Fundamentals of Superior Properties in Bulk NanoSPD Materials

Figures & data

Figure 1. Typical bright-field TEM images of a grain with high density of deformation nanotwins in UFG Cu that was subjected to ECAP and subsequent cryogenic rolling.[12]

Figure 2. Tomographic image of nanostructure of UFG Al alloy 7075. Segregations of alloying elements on grain boundaries and at triple junctions are shown.[22]

Figure 3. UFG structure of Al alloy 6061 after ECAP in parallel channels (four passes): nanosized precipitations in grains are clearly visible in areas A and B at higher magnification.[24]

Figure 4. Engineering stress–strain curves of the UFG alloys Al 1570 (a) and Al 7475 (b) processed by HPT in comparison with standard treatment.[23]

Figure 5. Empirical correlation between the fatigue limit and the UTS for UFG Ti and Al alloys.[59]

Figure 6. Wöhler plot for Mg alloy ZK60 in the as-received condition (open symbols) and after processing by integrated direct extrusion and ECAP.[63]

Figure 7. Elongation vs. strain rate at 473 K for a Mg–8% Li alloy in the cast condition, after casting and extrusion, and after casting and extrusion followed by ECAP.[75]

Figure 8. Appearance of a tensile specimen of a ZK60 magnesium alloy pulled to failure at 3,050% after extrusion and ECAP; the upper specimen is untested.[76]

Figure 9. (a) Vickers microhardness and (b) electrical resistivity/conductivity plotted against equivalent strain for samples processed by SPD methods.[82]

Figure 10. Variation of MR ratio with magnetic field in two different directions (X and Y) for HPT sample after N = 25 revolutions, where the definition of X and Y is as illustrated.[102]

Figure 11. Hydrogen storage kinetics showing high performance of ECAP-processed ZK60 alloy compared to its ball-milled counterpart (desorption,[104,105]).

Figure 12. Long time characteristics of hydrogen storage (absorption) measured in the ECAP-processed ZK 60 alloy (from [105]).

Figure 13. Hydrogen absorption of ZK60 after HPT processing at room temperature after different numbers of cycles of hydrogen loading and unloading, according to [108].

Figure 14. Hydrogen absorption of MgH₂ after cold rolling at room temperature after different numbers of cycles of hydrogen loading and unloading, according to [108].

Figure 15. Pressure–concentration (P–C) isotherms at 303 K for samples processed by (a) annealing at 1,273 K for 24 h and (b) HPT processing for 10 turns. Fourth cycle in (b) was terminated after absorption for conducting XRD analysis.[121]

Figure 16. Raman spectra after HPT processing for 20 revolutions and annealing. Each Raman spectrum was taken at about 2 mm from the disk center.[127]

Figure 17. PL spectra after HPT processing for 20 revolutions and annealing. Some of the sharp luminescence peaks are due to laser plasma lines.[127]

Figure 18. Temperature dependence of the magnetization M(T) of Nb in the magnetic field H = 2 Oe. (a) As-received sample; (b)–(e) HPT-processed samples with different revolution numbers N.[141]

Figure 19. Variation of (a) transition temperature for superconductivity, T_c, and (b) Vickers microhardness, UTS, and bending strength against annealing time for samples processed by HPT for N = 50 turns and annealed at 573 K.[143]

Figure 20. Electrical conductivity (a) and Seebeck coefficient (b) vs. temperature, for p-type Bi_0.5Sb_1.5Te_3.0 after processing by the Vertical Bridgman Method and HPT.[147]

Figure 21. Dependence of carrier mobility µ on preferred orientation angle P_0.2, after applying different numbers of passes of Route A ECAP (labeled ‘ECAE’ in the original figure (from [148]).

Figure 22. Increase in ZT in an n-type skutterudite after HPT processing at temperatures 400°C and 500°C. Letters A, B, and C refer to different strains achieved by HPT (from [145]).

Figure 23. (a) Increase in ZT to a world record ZT = 1.9 by HPT processing; the increase is mainly due to the decrease in thermal lattice conductivity λ_ph shown in (b) [151]

Figure 24. 3.5 mm diameter Timplant^® (above) and the new 2.4 mm diameter Nanoimplant^® produced from superstrong n-Ti (below).[156,158]

Figure 25. Stress–strain curves for initial and SPD-processed Ti-45Nb samples. HE-5 stands for 97% area reduction by HE, HPT-4-X for High-Pressure Torsion at a pressure of 4 GPa and X revolutions.[168]

Figure 26. Young's modulus E as measured by nanoindentation (open circles), and microhardness H (open triangles), as a function of von Mises equivalent strain ε, for R & F (a) and HPT samples (b). The values of E were also calculated from texture data (full squares).[168]

Figure 27. Microhardness of samples of Mg0.2Zn0.5Ca as a function of homologous annealing temperature T/T_m (T and T_m denoting the annealing temperature and the melting temperature in Kelvin, respectively): (i) after 1 h annealing (full circles) and (ii) after HPT processing and annealing (squares and triangles). HPT processing was done at a pressure of 4 GPa up to von Mises equivalent strains ε indicated.[183]

Figure 28. Principles of nanostructural design of bulk nanostructured materials.[5]

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