E ﬀ ect of the Ti6Al4V Alloy Track Trajectories on Mechanical Properties in Direct Metal Deposition

: The TiAl6V4 alloy is widely used in selective laser melting and direct laser melting. In turn, works devoted to the issue of how the track stacking scheme a ﬀ ects the value of mechanical properties is not enough. The inﬂuence of the Ti6Al4V alloy track trajectories on the microstructure and mechanical properties during direct laser deposition is studied in this article for the ﬁrst time. The results were obtained on the inﬂuence of «parallel» and «perpendicular» technique of laying tracks in direct laser synthesis. All studied samples have a microstructure typical of the hardened two-phase condition titanium. Here, it is shown that the method of laying tracks and the direction of load application during compression testing relative to the location of the tracks leads to a change in the ultimate strength of the Ti-6Al-4V alloy from 1794 to 1910 MPa. The plasticity of the Ti-6Al-4V alloy obtained by direct laser alloying can vary from 21.3 to 33.0% depending on the direction of laying the tracks and the direction of the compression test. The hardness of alloys varies in the range from 409 to 511 HV and depends on the method of laying the tracks and the direction of hardness measurements.


Introduction
Titanium and its alloys are widely used in high-tech industries: Aircraft and rocketry, shipbuilding, nuclear power, chemical industry, and medicine.
Titanium and titanium alloys are better than the majority of modern construction materials, such as steel and aluminum, in their physical and mechanical properties and manufacturability. Titanium and titanium-based alloys are characterized by high melting points and electrical resistivity, their strength is comparable to most grades of alloy steels, they have high corrosion resistance in air and water, and a chemically aggressive environment. They are non-magnetic and have many other useful properties. The titanium specific mass is 56% of the specific mass of steel, which is easily processed by pressure and has biological inertness [1].
Adding other metals to titanium makes it possible to obtain alloys with a certain level of mechanical and operational properties. Their classification is divided into three groups: (1) α-Structure alloys. This group of alloys does not have an increase in brittleness with prolonged exposure to high stresses and temperatures. (2) α + β-Structure alloys. The β-phase is more ductile, the alloys are more workable and better amenable to pressure processing than α-structure alloys.
small-scale products of small and medium size, with the possibility of creating closed cooling channels, which cannot be done by traditional methods of parts processing [15][16][17][18][19]. It is also possible to create net structures for facilitation, but with effective strength characteristics preservation of parts [21][22][23][24]. In addition, it is actively used to create prostheses, producing a specially porous structure for better melting of the prosthesis with bone tissues [24]. Laser metal deposition (LMD) is a process of direct material deposition under a constant source of laser treatment with the laser device movement along the product contours. It is possible to use several types of materials: Metal powder or wire in this method. The LMD process is applicable to create infinitely large products of complex geometric shapes with small tolerances and high properties [25]. Moreover, the process of direct laser deposition is used to create new components of parts with high geometric complexity [26], which would require much more production hours or the possibility of creating a single whole product using detachable components to create it using traditional processing methods. Earlier, we carried out work [26] on growing a special item of parabolic shape by combining the selective laser melting and direct metal deposition. There is no critical thermal effect on the entire remaining part due to spot heating by this method, in which the cost of creating a new product is reduced [27]. The direct laser melting process allows the gradient metal composites creation by mixing powders of different compositions in growing a product continuous process, thereby making it possible to obtain products that have no analogues on the market. Aircraft and machine builders use direct laser coating to repair high-value products.
Many disadvantage characteristics of traditional titanium and its alloys processing methods during the layer-by-layer alloying of powder material are absent, but they are replaced by other characteristic properties of additive technologies. The motion vector of the laser beam in the XYZ coordinate system during the layer-by-layer powder alloying in different components of the part changes repeatedly during the complex shape synthesis [20,22].
Defects, mainly microcracks and pores, may be present in products obtained by the selective laser melting technology [13]. Pores have a significant effect on the mechanical properties of the material due to their larger size and flat shape [15,16,19].
The porosity does not exceed 1% with direct laser melting, but the movement of the laser along different trajectories, with the possibility of texture formation in different metallographic planes [25][26][27], leads to the appearance of properties anisotropy [25].
The analysis of publications shows that the question of understanding the microstructure formation patterns and, as a consequence, the mechanical properties formation, depending on the scheme of layers deposition from a powder material during direct laser synthesis, remains unexplored. The relevance of such studies is determined by the need in developing effective additive processes for the production of complex shape products from the titanium alloy Ti6Al4V, which is widely demanded in the aviation industry.
The object of this work is to study the effect of the powder material deposition trajectory Ti6Al4V alloy on the microstructure and mechanical properties of the samples during direct laser synthesis.

Materials and Methods
The studies on the samples grown using the direct metal deposition (DMD) technology were carried out in the laboratories of the South Ural State University, Chelyabinsk, Russia.
The studies were carried out on a FL-Clad-R-4 laser complex ( Figure 1) equipped with a 4 kW laser LS-4, a 6-axis industrial robot, a KUKA R-120 manipulator with a KUKA DKP-400 2-axis positioner, a TWIN-10-CR-2 powder feeder, as well as technological equipment for creating an argon atmosphere. Titanium powder Ti-6Al-4V with a fraction of 30-100 µm was chosen to carry out the research ( Figure 2). The melting of the powder was conducted according to the previously obtained mode [24]: Power P = 1800 W; powder feed K = 27 g/min; laser movement speed U = 25 mm/s; displacement of the track in the layer plane Δl = 2.5 mm; track displacement in the vertical plane Δh = 0.3 mm; number of layers n = 150. Two types of powder deposition techniques have been developed. The layers were coated on each other by parallel tracks in the first technique (Figures 3a and 4a), and the layers parallel tracks were alternately shifted by 90 degrees in the second type (Figures 3b and 4b). The diameter of the titanium disk on which the sample was deposited was 54 mm. The overall dimensions of the obtained samples did not exceed 50 × 25 × 40 mm.  Titanium powder Ti-6Al-4V with a fraction of 30-100 µm was chosen to carry out the research ( Figure 2). The melting of the powder was conducted according to the previously obtained mode [24]: Power P = 1800 W; powder feed K = 27 g/min; laser movement speed U = 25 mm/s; displacement of the track in the layer plane ∆l = 2.5 mm; track displacement in the vertical plane ∆h = 0.3 mm; number of layers n = 150. Two types of powder deposition techniques have been developed. The layers were coated on each other by parallel tracks in the first technique (Figures 3a and 4a), and the layers parallel tracks were alternately shifted by 90 degrees in the second type (Figures 3b and 4b). The diameter of the titanium disk on which the sample was deposited was 54 mm. The overall dimensions of the obtained samples did not exceed 50 × 25 × 40 mm. Titanium powder Ti-6Al-4V with a fraction of 30-100 µm was chosen to carry out the research ( Figure 2). The melting of the powder was conducted according to the previously obtained mode [24]: Power P = 1800 W; powder feed K = 27 g/min; laser movement speed U = 25 mm/s; displacement of the track in the layer plane Δl = 2.5 mm; track displacement in the vertical plane Δh = 0.3 mm; number of layers n = 150. Two types of powder deposition techniques have been developed. The layers were coated on each other by parallel tracks in the first technique (Figures 3a and 4a), and the layers parallel tracks were alternately shifted by 90 degrees in the second type (Figures 3b and 4b). The diameter of the titanium disk on which the sample was deposited was 54 mm. The overall dimensions of the obtained samples did not exceed 50 × 25 × 40 mm.     The chemical composition of the samples structural components was analyzed on a JSM-6460LV scanning electron microscope (JEOL, Tokyo, Japan) equipped with an energy dispersive spectrometer (OxfordInstruments, Abingdon, UK) for qualitative and quantitative X-ray microanalysis. The microstructure of the samples was studied on the Axio Observer D1.m optical inverted metallographic microscope (Carl Zeiss Microscopy GmbH, Jena, Germany) equipped with the ThixometPro software (Thixomet Pro, Thixomet Company, Saint Petersburg, Russia).
Samples for mechanical tests were prepared using electrical discharge cutting ( Figure 5a). This was necessary since the hardness of the obtained samples is high, which complicates their mechanical processing. Electric discharge machining allows excluding the heating of the metal in the cut zone and obtaining a high quality of the samples surface, which is very important for brittle materials mechanical testing.   The chemical composition of the samples structural components was analyzed on a JSM-6460LV scanning electron microscope (JEOL, Tokyo, Japan) equipped with an energy dispersive spectrometer (OxfordInstruments, Abingdon, UK) for qualitative and quantitative X-ray microanalysis. The microstructure of the samples was studied on the Axio Observer D1.m optical inverted metallographic microscope (Carl Zeiss Microscopy GmbH, Jena, Germany) equipped with the ThixometPro software (Thixomet Pro, Thixomet Company, Saint Petersburg, Russia).
Samples for mechanical tests were prepared using electrical discharge cutting ( Figure 5a). This was necessary since the hardness of the obtained samples is high, which complicates their mechanical processing. Electric discharge machining allows excluding the heating of the metal in the cut zone and obtaining a high quality of the samples surface, which is very important for brittle materials mechanical testing. The chemical composition of the samples structural components was analyzed on a JSM-6460LV scanning electron microscope (JEOL, Tokyo, Japan) equipped with an energy dispersive spectrometer (OxfordInstruments, Abingdon, UK) for qualitative and quantitative X-ray microanalysis. The microstructure of the samples was studied on the Axio Observer D1.m optical inverted metallographic microscope (Carl Zeiss Microscopy GmbH, Jena, Germany) equipped with the ThixometPro software (Thixomet Pro, Thixomet Company, Saint Petersburg, Russia).
Samples for mechanical tests were prepared using electrical discharge cutting (Figure 5a). This was necessary since the hardness of the obtained samples is high, which complicates their mechanical processing. Electric discharge machining allows excluding the heating of the metal in the cut zone and obtaining a high quality of the samples surface, which is very important for brittle materials mechanical testing. The hardness was determined using the Vickers scale on a hardness tester HV-1000 according to GOST 2999-75. The determination of hardness and the study of the microstructure was carried out along three planes, according to the directions indicated by the arrows in Figure 5b. Hardness tests were carried out on the same specimens on which the microstructure was studied. The hardness was measured at 5 points (Figure 5b) for each sample and the average was determined.
The compression test pieces were 10 mm in diameter and 20 mm in height. Compression tests were carried out on a universal testing machine INSTRON 5882, compression speed was 2 mm/min according to GOST 25.503-97. Compression tests were repeated three times for each type of samples.
Since specimens for compression testing were made according to the scheme in Figure 5a and for specimen no. 1, the "parallel" technique, and for specimen no. 2, the "perpendicular" technique, then four types of specimens for testing are obtained with the layout of the tracks, as shown in Figure  6.

Results
Both samples externally show characteristic tracks inherent in different growing methods. In turn, there are no visually detected cracks and open pores on the grown samples ( Figure 4). Particles of over-fed powder form on the surface of the samples. The powder forms droplets or dendrites due to the high temperature. The hardness was determined using the Vickers scale on a hardness tester HV-1000 according to GOST 2999-75. The determination of hardness and the study of the microstructure was carried out along three planes, according to the directions indicated by the arrows in Figure 5b. Hardness tests were carried out on the same specimens on which the microstructure was studied. The hardness was measured at 5 points (Figure 5b) for each sample and the average was determined.
The compression test pieces were 10 mm in diameter and 20 mm in height. Compression tests were carried out on a universal testing machine INSTRON 5882, compression speed was 2 mm/min according to GOST 25.503-97. Compression tests were repeated three times for each type of samples.
Since specimens for compression testing were made according to the scheme in Figure 5a and for specimen no. 1, the "parallel" technique, and for specimen no. 2, the "perpendicular" technique, then four types of specimens for testing are obtained with the layout of the tracks, as shown in Figure 6. The hardness was determined using the Vickers scale on a hardness tester HV-1000 according to GOST 2999-75. The determination of hardness and the study of the microstructure was carried out along three planes, according to the directions indicated by the arrows in Figure 5b. Hardness tests were carried out on the same specimens on which the microstructure was studied. The hardness was measured at 5 points (Figure 5b) for each sample and the average was determined.
The compression test pieces were 10 mm in diameter and 20 mm in height. Compression tests were carried out on a universal testing machine INSTRON 5882, compression speed was 2 mm/min according to GOST 25.503-97. Compression tests were repeated three times for each type of samples.
Since specimens for compression testing were made according to the scheme in Figure 5a and for specimen no. 1, the "parallel" technique, and for specimen no. 2, the "perpendicular" technique, then four types of specimens for testing are obtained with the layout of the tracks, as shown in Figure  6.

Results
Both samples externally show characteristic tracks inherent in different growing methods. In turn, there are no visually detected cracks and open pores on the grown samples ( Figure 4). Particles of over-fed powder form on the surface of the samples. The powder forms droplets or dendrites due to the high temperature.

Results
Both samples externally show characteristic tracks inherent in different growing methods. In turn, there are no visually detected cracks and open pores on the grown samples ( Figure 4). Particles of over-fed powder form on the surface of the samples. The powder forms droplets or dendrites due to the high temperature.
The study of the microstructure of the obtained samples showed that a mechanical mixture of αand β-phases is formed as a result of melting (Figures 7 and 8). Earlier, we carried out work [26] in which we studied, in more detail, the phase composition of the samples obtained from the powder Ti-6Al-4V using similar fusion modes. The presence of two phases (α and β) in the structure is confirmed by XRD results. The study of the microstructure of the obtained samples showed that a mechanical mixture of α-and β-phases is formed as a result of melting (Figures 7 and 8). Earlier, we carried out work [26] in which we studied, in more detail, the phase composition of the samples obtained from the powder Ti-6Al-4V using similar fusion modes. The presence of two phases (α and β) in the structure is confirmed by XRD results.   The two-phase structure forms upon heating and fast cooling. Aluminum in an amount of 6% allows the formation of a long-range order α-solid solution phase with the possibility of preseparation of the α2-phase in the Ti-6Al-4V alloy. Vanadium is an isomorphic β-stabilizer, does not form chemical compounds with titanium, and does not lead to eutectoid reactions. The grains are formed independently of the applied layers, passing from one layer to another. The coarse-grained structure is formed during the powder melting process. It should be noted that the number of pores The two-phase structure forms upon heating and fast cooling. Aluminum in an amount of 6% allows the formation of a long-range order α-solid solution phase with the possibility of pre-separation of the α 2 -phase in the Ti-6Al-4V alloy. Vanadium is an isomorphic β-stabilizer, does not form chemical compounds with titanium, and does not lead to eutectoid reactions. The grains are formed independently of the applied layers, passing from one layer to another. The coarse-grained structure is formed during the powder melting process. It should be noted that the number of pores is very small, and their size does not exceed 20 µm (Figures 7a and 9a). All studied samples have a microstructure typical of the hardened state of two-phase titanium. The so-called "basket weave" structure is clearly visible in some fields of view: The α-phase stands out along the grain boundaries of the primary β-phase, the acicular α-phase in the grain body with thin layers of the β-phase between them (Figure 8b,d).
Machines 2020, 8, x FOR PEER REVIEW 9 of 14 is very small, and their size does not exceed 20 µm (Figures 7а and 9а). All studied samples have a microstructure typical of the hardened state of two-phase titanium. The so-called "basket weave" structure is clearly visible in some fields of view: The α-phase stands out along the grain boundaries of the primary β-phase, the acicular α-phase in the grain body with thin layers of the β-phase between them (Figure 8b,d). Figure 9. Energy-dispersive X-ray spectroscopy (EDS) mapping of the Ti-6Al-4V alloy samples: (a) Sample no. 1, the "parallel" technique; (b) sample no. 1, the "parallel" technique without pores; (c) sample no. 2, the "perpendicular" technique at times; (d) sample no. 2, the "perpendicular" technique without pores.
The results of studying the samples chemical composition using a scanning electron microscope are shown in Table 1 and Figure 9. Figure 9 shows the maps of the distribution of chemical elements in the samples under study. Areas of solid material without pores (Figure 9b,d) and areas with pores (Figure 9a,c) were studied. It can be seen from the results that the areas with pores do not differ in composition from the homogeneous area of the samples under study. The porosity is not localized. There are separate small spherical pores, the total percentage of porosity does not exceed 0.2%. The pore sizes do not exceed 20 µm. Pores are undesirable in this study. The reason for their formation is the shielding gas argon, which did not have time to escape when the powder was melted. The distribution of chemical elements in the field of observation is uniform. The only exception is V, the concentration of which is increased in the β-phase areas.  The results of studying the samples chemical composition using a scanning electron microscope are shown in Table 1 and Figure 9. Figure 9 shows the maps of the distribution of chemical elements in the samples under study. Areas of solid material without pores (Figure 9b,d) and areas with pores (Figure 9a,c) were studied. It can be seen from the results that the areas with pores do not differ in composition from the homogeneous area of the samples under study. The porosity is not localized. There are separate small spherical pores, the total percentage of porosity does not exceed 0.2%. The pore sizes do not exceed 20 µm. Pores are undesirable in this study. The reason for their formation is the shielding gas argon, which did not have time to escape when the powder was melted. The distribution of chemical elements in the field of observation is uniform. The only exception is V, the concentration of which is increased in the β-phase areas. The results of the hardness measurements in three directions (Figure 5b) of the samples grown by two methods are shown in Table 2. The hardness of the alloy depends on the tracks applying technique during the samples growth. Therefore, the «perpendicular» technique of tracks applying during melting allows increasing the hardness in comparison with the hardness of the samples obtained by the «parallel» technique. The largest increase in hardness is observed in one measurement direction and it is 36 HV or 8%. In turn, it should be noted that in both samples the value of hardness significantly depends on the direction of measurement. Therefore, the minimum value of hardness in samples 1 and 2 corresponds to direction 1, and the maximum to direction 3. The results of compression tests are presented in Table 3 and Figure 10. The maximum strength of 1910 MPa was shown by samples with a «vertical» track arrangement, and the minimum 1794 MPa with a «parallel» one. The alloy can resist higher stresses when a load is applied perpendicular to the track arrangement than when it is loaded parallel to the tracks. In turn, the deformation under compression for a sample with a «vertical» track arrangement is higher than for a sample with a «parallel» one. The "vertical" tracks arrangement provides a combination of high strength with high plasticity of the material. The highest plasticity, namely 33%, was shown by samples with a "mixed" track arrangement at the same time.

Discussion
It was shown that the laser complex FL-Clad-R-4 makes it possible to obtain billet or finished products [26] from titanium alloys by fusing the powder material in a protective argon atmosphere in the course of research [2,3]. A homogeneous microstructure from the Ti-6Al-4V alloy, which consists of a mechanical mixture of α-and β-phases (Figures 7 and 8), is formed when fusing a powder material with a fraction of 30-100 µm. The porosity of the obtained samples does not exceed 0.2%, and the size of spherical pores is less than 20 µm (Figures 7 and 9). The chemical analysis of the obtained samples showed that the alloy contains 89% Ti, 5.9% Al, and 4.3 to 4.7 V (Table 1). Vanadium is distributed unevenly, and its increased concentration leads to the formation of the β-phase in the microstructure (Figures 7-9). In turn, the presence of pores does not lead to a change in concentration, and the reason for their appearance is most likely argon gas bubbles. The melting of samples using «parallel» and «perpendicular» track arrangements affects the mechanical properties of alloys ( Figure  10). Tests of samples made in different directions relative to the melting tracks showed the influence of the direction on the mechanical properties. The maximum strength of 1910 MPa was shown by samples with a «vertical» track arrangement, and the minimum 1794 MPa with a «parallel» one. The highest plasticity, namely, a compression deformation of 33%, was shown by samples with a «mixed»

Discussion
It was shown that the laser complex FL-Clad-R-4 makes it possible to obtain billet or finished products [26] from titanium alloys by fusing the powder material in a protective argon atmosphere in the course of research [2,3]. A homogeneous microstructure from the Ti-6Al-4V alloy, which consists of a mechanical mixture of αand β-phases (Figures 7 and 8), is formed when fusing a powder material with a fraction of 30-100 µm. The porosity of the obtained samples does not exceed 0.2%, and the size of spherical pores is less than 20 µm (Figures 7 and 9). The chemical analysis of the obtained samples showed that the alloy contains 89% Ti, 5.9% Al, and 4.3 to 4.7 V (Table 1). Vanadium is distributed unevenly, and its increased concentration leads to the formation of the β-phase in the microstructure (Figures 7-9). In turn, the presence of pores does not lead to a change in concentration, and the reason for their appearance is most likely argon gas bubbles. The melting of samples using «parallel» and «perpendicular» track arrangements affects the mechanical properties of alloys ( Figure 10). Tests of samples made in different directions relative to the melting tracks showed the influence of the direction on the mechanical properties. The maximum strength of 1910 MPa was shown by samples with a «vertical» track arrangement, and the minimum 1794 MPa with a «parallel» one. The highest plasticity, namely, a compression deformation of 33%, was shown by samples with a «mixed» track arrangement ( Table 3). The hardness of the obtained samples varies in the range from 409 to 511 HV (Table 2) and also depends on the direction of measurement and the method of laying the tracks as «parallel» or «perpendicular». The reason for the pronounced anisotropy of properties is directional crystallization and subsequent recrystallization when the next layer is applied. Subsequent recrystallization is confirmed by the formation of grains larger than the track height. However, a more detailed explanation of the recrystallization mechanism and the dependence of properties on the direction of crystal growth requires targeted research that is planned for the future.

Conclusions
The influence of the Ti6Al4V alloy powder material deposition track on the microstructure and mechanical properties, during direct laser synthesis, is studied in this article for the first time. The study of the microstructure of the obtained samples showed that as a result of melting, a mechanical mixture of αand β-phases is formed. All studied samples have a microstructure typical of the hardened two-phase condition titanium. The so-called "basket weaving" structure is clearly visible in some fields of view: The α-phase stands out along the grain boundaries of the primary β-phase, the needlelike α-phase in the grain body with thin layers of β-phase between them. The studies carried out have shown that it is necessary to take into account the layout of the tracks during direct laser melting of the powder material when designing finished parts of complex shapes or billet requiring finishing machining. It is shown that the «parallel» and «perpendicular» track arrangement is reflected in the mechanical properties of the material using the Ti-6Al-4V alloy as an example. The direction of the load application during the mechanical properties testing also has a great effect. It is possible to increase the value of the ultimate strength that the Ti-6Al-4V alloy resists from 1794 to 1910 MPa only by taking into account the location of the tracks relative to the applied compression load. In turn, the ductility of the Ti-6Al-4V alloy obtained by direct laser melting can change from 21.3 to 33.0% depending on the direction of laying the tracks and the direction of the compression test. The hardness of alloys varies in the range from 409 to 511 HB and also depends on the method of laying the tracks and the direction of hardness measurements. Taking these factors into account when designing critical parts from titanium alloys will make it possible to correctly perform calculations and prevent mistakes. It is expedient to investigate the effect of the Ti6Al4V alloy powder material deposition track when testing samples for static tension in the future.