Plastic anisotropy and the role of non-basal slip in magnesium alloy AZ31B

The activity of non-basal slip systems and dynamic recovery at room temperature in fine-grained AZ31B magnesium alloys

Magnesium alloys have received an increasing interest in the past 12 years for potential applications in the automotive, aircraft, aerospace, and electronic industries. Many of these alloys are strong because of solid-state precipitates that are produced by an age-hardening process. Although some strength improvements of existing magnesium alloys have been made and some novel alloys with improved strength have been developed, the strength level that has been achieved so far is still substantially lower than that obtained in counterpart aluminum alloys. Further improvements in the alloy strength require a better understanding of the structure, morphology, orientation of precipitates, effects of precipitate morphology, and orientation on the strengthening and microstructural factors that are important in controlling the nucleation and growth of these precipitates. In this review, precipitation in most precipitation-hardenable magnesium alloys is reviewed, and its relationship with strengthening is examined. It is demonstrated that the precipitation phenomena in these alloys, especially in the very early stage of the precipitation process, are still far from being well understood, and many fundamental issues remain unsolved even after some extensive and concerted efforts made in the past 12 years. The challenges associated with precipitation hardening and age hardening are identified and discussed, and guidelines are outlined for the rational design and development of higher strength, and ultimately ultrahigh strength, magnesium alloys via precipitation hardening.

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Precipitation and Hardening in Magnesium Alloys

Magnesium and its alloys do not in general undergo the same extended range of plasticity as their competitor structural metals. The present work is part I of a study that examines some of the roles deformation twinning might play in the phenomenon. A series of tensile test results are reported for the common wrought alloy AZ31. These data are employed in conjunction with a simple constitutive model to argue that View the MathML source twinning (which gives extension along the c-axis) can increase the uniform elongation in tensile tests. This effect appears to be similar to that seen in Ti, Zr and Cu–Si and in the so called TWIP phenomenon in steel.

Twinning and the ductility of magnesium alloys Part I: “Tension” twins

Friction stir processing (FSP), developed based on the basic principles of friction stir welding (FSW), a solid-state joining process originally developed for aluminum alloys, is an emerging metalworking technique that can provide localized modification and control of microstructures in near-surface layers of processed metallic components. The FSP causes intense plastic deformation, material mixing, and thermal exposure, resulting in significant microstructural refinement, densification, and homogeneity of the processed zone. The FSP technique has been successfully used for producing the fine-grained structure and surface composite, modifying the microstructure of materials, and synthesizing the composite and intermetallic compound in situ. In this review article, the current state of the understanding and development of FSP is addressed.

Friction stir processing technology: A review

Effect of lamellar spacing on microstructural instability and creep behavior of a lamellar TiAl alloy

Strengthening of a fully lamellar TiAl + W alloy by dynamic precipitation of β phase during long-term creep

Single-phase regions in Mo-rich Mo–Si–B alloys at 1800 °C were experimentally determined using a field-emission (FE) gun-type electron probe micro-analyzer (EPMA) in this study. A quantitative analysis by FE-EPMA was conducted with the calibration method we applied in our previous study to improve the accuracy in the B measurements. The compositional ranges of the determined Mo solid solution, silicide and boride phases were in good agreement with those of Mo–Si and Mo–B binary phase diagrams. On the other hand, the determined solubility of B in Mo solid solution, Mo 3 Si and T 1 (Mo 5 Si 3 ) were quite different from that indicated in previously reported ternary phase diagrams. The compositional region of the T 2 (Mo 5 SiB 2 ) single-phase ranges from 9.7 to 13.3 at% for Si and from 23.5 to 26.8 at% for B. The following two points were made clear by the ternary phase diagram as determined in this study. One is that no stoichiometric T 2 composition is in the T 2 single-phase region, confirming no T 2 single-phase material can be obtained at the stoichiometric composition at 1800 °C. The another is that the T 2 region of this study expands to a Si-rich area from the stoichiometric composition.

Kouichi Maruyama

Papers

Effect of lamellar spacing on microstructural instability and creep behavior of a lamellar TiAl alloy

Strengthening of a fully lamellar TiAl + W alloy by dynamic precipitation of β phase during long-term creep

Compositional regions of single phases at 1800 °C in Mo-rich Mo–Si–B ternary system

Effects of discontinuour coarsening of lamellae on creep strength of fully lamellar TiAl alloys

Grain size dependence of active slip systems in an AZ31 magnesium alloy