Introduction

Modern life is significantly influenced by light and light-based technologies, which has altered the quality of life. Rare-earth-activated nanocrystals are a significant class of solid state lightings (SSLs) that have attracted the attention of materials scientists. In comparison to conventional solid-state lighting sources like halogen tungsten lamp, incandescent light, fluorescent lamp, and so on, white light-emitting diodes (w-LEDs), in particular the phosphor converted w-LEDs, have a longer working lifetime, higher energy efficiency, better eco-friendliness, and faster response time. There are currently two methods that are quite popular for making w-LEDs. The first method involves coating a blue LED with a single-phased yellow emitting phosphor or coating a near ultra-violet (NUV) LED with a single-phased white emitting phosphor. However, due to shortcomings in the red spectral area, such w-LEDs are still unable to fulfill the best demand in the illumination sector, resulting in high color correlated temperature (CCT) and a less color rendering index (CRI). The second method involves coating a NUV LED with three distinct red-blue-green phosphors. Now a days, single phased emanating nanophosphor is chosen over RGB-based systems in certain circumstances due to the second method's high cost and complicated fabrication approach [1,2,3,4,5,6,7,8].

Dy3+ is one of the most alluring rare earth ions, and because of its exceptional optical, electrical, and magnetic properties, it is frequently employed in optoelectronic functional materials. Excellent dopant candidates include dysprosium trivalent (Dy3+) ions with a 4f9 electronic configuration, which under UV irradiation efficiently emit yellow in a variety of matrixes. Two main emissions from Dy3+ ions can be seen in the blue and yellow zones, corresponding to the 4F9/2 → 6H13/2 and 4F9/2 → 6H15/2 transitions, respectively. The immediate environment of the Dy3+ activated host has very little impact on the magnetic-dipole transition of 4F9/2 → 6H15/2. But the environment in the immediate vicinity can easily influence the electric dipole transition of 4F9/2 → 6H13/2 [9, 10]. As a result, by choosing or adjusting the host framework, it is feasible to fine-tune the white light emission of Dy3+, specifically to alter the emission ratio of yellow to blue photons. Along with activator ions, the choice of host matrix must be taken into account. Aluminates, borate, nitrides, tungstate, and phosphates have all been used as hosts in the fabrication of various Dy3+ activated phosphors. But at this time, phosphate-based host series have several benefits, including inexpensive synthesis costs, good chemical stability, and low sintering temperatures [11]. With the aforementioned benefits of phosphate-based host matrixes in mind, the author chose Sr3Y(PO4)3 (SYPO) as the inorganic host matrix. In earlier reports, Wang et al. investigated the photouminescent properties of Dy3+ doped Sr3Y(PO4)3 [12]. Sr3Y(PO4)3:Dy3+ was investigated by Woo Seo et al. for near-ultraviolet white light-emitting diodes [13]. The luminescent properties of Dy3+ and Eu3+co-doped Sr3Y(PO4)3 were examined by Ren et al. [14]. Wang et al. investigated the photoluminescence and energy-transfer of Tm3+ and Dy3+ co-doped Sr3Y(PO4)3 [15]. The majority of investigations conducted on the current host have employed a long-term, high-temperature solid-state synthetic process. However, we have created Dy3+ activated Sr3Y(PO4)3 nanophosphors using a straightforward, highly efficient and energy-saving solution combustion method that allows for a 1200°C temperature drop and a 3-h sintering period. The activator ions are efficiently dissolved in the host matrix without changing the crystal phase of produced nanosamples. In comparison to other high-temperature methods, solution combustion produces crystalline, better pure, and uniform products with a worthy yield at a lower temperature. This improves the fabricated nanophosphor's emission profile and broadens its application domain in a variety of lighting applications.

Dy3+ activated Sr3Y(PO4)3 nanocrystals were fabricated using the solution combustion fabrication method for first time, which is a self-igniting, environmentally friendly, energy-efficient, simple, and quick process that uses urea as a fuel. Several approaches are used to characterize the generated nanophosphor. The purity of synthesized samples was studied using PXRD (powder X-ray diffraction) analysis. TEM (transmission electron microscopy) was employed to evaluate the surface topography and particle size of the produced nanopowder. EDAX (energy dispersive X-ray analysis) was used to analyze the prepared sample's elemental configuration and nanocrystalline nature. The emission and excitation regions were identified by examining photoluminescent characteristics. Moreover, using the PL (photoluminescence) decay curve as a guide, radiative rates, non-radiative rates and quantum efficiency were determined for the entire series. A strong white emission was detected by photoluminescence spectroscopy, and CIE colour coordinates support this finding. The information provided by all of the reported characterizations is crucial for the effective implementation of white-emitting Dy3+ activated Sr3Y(PO4)3 nanomaterials for lasers, latent fingerprinting, bio-imaging, photovoltaic, and advanced optoelectronic applications.

Synthesis and Characterization

Nanophosphor Fabrication

Sr3Y1-x(PO4)3: xDy3+ (x = 0.01 to 0.15 mol) nanomaterials were produced in a safe and efficient manner using the SC (solution-combustion) method. Beginning components such as Strontium nitrate (Sr(NO3)2), Yttrium (III) nitrate hexahydrate (Y(NO3)3.6H2O), Dysprosium (III) nitrate hydrate (Dy(NO3)3.xH2O), Diammonium hydrogen phosphate ((NH4)2HPO4), and Urea (NH2CONH2) are obtained from Sigma-Aldrich and have a high purity (99.999%). Prior to being heated on a hot plate for roughly 8–10 min, all of these beginning components are first allowed to dissolve in accordance with their stoichiometric ratio in a small quantity of solvent, such as deionized water. At the microscopic level, the generated solution was uniformly dissolved. The combination was specifically preheated to roughly 80°C, which allows the water that was loosely bound to evaporate and the gelled substance to burn evenly. After that, a muffle furnace set to 500°C for 15 min was connected to the glass beaker, causing an auto-limited combustion reaction to occur. Because urea accelerated the breakdown of metallic nitrates, a lot of heat was released along with gases including CO2, N2, and moisture, which eventually turned the solution in the glass into a lot of residue. It was brought down to the room temperature. The material produced exhibits remarkable crystallinity, which can be attributed to the substantial quantity of energy generated during the combustion process. The powder was then crushed and calcined by placing it in a silica crucible and heating it to 1200°C for three hours in a muffle furnace. After that, the manufactured material was allowed to come to room temperature and was once more finely milled into a powder. Following that, the resultant nanocrystalline powder was placed inside a desiccator and went through various characterization procedures [16, 17]. The methodical flow diagram illustrates the synthetic process used to create the aforementioned nanosamples in Fig. 1.

Fig. 1
figure 1

An illustration of the process flow for making Dy3+ activated Sr3Y(PO4)3 nanophosphor

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Characterization

A Rigaku Ultima IV Diffractometer (Japan) having λ = 0.154 nm was used to record PXRD outlines for the phase analysis of the synthesized nanophosphors. The measured diffraction profiles of the produced samples are expressed as 2θ at a scan speed of 2˚ per minute (with an angular range of 10—70˚). The TECNAI G2 FEI TEM technique was utilized to study the morphology and structure of nanocrystals. The presence of various components in nanocrystals was quantitatively evaluated using the Ametek (EDAX) technology. 15 kV and 11 mm were the operating power and distance settings, respectively. The Horiba-Jobin YVON Fluorolog Model FL-3–11 spectrophotometer, which is highly sophisticated and advanced, was utilized to investigate the attributes of photoluminescence, color compounds, and lifetime. The photomultiplier tube (PMT) voltage of 700 V and a slit width of 5 mm were used to trace the excitation and emission spectra. The CIE chromatic coordinate was computed using MATLAB software. Following extensive research, the superior optical performance of the Sr3Y0.93Dy0.07(PO4)3 nanophosphors, which includes their high emission intensity and high quantum efficiency, makes them the preferred material for use in photonic devices, solar cells, WLEDs, bioimaging, sensors, and other applications [18].

Results and Discussion

PXRD Analysis

A diffractometer (Rigaku Ultima-IV) was used to gather the PXRD patterns of the Sr3Y1-x(PO4)3: xDy3+ (x = 0.01 to 0.15 mol) nanopowders within the 10—70˚ scan range. PXRD analysis was utilized to conclude the crystallographic investigations. The powder diffraction pattern (PDF) reference code: 00–44-0320 is found to be exactly identical to the recorded diffraction patterns related to the synthesized series of nanophosphors. The resulting patterns in addition to the host matrix standard patterns, which are shown in Fig. 2, show that doping trivalent dysprosium ions in the Sr3Y(PO4)3 matrix does not change the phase prototype. The claimed standard diffraction pattern of the host and the experimental diffraction patterns for the activated system are identical. Because of their similar oxidation state and ionic radii, the efficient substitution of Y3+ (ionic radii = 1.01 Å) ions by activator ions raises the possibility of successful doping of Dy3+ (ionic radii = 0.91 Å) ions in Sr3Y(PO4)3 host lattice. As a result, Dy3+ ions fit nicely in the Sr3Y(PO4)3 host matrix and effectively substitute Y3+ ions. Still, a shift in peak intensities is noted, and this essentially depends on how the crystalline diffraction plane is oriented. In the event that there is a particular alignment, the intensity of the peak will be strong; in the event that the particles are placed in a disordered or random order, the peak's strength will be low. The radius percentage difference (∆r) could be calculated using the following equation to investigate the substitution mechanism [19, 20].

Fig. 2
figure 2

The collective powder XRD patterns of Dy3+ activated Sr3Y(PO4)3 exhibit perfect symbiosis with the standard host patterns

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$${\Delta }_{r}=\frac{{R}_{m}\left(CN\right) - {R}_{d}(CN)}{{R}_{m}(CN)}\times 100 \%$$
(1)

In Eq. (1), CN stands for the coordination number, although Rd and Rm indicate the radii of the activator and host ions respectively. The ionic radii of cations are: Y3+ (Rm = 1.01 Å), Sr2+ (Rm = 1.13 Å) and doped ion Dy3+ (Rd = 0.91 Å). The determined radius percentage difference (∆r) value for the pair Y3+ and Dy3+ is 9.9% and 19.47% for the pair Sr2+ and Dy3+. The radius percentage difference in case of Y3+ is less as compared to Sr2+. So, Dy3+ ions may occupy the position of the Y3+ ion. Secondly, the cations that are most likely to be replaced by the Dy3+ ion could be Sr2+ and La3+ both. But Dy3+ ions would take up the position of the Y3+ ion since both Y and Dy are in the trivalent oxidation state. Dy3+ will not replace Sr2+ because it results in a chemically non-equivalent replacement and adds an extra positive charge to the host lattice.

The average crystallite size of the nanosamples is evaluated using Scherrer's formula by estimating the crystallite size using full width at half maxima (FWHM) related to many strong XRD peaks. The equation for Debye Scherrer is provided below [21].

$$D=\frac{0.941\lambda }{\beta cos\theta }$$
(2)

In Eq. (2), the X-Ray wavelength (1.541 Å) is reported by λ, the diffraction angle is reported by θ, and the FWHM is implied by β. Using the aforementioned parameters, the generated nanophosphors series (Sr3Y1-x(PO4)3: xDy3+ (x = 0.01 to 0.15 mol)) has an average extent value of D which lies between 35 and 42 nm. Additionally, the following equations are used to compute the strain (ε) and dislocation density (δ) [22, 23].

$$\varepsilon =\frac{\beta cos\theta }{4}$$
(3)
$$\delta =\frac{1}{{D}^{2}}$$
(4)

The outcomes derived from the aforementioned equations are listed in the Table 1.

Table 1 The crystal size, dislocation density, and strain parameters of Sr3Y1-x(PO4)3: xDy3+ (x = 0.01 to 0.15 mol) nanophosphors
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Morphological Analysis

TEM was used to evaluate the grain size and surface morphological characteristics of the synthesized nanosamples. A TEM image of Sr3Y0.93Dy0.07(PO4)3 phosphor that has been calcined at 1200°C is seen in Fig. 3. The TEM image demonstrated the crystalline nature of the manufactured Sr3Y0.93Dy0.07(PO4)3 powder, with particles located in the nanoscale (1–100 nm), reliable with the XRD findings. The grain size calculated through TEM is ~ 38 nm. Figure 4 shows the elemental estimation of the Sr3Y0.93Dy0.07(PO4)3 (optimal sample), which was obtained via the EDAX investigation. The elements strontium (Sr), yttrium (Y), dysprosium (Dy), phosphorus (P), and oxygen (O) are indicated by the EDAX examination. The presence of these components alone confirmed successful doping with Dy3+ ions in the host matrix Sr3Y(PO4)3.

Fig. 3
figure 3

TEM micrograph of Sr3Y0.93Dy0.07(PO4)3 nanophosphor representing the surface morphology of the prepared nanosample

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Fig. 4
figure 4

EDAX study of Sr3Y0.93Dy0.07(PO4)3, an optimal nanophosphor

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Optical Analysis

Photoluminescence (PL) excitation and emission spectra are used to examine the photoluminescence performance of Dy3+ ions in Sr3Y(PO4)3: Dy3+ nanophosphors. The PL-excitation spectrum of the representative sample Sr3Y0.93Dy0.07(PO4)3 over the 300–500 nm spectral range is shown in Fig. 5. A type of powerful excitation peaks have been identified at 327, 352, 366, 389, 431, 457, and 472 nm corresponds to 6H15/2 → 6P3/2, 6H15/2 → 6P7/2, 6H15/2 → 6P5/2, 6H15/2 → 4I13/2, 6H15/2 → 4G11/2, 6H15/2 → 4I15/2 and 6H15/2 → 4F9/2 respectively, which masks the emission areas of blue and UV LED chips that are sold commercially. Consequently, their permissible use in nUV-triggered wLEDs is reflected in their abundant intense absorption in the near UV domain [24]. The excitation spectrum of Dy3+ ions revealed that the distinctive f-f transitions originated from the 6H15/2 ground state. Figure 6 displays the emission spectra of all produced materials, which are identical in shape except their photoluminescence intensity. The emission spectrum is recorded at excitation wavelength 350 nm. Two prominent peaks were seen in the blue and yellow regions of the spectrum at 486 and 577 nm, respectively, which were subjected to the 4F9/2 → 6H15/2 and 4F9/2 → 6H13/2 transitions. Therefore, a mixture of yellow and blue light could produce white light. High symmetry locations in the host lattice containing Dy3+ ions were indicated by the magnetic dipole type of the notable 4F9/2 → 6H15/2 transition [25].

Fig. 5
figure 5

Photoluminescent excitation spectra of Sr3Y0.93Dy0.07(PO4)3 nanophosphor recorded at λem = 570 nm

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Fig. 6
figure 6

Photoluminescent emission spectra of the series of Dy3+ activated Sr3Y(PO4)3 nanophosphors recorded at λex = 350 nm

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Moreover, White-light emission depends on the proper photoluminescence intensity, or Y/B (yellow to blue emission) ratio. The Y/B ratio is a quantitative measure of the asymmetry integral that takes into account the relative emission of the two prominent transitions of the dysprosium doped nanophosphor having stimulated wavelength 350 nm. The ratio of Y to B is calculated using the following formula [1, 26].

$$\frac{Y}{B}= \frac{\int\nolimits_{550}^{600}{I}_{2}\left(\lambda \right)d\lambda }{\int\nolimits_{450}^{500}{I}_{1}\left(\lambda \right)d\lambda }$$
(5)

It is discovered that as the concentration of Dy3+ ions varies, the Y/B ratio remains almost constant. Whereas the transition causing yellow emission at 577 nm (4F9/2 → 6H13/2) is an electric dipole one that depends on the environment of crystal field, the one causing blue emission at 486 nm (4F9/2 → 6H15/2) is a magnetic dipole change. The magnetic-dipole type of the significant 4F9/2 → 6H15/2 transition, however, suggests that dopant ions might be present at high symmetry sites in the lattice.

Energy-Transfer Process

Figure 7 further illustrates the relationship between luminescence intensity and dopant content, showing that the PL emission intensity of manufactured nanophosphors increased as the concentration of Dy3+ ions increased up to 7 mol%, after which it started to decrease. This might be the result of the concentration scavenging phenomena, which happened as a result of non-radiative energy loss and has a variety of potential sources, including exchange communication, radiative reabsorption, and multipolar exchanges. There is a slim probability of radiative reabsorption occurring because there was no gurgling seen in the PL spectra. A critical distance of 4 Å must not be exceeded for energy exchange to occur between activator ions. The critical distance can be determined using Blasse's formulation in the manner shown below to confirm this [27].

$${R}_{c}=2{\left[\frac{3V}{4\pi {x}_{c}N}\right]}^{1/3}$$
(6)

where N is the number of cations living in a single unit cell, V denotes the volume of the unit cell, and x denotes the dopant composition for which the PL intensity is highest. Based on these values, the Rc was determined to be 19 Å, which is far greater than the recognized critical distance required for the exchange mechanism to occur. Multipolar exchanges, which might be dipole–dipole, dipole–quadrupole, or quadrupole–quadrupole in type, may therefore be the most widely recognised process for concentration scavenging. Dexter's formulation can be used to confirm the kind of exchanges that are actually occurring in the particular scenario, as follows [28]:

$$log\left(\frac{I}{x}\right)=log\left(f\right)-\left(\frac{s}{d}\right)logx$$
(7)

where d denotes the nanosample dimension, which in this case is 3, the ratio of emission intensity to activator ion content is represented by the symbol I/x., and s is a constant with values of 6, 8, and 10 for d-d, d-q, and q-q interactions, respectively. A straight line with a slope of -1.3815 ± 0.05 is produced when log(I/x) and log(x) are plotted (as displayed in Fig. 8). This line yields the values of s = 4.1445, demonstrating the presence of multipolar exchanges that are in charge of the concentration quenching. Figure outlining in detail the many types of transitions associated with the excitation and emission phenomena for Dy3+ activated Sr3Y(PO4)3 nanophosphors (as shown in Fig. 9).

Fig. 7
figure 7

Variation of the emission intensity at λex = 350 nm as a function of Dy3+ concentration in nanophosphors

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Fig. 8
figure 8

A linear variation of log(I/x) with log(x) in Dy3+ activated Sr3Y(PO4)3 nanophosphor

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Fig. 9
figure 9

Descriptive energy level diagram displaying various electronic transitions in different energy levels for the Dy3+ activated Sr3Y(PO4)3 nanophosphors

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Lifetime Decay

The decay profile of Sr3Y1-x(PO4)3: xDy.3+ (x = 0.01 to 0.15 mol) nanocrystals is analyzed for the emission transition observed at 570 nm and excitation transition observed at 350 nm in order to further analyze the energy transfer behavior. Figure 10 displays the photoluminescence decay curves, which fit well with a 1st-order exponential decay mode. Mathematically, the 1st-order exponential decay equation is represented as [29]

$$I= {I}_{0}\,{e}^{^{-t}/_{\tau}}$$
(8)

where I and I0 are the photoluminescence intensities at time t and 0, respectively, and τ is the decay time. The first decay curve's exponential character indicates that the dopant ions are uniformly distributed throughout the host matrix. Figure 11 shows how the observed lifetimes in the Sr3Y(PO4)3 host lattice vary with varying Dy3+ doping concentrations. As the concentration of activator ions rises from 0.01 mol to 0.15 mol, Table 2 and Fig. 11 clearly show a linear decrease in the average life expectancies from 1.03119 to 0.69022 ms. This can be explained by the non-radiative energy transmission that occurs between the different energy states of the activator ions. Apart from the fluorescence lifetime values (measured in milliseconds) for the nanophosphor series, the auzel's model provides an explanation for the relationship that reveals the dependency of the obtained lifetime values on the concentration of Dy3+ ions [30].

$${\tau }_{c}=\frac{{\tau }_{R}}{1+\frac{c}{{c}_{0}}{e}^{-\frac{N}{3}}}$$
(9)

where τc is the decay lifespan at a concentration of c, N is the phonon number, and c0 is the concentration constant. Aforementioned calculation is used to fit the experimentally evaluated PL lifespan data, and the resulting figures are displayed in Fig. 11. The fitting curve is signified by the solid black line, while the experimental data is shown by the pink round-shaped points. As can be seen in figure, the fitting curve derived from equation fits the experimental data quite well. During the fitting procedure, the value of N is found to be 8.016 ± 0.21, indicating that the quenching of the 4F9/2 level through non-radiative relaxation results in the generation of about 8 phonons.

Fig. 10
figure 10

Lifetime decay profile for the emission of Dy3+ activated Sr3Y(PO4)3 nanophosphors recorded at λem = 570 nm and λex = 350 nm

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Fig. 11
figure 11

Variation of decay lifetime with the doping concentration of Dy3+ ions using Auzel’s formulation

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Table 2 The Y/B ratio, lifetime decay values, non-radiative relaxation rates and quantum efficiencies of Sr3Y1-x(PO4)3: xDy3+ (x = 0.01 to 0.15 mol) nanophosphors
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Additionally, based on Auzel's model, the intrinsic radiative lifetime (τR) for the 4F9/2 level is determined to be 1.074 ± 0.04 ms. This information is then used to use the following equation to calculate the quantum efficiencies (φ) of the nanophosphor series.

$$\varphi = \frac{{\tau }_{0}}{{\tau }_{R} }= \frac{{A}_{R}}{{A}_{R}+{A}_{nR}}$$
(10)

In this case, the radiative and nonradiative rates of relaxation are represented by AR and AnR, respectively, and the measured average and intrinsic lifespan values (in ms) by τo and τR. Furthermore, by utilizing the τo and τR values in the given expression, the nonradiative relaxation rate AnR (in s−1) can be computed as follows [31].

$${A}_{nR}= \frac{1}{{\tau }_{0}}- \frac{1}{{\tau }_{R}}$$
(11)

As a result, Table 2 presents estimated values for the non-radiative rates and quantum efficiencies for the entire series of Dy3+ activated Sr3Y(PO4)3 nanophosphors. Our nanophosphor sample Sr3Y0.93Dy0.07(PO4)3 has a considerable quantum efficiency of approximately 81% for the optimum mol% doped composition, indicating its efficient use in solid-state lighting (SSL) devices and displays.

Chromaticity Coordinates and CCT

MATLAB software was used to analyze the color of the light produced from the created lighting nanopowders i.e. Sr3Y1-x(PO4)3: xDy3+ (x = 0.01 to 0.15 mol). The result of optimum concentration was certified by displaying the analyzed chromaticity coordinates in the CIE diagram (Fig. 12). The observed color coordinates are listed in Table 3. It was discovered that these values resembled the coordinates of the NTSE (National Television System Committee) and the commercial LEDs, which are (0.310, 0.316) and (0.320, 0.320), respectively.

Fig. 12
figure 12

CIE chromaticity diagram for optimal i.e. Sr3Y0.93Dy0.07(PO4)3 nanophosphors

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Table 3 CIE 1931 color co-ordinates, (uˈ, vˈ) and CCT values for Sr3Y1-x(PO4)3: xDy3+ (x = 0.01 to 0.15 mol) nanophosphors
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Furthermore, in order to investigate the characteristics of the white light emitted, correlated color temperature (CCT) values were computed. These values show the temperature-based nature of the light, indicating its coolness (CCT ≥ 4000 K) and warmth (CCT ≤ 3200 K). Additionally, the CCT values are measured using the Mc-Camy relation as stated below [32].

$${\text{CCT}} = - 437{{\text{n}}}^{3} + 3601{{\text{n}}}^{2} - 6861{\text{n}} + 5514.31$$
(12)

where x and y are the co-ordinates of the provided samples, and xe and ye are the chromaticity epicenter co-ordinates (0.332 and 0.186). In this case, n is the ratio between x-xe and y-ye. The equation given below is also used to investigate a substantial partition of facets such as u' & v' coordinates [33];

$${u}^{\prime}= \frac{4x}{-2x+12y+3}$$
(13)
$${v}^{\prime}= \frac{9y}{-2x+12y+3}$$
(14)

As a result, the computed values of CCT are listed in Table 3 along with the u' and v' coordinates. For the Sr3Y1-x(PO4)3: xDy3+ (x = 0.01 to 0.15 mol) nanosample, the accumulated CCT values are observed to be more than 4000 K, confirming the fruitful use of the synthesized nanophosphors via solution-combustion methodology as an excellent source for the emission of cool white light in single-phased lights.

Conclusion

This work describes the effective creation of a series Sr3Y1-x(PO4)3: xDy3+ (x = 0.01 to 0.15 mol) nanophosphors using urea assisted combustion, a non-hazardous and environmentally friendly method, following sintering at 1200°C. A single phase with nearly no impurities was revealed by XRD examination of these nanophosphors. The nano-sized grains were revealed by TEM micrograph of the optimal nanopowder (Sr3Y0.93Dy0.07(PO4)3) phosphor. An examination of the morphology revealed the irregularly clumped particles, measuring between 35 and 42 nm. SAED analysis is used to determine the polycrystalline nature, while EDAX study is used to confirm the elemental composition. White light was manifested by as-synthesized nanopowders, which displayed a blue (486 nm) and yellow (577 nm) band lead by 350 nm illumination. 7 mol% is found to be the ideal composition of trivalent dysprosium ions. There were multipolar exchanges that controlled the ability of phosphor powders to quench light. The single decay function conduct was represented by the decay curves, which also yielded the following results (for Sr3Y0.93Dy0.07(PO4)3): decay time of 0.86423 ms, quantum efficiency of 81%, and non-radiative rate of 226 s−1. The CIE 1931 coordinates of white light (x = 0.305, y = 0.321), along with the CCT value i.e. 6902 K, suggest that Sr3Y0.93Dy0.07(PO4)3 is a superfine material that emits cool white light and is ideal for portable electronics, NUV-activated WLEDs, signage, aircraft cabins, digital communication, sensors, horticulture, advanced lasers, and solar cells.