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Article

Preparation and Mechanical Characteristics of Multicomponent Ceramic Solid Solutions of Rare Earth Metal Oxides Synthesized by the SCS Method

by
Victor Zhuravlev
*,
Larisa Ermakova
,
Rina Samigullina
and
Alexey Ermakov
Institute of Solid State Chemistry, Ural Branch, Russian Academy of Sciences, 91, Pervomaiskaya, Ekaterinburg 620108, Russia
*
Author to whom correspondence should be addressed.
Ceramics 2023, 6(2), 1017-1030; https://doi.org/10.3390/ceramics6020060
Submission received: 24 March 2023 / Revised: 14 April 2023 / Accepted: 20 April 2023 / Published: 22 April 2023
(This article belongs to the Special Issue Ceramic Processing and Sintering, Volume II)
Browse Figures
Versions Notes

Abstract

:
A study into the use of the Solution Combustion Synthesis (SCS) method with glycine and citric acid to synthesize fine powders of multicomponent solid solutions of oxides of rare earth (RE) metals (Nd, Sm, Eu, Gd, Dy, and Ho) for the preparation of ceramic materials is presented. Synthesis parameters of 4-, 5-, and 6-component entropy-stabilized rare earth oxides (REOs) with a C-type cubic structure are determined. The stability of entropy-stabilized oxides (ESOs) with a C-type structure is shown to depend not only on heavy RE metal quantity, but also on the rate of heating/cooling of the samples. The temperature of the polymorphic transformation of C-type REO structures into B-type (monoclinic) or H-type (hexagonal) structural variants can be described by the equation T (°C) = 0.0214Vcr2 − 62.737Vcr + 46390, where Vcr is the unit cell volume of an oxide with a C-type structure regardless of the number of cations in the solid solution. High-temperature thermal analysis up to 1250 °C revealed that dispersed powders, which contain impurities of basic carbonates along with hydroxocarbonates of RE metals and X-ray amorphous carbon formed during SCS reactions, also react with air moisture during storage. The influence of the ESO phase and cationic composition on the morphology, porosity and microhardness of ceramics was studied. Higher-entropy oxides form samples with higher density, microhardness and a smaller size of particle agglomerates.

1. Introduction

Rare earth metal oxides (REOs) and their solid solutions are very important components of optical isolators and magneto-optical materials, offering high optical quality for information and communication technologies, data storage and processing elements, optics, magnetic, and laser generation [1,2,3,4,5,6]. Semiconductor films are used as dielectrics in metal oxide semiconductors due to their high dielectric constant and wide band gap (Eg), along with excellent physical and chemical stability when in contact with a silicon substrate [1,7]. Disposing high thermal stability, bright colors, and narrow emission bands, rare earth luminescent nanomaterials can withstand exposure to strong ultraviolet and high-energy radiation [8,9]. Among other REOs, Y2O3, Nd2O3, and Sm2O3 impart high strength and impact toughness to ceramics for various purposes [10,11], including anticorrosion [12,13,14] and thermal barrier coatings [11,12,13,14,15,16,17,18]. The use of REOs as cryocoolers is another area of application. Materials based on Gd2O3 with the addition of europium exhibit an increased magnetocaloric effect. Such magnetic coolants have a high heat transfer rate and efficiency [11,19,20,21,22,23].
Oxides of ytterbium, terbium, europium, and samarium are included in the composition of catalysts for the selective oxidation of styrene [24], mixed Gd2-xDyxO3 are used in electrocatalysis [25], while, for catalytic smoke toxicity suppression of epoxy resin, mixed RE oxides and yttrium are used [26]. Due to the similarity of the external electronic levels of lanthanides and yttrium, they are widely interchangeable in the crystal structures of complex oxides, allowing the complex doping of luminescent matrices, etc. However, the formation of solid solutions over the wide range of relative concentrations in binary, ternary, and more complex REO systems can be hindered by the following factors:
1. Differences in oxidation states. For example, terbium oxide under normal conditions exists in the form of 2Tb2O3·3TbO2 (rhombohedral structure) and 2Tb2O3·7TbO2 (triclinic structure) [27,28]. While Tb2O3 can be obtained after calcination in an inert or reducing atmosphere, it decomposes into the original oxides in air above 280 °C.
2. Crystallization of REOs in various crystal structures and the presence of polymorphism. Under ambient conditions, CeO2 and PrO2 oxides with a fluorite structure are formed, in the most oxidized state of which cations exist (4+). When heated, Ln2O3 oxides generally undergo several polymorphic transformations [29,30]. Three structures were identified at temperatures below 2000 °C: in the A-type hexagonal structure, lighter oxides (La–Pm); in the C-type cubic structure, oxides with smaller cation radii (Tb–Lu and Y); in medium-sized cations, Sm—Gd crystallizing in a C-type structure or in a B-type monoclinic structure [31]. At higher temperatures, transformations into hexagonal (H) and cubic (X) modifications are observed [30].
Information on phase equilibria in binary systems of REOs is most fully presented in the scientific literature for systems with the participation of CeO2—Ln2O3; this may be because solid solutions with the fluorite structure have an ionic conductivity 4–5-fold higher than that of YSZ solid solutions [32]. However, since the maximum electrical conductivity was found precisely for the compositions of this range most authors limited themselves to the study of Ce1-xLnxO2−Δ materials, where x = 0–0.3 [33]. Prior to the discovery of high-entropy oxides, less attention was paid to the description of solid solutions based on REOs with a C-type structure. Table 1 presents the information obtained on binary solid solutions of REOs with a C-type crystal structure [5,9,34,35,36,37,38,39]. As a rule, these solid solutions were obtained by slow cooling after annealing at 1400 °C. The presence of Ce4+ cations in the crystal lattice leads to the appearance of excess oxygen [34,35,36,37].
In recent years, much attention has been paid to studies of high-entropy oxides [38,40,41]. The first empirical descriptions of their structural formation were formulated: close ionic radii, mandatory nonisostructurality of one of the oxides, and the absence of complete miscibility in the binary phase diagram of at least one pair of oxides [38,41]. The general concept of entropy stabilization of the oxide system, which can be achieved by increasing the number of elements, is based on the stabilization of single-phase crystal structure by increasing the configurational entropy (𝑆conf) of the system [42]. Based on the maximum entropy of mixing, a higher stability of equiatomic high-temperature high-entropy oxides is postulated compared to asymmetric compositions, since, with the exception of the commensurability of the ionic radii of the cations, other factors do not offer sufficient evidentiality. According to the literature data, special techniques and techniques for synthesis and annealing are required for a number of compounds. Table 2 presents some published data on the compositions of high-entropy rare earth oxides with a C-type cubic crystal lattice.
Thus, the present article reports on the possibility of obtaining entropy-stabilized oxides (ESOs) with a non-equiatomic ratio of rare earth elements crystallizing with a C-type structure in Solution Combustion Synthesis (SCS) reactions. The dependence of the formation of single-phase oxides with a C-type structure on the content of glycine and citric acid, as well as on the annealing temperature, has been studied. The thermal behavior of single-phase powders after 700 °C has also been studied and described. Considering the morphology of powders following SCS, an attempt was made to obtain dense ESO ceramics with preservation of a C-type structure and subsequent evaluation of their mechanical properties. A new concept of designing materials already used in various fields of science and technology is based on the possibility of controlling the phase stability and functional properties of multicomponent solid solutions by controlling their configurational entropy [42]. Such studies were undertaken in the present work for entropy-stabilized oxides.

2. Materials and Methods

2.1. Preparation and Processing of Powders

Fine powders of multicomponent solid-solution REOs were synthesized by SCS [43,44]. The initial solutions were prepared by dissolving RE(NO3)3·6H2O, where RE = Nd, Sm, Eu, Gd, Dy, and Ho, in distilled water. Dual fuel was used for SCS, glycine and citric acid, with φcitr + φgl ≤ 1.1. The resulting oxide powders were calcined at 700 °C for primary burnout of expected volatile impurities, fuel residues, decompose rare earth hydroxides, and structural crystallization and form a c-type structure. To study the phase stability of the C-type structure, successive high-temperature annealing of both powders and ceramics was carried out. The annealing temperature of 1250 °C, used both for powder annealing and ceramic sintering, is determined by the C→B transition temperature for Gd2O3. The composition of the samples, preparation conditions, and content of the C-type phase are given in Table 3.

2.2. Preparation and Processing of Ceramics

After annealing at 700 °C, the resulting powders were compacted on a tensile testing machine manufactured by Fritz Heckert (GDR) at a speed of movement of the object table of 4 mm/min. Compact samples in the form of disks of 2–3 mm in thickness were fabricated by dry uniaxial pressing at 8.2 GPa with following sintering at 1250 °C for 7 h in corundum crucibles. The sintering profile included the following stages: heating to 700 °C at a heating rate of 6.5°/min; heading to 1250 °C at a rate of 4.5°/min; holding at 1250 °C for 7 h; cooling to 700 °C at a rate of 3°/min; free cooling to room temperature.
The density of sintered ceramics, ρ, %, was determined from the ratio of the effective volume, Vef, not taking into account the pore space, to the apparent volume, Vk, including both the solid core and the volume of closed and open pores. Vk was calculated from the geometric dimensions of the sintered samples, Vef was measured by the pycnometric method on an AccuPyc II 1340 V1.09 helium pycnometer in a 1 cm3 cuvette at a measurement error of 0.03%. The porosity, Φ, was determined from relation (1).
Φ = [1 − Vef/Vk] ∗ 100

2.3. Characterization Techniques

The phase composition and structure refinement of the powders and ceramics samples were performed on an XRD-7000 (Shimadzu, Japan) diffractometer using Cu Kα1 radiation in the 2θ range from 10 to 70° with a step of Δ(2θ) = 0.05° and exposure time of 3 s. Possible impurity phases were checked by comparing their XRD patterns with those in the PDF-2 database (ICDD, 2016). The unit cell parameters were refined using the POWDER CELL 2.4 software package. The microstructures of the powder and ceramic samples were characterized with a JSM 6390 LA (JEOL, Japan) scanning electron microscope (SEM). All of the thermogravimetry (TG) and differential scanning calorimetry (DSC) curves were obtained simultaneously using a Setaram Setsys Evolution-1750 thermal analyzer in air with heating/cooling rate of 10°/min in the temperature range, ΔT, 20–1250 °C. The microhardness of ESO ceramics was measured using a Micromet 1 microhardness tester (Buehler LTD. Lake Bluff, Illinois, USA) with automatic diamond pyramid indentation under a load of 100 g and a load time of 10 s. From the data obtained by performing at least 10 measurements of microhardness (indentations of a diamond pyramid) on each sample, where both diagonals were measured on each print, the average value of microhardness was determined and the measurement error was estimated.

3. Results and Discussion

3.1. Dispersed Solid Solutions of Rare Earth Metal Oxides

The production of multicomponent oxides of rare earth metals with a C-type structure using the SCS method implies the selection of a fuel such that the combustion process does not develop a temperature at which the formation of the monoclinic B form begins. By carrying out the synthesis under various conditions, it was possible to experimentally establish the ratio of glycine and citric acid, comprising the most universal ratio for the synthesis of the studied systems with the desired cubic structure. Table 3 shows that an increase in the relative content of glycine in the fuel contributes to an increase in the time of fire activation, as well as increasing the exothermicity of the reaction; the precursors ESO-1-1, ESO-1-2 and ESO-2-1 contain noticeable amounts of the monoclinic phase following heat treatment at 700 °C. The predominance of citric acid in the fuel composition reduces the synthesis temperature and the degree of crystallinity of the products under such conditions, as well as promoting the formation of the C-type phase.
In addition to the synthesis conditions, the formation of the C-type structure is affected by the weighted average ionic radius of the incoming cations [46]. An REO with a smaller cationic ionic radius than gadolinium crystallizes in the cubic C-type. The stability of the cubic structure of C-type for NdO1.5 is limited by a temperature of 590 °C, 860 °C for SmO1.5, and 1060 °C for EuO1.5. Based on the obtained data, inclusion in the composition of samples of rare earth element (REE) cations with a radius greater than that of gadolinium in an amount > 50 at. % prevents the formation of entropy-stabilized C-type oxides. In particular, a relative content of the Nd3+ cation in the crystal lattice of ESO samples in the range of 12.5–20% does not prevents the formation of a cubic structure. All samples of ESO-1—ESO-6 obtained in combustion reactions at a certain ratio of glycine and citric acid demonstrated a cubic structure after annealing at 700 °C, as well as retaining it after cooling. The change in the upper temperature limit of the region of existence of the C-type structure can be more accurately traced by the change in the volume of the crystal cell depending on the type of REE (Figure 1). The figure is constructed on the basis of data on the structural phase transitions of rare earth oxides [29,47] and unit cell volumes Vcr for cubic structures of REOs taken from the PDF-2 database (ICDD, 2016).
This dependence can be written by Equation (2) with reliability R2 = 0.9775:
T, °C = 0.0214Vcr2 − 62.737Vcr + 46390
The temperatures of the upper limit of stability of ESO samples with a C-type structure, calculated using Equation (2), are presented in Table 4.
The calculated transition temperatures C→B(H) are consistent with the data of X-ray diffraction analysis of the samples. As the X-ray phase analysis showed, only ESO-1-3, ESO-1-4, and ESO-3 samples retain the C-type structure up to 1250 °C (Figure 2), while, for the remaining ESO samples (Table 3), the upper stability temperature C-type structures appear below. For example, for ESO-2-3, the appearance of a monoclinic phase is observed already after annealing at 800 °C (Figure 3). The mass fraction of the C-type phase of ESO samples after annealing at 1250 °C is given in Table 3. As can be seen, the synthesis parameters (the ratio of glycine and citric acid) have a significant effect on the phase composition of ESO samples. We will consider these patterns in our next article.
There are no thermal effects that could be attributed to polymorphic transformations shown on the DSC curves of dispersed powders ESO-1-2 and ESO-2-3 on the heating and cooling curves in the range of 100–1250 °C (Figure 4a,b). It follows from this that cubic ESO-1-2 and ESO-2-3 are stable over a wider temperature range than the simple oxides of neodymium and samarium included in their composition. The appearance of an exo-effect on the DSC curve of the ESO-1-2 sample associated with the presence of a carbon impurity is explained below.
The X-ray diffraction data of a ceramic sample ESO-2-3 contradict the thermogram of the powder of this composition: it is two-phase after 1250 °C and contains 72 wt. % monoclinic phase (type B). It can be assumed that the sample does not have time to complete the C→B transition during thermal analysis (at a heating rate of 10°/min); however, in the ESO powders that underwent 7-h annealing in a furnace at 1250 °C, this process is completed. The two-phase nature of ESO-2-3 after cooling in a furnace also speaks in favor of a low rate of polymorphic transformation. After 7 h of annealing at 1250 °C, ceramic samples ESO-4, ESO-5, ESO-6 also decompose; however, in the first two, the amount of the monoclinic phase is small, while ESO-3 remains monophasic.
TG-DSC analysis of ESO samples obtained by the SCS method and annealed at 800 °C in air revealed the presence of impurities in an amount of 0.43–1.53 wt. %, which are removed upon heating (Table 5, Figure 5a–d). Similar effects were described by Shlyakhtina A.V. et al. [48] in their complex analysis (DSC–TG, XRF, IR and Raman spectroscopy) of obtaining ceramics Nd2O3+2HfO2 and Dy2O3-2HfO2. These were identified as decomposition products of basic REE carbonates and hydroxocarbonates in the range of 250–600 °C and of X-ray amorphous carbon in the range of 750–1200 °C [48]. In our opinion, the presence of exo-effects on the DSC curve in the range of 800–1250 °C confirms the oxidation of amorphous carbon formed from citric acid under combustion conditions.
On TG and DSC curves of samples ESO-3 and ESO-4 in the region 800–1100 °C (Figure 5a,b), the gravimetric curve fixes a weight gain (+ΔP) of 0.04–0.018% (Table 5). It can be assumed that this is due to the oxidation of either Sm2+ cations or REE carbides, whose formation is quite possible, since the ESO-3 and ESO-4 samples were obtained in a more reducing (as compared to other ESOs) medium (see Table 3).
Carbon impurities often present in the products of SCS reactions [43] due to various modifications can be oxidized or decomposed only at high temperatures [44]. These assumptions explain the observed exo-effects on the DSC curves of all ESO samples, whose heating is also accompanied by a decrease in mass (−ΔP) (Table 5).
Such interpretations of the results of thermal analysis are supported by an additional experiment performed by the authors. Figure 6 shows the results of TG—DSC analysis of sample ESO-1-4 after synthesis and annealing at 800 °C (blue and green lines) and repeated thermal analysis of sample ESO-1-4 after annealing at 1250 °C.
The powder can be seen to lose up to 0.41% following synthesis, annealing at 800 °C and storage in air; the thermogram shows a blurred exo-effect with a maximum at 1074 °C, which is accompanied by a significant weight loss in the amount of 1.6% up to 1200 °C. During cooling, there is no change in the mass of the sample and no thermal effects. Repeated DSC of this sample annealed at 1250 °C shows no weight loss and no corresponding thermal effects both on heating and on cooling. This proves the removal of volatile impurities and the absence of polymorphic transformations at a heating/cooling rate of 10 °C/min.

3.2. Ceramic Solid Solutions of Rare Earth Metal Oxides

Along with the heat treatment conditions on the microstructure and physical and mechanical properties of ceramics, the influence of the ESO composition was studied on samples of dense ceramics obtained by firing samples in the form of tablets at a temperature of 1250 °C. The indicators of relative density, open porosity, as well as the micro-structure and microhardness of ceramics were evaluated.
The morphology of the powders used to manufacture ceramics determines its sinterability and density. The particle size and distribution, as well as the presence and shape of agglomerates, have a significant effect on both the consolidation of the powder and the microstructure of the sintered ceramic. In turn, the powder morphology is determined by the SCS parameters. The gases released during the combustion reaction, as well as during annealing at 700 °C, when the carbon-containing fuel residues are decomposed, loosen the reaction mass. However, the presence of glycine in the fuel composition increases the duration of fire retention, leading to the formation of agglomerates in which the particles are chemically bonded to each other. As shown in Figure 7a–c, the powders have a submicron particle size (less than 1 µm) following annealing at 700 °C. During annealing of the ESO-1-4 and ESO-2-3 powders at 1250 °C, coarsening of particles is observed due to sintering of smaller particles; although their size still does not exceed 1 μm, the shape of the particles becomes rounded (Figure 7d,e). As in ESO-6-2, the observed agglomerates are larger and denser and more consolidated (Figure 7f). The agglomeration presence can lead to an uneven distribution of the packing density of powder particles in the compact and consequent inhomogeneous sintering of various pressing areas.
Studies of the microstructure of ceramic surfaces carried out under similar conditions for the preparation of both powders and tablets, show that ceramics from 6-cationic ESO-1-4 and ESO-2-3 are characterized by smaller particles in close contact with each other and with pronounced boundaries; these are uniform in shape and size from 0.2 to 1.4 µm (Figure 8a,b). With a decrease in the number of cations to 5 in a monophasic C-type structure ESO-3, the aggregate sizes increase (Figure 8c); however, an increase in the specific holmium cation content and a decrease in the amount of the Sm3+ cation in the ESO-4 crystal lattice gives the ceramics a denser packing and some reduction in grain size (Figure 8d). The disintegration of the monophasic sample ESO-6-2 after sintering at 1250 °C and the appearance of a significant amount of a phase with a monoclinic structure (Table 3) is accompanied by the formation of elongated particles and an increase in their size in length up to 3 µm (Figure 8f). As a result, the porosity of ceramics increases significantly (Table 6). In addition, the transition from low- and medium-entropy oxides (ESO-6, ESO-3) to high-entropy oxides (ESO-1, ESO-2) correlates with an increase in the relative density of samples upon pressing (Table 6).
The resulting samples of ESO ceramics are characterized by microhardness values in the range from 2.6 to 5.7 GPa (Table 6), whose fluctuations are mainly due to differences in the microstructure of the samples. The microhardness of ceramics obtained by the same method is determined both by a smaller average particle size of the initial powder (as in the case of ESO-1-4 and ESO-2-3) and a higher sintering process intensity (ESO-5). In addition, a correlation between the ceramic microhardness and its relative density is recorded (Table 6). The highest values of microhardness were found in high-entropy samples ESO-1 (monophase) and ESO-2 (dual phase). While it is generally accepted that high-entropy ceramics should be principally single phase, dual-phase high-entropy ceramics are recently included in this family of materials [42].

4. Conclusions

Six mixed, entropy-stabilized REOs were obtained by SCS reactions with glycine and citric acid. By replacing glycine with citric acid to reduce the temperatures of the synthesis process, it becomes possible to obtain solid solutions of oxides of neodymium, europium, samarium, gadolinium, dysprosium, and holmium in the C-type crystal structure after annealing at 700 °C. It has been established that the maximum temperatures of the polymorphic transformation of 4-, 5- and 6-cationic ESOs, as well as those of simple REOs, increase with a decrease in the volume of the elementary crystal lattice and can be described by a second-degree equation. The obtained data on X-ray phase and DSC analysis of dispersed ESOs indicate a low rate of mutual polymorphic transformations of polycationic oxides C ↔ B(H).
Dispersed ESOs are prone to sorption of water vapor during storage with the formation of hydroxides, carbonates, hydroxocarbonates. Under reducing conditions, SCS is accompanied by the formation of carbon impurities or rare earth metal carbides in low-entropy ESOs, as well as, presumably, by partial reduction of Sm3+ cations to Sm2+. Ceramic ESOs with a C-type structure with 6 cations in the crystal lattice form denser samples compared to 4-cation and composite oxides. The microhardness of the ceramic also increases when increasing the number of heavy rare earth elements in the composition of the ESO.

Author Contributions

Conceptualization, data curation, project administration, supervision, writing—original draft, and writing—review and editing, V.Z.; formal analysis, investigation, methodology, visualization, writing—original draft, and writing—review and editing, L.E.; formal analysis, investigation, methodology, visualization, and writing—review and editing, R.S.; formal analysis, investigation, and methodology, A.E. All authors have read and agreed to the published version of the manuscript.

Funding

This research received no external funding. The work was carried out in accordance with the state assignment and R&D plans of ISSC UB RAS: AAAA–A19–119031890026–6 and AAAA-A19-119031890025-9.

Conflicts of Interest

The authors declare no conflict of interest.

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Ceramics 06 00060 g001 550
Figure 1. Dependence of the change in the temperatures of the C→B(H) rare earth metal oxide polymorphic transition on Vcr.
Figure 1. Dependence of the change in the temperatures of the C→B(H) rare earth metal oxide polymorphic transition on Vcr.
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Ceramics 06 00060 g002 550
Figure 2. In situ X-ray diffraction patterns of the ESO-1-4 sintered at various temperatures.
Figure 2. In situ X-ray diffraction patterns of the ESO-1-4 sintered at various temperatures.
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Figure 3. In situ X-ray diffraction patterns of the ESO-2-3 sintered at various temperatures.
Figure 3. In situ X-ray diffraction patterns of the ESO-2-3 sintered at various temperatures.
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Figure 4. DSC and TG heating and cooling curves of: (a) ESO-1-2 and (b) ESO-2-3.
Figure 4. DSC and TG heating and cooling curves of: (a) ESO-1-2 and (b) ESO-2-3.
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Figure 5. DSC and TG heating and cooling curves of: (a) ESO-3, (b) ESO-4, (c) ESO-5, and (d) ESO-6-2.
Figure 5. DSC and TG heating and cooling curves of: (a) ESO-3, (b) ESO-4, (c) ESO-5, and (d) ESO-6-2.
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Figure 6. DSC and TG heating and cooling curves of ESO-1-4 after synthesis and annealing at 800 °C (blue and green curves) and after annealing at 1250 °C (red and orange curves).
Figure 6. DSC and TG heating and cooling curves of ESO-1-4 after synthesis and annealing at 800 °C (blue and green curves) and after annealing at 1250 °C (red and orange curves).
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Figure 7. SEM images of the morphology of powder samples sintered at 700 and 1250 °C, respectively: (a,d) ESO-1-4, (b,e) ESO-2-3, and (c,f) ESO-6-2.
Figure 7. SEM images of the morphology of powder samples sintered at 700 and 1250 °C, respectively: (a,d) ESO-1-4, (b,e) ESO-2-3, and (c,f) ESO-6-2.
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Figure 8. SEM images of the surface morphology of the ceramic samples sintered at 1250 °C: (a) ESO-1-4, (b) ESO-2-3, (c) ESO-3, (d) ESO-4, (e) ESO-5 and (f) ESO-6-2.
Figure 8. SEM images of the surface morphology of the ceramic samples sintered at 1250 °C: (a) ESO-1-4, (b) ESO-2-3, (c) ESO-3, (d) ESO-4, (e) ESO-5 and (f) ESO-6-2.
Ceramics 06 00060 g008aCeramics 06 00060 g008b
Table
Table 1. Binary REOs with the C-type crystal structure.
Table 1. Binary REOs with the C-type crystal structure.
Compounda, ÅRefs.
Ce0.55Eu0.45O1.77510.885(1)[34]
Ce0.50Eu0.50O1.7510.886(3)
Ce0.45Eu0.55O1.72510.886(8)
Ce0.40Eu0.60O1.7010.886(1)
Ce0.30Eu0.70O1.6510.887(1)
Ce0.25Eu0.75O1.62510.886(1)
Ce0.20Eu0.80O1.6010.884(2)
Ce0.10Eu0.90O1.5510.883(6)
Ce0.50Sm0.50O1.7510.914(1)
Ce0.40Sm0.60O1.7010.917(2)
Ce0.30Sm0.70O1.6510.920(2)
YO1.510.604(1)[35]
Ce0.50Gd0.50O1.7510.862(2)[36,37]
Ce0.40Gd0.60O1.7010.854(3)
Ce0.30Gd0.70O1.6510.855(1)
Ce0.20Gd0.80O1.6010.849(1)
Ce0.15Gd0.85O1.57510.838(1)
Ce0.10Gd0.90O1.5510.837(1)
Ce0.05Gd0.95O1.52510.831(1)
[(Y1-xGdx)0.99Dy0.01]2O3 (x = 0 and 0.4)10.483–10.567[9]
Table
Table 2. Multicomponent solid solutions of REE oxides.
Table 2. Multicomponent solid solutions of REE oxides.
Compounda, ÅT, °CRefs.
Ce1/3La1/3 Nd1/3Pr1/3Sm1/3Y1/3O3.1610.9652(2)1000[38]
Ce1/3Gd1/3 Nd1/3Pr1/3Sm1/3Y1/3O3.1610.9319(3)[38]
Ce0.4La0.4 Pr0.4Sm0.4Y0.4O3.210.9957(8)1000[38]
Gd0.4Tb0.4Dy0.4Ho0.4Er0.4O310.66029(8)1200[39]
Ce0.4La0.4Pr0.4Sm0.4Y0.4O310.919[39]
Ce0.5La0.5Sm0.5Y0.5O3,2510.961[39]
Yb0.118Lu0.464Y1.418O310.538180[5]
Ce2/3Gd2/3La2/3O3.3311.0381400[39]
Table
Table 3. Preparation conditions, composition and weighted average ionic radius of rare earth cations, rav.
Table 3. Preparation conditions, composition and weighted average ionic radius of rare earth cations, rav.
ESOCompositionFuelPhase C-Type, wt. %rav, Å
[45]
φglφcitr700 °C1250 °C
1-1Nd0.25Sm0.25Eu0.25Gd0.25Dy0.5Ho0.5O30.90.182.7 0.9313
1-20.80.292.2
1-30.50.5100100
1-40.40.5100100
2-1Nd0.5Sm0.5Eu0.25Gd0.25Dy0.25Ho0.25O30.70.37.6 0.9475
2-20.50.610025.6
2-30.50.210028.0
2-40.40.610021.9
3Nd0.4Sm0.3Gd0.4Dy0.5Ho0.4O30.40.51001000.9355
4Nd0.4Sm0.2Gd0.4Dy0.5Ho0.5O30.40.599.498.30.9325
5Nd0.4Sm0.4Gd0.4Dy0.4Ho0.4O30.40.598.299.40.9380
6-1Nd0.5Sm0.5Gd0.5Dy0.5O30.40.527.5 0.9475
6-20.50.610022.4
6-30.40.610040.4
Table
Table 4. Temperatures of polymorphic transitions C→B(H) for ESOs.
Table 4. Temperatures of polymorphic transitions C→B(H) for ESOs.
ESOCompositiona, ÅT, °C
C→B(H)
1-4Nd0.25Sm0.25Eu0.25Gd0.25Dy0.5Ho0.5O310.787(1)1313
2-3Nd0.5Sm0.5Eu0.25Gd0.25Dy0.25Ho0.25O310.881(1)993
3Nd0.4Sm0.3Gd0.4Dy0.5Ho0.4O310.795(1)1282
6-3Nd0.5Sm0.5Gd0.5Dy0.5O310.878(1)1002
Table
Table 5. ESO weight change during thermal analysis.
Table 5. ESO weight change during thermal analysis.
ESOComposition−ΔP, %ΔT, °C+ΔP, %Exo-Effect Temperature T, °C
1-2Nd0.25Sm0.25Eu0.25Gd0.25Dy0.5Ho0.5O30.920–1100 1154; 1205
1-40.8520–1250 1074; 1197
2Nd0.5Sm0.5Eu0.25Gd0.25Dy0.25Ho0.25O30.9920–1025
3Nd0.4Sm0.3Gd0.4Dy0.5Ho0.4O30.5220–8000.18953; 1163
4Nd0.4Sm0.2Gd0.4Dy0.5Ho0.5O30.4320–8000.04856; 1101
5Nd0.4Sm0.4Gd0.4Dy0.4Ho0.4O30.8820–1250 1246
6-2Nd0.5Sm0.5Gd0.5Dy0.5O31.5320–1250 996; 1092
Table
Table 6. Density ρ, porosity ϕ and microhardness of ESO ceramics.
Table 6. Density ρ, porosity ϕ and microhardness of ESO ceramics.
ESOComposition ρ, %ϕ, %Hv, GPa
1-3Nd0.25Sm0.25Eu0.25Gd0.25Dy0.5Ho0.5O379.920.13.5
1-492.67.45.1
2-2Nd0.5Sm0.5Eu0.25Gd0.25Dy0.25Ho0.25O375.924.14.4 *
2-392.27.85.3 *
3Nd0.4Sm0.3Gd0.4Dy0.5Ho0.4O371.928.14.5
4Nd0.4Sm0.2Gd0.4Dy0.5Ho0.5O364.835.22.6
5Nd0.4Sm0.4Gd0.4Dy0.4Ho0.4O378.421.65.7
6-2Nd0.5Sm0.5Gd0.5Dy0.5O369.031.03.1 *
6-369.730.33.8 *
*—mixture of cubic and monoclinic phases.
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Zhuravlev, V.; Ermakova, L.; Samigullina, R.; Ermakov, A. Preparation and Mechanical Characteristics of Multicomponent Ceramic Solid Solutions of Rare Earth Metal Oxides Synthesized by the SCS Method. Ceramics 2023, 6, 1017-1030. https://doi.org/10.3390/ceramics6020060

AMA Style

Zhuravlev V, Ermakova L, Samigullina R, Ermakov A. Preparation and Mechanical Characteristics of Multicomponent Ceramic Solid Solutions of Rare Earth Metal Oxides Synthesized by the SCS Method. Ceramics. 2023; 6(2):1017-1030. https://doi.org/10.3390/ceramics6020060

Chicago/Turabian Style

Zhuravlev, Victor, Larisa Ermakova, Rina Samigullina, and Alexey Ermakov. 2023. "Preparation and Mechanical Characteristics of Multicomponent Ceramic Solid Solutions of Rare Earth Metal Oxides Synthesized by the SCS Method" Ceramics 6, no. 2: 1017-1030. https://doi.org/10.3390/ceramics6020060

APA Style

Zhuravlev, V., Ermakova, L., Samigullina, R., & Ermakov, A. (2023). Preparation and Mechanical Characteristics of Multicomponent Ceramic Solid Solutions of Rare Earth Metal Oxides Synthesized by the SCS Method. Ceramics, 6(2), 1017-1030. https://doi.org/10.3390/ceramics6020060

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