Effect of Ceramic Formation on the Emission of Eu3+ and Nd3+ Ions in Double Perovskites

Herein, the structure, morphology, as well as optical properties of the powder and ceramic samples of Ba2MgWO6 are presented. Powder samples were obtained by high temperature solid-state reaction, while, for the ceramics, the SPS technique under 50-MPa pressure was applied. The morphology of the investigated samples showed some agglomeration and grains with a submicron size of 490–492 µm. The theoretical density and relative density of ceramics were calculated using the Archimedes method. The influence of sample preparation on the position, shape, and character of the host, as well as dopants emission was investigated. Sample sintering enhances regular emission of WO6 groups causing a blue shift of Ba2MgWO6 emission. Nonetheless, under X-ray excitation, only the green emission of inversion WO6 group was detected. For the ceramic doped with Eu3+ ions, the emission of both host and dopant was detected. However, for the powder efficient host to activator energy, the transfer process occurred, and only the magnetic dipole emission of Eu3+ was detected. The intensity of Nd3+ ions of Ba2MgWO6 powder sample is five times higher than for the ceramic. The sintering process reduces inversion defects and creates a highly symmetrical site of neodymium ions. The emission of Ba2MgWO6:Nd3+ consists of transitions from the 4F3/2 excited level to the 4IJ multiplet states with the dominance of the 4F3/2→4I11/2 one. The spectroscopic quality parameter and branching ratio of Nd3+ emission are presented.

Substitution of a divalent ion (Mg 2+ ) with a third oxidation state lanthanide ion (Eu 3+ and Nd 3+ ) can cause defects in the matrix, which occur to compensate the created charges locally in the host. For this reason, charge compensation was applied through the addition of lithium in an amount of 50%, based on the amount of dopant ions. The samples were pre-sintered at 600 • C/6 h and re-sintered at 1300 • C/6 h two times in air atmosphere in a muffle furnace in an Al 2 O 3 crucible. The products were obtained after cooling the samples to room temperature naturally and subsequently they were ground into fine powder.
The obtained powder was then sintered using the spark plasma sintering (SPS) method (SPS Dr Sinter 825, Syntex, Kawasaki, Japan). First, 1.3 g of powder was introduced in a graphite die with a 10-mm inner diameter. Next, the samples were sintered under vacuum at temperatures of 1350 • C, under uniaxial pressure of 50 MPa. Both the heating rate and the cooling rate were set to 100 • C/min. Figure 1 presents the diagram of the SPS sintering thermomechanical schedule (RT = room temperature). After sintering, the samples were annealed at 1000 • C for 10 h in air for decoloring (reoxidation) and graphite burnout. The last stage of the process was machining and polishing. BaWO4 as an impurity, were first mixed and ground thoroughly in a mortar for 20 min. Substitution of a divalent ion (Mg 2+ ) with a third oxidation state lanthanide ion (Eu 3+ and Nd 3+ ) can cause defects in the matrix, which occur to compensate the created charges locally in the host. For this reason, charge compensation was applied through the addition of lithium in an amount of 50%, based on the amount of dopant ions. The samples were pre-sintered at 600 °C/6 h and re-sintered at 1300 °C/6 h two times in air atmosphere in a muffle furnace in an Al2O3 crucible. The products were obtained after cooling the samples to room temperature naturally and subsequently they were ground into fine powder. The obtained powder was then sintered using the spark plasma sintering (SPS) method (SPS Dr Sinter 825, Syntex, Kawasaki, Japan). First, 1.3 g of powder was introduced in a graphite die with a 10-mm inner diameter. Next, the samples were sintered under vacuum at temperatures of 1350 °C, under uniaxial pressure of 50 MPa. Both the heating rate and the cooling rate were set to 100 °C/min. Figure 1 presents the diagram of the SPS sintering thermomechanical schedule (RT = room temperature). After sintering, the samples were annealed at 1000 °C for 10 h in air for decoloring (reoxidation) and graphite burnout. The last stage of the process was machining and polishing.

Research Techniques
The crystalline phases were identified and indexed by the X-ray diffraction (XRD) analysis (D8 ADVANCE, Bruker, Karlsruhe, Germany) using monochromatic Cu Kɑ1 radiation (λ = 1.54056 Ǻ). The data were collected in a 2θ range from 10° to 90° with a step of 0.026.
The microstructure of the sample was investigated by a scanning electron microscope FEG-SEM (Quanta 450, FEI, Thermo Fisher Scientific, Waltam, MA,,USA).
The apparent density of materials was determined using the Archimedes method in absolute ethanol (density δeth = 0.79 g/cm 3 ), and then the relative density was obtained using a theoretical density of BMW double perovskite δBMW = 7.20 g/cm 3 . The measurement error of this technique is of about ±1% in our case as the sample mass is low. As part of the density measurement by the Archimedes method, the following masses were determined: m1-the mass of dry pellet; m2-the mass of pellet immersed in ethanol; and m3-the mass of pellet impregnated with ethanol. The apparent density, open porosity, and relative density of the samples before and after sintering were calculated using the following Equations (1-3):

Research Techniques
The crystalline phases were identified and indexed by the X-ray diffraction (XRD) analysis (D8 ADVANCE, Bruker, Karlsruhe, Germany) using monochromatic Cu K A1 radiation (λ = 1.54056Ǻ). The data were collected in a 2θ range from 10 • to 90 • with a step of 0.026.
The microstructure of the sample was investigated by a scanning electron microscope FEG-SEM (Quanta 450, FEI, Thermo Fisher Scientific, Waltam, MA, USA).
The apparent density of materials was determined using the Archimedes method in absolute ethanol (density δeth = 0.79 g/cm 3 ), and then the relative density was obtained using a theoretical density of BMW double perovskite δBMW = 7.20 g/cm 3 . The measurement error of this technique is of about ±1% in our case as the sample mass is low. As part of the density measurement by the Archimedes method, the following masses were determined: m1-the mass of dry pellet; m2-the mass of pellet immersed in ethanol; and m3-the mass of pellet impregnated with ethanol. The apparent density, open porosity, and relative density of the samples before and after sintering were calculated using the following Equations (1)-(3): where δ app is the apparent density (i.e., with closed porosity), Π o is the open porosity (in %), and ρ is the relative density (in %).
As an excitation source, a 266-nm line from a Nd:YAG pulse laser and a laser diode operating at 808 nm were used. The emission spectra were recorded using a Hamamatsu PMA-12 detector (Hamamatsu, Japan). An InGaAs detector equipped with VUV McPherson spectrometer (Chelmsford, MA, USA) was used for NIR analysis. Decay profiles were obtained on a Lecroy digital oscilloscope (Chestnut Ridge, NY, USA). A Varian VF-50J/S RTG tube (Salt Lake, UT, USA) was used as an X-ray radiation source. The voltage and amperage for the X-ray source were 40 kV and 0.7 mA, respectively.
To ensure repetition and comparatives of the results, a special setup for measuring the emission in the same condition was applied when it comes to the excitation source and its power, the detector, integration time, geometry, etc. As for the illuminated material, the powder was placed in a flat holder with a quartz window with negligible absorbance, while the ceramic sample was measured without a holder in the same plane as the powder. The spot of the illuminating source was small enough so that the illuminated area of the powder and the ceramic was the same.
Structural and microstructural properties were tested at the University of Limoges, while spectroscopic measurements were made at the Institute of Low Temperature and Structure Research Polish Academy of Sciences.

BMW Powders Characterizations
Initially, structural studies of polycrystalline powders were conducted in order to verify whether the material has the ability to be compacted and thus form ceramic materials. For this purpose, a structure analysis by X-ray diffraction and SEM images were performed. Figure 2 shows X-ray diffraction patterns of polycrystalline powders. It was observed that the diffraction peaks of the samples match well with the ICDD card no. 70-2023 for BMW. Each of the materials has a cubic double perovskite structure, with the space group Fm-3m and the following crystallographic structural parameters: lattice parameter a = 8.1120 A, unit cell volume V = 533.81 A 3 , Z = 4, and theoretical density δth = 7.2. Our current interest is focused mainly on obtaining the pure composition. Transparent ceramics would be obtained only for the pure host, because the secondary phases of the different refractive index will act as light scattering centers. In the case of the tested materials, the XRD results confirm that all polycrystalline powders obtained the structure of a double perovskite, and also the Eu 3+ and Nd 3+ ions were introduced into the crystal lattice with no change of their structure. However, only BMW-Eu has a single phase, while BMW and BMW-Nd have the main crystalline phase of Ba 2 MgWO 6 , accompanied by small amounts of BaWO 4 ( Figure 2). The SEM images of the BMW, BMW-Eu, and BMW-Nd powders are presented in Figure 3. The grains tend to agglomerate, but individual grains also appear. The grains are of relatively large sizes in the range of 490 nm -2 µm; however, the BMW-Nd composition has the smallest size ( Table 1). The analysis of SEM images shows that the solid-  The SEM images of the BMW, BMW-Eu, and BMW-Nd powders are presented in Figure 3. The grains tend to agglomerate, but individual grains also appear. The grains are of relatively large sizes in the range of 490 nm-2 µm; however, the BMW-Nd composition has the smallest size ( Table 1). The analysis of SEM images shows that the solid-state synthesis produces isotropic, slightly agglomerated, and submicrometric double perovskite powders, such as Ba 2 MgWO 6 ; therefore, these materials should exhibit good sinterability.  The SEM images of the BMW, BMW-Eu, and BMW-Nd powders are presented in Figure 3. The grains tend to agglomerate, but individual grains also appear. The grains are of relatively large sizes in the range of 490 nm -2 µm; however, the BMW-Nd composition has the smallest size ( Table 1). The analysis of SEM images shows that the solidstate synthesis produces isotropic, slightly agglomerated, and submicrometric double perovskite powders, such as Ba2MgWO6; therefore, these materials should exhibit good sinterability. In our previous work [6], an analysis of the thermal behavior with the natural sintering method was performed using dilatometry and the TG-DSC analysis in air, which supplements the test results obtained. The measurements were caried out on the BMW host and were described in detail in the previous paper [6], and therefore were not included in this paper. Overall, the dilatometry results show that our BMW powders have excellent compaction ability, which may be related to the low friction and rearrangement forces experienced during compaction. In addition, the sinterability of BMW synthetic powders remains low during natural sintering, which can be explained by the large grain size. The obtained results of TG-DSC indicate that the sintering temperature of this material should In our previous work [6], an analysis of the thermal behavior with the natural sintering method was performed using dilatometry and the TG-DSC analysis in air, which supplements the test results obtained. The measurements were caried out on the BMW host and were described in detail in the previous paper [6], and therefore were not included in this paper. Overall, the dilatometry results show that our BMW powders have excellent compaction ability, which may be related to the low friction and rearrangement forces experienced during compaction. In addition, the sinterability of BMW synthetic powders remains low during natural sintering, which can be explained by the large grain size. The obtained results of TG-DSC indicate that the sintering temperature of this material should not exceed 1400 • C. For this reason, the SPS sintering method has been studied to help lower the densification temperature. In conclusion, Ba 2 MgWO 6 powder with a double perovskite structure can be used to obtain ceramics.

Study of BMW Sintering by SPS
BMW powders were sintered by SPS according to the schedule presented in Figure 1. Figure 4 shows the sintering profiles of double Ba 2 MgWO 6 perovskites. The upper profiles show the shrinkage (∆L, mm) of the material as a function of temperature, which tells us if the material has been compacted and if a ceramic material has been formed. However, the lower profiles show the change in pressure (p, kN) supplied to the system, also depending on the temperature. The sintering profiles are difficult to compare with each other because during the process there was a problem with the applied pressure was too small, which led to poor pressure control. Nevertheless, on the basis of the obtained results, it can be concluded that all samples have very similar compaction behavior. The first shrinkage due to rearrangement of the powder particles is observed at about 600 • C when the starting pressure is applied. The second contraction is observed due to compaction starting in the range of about 1150-1200 • C. In this temperature range, a shrinkage of about 1 mm is observed in all cases. The corresponding relative shrinkage is approximately 26%, calculated on the basis of Equation (4): shrinkage due to rearrangement of the powder particles is observed at about 600 °C when the starting pressure is applied. The second contraction is observed due to compaction starting in the range of about 1150-1200 °C. In this temperature range, a shrinkage of about 1 mm is observed in all cases. The corresponding relative shrinkage is approximately 26%, calculated on the basis of Equation (4): where ∆L(T)[%] is the shrinkage, ∆L(T)[mm] is the thickness variation (ΔL(T) = L(T)-L0), and Lo is the initial thickness equal to around 3.8 mm.

Microstructural Features of BMW Ceramics
Ceramic materials obtained by the SPS method on the basis of BMW, BMW-Eu, and BMW-Nd polycrystalline powders were microstructurally analyzed. For this purpose, XRD, SEM, and density measurement by the Archimedes method were performed. Overall, the obtained results confirm the obtaining of well-dense double perovskite ceramics.

Microstructural Features of BMW Ceramics
Ceramic materials obtained by the SPS method on the basis of BMW, BMW-Eu, and BMW-Nd polycrystalline powders were microstructurally analyzed. For this purpose, XRD, SEM, and density measurement by the Archimedes method were performed. Overall, the obtained results confirm the obtaining of well-dense double perovskite ceramics. Table 1 summarizes the density parameters, determined by the Archimedes method. All samples appear to be almost densified-relative density is more than 84% (δ > 84%). The structure of the double perovskite Ba 2 MgWO 6 of the obtained ceramic materials, sintered at 1350 • C by the SPS method, was also confirmed. It can be observed in Figure 5 that the diffraction peaks of the samples match well with the ICDD card no. 70-2023 for cubic Ba 2 MgWO 6 . The materials are practically single-phase, only in the case of BMW-Eu material, whereby there is an additional phase of BaWO 4 with the ICDD card no. 43-0646 ( Figure 5). By comparing the X-ray diffraction patterns of polycrystalline powders and ceramic materials (Figures 2 and 5), it can be noticed that the sintering process does not change the structure of the obtained materials, but affects their phase nature. In the case of powders, only BMW-Eu is single-phase, while BMW and BMW-Nd also have small amounts of BaWO 4 (Figure 2), while for ceramics, the materials are practically single-phase, except BMW-Eu materials ( Figure 5). One may even be tempted to say that the SPS sintering method helps to obtain materials with higher phase purity (Figures 2 and 5).
ceramic materials (Figures 2 and 5), it can be noticed that the sintering change the structure of the obtained materials, but affects their phase n of powders, only BMW-Eu is single-phase, while BMW and BMW-Nd amounts of BaWO4 (Figure 2), while for ceramics, the materials are p phase, except BMW-Eu materials ( Figure 5). One may even be tempted t sintering method helps to obtain materials with higher phase purity (Fi The SEM micrographs of the BMW ceramics are shown in Figure  materials with high relative density (higher than 84%, see Table 1) were composition. These results show that the SPS schedule at 1350 °C under 5 pressure seems to be well adapted to densify such ceramic materials. Fr tos, it can be seen that all the materials subjected to the SPS sintering tests The photos show grains connected by distinct shapes with a few visibl images confirm that all materials were sintered with limited grain grow good microstructure homogeneity and fine microstructure to be mainta grain size of the polycrystalline powders and the obtained ceramic sint significantly from one another (see Table 1). This shows that the app submicrometric powders allowed to limit the grain growth due to the The SEM micrographs of the BMW ceramics are shown in Figure 6. Dense ceramic materials with high relative density (higher than 84%, see Table 1) were obtained for each composition. These results show that the SPS schedule at 1350 • C under 50 MPa of uniaxial pressure seems to be well adapted to densify such ceramic materials. From the SEM photos, it can be seen that all the materials subjected to the SPS sintering tests were compacted. The photos show grains connected by distinct shapes with a few visible pores. The SEM images confirm that all materials were sintered with limited grain growth, which allows good microstructure homogeneity and fine microstructure to be maintained. The average grain size of the polycrystalline powders and the obtained ceramic sinters did not differ significantly from one another (see Table 1). This shows that the application of SPS to submicrometric powders allowed to limit the grain growth due to the fast compaction. On the basis of the previously described X-ray diffraction patterns, the obtained ceramic materials ( Figure 5) are practically single-phase, except for in the case of the BMW-Eu material where there is an additional phase of BaWO 4 . The dark spaces visible in the SEM images are pores, while the impurities of the structure in the form of an additional phase BaWO 4 are visible in the images in the form of heterogeneity, i.e., where bright and darker areas in the form of streaks are visible. However, it should be emphasized that the additional phase in the form of BaWO 4 is much more visible on the X-ray diffraction pattern in the form of an additional reflex; the SEM images only confirm this.

Spectroscopic Properties of BMW Double Perovskites
The maximum of BMW powder emission is at 522 nm and the emission spectrum (see Figure 7) consists of two bands assigned to the blue-green emission of regular (in the range 350-500 nm) and yellow-green emission (in the range 450-800 nm) of inverse WO 6 groups. The maximum of the ceramic emission spectrum is blue shifted with the maximum at 503 nm and the proportion of regular/inverse emission is larger. The overall emission intensity is about nine times stronger for ceramics, but the relative intensity of the inverse WO 6 group is weaker, probably due to the fact that the sintering under big pressure does not allow for the formation of inversion defects in ceramics. material where there is an additional phase of BaWO4. The dark spaces visible in the SEM images are pores, while the impurities of the structure in the form of an additional phase BaWO4 are visible in the images in the form of heterogeneity, i.e., where bright and darker areas in the form of streaks are visible. However, it should be emphasized that the additional phase in the form of BaWO4 is much more visible on the X-ray diffraction pattern in the form of an additional reflex; the SEM images only confirm this.

Spectroscopic Properties of BMW Double Perovskites
The maximum of BMW powder emission is at 522 nm and the emission spectrum (see Figure 7) consists of two bands assigned to the blue-green emission of regular (in the range 350-500 nm) and yellow-green emission (in the range 450-800 nm) of inverse WO6 groups. The maximum of the ceramic emission spectrum is blue shifted with the maximum at 503 nm and the proportion of regular/inverse emission is larger. The overall emission intensity is about nine times stronger for ceramics, but the relative intensity of the inverse WO6 group is weaker, probably due to the fact that the sintering under big pressure does not allow for the formation of inversion defects in ceramics.  The BMW pure ceramics sample was excited also using the X-ray radiation (see Figure 8a). The emission from the WO6 groups was observed. However, this was mainly at  The BMW pure ceramics sample was excited also using the X-ray radiation (see F ure 8a). The emission from the WO6 groups was observed. However, this was mainly the green region, suggesting that the inverse WO6 groups are more sensitive to this hi energy radiation than the regular groups. The observations of the visible light under The BMW pure ceramics sample was excited also using the X-ray radiation (see Figure 8a). The emission from the WO 6 groups was observed. However, this was mainly at the green region, suggesting that the inverse WO 6 groups are more sensitive to this high energy radiation than the regular groups. The observations of the visible light under X-rays lead to creating new opportunities of using this material as a scintillator to detect high-energy ionizing radiation. The emission intensity of regular and inverse WO 6 groups not only strongly depends on the form of the sample but also on the source of the excitation. As a consequence, the emission chromaticity CIE (x, y) of investigated samples change from (0.222, 0.329) by (0.309, 0.422) to (0.354, 0.486) for ceramics, powder, and ceramics under X-ray excitation, respectively (Figure 8b). The color of observed emission varies from bluish-green for ceramics to yellowish-green for powder and yellow-green for ceramic under X-ray excitation.
Materials 2021, 14, 5996 10 of 16 rays lead to creating new opportunities of using this material as a scintillator to detect high-energy ionizing radiation. The emission intensity of regular and inverse WO6 groups not only strongly depends on the form of the sample but also on the source of the excitation. As a consequence, the emission chromaticity CIE (x, y) of investigated samples change from (0.222, 0.329) by (0.309, 0.422) to (0.354, 0.486) for ceramics, powder, and ceramics under X-ray excitation, respectively (Figure 8b). The color of observed emission varies from bluish-green for ceramics to yellowish-green for powder and yellow-green for ceramic under X-ray excitation. Contrary to the host emission, the Eu 3+ emission (see Figure 9) seems to be little affected by the sintering process. The emission spectrum of the Eu 3+ ions conserves its characteristics for both powder and ceramics, with dominant 5 D0 → 7 F1 magnetic-dipole transition around 596 nm and weak electric-dipole transitions 5 D0 → 7 FJ, where J = 0,2,3,4,5,6 characteristic of the highly symmetrical position of the Eu 3+ . The regular/inverse WO6 groups emission ratio (visible in the inset of Figure 9) is visibly lower, which confirms the energy transfer between the regular WO6 and Eu 3+ ions, previously reported in [24]. The emission of the tungsten group is not visible for powder materials (see Figure 9). Contrary to the host emission, the Eu 3+ emission (see Figure 9) seems to be little affected by the sintering process. The emission spectrum of the Eu 3+ ions conserves its characteristics for both powder and ceramics, with dominant 5 D 0 → 7 F 1 magnetic-dipole transition around 596 nm and weak electric-dipole transitions 5 D 0 → 7 F J , where J = 0,2,3,4,5,6 characteristic of the highly symmetrical position of the Eu 3+ . The regular/inverse WO 6 groups emission ratio (visible in the inset of Figure 9) is visibly lower, which confirms the energy transfer between the regular WO 6 and Eu 3+ ions, previously reported in [24]. The emission of the tungsten group is not visible for powder materials (see Figure 9). Bode and Oosterhout [25] assigned blue-green and yellow-green emission bands to the regular and irregular emission of the WO 6 group, respectively. In the latter, the tungsten ions, instead of entering their permanent place at BMW, replace the Mg 2+ position. It has been shown [24] that, with the increase in Eu 3+ , the emission intensity of WO 6 decreases, which confirms that the excitation energy is transferred from the host to the dopant. Based on Dexter's theory, Blasse analyzed the energy transfer from WO 6 groups to Eu 3+ ions [26]. He argues that the probability of energy transfer through the exchange mechanism is equal to the product of the overlap of the orbital wave functions W 6+ and Eu 3+ , and that the overlap of the emission energy of the WO 6 groups with the states of absorption of Eu 3+ ions. The orbital overlap, and hence the energy transfer mechanism, is regulated by the angle between the W 6+ -O 2--Eu 3+ bonds. If the angle is 90 • , the orbital overlap is negligible, and the largest is observed for the angle of 180 • [9,24]. In the previous report on BMW, Eu 3+ prepared by the mechanical-chemical method [9], it was calculated that the angle between W 6+ ( regular )-O 2-Eu 3+ is equal to 180º; however, the angle between W 6+ ( irregular )-O 2--Eu 3+ is equal to 135 • . This is why energy transfer to Eu 3+ ions mainly occurs from regular WO 6 groups. Bode and Oosterhout [25] assigned blue-green and yellow-green emission ban the regular and irregular emission of the WO6 group, respectively. In the latter, the sten ions, instead of entering their permanent place at BMW, replace the Mg 2+ positi has been shown [24] that, with the increase in Eu 3+ , the emission intensity of WO creases, which confirms that the excitation energy is transferred from the host to th pant. Based on Dexter's theory, Blasse analyzed the energy transfer from WO6 grou Eu 3+ ions [26]. He argues that the probability of energy transfer through the exch mechanism is equal to the product of the overlap of the orbital wave functions W 6 Eu 3+ , and that the overlap of the emission energy of the WO6 groups with the sta absorption of Eu 3+ ions. The orbital overlap, and hence the energy transfer mechani regulated by the angle between the W 6+ -O 2--Eu 3+ bonds. If the angle is 90°, the o overlap is negligible, and the largest is observed for the angle of 180° [9,24]. In the pre report on BMW, Eu 3+ prepared by the mechanical-chemical method [9], it was calcu that the angle between W 6+ (regular)-O 2-Eu 3+ is equal to 180º; however, the angle bet W 6+ (irregular)-O 2--Eu 3+ is equal to 135°. This is why energy transfer to Eu 3+ ions mainly o from regular WO6 groups.
To evaluate the impact of the form of material on the efficiency of the energy tra process from the WO6 groups to Eu 3+ ions, the energy transfer efficiency η was c lated using the following Equation (5). η = 1 − I I To evaluate the impact of the form of material on the efficiency of the energy transfer process from the WO 6 groups to Eu 3+ ions, the energy transfer efficiency (η ET ) was calculated using the following Equation (5).
where I Eu 3+ , I o is the integrated intensity of the sample with Eu 3+ and the host, respectively. The energy transfer efficiency between WO 6 groups and Eu 3+ ions was found to be 93.3% for the ceramic as compared to 99.2% for the sample in a powder form. The sintering process, while enhancing the host emission intensity, slightly restricts the energy transfer to Eu 3+ ions. The luminescence lifetimes of the main Eu 3+ ions emission were calculated using the integral equation due to the non-exponential character of the decay curves. The results are given in Figure 10. The shorter lifetime of the Eu 3+ emission in the BMW ceramic material is a result of the deformation of the vicinity of the Eu 3+ ions due to a large pressure applied to the powdered materials during sintering. Even a slight distortion of the environment will lower the ideal O h symmetry with the inversion center in which the Eu 3+ ions are located, making the observed emission more likely, and therefore shortening the lifetime of the excited 5 D 0 level. is a result of the deformation of the vicinity of the Eu 3+ ions due to a large pressure applied to the powdered materials during sintering. Even a slight distortion of the environment will lower the ideal Oh symmetry with the inversion center in which the Eu 3+ ions are located, making the observed emission more likely, and therefore shortening the lifetime of the excited 5 D0 level. The ratio of the integrated intensities between 5 D0→ 7 F2 (electric dipole) and 5 D0→ 7 F1 (magnetic dipole) transitions of the Eu 3+ ions is so-called the asymmetry factor R, and can be calculated with the Equation (6): This ratio describes the asymmetry around the Eu 3+ ions. The obtained values are the same for the BMW-Eu 3+ ceramics and powders, and are equal to 0.44. This indicates the high symmetric environment around the europium (III) ions in the investigated samples.
The emission spectra of Nd 3+ in powder and ceramic BMW are presented in the normalized form in Figure 11. The emission intensity is reduced for the ceramics sample by the factor of 5-6. This may suggest that the sintering process either eliminates the residual foreign phases present in the powder or, similarly to the results of the pure host, reduces the number of inversion defects and creates a highly symmetrical surrounding for Nd 3+ ions. The ratio of the integrated intensities between 5 D 0 → 7 F 2 (electric dipole) and 5 D 0 → 7 F 1 (magnetic dipole) transitions of the Eu 3+ ions is so-called the asymmetry factor R, and can be calculated with the Equation (6): This ratio describes the asymmetry around the Eu 3+ ions. The obtained values are the same for the BMW-Eu 3+ ceramics and powders, and are equal to 0.44. This indicates the high symmetric environment around the europium (III) ions in the investigated samples.
The emission spectra of Nd 3+ in powder and ceramic BMW are presented in the normalized form in Figure 11. The emission intensity is reduced for the ceramics sample by the factor of 5-6. This may suggest that the sintering process either eliminates the residual foreign phases present in the powder or, similarly to the results of the pure host, reduces the number of inversion defects and creates a highly symmetrical surrounding for Nd 3+ ions. The 4 F 3/2 → 4 I 11/2 transition is the strongest for all samples. At 77 K, the shape of the peaks is altered. Interestingly, the rarely observed 4 F 3/2 → 4 I 15/2 occurs in all cases; however, it is relatively stronger for the BMW ceramics, especially at the liquid nitrogen temperature. The 4 F3/2 → 4 I11/2 transition is the strongest for all samples. At 77 K, the shape of the peaks is altered. Interestingly, the rarely observed 4 F3/2 → 4 I15/2 occurs in all cases; however, it is relatively stronger for the BMW ceramics, especially at the liquid nitrogen temperature.
The spectroscopic quality parameter XNd, defined as a ratio of Judd-Ofelt intensity parameters, was calculated with using the formula described by A. Kaminskii [27].
where YNd = IJ, 11/2/IJ, 13/2 and IJ is integrated emission intensity; J is the total angular momentum quantum number. Depending on the sample, XNd has a different value in the range from about 0.65 up to 2.81 (see Table 2). At a lower temperature, when the influence of phonons is lower, both ceramics and powder of BMW:Nd 3+ had a higher value of the SQP.
All samples were measured both at 77 K and room temperature. The reason the results were not presented in their entirety is the following: only Nd samples exhibit a relevant difference in the emission spectra measured at both temperatures. The emission spectra of other samples are virtually identical in both temperatures.
Based on the emission spectra, the branching ratio of emission from 4 F3/2 to 4 IJ multiplets was obtained (see Figure 12). The contribution of the emission, depending on the sample and measurement temperature, shows low differences for the investigated samples at different temperatures.  The spectroscopic quality parameter X Nd , defined as a ratio of Judd-Ofelt intensity parameters, was calculated with using the formula described by A. Kaminskii [27].
where Y Nd = I J, 11/2 /I J, 13/2 and I J is integrated emission intensity; J is the total angular momentum quantum number. Depending on the sample, X Nd has a different value in the range from about 0.65 up to 2.81 (see Table 2). At a lower temperature, when the influence of phonons is lower, both ceramics and powder of BMW:Nd 3+ had a higher value of the SQP. All samples were measured both at 77 K and room temperature. The reason the results were not presented in their entirety is the following: only Nd samples exhibit a relevant difference in the emission spectra measured at both temperatures. The emission spectra of other samples are virtually identical in both temperatures.
Based on the emission spectra, the branching ratio of emission from 4 F 3/2 to 4 I J multiplets was obtained (see Figure 12). The contribution of the emission, depending on the sample and measurement temperature, shows low differences for the investigated samples at different temperatures.  The differences in luminescent properties between powdered and SPSed samples are mainly due to three reasons.
The first has already been mentioned in the description of the lifetimes of the emissions. The high pressure applied during the sintering of ceramics causes slight changes in the symmetry of the environment of Eu 3+ ions. Even slight changes in the environment reduce the ideal symmetry of the ions observed for the powder material. In the lowered symmetry, the participation of the electric dipole in the transitions increases, and, therefore, the ion emission transitions, either Eu 3+ or Nd 3+ , become more admissible because the selection rules are partially released. This, in turn, results in a shorter lifetime of the excited level and a higher emission intensity.
The second reason for the differences in spectroscopic properties of the BMW powder and ceramic materials is the influence of the pressure used in sintering ceramics on the formation of more WO6 inversion sites. This can most prominently be seen in Figure 9, which shows a much larger share of the emission of irregular groups of WO6, while, in the powder material, this emission is almost absent (see inset in Figure 9). This observation is also confirmed by the approximately 6% reduction in the efficiency of transfer of emissions from the host to the dopant for ceramics. As mentioned above, the irregular groups, i.e., WO6, hardly transfer energy to Eu 3+ .
Finally, the third effect of changes in the emission properties of ceramic materials results from the reduction in surface area and grain boundaries that occur in powder samples. This reduction primarily affects emission intensity by eliminating light scattering at grain boundaries and by improving overall light output.

Conclusions
The conventional solid-state reaction and the SPS technique were successfully applied to prepare powder samples and ceramics of Ba2MgWO6. All of them, pure BMW, BMW: 1% Eu 3+ , and BMW: 1% Nd 3+ , possess a regular double perovskite structure with the space group Fm-3m. SEM images showed that the prepared ceramics were well compacted; however, some pores were also visible. The highest relative density δ determined by the Archimedes method equals 91.99% for the undoped BMW. The proportion between The differences in luminescent properties between powdered and SPSed samples are mainly due to three reasons.
The first has already been mentioned in the description of the lifetimes of the emissions. The high pressure applied during the sintering of ceramics causes slight changes in the symmetry of the environment of Eu 3+ ions. Even slight changes in the environment reduce the ideal symmetry of the ions observed for the powder material. In the lowered symmetry, the participation of the electric dipole in the transitions increases, and, therefore, the ion emission transitions, either Eu 3+ or Nd 3+ , become more admissible because the selection rules are partially released. This, in turn, results in a shorter lifetime of the excited level and a higher emission intensity.
The second reason for the differences in spectroscopic properties of the BMW powder and ceramic materials is the influence of the pressure used in sintering ceramics on the formation of more WO 6 inversion sites. This can most prominently be seen in Figure 9, which shows a much larger share of the emission of irregular groups of WO 6 , while, in the powder material, this emission is almost absent (see inset in Figure 9). This observation is also confirmed by the approximately 6% reduction in the efficiency of transfer of emissions from the host to the dopant for ceramics. As mentioned above, the irregular groups, i.e., WO 6 , hardly transfer energy to Eu 3+ .
Finally, the third effect of changes in the emission properties of ceramic materials results from the reduction in surface area and grain boundaries that occur in powder samples. This reduction primarily affects emission intensity by eliminating light scattering at grain boundaries and by improving overall light output.

Conclusions
The conventional solid-state reaction and the SPS technique were successfully applied to prepare powder samples and ceramics of Ba 2 MgWO 6 . All of them, pure BMW, BMW: 1% Eu 3+ , and BMW: 1% Nd 3+ , possess a regular double perovskite structure with the space group Fm-3m. SEM images showed that the prepared ceramics were well compacted; however, some pores were also visible. The highest relative density δ determined by the Archimedes method equals 91.99% for the undoped BMW. The proportion between regular and irregular emission of WO 6 groups depends on sample forms and the excitation source. As was shown, regular WO 6 emission was enhanced for the BMW ceramic in contrast to BMW powder. However, under X-ray excitation, only irregular emission of WO 6 groups was detected. Green emission located at 522 nm after X-ray excitation offers a novel approach to this material as a scintillator. The sample also influences the energy transfer WO 6 → Eu 3+ efficiency; for powder η ET , it is almost 100%, while for the ceramic, η ET = 93.3%. As a consequence, both emissions of host and dopant ions are presented for the ceramic. High temperature and pressure during SPS reduce the inversion defect; as a result, characteristic Nd 3+ emission positioned in a high symmetry site was detected with the dominance of 4 F 3/2 → 4 I 11/2 transition.