Introduction
NiTi shape memory alloys (SMAs) found a wide range of applications in the industry, including aerospace (tubing couplings, actuators), medical (stents, orthodontic wires, bone fixation plates), and automotive (valves, actuators) (Ref
1,
2). This is associated with the unique functional properties exhibited by this material such as shape memory (SM) and superelastic (SE) properties, low stiffness, damping behavior, high corrosion resistance, and biocompatibility. The shape recovery observed for the NiTi alloys results from the occurrence of the reversible martensitic transformation (MT) that takes place between the B2 austenite and B19’ martensite. The wide interest of the industry in the NiTi alloys is limited by difficulties in fabrication of elements from this material due to the high reactivity of melted alloy, which results in the formation of Ti-rich compounds like TiC or Ti
4Ni
2O
x, degrading their functional properties. Another problem is associated with the low ductility of NiTi alloys, resulting in difficulties in processing and machining (Ref
3). These drawbacks limit the geometries of the fabricated elements mainly to the rods, wires, bars, tubes, or sheets. In recent years, additive manufacturing (AM) technology becomes a promising approach to direct fabrication of NiTi parts with complex geometries, which is difficult or even impossible to obtain in the conventional plastic deformation methods (Ref
3). In the AM process, the elements are reconstructed, based on 3D CAD models, using powder or wire feedstock, which is melted using highly focused laser or electron beam. This provides great opportunities of fabrication of the parts with complex shapes, internal channels, internal porosity, or near-net-shape elements (Ref
4).
Recently, a few different powder-based AM techniques were applied in the fabrication of elements from NiTi alloys, e.g., selective laser melting (SLM) (Ref
3), electron beam melting (EBM) (Ref
5), direct energy deposition (DED) (Ref
6), or laser-engineered net shaping (LENS) (Ref
7). The effect of the processing parameters such as laser power, scanning velocity, layer thickness, or energy input on the microstructure, transformation behavior, and mechanical properties of the fabricated parts were investigated earlier (Ref
8-
10). The microstructure of the AM-fabricated NiTi alloys consists usually of columnar grains elongated into the built direction, which was found to be associated with the epitaxial growth mechanism that takes place during the deposition. This also resulted in strong [001] texture along the build direction frequently reported for the AM-manufactured NiTi parts (Ref
7,
11). However, in order to fabricate elements exhibiting high density, high-dimensional accuracy, and low fraction of defects, the deposition has to be conducted in a previously specified process window, e.g., in the case of SLM method full-density NiTi parts may be obtained at energy input of about 55 J/mm
3 (Ref
3). The application of lower energy densities typically results in incomplete melting of the powder particles causing the formation of irregular porosity (Ref
10). On the other hand, the use of high energy densities leads to the formation of large Ni
4Ti
3 particles and higher level of impurities (Ref
12,
13). Wang et al. (Ref
8) showed that the change in the fabrication conditions not only affects the microstructure of the alloy, but also the transformation temperature and shape memory properties. This was associated with the changes in the chemical composition of the materials with the energy input as a result of Ni evaporation in melt pool, reported also by other authors (Ref
13). Ma et al. (Ref
14) utilized this effect for fabrication of NiTi parts with the location-dependent shape memory response. In this case, different areas of the part exhibited varied transformation temperatures due to different parameters used during the fabrication by SLM. The superelastic response of the AM-fabricated parts was registered for Ni-rich alloys, e.g., Ni
50.8Ti
49.2 fabricated by SLM (Ref
15-
17), Ni
51.2Ti
48.8 by EBM (Ref
11), or Ni
50.1Ti
49.9 by LENS (Ref
7). The superelasticity of NiTi alloys in the as-deposited state is moderate—they exhibited a recoverable strain of about 2-3% (Ref
16-
18). This results mainly from the wide temperature range of the martensitic transformation observed for alloys in as-deposited state, associated with the formation of Ni-rich precipitations during the deposition and slight fluctuation of chemical composition of the matrix (Ref
16). Therefore, the superelastic properties of additively manufactured NiTi alloys may be enhanced by an additional heat treatment, e.g., Seadi et al. (Ref
16) showed the increase of recoverable strain of SLM-manufactured NiTi from 3.2 to 5.5% for solution-treated and aged at 600 °C sample. The positive effect of post-processing heat treatment was also reported in other works (Ref
17,
19). On the other hand, Moghaddam et al. (Ref
15) showed that by controlling the microstructure and texture during the SLM deposition is possible to fabricate elements exhibiting superior recoverable strain of 5.6% without the application of additional heat-treatment.
Recently, a new additive manufacturing technology utilized a wire as an additive material, instead of powder, what found the application in fabrication of metallic components from different materials such as aluminum alloys (Ref
20), titanium alloys (Ref
21), nickel alloys (Ref
2), and steels (Ref
23). Depending on the energy source used for the metal deposition, the wire-based AM may be classified into three groups, such as wire and laser additive manufacturing (WLAM), wire and arc additive manufacturing (WAAM), and electron beam additive manufacturing (EBAM) (Ref
24). Those methods offer the possibility of fabrication of larger components in comparison with the powder-based methods, higher material efficiently and much higher deposition rates, e.g., in the case of EBAM, it may reach up to 300 g/min, whereas for SLM it is only about 2-4 g/min (Ref
24,
25). In the case of NiTi alloys, the application of wire-based methods may be favorable considering the fact that the NiTi wires are commercially available in contrast to the highly expensive atomized powders. However, the literature data regarding the application of such methods in fabrication of elements from NiTi alloys are very limited. In recent two years, a few papers concerning the use of WAAM technique were published (Ref
26-
29). Wang et. al (Ref
26) used Ni and Ti wires in order to manufacture Ni-rich NiTi parts by WAAM, which exhibited anisotropic microstructure with increased amount of Ni
4Ti
3 and decreased amount of Ni
3Ti precipitations from lower to upper region. These differences in the phase composition of the material resulted in changes of the martensitic transformation temperature along the height of the sample. Zeng et al. (Ref
27) showed that the application of a dedicated NiTi wire resulted in more homogenous microstructure consisting of elongated grains into the built direction, similar to what is observed in materials deposited using powder feedstock. The fabricated part exhibited a high relative density and low defects density, which resulted in relatively high ductility (elongation up to 17%). Nevertheless, the microstructure of the deposited elements is highly dependent on the applied process parameters, e.g., Wang et al. (Ref
28) reported austenite grain coarsening and increase in size of Ni
4Ti
3 precipitations with the increasing deposition current in NiTi fabricated by the WAAM process. As a result, the increase in the transformation temperature and decrease in the recoverable strain from 3.2 to 2.2% with the increasing deposition current from 80 A to 120 A were registered. Similar superelastic properties of the WAAM-deposited element, with the 2.7% of recoverable strain, were reported by Zeng et al. (Ref
27).
Although the application of WAAM process in the fabrication superelastic elements from NiTi alloys seems to be promising, other wire-based methods like EBAM may provide even better characteristics of as-deposited parts. Here, the essential may be the atmosphere used during the deposition. In the case of WAAM method, the deposition is conducted under the shielding gas, which may lead to pick up the impurities due to a high reactivity of Ti. The formation of Ti-rich phases, such as Ti
4Ni
2O, significantly changes Ti/Ni ratio and affects the phase transformation temperatures as well as functional and mechanical properties of the fabricated parts (Ref
30). In the case of SLM method, the application of the shielding gas was insufficient, and in order to obtain the materials exhibiting good ductility, the process has to be conducted in protective atmosphere inside the building chamber (Ref
8,
31). On the other hand, in the EBAM method the deposition process is conducted in high vacuum, due to the use of an electron beam as an energy source. It may further decrease the amount of impurities in as-deposited elements and enhance their functional properties. This technique was used for the first time in the fabrication of NiTi alloys in our previous work (Ref
7). The produced preliminary element in the as-deposited state showed homogenous microstructure and high recoverable strain of nearly 3% in the compression mode. In this study, a larger NiTi element was fabricated with the application of EBAM technique in order to determine its mechanical and functional properties in a tensile mode. The aim of the presented work was also to perform investigation of the martensitic transformation behavior during the in situ SEM tensile test applying the EBSD technique which allows to determine texture changes, twinning modes, and determination of the crystallographic relationship between formed martensite and austenite.
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