Strain path dependence of the precipitate size evolution of an Al–Mg–Li alloy under combined thermal and mechanical loading

Murken, J.; Höhner, R.; Skrotzki, Birgit

doi:10.1016/s0921-5093(03)00596-3

Cited by 13 publications

(16 citation statements)

References 37 publications

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“…1016/j.ijplas.2009.03.002 depending on the solder shape (Dutta et al, 2005;Gong et al, 2006). Likewise in Al and Ni containing alloys, used in aerospace applications, high homologous temperatures give rise to second particle growth and even phase transformation, thereby the microstructure depends strongly on the loading conditions applied (Murken et al, 2003). Precipitate coarsening in particular reduces strength when dislocation bowing is the rate-controlling creep mechanism (Manonukul et al, 2002), but also transformation-mismatch plasticity related to second phase transformation could contribute to creep (Zwigl and Dunand, 2001).…”

Section: Introductionmentioning

confidence: 99%

Precipitate coarsening-induced plasticity: Low temperature creep behaviour of tempered SAE 52100

Morra

Radelaar

Yandouzi

et al. 2009

International Journal of Plasticity

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Section: Introductionmentioning

confidence: 99%

Precipitate coarsening-induced plasticity: Low temperature creep behaviour of tempered SAE 52100

Morra

Radelaar

Yandouzi

et al. 2009

International Journal of Plasticity

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“…The third type of precipitate consists of small black cuboids, which are randomly distributed in the a-Al. Comparing the TEM image of the Li alloy with literature data about Li-containing alloys [24,25], the third precipitate can be identified as the d' Al 3 Li phase (which coexists with two types of Mg 2 Si compounds). A confirmation of the particle composition by EDX measurements is not possible because the light element Li cannot be detected by energy dispersive analysis.…”

Section: Microstructure and Phases Composition Changes During Artificmentioning

confidence: 81%

EFFECT OF ADDITIONAL ALLOYING AND HEAT TREATMENT ON THE PHASE COMPOSITION AND MORPHOLOGY IN Al-Mg-Si TYPE CASTING ALLOY

Boyko

Czekaj²,

Warmuzek

et al. 2017

mafe

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The structure of permanent mold and high pressure die castings of the AlMg5Si2Mn alloy after alloying with Li and Sc has been investigated by scanning and transmission electron microscopy, hardness and microhardness measurements, energy dispersive X-ray analysis. Three conditions, as cast, solution treated and aged, were investigated. It was shown that in as-cast state, the structure of an alloy having the nominal composition AlMg5Si2Mn consists of four phases: first-the Al based solid solution, second-the (Al) + (Mg 2 Si) eutectic, third-the primary Mg 2 Si crystals and fourth-the a-Al(Mn, Fe)Si phase. Similar phases were observed in the alloys containing Sc or Li. After two days of storing in an as-cast condition, the solid solution in all tested alloys decomposes and forms zebra-crossing shaped precipitates. TEM examinations revealed that these precipitates nucleate heterogeneously on dislocations. The solution treatment at 575.0°C results in spheroidization of the Mg 2 Si lamellas, dissolution of the precipitates and formation of a-Al(Mn, Fe)Si dispersoids, nucleating on the surfaces of Mg 2 Si lamellas. In the Sc containing alloys, the formation of Al 3 Sc was detected after 120 min soaking. Further heating resulted in the growth of these precipitates. Aging of the Al-Mg-Si alloys leads to an increase of hardness in all studied alloys. This effect is mainly related to precipitation strengthening, via solid solution decomposition and formation of b''-phase. In Li-alloyed specimens, plates of b Mg 2 Si phase were observed together with small cubic-shaped d' Al 3 Li precipitates.

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“…On the other hand, by adding Li to the alloy, nucleation of the T 1 phase constitutes the highest nanometric scale alloy-strengthening feature. This phase has a hexagonal (hcp) structure with lattice parameters a = 4.97, and c = 9.35 Å, and plate-like morphology with large aspect ratio of which the longer edge (needle) lying on [111] Al planes and orientation relationship (0001)-T 1 || (100) Al . In particular, this phase shows its maximum strengthening effect when the needle-shaped edge of the precipitates lye as to have (0001) T1 habit planes || (111) Al , and a [10,11] T1 || Al 110 matrix plane.…”

Section: Introductionmentioning

confidence: 99%

“…This phase has a hexagonal (hcp) structure with lattice parameters a = 4.97, and c = 9.35 Å, and plate-like morphology with large aspect ratio of which the longer edge (needle) lying on [111] Al planes and orientation relationship (0001)-T 1 || (100) Al . In particular, this phase shows its maximum strengthening effect when the needle-shaped edge of the precipitates lye as to have (0001) T1 habit planes || (111) Al , and a [10,11] T1 || Al 110 matrix plane. The T 1 phase has a space group P6/mmm [29] and it has been shown to be shearable by dislocations introduced during plastic deformation techniques [29][30][31].…”

Section: Introductionmentioning

confidence: 99%

High-Temperature Equal-Channel Angular Pressing of a T6-Al-Cu-Li-Mg-Ag-Zr-Sc Alloy

Cabibbo

Paoletti

2021

JMMP

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Equal-channel angular pressing (ECAP) is known to induce significant grain refinement and formation of tangled dislocations within the grains. These are induced to evolve to form low-angle boundaries (i.e., cell boundaries) and eventually high-angle boundaries (i.e., grain boundaries). On the other hand, the precipitation sequence of age hardening aluminum alloys can be significantly affected by pre-straining and severe plastic deformation. Thus, ECAP is expected to influence the T6 response of aluminum alloys. In this study, a complex Al-Cu-Mg-Li-Ag-Zr-Sc alloy was subjected to ECAP following different straining paths. The alloy was ECAP at 460 K via route A, C, and by forward-backward route A (FB-route A) up to four passes. That is, ECAP was carried out imposing billet rotation between passes (route A), billet rotation by +90° between passes (route C), and billet rotation by +90° and inversion upside down between passes (FB-route A). The alloy was also aged at 460 K for different durations after ECAP. TEM microstructure inspections showed a marked influence of the different shearing deformations induced by ECAP on the alloy aging response. The precipitation kinetics of the different hardening secondary phases were affected by shearing deformation and tangled dislocations. In particular, the T1-Al2CuLi phase was the one that mostly showed a precipitation sequence speed up induced by the tangled dislocations formed during ECAP. The T1 phase was found to grow with aging time according to the Lifshitz-Slyozov-Wagner low-power regime.

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Strain path dependence of the precipitate size evolution of an Al–Mg–Li alloy under combined thermal and mechanical loading

Cited by 13 publications

References 37 publications

Precipitate coarsening-induced plasticity: Low temperature creep behaviour of tempered SAE 52100

Precipitate coarsening-induced plasticity: Low temperature creep behaviour of tempered SAE 52100

EFFECT OF ADDITIONAL ALLOYING AND HEAT TREATMENT ON THE PHASE COMPOSITION AND MORPHOLOGY IN Al-Mg-Si TYPE CASTING ALLOY

High-Temperature Equal-Channel Angular Pressing of a T6-Al-Cu-Li-Mg-Ag-Zr-Sc Alloy

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