Fundamentals of Cubic Phase Synthesis in PbF2 – EuF3 System

1. Introduction

Lead fluoride crystal has favorable properties such as a high density, non-hygroscopic, relatively chemically inert and short radiation length, while the scintillation light output is too small to obtain a photo-absorption peak under gamma ray excitation. Thus, it could not be used in medical imaging applications [1]. Lead fluoride crystal is widely used for detection of beta rays due to its relatively small back scattering. Lead fluoride activated by Europium (PbF₂:Eu) is light scintillators which are used for detection of charged particles and soft gamma ray up to several hundred keV [2].

Timing performance of PbF₂ crystals of various lengths and surface conditions coupled to SiPMs was evaluated against a reference detector with an optimized test setup using high-frequency readout and novel time walk correction, with special attention to the inherent limitations of single-photon Cherenkov detection only [3, 4].

Ce doped PbF₂ crystals did not show intense photo- and radio-luminescence, Eu and Ho doped ones showed several peaks excited under UV and 5.5-MeV alpha ray excitation, respectively [5].

In general, fluoride compounds and solid solutions in PbF₂-REF₃ systems (RE = rare earth element) are of interest for research as luminescent [6,7,8,9,10] and laser materials [11,12,13,14], especially effective in the mid-infrared range and in up-conversion imaging [10], as well as ionic conductors [15]. These systems have a wide crystallization region of the cubic fluorite phase Fm$\overline{3}$m (over 20 mol% at 650-700 °C) [6,7], but the phase diagrams and the phase existence regions at low temperatures (below 650 °C) are insufficiently studied. The complexity of studying these phase diagrams lies in the fact that lead fluoride undergoes a phase transition at 335-360 °C. The high-temperature cubic modification of lead difluoride (β-PbF₂) crystallizes in a cubic fluorite-like structure (Fm$\overline{3}$m), while the low-temperature phase (α-PbF₂) crystallizes in a rhombic structure (Pnma) [6]. There is no reliable information about the homogeneity limits of PbF₂, given the need to conduct research with highly pure materials. Typically, the declared chemical purity of the PbF₂ under study is no more than 99.9 wt%.

PbF₂ β→α phase transition is "frozen" because of the metastable state of β-PbF₂ at room temperature. It allows using this material as a fluoride-ion conductor and optical material. When heated, the phase transition occurs easily, whereas when β-PbF₂ is cooled from high temperatures, the phase transition is kinetically hindered.

In general, for the systems (MF₂ – REF₃, where M=Ba²⁺, Sr²⁺, Ca²⁺, and Pb²⁺; RE=rare earth element), the presence of a rhombohedral ordered phase (R-phase) with the ideal composition M₄RE₃F₁₇, existing in a relatively narrow concentration range of about 40 mol% REF3 [7,16,17,18,19,20] is assumed. According to the data [18], this phase is close to the fluorite phase, which complicates the identification of "rhombohedral fluorite".

The phase diagram of the PbF₂-EuF₃ system is insufficiently explored – the high-temperature range of 650-1300 °C is only predicted [6] based on diagrams of other rare earth elements, both F- and R-phases were identified at 650 °C [7], analysis conducted at 50 and 500 °C did not establish the presence of the R-phase, as this region was examined with a large interval of 10 mol%. Meanwhile, highly concentrated environments with reduced symmetry, activated by Eu, are promising materials for laser generation in the red spectral range [21].

Studies of solid solutions of PbF₂-EuF₃ and glass-ceramic materials have shown that the introduction of EuF₃ in concentrations of 7-10 mol% stabilizes the high-temperature phase even when synthesized at temperatures below 300 °C [8,9]. Thus, on the T-X diagram of PbF₂-EuF₃ at temperatures below 365 °C and EuF₃ concentrations of 0-10 mol%, there should be a line between the regions of crystallization of a single cubic phase solid solution Pb_1-xRE_xF_2+x and the region of crystallization of two phases (solvus line). In the two-phase region, the above-mentioned solid solution phase and a phase extremely close to α-PbF₂ are in equilibrium, as the solubility of RE in the low-temperature phase of lead fluoride is negligible (Figure 1).

It is known that impurities even in concentrations of hundredths of a mol.% can significantly shift the boundaries of the homogeneity region, including the temperatures of polymorphic transitions. [22].

The global task of the research was to clarify the boundaries of the homogeneity re-gion of the cubic phase for future development of synthesis technology of single phase extra pure cubic phase preparations in PbF₂-EuF₃ system. To solve the task, we investigated two regions of the phase diagram of the quasi-binary system PbF₂-EuF₃ within the composition range of 0-45 mol% EuF₃ and identified the R-phase within the composition range of 35-45 mol% EuF₃.

2. Materials and Methods

Preparations within the PbF₂-EuF₃ system with EuF₃ content ranging from 0 to 12 mol% and from 35 to 45 mol% were synthesized at low temperature using the co-precipitation technique [9,23]. The starting materials included Pb(NO₃)₂ (99.99 wt%, LANHIT, Russia), Eu(NO₃)₃ (99.99 wt%, LANHIT, Russia), and HF (99.9 wt%, TECH Systems, Russia) and additionally purified to 99.99999 wt%. Initially, lead and europium nitrate solutions were prepared in bidistilled water (0.08 mol/L). Subsequently, these solutions were meticulously mixed in predetermined proportions. The resulting solution was added dropwise to hydrofluoric acid solution (5 vol%) with continuous stirring and a 10-fold excess of hydrofluoric acid to maintain a constant pH during the process. The process involved continuous stirring of the mother liquor using a magnetic stirrer. At this stage, a chemical reaction has been conducting:

(1-x)Pb(NO₃)₂ + xEu(NO₃)₃·6H₂O + (2+x)HF → Pb_1-xEu_xF_2+x↓ + H₂O,

(1)

The synthesis was carried out in a polypropylene reactor, and upon completion, the matrix solution was further stirred for one hour. The resulting precipitate was decanted, washed with bidistilled water until a negative reaction of diphenylamine to nitrate ions was observed, and then air-dried at 40–50 °C.

In order to determine the temperature of the phase transition, the powders were subjected to heat treatment at temperatures of 200, 300, 330, 350, 360, and 400°C for 48 hours in a resistance tube furnace. Subsequently, a comprehensive set of analysis was conducted. The samples were then placed in the furnace and subjected to heat treatment at the same temperatures for an additional 24 hours, followed by further investigation.

Preparations in the PbF₂-EuF₃ system with EuF₃ concentrations ranging from 35 to 45 mol% were also obtained via solid-state synthesis at 550°C. PbF₂ (99.99% purity, LANHIT, Russia) and EuF₃ (99.99% purity, LANHIT, Russia) were used as starting materials. The solid-state synthesis was conducted in a resistance tube furnace at 550°C for 2 hours in corundum crucibles. Initially, the fluoride powders were ground in a mortar to increase the contact area between the reacting substances. Additionally, a fluorinating atmosphere was established [8, 9, 24] to prevent pyrohydrolysis.

The formation of a solid solution is described by the following chemical reaction.

(1-x)PbF₂ + xEuF₃→ Pb_1-xEu_xF_2+x

(2)

After completion of the first stage, the resulting sintered powders were re-ground and placed in the furnace under identical conditions.

X-ray diffraction analysis was conducted using an Equinox 2000 X-ray diffractometer (CuK_α radiation with a wavelength of λ = 1.54 Å), with an accuracy of lattice parameter determination of +1%·and sensitivity up to 1% of the impurity phase. X-ray diffraction patterns were interpreted using TOPAS software (PCPDFWIN electronic catalog and JCPDS-ICDD database), and phase ratios were calculated using Match! software. During the analysis, the absence of partially oxidized phase (Pb₂OF₂) was additionally monitored based on the peak at 2Θ = 26.75° [8,26].

Energy-dispersive X-ray spectroscopy (EDS) microanalysis was performed to determine the actual composition of the samples using a scanning electron microscope (SEM) model VEGA3-LMU (TESCAN, Brno, Czech Republic) equipped with a lanthanum hexaboride thermionic cathode and an Oxford Instruments X-MAX-50 EDS detector, operating in secondary electron mode. The AZTec software was utilized for data collection and processing. All measurements were conducted at room temperature, with no fewer than 8 points measured for each sample. Imaging was carried out at an accelerating voltage of 30 kV.

The impurity content of the starting materials and the resulting powders was determined by inductively coupled plasma mass spectrometry (ICP-MS). Lead fluoride-based powders were dissolved in 20 mL of sulfuric acid (7N, 96%) purified by a surface distillation systems Milestone DuoPUR (Milestone S.r.l., Sorisole, Italy) with microwave digestion of the sample in polytetrafluoroethylene autoclaves (DAP-100, PTFE, BERGHOFF GmbH&Co., Wenden, Germany) using a SPEEDWAVEFOUR microwave decomposition setup (BERGHOFF GmbH&Co., Wenden, Germany). The resulting solution was transferred to a polypropylene test tube, and diluted with water. Deionized water was obtained using an Aquapuri 5 - 551 Series (Young Lin Instruments Co., Ltd., Hogye, South Korea) and had an electrical resistance of 18.2 MΩ cm. The prepared solution was analyzed using inductively coupled plasma mass spectrometry (ICP-MS). Analytical measurements were carried out using an inductively coupled plasma mass spectrometer NexION300D (PerkinElmer Inc., Waltham, MA, USA) [26]. The resulting powders had a purity of greater than 99.99 wt% (see Table S1).

Europium (Eu³⁺) photoluminescence (PL) spectra were recorded using a Fluorolog FL3-22 spectrofluorometer (Horiba Jobin Yvon, USA) in the wavelength range of 400–700 nm with 0.1 nm step, excited by a diode laser (λ = 377 nm).

Raman scattering spectra (RS) were investigated using a HORIBA LabRam Soleil instrument (Horiba Jobin Yvon GmbH, Bensheim, Germany) with the ability to excite RS with lasers of three wavelengths: 377 nm, 532 nm, and 785 nm. In our case, only the 785 nm excitation wavelength was used, since in other caused excitation of Eu³⁺ fluorescence [27]. Measurements were carried out in the range of 149–3500 cm^-1 with 2 cm^-1 step.

Infrared (IR) transmittance measurements were performed using a Tensor 27 Fourier-transform infrared spectrometer (FTIR) (Bruker Optics Inc., Billerica, MA, USA) in the range of 400-8000 cm^-1 with 1.9 cm^-1 step.

3. Results and Discussion

3.1. Position of the Solvus line on the PbF₂-EuF₃ Diagram

The samples synthesized by co-precipitation method have appeared as fine white powders. The appearance did not change depending on the nominal europium content, indirectly indicating the absence of oxidized phases. Analysis of the phase composition of the samples after synthesis at nominal Eu concentrations from 0.5% to 7 mol% revealed the presence of two phases simultaneously: α-PbF₂ and Pb_1-xEu_xF_2+x. From 8 to 12 mol%, only one cubic phase of the solid solution with parameters corresponding to the nominal composition (Figure 2). In the composition range 0-5 mol% the X-ray reflections belonging to rhombic phase correspond to pure α-PbF₂.

It is worth noting that the reflections of the cubic solid solution Pb_1-xEu_xF_2+x are shifted relative to the reflections of nominally pure β-PbF₂ in the greater Θ angles which indicates on compression of cubic lattice parameters because of incorporation of smaller Eu3+ ion in the crystal lattice of the solid solution.

The lattice parameter for these solid solutions obeys a linear equation (Vegard's law):

a = 5.940 + k_Eu‧x,

(3)

where 5.940 Å – β-PbF₂ lattice parameter, x – the mol% of RE, the coefficient k_Eu = – 0.00237 was determined in [Error! Reference source not found.,Error! Reference source not found.].

The lattice parameter of the obtained solid solutions in the range of nominal EuF₃ content from 1 to 7 mol% was found to be 5.919±0.003 Å, corresponding to EuF3 content of 7.0-9.5 mol% according to the Vegard law.

The examination of the PXRD patterns after heat treatments revealed (Figure 3, Figure S1, Table S2) that the proportion of the cubic phase began to increase starting from 300°C. For the sample with a nominal composition of Pb_0.97Eu_0.03F_2.03, at 330°C, the volume fraction of α-PbF₂ is small compared to the cubic phase of the solid solution (Fig. 3), which is consistent with the findings of a previous study [7].

A sharp increase in the proportion of the cubic phase is observed after 330°C; samples with a nominal EuF₃ content exceeding 5 mol% in this temperature range are already the single-phase. In nominally pure PbF₂, the rhombic phase is detected even after heat treatment at 360°C (Figure 4).

Remarkably, the lattice parameters of the cubic phase after heat treatment show a tendency to increase, indicating an approach to the lattice parameters of solid solutions obtained by solid-state synthesis at 500°C [8].

Figure 5. Variation of lattice parameters of the cubic phase after heat treatment of samples with nominal composition Pb_1-xEu_xF_2+x.

Figure 5. Variation of lattice parameters of the cubic phase after heat treatment of samples with nominal composition Pb_1-xEu_xF_2+x.

Such lattice parameter behavior and the unchanged properties of the powders after an additional 24-hour heat treatment indicate that the obtained values are close to equilibrium state.

Eu³⁺ is a luminescent-active impurity, and its spectrum is sensitive to changes in the symmetry of the surrounding environment. Thanks to this, the Eu³⁺ ion is often used as a spectroscopic probe, making samples with Eu³⁺ concentration of 0.1 mol% [28]. It is considered that at such concentrations, the additional introduction of Eu does not significantly alter the structure. In our case, the Eu concentration is knowingly higher and varies from sample to sample, so the use of all the fine capabilities of spectroscopic probing analysis may be incorrect, hence we used only an estimation of local symmetry by the asymmetry coefficient [8,9].

The electric dipole transition ⁵D₀→⁷F₂ (~ 612 nm) in the Eu³⁺ ion is highly sensitive. The magnetic dipole transition ⁵D₀→⁷F₁ (~ 590 nm), permitted in terms of parity, has an intensity that is practically independent of the point symmetry of the luminescent center and its environment. To characterize the local environment of Eu³⁺ ions, the asymmetry coefficient R21 is used. By definition, it is the ratio of the intensities of the highly sensitive electric dipole transition ⁵D₀→⁷F₂ and the magnetic dipole transition ⁵D₀→⁷F₁ [9]:

$$R21={\displaystyle \frac{I_{ED}\left({{}_{5}D}_0\to {{}_{7}F}_2\right)}{I_{MD}\left({{}_{5}D}_0\to {{}_{7}F}_1\right)}}$$

(4)

,

The greater the value of this ratio, the less symmetrical the environment of the europium ion in this matrix. Dominance in intensity of the band corresponding to the magnetic dipole transition ⁵D₀→⁷F₁ over the electric dipole transition ⁵D₀→⁷F₂ indicates an environment of the Eu³⁺ ion close to centrosymmetric, as observed in solid solutions (Figure 6).

The transition between the energy levels ⁵D₀ and ⁷F₀ is also forbidden by the selection rules for electronic dipole transitions, and moreover, these levels are degenerate and therefore have zero Stark splitting. This transition is practically absent in the fluorescence spectra of solid solutions, confirming a symmetry close to cubic for the Eu³⁺ optical centers.

As the annealing temperature increases, the asymmetry coefficient behaves differently depending on the nominal composition (Figure 7).

In samples with a nominal content of EuF₃ ranging from 3 to 9 mol%, there is a gradual decrease in R21, indicating an increase in symmetry. In samples with 0.5 and 1 mol% EuF₃, initially up to 200 °C, R21 increases due to structure relaxation, followed by a sharp decrease in R21, indicating increased centrosymmetry. In the phase transition region, R21 in all samples ranges from 0.30 to 0.35 (Table S2). Thus, the structural data obtained from XRD and luminescence studies coincide.

Figure 8 schematically represents a fragment of the T-X diagram of the quasi-binary system PbF₂-EuF₃ in the investigated range of temperatures and compositions. It is evident that with the increase in the nominal content of EuF₃, the temperature of the phase transition sharply decreases. It is worth noting that the phase transition in all investigated compositions is frozen, as in nominally pure PbF₂ [6], meaning that no phase separation occurs upon cooling for a long time (at least, no changes in the structure and luminescence of annealed powders have occurred over the course of a year).

3.2. Determining the Existence Region of the Rhombohedral R-Phase in the PbF₂-EuF₃ System

To determine the existence of the R-phase, samples were synthesized in the nominal Eu concentration range of 35 – 45 at% using co-precipitation and solid-phase methods. In both cases the synthesized samples appeared as white powders. It was particularly important in the case solid-phase synthesis, indicating the absence of oxidation processes and the formation of lead oxyfluorides and oxides.

X-ray spectral microanalysis allowed determining that the deviations from the theoretically calculated compositions of the samples during synthesis do not exceed 0.05 at% (Table S4). SEM analysis of powder images shows that the particle sizes obtained by co-precipitation technique vary widely from microns to tens of microns, with irregular shapes (Table S4). Finer powders (ranging from 0.5 to 1 micron) were obtained through solid-phase synthesis, attributed to several grinding steps during synthesis.

When studying the diffraction patterns of samples obtained by solid-phase synthesis (Figure 9a) and coprecipitation from aqueous nitrate solutions (Figure 9b), the presence of a solid solution with parameters different from the high-temperature cubic modification of PbF₂ was discovered, which was especially noticeable at large values ​​of 2Θ.

To confirm the assumption of the presence of the R-phase, the calculation of the unit cell parameter was carried out based on the obtained XRD data. Initially, the peaks were indexed within the framework of a cubic cell (Fm$\overline{3}$m) with parameters close to the high-temperature modification of lead fluoride. The obtained values of the unit cell parameter for samples obtained by solid-phase synthesis and co-precipitation technique are presented in Table S5.

Graphically analyzing the obtained results (Figure 10a), a significant difference is noticeable between the theoretical values obtained according to Vegard's law for a hypothetical solid solution Pb_1-xEu_xF_2+x and the values of the unit cell parameter calculated for samples synthesized by co-precipitation and solid-phase methods. According to [28], the deviation is better observed in terms of the volume of the crystalline cell (Figure 10b), and correspondingly in linear equations (Röttgers’s rule):

V = V₀ + k_V‧x,

(5)

where V₀ – refers to the unit cell volume of the fluorite matrix MF₂ (for β-PbF₂ 209,58 ų), x – the mol% of RE, k_V is the coefficient.

k_V = 3a0k,

(6)

Thus, from equations (3) and (6), k_VEu = -0.2509.

In the range of 40-45 mol% EuF₃, deviations in cell parameter and volume from the calculated values are observed. Scanning with a larger step [8] indicated that the violation of Vegard's law begins at 36±2 mol% EuF₃, but a significantly different phase, based on the rhombic (Pnma) modification of europium trifluoride Er_1-yPb_yF_3-y, can only be observed starting from 60 mol% EuF₃. Thus, deviations from linear laws in the 40-45 mol% EuF₃ range may be associated with the existence of a phase in this range, with reflections close to the Pb_1-xEu_xF_2+x cubic solid solution, i.e., the R-phase.

We discovered, deviations from the linear law for samples obtained by solid-phase synthesis and co-precipitation were in opposite directions. A slight increase in the cell parameter for solid-phase samples corresponding to a solid solution with lower Eu concentration may indicate the presence of a narrow two-phase equilibrium region of the cubic solid solution Pb_1-xEu_xF_2+x and its distorted modification, the R-phase. A decrease in the cell parameter for samples obtained by co-precipitation technique may be related to the non-equilibrium nature of the obtained phases.

Fluorescence spectra of powder samples in this concentration range were also investigated (Figure 11).

In 37-45 mol% EuF₃ concentration range the asymmetry coefficient was significantly higher than in the range up to 10 mol% EuF₃. For samples with composition (100-x)PbF₂-xEuF₃ (x=41 – 45 mol% EuF₃), the coefficient R21 gradually increases (see Figure 12), indicating a slight increase in asymmetry due to the heterovalent substitution in the solid solution. However, with further increase in Eu concentration, R21 undergoes a sharp increase. Thus, the boundary at which the local structure begins to distort significantly is approximately 39 mol% Eu.

Additionally, vibrational spectra were investigated in this system. The complete vibrational representation for crystals with a fluorite structure can be expressed as [30]:

Г = F_1u (IR) + F_2g (R),

(7)

where F_1u - represents a triply degenerate, antisymmetric vibration with respect to the center of symmetry, active in the infrared spectrum, and F_2g - represents a triply degenerate, symmetric vibration with respect to the center of symmetry, active in the Raman spectrum.

FTIR spectroscopy (Figure S2) in our case does not allow determining the vibrational modes of cubic PbF₂, as the F_1u vibrations lie around 347 cm^-1 (less than 400 cm^-1) [30]. However, it did reveal the presence of nitro groups [NO₃]^– [31] and hydroxyl groups [OH]^– [31] in samples obtained by co-precipitation (Fig. S2, Table S6), indicating the high sensitivity of the method, as the qualitative reaction of diphenylamine was negative, and the samples were dried for an extended period.

In the Raman spectra of crystals of undistorted fluorite type, a single line will be observed, and the frequency of this line for a crystal of nominally pure β-PbF₂ falls within the range of 256-259 cm^-1 [32], corresponding to the F_2g vibration mode. This is clearly seen in the spectra of single-phase samples with concentrations of 5 and 11 mol% EuF₃. When comparing the Raman spectra of samples with Eu concentrations ranging from 37 to 45 mol% EuF₃, a noticeable shift in the peak maximum and broadening of the peaks can be observed (Figure 13, Table S7).

One can observe a significant shift in the peak maximum for samples containing Eu 37-43 at%, indicating the presence of another phase structurally similar (Figure 13). Since the phase of the cubic solid solution Pb_1-xEu_xF_2+x and the R-phase are very close in structure and parameters, the splitting of the band into close components leads to its broadening. The narrowing of the band in the region of 43 at% Eu may be associated with the crystallization region of only the R-phase.

Summarizing the results of phase equilibria analysis we reconstructed T-X-Y diagram of Pb-Eu-F ternary system within the PbF₂-EuF₃ section (Figure 14). In this study we proved the general view of T-X-Y diagram [8] but expanded the temperature range from 50 to 550°C and clarified the concentration ranges of homogeneity limits for cubic and orthorhombic PbF₂:Eu and R-phase. To better understanding we presented the fragment of T-X-Y diagram nearby PbF₂-EuF₃ quasi-binary cross-section in a variable scale with the large logarithmic scale near PbF₂ and the linear scale starting from 10 mol.% of EuF₃. The homogeneity limits were determined along PbF₂-EuF₃ quasi-binary cross-section in mol.% of EuF₃. Their width towards Metal-F direction were less than 1 mol% which is typical for the homogeneity ranges of fluoride binary compounds [6].

The main features of the analyzed system were determined and it was established that the homogeneity region of the R-phase is about 1 mol.% and is within 44-45 mol.% EuF₃, changing slightly with temperature over the entire temperature range under consideration.

The cubic solid solution Pb_1-xEu_xF_2+x is located from 7.5 to 38 mol% EuF₃ at 50-200°C with a retrograde motif. It then expanded from 7.5 to 37 mol.% EuF₃ at 300°C. Starting at 330°C it reaches the T-Pb-F plane and no longer deviates from it with increasing temperature. The Eu-rich boundary of the cubic solid solution Pb_1-xEu_xF_2+x shifts from 37 to 32 mol.% EuF₃ at 550°C.

Simultaneously, the orthorhombic PbF₂:Eu phase expanded from 0.1 to 1 mol.% EuF₃ at temperature rise from 50 to 280°C. After then it is quickly compressed to zero at 360°C. In the entire temperature range under consideration, the homogeneity region of the orthorhombic PbF₂ phase does not detach from the T-Pb-F plane.

So, we established that the stable cubic phase in PbF₂-EuF₃ quasi-binary system could be obtained at all temperatures starting from RT to 550°C and it exists in a wide concentration range up to 38 mol% of EuF₃.

The only currently unclear issue is the existence of S_α-PbF2S_β-PbF2S_R-phaseV monovariant equilibrium at low temperatures (Figure 15 – red triangle). We believe this issue is important for the future operation of devices based on a cubic solid solution Pb_1-xEu_xF_2+x phase.

4. Conclusions

Samples in the system (100-x)PbF₂-xEuF₃ were synthesized by co-precipitation from aqueous solutions with values of x ranging from 0 to 12 mol% EiF₃. The phase composition of the obtained samples was determined as follows: for x equal to 0 mol% - α-PbF₂, for the range 0.5 – 7 mol% - a mixture of phases α-PbF₂ and a cubic solid solution with a composition close to Pb_0.93Eu_0.07F_2.07, and for the range 8-12 mol% - a cubic solid solution corresponding to the nominal Pb_1-xEu_xF_2+x. Thermal treatment was carried out at various temperatures (200 - 400°C), allowing the determination of phase transition temperatures for samples with x from 0 to 7. Investigation of the local structure of the Eu³⁺ ion environment showed a significant increase in symmetry during thermal treatments in the range of 300-350°C. The solvus line position was determined based on the combined data.

Samples in the quasi-binary system (100-x)PbF₂-xEuF₃ with x values from 35 to 45 mol% EuF₃ were synthesized by solid-state and liquid-phase methods. A comparative X-ray diffraction analysis was conducted, showing deviation from Vegard's law and Röttgers's rule in the range of 39-44 mol% Eu. Spectral-luminescent analysis of samples obtained by co-precipitation with 37-44 mol% EuF₃ content revealed a significant change in the asymmetry coefficient R21, indicating a change in the symmetry of the europium ion environment. The presence of a phase slightly different from the cubic one in the range of 37-43 at% Eu was established using Raman spectroscopy. Thus, in the range of x from 36 to 42 mol% EuF₃, two close phases are present: cubic Pb_0.64Eu_0.36F_2.36 and a rhombically distorted R-phase. It is likely that only the R-phase is present in the region of 43 mol% EuF₃, as evidenced by the narrowing of the Raman band, and at higher EuF₃ concentrations, a phase equilibrium is established, where the R-phase, Eu_1-yPb_yF_3-y, and EuF₃ are in equilibrium.