Eu-Doped Pyrochlore Crystal Nano-Powders as Fluorescent Solid for Fingerprint Visualization and for Anti-Counterfeiting Applications

Undoped Y2Sn2O7 and Eu3+ doped Y2Sn2O7 samples with doping concentrations 7%, 8%, 9%, and 10% are successfully synthesized by the co-precipitation method. A complete structural, morphological, and spectroscopic characterization is carried out. XRD measurements reveal that samples crystallize in the pure single pyrochlore phase and Eu3+ ions occupy sites with D3d symmetry. After mechanical grinding, the average crystallite size is less than 100 nm for all compositions. Optical characterization shows emission from the 5D0 level towards the lower lying 7F0,1,2,3,4 levels. The CIE color coordinates of all the pyrochlore phosphors are very close to those of the ideal red light. For the visualization of latent fingerprints, different surfaces are tested, including difficult ones (wood and ceramic), with excellent results. All three levels of fingerprint ridge patterns are visualized: core (Level 1), bifurcation and termination (Level 2), and sweat pores (Level 3). Moreover, our nano-powders are used to prepare a stable fluorescent ink.


Introduction
Fingerprints are valuable information in forensic science because they provide unique and immutable features for human identification [1]. However, at crime scenes fingerprints are not apparent to the naked eye. For this reason, they are called latent fingerprints (LFPs) and need to be made sufficiently visible with specific techniques [2] like single-metal deposition methods [3], fuming, and powder-dusting techniques [4][5][6]. The details that form the ridge pattern are called loops, arches, and whorls and are organized in different levels. While it is easy to detect the first and the second level ridge details, the third level is quite difficult to be identified, especially on some difficult surfaces like wood and ceramic, and this makes the pattern recognition more difficult and time consuming [7][8][9][10]. Moreover, traditional methods for developing fingerprints have some drawbacks, especially low detection efficiency and high toxicity and very few of them permit the visualization of the third level, i.e., sweat pores.
Among the various methods, power dusting is one of the most used thanks to its extreme simplicity and effectiveness [11]. In this case, the use of fluorescent nanoparticles greatly increases the types of surfaces from which a LFP can be detected and the level of details that can be identified. For this reason, the quest for new materials that can enable the efficient visualization of LFPs is still lively. For example, quantum dots have been proposed as fluorescent powders [12]. They show a good contrast, high selectivity, and sensitivity, but they have relatively high toxicity levels. Organic nanophosphors have some advantages in detecting the LFPs, like long luminescence lifetime, narrow emission, and large Stokes shifts [13]; however, they develop weak prints under ultraviolet light or laser light. Rare earth upconversion fluorescent nanomaterials show bright visible emission under infrared pumping and low toxicity values, but the upconversion efficiency is usually low.
Down-converting rare earth doped nanoparticles overcome this limitation. Among the Lanthanide family Europium (Eu 3+ ), Terbium (Tb 3+ ), Erbium (Er 3+ ), Dysprosium (Dy 3+ ), Ytterbium (Yb 3+ ), and Praseodymium (Pr 3+ ) ions have been identified as the most effective down-converting materials that convert ultraviolet light to visible emission and have been proposed for fingerprint visualization. Moreover, pyrochlore nanoparticles, having the chemical compositions of A 2 B 2 O 7 [14] doped with lanthanide ions, are one of the most promising powder materials to enhance the development of the LFPs due to their high fluorescence capability, chemical stability, and ease of production in nanometric size [15,16]. These crystal nano-powders are expected to work particularly well on raw surfaces such as household woodwork and multi-colored non-porous items where traditional methods are not so efficient. Among the rare earth ions, Europium in Y 2 Sn 2 O 7 can generate intense red emission under UV excitation [17][18][19] and has already been proposed as an excellent phosphor for while light LED emission [20], display devices [21], and radioluminescence detection [22]. In this work we analyzed the possibility of using Eu-doped pyrochlores for fingerprint detection as well as for the production of luminescent inks.

Synthesis of Phosphor Samples
Undoped Y 2 Sn 2 O 7 and Eu 3+ doped Y 2 Sn 2 O 7 samples with doping concentrations of 7%, 8%, 9%, and 10% were successfully synthesized by co-precipitation method [17] using Yttrium oxide (99.99%), Europium (III) oxide (99.99%), Tin (II) chloride dihydrate (99.99%), ethylene glycol, and chloridric acid purchased from Merck KGaA (Darmstadt, Germany). Stoichiometric amounts of SnCl 2 .2H 2 O, Eu 2 O 3 , and Y 2 O 3 were dissolved in 1 M HCl solution and stirred for 2 h. Then, 40 mL of ethylene glycol was added and the solution was slowly heated up to 100 • C. Afterwards, 2 g of urea was added and the solution was stirred 2 h at 150 • C. After being cooled to room temperature, the precipitate was collected by centrifugation at 2500 rpm for 15 min, washed two times with acetone, and dried at room temperature. The samples thus prepared were finally calcined at 900 and 1300 • C in air at a heating rate of 10 • C per minute for 5 h. The undoped Y 2 Sn 2 O 7 nanoparticles were synthesized by similar method taking only the yttrium and tin precursor.

Ball Milling
As-grown samples were ground using FRITSCH (Idar-Oberstein, Germany) Planetary Ball Milling. Samples were put in a zirconium jar with zirconium balls. Samples were ground at 500 rpm speed for 60 min including 5 min for resting.

Characterization
The phase structure of the samples was analyzed using a Panalytical Pro X'Pert MPD (40 kV, 30 mA) diffractometer (Malvern Panalytical, Malvern, United Kingdom) with a Cu Kα (λ = 1.5406 and 1.5444 Å) radiation at room temperature in the range of 10 • -70 • with a step size of 2θ = 0.02. The crystallographic phases were identified by comparison with the X-ray patterns of the JCPDS database. The crystallographic parameters were refined using the Rietveld-fit program FullProf [23]. The average crystallite size was calculated from the diffraction line width, based on Scherrer's equation: where D is the crystallite size for the (hkl) plane, λ indicates the wavelength of the incident X-rays, and β is the corrected full width at half maximum in radians. Angle θ is the diffraction angle for the (hkl) plane. The error on calculated XRD crystallite size is 0.4 nm.
The hydrodynamic diameter of the powder was measured with the Dynamic Light Scattering technique (DLS) with a Zetasizer Nano series (Malvern Panalytical, Malvern, United Kingdom). Just before the measurement, the powder was dispersed into deionized water and sonicated to separate aggregates of nanoparticles. The sizing was produced in a glass cuvette with round aperture at room temperature. The average particle size was calculated from the autocorrelation function of the intensity of scattered light from the nanoparticles by Malvern Zetasizer nano software.
The morphology of the samples was observed by high resolution field emission scanning electron microscopy performed with a FEI (Hillsboro, Oregon, USA) Quanta 450 FEG system operating in low vacuum.
Photoluminescence (PL) spectra were measured at room temperature under diode laser pumping at 450 nm as an excitation source. Detection was accomplished using a compact spectrometer (AvaSpec-ULS2048L-SPU2, Avantes, Apeldoorn, The Netherlands) equipped with a 600 line/mm holographic grating and a 10 µm slit working in the 390-900 nm range with a resolution of 0.4 nm. All the spectra were corrected for the spectral response of the system using a halogen lamp as blackbody source.

Structure of the Prepared Samples
The powder XRD patterns at room temperature of the undoped and doped Y 2 Sn 2 O 7 samples are depicted in Figure 1a.

D = Kλ βcosƟ
where D is the crystallite size for the (hkl) plane, λ indicates the wavelength of the incident X-rays, and β is the corrected full width at half maximum in radians. Angle θ is the diffraction angle for the (hkl) plane. The error on calculated XRD crystallite size is 0.4 nm.
The hydrodynamic diameter of the powder was measured with the Dynamic Light Scattering technique (DLS) with a Zetasizer Nano series (Malvern Panalytical, Malvern, United Kingdom). Just before the measurement, the powder was dispersed into deionized water and sonicated to separate aggregates of nanoparticles. The sizing was produced in a glass cuvette with round aperture at room temperature. The average particle size was calculated from the autocorrelation function of the intensity of scattered light from the nanoparticles by Malvern Zetasizer nano software.
The morphology of the samples was observed by high resolution field emission scanning electron microscopy performed with a FEI (Hillsboro, Oregon, USA) Quanta 450 FEG system operating in low vacuum.
Photoluminescence (PL) spectra were measured at room temperature under diode laser pumping at 450 nm as an excitation source. Detection was accomplished using a compact spectrometer (AvaSpec-ULS2048L-SPU2, Avantes, Apeldoorn, The Netherlands) equipped with a 600 line/mm holographic grating and a 10 μm slit working in the 390-900 nm range with a resolution of 0.4 nm. All the spectra were corrected for the spectral response of the system using a halogen lamp as blackbody source.

Structure of the Prepared Samples
The powder XRD patterns at room temperature of the undoped and doped Y2Sn2O7 samples are depicted in Figure 1a.  Y 2 Sn 2 O 7 compounds can crystalize in the three different types of crystalline structures, pyrochlore, defect-fluorite, and monoclinic, that can be easily differentiated by XRD analysis [24]. In our case, diffraction peaks are in accordance with the Joint Committee on Powder Diffraction Standards (JCPDS) card No. 01-088-0508, as depicted in Figure 1a. According to these results, Y 2 Sn 2 O 7 crystallized in pure single pyrochlore phase, and the crystal structure belongs to the cubic crystal system with the Fd-3m space group [21,[24][25][26][27]. Moreover, no additional peaks of unreacted SnCl 2 ·2H 2 O, Eu 2 O 3 , and Y 2 O 3 were observed in the XRD-data, indicating that the reaction among the raw materials was complete. The incorporation of Eu 3+ ions did not modify the XRD-pattern and this, together with the good fitting results, demonstrates that doping with Eu 3+ does not affect the crystalline structure of the phosphor (Figure 1b). This is not unexpected because the ionic radius of the Eu 3+ ions (r = 0.95 Å) is similar to that of Y 3+ ions (r = 0.92 Å); therefore, Eu 3+ ions can be effectively incorporated into the Y 2 Sn 2 O 7 host lattice, replacing Y 3+ ions without distorting the crystal structure.
The cell parameters and the atomic coordinates obtained from a least-square fitting procedure are shown in Table 1. Figure 1c shows an example of the result of the fitting procedure. Table 1. Atomic coordinates and site occupancy fraction for Y 2 Sn 2 O 7 :9%Eu.

Atom
Site The occupancy probability of Y and Eu atoms present in Site A and the Sn atoms present in Site B was refined in such a way that the total occupancy of each site was equal to 1.0000.  [27]. The two bond-valence with both atoms present in Site B is reported in Table 1.
From the Scherrer equation, we calculated the average crystallite size before mechanical grinding. Results are depicted in Table 2 and compared with the average crystallite size obtained with the DLS technique. The average crystallite size of the samples before grinding was found to be in between 311 and 384 nm with XRD and between 387 and 503 nm with DLS. In all cases, the DLS size is slightly larger than that measured with XRD. This is expected since DLS measures the hydrodynamic diameter that can be slightly larger than the physical dimension of the particle and that can be affected by possible aggregation of the particles.

SEM Characterization
SEM analysis was performed on the samples after grinding. A representative SEM image of the ground Y 2 Sn 2 O 7 :10%Eu sample is shown in Figure 2 together with the corresponding histogram. The formation of very small particles with diameters below 100 nm can be clearly seen. We performed a statistical analysis on the visible particles. Table 3 shows the average mean diameter and standard deviation obtained from the image analysis of the SEM images of the various compositions after grinding. In all cases, the analysis was performed on more than 100 particles and the average diameter obtained was below 100 nm.

SEM Characterization
SEM analysis was performed on the samples after grinding. A representative SEM image of the ground Y2Sn2O7:10%Eu sample is shown in Figure 2 together with the corresponding histogram. The formation of very small particles with diameters below 100 nm can be clearly seen. We performed a statistical analysis on the visible particles. Table 3 shows the average mean diameter and standard deviation obtained from the image analysis of the SEM images of the various compositions after grinding. In all cases, the analysis was performed on more than 100 particles and the average diameter obtained was below 100 nm.    Figure 3 presents the typical room temperature photoluminescence (PL) spectra of Y 2 Sn 2 O 7 :x%Eu (x = 7, 8, 9, 10) nanophosphors together with the transition assignment. The measured emission spectra are in good agreement with the literature [17,19,21,28,29]. The Eu 3+ emission comes from several transitions.    Figure 3 presents the typical room temperature photoluminescence (PL) spectra of Y2Sn2O7:x%Eu (x = 7, 8, 9, 10) nanophosphors together with the transition assignment. The measured emission spectra are in good agreement with the literature [17,19,21,28,29]. The Eu 3+ emission comes from several transitions.

Optical Characterization
All emission channels start from the 5 D0 level towards the lower lying 7 F0,1,2,3,4 levels. Starting from high energy the first transition is the 5 D0 → 7 F0. Since both levels involved are non-degenerate, it can only give rise to one emission line, but transitions from J = 0 to J = 0 are strictly forbidden in the standard Judd-Ofelt theory. Nevertheless, the occurrence of this transition is a well-known example of the breakdown of the selection rules of the Judd-Ofelt theory due to J-mixing or to mixing of low-lying charge-transfer states into the wavefunctions of the 4f 6 configuration [30], and it is usually weak in intensity. In our case it is only visible at the highest-doping level, namely 10%Eu with the appearance of a weak peak at 579 nm. The 5 D0 → 7 F1 can show up to three emission lines because the multiplicity of the 7 F1 level is three, but the D3d point symmetry of the Eu site in pyrochlore structure can only split this level into two components, one of which is doubly degenerate. In fact, we only observed two emission lines at 589.3 nm and 597.5 nm. Moreover, this transition is magnetic dipole in nature, and this means that it is particularly insensible to changes of the environment. For this reason, the intensity of this transition is often considered to be constant and can be used to calibrate the intensity of Eu 3+ luminescence spectra. We used this line as a probe for the luminescence behavior as a function of the doping level. The  Figure 3; the trend is linear a quenching or other nonlinear energy transfer processes are v ing level. The 5 D0 → 7 F2 transition is a so-called "hypersensit that its intensity is strongly influenced by the local symmetry of the ligands and this is also the reason why emission lines transitions. In our case, the 10%Eu doped sample shows a ve transition, while it is much weaker at lower doping levels. I broad bands centered at 612.7 nm and 629.6 nm, one of whic in D3d symmetry the 7 F2 multiplet is split into three energy l rise to up to five lines in D3d symmetry, but this is forbidden theory; therefore, it usually produces a very weak emission, tends from 640 nm to 660 nm and appears as a broad ban Finally, the 5 D0 → 7 F4 transition extends from 690 nm to 720 10%Eu doped sample while it is extremely weak at lower do transition. This is not unexpected, because, although not for tive, this transition is strongly influenced by the symmetry a the Eu 3+ ions [30] Color coordinates of the phosphors were calculated usi tionale de l'Eclairage (CIE) 1931 color chromaticity diagram diagram of Y2Sn2O7:x%Eu (x = 7, 8, 9, 10) nanophosphors. Th the pyrochlore phosphors lie in the range (0.64 ± 0.02, 0.36 ± that of the ideal red light (0.67, 0.33) [31,32]. 7 F 0 . Since both levels involved are non-degenerate, it can only give rise to one emission line, but transitions from J = 0 to J = 0 are strictly forbidden in the standard Judd-Ofelt theory. Nevertheless, the occurrence of this transition is a well-known example of the breakdown of the selection rules of the Judd-Ofelt theory due to J-mixing or to mixing of low-lying charge-transfer states into the wavefunctions of the 4f 6 configuration [30], and it is usually weak in intensity. In our case it is only visible at the highest-doping level, namely 10%Eu with the appearance of a weak peak at 579 nm. The 5 D 0 result is shown in the inset of Figure 3; the trend is linear and no hints of concentration quenching or other nonlinear energy transfer processes are visible up to the 10% Eu doping level. The 5 D0 → 7 F2 transition is a so-called "hypersensitive transition", which means that its intensity is strongly influenced by the local symmetry of the Eu 3+ ion and the nature of the ligands and this is also the reason why emission lines are broader that in the other transitions. In our case, the 10%Eu doped sample shows a very intense emission from this transition, while it is much weaker at lower doping levels. It is composed by two intense broad bands centered at 612.7 nm and 629.6 nm, one of which is probably a doublet since in D3d symmetry the 7 F2 multiplet is split into three energy levels. The 5 D0 → 7 F3 can give rise to up to five lines in D3d symmetry, but this is forbidden according to the Judd-Ofelt theory; therefore, it usually produces a very weak emission, as in our case. This band extends from 640 nm to 660 nm and appears as a broad band with some small features. Finally, the 5 D0 → 7 F4 transition extends from 690 nm to 720 nm and is evident only in the 10%Eu doped sample while it is extremely weak at lower doping levels, like the 5 D0 → 7 F4 transition. This is not unexpected, because, although not formally considered hypersensitive, this transition is strongly influenced by the symmetry and chemical environment of the Eu 3+ ions [30] Color coordinates of the phosphors were calculated using The Commission Internationale de l'Eclairage (CIE) 1931 color chromaticity diagram. Figure 4 represents the CIE diagram of Y2Sn2O7:x%Eu (x = 7, 8, 9, 10) nanophosphors. The CIE color coordinates of all the pyrochlore phosphors lie in the range (0.64 ± 0.02, 0.36 ± 0.02), which is very close to that of the ideal red light (0.67, 0.33) [31,32]. 7 F 1 can show up to three emission lines because the multiplicity of the 7 F 1 level is three, but the D 3d point symmetry of the Eu site in pyrochlore structure can only split this level into two components, one of which is doubly degenerate. In fact, we only observed two emission lines at 589.3 nm and 597.5 nm. Moreover, this transition is magnetic dipole in nature, and this means that it is particularly insensible to changes of the environment. For this reason, the intensity of this transition is often considered to be constant and can be used to calibrate the intensity of Eu 3+ luminescence spectra. We used this line as a probe for the luminescence behavior as a function of the doping level. The result is shown in the inset of Figure 3 result is shown in the inset of Figure 3; the trend is linear and no hints of concentration quenching or other nonlinear energy transfer processes are visible up to the 10% Eu doping level. The 5 D0 → 7 F2 transition is a so-called "hypersensitive transition", which means that its intensity is strongly influenced by the local symmetry of the Eu 3+ ion and the nature of the ligands and this is also the reason why emission lines are broader that in the other transitions. In our case, the 10%Eu doped sample shows a very intense emission from this transition, while it is much weaker at lower doping levels. It is composed by two intense broad bands centered at 612.7 nm and 629.6 nm, one of which is probably a doublet since in D3d symmetry the 7 F2 multiplet is split into three energy levels. The 5 D0 → 7 F3 can give rise to up to five lines in D3d symmetry, but this is forbidden according to the Judd-Ofelt theory; therefore, it usually produces a very weak emission, as in our case. This band extends from 640 nm to 660 nm and appears as a broad band with some small features. Finally, the 5 D0 → 7 F4 transition extends from 690 nm to 720 nm and is evident only in the 10%Eu doped sample while it is extremely weak at lower doping levels, like the 5 D0 → 7 F4 transition. This is not unexpected, because, although not formally considered hypersensitive, this transition is strongly influenced by the symmetry and chemical environment of the Eu 3+ ions [30] Color coordinates of the phosphors were calculated using The Commission Internationale de l'Eclairage (CIE) 1931 color chromaticity diagram. Figure 4 represents the CIE diagram of Y2Sn2O7:x%Eu (x = 7, 8, 9, 10) nanophosphors. The CIE color coordinates of all 7 F 2 transition is a so-called "hypersensitive transition", which means that its intensity is strongly influenced by the local symmetry of the Eu 3+ ion and the nature of the ligands and this is also the reason why emission lines are broader that in the other transitions. In our case, the 10%Eu doped sample shows a very intense emission from this transition, while it is much weaker at lower doping levels. It is composed by two intense broad bands centered at 612.7 nm and 629.6 nm, one of which is probably a doublet since in D 3d symmetry the 7 F 2 multiplet is split into three energy levels. The 5 D 0 Materials 2022, 15, x FOR PEER REVIEW result is shown in the inset of Figure 3; the t quenching or other nonlinear energy transfer ing level. The 5 D0 → 7 F2 transition is a so-calle that its intensity is strongly influenced by the of the ligands and this is also the reason why transitions. In our case, the 10%Eu doped sam transition, while it is much weaker at lower d broad bands centered at 612.7 nm and 629.6 n in D3d symmetry the 7 F2 multiplet is split into rise to up to five lines in D3d symmetry, but t theory; therefore, it usually produces a very tends from 640 nm to 660 nm and appears Finally, the 5 D0 → 7 F4 transition extends from 10%Eu doped sample while it is extremely w 7 F 3 can give rise to up to five lines in D 3d symmetry, but this is forbidden according to the Judd-Ofelt theory; therefore, it usually produces a very weak emission, as in our case. This band extends from 640 nm to 660 nm and appears as a broad band with some small features. Finally, the 5 D 0 2, 15, x FOR PEER REVIEW 7 of 12 result is shown in the inset of Figure 3; the trend is linear and no hints of concentration quenching or other nonlinear energy transfer processes are visible up to the 10% Eu doping level. The 5 D0 → 7 F2 transition is a so-called "hypersensitive transition", which means that its intensity is strongly influenced by the local symmetry of the Eu 3+ ion and the nature of the ligands and this is also the reason why emission lines are broader that in the other transitions. In our case, the 10%Eu doped sample shows a very intense emission from this transition, while it is much weaker at lower doping levels. It is composed by two intense broad bands centered at 612.7 nm and 629.6 nm, one of which is probably a doublet since in D3d symmetry the 7 F2 multiplet is split into three energy levels. The 5 D0 → 7 F3 can give rise to up to five lines in D3d symmetry, but this is forbidden according to the Judd-Ofelt 7 F 4 transition extends from 690 nm to 720 nm and is evident only in the 10%Eu doped sample while it is extremely weak at lower doping levels, like the 5 D 0 Materials 2022, 15, x FOR PEER REVIEW result is shown in the inset of Figure 3; the quenching or other nonlinear energy transf ing level. The 5 D0 → 7 F2 transition is a so-ca that its intensity is strongly influenced by th of the ligands and this is also the reason wh transitions. In our case, the 10%Eu doped sa transition, while it is much weaker at lowe broad bands centered at 612.7 nm and 629.6 in D3d symmetry the 7 F2 multiplet is split in 7 F 4 transition. This is not unexpected, because, although not formally considered hypersensitive, this transition is strongly influenced by the symmetry and chemical environment of the Eu 3+ ions [30].
in D3d symmetry the 7 F2 multiplet is split into three energy levels. The 5 D0 → 7 F3 can give rise to up to five lines in D3d symmetry, but this is forbidden according to the Judd-Ofelt theory; therefore, it usually produces a very weak emission, as in our case. This band extends from 640 nm to 660 nm and appears as a broad band with some small features. Finally, the 5 D0 → 7 F4 transition extends from 690 nm to 720 nm and is evident only in the 10%Eu doped sample while it is extremely weak at lower doping levels, like the 5 D0 → 7 F4 transition. This is not unexpected, because, although not formally considered hypersensitive, this transition is strongly influenced by the symmetry and chemical environment of the Eu 3+ ions [30] Color coordinates of the phosphors were calculated using The Commission Internationale de l'Eclairage (CIE) 1931 color chromaticity diagram. Figure 4 represents the CIE diagram of Y2Sn2O7:x%Eu (x = 7, 8,9,10) nanophosphors. The CIE color coordinates of all the pyrochlore phosphors lie in the range (0.64 ± 0.02, 0.36 ± 0.02), which is very close to that of the ideal red light (0.67, 0.33) [31,32].

Visualization of Latent Fingerprints
In order to test our nanophosphors as LFP development agents, we selected different kinds of surfaces, including porous and non-porous, such as a compact disk, aluminum foil, wood, and ceramic, as shown in Figure 5. After washing and cleaning the donor hands, the fingerprint donor pressed their finger on the different surfaces. Afterwards, the Eu 3+ doped Y 2 Sn 2 O 7 nano-powders were stained smoothly over the full area of the LFPs using a feature brush. Then, the excess powder was removed by brushing. Figure 5 shows the fingerprint images developed under a UV lamp at 256 nm, onto a CD, aluminum foil, wood, a banknote, and a credit card. A clear visualization of LFPs was observed on all surfaces; in fact, thanks to the small size of the nanophosphors, the fingerprint ridges are very clear. The finer details of the fingerprints such as the pores were successfully developed, especially on wood and ceramic surfaces, thanks to the shiny red color emitted by these nano-powders. Moreover, Figure 5 also presents a comparison between the fingerprint development on a credit card with luminescent and nonluminescent powder. It can be seen that the nonluminescent powder under ambient light cannot effectively develop the fingerprint pattern on some of the card details, while the whole pattern is clearly visualized under UV illumination.
shows the fingerprint images developed under a UV lamp at 256 nm, onto a CD, aluminum foil, wood, a banknote, and a credit card. A clear visualization of LFPs was observed on all surfaces; in fact, thanks to the small size of the nanophosphors, the fingerprint ridges are very clear. The finer details of the fingerprints such as the pores were successfully developed, especially on wood and ceramic surfaces, thanks to the shiny red color emitted by these nano-powders. Moreover, Figure 5 also presents a comparison between the fingerprint development on a credit card with luminescent and nonluminescent powder. It can be seen that the nonluminescent powder under ambient light cannot effectively develop the fingerprint pattern on some of the card details, while the whole pattern is clearly visualized under UV illumination.    In fact, Level 1 details provide general morphological information such as orientation field, ridge pattern, and fingerprint ridge flow. Level 2 details give information about pattern agreement of the ridges of individual fingerprints. Level 3 details are defined as fingerprint ridge dimensional features, including sweat pores, curvature, and dots [33].
Since the ridges were clearly observed, our new fluorescent samples showed clear patterns with high brightness and contrast to the naked eye on top of the wood, which is considered as a difficult surface. In fact, the red color can be clearly distinguished between brightness of ridges and darkness of furrows.

Application of Luminescent Ink for Detection of Counterfeiting
In recent years, much attention has been devoted to performing fluorescent inks using nanomaterials. However, as far as we know, no serious attempts have been reported to synthesize these transparent and stable Y 2 Sn 2 O 7 : Eu 3+ colloids for use as fluorescent ink, but the synthesis of stable and transparent luminescent NP colloids in an aqueous medium is a challenging task [34][35][36]. We prepared a luminescent aqueous ink for anti-counterfeiting applications.
In our work, we adapted an encapsulation method in order to produce a transparent and stable Y 2 Sn 2 O 7 : Eu 3+ colloidal solution from the nano-powders. Initially, 3 g of poly(vinyl alcohol) PVA was dissolved in de-ionized water followed by agitation at 90 • C for half an hour. Then, we added different amounts (10, 20, and 40 mg) of our nanopowders into the previous solution followed by vigorous stirring at room temperature for around 20 min. Finally, we kept the solution under sonification for about 15 min followed by centrifugation to produce highly transparent (>80% in the visible region) luminescent ink. Under ambient conditions, our ink remained stable for about one week without any precipitation. The ink was transparent under visible light but became pink-red in color under UV irradiation. Figure 6 shows the letter L written with the florescent ink on tissue. Under ambient light the ink is invisible, but it becomes visible under UV irradiation, with increasing visibility at increasing amount of nano-powder dispersed.
Materials 2022, 15, x FOR PEER REVIEW 10 of 12 centrifugation to produce highly transparent (>80% in the visible region) luminescent ink. Under ambient conditions, our ink remained stable for about one week without any precipitation. The ink was transparent under visible light but became pink-red in color under UV irradiation. Figure 6 shows the letter L written with the florescent ink on tissue. Under ambient light the ink is invisible, but it becomes visible under UV irradiation, with increasing visibility at increasing amount of nano-powder dispersed.

Conclusions
In this work, Eu:Y2Sn2O7 nanophosphors were successfully synthesized via the coprecipitation method followed by a further grinding treatment. XRD confirmed the cubic single phase pyrochlore structure of the phosphors. After mechanical grinding, all the samples showed an average dimension of less than 100 nm. Bright red light is emitted by the nanophosphors after UV illumination. This led to an efficient visualization of LFPs on different surfaces like a compact disk, aluminum foil, wood, and ceramic. Moreover, we prepared a stable luminescent ink for anti-counterfeiting applications. We believe these findings can be useful both in forensic science and in anti-counterfeiting applications.

Conclusions
In this work, Eu:Y 2 Sn 2 O 7 nanophosphors were successfully synthesized via the coprecipitation method followed by a further grinding treatment. XRD confirmed the cubic single phase pyrochlore structure of the phosphors. After mechanical grinding, all the samples showed an average dimension of less than 100 nm. Bright red light is emitted by the nanophosphors after UV illumination. This led to an efficient visualization of LFPs on different surfaces like a compact disk, aluminum foil, wood, and ceramic. Moreover, we prepared a stable luminescent ink for anti-counterfeiting applications. We believe these findings can be useful both in forensic science and in anti-counterfeiting applications. Funding: This work was funded by the Tunisian Ministry of Higher Education and Scientific Research MHESR through the project "PBMLT" and the project PAQ Collabora T2-C3 "KIDAEM".
Informed Consent Statement: Informed consent was obtained from all subjects involved in the study.

Data Availability Statement:
The data presented in this study are available on request from the corresponding author.