Rapid synthesis of phosphor-glass composites in seconds based on particle self-stabilization

Sun, Yongsheng; Wang, Yuzhen; Chen, Weibin; Jiang, Qingquan; Chen, Dongdan; Dong, Guo**; **a, Zhiguo

doi:10.1038/s41467-024-45293-0

Rapid synthesis of phosphor-glass composites in seconds based on particle self-stabilization

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Published: 03 February 2024

Volume 15, article number 1033, (2024)
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Rapid synthesis of phosphor-glass composites in seconds based on particle self-stabilization

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Abstract

Phosphor-glass composites (PGC) are excellent candidates for highly efficient and stable photonic converters; however, their synthesis generally requires harsh procedures and long time, resulting in additional performance loss and energy consumption. Here we develop a rapid synthetic route to PGC within about 10 seconds, which enables uniform dispersion of Y₃Al₅O₁₂:Ce³⁺ (YAG:Ce) phosphor particles through a particle self-stabilization model in molten tellurite glass. Thanks for good wettability between YAG:Ce micro-particles and tellurite glass melt, it creates an energy barrier of 6.94 × 10⁵ zJ to prevent atomic-scale contact and sintering of particles in the melt. This in turn allows the generation of YAG:Ce-based PGC as attractive emitters with high quantum efficiency (98.4%) and absorption coefficient (86.8%) that can produce bright white light with luminous flux of 1227 lm and luminous efficiency of 276 lm W⁻¹ under blue laser driving. This work shows a generalizable synthetic strategy for the development of functional glass composites.

Highly efficient phosphor-glass composites by pressureless sintering

Article Open access 04 June 2020

Facile fabrication of Eu3+ activated YAG:Ce3+ glass ceramics exhibiting high thermal stability and tunable luminescence for warm white LEDs

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Synthesis of High-Performance YAG:Ce Phosphor Powder with Low Sintering Temperature and YAG:Ce-Doped Bi-B Glass by a One-Step Method

Article 27 May 2024

Introduction

Rare earth phosphor materials as photonic converters, exampled by commercial Y₃Al₅O₁₂:Ce³⁺(YAG:Ce), CaAlSiN₃:Eu²⁺, and Sr[LiAl₃N₄]:Eu²⁺, etc., have received broad attentions in lighting and display^{1,2,Full size image}

To investigate the interfacial stability between YAG:Ce particles and tellurite glass, we firstly measured the X-ray diffraction (XRD) patterns of YAG:Ce-PGC. Obviously, all diffraction peaks are coincident to YAG phase suggesting that the incorporation of YAG:Ce did not induce the precipitation of other crystalline phases (Supplementary Fig. 6). Subsequently, the local structures of YAG:Ce-PGC were evaluated by Raman vibrational modes (Supplementary Fig. 7). The Raman spectra of the YAG:Ce-PGC fabricated at 650 °C, with a superposition of those from tellurite glass and YAG:Ce, represents a pivotal signal that the interface reaction is absent during rapid synthesis. The interfacial stability of YAG:Ce particles dispersed in tellurite glass at nanometer scale was further characterized by high-resolution transmission electron microscopy (HRTEM), selected area electron diffraction (SAED), and energy dispersive spectroscopy (EDS) map** analysis. As illustrated, a boundary line between crystal and amorphous phases is explicit, and HRTEM images and SAED patterns confirm the cubic garnet phase of YAG:Ce and the amorphous phase of tellurite glass (Supplementary Fig. 8). From the high-angle annular dark-field scanning transmission electron microscopy (HAADF-STEM) image, a well-defined boundary can be also observed, which is manifested by the EDS map** profile, showing significant elemental differences and no observable element diffusion region between the YAG:Ce crystal and tellurite glass (Fig. 1g). These results indicate that interfacial interactions between YAG:Ce particles and tellurite glass are negligible, which is in stark contrast to the thickness of about 50–300 nm in the previous studies^13,26,36,37, and it further proves that our synthesis method is a nondestructive composite strategy.

Verification of particle self-stabilization model

To investigate the dispersion stability of YAG:Ce particles in tellurite glass melt, we put the glass melt with uniformly dispersed YAG:Ce particles back into the high-temperature furnace to continue heating at 650 °C and took it out at different holding times, quenched, and formed. The YAG:Ce particles were uniformly dispersed even after our samples remained in the liquid state for about 120 s without agitation processing (Supplementary Fig. 9). This provides convincing evidence that YAG:Ce particles realize good dispersion and self-stabilization in molten tellurite glass before solidification. To better understand the physical process, a theoretical analysis was performed, and the details were given in the methods section on the particle self-stabilization model. The results show that the particle self-stabilization is ascribed to the synergy of the following three main factors, as schematically shown in Fig. 2a: (1) At 650 °C, the small wetting angle between YAG:Ce particles and the molten tellurite glass is 43.5°, which promotes the formation of the new interface with an energy barrier of about 6.94 × 10⁵ zJ, preventing the atomic-scale contact and sintering of YAG:Ce particles in the melt. (2) A attractive van der Waals potential between the YAG:Ce particles in the tellurite glass melt, about −2.42 × 10⁵ zJ at the secondary minimum of Fig. 2a, inducing particle aggregation. (3) A weak thermal energy of about 12.74 zJ helps to drive YAG:Ce particle dispersion.

**Fig. 2: Agitation-based particle self-stabilization model of phosphor-glass composites.**

When we pour the YAG:Ce particles into the low-viscosity tellurite glass melt, the YAG:Ce particles are rapidly dispersed in the melt under the agitation drive of the quartz glass rod and the heat drive (Fig. 2b). Simultaneously, the glass melt quickly wraps the surface of YAG:Ce particles owing to the good wettability between tellurite glass melt and YAG:Ce particles, and forms new interface layers with high energy barrier. The repulsive energy barrier to prevent YAG:Ce particles from contact and sintering, which is the main driving force behind the self-stabilization of YAG particles in the tellurite glass melt, is much higher than attractive van der Waals potential (Fig. 2a). Consequently, the synergy of high repulsive energy barrier and heat energy make the YAG:Ce particles break free from the quasi-clusters formed by van der Waals potential attraction, resulting in dispersed particles in the melt. This particle self-stabilization model allows to create a uniform dispersion of dense particles in liquids and providing more possibilities for functional composites when the repulsive force cannot be generated by conventional techniques. The visualization of intermediate state and final state for YAG: Ce particles in tellurite glass melt by simple agitation, which is helpful to understand the dynamic process of particle dispersion. We utilized the shear stress transport k-omega turbulence model and the discrete phase model in ANSYS Fluent to simulate the flow characteristics of the fluid and the motion state of the particles^38,39. The particles in the crucible container were dispersed downward in a spiral shape under the different agitation speed to 1, 3, and 5 rev s⁻¹ (Fig. 2c and Supplementary Fig. 10). When the agitation speed is increased to 5 rev s⁻¹ for 3–5 s, the particles are uniformly filled throughout the fluid, and the velocity of the particles is almost the same. The simulation results fully demonstrate that the complete dispersion of YAG:Ce particles can be achieved only by using simple agitation strategy under the low viscosity characteristic of tellurite glass.

Performance characterizations of YAG:Ce-PGC

Thanks for stable particle interface and uniform dispersion of YAG:Ce phosphor particles in tellurite glass, the YAG:Ce-based PGC can be used as an attractive photonic converter. As depicted in Fig. 3a, the photoluminescence excitation (PLE) spectra of YAG:Ce-PGC consist of two excitation bands centered at 343 nm and 450 nm, respectively. Under 450 nm blue light excitation, the 5d → 4 f transition of Ce³⁺ brings a broad yellow emission with the center wavelength of 552 nm⁴⁰. However, the weak excitation peak at 343 nm in YAG:Ce-PGC contributes to the high absorption of the tellurite glass in the ultraviolet range (Fig. 1d). The PLE and PL spectra of YAG:Ce-PGC exhibit similar profiles to YAG:Ce powder, demonstrating that the embedded YAG:Ce particles are the active components of YAG:Ce-PGC. Similarly, the PL decay curves of YAG:Ce-PGC and YAG:Ce powder overlap almost completely (Supplementary Fig. 11). The unchanged steady-state and transient PL properties of YAG:Ce further confirm the negligible interface reaction between YAG:Ce and tellurite glass. As portrayed in Fig. 3b, the IQE of all samples is no less than 92%, with an absorption of no less than 85% (Supplementary Table 2). The high quantum efficiency and absorption are put down to the fact that the undamaged YAG:Ce particles are densely and uniformly dispersed in the tellurite glass matrix, producing high-efficient light scattering. Moreover, YAG:Ce-PGC 20 wt% sample possesses thermal conductivities of 1.52 and 1.78 W m⁻¹ K⁻¹ at ambient temperature and 250 °C, respectively, which is seven times that of organic resins (0.2 W m⁻¹ K⁻¹) and comparable to silica glass (1.49 W m⁻¹ K⁻¹) (Supplementary Fig. 12)²⁵. The relatively high thermal conductivity also facilitates the application of high-power light sources. The proposed strategy is a general way for the development of various PGC. To verify this, diverse translucent PGC samples have been synthesized by replacing YAG:Ce with LuAG:Ce and GdAG:Ce (denoted as LuAG:Ce-PGC and GdAG:Ce-PGC, respectively). As expected, all the as-synthesized PGC are highly efficient with limited IQE loss (Supplementary Fig. 13).

**Fig. 3: Optical characterization of YAG:Ce-PGC flat discs.**

To evaluate the potential application of laser-driven white light illumination, the photoelectric properties of YAG:Ce-PGC were characterized (Fig. 3c). Under the excitation of focused blue laser, the luminous flux (LF) initially showed a linear increase with the incident laser power, reaching its peak value and then sharply decreased (Fig. 3d). This emission saturation at high power density is commonly observed in laser-driven illumination, attributed to the accumulated heat in the color converter and subsequent PL thermal quenching³³. With increasing do** concentration, the saturation threshold of the YAG:Ce-PGC sample first increased and then decreased, almost the same as that of the sample temperature (Supplementary Fig. 14), which indicates the higher the concentration of YAG:Ce phosphor, the more blue lasers may be down-converted in the same radiation region, generating more heat and accelerating the luminous saturation of the sample²⁶. Prior to the occurrence of emission saturation, the luminous efficiency gradually decreased (Fig. 3e), and the maximum values of luminous flux, luminous efficiency, and the laser saturation threshold are 1227 lm, 276 lm W⁻¹ mm⁻¹, 8.5 W mm⁻¹, respectively. It is found that the as-measured parameters are superior to commercial YAG:Ce phosphor in glass (YAG:Ce-PiG), and the detailed composition is shown in Supplementary Fig. 15 and Supplementary Table 3. The corresponding CRI and CCT decreased with increasing do** concentration (Supplementary Fig. 16). The CRI and CCT of the PGC samples with YAG:Ce do** concentration between 10 wt% and 15 wt% show a sudden drop, attributed to the synergy of increase in YAG:Ce content and porous characters (Supplementary Fig. 17). The thermal performance of the color converter is crucial in light source applications. As shown in the supplementary Fig. 18, the integrated emission intensity of YAG:Ce-PGC at 150 °C can still maintain 96% of that at 30 °C, and is also superior to that of YAG:Ce phosphor in silicone resin (YAG:Ce-PiS) and YAG:Ce powder. In addition, the operational stability of composites was tested under different encapsulation strategies under continuous 2 W mm⁻² blue laser irradiation. As plotted in Fig. 3f, YAG:Ce-PGC exhibited comparable operation stability as the commercial YAG:Ce-PiG under continuous 7.5 h blue laser irradiation, while the YAG:Ce-PiS was irreversibly destroyed merely within 30 s at the same power. These excellent optical performance and stability undoubtedly validate that the rapid synthesis strategy of YAG:Ce fully encapsulated in dense tellurite glass can not only achieve phosphor particle integrity, but also effectively protect YAG:Ce phosphor from oxygen, moisture, light exposure, and heat damage.

In summary, we propose a facile and fast agitation synthetic protocol in seconds for phosphor-glass composites with stable particle interface and dense uniform dispersion. Theoretical and experimental studies reveal that the dense uniform dispersion of phosphor particles in tellurite glass originates from the good wettability between YAG:Ce particles and the tellurite glass melt, which creates an energy barrier to prevent particle clustering in the melt. The nondestructive interface of phosphor and tellurite glass can be emanated in local structures and confirmed by the improved luminescence properties. The resultant YAG:Ce-based PGC possess high quantum efficiency of 98.4% and absorption coefficient of 86.8%, presenting great potential for high-power white lighting. In addition, the universality of the strategy is confirmed, and different color-tunable translucent composites are also prepared. This work provides a straightforward and general synthetic protocol to functional glass composites for various light-emitting and light-detecting applications, and further expands the scope of imagination for the design and practical application of glass based composite materials with high stability.

Methods

Raw materials

TeO₂, ZnO₂, and Na₂CO₃ (Shanghai Aladdin Biochemical Technology Co., Ltd.) were used as the starting ingredients with a purity of 99.99%. Commercial yellow phosphor YAG:Ce, green phosphor LuAG:Ce, orange-yellow phosphor GdAG:Ce, and silicone resin A/B was purchased from Shenzhen Looking Long Technology Co., Ltd, China. Commercially available YAG:Ce-PiG was offered by Bright Phosphor Composites Tech., Ltd. in China.

Precursor glass, YAG:Ce-PGC, and YAG:Ce-PiS fabrications

The precursor tellurite glass matrix consisted of 75TeO₂, 15ZnO, and 10Na₂O (mol%) was produced using the traditional melt-quenching method. The process involved melting the corresponding raw ingredients in the presence of air for 40 min at 700 °C and subsequent melt-quenching to form glass. The as-prepared precursor glass was then crushed and ground into powders for the second melting process. The glass powder is put into the corundum crucible and melted in 650 °C for 40 min until the high-temperature melt is completely clarified. The crucible is removed and the YAG:Ce phosphor is quickly poured into the high-temperature melt, and the quartz glass agitation rod is quickly agitated for about 5 s, then the melt mixture is immediately poured out to form and placed in the 280 °C annealing furnace to remove internal stress. YAG:Ce phosphor in silicone resin (YAG:Ce-PiS) sample with 10 wt% phosphor concentrations was prepared in this study for a comparison. The YAG:Ce-PiS sample preparation method is as follows: the silicone resin A/B and phosphor are first weighed according to the mass ratio, stirred evenly, and then subjected to vacuum drying to remove the bubbles. Finally, the mixture is injected into the disc mold, heated to 100 °C for 3 h, and finally the composite material is obtained.

Characterizations

An Aeris X-ray diffractometer (PANalytical Corp.) operating at 40 kV and 15 mA with monochromatized Cu Kα radiation (λ = 1.5406) and a linear VANTEC detector was employed for collecting the powder X-ray diffraction (XRD) patterns. Using a confocal laser scanning microscope (TCS SPE, Leica, Germany) at an excitation wavelength of 488 nm, the 3D distribution of phosphor particles within tellurite glass was studied. PL spectra and decay curves were characterized using a high-resolution spectrofluorometer (FLS1000, Edinburgh Instruments, UK) equipped with a Xe lamp as an excitation source and R928 photomultiplier (200–900 nm) as a detector. The temperature-dependent emission spectra were measured on a temperature controller in the same instrument. The Raman spectra were recorded on a Raman spectrometer (Renishaw in Via, London, UK) under the excitation of a 785 nm laser. The QE and absorption efficiency of all samples were measured by the absolute photoluminescence quantum yield spectrometer (Hamamatsu, C13534). The morphology image of YAG:Ce was acquired on SEM (Zeiss Merlin), and, and a layer of gold was sputtered to the surface of the sample to enhance the conductivity. The surface morphology and compositions of the samples were characterized by a TEM (Titan Themis Z 300 kV, Thermos-Fisher scientific) and a dual-beam FIB microscope (FIB-SEM, Helios G4, Thermo Scientific, USA) was used to thin the sample. High-resolution lattice fringe and selected area electron diffraction (SAED) were tested using environmental transmission electron microscopy (FEI Titan G2 60–300). The thermogravimetric-differential scanning calorimetric (TG-DSC) curves of precursor glass powders were detected by a simultaneous thermal analyzer (STA, STA449C, NETZSCH, Germany). A heating rate of 10 °C min⁻¹ and air atmosphere were adopted. The surface tension and was measured by a surface tension measuring instrument (Dataphysics OCA25-HTV1800, Germany). The viscosity curve of tellurite glass was tested by a high temperature viscometer (BCT1700, Shanghai Huanao Technology Co., LTD). Using a Metricon 2010/M prism coupler, the refractive indexes of tellurite glass were measured. The dielectric constant of samples is measured by a precision impedance analyzer (6500B/4294A WAYNE KERR/Agilent). Thermal diffusivities of the PGC were measured by a laser flash apparatus (LFA 467, Netzsch, Germany).

Fluent simulation model description

The geometry of the model is shown in Supplementary Fig. 10a. The quartz glass agitation rod has a diameter of 5 mm. The composition of liquid tellurite glass is 75TeO₂−15ZnO−10Na₂O, which has a density of 5020 kg m⁻³ and a viscosity of 0.08693 kg ms⁻¹. The YAG:Ce particles with an average particle size of 10.8 μm and density of 4700 kg m⁻³ are treated as inert-particles. The 10 wt% particles can be injected above the top of the crucible for 1 s. We utilized the shear stress transport k-omega turbulence model and the discrete phase model in ANSYS Fluent to simulate the flow characteristics of the fluid and the motion state of the particles. This model enabled transient simulation and incorporated gravity to investigate the intricate interactions between molten tellurite and YAG:Ce particles.

YAG:Ce particles self-stabilization model

The self-stabilization of YAG:Ce particles in tellurite glass melt is contributed to the synergistic effect of attractive van der Waals forces between YAG:Ce particles, thermal energy, and a high interfacial energy barrier due to a good wettability between YAG:Ce particles and tellurite glass melt. The interfacial energy barrier is much higher than the van der Waals attraction and thermal energy, so it can prevent the atomic-size contact and sintering of YAG:Ce particles, breaking the limits of agglomerations in tellurite glass melt, as shown in Fig. 2a, b.

van der Waals attraction

The van der Waals interaction for two YAG:Ce particles in tellurite glass melt at 923 K can be approximately calculated by the following equation:^41,42,43

$${W}_{{{{{{\rm{vdW}}}}}}}(D)=-\frac{A({a}^{2}+{RD})}{12{D}^{2}}$$

(1)

$$A=\frac{3}{4}{{{{{{\rm{k}}}}}}}_{{{{{{\rm{B}}}}}}}T{\left(\frac{{\varepsilon }_{{{{{{\rm{G}}}}}}}-{\varepsilon }_{{{{{{\rm{Y}}}}}}}}{{\varepsilon }_{{{{{{\rm{G}}}}}}}+{\varepsilon }_{{{{{{\rm{Y}}}}}}}}\right)}^{2}+\frac{3{{{{{\rm{h}}}}}}{v}_{{{{{{\rm{e}}}}}}}}{16\sqrt{2}}\frac{{({n}_{{{{{{\rm{G}}}}}}}^{2}-{n}_{{{{{{\rm{Y}}}}}}}^{2})}^{2}}{({n}_{{{{{{\rm{G}}}}}}}^{2}+{n}_{{{{{{\rm{Y}}}}}}}^{2})\sqrt{{n}_{{{{{{\rm{G}}}}}}}^{2}+{n}_{{{{{{\rm{Y}}}}}}}^{2}}}$$

(2)

where D is the distance between two particles in nanometers. A is the Hamaker constants for the van der Waals interaction. a is the radius of the particle contact surface (a is negligible relative to the micron size R of the YAG:Ce particles). R is the radii of YAG:Ce particles. k_B is the Boltzmann constant; T is the ambient temperature; ${\varepsilon }_{{{{{{\rm{G}}}}}}}$ and ${\varepsilon }_{{{{{{\rm{Y}}}}}}}$ are the relative permittivity of tellurite glass and YAG:Ce, respectively. h is Planck constant. v_e is the main electron absorption frequency in ultraviolet light. n_G and n_Y are the refractive indices of tellurite glass and YAG:Ce, respectively. According to the parameters in Supplementary Table 1, it can be calculated that A is approximately equal to 2.15 zJ. Therefore, the van der Waals interaction between two similar YAG:Ce particles in tellurite glass melt can be further derived as follows:

$${W}_{{{{{{\rm{vdW}}}}}}}(D)=-\frac{2.15R}{12D}$$

(3)

Equation (3) is valid only if the contact distance D between two YAG:Ce particles in tellurite glass melt is about more than two atomic layers (about 0.4 nm)^44,45. Thus, when D = 0.4 nm, the maximum attraction W_{vdW (min)} between two YAG:Ce particles in tellurite glass melt is calculated to be −2.42 × 10³ zJ. The van der Waals potential energy easily induces YAG:Ce particles to aggregate when the other repulsive force cannot be generated.

Thermal energy for particle dispersion

The thermal energy of YAG:Ce particles for Brownian motion, E_b, can be estimated by⁴⁴

$${E}_{{{{{{\rm{b}}}}}}}={{{{{{\rm{k}}}}}}}_{{{{{{\rm{B}}}}}}}T$$

(4)

where T is the absolute temperature. At a synthesis temperature of 923 K, the E_b value of 12.74 zJ is less than the maximum van der Waals attraction in tellurite glass-YAG system, but it also contributes to the dispersion of YAG:Ce particles when the distance D between two particles is relatively far.

Interfacial energy barrier preventing particle contacting and sintering

In the tellurite glass-YAG:Ce system, when the two YAG:Ce particles are close to each other at a distance of about 0.2 nm, the last atomic layer will be extruded, and the particle contact may induce sintered particles. The tellurite glass-YAG:Ce interface will be replaced by a YAG:Ce surface. Therefore, we can calculate the interface energy barrier to estimate the possibility of two particles being sintered. The interfacial energy barrier will be calculated by:

$${W}_{{{{{{\rm{barrier}}}}}}}=S\left({\sigma }_{{{{{{\rm{Y}}}}}}}-{\sigma }_{{{{{{\rm{Y}}}}}}-{{{{{\rm{G}}}}}}}\right)$$

(5)

According to Young’s equation, W_barrier will be calculated by:

$${W}_{{{{{{\rm{barrier}}}}}}}=S{\sigma }_{{{{{{\rm{G}}}}}}}\cos \theta$$

(6)

where S is the effective area, σ_Y is the surface energy of YAG:Ce, σ_Y–G is the interfacial energy between YAG:Ce and tellurite glass melt, σ_G is the surface energy of tellurite melt, and θ is the contact angle of tellurite glass melt on YAG:Ce surface. The equation clearly shows that the better the wettability (the smaller the θ) between the particles and the molten glass in this synthesis method, the higher the interfacial energy barrier that prevents the particles from contacting each other.

The surface energy of tellurite glass melt is 0.141 J m⁻² (Supplementary Table 1). As shown in Fig. 2a, at 923 K, the contact angle between the tellurite glass and YAG:Ce is 43.5°. According to the Lambert approximation, ideally the effective interaction area between the two spheres is S = 2πRD₀ (where D₀ = 0.2 nm)⁴⁵. For two YAG:Ce particles with a radius of 5.4 μm, the interface barrier is calculated to be 6.94 × 10⁵ zJ, which is more than 280 times the van der Waals potential energy that causes the particles to cluster. Therefore, it is almost impossible for YAG:Ce particles to overcome the interfacial energy barrier to contact each other for sintering. Thus, YAG:Ce particles can still exist stably after being dispersed in tellurite glass melt.

Reporting summary

Further information on research design is available in the Nature Portfolio Reporting Summary linked to this article.

Data availability

The data that support the findings of this study are available from the corresponding author upon request. Source data are provided with this paper.

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Acknowledgements

This research was supported by National Natural Science Foundations of China (grant no. 51972118), and the Local Innovative and Research Teams Project of Guangdong Pearl River Talents Program (2017BT01X137).

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State Key Laboratory of Luminescent Materials and Devices, Guangdong Provincial Key Laboratory of Fiber Laser Materials and Applied Techniques, Guangdong Engineering Technology Research and Development Centre of Special Optical Fiber Materials and Devices, School of Physics and Optoelectronics, South China University of Technology, Guangzhou, 510641, China
Yongsheng Sun, Yuzhen Wang & Zhiguo ** Dong

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Yongsheng Sun
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Yuzhen Wang
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Weibin Chen
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Qingquan Jiang
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Dongdan Chen
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Guo** Dong
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Zhiguo **a
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X.Z.G. conceived the initial concept. Y.S.S. prepared the sample and processed the experimental data. X.Z.G., Y.S.S., Y. Z. W., W. B. C., Q. Q. J., D. D. C and G. P. D. interpreted the theoretical and experimental results. Y.S.S. wrote the paper, X.Z.G supervised the work and revised the paper. All authors discussed and edited the paper.

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Correspondence to Zhiguo **a.

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Nature Communications thanks Mathieu Allix, Tomokatsu Hayakawa and the other, anonymous, reviewer(s) for their contribution to the peer review of this work. A peer review file is available.

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Sun, Y., Wang, Y., Chen, W. et al. Rapid synthesis of phosphor-glass composites in seconds based on particle self-stabilization. Nat Commun 15, 1033 (2024). https://doi.org/10.1038/s41467-024-45293-0

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Received: 18 September 2023
Accepted: 19 January 2024
Published: 03 February 2024
DOI: https://doi.org/10.1038/s41467-024-45293-0
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Rapid synthesis of phosphor-glass composites in seconds based on particle self-stabilization

Abstract

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Introduction

Verification of particle self-stabilization model

Performance characterizations of YAG:Ce-PGC

Methods

Raw materials

Precursor glass, YAG:Ce-PGC, and YAG:Ce-PiS fabrications

Characterizations

Fluent simulation model description

YAG:Ce particles self-stabilization model

van der Waals attraction

Thermal energy for particle dispersion

Interfacial energy barrier preventing particle contacting and sintering

Reporting summary

Data availability

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Acknowledgements

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