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Article

The Structural and Phase State of the TiAl System Alloyed with Rare-Earth Metals of the Controlled Composition Synthesized by the “Hydride Technology”

by
Akbayan Belgibayeva
1,2,*,
Yuri Abzaev
1,3,
Natalia Karakchieva
1,
Rakhmetulla Erkasov
2,
Victor Sachkov
1 and
Irina Kurzina
1
1
Chemical Technology Laboratory, National Research Tomsk State University, Lenin 36, 634050 Tomsk, Russia
2
Department of Chemistry, Eurasian National University, Kazhymukan 13, Nur-Sultan 010008, Kazakhstan
3
Material Research Centre for collective use, Tomsk State University of Architecture and Building, Solyanaya 2, 634003 Tomsk, Russia
*
Author to whom correspondence should be addressed.
Metals 2020, 10(7), 859; https://doi.org/10.3390/met10070859
Submission received: 30 May 2020 / Revised: 16 June 2020 / Accepted: 22 June 2020 / Published: 29 June 2020
(This article belongs to the Special Issue Casting and Solidification of Light Alloys)
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Abstract

The structural state and the quantitative phase analysis of the TiAl system, alloyed with rare-earth metals synthesized using hydride technology, were studied in this work. Using the Rietveld method, the content of the major phases in the initial system Ti(50 at.%)–Al(50 at.%), as well as Ti(49 at.%)–Al(49 at.%), with alloying additions Ta, Y and Dy having a high accuracy was determined. The methods of scanning electron microscopy, transmission electron microscope and X-ray spectral microanalysis of the local areas of the structure for studying the distribution of alloying elements were used. The energies of lattices of separate phases were also determined after the full-profile specification. All the lattices of the identified structures (about 30) turned out to be stable. It was established that in the Ti(49 at.%)–Al(49 at.%) systems under study with alloying additions of metals Ta, Y and Dy, there were intermetallides composed of AlTi3, TiAl in the hexagonal, tetragonal and triclinic units. It is known that after microalloying alloys by Y and Dy metals, the mass fraction of TiAl phases increases significantly (>70%).

1. Introduction

Intermetallic alloys based on γ-TiAl are a good example of the way basic and applied research along with industrial development can lead to obtaining a new innovative class of advanced structural materials [1,2,3,4]. Nowadays, intermetallic alloys based on the γ-TiAl phase are promising materials for application in aeronautical engineering, owing to their attractive properties: high specific strength, stiffness, creep resistance at temperatures of T = 600–800 °C, oxidation resistance and burn resistance at temperatures up to T = 900 °C. In the temperature range of T = 20–800 °C, the specific modulus of elasticity of these alloys is higher than that of the nickel by 30–50% [2]. It is supposed that in the gas-turbine engine, light γ-TiAl alloys (ρ ≈ 4 g/cm3) will partially replace heat-resisting heavy nickel alloys (ρ = 8–8.5 g/cm3), which will allow significant increases in its specific power characteristics during a simultaneous decrease in the fuel consumption, carbon dioxide emissions and nosiness [4].
To achieve a certain combination of properties, it is necessary to optimize the chemical composition and the microstructure [4,5,6,7,8]. Therefore, in the past two decades, the increased focus of researchers of γ-TiAl alloys has been on achieving an optimal combination of mechanical properties by varying the elemental composition and the microstructure with various sizes of columns/grains and thickness of plates. For that, a detailed work on the optimization of the composition and conditions of thermomechanical/thermal treatment of the alloys is being performed.
In modern materials science, a new method of synthesis of binary and multicomponent alloys is of interest, which is called a “hydride” technology (HT) [9]. Modern technologies of production of alloys (mechanical alloying, arc smelting, powder metallurgy, etc.,) are associated with notable labor intensity and hardware difficulties (application of a deep vacuum and creation of inert environment at high temperatures, duration and multiplicity of processes, etc.). The powder metallurgy technique is characterized by a special duration because the result of the interaction of metals in the initial mixtures is mainly determined by solid diffusion rates. The specific difficulties of obtaining quality alloys are also associated with the presence of a dense oxide film on the surfaces of particles of refractory metals, which prevents the passage of mutual diffusion. The HT method allows the avoidance of the majority of them (in particular, it excludes melting). HT is a high-tech method based on the combination of self-propagating high-temperature synthesis SHS of transition metal hydrides and heat treatment of a mixture of hydrides, resulting in alloy formation [10,11,12]. In the HT method, to obtain high-strength alloys based on transition metals, the powders of hydrides of refractory metals and alloys are used as initial materials. The essence of HT consists of the successive use of processes of hydrides synthesis, their combined compacting and dehydration. The advantage of HT is that the alloy is formed at a relatively low temperature (from 900 to 1150 °C) during rapid exposition (from 1 to 2 h). It is important that metals with different values of melting temperature and density should alloy without melting [10,11,12]. Other advantages of the method are relative cheapness, the use of refractory materials, as well as obtaining materials with high purity. It is also known that the formation of metal alloys can be carried out easier from hydrides than from metals themselves, since chemical bonds in hydrides are less strong than bonds in metal structures [11,12].
It is well known that the compaction of the alloy structure is one of the most effective ways of improvement of strength and plasticity of the materials. Alloying was demonstrated as a viable approach to enhance the mechanical properties of TiAl alloys at room temperature through improving the materials microstructure [13,14].
To improve the mechanical properties of γ-TiAl alloys, their alloying with rare-earth elements is of interest. It is known that [15,16,17] the introduction of rare-earth elements (La, Er and Dy) into titanium and intermetallic alloys based on γ-TiAl can lead to the improvement in machinability in the as-cast state, owing to refinement of the structure, to increased heat-resistance and refractoriness, and in the γ-TiAl alloys, in some cases, to the enhancement of the technological plasticity at elevated temperatures.
Previous studies supposed that the addition of yttrium [18] and gadolinium [19,20,21,22] could significantly reduce the grain sizes and lamellar spaces of TiAl alloys, enhance strength and plasticity at room temperature, as well as creep resistance at high temperatures. However, the mechanisms of microstructure refinement in the rare-earth metals-modified (REM-modified) TiAl alloys were studied insufficiently because of the complex succession of solidification and solid-phase transformations of TiAl during thermal treatment and cooling [23]. Systematic data on the influence of additions of rare-earth elements on the structure and mechanical properties of γ-TiAl alloys in the literature are practically not presented.
Thus, the development of the methods for producing high-strength alloys of the TiAl system, the study of the dependence of the structural phase state on the synthesis parameters, and the study of the effect of various modifying additives on the physical and mechanical properties is an actual task.
The purpose of the present work is the development of the basics of hydride technology for the production of TiAl alloys and the study of the influence of alloying additions Ta, Y and Dy on the microstructure and the phase composition of the titanium–aluminum system obtained by the HT method. The Ti(50 at.%)–Al(50 at.%) system has been accepted as a basis of the composite material with REM additions of no more than 2 at.%.

2. Materials and Methods

2.1. Obtaining Alloys

Samples with the following selected atomic compositions were prepared TA (TiAl); TAT (TiAlTa); TAY (TiAlY); TAD (TiAlDy). Sample TA was prepared as follows: a weighed amount of the titanium was placed in a quartz boat and heated in a furnace (Nabertherm RS 120/750/13, Lilienthal, Germany) in a stream of the hydrogen. The heating rate of the furnace was 10 °C/min to 450 °C, with a hydrogen volume flow of 500 mL/min.
This sample was cured for 3 h at this temperature; after that, it was cooled down to room temperature. The obtained metal hydrides were mixed with a nanodispersed aluminum powder (the average size of particles was 115 ± 10 nm, specific surface area—19.4 ± 3 m2/g, loading of active aluminum—80.8 ± 0.6%). Then, the mixture was pressed into a round plate and was formed (collapsible compression mold, Lab Tools, diameter of 13 mm, thickness of 2 mm), pressing load was under a pressure of 5.3 tons/sm2, bulk density was 3 g/sm3 (Lab Tools PAH-20, 2019, St. Petersburg, Russia)). The equation for obtaining the TA sample can be written as:
Ti + H2 = TiH2 + 27.3 kcal/mole
The TAT sample was prepared as follows: a weighed amount of the tantalum was placed in a quartz boat and heated in a furnace (Nabertherm RS 120/750/13, Lilienthal, Germany) in a stream of the hydrogen. The heating rate of the furnace was 10 °C/min to 550 °C, with a hydrogen volume flow of 500 mL/min. This sample was cured for 3 h at this temperature; after that, it was cooled down to room temperature. The equation for the production of titanium hydride can be written as:
2Ta + H2 = 2TaH + 56 kcal/mole
Titanium hydride was obtained as in the case of sample TA. Then, the obtained titanium hydride and tantalum hydride were mixed with a nanodispersed aluminum powder (according to the manufacturer, the average size of the particles was 115 ± 10 nm, specific surface area—19.4 ± 3 m2/g, loading of active aluminum—80.8 ± 0.6%). Then, the mixture is pressed similar to TA.
Samples of TAY and TAD were obtained similarly to the method of obtaining TAT. The temperature for yttrium hydride and dysprosium hydride was 420 °C. The equation for obtaining a TAY sample can be written as:
Y + H2 = YH2 + 56 kcal/mole
2Y + 3H2 = 2YH3 + 21.5 kcal/mole
The equation for the preparation of dysprosium hydride can be written as:
2Dy + 3H2 = 2DyH3
The obtained sample blanks were obtained in a vacuum unit and heated to a temperature of 1150 °C, with a heating rate of 2 °C/min. The vacuum value was 10−4 atm. They were maintained under these conditions for 3 h and cooled at a rate of 5 °C/min.
The equations for obtaining samples TA, TAT, TAY and TAD can be written as:
TiH2 + Al = TiAl + 2H2↑
2TiH2 + 2Al + 2TaH = 2TiAlTa + 3H2↑
TiH2 + Al + YH2 = TiAlY + 2H2↑
2TiH2 + 2Al + 2DyH3 = 2TiAlDy + 5H2↑

2.2. Research Methods

The structural state and the quantitative phase analysis of the system TiAl-alloying metal (TA-REM), synthesized by HT, were studied in this work by the Rietveld method and scanning electron microscopy (SEM) [24,25]. Ta, Y and Dy metals were used as alloying additions. The X-ray diffraction studies of the TA-REM system were undertaken using DRON4-07 (Bourevestnik, St. Petersburg, Russia), which was modified for the digital processing of the signal. Spectra were made using copper radiation (Ka) according to the Bragg–Brentano scheme with an increment of 0.02°, exposure time at a point of 1 sec and in the angle range of 10–86°. The voltage on the X-ray tube was 30 kV, beam current—25 mA. The structural state and the quantitative content of the phases were identified by the Rietveld method by means of reflex [26,27,28,29]. As the standard lattices, the crystallographic data of the COD base [26] and the model structures of the TiAl system, predicted by the program code USPEX with the interface shell SIESTA [30], were used. In connection with the promising physicochemical properties of the TiAl systems, they were alloyed with metal additions [24,25,26,27,28,29,30,31,32,33,34]. In this work, the search for standards of the TiAl system was supplemented by the USPEX program with the outer shell SIESTA [31,35,36].
To study the distribution of alloying elements in the structure at the local level, the quantitative X-ray spectral microanalysis of the near-surface layer, accompanied by the analysis of the microstructure and the morphology of the surface by the method of scanning electron microscopy, was carried out using the X-ray fluorescence spectral analyzer S4 Pioneer (Bruker, Karlsruhe, Germany) and the raster electron microscope “LEOEVO 50” (Zeiss, Oberkochen, Germany).
Electron microscope studies of the surface microstructure of TA-REM samples were conducted using the transmission electron microscope “JEM-2100F” (JEOL, Tokyo, Japan) with accelerating voltage of 200 kV using the attachment “JEOL” (JEOL, Tokyo, Japan), intended for energy-dispersive spectral analysis. The phases were identified applying well-known procedures using schemes of microdiffraction patterns calculated by the table values of parameters of crystalline lattices.

3. Results and Discussion

The USPEX-SIESTA program by means of the evolution code can predict stable structures of the known elemental composition, space group, among which the structures with the global minimum of enthalpy of the system are predicted. In the present work, the TiAl structures were used for the quantitative phase analysis. For the discovered structures (about 30) based on complete structural information, the energies of lattices were calculated proceeding from the first principles. All the lattices turned out to be stable and they were used at the next stage for qualitative and quantitative phase analysis by the Rietveld method. In Table 1, Table 2, Table 3, Table 4 and Table 5, there are standards in the initial state, obtained from the COD base (AlTi3, AlTi), as well as the structure predicted by means of the USPEX code (TiAl-Struct2, AlTi3-2768). For the alloy with the conventional designation TiAl-Struct2, AlTi3-2768, the energy was calculated in the framework of the electron density functional by the gradient pseudo potential of electron density (GGA). The details of the code are given in the work of reference [26]. The total energy of the lattices was determined at 0 K. Wave functions of valence electrons of TiAl-Struct2 atoms were analyzed on the basis of flat waves with a cutoff radius of kinetic energy of 330 eV. In this case, the convergence of the total energy was ~ 0.5 × 10−6 eV/atom. It was established that the lattice energy after geometric optimization turned out to be equal to ETiAl-Struct11 = −4978.555 eV, and in the initial state −4976.099 eV. The final enthalpy of the TiAl-Struct2 structure in both cases is evidence of its stability. TiAl lattices (AlTi3-2768) with Y, Ta and Dy additives (Table 2, Table 3 and Table 4) also turn out to be stable, and the lattice energies are substantially negative. In this work, based on the results of the qualitative phase analysis of the TA-REM system, it was suggested that the REM nanoadditions were embedded into the interstitial site [0.5 0.5 0.5] of the lattice of the AlTi3 alloy. Quantum chemical calculations of the AlTi3 energy in the initial state, as well as with the embedded nanoadditions in the mentioned site, were made. It was established that: EAlTi3 = −19,318.285 eV; EAlTi3-Y = −19,712.792 eV; EAlTi3-Ta = −19,613.620 eV; EAlTi3-Dy = −31,227.561 eV.
The calculations are evidence of the fact that the introduction of the alloying metals into the indicated interstitial site is possible and it leads to the significant stabilizing effect of the lattices in each TA-REM system without exception. In fact, the binding energy of (|EAlTi3|) atoms in the lattices accompanied by the addition of the alloying metal increased significantly. It is interesting to note that the increase in the binding energy is accompanied by significant polarization of the Millikan charges [37,38]. The Millikan charges in the metal additions are equal: [(−5.96)Y], [(−4.42)Ta], [(+0.73)Dy], but on the atoms of the main elements—[(−0.16)Al, (+1.540)Ti], [(−0.35)Al, (+1.22)Ti], [(−0.13)Al, (−0.12)Ti], [(−0.17)Al, (−0.13)Ti] in ternary compounds TAT, TAY and TAD, respectively. The analysis of distances between atoms of the main elements and additions showed that these distances were significantly less than the sum of the covalent radii of free elements Ti and Al, and Ta, Y and Dy, which are equal, respectively, to 1.6, 1.21, 1.7, 1.90, 1.92Å [39]. For instance, in the TAT system, the lengths of bonds TiTa and AlTa are equal to 2.030 and 2.031 Å, respectively. Polarization of the charges is indicative of the growth in the share of the covalent bond as a result of introduction of the alloying metals.
The results of the quantitative content of phases in the studied systems are given in Table 1, Table 2, Table 3 and Table 4. The tables show the phases, the structural state of the phases before (Init) and after (Spec) the Rietveld refinement of the experimental diffractograms, the corresponding lattice parameters, the lattice volume (V), the space group, the fraction of the individual phases (Share) and the lattice energy after refinement by the Rietveld method (E). The tables also show the fraction of the calculated integrated intensity (Rwp) in the experimental diffractogram. The analysis of the contributions into the integral intensity of separate phases (Table 1, Figure 1) showed that to a high degree of reliability (Rwp < 7.2%), the major phases were intermetallides AlTi3, AlTi3-REM, AlTi and TA-Struct2 in the initial and optimized states. The experimental diffraction patterns of the TA, TAT, TAY and TAD systems can be approximated well by the calculated integral intensity; the difference between them is an insignificant value (Figure 1). However, as Table 1, Table 2, Table 3 and Table 4 show, the contributions of separate phases differ in different systems. Using the Rietveld method, it is established that in the TA system, the contribution of the triclinic TiAl system (over 73%) predominates. Both lattices differ by parameters, atoms coordinates, as well as the volume (Table 1). The number of the main systems also includes the hexagonal lattice of AlTi3 (22.33%). The introduction of an insignificant amount of Ta, Y and Dy leads to the redistribution of the contributions of the hexagonal and triclinic systems. In the TA-REM systems, the contribution of the geometrically optimized lattice (TA-Struct2-GeomOpt) disappears, and the phase with the AlTi tetragonal lattice appears (Table 2, Table 3 and Table 4). The introduction of Ta into the AlTi3 lattice significantly increases its binding energy and stimulates the contribution to the integral intensity up to 26.99%. On the contrary, in the TAY and TAD systems, additions Y and Dy lead to the reduction in the share of AlTi3 to 16.66, 4.78 and 11.20%, respectively. The share of phases and the energy of the lattices allow evaluation of the effective energy of the TA, TAT, TAY and TAD systems according to the formula αE1+βE2+γE3, where α, β, γ—the share of phases; E1, E2, E3—the energy of the lattices of separate phases. It was established that the energies of the mentioned systems were equal to −7907.453, −5407.31, −7341.104, −21,188.219 and −15,920.023 eV, respectively.
The relative coordinates of the atoms and isotropic parameters of displacements are given in Table 5 and Table 6). The lattice parameters and space group are shown in Table 1, Table 2, Table 3 and Table 4.
Figure 2 shows the results of the observed and calculated intensities of the initial alloy and alloys obtained by doping with rare-earth metals. X-ray phase analysis of the samples obtained by doping with rare-earth metals showed that they have a complex multiphase structure: the initial components (Ti, Al) and the new phases—intermetallic phases AlTi3, AlTi3–REM, AlTi, TiAl-Struct2—in the initial and optimized states were identified.
The study of the microstructure showed that the base of the material was the alloy of titanium and aluminum with a small quantity of alloying metals (no more than 2 at.%). The ratio between the atomic concentrations of Al and Ti is close to the initial 1:1 (Figure 3). The spectra of characteristic X-ray radiation are also given in Figure 3.
As a result of the quantitative analysis, it was established that the matrix of the TAY alloy on average had a composition in mass percent: 29.60% of Al and 68.35% of Ti, which corresponds to the intermetallide phase α2-Ti3Al according to the stoichiometric ratio (Figure 3a). The elemental analysis of the TAT and TAD alloys (Figure 3b,c) also revealed the presence of titanium aluminide α2-Ti3Al. This agrees with the results obtained in the works [40,41]. It was established that the microstructure of the rest of the alloys was also characterized by the formation of the α2-Ti3Al intermetallide.
The choice of these metals as alloying microadditions in the alloys under study is conditioned by a number of positive effects. In particular, metals as an effective modifier of the cast structure [15,16,17,18,19,20,21,22] possess an increased affinity with oxygen, which in turn leads to a substantial decrease in the amount of oxygen in the alloy and, as a consequence, to an increase in low-temperature plasticity because of the reduction in the number of barriers in the form of oxygen atoms, which decelerate the dislocations motion during deformation.
The X-ray phase analysis results of the initial intermetallic alloy TA showed that the basic thermodynamically stable phases were intermetallide compounds Ti3Al, TiAl, TiAl2 and a solid aluminum solution in titanium α-Ti (Table 7).
A small fraction of the sample consists of the following intermediate phases having practically constant chemical compositions: Ti5Al11, Ti3Al5, TiAl2, Ti2Al5. The X-ray phase analysis (XPA) results are confirmed by TEM studies. The TEM studies showed that, before the introduction of rare-earth metals, in the initial state, the TA alloy contained phases Ti3Al, TiAl, TiAl2, α-Ti, Ti5Al11 and Ti3Al5 (Figure 4e). Consequently, the obtained TA alloy has a complex multiphase structure, as it contains a number of phases with different crystal lattices. This fact confirms a possibility of obtaining intermetallic alloys by hydride technology.
First of all, the obtained studies of the microstructure confirmed the formation of Ti3Al and TiAl phases. The Ti3Al phase is an ordered phase with a D019 superstructure having an HCP crystal lattice; its space group is P63/mmc. Ti3Al is formed as parallel lamellar precipitates (Figure 4a). The intermetallide Ti3Al and TiAl phases under formation are microdimensional, which is evident owing to the dark-field images (Figure 4c,d). The presence of Ti3Al and TiAl is associated with thermodynamics of the phases’ formations. The formation of these phases is characterized by a minimum of Gibbs energy [42]. The existence of these intermetallide phases must result in significant alloy strengthening [6,43,44].
A layer-by-layer location of intermetallide phases—that is, alternation by the composition—is possible. Thus, using hydride technology allows for obtaining of complex sandwich structures. Owing to alternation of intermetallide phases, it becomes possible to obtain super strong materials, where each layer strengthens the previous one.
To predict the composition of the formed phases when microalloying the TiAl alloys with rare-earth metals, ternary diagrams of the corresponding ternary systems were considered. The analysis of the TiAlY ternary diagram of the partial isothermal cross-section at 1000 °C shows that the content of the Ti:Al:Y = 49:49:2 components corresponds to the highlighted area of formation of γ-TiAl + YAl2 phases (Figure 5). The ternary diagram of the TiAlTa system at 1100 °C implies that at a ratio of Ti:Al:Ta = 49:49:2 components the TiAl phase is formed (Figure 5c). According to the ternary diagram, TiAlDy at a ratio of components Ti:Al:Dy = 49:49:2, the formation of the area, where DyAl2 + TiAl phases are present, can be expected (Figure 5b).
The X-ray phase analysis of the samples, obtained during alloying with yttrium, is given in Table 8.
According to the XPA data, the TAY alloy contains the basic Ti3Al5 phase. The Ti3Al5 phase has a rhombic crystal lattice and the space group P/mmm. Along with the Ti3Al5 grains, the structure of the alloy contains a small number of grains of the Ti3Al phase, having an HCP crystal lattice and the space group P63/mmc. A small fraction belongs to phases TiAl, Al, α-Ti and Y.
Figure 6 presents electron microscope images of the TAY alloy. On the microdiffraction pattern (Figure 6b), there are reflexes belonging to planes (110) and (201) TiAl; (101), (200), (302), (411) Ti3Al; (400) Ti3Al5; (311) YAl2; (100) α−Ti; (200) Al. Thus, the XPA results are confirmed by TEM.
Figure 7 presents TEM images of the depositions of yttrium particles of different shapes inside the grain of titanium aluminide. According to the TEM results, yttrium and Al form the YAl2 intermetallide in intermetallide phases and are located on dislocations or on grain boundaries.
The X-ray phase analysis of the samples obtained when alloying with dysprosium (TAD) and tantalum (TAT) showed that these alloys had a complex multiphase structure: initial components Al, α-Ti and new phases—intermetallide phases TiAl, Ti3Al, Ti5Al11, Ti3Al5—were identified (Table 9). The basic phase of the TAD alloy is the TiAl phase, which has an ordered tetragonal-distorted face-centered structure and the P4/mmm space group.
The results of the X-ray phase analysis of the TAT alloy showed that in the alloy, the main share belonged to intermetallide phases: 30.1% of titanium aluminide TiAl of tetragonal syngony with the space group P4/mmm; 22.9% of the Ti3Al phase, having a space-centered lattice of tetragonal syngony with the space group P63/mmc; 26.4% of the Ti3Al5 phase with the space group P/mmm (Table 9). The smallest share belongs to 1.9% of Ti2Al5 with the space group P4/mmm and 3.9% of Ti5Al11 with the space group P/mmm. In addition, the intermetallide of tantalum and aluminum (Ta161,8Al282,2) is present in the sample.
The results of the X-ray phase analysis of the TiAlDy alloy are confirmed by the TEM results (Figure 8). On the microdiffraction pattern there are reflexes belonging to planes (002), (004), (402), (413) TiAl; (600), (203) and (423) Ti3Al; (312) TiAl2; (008) Ti5Al11; (511) Al; (300) α-Ti; (551) DyAl2.
Figure 9 shows the electron microscope images of the TAT alloy. According to the microdiffraction analysis in the layers of the TAT alloy, there are the following intermetallide phases with reflexes belonging to planes (312), (412) TiA; (110), (402) and (210) Ti3Al; (311), (440) Ti3Al5; (314) Ti5Al11; (103) α-Ti; (008) and (215) TaAl3.
Thus, the TEM studies confirmed the formation of a number of phases of titanium aluminide. The tantalum compounds indicated by the XPA method probably remain in the volume of the sample, but only TaAl3 is present in the film structure.
As Ti and Ta have significant solubility in Al, Ta can form a solid substitutional solution in titanium and contribute to formation of the Widmanstatten microstructure. In addition, it is well known that the TaAl system also dissolves Ti (Ti aluminide) by as much as 60 at.%. Aluminides TiAl and Ti3Al dissolve Ta (Ta aluminide) up to 10 and 15 at.%, respectively [47,48,49]. The TEM research results comply with the data of the X-ray phase analysis, which imply that an insignificant amount of Ta dissolves in the crystals of TiAl and Ti3Al and are present in the (Ti,Ta)Al3 phase.
Thus, the XPA and TEM studies have shown that the formed solid solution based on titanium and the alloys under study have particles of the new phase in their structure. It is also well known that after microalloying of the alloys with metals Y and Dy, the mass fraction of the TiAl phases increases significantly (>70%). A distribution of tantalum in the titanium–aluminum matrix is evidence of the possibility of the formation of the three component system (Ti,Ta)Al3 [47,48,49]. Alloying metals, Y and Dy, form a compound with aluminum; they are applied as a dispersion phase and strengthen the alloy structure by the introduction of the second phase into the metal matrix in the form of a high-melting compound. If YAl2 is located on the dislocations or on the grain boundaries, DyAl2 is chaotically distributed in the grain volume.

4. Conclusions

The composite materials based on gamma-aluminides of titanium TiAl-REM were obtained by a new method—“hydride technology”. The content of the major phases in the initial TA system, as well as TA-REM, containing microadditions Ta, Y and Dy, was determined by the Rietveld method with high reliability.
1. It was established that in the initial TA system and in the TA-REM system, containing microadditions, TiAl predominate in tetragonal and triclinic units. It was established that the used initial standard lattices, as well as the structures after the full-profile specification, were in the stable states.
2. The results of X-ray phase analysis are confirmed by the results of TEM. It is known that after microalloying alloys by Y and Dy metals, the mass fraction of TiAl phases increases significantly (>70%).
3. From the results of X-ray phase analysis and TEM studies, it follows that an insignificant amount of Ta dissolves in the crystals of TiAl and Ti3Al and are present in the (Ti,Ta)Al3 phase. This fact indicates the possibility of the formation of a three component system (Ti, Ta)Al3.

Author Contributions

Y.A. studied structural state and determined the energies of lattices of separate phases and fraction of quantitative phase, and wrote the paper; N.K. conducted the microstructure research of samples and analyzed the data; I.K. conducted the X-ray phase analyses of samples; A.B. wrote the introduction and conducted the synthesis of samples; V.S. and R.E. analyzed data. All authors have read and agreed to the published version of the manuscript.

Funding

This work was carried out with the support of the Program of Competitive Recovery of TSU, NU 8.2.10.2018 L. and project No. 10.3031.2017/4.6.

Acknowledgments

The authors are grateful to Mark Kalashnikov for fruitful cooperation.

Conflicts of Interest

The authors declare no conflict of interest. The funding sponsors had no role in the design of the study; in the collection, analyses, or interpretation of data; in the writing of the manuscript, and in the decision to publish the results.

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Figure 1. 3D lattice of the AlTi3 alloy with the Y atom embedded in the site [0.5 0.5 0.5].
Figure 1. 3D lattice of the AlTi3 alloy with the Y atom embedded in the site [0.5 0.5 0.5].
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Figure 2. Diffraction patterns of alloys TA (a,b); TAY (c,d); TAT (e,f); TAD (g,h): 1—experiment, 2—summary model intensity, 3—difference between intensities, 4–6—contributions to the integral intensity of separate phases.
Figure 2. Diffraction patterns of alloys TA (a,b); TAY (c,d); TAT (e,f); TAD (g,h): 1—experiment, 2—summary model intensity, 3—difference between intensities, 4–6—contributions to the integral intensity of separate phases.
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Figure 3. EDX-spectra and elemental composition of the TAY (a), TAT (b) and TAD (c) alloys.
Figure 3. EDX-spectra and elemental composition of the TAY (a), TAT (b) and TAD (c) alloys.
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Figure 4. Electron microscope images of the matrix of the initial alloy TA: (a) bright-field image; (b) microdiffraction pattern; (c), (d) dark-field images in reflexes, marked by arrows; (e) microdiffraction pattern identification.
Figure 4. Electron microscope images of the matrix of the initial alloy TA: (a) bright-field image; (b) microdiffraction pattern; (c), (d) dark-field images in reflexes, marked by arrows; (e) microdiffraction pattern identification.
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Figure 5. Isothermal cross-sections of the TiAlY system at 1000 °C [45] (a), of the TiAlDy system at 500 °C [46] (b), of the TiAlTa system at 1100 °C [47] (c).
Figure 5. Isothermal cross-sections of the TiAlY system at 1000 °C [45] (a), of the TiAlDy system at 500 °C [46] (b), of the TiAlTa system at 1100 °C [47] (c).
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Figure 6. Electron microscope images of the TAY alloy: (a) bright-field image; (b) microdiffraction pattern; (c,d) dark-field images in reflexes, marked by arrows; (e) microdiffraction pattern identification.
Figure 6. Electron microscope images of the TAY alloy: (a) bright-field image; (b) microdiffraction pattern; (c,d) dark-field images in reflexes, marked by arrows; (e) microdiffraction pattern identification.
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Figure 7. TAY alloy microstructure.
Figure 7. TAY alloy microstructure.
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Figure 8. Electron microscope images of the TAD alloy: (a) bright-field image; (b) microdiffraction pattern; (c) dark-field images in the reflex; (d) microdiffraction pattern identification.
Figure 8. Electron microscope images of the TAD alloy: (a) bright-field image; (b) microdiffraction pattern; (c) dark-field images in the reflex; (d) microdiffraction pattern identification.
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Figure 9. Electron microscope images of the TAT alloy: (a) bright-field image; (b) microdiffraction pattern; (c) dark-field image in reflex; (d) microdiffraction pattern identification.
Figure 9. Electron microscope images of the TAT alloy: (a) bright-field image; (b) microdiffraction pattern; (c) dark-field image in reflex; (d) microdiffraction pattern identification.
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Table 1. Structural parameters of the lattices and the share of phases, and the convergence criterion of the TA alloy.
Table 1. Structural parameters of the lattices and the share of phases, and the convergence criterion of the TA alloy.
PhaseStatea, Åb, Åc, ÅAlphaBetaGammaV,
A^3		Space GroupShare,
%		E, eVRwp, %
AlTi3-2768Init.5.7645.7644.66490.0090.00120.00132.56P6/mmm, Hexagonal22.33−19,317.4847.193
Spec.5.7635.7634.64590.0090.00120.00131.996
TiAl-Struct2-GeomOptInit.6.3394.1504.234113.3693.3692.52132.56P1, Triclinic49.80−4810.6263
Spec.6.1294.2374.017113.6288.2492.42133.711
TiAl-Struct2Init.6.3394.1504.234113.3693.3692.52101.791P1, Triclinic24.08−4975.776
Spec.6.1944.1194.215113.0792.8891.9798.64
Table 2. Structural parameters of the lattices and the share of phases, and the convergence criterion of the TAY alloy.
Table 2. Structural parameters of the lattices and the share of phases, and the convergence criterion of the TAY alloy.
PhaseStatea, Åb, Åc, ÅAlphaBetaGammaV,
A^3		Space GroupShare
%		E, eVRwp, %
AlTi3-2768Init.5.7645.7644.66490.0090.00120.00132.56P6/mmm, Hexagonal26.99−19,603.1516.317
Spec.5.7365.7364.62690.0090.00120.00131.828
AlTi-2770Init.2.8372.8374.05990.0090.0090.0032.677P4/mmm, Tetragonal41.04−1660.340
Spec.2.8242.8244.07090.0090.0090.0032.466
TiAl-Struct2Init.6.3394.1504.234113.3693.3692.52101.791P1, Triclinic27.63−4954.073
Spec.6.2454.1284.319114.6791.2793.84100.802
Table 3. Structural parameters of the lattices and the share of phases, and the convergence criterion of the TAT alloy.
Table 3. Structural parameters of the lattices and the share of phases, and the convergence criterion of the TAT alloy.
PhaseStatea, Åb, Åc, ÅAlphaBetaGammaV,
A^3		Space GroupShare,
%		E, eVRwp, %
AlTi3-2768Init.5.7645.7644.66490.0090.00120.00132.56P6/mmm, Hexagonal16.66−19,705.8726.701
Spec.5.7915.7914.73690.0090.00120.00137.565
AlTi-2770Init.2.8372.8374.05990.0090.0090.0032.677P4/mmm, Tetragonal50.61−1660.341
Spec.2.8312.8314.06790.0090.0090.0032.609
TiAl-Struct2Init.6.3394.1504.234113.3693.3692.52101.791P1, Triclinic25.79−4978.726
Spec.6.5684.1334.093160.2795.8592.6433.821
Table 4. Structural parameters of the lattices and the share of phases, and the convergence criterion of the TAD alloy.
Table 4. Structural parameters of the lattices and the share of phases, and the convergence criterion of the TAD alloy.
PhaseStatea, Åb, Åc, ÅAlphaBetaGAMMAV,
A^3		Space GroupShare, %E, eVRwp, %
AlTi3-2768Init.5.7645.7644.66490.0090.00120.00132.56P6/mmm, Hexagonal11.20−31,228.5266.504
Spec.5.7715.7714.65790.0090.00120.00134.34
AlTi-2770Init.2.8372.8374.05990.0090.0090.0032.677P4/mmm, Tetragonal65.04−1660.341
Spec.2.8262.8264.07490.0090.0090.0032.537
TiAl-Struct2-GeomOptInit.6.3394.1454.234113.3693.3692.52101.79P1, Triclinic16.88−4978.606
Spec.6.2944.1394.260115.2392.7291.94100.09
Table 5. Relative coordinates of the atoms in the TiAl-Struct2 lattice.
Table 5. Relative coordinates of the atoms in the TiAl-Struct2 lattice.
Symbol of the AtomxyzDisplacement Parameters,
(U_iso)		Occupancy
Ti10.310−0.359−0.6780.01271.0
Ti2−0.5000.3340.6670.01271.0
Ti3−0.3110.0270.0120.01271.0
Ti40.227−0.017−0.0360.01271.0
Al5−0.0000.334−0.3330.01271.0
Al6−0.227−0.3160.3700.01271.0
Table 6. Relative atomic coordinates in the AlTi lattice (AlTi3-2768) with an embedded atom Dy, Ta and Y.
Table 6. Relative atomic coordinates in the AlTi lattice (AlTi3-2768) with an embedded atom Dy, Ta and Y.
ElementxyzU_isoOccupancy
Ti0.8330.1670.250.01271
Al0.3330.6670.250.01271
Dy; Ta; Y0.50.50.50.01271
Table 7. Crystallographic data of phases in the system TA.
Table 7. Crystallographic data of phases in the system TA.
CompositionSpace GroupSyngonyCSR Volume,
Å^3		Weight Fraction, %Lattice Parameters, Å
abc
TiAlP4/mmmtetragonal33 ± 538.42.82342.82344.0768
Ti3AlP63/mmctetragonal134 ± 525.25.76715.76714.64646
α-TiC6/mmchexagonal31 ± 518.02.92532.92534.6184
TiAl2C/mmmrhombic195 ± 511.812.01874.02324.0253
Ti5Al11P/mmmrhombic261 ± 58.33.95223.952217.3119
Ti3Al5P/mmmrhombic61 ± 52.93.86753.82124.1445
Ti2Al5P4/mmmtetragonal440 ± 52.53.81643.816430.1785
Table 8. Crystallographic data of phases in the TAY system.
Table 8. Crystallographic data of phases in the TAY system.
CompositionSpace GroupSyngonyCSR Volume,
Å^3		Weight Fraction, %Lattice Parameters, Å
abc
Ti3Al5P/mmmrhombic65 ± 570.34.00404.00494.0710
Ti3AlP63/mmctetragonal134 ± 518.35.76615.76614.6371
AlFm-3mcubic66±58.64.03114.03114.0311
α-TiP63/mmchexagonal31 ± 51.42.91862.91864.6006
TiAlP4/mmmtetragonal40 ± 51.22.74532.74535.3402
YP63/mmchexagonal67± 50.33.66893.66895.7302
Table 9. Crystallographic data of phases in the TAD and TAT systems.
Table 9. Crystallographic data of phases in the TAD and TAT systems.
AlloyCompositionSpace GroupSyngonyWeight Fraction, %AlloyCompositionSpace GroupSyngonyWeight Fraction, %
TADTiAlP4/mmmtetragonal74.3TATTiAlP4/mmmtetragonal30.1
Ti3Al5P/mmmrhombic10.9Ti3AlP63/mmctetragonal22.9
TiAl2C/mmmrhombic5.0Ti3Al5P/mmmrhombic26.4
AlFm-3mcubic3.9Ti5Al11P/mmmrhombic3.9
Ti5Al11I4/mmmrhombic1.4α-TiP63/mmchexagonal3.9
α-TiP63/mmchexagonal1.4TaAl3F-43mcubic2.8
DyP63/mmchexagonal1,6Ti2Al5P4/mmmtetragonal1.9

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Belgibayeva, A.; Abzaev, Y.; Karakchieva, N.; Erkasov, R.; Sachkov, V.; Kurzina, I. The Structural and Phase State of the TiAl System Alloyed with Rare-Earth Metals of the Controlled Composition Synthesized by the “Hydride Technology”. Metals 2020, 10, 859. https://doi.org/10.3390/met10070859

AMA Style

Belgibayeva A, Abzaev Y, Karakchieva N, Erkasov R, Sachkov V, Kurzina I. The Structural and Phase State of the TiAl System Alloyed with Rare-Earth Metals of the Controlled Composition Synthesized by the “Hydride Technology”. Metals. 2020; 10(7):859. https://doi.org/10.3390/met10070859

Chicago/Turabian Style

Belgibayeva, Akbayan, Yuri Abzaev, Natalia Karakchieva, Rakhmetulla Erkasov, Victor Sachkov, and Irina Kurzina. 2020. "The Structural and Phase State of the TiAl System Alloyed with Rare-Earth Metals of the Controlled Composition Synthesized by the “Hydride Technology”" Metals 10, no. 7: 859. https://doi.org/10.3390/met10070859

APA Style

Belgibayeva, A., Abzaev, Y., Karakchieva, N., Erkasov, R., Sachkov, V., & Kurzina, I. (2020). The Structural and Phase State of the TiAl System Alloyed with Rare-Earth Metals of the Controlled Composition Synthesized by the “Hydride Technology”. Metals, 10(7), 859. https://doi.org/10.3390/met10070859

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