High E ﬃ cient YVPO 4 Luminescent Materials Activated by Europium

: YPO 4 :Eu, YVO 4 :Eu, and YVPO 4 :Eu based phosphors with various Eu(III) activator contents and phosphate-vanadate ratios were synthesized by the self-propagating high-temperature synthesis method. The samples were characterized by scanning electron microscopy, nitrogen sorption, acid-base indicators and photoluminescence. The particle surface features with a ﬁnely dispersed structure comprising all the involved elements. The pore structure and the speciﬁc surface areas of the samples were di ﬀ erent depending on the compositions of the samples. The most ﬁnely dispersed sample was YVO 4 :Eu samples. The speciﬁc surface areas of the YPO 4 :Eu samples were 10 to 15 times greater than those of vanadate samples. The phosphors samples had a slightly basic (YVO 4 :Eu, YVPO 4 :Eu) or slightly acidic (YPO 4 :Eu) properties of the surface with di ﬀ erent contents of Lewis and Brönsted sites. The di ﬀ erences in the compositions and acid-base state resulted in the di ﬀ erence in the intensity and brightness of the photoluminescence (PL) of the samples. The yttrium-phosphate-vanadate phosphors of the mixed YV x P 1 − x O 4 -Eu had higher brightness and PL intensity than those samples with similar phosphate as well as vanadate phosphors.


Introduction
The development of novel synthetic approaches to oxide phosphors with high luminescence efficiency is one of the most important steps towards various high-tech devices, such as plasma panels, auto-electron emission displays, light sources, thermoluminescent dosimeters, etc. The application in such devices needs specific functional properties of the relating luminescent materials, particularly involving a high quantum yield of luminescence and presence of certain absorption and emission bands. There are many compounds doped with rare-earth ions, the most attractive ones are the oxides of these ions [1][2][3]. Most of them have high thermal stability and chemical activity. Particularly, phosphors based on rare-earth activated yttrium phosphates and vanadates are some of the most promising compounds of this type [4][5][6][7][8][9][10][11].
These compounds are promising as red-light sources in displays, various light sources providing "warmer" white color for medical applications. These phosphors are obtained by different approaches [4][5][6][7][8][9][10][11] involving hydrolysis in colloids, flow synthesis, solvothermal synthesis, sol-gel techniques, Pechini process, precipitation, hydrothermal synthesis, and microwave heating. The efficiency of the phosphors is determined by the host composition, crystallinity, concentration of structural defects, compositions of the components, distribution uniformity of dopant ion, degree of Y replacement by Eu, specific properties of V and P, as well as the formation of active centers. Therefore, the study of relationships between the synthesis methods/conditions of the materials, compositions, mechanisms of active centers formation, surface features, and luminescence characteristics is an important issue for the development of an approach to adjust their performances and search for optimal preparation conditions. The aim of this study was to synthesize the phosphors activated by europium, yttrium phosphate and their combinations, and to investigate the relationship between morphology, acid-base properties, and luminescent characteristics of these materials.
The structure of the synthesized samples was confirmed by XRD analysis performed using a Diffray diffractometer. XRD data shown in Figure 1 indicate that the prepared samples correspond to yttrium vanadate structure. The addition of phosphorous results in XRD peak shifting to larger angles due to the formation of YPO4-YVO4 solid solution.  10 (2) and 20 mol% (3) and pattern for the card № 16-250* ICDD PDF database (4). The enlarged peak near 25° is shown in the caption to illustrate the effect of phosphorous content.  10 (2) and 20 mol% (3) and pattern for the card № 16-250* ICDD PDF database (4). The enlarged peak near 25 • is shown in the caption to illustrate the effect of phosphorous content.

Characterization
Porous structure and specific surface area of the prepared phosphors were characterized by BET and BJH methods via low-temperature nitrogen adsorption-desorption using an automated gas adsorption analyzer Micromeritics TriStar II 3020, USA. Degassing of samples was conducted at 200 • C for 2 h [13].
The morphology and particle size of the sample were examined by Scanning Electron Microscopy (Hitachi TM3000, Hitachi, Ltd., Tokyo, Japan) at an accelerating voltage of 15 kV and under the conditions of a charge-off mode from the sample (electron gun: 5 × 10 −2 Pa). The nature of the element's distribution on the surface of the samples and the quantitative elemental analysis was carried out on the device for the energy dispersive microanalysis (Quantax 70).
Acid-base properties of the samples were characterized by measuring changes of pH values in bi-distilled water upon suspending a 20 mg sample of the studied material as described in [13][14][15].
The surface functionality of the phosphors was studied by the adsorption of acid-base indicators with various intrinsic pKa values selectively adsorbing on surface centers with the corresponding pKa with spectrophotometric measurement of the corresponding changes in optical density [14][15][16] using an SF-56 spectrophotometer (LOMO, St. Petersburg, Russia). Photoluminescent (PL) performances of the synthesized phosphors were characterized using an SM-2203 spectrofluorimeter (SOLAR, Belarus). The recorded luminescence spectra were analyzed to determine the number and positions of maximum in the excitation and luminescence spectra, intensity and FWHM level corresponding to 50% photoluminescence intensity relating to the maximum intensity. Photoluminescent (PL) performances of the synthesized phosphors were characterized using an SM-2203 spectrofluorimeter (SOLAR, Belarus). The recorded luminescence spectra were analyzed to determine the number and positions of maximums (max) in the excitation and luminescence spectra, intensity (I) and FWHM level corresponding to 50% photoluminescence intensity relating to the maximum intensity. The excitation spectra were recorded upon the adjustment of the excitation monochromator Ex to a certain wavelength range and fixing the emission monochromator Em at the selected wavelength. The luminescence spectra were recorded upon fixing Ex at the target excitation wavelength and Em was used for scanning over the emission wavelength range [8,17].
The exciting light of the radiation source (high-pressure xenon arc lamp DKsSh 150-1M, (Zelenograd, Moscow, Russia) fell on the sample perpendicular to its surface, and luminescence was recorded at an angle of 450, which reduced the contribution of reflected light from the radiation source. We used a holder for solid samples with a gap of 2.2, a step of 1 nm, and a medium velocity. The excitation spectra of samples activated by europium ions have maxima in the range of 320-336 nm.
The luminescence brightness of the phosphors was measured using an IL1700 research radiometer (International Light Technologies, Inc., Peabody, MA, USA) at optimal wavelengths for both materials (286 nm for YVO 4 based phosphors and 365 nm for YPO 4 based ones). Investigated the phosphor is filled in the cell. When the UV lamp is off, the radiometer readings are set to zero. After that, the lamp turns on, the cuvette with the phosphor is placed in the box, the shutter closes, and the readings of the radiometer are read [18].

Pore Structure
The data of low-temperature nitrogen adsorption/ for the sample YPO 4 :Eu(8) shown in Figure 2 feature with a prominent hysteresis that suggests a capillary condensation in the pores. Processing of these data using BET equation at P/P 0 = 0.05-0.35 gives the specific surface 83 m 2 /g, whereas treatment according to Thomson-Kelvin equation indicates that this sample is mesoporous with the pore sizes ranging from 4 to 6 nm and the average pore volume V pore about 0.13 cm 3 /g. The porous structure and adsorptive properties of the studied phosphors are summarized in Table 1. YPO4:Eu (5% and 8%) samples are also mesoporous with pore sizes 4-10 nm. On the contrary, the phosphors based on yttrium vanadate and mixed vanadate-phosphate are nonporous (contain only a small number of large mesopores), as indicated by adsorption isotherms and small the specific surface values.  The porous structure and adsorptive properties of the studied phosphors are summarized in Table 1. YPO 4 :Eu (5% and 8%) samples are also mesoporous with pore sizes 4-10 nm. On the contrary, the phosphors based on yttrium vanadate and mixed vanadate-phosphate are nonporous (contain only a small number of large mesopores), as indicated by adsorption isotherms and small the specific surface values.

Acid-Basic Properties of the Samples
The dispersity, chemical compositions, and the imperfection of the crystal structure affect the state of the surface, which is reflected in the acid-base and luminescence properties of the crystal phosphors. The change of pH value for the aqueous medium after immersing the samples until the equilibrated isoionic state (iis) are presented in Figure 4. The pHiis results indicate a weak acidity on YPO4-based samples and weak basicity on the YVO 4− and YV0.9P0.1O4-based samples. The presence of europium slightly modified the surface to basicity.
The initial period straight after the suspending of the sample's features with the most significant pH changes, followed by a trend to saturation. pH drops sharply to a minimum for YPO4-based samples a predominantly occupation of their surface with Lewis acidic centers (probably corresponding to phosphorous atoms) featuring with a rapid interaction with water. The subsequent slight increase of pH indicates the participation of Brӧnsted acidic hydroxyl. For YVO4 The elemental analysis based on the element distribution profiles and energy spectra for YVO 4 :Eu (8) phosphor sample is shown in Figure 3. It clearly shows uniform distributions of all elements on the surface. All samples show the same uniform elemental distribution.
The contents of various elements on the phosphor surface are tabulated in Table 2 for the samples with Eu content 8 mol%. The results of other samples featured with similar ratios.

Acid-Basic Properties of the Samples
The dispersity, chemical compositions, and the imperfection of the crystal structure affect the state of the surface, which is reflected in the acid-base and luminescence properties of the crystal phosphors. The change of pH value for the aqueous medium after immersing the samples until the equilibrated isoionic state (iis) are presented in Figure 4. The pH iis results indicate a weak acidity on YPO 4 -based samples and weak basicity on the YVO 4− and YV 0.9 P 0.1 O 4 -based samples. The presence of europium slightly modified the surface to basicity. and YV0.9P0.1O4-based phosphors, a steady pH growth was observed in the initial phase that suggests the presence of both Lewis and Brӧnsted basic centers.  Figure 5 shows the change in the total surface acidity of yttrium phosphate, yttrium vanadate, and mixed samples. The smooth increase in the surface acidity from YVO4 to YPO4 is in accordance with the chemical properties of these compounds. It can be seen in Table 3 that activation by europium ions changed the pHiis parameter. The dependence is not unique, however, the regularity in the change in total acidity persists for the samples with the same percentage of europium (5 or 8) was observed. Phosphor plays a crucial role in these samples.  The study of the prepared materials by the adsorption of acid-base indicators ( Figure 6) indicates that the surface of Eu-free YVO4 features with a relatively low content of adsorption centers, whereas the addition of europium results in a drastic increase in the content of different sites, particularly with pKa −4.4 (7% Eu), −0.9 and 1.3 (5% Eu), 2.5 and 5 (5-10% Eu), 7…9 (5% Eu) and 14.2 (5, 10 and 8 % Eu). The initial period straight after the suspending of the sample's features with the most significant pH changes, followed by a trend to saturation. pH drops sharply to a minimum for YPO 4 -based samples a predominantly occupation of their surface with Lewis acidic centers (probably corresponding to phosphorous atoms) featuring with a rapid interaction with water. The subsequent slight increase of pH indicates the participation of Brönsted acidic hydroxyl. For YVO 4 and YV 0.9 P 0.1 O 4 -based phosphors, a steady pH growth was observed in the initial phase that suggests the presence of both Lewis and Brönsted basic centers. Figure 5 shows the change in the total surface acidity of yttrium phosphate, yttrium vanadate, and mixed samples. The smooth increase in the surface acidity from YVO 4 to YPO 4 is in accordance with the chemical properties of these compounds. It can be seen in Table 3 that activation by europium ions changed the pHiis parameter. The dependence is not unique, however, the regularity in the change in total acidity persists for the samples with the same percentage of europium (5 or 8) was observed. Phosphor plays a crucial role in these samples.   Figure 5 shows the change in the total surface acidity of yttrium phosphate, yttrium vanadate, and mixed samples. The smooth increase in the surface acidity from YVO4 to YPO4 is in accordance with the chemical properties of these compounds. It can be seen in Table 3 that activation by europium ions changed the pHiis parameter. The dependence is not unique, however, the regularity in the change in total acidity persists for the samples with the same percentage of europium (5 or 8) was observed. Phosphor plays a crucial role in these samples.  The study of the prepared materials by the adsorption of acid-base indicators ( Figure 6) indicates that the surface of Eu-free YVO4 features with a relatively low content of adsorption centers, whereas the addition of europium results in a drastic increase in the content of different sites, particularly with pKa −4.4 (7% Eu), −0.9 and 1.3 (5% Eu), 2.5 and 5 (5-10% Eu), 7…9 (5% Eu) and 14.2 (5, 10 and 8 % Eu).  The study of the prepared materials by the adsorption of acid-base indicators ( Figure 6) indicates that the surface of Eu-free YVO 4 features with a relatively low content of adsorption centers, whereas the addition of europium results in a drastic increase in the content of different sites, particularly with pK a −4.4 (7% Eu), −0.9 and 1.3 (5% Eu), 2.5 and 5 (5-10% Eu), 7 . . . 9 (5% Eu) and 14.2 (5, 10 and 8% Eu).  Generally, the surface acidity of the considered samples increased in the order: YVO4:Eu < YVPO4(Р10):Eu < YVPO4(Р20):Eu < YРO4:Eu, that is in agreement with indicator adsorption data (Figures 8,9). Furthermore, comparative data for the distributions of adsorption centers (Figure 8, 9) indicate that the contents of Lewis acidic centers (LAC) with pKa 14.2 increased in the order of YVO4:Eu < YV0.9P0.1O4:Eu < YPO4:Eu, confirming the results of acidities from pH-metric data. According to the earlier studies [14,15], such centers relating to oxygen vacancies or surface cations deteriorate the luminescence performances due to their ability to electron trapping, however, their transition into Brӧnsted sites (particularly hydroxyls with pKa 2.5) leads to the increase in luminescence characteristic. Instead, an increase in the concentration of Lewis base sites in the opposite row leads to an increase in the photoluminescence intensity. Europium concentration clearly correlates with the content of adsorption centers with pK a 5.0 ( Figure 7) probably corresponding to weakly acidic hydroxyl groups formed due to the distortion of element-oxygen bonds in the surface layer.  Generally, the surface acidity of the considered samples increased in the order: YVO4:Eu < YVPO4(Р10):Eu < YVPO4(Р20):Eu < YРO4:Eu, that is in agreement with indicator adsorption data (Figures 8,9). Furthermore, comparative data for the distributions of adsorption centers (Figure 8, 9) indicate that the contents of Lewis acidic centers (LAC) with pKa 14.2 increased in the order of YVO4:Eu < YV0.9P0.1O4:Eu < YPO4:Eu, confirming the results of acidities from pH-metric data. According to the earlier studies [14,15], such centers relating to oxygen vacancies or surface cations deteriorate the luminescence performances due to their ability to electron trapping, however, their transition into Brӧnsted sites (particularly hydroxyls with pKa 2.5) leads to the increase in luminescence characteristic. Instead, an increase in the concentration of Lewis base sites in the opposite row leads to an increase in the photoluminescence intensity. Generally, the surface acidity of the considered samples increased in the order: YVO 4 :Eu < YVPO 4 (P10):Eu < YVPO 4 (P20):Eu < YPO 4 :Eu, that is in agreement with indicator adsorption data (Figures 8 and 9).  The considered differences in acid-base properties of the studied samples surface can be attributed to relatively high acidity and low size of phosphorous atoms promoting their localization on the surface, whereas V ions are keener towards hydroxylation.

Excitation and Luminescence
The excitation and luminescence spectra of the phosphors samples and their luminescence brightness as a function of europium content are shown in Figures 10 and 11. The luminescence performances of the phosphors materials are summarized in Table 4.  The considered differences in acid-base properties of the studied samples surface can be attributed to relatively high acidity and low size of phosphorous atoms promoting their localization on the surface, whereas V ions are keener towards hydroxylation.

Excitation and Luminescence
The excitation and luminescence spectra of the phosphors samples and their luminescence brightness as a function of europium content are shown in Figures 10 and 11. The luminescence performances of the phosphors materials are summarized in Table 4. Furthermore, comparative data for the distributions of adsorption centers (Figures 8 and 9) indicate that the contents of Lewis acidic centers (LAC) with pK a 14.2 increased in the order of YVO 4 :Eu < YV 0.9 P 0.1 O 4 :Eu < YPO 4 :Eu, confirming the results of acidities from pH-metric data. According to the earlier studies [14,15], such centers relating to oxygen vacancies or surface cations deteriorate the luminescence performances due to their ability to electron trapping, however, their transition into Brönsted sites (particularly hydroxyls with pK a 2.5) leads to the increase in luminescence characteristic. Instead, an increase in the concentration of Lewis base sites in the opposite row leads to an increase in the photoluminescence intensity.
The considered differences in acid-base properties of the studied samples surface can be attributed to relatively high acidity and low size of phosphorous atoms promoting their localization on the surface, whereas V ions are keener towards hydroxylation.

Excitation and Luminescence
The excitation and luminescence spectra of the phosphors samples and their luminescence brightness as a function of europium content are shown in Figures 10 and 11. The luminescence performances of the phosphors materials are summarized in Table 4.   The excitation spectra of all Eu(III) activated samples are similar to each other featuring with an intensive short wavelength band λmax = 327 nm commonly accounted for charge transfer transitions from O 2− to Eu 3+ (O 2 p → Eu 4 f). In addition, a set of low intensity narrow bands were observed in the region 350-500 nm relating to Eu ion intra configuration 4f-4f-transitions 7 F 0 -5 D4, 7 F 0 -5 G2, 7 F 0 -5 L6, 7 F 0 -5 D3, 7 F 0 -5 D2 with respective peaks at 362, 382, 396, 412 and 466 nm. The intensity of the short-wave bands with maxima at 327 nm is significantly higher than the intensity of the most pronounced band in the excitation spectrum of the Eu 3+ with a maximum at 396 nm for the samples YV0.9P0.1O4:Eu(8) and YVO4:Eu(10) (Figure 8a,b and Table 4). The intensity of the short-wave band is weaker than those in the previous samples for the YPO4:Eu(10) excitation spectra. The intensity of the bands due to the transitions of Eu 3+ ion was high.
The PL spectra of the studied Eu(III) activated phosphors are almost the same featuring with bands corresponding to transitions from 5 D0 metastable level to the basic multiplet level 7 Fj of Eu 3+ ion with wavelength maxima at 600, 620. 623, 702, and 708 nm. The intensities of the bands depend on the europium content, but this is ambiguous. In the case of YVPO4 P10 phosphor, the intensity decreased with an increase in europium content, and an inverse relationship was observed for the remaining phosphors. The most intensive band with the maximum at 623 nm relates to 5 D0 → 7 F2 transition. The highest luminescence intensity was observed for YV0.9P0.1O4:Eu(8) and YVO4:Eu (10) samples, about 60 times exceeding the value for YPO4:Eu(10) ( Table 4).  The excitation spectra of all Eu(III) activated samples are similar to each other featuring with an intensive short wavelength band λ max = 327 nm commonly accounted for charge transfer transitions from O 2− to Eu 3+ (O 2 p → Eu 4 f). In addition, a set of low intensity narrow bands were observed in the region 350-500 nm relating to Eu ion intra configuration 4f-4f-transitions 7 F 0 -5 D 4 , 7 F 0 -5 G 2 , 7 F 0 -5 L 6 , 7 F 0 -5 D 3 , 7 F 0 -5 D 2 with respective peaks at 362, 382, 396, 412 and 466 nm. The intensity of the short-wave bands with maxima at 327 nm is significantly higher than the intensity of the most pronounced band in the excitation spectrum of the Eu 3+ with a maximum at 396 nm for the samples YV 0.9 P 0.1 O 4 :Eu(8) and YVO 4 :Eu(10) (Figure 10a,b and Table 4). The intensity of the short-wave band is weaker than those in the previous samples for the YPO 4 :Eu(10) excitation spectra. The intensity of the bands due to the transitions of Eu 3+ ion was high.
For YV 0.9 P 0.1 O 4 :Eu(8) and YVO 4 :Eu(10) samples, the intensity of bands at 327 nm was significantly higher that of 394 nm (Table 4). In the vanadium-free YPO 4 :Eu(10) phosphor sample, the intensity of short wave band at 322 nm was very low (I 327 /I 396 = 0,7), indicating unfavorable conditions for O 2− → Eu 3+ charge transfer in this sample.
The PL spectra of the studied Eu(III) activated phosphors are almost the same featuring with bands corresponding to transitions from 5 D 0 metastable level to the basic multiplet level 7 Fj of Eu 3+ ion with wavelength maxima at 600, 620. 623, 702, and 708 nm. The intensities of the bands depend on the europium content, but this is ambiguous. In the case of YVPO 4 P10 phosphor, the intensity decreased with an increase in europium content, and an inverse relationship was observed for the remaining phosphors. The most intensive band with the maximum at 623 nm relates to 5 D 0 → 7 F 2 transition. The highest luminescence intensity was observed for YV 0.9 P 0.1 O 4 :Eu(8) and YVO 4 :Eu (10) samples, about 60 times exceeding the value for YPO 4 :Eu(10) ( Table 4).
In the spectra of these phosphors, the absence of a short-wave band with the maximum at 462 nm relating to the host material luminescence is probably due to the absorbed energy transfer from the host matrix to Eu ions. In conclusion, the host material composition is one of the significant factors affecting the PL intensity of Eu(III) ions.
The comparison characteristic of peaks intensities in luminescent spectra for YV 0.9 P 0.1 O 4 :Eu(8), YVO 4 Eu(8), and YPO 4 Eru(8) phosphors, obtained at the excitation wavelength of 305 nm (λ ex ) is shown in Figure 12, while the gap was 1-1. Thus, one of the factor, that influence on the PL intensity of Eu(III) ions under the same research conditions is probably the matrix composition.
Crystals 2019, 9, x FOR PEER REVIEW 11 of 14 In the spectra of these phosphors, the absence of a short-wave band with the maximum at 462 nm relating to the host material luminescence is probably due to the absorbed energy transfer from the host matrix to Eu ions. In conclusion, the host material composition is one of the significant factors affecting the PL intensity of Eu(III) ions. The comparison characteristic of peaks intensities in luminescent spectra for YV0.9P0.1O4:Eu(8), YVO4Eu (8), and YPO4Eгu (8) phosphors, obtained at the excitation wavelength of 305 nm (λex) is shown in Figure 12, while the gap was 1-1. Thus, one of the factor, that influence on the PL intensity of Eu(III) ions under the same research conditions is probably the matrix composition.
As shown in Figure 13, the luminescence brightness of almost all the studied phosphors passes through the maximum at Eu content 7 mol% (x = 0.07). At this optimal Eu content, the highest brightness is observed for the mixed vanadate-phosphate sample with phosphorous content 10 mol%. and for the sample with 20 mol % P the brightness is almost the same as for the pure YVO4 based phosphor.  As shown in Figure 13, the luminescence brightness of almost all the studied phosphors passes through the maximum at Eu content 7 mol% (x = 0.07). At this optimal Eu content, the highest brightness is observed for the mixed vanadate-phosphate sample with phosphorous content 10 mol%. and for the sample with 20 mol % P the brightness is almost the same as for the pure YVO 4 based phosphor.
Crystals 2019, 9, x FOR PEER REVIEW 11 of 14 In the spectra of these phosphors, the absence of a short-wave band with the maximum at 462 nm relating to the host material luminescence is probably due to the absorbed energy transfer from the host matrix to Eu ions. In conclusion, the host material composition is one of the significant factors affecting the PL intensity of Eu(III) ions. The comparison characteristic of peaks intensities in luminescent spectra for YV0.9P0.1O4:Eu(8), YVO4Eu (8), and YPO4Eгu (8) phosphors, obtained at the excitation wavelength of 305 nm (λex) is shown in Figure 12, while the gap was 1-1. Thus, one of the factor, that influence on the PL intensity of Eu(III) ions under the same research conditions is probably the matrix composition.
As shown in Figure 13, the luminescence brightness of almost all the studied phosphors passes through the maximum at Eu content 7 mol% (x = 0.07). At this optimal Eu content, the highest brightness is observed for the mixed vanadate-phosphate sample with phosphorous content 10 mol%. and for the sample with 20 mol % P the brightness is almost the same as for the pure YVO4 based phosphor.  The comparison of these data with the phosphor surface functionality ( Figure 6) shows that the sample with Eu content 7 mol% providing the highest luminescence brightness features with the highest content of Lewis basic centers with pK a −4.4 in couple with a reduced content of Brönsted basic sites with pKa 7 . . . 13 and absence of Lewis acidic centers with pK a 14.2 (i.e. "electron traps" preventing from luminescent electron transitions). The considered functionality likely reflects the structural perfection of the surface predominantly occupied with V=O or P=O groups (and, consequently, oxygen atoms) intrinsic to vanadate structure.
In this study, much attention was paid to the investigation of the phosphors surface properties without a detailed consideration of the effect of the matrix structure on the corresponding luminescent transitions. In the previous studies [19][20][21], we have shown that acid-base active sites, dispersity, and porosity reflect the imperfection of the solids surface structure and affect the luminescent properties of materials sensitive to the surface state. This study shows that the phosphors based on YVO 4 had more intense PL and increased brightness compared with the samples based on YPO 4 .
In addition, they are distinguished by a more basic surface state (pH iis > 7), a small value of the specific surface area, and low porosity. Phosphate phosphors have an acidic surface, a large value of the specific surface area, narrow mesoporous size distribution, and predominance of Lewis acid sites on the surface, in comparison with vanadate samples on the surface of which the Lewis base sites predominate. Phosphors based on yttrium phosphates are less photoluminescent active than the phosphors based on yttrium vanadate.
The results of this study infer that the increased brightness of YVO 4 based phosphors relating to YPO 4 based samples correlates with a decrease concentration of Lewis acidic centers, probably corresponding to the surface P or V atoms featuring with electron-accepting (or "electron trapping") properties preventing from luminescent electron transitions. Phosphorous atoms possess higher acidity and tendency to localization on the surface than the vanadium due to lower size, while V is capable to coordinate more oxygen atoms blocking such undesirable Lewis acid sites and either forming bridging bonds between ions to stabilize the surface compounds facilitating the luminescence increase or yielding Brönsted sites (hydroxyl groups) present on the surface of vanadate samples in a significantly higher amount. Furthermore, a high concentration of Lewis acid sites on the surface of yttrium phosphate-based samples can be responsible for their tendency to agglomeration due to strong interparticle interactions, that also contributes to reduced PL brightness correlating with the overall surface activated by UV radiation to stimulate luminescence.
In summary, the synthesis of mixed yttrium vanadate-phosphate phosphors provides an increase in PL brightness compared with both individual components due to their interphase interactions yielding new surface compounds. This approach is promising for the further optimization of the compositions of the phosphors to improve their performance [20][21][22].

Conclusions
A series of YPO 4 :Eu, YVO 4 :Eu and YVPO 4 :Eu phosphors with different contents of Eu(III) activator and with different phosphorus-vanadium ratios for the mixed phosphors were synthesized by SHS technique. The host material composition in Eu(III)-activated YVO 4 , YPO 4 and mixed YV 1−x P x O 4 based phosphors significantly affected their luminescence performances due to the differences in matrix structure as well as the surface acid-base properties and functional composition. YPO 4 based phosphors provided much lower photoluminescence intensity and brightness than the YVO 4 analogs, due to finely mesoporous nature, higher specific surface area, stronger acidity and more reactive surface by a large content of Lewis acidic sites featuring with "electron trapping" properties hampering luminescent electron transitions and facilitating particle agglomeration. Although the luminescence brightness of a pure YPO 4 based phosphor is much lower compared to YVO 4 based analog, a partial (10%) replacement of vanadium by phosphorous provides a considerable brightness increase compared with a pure vanadate-based material. Furthermore, this effect is promising in respect of cost reduction for the considered phosphors. The optimal europium content 7 mol% providing the highest luminescence brightness for both vanadate-and mixed vanadate-phosphate phosphors is determined and found to correlate with the lowest content of "electron trapping" centers, prevailing of oxygen centers corresponding to V=O groups and reflecting the most perfect surface structure.