Microstructural Characterization of Dissimilar Titanium Alloys Joints Using Ni / Al Nanolayers

This study demonstrates the potential of the use of Ni/Al nanolayers for joining dissimilar titanium alloys. For this purpose, a detailed microstructural characterization of the diffusion bonding interfaces of TiAl to Ti6Al4V, TiAl to TiNi and TiNi to Ti6Al4V was carried out. The nanolayers (alternated aluminum and nickel (Ni-7V wt.%) layers) were deposited onto the base material surfaces. Diffusion bonding was performed at 700 and 800 ◦C under pressures ranging from 5 to 40 MPa and at dwell times between 60 and 180 min. Microstructural characterization was performed using high resolution transmission and scanning electron microscopies. The results revealed that dissimilar titanium joints (TiAl to Ti6Al4V, TiAl to TiNi and TiNi to Ti6Al4V) assisted by Ni/Al nanolayers can be obtained successfully at 800 ◦C for 60 min using a pressure of 20 MPa. The bond interfaces are thin (less than 10 μm) and mainly composed of NiAl grains with a few nanometric grains of Al8V5. Thin layers of Al-Ni-Ti intermetallic compounds were formed adjacent to the base materials due to their reaction with the nanolayers.


Introduction
Titanium alloys combine good mechanical properties, such as high specific strength, with low density and good resistance to corrosion, making them a good option for numerous applications.A significant proportion of the scientific community's studies on titanium alloys has focused on the Ti6Al4V, TiNi and TiAl alloys, the latter more recently and due to their high temperature properties [1][2][3].
The aerospace industry's continuous focus on reducing weight for increased fuel economy and operating efficiency requires the development of weight-saving structural materials for high service temperatures [1][2][3][4].Conventional titanium alloys are continuously challenged by the operation at temperatures higher than 550 • C due to poor high-temperature oxidation resistance and creep properties, and undesirable grain growth in single phase titanium alloys, with consequent degradation of mechanical properties [2].The possibility of using Ti6Al4V, TiNi and TiAl alloys in various applications has been increased by the development of production processes tailored to obtain the microstructures and mechanical properties adjusted to the needs of the market.The joining of these alloys facilitates the production of more complex components with a unique combination of properties and characteristics [5,6].For instance, the joining of TiNi and Ti6Al4V alloys is vital for the development of a shape memory alloy (SMA) adaptive serrated nozzle to aid noise reduction in next-generation gas turbine engines and the blade SMA actuator to enable inflight rotor tracking in commercial and military helicopters [7,8].
However, the development of suitable joining techniques is crucial to further increase the applications of these alloys or even replace conventional alloys with combinations of high performance titanium alloys.In fact, it is known that these alloys are reactive, and thus it is difficult to obtain high quality joints by conventional processes, such as welding.
Processes which do not involve the melting of the base material, such as diffusion bonding or brazing, have proved to be the most advantageous in the production of sound joints with appreciable mechanical properties.These two bonding processes present competitive advantages over the fusion welding processes.Among the many advantages to be underlined is the possibility of bonding materials with very different mechanical and physical properties, whereby joints can be obtained with mechanical properties similar to those of the base materials, not only maintaining the mechanical performance of the component, but also reducing or eliminating residual stresses and distortions.However, the processing conditions normally involved in these processes make them less attractive economically.Considerable effort has been made in the development of new brazing alloys or interlayers that make brazing and diffusion bonding processes more suitable for industrial implementation.
Reactive multilayer thin films are an alternative interlayer for reducing the temperature and/or the pressure needed for diffusion bonding.These multilayers can improve the diffusivity, due to their nanocrystalline nature and high density of defects, and simultaneously act as a local heat source, as the result of the heat released by the exothermic reaction of the multilayers to form intermetallic compounds [15][16][17][18][19][20].Previous studies [15][16][17] have shown that Ni/Al multilayers are effective in the diffusion bonding of TiAl to themselves [15], to steel [16] and to Ni-based superalloys [17].The use of reactive nanolayers in the diffusion bonding process enables the reduction of the joining conditions or the obtaining of better mechanical properties when compared with the joints processed by conventional diffusion bonding processes.
Other multilayer systems can also be of use in assisting the diffusion bonding of similar and dissimilar titanium alloys joints.For instance, Ni/Ti nanolayers aided the production of sound joints with appreciable mechanical properties under less demanding processing conditions [18][19][20].However, the interfaces formed are more complex than those obtained with reactive Ni/Al multilayers.The interface is formed from a mixture of TiNi and TiNi 2 grains.In some cases, the formation of aligned nanometric grains that do not promote a uniformity of mechanical properties through the interface was observed.
In this context, the main objective of this study is the diffusion bonding of dissimilar titanium alloys assisted by Ni/Al nanolayers.The present study centers on the microstructural characterization of the interface of these joints.Interface characterization was performed by scanning electron microscopy (SEM), energy dispersive X-ray spectroscopy (EDS), electron backscatter diffraction (EBSD), transmission electron microscopy (TEM), and selected area electron diffraction (SAED), high resolution TEM (HRTEM) and Fast Fourier transform (FFT).Microstructural characterization of the joints is essential for evaluating the effectiveness of using the Ni/Al nanolayers.Defect-free interfaces are crucial for the processing of joints with desired mechanical behavior.
The base materials were cut and polished down to a 1-µm diamond suspension.Nickel and aluminum nanolayers were deposited alternately onto the polished surfaces of the base materials by direct current magnetron sputtering using targets of aluminum (99.99% pure) and nickel (Ni-7V wt.%).The reactive nanolayers were designed to have ~25 nm of modulation period (bilayer thickness), an equiatomic chemical composition and a total thickness of ~2.5 µm.

Diffusion Bonding Experiments
Dissimilar joining experiments were conducted in a vertical furnace at a vacuum level better than 10 −2 Pa, at 700 and 800 • C, with pressures ranging from 5 to 40 MPa, bonding times from 60 to 180 min and heating and cooling rates of 10 • C /min.A description of the diffusion bonding apparatus can be found in a previous study [18] that consist in an infrared tubular furnace with an attached vacuum system mounted on a tensile test machine.

Microstructural Characterization
In order to perform microstructural and chemical characterization of the interfaces, cross sections of the joints were prepared using standard metallographic techniques.The interfaces were observed by scanning electron microscopy (SEM), and were analyzed by energy dispersive X-ray spectroscopy (EDS) using a high-resolution FEI QUANTA 400 FEG SEM (FEI Company, Hillsboro, OR, USA).The EDS measurements were made at an accelerating voltage of 15 keV by the standardless quantification method.The results obtained by this method provide a fast quantification with an automatic background subtraction, matrix correction and normalization to 100% for all the elements in the peak identification list.
Electron backscattered diffraction (EBSD) was performed on cross sections of the joints using a SEM FEI 400 FEG QUANTA (FEI Company, Hillsboro, OR, USA).The EBSD Kikuchi patterns were indexed using the database ICDD PDF-2 (PDF-2, ICDD-International Centre for Diffraction Data, Newtown Square, PA, USA, 2006) to identify the crystal structure of the phases at the interface.EBSD is a very useful technique to identify phases at very thin interfaces, since the interaction volume for this technique is reduced.A careful preparation of the surfaces is the key factor in achieving good quality EBSD patterns; the joint interfaces were submitted to a final chemo-mechanical polishing stage, using colloidal silica to remove the damage and deformation of the surfaces.This technique can also be used to obtain grain or crystallographic orientation maps of different phases that constitute the interfaces, enabling a better understanding of the distribution of the phases through them.

Results and Discussion
The effectiveness of using Ni/Al nanolayers to bond dissimilar titanium alloys was assessed through the microstructural characterization of the interfaces by different techniques of characterization.
Microstructural characterization reveals that interfaces with apparent soundness were produced during solid-state diffusion bonding of dissimilar titanium alloys using Ni/Al nanolayers.The TiAl to Ti6Al4V, TiAl to TiNi and TiNi to Ti6Al4V bonds were successful at 800 • C under a pressure of 20 MPa for 60 min.A lower bonding temperature (700 • C) or reduced pressure (10 MPa) promotes the formation of interfaces with pores and cracks in the central region, showing that it is not possible to further reduce the processing conditions.Figure 1 shows the SEM image of the TiAl/Ti6Al4V interface produced at 700 • C under a pressure of 20 MPa using Ni/Al nanolayers where the presence of cracks and unbonded areas is evident.Increasing dwell time to 180 min results in a better bond but also induces a strong plastic deformation of Ti6Al4V due to the reduced creep strength of this alloy at 800 • C.
The interfaces are very thin (thickness from 3.8 to 5.4 µm). Figure 2 shows the SEM images of the interfaces obtained for the dissimilar titanium alloys joints.The microstructure of the central zone of the interfaces is very similar for all the joints and does not depend on the base materials.This zone is composed of equiaxial grains and corresponds to the larger area of the interface.This microstructure is typical of the diffusion bonding joints assisted by Ni/Al nanolayers and corresponds to the reaction of the multilayers as observed in previous researches [15][16][17].
but also induces a strong plastic deformation of Ti6Al4V due to the reduced creep strength of this alloy at 800 °C.
The interfaces are very thin (thickness from 3.8 to 5.4 µm). Figure 2 shows the SEM images of the interfaces obtained for the dissimilar titanium alloys joints.The microstructure of the central zone of the interfaces is very similar for all the joints and does not depend on the base materials.This zone is composed of equiaxial grains and corresponds to the larger area of the interface.This microstructure is typical of the diffusion bonding joints assisted by Ni/Al nanolayers and corresponds to the reaction of the multilayers as observed in previous researches [15][16][17].The main differences between the interfaces are the thin layers formed by the reaction of the multilayers with the base materials and the extent of diffusion during the bonding process.Higher magnifications of the SEM images and microstructure schemes of the interfaces can be observed in Figure 3.
When the base material is the TiAl alloy, for any combination, the formation of two very thin reaction layers is observed (Z1 and Z2 in Figure 3a,b) corresponding to the reaction between the multilayers and TiAl.There is no change in the microstructure of TiAl adjacent to the interface, which is an indication of the limited diffusion.Regarding TiNi and Ti6Al4V alloys, different results are observed.For Ti6Al4V, only one reaction layer is observed, Z4 in Figure 3a and Z3 in Figure 3c, but the diffusion extends towards the Ti6Al4V and some bright particles are observed at approximatively 3 µm from the interface, Z5 in Figure 3a and Z4 in Figure 3c.For TiNi only one reaction layer is formed, Z4 in Figure 3b and Z1 in Figure 3c.In the TiNi/TiAl bond interface, small bright particles, Z5 in Figure 3b, are observed adjacent to this reaction layer.These particles are detected in localized areas.
Another important aspect to note for all bonds is the fact that the bond line is visible.A higher bonding temperature is required so that this line becomes no longer visible, as observed in a previous study.In similar TiAl diffusion bonds assisted by Ni/Al nanolayers, the bond line begins to disappear at temperatures above 900 °C [15].However, these temperatures are too high, especially for Ti6Al4V, due to its low creep strength.The identification of the phases present at the interfaces was carried out through the combination of different characterization techniques such as EDS in SEM and TEM, EBSD, SAED and FFT.The need to use these techniques is related to the dimensions of the particles and layers formed during bonding, ranging from a few micrometers to nanometers.For example, the interaction volume of EDS in SEM is greater than the thickness of the two layers close to the TiAl base material or the thickness of the reaction layer of the Ti6Al4V and the multilayers.High resolution techniques and techniques with small interaction volume are therefore essential for the microstructural characterization of these interfaces, composed of thin layers and nanometric phases.The main differences between the interfaces are the thin layers formed by the reaction of the multilayers with the base materials and the extent of diffusion during the bonding process.Higher magnifications of the SEM images and microstructure schemes of the interfaces can be observed in Figure 3.
When the base material is the TiAl alloy, for any combination, the formation of two very thin reaction layers is observed (Z1 and Z2 in Figure 3a,b) corresponding to the reaction between the multilayers and TiAl.There is no change in the microstructure of TiAl adjacent to the interface, which is an indication of the limited diffusion.Regarding TiNi and Ti6Al4V alloys, different results are observed.For Ti6Al4V, only one reaction layer is observed, Z4 in Figure 3a and Z3 in Figure 3c, but the diffusion extends towards the Ti6Al4V and some bright particles are observed at approximatively 3 µm from the interface, Z5 in Figure 3a and Z4 in Figure 3c.For TiNi only one reaction layer is formed, Z4 in Figure 3b and Z1 in Figure 3c.In the TiNi/TiAl bond interface, small bright particles, Z5 in Figure 3b, are observed adjacent to this reaction layer.These particles are detected in localized areas.
Another important aspect to note for all bonds is the fact that the bond line is visible.A higher bonding temperature is required so that this line becomes no longer visible, as observed in a previous study.In similar TiAl diffusion bonds assisted by Ni/Al nanolayers, the bond line begins to disappear at temperatures above 900 • C [15].However, these temperatures are too high, especially for Ti6Al4V, due to its low creep strength.The identification of the phases present at the interfaces was carried out through the combination of different characterization techniques such as EDS in SEM and TEM, EBSD, SAED and FFT.The need to use these techniques is related to the dimensions of the particles and layers formed during bonding, ranging from a few micrometers to nanometers.For example, the interaction volume of EDS in SEM is greater than the thickness of the two layers close to the TiAl base material or the thickness of the reaction layer of the Ti6Al4V and the multilayers.High resolution techniques and techniques with small interaction volume are therefore essential for the microstructural characterization of these interfaces, composed of thin layers and nanometric phases.The evaluation of the elemental distribution through EDS in TEM (Figures 4 and 5) confirms that at the center interface of all dissimilar joints, a larger layer of equiaxed grains composed essentially of Ni and Al is observed.The formation of these equiaxed grains is the result of the reaction of Ni and Al nanolayers during the bonding process.This multilayer reaction is essential for ensuring the bond and is well documented for TiAl alloys in previous studies [15][16][17].However, for the bonding to be successfully achieved, the reaction and adhesion between the base materials and the multilayers is also essential.A good adhesion/bond without the formation of very brittle phases is crucial for obtaining interfaces with good mechanical behavior.
EDS analysis in TEM clearly shows that the center of the interface consists mainly of Ni and Al.However, the V map reveals some bright points.These particles or grains enriched in V are mainly observed along the bond central line but also dispersed in the central NiAl layer.EDS and EBSD analyses in SEM did not detect the presence of these grains, probably due to their size being smaller than the interaction volume of these techniques.
In Figure 6 it is possible to observe the TEM image of the larger central zone of the interface.The SAED pattern from this region reveals spots that were indexed as the NiAl phase, but some were indexed as the Al8V5 phase.The presence of this phase has been reported by Maj et al. [21,22] as a reaction product of Ni(V)/Al reactive multilayers.In multilayers without the addition of vanadium The evaluation of the elemental distribution through EDS in TEM (Figures 4 and 5) confirms that at the center interface of all dissimilar joints, a larger layer of equiaxed grains composed essentially of Ni and Al is observed.The formation of these equiaxed grains is the result of the reaction of Ni and Al nanolayers during the bonding process.This multilayer reaction is essential for ensuring the bond and is well documented for TiAl alloys in previous studies [15][16][17].However, for the bonding to be successfully achieved, the reaction and adhesion between the base materials and the multilayers is also essential.A good adhesion/bond without the formation of very brittle phases is crucial for obtaining interfaces with good mechanical behavior.
EDS analysis in TEM clearly shows that the center of the interface consists mainly of Ni and Al.However, the V map reveals some bright points.These particles or grains enriched in V are mainly observed along the bond central line but also dispersed in the central NiAl layer.EDS and EBSD analyses in SEM did not detect the presence of these grains, probably due to their size being smaller than the interaction volume of these techniques.
In Figure 6 it is possible to observe the TEM image of the larger central zone of the interface.The SAED pattern from this region reveals spots that were indexed as the NiAl phase, but some were indexed as the Al 8 V 5 phase.The presence of this phase has been reported by Maj et al. [21,22] as a reaction product of Ni(V)/Al reactive multilayers.In multilayers without the addition of vanadium to the nickel target this phase is not observed, but they exhibit several defects and the deposition rate is low, since pure nickel is a ferromagnetic material [23].
to the nickel target this phase is not observed, but they exhibit several defects and the deposition rate is low, since pure nickel is a ferromagnetic material [23].to the nickel target this phase is not observed, but they exhibit several defects and the deposition rate is low, since pure nickel is a ferromagnetic material [23].On the Ti6Al4V side, the elemental EDS maps obtained in TEM (Figure 5) clearly show that the reaction layer is constituted by Al, Ni and Ti.The TEM image and SAED pattern in Figure 7 identified the AlNi 2 Ti phase in this layer.
On the Ti6Al4V side, the elemental EDS maps obtained in TEM (Figure 5) clearly show that the reaction layer is constituted by Al, Ni and Ti.The TEM image and SAED pattern in Figure 7  The EDS maps of Figure 5 also show the distribution of Ti, Al and V on the Ti6Al4V alloy.On the V map it is possible to observe not only the bright Al8V5 particles in the central AlNi layer, but also larger bright areas in the base material that must correspond to the grains of the β-Ti phase.Observing the Ni map, it is possible to detect Ni diffusion from the center of the interface towards the Ti6Al4V alloy, accumulating in regions adjacent to β-Ti grains.Ni diffusion is more intense on this side of the interface, extending for distances as long as 3 µm.
The diffusion of Ni to Ti6Al4V was analyzed in more detail by EBSD.Crystallographic orientation maps of Figure 8 were used to characterize the distribution of α-Ti and β-Ti phases of Ti6Al4V close to the interface.These maps show some dark unidentified areas due to the relief of the surface, visible in Figure 8a.This relief prevents the detection of the diffraction patterns of the saliences, hindering the identification of the phases in these regions.The areas that are composed of Ni rich grains were identified as Ti2Ni by indexing Kikuchi patterns by point analysis, as shown in Figure 9.The EDS maps of Figure 5 also show the distribution of Ti, Al and V on the Ti6Al4V alloy.On the V map it is possible to observe not only the bright Al 8 V 5 particles in the central AlNi layer, but also larger bright areas in the base material that must correspond to the grains of the β-Ti phase.Observing the Ni map, it is possible to detect Ni diffusion from the center of the interface towards the Ti6Al4V alloy, accumulating in regions adjacent to β-Ti grains.Ni diffusion is more intense on this side of the interface, extending for distances as long as 3 µm.
The diffusion of Ni to Ti6Al4V was analyzed in more detail by EBSD.Crystallographic orientation maps of Figure 8 were used to characterize the distribution of α-Ti and β-Ti phases of Ti6Al4V close to the interface.These maps show some dark unidentified areas due to the relief of the surface, visible in Figure 8a.This relief prevents the detection of the diffraction patterns of the saliences, hindering the identification of the phases in these regions.The areas that are composed of Ni rich grains were identified as Ti2Ni by indexing Kikuchi patterns by point analysis, as shown in Figure 9.The same microstructural characterization sequence was performed for the other dissimilar bonds between the titanium alloys.Table 1 presents the possible phases, the techniques used for the  The same microstructural characterization sequence was performed for the other dissimilar bonds between the titanium alloys.Table 1 presents the possible phases, the techniques used for the The same microstructural characterization sequence was performed for the other dissimilar bonds between the titanium alloys.Table 1 presents the possible phases, the techniques used for the identification of the different zones that constitute the interfaces and the thickness of each layer.It is important to point out that the combination of different characterization techniques was fundamental for the complete microstructural characterization of the interface.The identification of the reaction layer close to the TiNi base material was based on the indexation of the FFT of the area represented in the HRTEM image of Figure 10.From the analysis of these results it was possible to conclude that this zone consists of the AlNi 2 Ti phase.To sum up, the dissimilar diffusion bonding of titanium alloys assisted by nanolayers is achieved by the reaction of the multilayers, which provides good quality defect-free interfaces, and by the interdiffusion and reaction of the nanolayers with the base materials.
The larger central zone of the interfaces is composed mainly of nanometric NiAl grains, formed by the exothermic reaction of the multilayer.Grains of the Al8V5 phase are observed along the central bond line but also dispersed in this NiAl layer.These grains are formed by the reaction of Al with the V incorporated in the Ni nanolayers during sputtering.
If the base material is the TiAl alloy, two fine reaction layers consisting of AlNiTi and AlNi2Ti are formed due to the reaction between this alloy and the multilayers.These layers ensure the adhesion between the base material and the multilayers.When the base materials are Ti6Al4V and TiNi alloys, the bond is ensured by the formation of the AlNi2Ti layer.To sum up, the dissimilar diffusion bonding of titanium alloys assisted by nanolayers is achieved by the reaction of the multilayers, which provides good quality defect-free interfaces, and by the interdiffusion and reaction of the nanolayers with the base materials.
The larger central zone of the interfaces is composed mainly of nanometric NiAl grains, formed by the exothermic reaction of the multilayer.Grains of the Al 8 V 5 phase are observed along the central bond line but also dispersed in this NiAl layer.These grains are formed by the reaction of Al with the V incorporated in the Ni nanolayers during sputtering.
If the base material is the TiAl alloy, two fine reaction layers consisting of AlNiTi and AlNi 2 Ti are formed due to the reaction between this alloy and the multilayers.These layers ensure the adhesion between the base material and the multilayers.When the base materials are Ti6Al4V and TiNi alloys, the bond is ensured by the formation of the AlNi 2 Ti layer.
For Ti6Al4V joints to TiAl and to TiNi, an intense diffusion of Ni is observed from the interface towards the Ti6Al4V, extending up to 3 µm from the AlNi 2 Ti reaction layer.Ni accumulates adjacent to the β-Ti phase in the form of Ti 2 Ni grains.
For the TiAl to TiNi joint a new phase, TiNi 3 , is observed on the TiNi side of the interface, adjacent to the AlNi 2 Ti reaction layer and only in localized areas.
The formation of two reaction layers composed of Al-Ni-Ti phases close to TiAl is not observed at the interface of TiAl similar joints [15].However, these layers were observed at the interface of dissimilar joints of TiAl to steels or superalloys [16,17].
The TiNi to Ti6Al4V joints with Ni/Al nanolayers promote the formation of an interface with a more uniform microstructure than that obtained under the same processing conditions but with Ni/Ti nanolayers [18].With the Ni/Al multilayers it is possible to avoid the formation of TiNi and Ti 2 Ni in alternated layers observed in joints with Ni/Ti nanolayers, which may have a beneficial effect on the mechanical properties of the joints, representing an advantage in the use of this multilayered system.
The use of multilayers is effective for the dissimilar bonding of titanium alloys.For example, in the dissimilar bond between TiAl and Ti6Al4V, published studies report temperatures of 915-1000 • C and pressures of 20 to 80 MPa for the diffusion bond [11,12].With the multilayers it is possible to reduce these conditions to 800 • C and 20 MPa.This decrease is particularly important for the Ti6Al4V alloys and for the new generation of TiAl alloys, since these processing conditions avoid macroscopic plastic deformation, thus maintaining the dimensional stability of the base materials.
Regarding the TiNi to Ti6Al4V joints, the use of nanolayers does not significantly reduce the bonding conditions compared to those used in infrared brazing using an Ag-based braze alloy [13].However, the use of the nanolayers has a clear advantage when it is applied to this dissimilar joint, since it avoids the formation of low melting temperature Ag-rich phases, thus not compromising the service temperature of the joints.When compared with diffusion braze joints using TiNi and TiCuNi braze alloys, then the use of the nanolayers enables the reduction of the bonding temperature from 970 to 800 • C [14], which is a significant reduction.

Conclusions
The use of Ni/Al nanolayers is effective in obtaining defect-free interfaces in dissimilar diffusion bonding of titanium alloys.The joining of TiAl to Ti6Al4V, TiAl to TiNi and TiNi to Ti6Al4V, assisted by Ni/Al nanolayers, can be successfully processed at 800 • C, for 60 min and under a pressure of 20 MPa.The dissimilar joining of titanium alloys assisted by nanolayers is achieved by the reaction of the multilayers, which provides good quality defect-free interfaces, and by the interdiffusion and reaction of the nanolayers with the base materials.
The wider layer was observed in the central zone of all interfaces, which is composed of a mixture of NiAl and Al 8 V 5 nanometric grains, formed by the exothermic reaction of the multilayer.
For the TiAl to Ti6Al4V joints, two thin reaction layers, consisting of AlNiTi and AlNi 2 Ti, are formed close to the TiAl and one AlNi 2 Ti layer formed close to Ti6Al4V.Dispersed Ti 2 Ni particles were detected in the Ti6Al4V alloy.
For the TiAl to TiNi joints, intermetallic layers similar to those formed at the TiAl/Ti6Al4V bond were observed at the interface, whereas TiNi 3 dispersed particles were observed in the TiNi alloy.
When the base materials are Ti6Al4V and TiNi alloys, the bond has fewer intermetallic layers, AlNi 2 Ti layers being detected close to both base materials.The dispersed particles observed in the Ti6Al4V alloy are composed by Ti 2 Ni.
Compared with the diffusion bonding of these alloys without the use of multilayers, a significant decrease in bonding temperature and processing pressure is achieved.This decrease is very important, taking into consideration the mechanical response of the Ti6Al4V alloy and the new TiAl alloys at higher temperatures and higher pressures.
The application of these multilayers also presents a clear advantage in relation to brazing as a process of joining these dissimilar alloys.In fact, although being possible to obtain brazed joints at temperatures similar to those observed in this study, especially in bonding TiNi to Ti6Al4V, brazing at these temperatures is only possible with the use of Ag-based alloys, consequently limiting the application of components to low service temperatures.Thus, by replacing the brazing process with the multilayer-assisted diffusion bonding process, similar bonding conditions can be obtained without compromising the mechanical properties at high temperatures.

Figure 1 .
Figure 1.Scanning electron microscopy (SEM) image of a TiAl/Ti6Al4V interface produced at 700 °C under a pressure of 20 MPa using Ni/Al nanolayers.

Figure 1 .
Figure 1.Scanning electron microscopy (SEM) image of a TiAl/Ti6Al4V interface produced at 700 • C under a pressure of 20 MPa using Ni/Al nanolayers.

Figure 3 .
Figure 3. SEM images and schematic draw of the interfaces of the (a) TiAl/Ti6Al4V, (b) TiAl/TiNi and (c) TiNi/Ti6Al4V joints produced at 800 °C under a pressure of 20 MPa using Ni/Al nanolayers.

Figure 4 .
Figure 4. (a) Scanning transmission electron microscopy (STEM) image of the TiNi/Ti6Al4V interface close to the TiNi alloy and EDS elemental maps of (b) Al, (c) Ti, (d) Ni and (e) V.

Figure 3 .
Figure 3. SEM images and schematic draw of the interfaces of the (a) TiAl/Ti6Al4V, (b) TiAl/TiNi and (c) TiNi/Ti6Al4V joints produced at 800 • C under a pressure of 20 MPa using Ni/Al nanolayers.

Figure 3 .
Figure 3. SEM images and schematic draw of the interfaces of the (a) TiAl/Ti6Al4V, (b) TiAl/TiNi and (c) TiNi/Ti6Al4V joints produced at 800 °C under a pressure of 20 MPa using Ni/Al nanolayers.

Figure 4 .
Figure 4. (a) Scanning transmission electron microscopy (STEM) image of the TiNi/Ti6Al4V interface close to the TiNi alloy and EDS elemental maps of (b) Al, (c) Ti, (d) Ni and (e) V.

Figure 4 .
Figure 4. (a) Scanning transmission electron microscopy (STEM) image of the TiNi/Ti6Al4V interface close to the TiNi alloy and EDS elemental maps of (b) Al, (c) Ti, (d) Ni and (e) V.

Figure 5 .Figure 6 .
Figure 5. (a) STEM image of the TiNi/Ti6Al4V interface close to the Ti6Al4V alloy and EDS elemental maps of (b) Al, (c) Ti, (d) Ni and (e) V.

Figure 6 .
Figure 6.(a) Transmission electron microscopy (TEM) image of the grains that composed the center of the TiNi/Ti6Al4V interface and (b) Selected area electron diffraction (SAED) of the selected area indicated in (a) and the indexing scheme of the diffraction pattern.

Figure 7 .
Figure 7. (a) TEM image of the TiNi/Ti6Al4V joint and (b) SAED of the selected area indicated in (a) and the indexing scheme of the AlNi2Ti phase.

Figure 7 .
Figure 7. (a) TEM image of the TiNi/Ti6Al4V joint and (b) SAED of the selected area indicated in (a) and the indexing scheme of the AlNi 2 Ti phase.

Figure 9 .
Figure 9. Kikuchi patterns of the point 2 indicated on Figure 8a indexed as Ti 2 Ni phase (a) Kikuchi pattern and (b) indexation of the pattern presented in (a).

Metals 2018, 8 ,Figure 10 .
Figure 10.(a) High resolution TEM (HRTEM) image of the reaction layer close to the TiNi of the TiNi/Ti6Al4V joint and (b) Fast Fourier transform (FFT) of the selected area indicated in (a) and the indexing scheme of the AlNi2Ti phase.

Figure 10 .
Figure 10.(a) High resolution TEM (HRTEM) image of the reaction layer close to the TiNi of the TiNi/Ti6Al4V joint and (b) Fast Fourier transform (FFT) of the selected area indicated in (a) and the indexing scheme of the AlNi 2 Ti phase.

Table 1 .
Phase identification of the zones indicated in Figure3that comprised the interfaces of the titanium alloys dissimilar joints produced at 800 • C under a pressure of 20 MPa.