Fig. 1 a OM, b SEM microstructures of the initial alloy for the study

Fig. 2 A schematic representation of the thermo-mechanical treatment (TMT) process

Fig. 3 a X-ray diffraction patterns of the Ti6Al4V-5Cu alloy after hot rolling, b magnified image of selected diffraction areas of a. The legend expressed the initial alloy for study (OI) and various thickness reduction ratios of 15%, 58%, and 73%

Fig. 4 a DSC curve of as cast Ti6Al4V-5Cu alloy, b OM observation of the heat-treated sample at 920 °C for 1 h, and exposed to slower air-cooling rate (AC), c SEM metallographic revealing the formation of kinked α lamellar structures and presence of β phase at 790 °C

Fig. 5 OM images demonstrating the effect of hot rolling deformation on microstructure evolution of the Ti6Al4V-5Cu alloy at TRR’s of: a 15%, b 58%, c 73%. EBSD images showing the grain structure in the alloy deformed at TRR’s of: d 15%, e 58%, f 73%

Fig. 6 IPF maps obtained during deformation of Ti6Al4V-5Cu alloy at various TRR’s of: a 15%, b 58%, c 73%

Fig. 7 Relationship plot showing the influence of grain rotation on the texture fiber separation angle to maintain the BOR of {0001}α//{110}β on the 15% hot-rolled Ti6Al4V-5Cu alloy

Fig. 8 Texture evolution of the α phase in Ti6Al4V-5Cu alloy obtained during hot rolling in various TRR’s of: a 15%, b 58%, c 73%

Fig. 9 Relationship plot showing the influence of grain rotation on the α/β fiber texture interface separation angle between {0001}α and {110}β of the 58% hot rolled Ti6Al4V-5Cu alloy

Fig. 10 Texture evolution of the β phase in Ti6Al4V-5Cu alloy observed during hot rolling in various TRR’s: a 15%, b 58%, c 73%

Fig. 11 Relationship plot showing the influence of grain rotation on the α/β fiber texture separation angle between {0001}α and {110}β of the 73% hot rolled Ti6Al4V-5Cu alloy

Fig. 12 a High resolution TEM investigation showing that an activated prismatic and pyramidal slip planes along the [$\overline{2 }$ 4 $\overline{2 }$ 3], and Ti2Cu intermetallic compound, b basal, prismatic, and pyramidal slip plane in the [2 $\overline{1 }\overline{1 }$ 0] and [1 $\overline{2 }$ 1 $\overline{3 }$] slip directions observed on the 15% deformed sample

Fig. 13 a SADP using TEM at lower magnification, b the higher magnification of the portion, Pt.1, revealed that the Ti6Al4V-5Cu alloy after 58% thickness reduction was made up of α pyramidal plane along [01 $\overline{1 }$ 1] and, β of [$\overline{2 }$ 33] and [$\overline{1 }$ 23] slip directions c

Fig. 14 Selected high bright diffraction pattern using TEM investigation revealed that the Ti6Al4V-5Cu alloy after a 73% thickness reduction was made up of various activated slip planes

Fig. 15 Selected high bright fields of diffraction obtained using TEM investigation revealed that the 73% deformed Ti6Al4V-5Cu alloy was composed of slip planes of: α (hcp) pyramidal along the [$1\overline{2 }$ 1 $\overline{3 }$], [01 $\overline{1 }$ 2], and β of [$\overline{1 }$ 11], [$\overline{2 }$ 33], [01 $\overline{3 }$], and [113]

Fig. 16 Grain boundary misorientation angle distributions in the Ti6Al4V-5Cu alloy deformed at various thickness reduction ratios of: a 15%, b 58%, c 73%. The peaks at 65$^\circ$ and 85$^\circ$ correspond to {11 $\overline{2 }$ 2} < 11 $\overline{2 }\overline{3 }$> compressive twins and {10 $\overline{1 }$ 2} < 10 $\overline{1 }\overline{1 }$> tensile twins, respectively

Fig. 17 a Hardness (in kgf/mm2), b true stress-strain relationship on the hot rolled Ti6Al4V-5Cu alloy at various TRR’s of 15%, 58%, and 73%

Fig. 18 SEM fracture investigation of the hot-rolled Ti6Al4V-5Cu alloy at various thickness reduction ratios of 15% a and b, 58% c and d, 73% e and f