 15 arrangement of quantum dots.  16 3.2 Luminescence Properties  17 In order to clarify the fluorescence property of CsPbI3 QDs glasses doped with 18 different concentrations of Dy3+, the absorption and emission spectra were examined 19 and shown in Figure 3a-b, respectively. The absorption spectra of glass samples have 20 five sharp absorption peaks located at 800 nm, 896 nm, 1088 nm, 1271 nm and 1675 21 nm, which are characteristic absorption peaks of rare earth ion Dy3+[20]. Moreover, a 22 wide absorption band peaked around 680 nm is attributed to CsPbI3 PQDs[29]. 23 Interestingly, the absorption cut-off edge is detected to shift to the ultraviolet sideband 24 with the increasing Dy3+ concentration, which is probably associated with the lower 25 PQDs concentration resulting from the inhibiting effect aroused by excessive Dy3+ 26 ions. Figure 2b exhibits the photoluminescence (PL) spectra of as-made samples 27 under excitation at 365 nm. Three emission peaks can be easily seen from PL spectra 28 except for the un-doped sample. The blue emission band peaked at 484 nm and 29 yellow emission band peaked at 576 nm are attributed to the 4f-4f electronic transition 30 4F9/2→6H15/2 and 4F9/2→6H13/2 of Dy3+ ions, respectively. Besides, the red emission 31 band around 620-650 nm originates from direct exciton recombination[12]. Except for 32 the sample doped with 0.1 mol% Dy3+ ions, the peak wavelength of red emission shift 33 towards the shorter wavelength side until it nearly quenches as the concentration of 34 Dy3+ increases. Meanwhile, the intensity of red emission exhibits a similar change 35 8  tendency. Based on the above discussion, both sides of the introduction of Dy3+ ions 1 into glass system should be responsible for this phenomenon. It is reasonable to 2 conclude that there exists an optimal concentration of Dy3+ ions around 0.1 mol% in 3 glass, which can boost the migration of PQDs element by loosening the glass grid. 4 Dy3+ ion as glass network modifier breaks the bridging oxygen’s links, as a result, 5 reduces the energy required for precipitation and nucleation of CsPbI3 PQDs[1,13]. 6  The PL spectra reveal that the optimal Dy3+ doping concentration is circa 0.1 7 mol%. Correspondingly, the PLQY results also support this finding. Figure 3c 8 exhibits the quantitative emission spectra of 0.1 mol% Dy3+ CsPbI3 quantum dot glass 9 and the reference sample and the corresponding absolute quantum yield, which was 10 measured at an excitation wavelength of 365nm. The dependence of absolute PLQY 11 values on the Dy2O3 content was recorded, as shown in Figure 3c, which has a similar 12 tendency with CsPbI3 QDs luminescence intensity. When Dy concentration is 0.1 13 mol%, the PLQY of red emission from PQDs embedded glass reaches the maximum 14 value that is 31.82%. The excess Dy offer results in a drop of PLQY, which further 15 evidences our insights of both sides. A similar change has also been detected in PL 16 decay curve measurements (Figure 3d). To gain more understanding of the ligand 17 surrounding Dy3+ in glass, the yellow-blue emission intensity (Y/B) ratio of Dy3+ was 18 calculated and exhibited in the inset of Figure 3c. The 4F9/2→6H13/2 (yellow) transition 19 is electric dipole (ED) transition and hypersensitive in nature, while the 4F9/2→6H15/2 20 (blue) transition is magnetic dipole (MD) dominant. The intensity ratio of electric 21 dipole to magnetic dipole transitions has been used to measure the asymmetry and 22 degree of covalence of the local environment of Dy3+ ions[30,31]. With the increasing 23 Dy3+concentration, Y/B ratio roughly exhibits the increasing trend. A twofold increase 24 suggests the great change in ligand environment surrounding Dy3+ ions. It can be 25 concluded that a great number of Dy3+ ions are located inside the distorted iodine 26 octahedron, resulting in the formation of CsDyI3. The regular structure of quantum 27 dot and low covalence state of Dy3+-I- should be responsible for the low Y/B ratio 28 when the concentration of Dy3+ ion in glass is 0.1 mol%. After the excess amount of 29 Dy3+ ions were introduced into glass system, the structural tolerance capacity and low 30 content of perovskite quantum dot drive the doped Dy3+ into amorphous phase. As a 31 result, Y/B ratio is increased. Figure 3d exhibits the decay curves of CsPbI3 PQDs in 32 glasses, Nanosecond lifetime confirmed the typical exciton recombination 33 characteristics of CsPbI3 PQDs embedded in glass. 34 9   1 Figure 3. (a) Absorption spectra of CsPbI3 QDs glasses doped with different concentrations 2 of Dy3+. The illustration shows the amplified absorption spectra near 690 nm (b) Emission 3 spectra of glass samples excited by ultraviolet light at 365 nm. (c) The corresponding 4 absolute quantum yield of CsPbI3 PQDs glass doped with different concentrations of Dy3+ 5 under excitation at 365 nm. Inset: the RIR value of CsPbI3 QDs glasses doped with different 6 concentrations of Dy3+. (d) Fluorescence attenuation curves of monitored wavelengths at 7 620-650 nm under excitation at 365 nm. 8 3.3 Thermal and moisture stabilities 9 Poor stability is a major problem which limits the use of CsPbI3 quantum dots in 10 different applications[32]. The samples were tested for stability and Figure 4a presents 11 the temperature-dependent PL spectra of glass sample measured at an excitation of 12 365 nm. It can be seen that there is no obvious change of the two characteristic peaks 13 of Dy3+ with the temperature rise to 200 from 25℃, but the emission intensity of 14 CsPbI3 PQDs decreases continuously, which is due to the non-radiative transition and 15 lattice relaxation of the luminescence center. Interestingly, as shown in Figure 4b, the 16 intensity of luminescence recovered gradually until it was 82% of its initial intensity 17 as temperature dropped. In addition, the moisture resistance test results showed that 18 the location and intensity of emission peaks of glass sample had little change after 60 19 days (Figure 4c) The integral intensity of PL peak only decreased by less than 5% 20 (Figure 4d), and luminance and color also was no significant change (Figure 4e). 21 Similarly, PLQY is measured as 9.82% for day 0 and 9.79% for day 60 revealing very 22 10  close values. Therefore, it can be concluded that an inorganic glass host is indeed 1 beneficial to efficiently protect PQDs from decomposition by water. In summary, it is 2 borosilicate zinc glass matrix that improves remarkably the thermal stability and 3 moisture resistance of Dy3+ doped CsPbI3 PQDs. 4  5  6 Figure 4. (a) CsPbI3: temperature-dependent fluorescence spectra of Dy3+ perovskite quantum 7 dot glass in the range of 25-200℃ under excitation at 365 nm; (b) CsPbI3: Heating and cooling 8 cycle of emission strength of Dy3+ perovskite quantum dot glass from 25℃ to 200℃.(c) PL 9 spectrum of Dy3+ doped CsPbI3 perovskite quantum dot glass irradiated by UV lamp at 365 nm 10 during immersion in water for 60 days; (d) The variation of the integral intensity of peak PL 11 with time; (e) Photoluminescence photos of Dy3+ doped CsPbI3 perovskite quantum dot glass 12 under the irradiation of 365 nm UV lamp during immersion in water for 60 days 13 3.4. CIE chromaticity coordinates and light-emitting devices 14 Due to the excellent optical properties and stability of the prepared Dy-doped CsPbI3 15 PQDs@glasses, we consider it may have potential application in W-LEDs[33].  It is 16 well known that the most common way to produce W-LEDs is to combine a 17 yellow-emitting yttrium aluminum garnet phosphor with a blue-emitting LED chip[34]. 18 11  This is inconvenient for the human eye to recognize the original color of the object 1 due to its lack of a red-emitting portion[35]. In this work, we prepared Dy-doped 2 CsPbI3 PQDs@glasses, which can be used as a supplement to red light emission. A 3 series of fluorescent glass films of CsPbI3 PQDs with different dysprosium 4 concentrations are prepared. The prepared glass samples of Dy3+ doped CsPbI3 5 quantum dots were ground into powders and dispersed in a uniform mixture of 6 solvents which is terpineol and ethyl cellulose ten to one in a certain proportion 7 prepared a non-precipitating and uniform fluorescent slurry. Subsequently, the 8 fluorescent paste was then evenly applied to the round glass substrate by a rotary 9 coating method. Ultimately, the fluorescent glass film was prepared by drying the 10 organic matter to completely volatilize for 3 hours in a draught drying cabinet at 150℃ 11 (Figure. 5a). As shown in Figure 5b, it is can be seen the color of the glass film 12 gradually changes under UV light. Noteworthy, when the doping concentration of 13 Dy3+ is 0.5 mol%, the color of the glass changes into yellowish-white, manifesting 14 that the as-prepared samples can be applied to W-LED. Therefore, the as-prepared 15 Dy-doped CsPbI3 PQDs@glass was combined with a UV chip to construct a W-LED 16 device (Figure. 5c). Then the photoelectric properties of the LED devices were 17 measured at a current of 20 mA. Besides, the color of these light-emitting diodes 18 changes from red to yellow-green, and it can be certified in the CIE color coordinate 19 diagram (Figure. 5d). The locus of CsPbI3:0.5 mol% Dy3+ glass sample were in a 20 blackbody radiance curve emitting dazzling white light. The corresponding CIE 21 coordinates (x, y), correlated color temperature (CCT), color rendering index (CRI) 22 and purity are listed in Table 1. Therefore, by modifying the content of Dy in the 23 CsPbI3 PQDs glass sample, the optical parameter can be easily tuned to find the best 24 W-LED. The excellent performance of the W-LED device indicates that the 25 as-prepared CsPbI3 PQDs glass has potential applications in solid-state lighting and 26 display[36]. 27 12   1 Figure 5. (a) CsPbI3 PQDs fluorescent glass films with different Dy3+ doping 2 concentrations;(b) a photograph of it under an ultraviolet lamp;(c) Light emitting photos of 3 the prepared white LED devices;(d) CIE color coordinates 4  5 Table 1   Optical performance devices of white LED devices with different Dy3+ concentrations 6 Dy2O3 Concentration (mol%)  CIE coordinates  CCT (K)  CRI  Purity (%) 0 (0.4093,0.3354) 2874 52.9 23.4 0.1 (0.4891,0.3159) 1676 29.3 41.5 0.3 (0.4593,0.3254) 2015 6.6 35.4 0.5 (0.4104,0.3947) 3423 86.6 41.6 0.7 (0.4168,0.3733) 3104 89.7 37.1 0.8 (0.4126,0.3826) 3273 95.6 38.7 1.0 (0.3842,0.3867) 3974 69.7 31.4 4. Conclusion 7 In summary, Dy3+-doped borosilicate glasses embedding CsPbI3 PQDs were 8 successfully prepared by a conventional melt quenching method, and the effect of Dy 9 on optical properties of CsPbI3 quantum dots has been investigated systematically. 10 The TEM measurements verified that Dy3+ doped CsPbI3 quantum dots are uniformly 11 distributed in the glass. Since the increase of Dy3+ doping, the average size of CsPbI3 12 13  PQDs is reduced, leading to blue shift of absorption cut-off wavelength and emission 1 peak. The element distribution diagram shows that a part of Dy3+ exists the lattice of 2 CsPbI3 quantum dots, which promotes the formation of CsPbI3 QDs. The effect of 3 excessive Dy doping is opposite. The fluorescence spectrum revealed that the doping 4 concentration circa 0.1 mol% is conducive to the generation of quantum dots, and the 5 maximum quantum efficiency of 31.8% is obtained. Most importantly, benefiting 6 from the remarkable optical performance and thermal stability, a simple W-LED was 7 fabricated by combining UV chips based on the remote Dy3+ doped CsPbI3 PQDs 8 glass film, which demonstrated outstanding CRI of 95.6 at an operating current of 20 9 mA. By modifying the content of Dy in the CsPbI3 PQDs glass sample, the color of 10 simple W-LED can be easily modified without the other photoluminescent matrial 11 system. This work exploits a new strategy to prepare high-performance CsPbI3 PQDs 12 glass and provides an interesting insight to develop their practical applications in solid 13 state lighting and display.  14  15 Acknowledgement 16 Yongzheng Fang acknowledges financial supported by the the National Key Research 17 and Development Program of China (Grant No. 2021YFB3500500). Guoying Zhao 18 acknowledges financial supported by Science and Technology Talents Development 19 Fund for Young Middle-aged Teachers Fund, Collaborative Innovation Fund (No. 20 XTCX2022-03) of Shanghai Institute of Technology and Development of key 21 technologies for the preparation and application of high-performance rare earth 22 fluorescent block materials (No. BFXT-2022-D0046).  23  24 References: 25 [1] Qi F, Shao X, Ma Y, et al. Improved luminescent performances of CsPbI3 perovskite quantum 26 dots via optimizing the proportion of boron-silicate glass and precipitation processing[J]. Optical 27 Materials, 2022, 124: 111981. 28 [2] Huang X, Guo Q, Yang D, et al. Reversible 3D laser printing of perovskite quantum dots inside 29 a transparent medium[J]. Nature Photonics, 2020, 14(2): 82-88. 30 [3] Lin J, Lu Y, Li X, et al. Perovskite Quantum Dots Glasses Based Backlit Displays[J]. ACS 31 Energy Letters, 2021, 6(2): 519-528. 32 [4] Peng Q, Wang T, Tang H, et al. 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Credit Author StatementDeclaration of interests  ☑The authors declare that they have no known competing financial interests or personal relationships that could have appeared to influence the work reported in this paper.  ☐The authors declare the following financial interests/personal relationships which may be considered as potential competing interests:        Declaration of Interest Statement