“…CMT HAZ and P-MIG HAZ are both dominated by LAGB, but the LAGB in CMT HAZ occupies a larger proportion and has larger distortion energy. LAGBs are more likely to cause changes in the crack expansion path [42] and are more effective in blocking the crack expansion, thus improving plasticity and toughness. Figure 17 Grain Boundary Distribution Map of P-MIG HAZ and CMT HAZ (the red grain boundary is the LAGB, and the green grain boundary is the SAGB: (a) P-MIG HAZ, (b) CMT HAZ, (c) Comparison of grain boundary distribution in Figure 17(a,b).…”
Section: Resultsmentioning
confidence: 99%
“…CMT HAZ and P-MIG HAZ are both dominated by LAGB, but the LAGB in CMT HAZ occupies a larger proportion and has larger distortion energy. LAGBs are more likely to cause changes in the crack expansion path [42] and are more effective in blocking the crack expansion, thus improving plasticity and toughness.…”
Section: Haz Microstructure and Property Analysismentioning
This paper focuses on pulse metal inert gas welding (P-MIG) and cold metal transfer (CMT) of 6082-T6 aluminium alloy. The microstructure and properties of joints were analysed and the phase transformation of the welding zones (WZ) was calculated using JMatPro. The results showed that CMT joints are better than P-MIG joints in tensile strength and hardness. The main reason is that the average grain size and the second phase size of CMT joints are smaller than those of P-MIG joints. Moreover, the larger number of large-angle grain boundaries (LAGB), diffusely distributed Al3Mg2 and Al6Mn phases in CMT WZ, as well as a small amount of distributed Al3Zr, are beneficial to the joints properties too.
“…CMT HAZ and P-MIG HAZ are both dominated by LAGB, but the LAGB in CMT HAZ occupies a larger proportion and has larger distortion energy. LAGBs are more likely to cause changes in the crack expansion path [42] and are more effective in blocking the crack expansion, thus improving plasticity and toughness. Figure 17 Grain Boundary Distribution Map of P-MIG HAZ and CMT HAZ (the red grain boundary is the LAGB, and the green grain boundary is the SAGB: (a) P-MIG HAZ, (b) CMT HAZ, (c) Comparison of grain boundary distribution in Figure 17(a,b).…”
Section: Resultsmentioning
confidence: 99%
“…CMT HAZ and P-MIG HAZ are both dominated by LAGB, but the LAGB in CMT HAZ occupies a larger proportion and has larger distortion energy. LAGBs are more likely to cause changes in the crack expansion path [42] and are more effective in blocking the crack expansion, thus improving plasticity and toughness.…”
Section: Haz Microstructure and Property Analysismentioning
This paper focuses on pulse metal inert gas welding (P-MIG) and cold metal transfer (CMT) of 6082-T6 aluminium alloy. The microstructure and properties of joints were analysed and the phase transformation of the welding zones (WZ) was calculated using JMatPro. The results showed that CMT joints are better than P-MIG joints in tensile strength and hardness. The main reason is that the average grain size and the second phase size of CMT joints are smaller than those of P-MIG joints. Moreover, the larger number of large-angle grain boundaries (LAGB), diffusely distributed Al3Mg2 and Al6Mn phases in CMT WZ, as well as a small amount of distributed Al3Zr, are beneficial to the joints properties too.
“…Nokhrin et al [88] performed a thorough study in which they treated AlZr alloys with additions of Si, Nb, and rare earth elements via the SPD method of ECAP followed by RS and annealing to introduce the formation of the UFG microstructure with the average grain size of ~2 µm and nano-sized Al 3 (Zr,Hf,Er) precipitates, therein achieving a Vickers microhardness that exceeded 480 HV. Similarly, Bochvar et al [89] used combinations of cold ECAP, cold RS, and ageing to prepare AlMgSi alloys with additions of Sc, Hf, and Zr featuring optimized nano-sized precipitates of β and β' secondary phases and a UTS reaching to 400 MPa. Jin et al [90] applied solution treatment and ageing in combination with RS to an AlMgSiCu alloy.…”
Rotary swaging is an industrially applicable intensive plastic deformation method. Due to its versatility, it is popular, especially in the automotive industry. Similar to the well-known methods of severe plastic deformation (SPD), rotary swaging imparts high shear strain into the swaged materials and thus introduces grain refinement down to a very fine, even ultra-fine, level. However, contrary to SPD methods, one of the primary characteristics of which is that they retain the shapes and dimensions of the processed sample, rotary swaging enables the imparting of required shapes and dimensions of workpieces (besides introducing structure refinement and the consequent enhancement of properties and performance). Therefore, under optimized conditions, swaging can be used to process workpieces of virtually any metallic material with theoretically any required dimensions. The main aim of this review is to present the principle of the rotary swaging method and its undeniable advantages. The focus is primarily on assessing its pros and cons by evaluating the imparted microstructures.
“…Metal matrix composites with Mg 2 Si as reinforcements have been widely used in automotive and aerospace fields due to their excellent properties such as high specific strength and high‐temperature resistance. [ 1 ] The intermetallic compound Mg 2 Si has excellent intrinsic characteristics such as low density (1.99 × 10 3 Kg m −3 ), high elastic modulus (120 GPa), and low thermal expansion coefficient (7.5 × 10 −6 K −1 ). As an attractive reinforcement, Mg 2 Si possesses great potential to improve the comprehensive performance of aluminum alloys.…”
Herein, the microstructure control and performance evolution of hypereutectic Al–20Mg2Si alloy with the addition of novel Al–3.3Ca–10Sb master alloy are investigated. It is found that AlCa11Sb9 and CaSb2 compounds are successfully synthesized through in situ melt reaction of masteralloy. With 0.45 wt% Al–3.3Ca–10Sb master alloy addition, primary Mg2Si particles in hypereutectic Al–20Mg2Si alloy are significantly refined from more than 150 μm to 10.7 μm, which are accompanied with the 3D morphologies changing from dendrites to octahedrons. After heat treatment, Brinell hardnesses of Al–20Mg2Si alloys are remarkably improved to 112 HB. Furthermore, it is also found that the cooling rate of Al–3.3Ca–10Sb master alloys has certain influence on the refinement effect of Al–Mg2Si alloys. The excellent complex modification of this master alloy on Al–20Mg2Si alloy can be attributed to the existence of CaSb2 particles as the heterogeneous nucleation sites of Mg2Si particles and the inhibiting growth effect of residual Ca atoms adsorbed on the surface of Mg2Si phase.
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