Precipitate strengthening mechanisms in magnesium zinc alloy single crystals

Chun, Jong Ahn; Byrne, J. G.

doi:10.1007/bf00549777

Cited by 103 publications

(59 citation statements)

References 10 publications

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“…They are identified as b 0 1 and b 0 2 phases, which are typically observed in Mg-Zn based alloys. The b 0 1 phase has the orientation relationship (OR) with the magnesium matrix described as ð2 as reported previously[33][34][35][36]. The double-aging results in the significant refinement of these precipitates as shown inFig.…”

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confidence: 84%

Strong and ductile heat-treatable Mg–Sn–Zn–Al wrought alloys

et al. 2015

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a b s t r a c tA newly developed Mg-Sn-Zn-Al based alloy shows substantial strengthening by artificial aging. A Na-doped Mg-5.4Sn-4.2Zn-2.0Al-0.2Mn-0.1Na (TZAM5420À0.1Na) (wt.%) alloy exhibited a significant increase in yield strength from 243 to 347 MPa by a T6 treatment due to the uniform dispersion of nanoscale precipitates by aging. The trace addition of Na causes the formation of Sn-Na co-clusters in the early stage of aging, which provides heterogeneous nucleation sites for Mg 2 Sn precipitates. However, Na strongly segregates at grain boundaries and this degrades the ductility significantly. To overcome this problem, we developed a Na-free Mg-6.6Sn-5.9Zn-2.0Al-0.2Mn (TZAM6620) alloy, in which nano-scale MgZn 2 precipitates are uniformly dispersed by double aging. Pre-aging caused the formation of Zn-rich Guinier Preston zones, which acted as heterogeneous nucleation sites for the MgZn 2 precipitates. The double-aged TZAM6620 alloy exhibited a very high yield strength of 370 MPa with large elongation of 14%.

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confidence: 84%

Strong and ductile heat-treatable Mg–Sn–Zn–Al wrought alloys

et al. 2015

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“…The metastable phase b 0 1 , which is also described as MgZn¢, [52,59] forms as 0001 ½ a rods, whereas the metastable phase b phases were suggested to have a hexagonal structure (a = 0.520 nm, c = 0.857 nm) [56,[60][61][62][63] that is identical to that of MgZn 2 (space group P6 3 /mmc, a = 0.5221 nm, c = 0.8567 nm). [64] Another hexagonal structure (a = 0.556 nm, c = 0.521 nm) was also reported for b 0 1 , [59] but it has not been confirmed so far.…”

Section: Phase Equilibria and Precipitationmentioning

confidence: 99%

Precipitation and Hardening in Magnesium Alloys

Nie

2012

Metall Mater Trans A

1,394

519

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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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“…[7] In the Mg-Zn alloy, the intermetallic precipitates taking part in the age-hardening process include the rectangular rods b 1 ' with the long axis parallel to the [0001] Mg direction and hexagonal tablets b 2 ' with the large face parallel to the basal plane of the magnesium matrix. [8] In the WE alloys, the ageing process is connected with the precipitations of b' (Mg 12 NdY), b 1 ' and final equilibrium phase b' (Mg 14 Nd 2 Y). [9] The metastable b' phase has a basecentered orthorhombic Bravais lattice, with lattice parameters of a=0.640 nm, b=2.223 nm and c=0.521 nm.…”

Section: Reviewsmentioning

confidence: 99%

Intermetallics in Magnesium Alloys

Hort¹,

Huang²,

Kainer³

2006

Adv Eng Mater

217

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Intermetallic phases can be found in almost every magnesium alloy. These intermetallic compounds play a very important role in optimizing the microstructure and mechanical properties. The present paper reviews the effects of intermetallics in magnesium alloys mainly based on their stabilities: dissolvable intermetallics at low temperatures and thermal stable intermetallics at elevated temperatures. The effects of intermetallics are discussed in the age hardenable and creep resistant magnesium alloys, separately. Finally, the further investigations are remarked on the intermetallics, including their precipitation processes, crystal structures and crystallographic orientation relations with magnesium matrix. The aim is to supply useful information in developing new wrought and creep‐resistant magnesium alloys which will be used in the powertrain at elevated temperatures.

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Precipitate strengthening mechanisms in magnesium zinc alloy single crystals

Cited by 103 publications

References 10 publications

Strong and ductile heat-treatable Mg–Sn–Zn–Al wrought alloys

Strong and ductile heat-treatable Mg–Sn–Zn–Al wrought alloys

Precipitation and Hardening in Magnesium Alloys

Intermetallics in Magnesium Alloys

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