Role of the β-phase in grain boundary and dislocation anelasticity in binary Al–Mg alloys

Golovin, I.S.; Mikhaylovskaya, A. V.; Sinning, H.‐R.

doi:10.1016/j.jallcom.2013.06.138

Cited by 47 publications

(21 citation statements)

References 35 publications

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“…For example, the Zener peak often present in solution treated and quenched Al-Cu alloys at 173-175 ∘ C and 1 Hz [1] is not observed in our results. If for AA 2024 (which was solution treated and quenched) the peak is not present, this may be due to (1) presence of GP-II zones, (2) the effect of the other elements present in this alloy aside from Cu, (3) the formation of phase , causing a decline of the Zener peak, which may eventually vanish when phase formation is complete [1], or, (4) most likely, the Cu content in the studied alloys being so low that there are not enough Cu atomic pairs for this Zener peak to become visible (for instance, Golovin et al [15] did not distinguish a Zener peak in Al-Mg alloys due to reorientation of Mg-Mg atom pairs in the aluminum solid solution for alloys with Mg content below 5 wt.%). In most of…”

Section: Analysis Of the Measuredmentioning

confidence: 99%

“…Finally, polycrystalline aluminum presents a peak related to grain boundaries at about 300 ∘ C at 1 Hz [1]. Some of these and other internal friction mechanisms suggested for aluminum and related metallic materials are explained in [15,16], like a peak in Al-Mg alloys at 100-200 ∘ C also controlled by the Zener mechanism. The dynamic properties of viscoelastic solids can be described using the complex compliance approach.…”

Section: Introductionmentioning

confidence: 99%

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Study on Mechanical Relaxations of 7075 (Al–Zn–Mg) and 2024 (Al–Cu–Mg) Alloys by Application of the Time-Temperature Superposition Principle

Rojas

Nicolas

Crespo

2017

Advances in Materials Science and Engineering

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The viscoelastic response of commercial Al–Zn–Mg and Al–Cu–Mg alloys was measured with a dynamic-mechanical analyzer (DMA) as a function of the temperature (from 30 to 425°C) and the loading frequency (from 0.01 to 150 Hz). The time-temperature superposition (TTS) principle has proven to be useful in studying mechanical relaxations and obtaining master curves for amorphous materials. In this work, the TTS principle is applied to the measured viscoelastic data (i.e., the storage and loss moduli) to obtain the corresponding master curves and to analyze the mechanical relaxations responsible for the viscoelastic behavior of the studied alloys. For the storage modulus it was possible to identify a master curve for a low-temperature region (from room temperature to 150°C) and, for the storage and loss moduli, another master curve for a high-temperature region (from 320 to 375°C). These temperature regions are coincidental with the stable intervals where no phase transformations occur. The different temperature dependencies of the shift factors for the identified master curves, manifested by different values of the activation energy in the Arrhenius expressions for the shift factor, are due to the occurrence of microstructural changes and variations in the relaxation mechanisms between the mentioned temperature regions.

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Section: Analysis Of the Measuredmentioning

confidence: 99%

Section: Introductionmentioning

confidence: 99%

Study on Mechanical Relaxations of 7075 (Al–Zn–Mg) and 2024 (Al–Cu–Mg) Alloys by Application of the Time-Temperature Superposition Principle

Rojas

Nicolas

Crespo

2017

Advances in Materials Science and Engineering

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“…If we presume that the recrystallization began with the temperature at the turning point in the G/G 0 , namely 707ºC, and ended at 745ºC, which just correspond to the peak and valley on high-temperature side of the internal friction peak in the first heating run, respectively. Thus, similarly to Al [11], Cu [22,23], and Mg [5], it can be suggested that in the studied steels, the low-temperature side of the peak P 1 may be related to the reversible dislocation movement while the high-temperature side of the peak correlates to an irreversible recrystallization process. This observation underlines common features of loosing thermal stability by various severely deformed metals.…”

Section: Shear Modulus In T91 Steelmentioning

confidence: 71%

“…The equal-channel angular pressing (ECAP) is an important technique, which can produce a fine grain size in bulk materials in the ultrafine scale and the nanometer scale [3]. The ECAP technique is successfully used to produce a variety of materials such as Cu [4], Mg [5], Fe [6], W [7], 7075 Al alloy [8], low carbon steel [9], Eurofer 97 steel [10], Al-Mg [11], etc.…”

Section: Introductionmentioning

confidence: 99%

Mechanical Spectroscopy Of Equal-Channel Angular Pressed Fe-Cr Alloys And Tungsten

Hao¹,

Tang²,

Jiang³

et al. 2015

Archives of Metallurgy and Materials

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Internal friction technique was used to investigate the microstructural stability of equal-channel angular pressed (ECAP) 9Cr1Mo steel (T91), Fe-18wt.%Cr alloy, and pure W. Several non-relaxation internal friction peaks are observed in three ECAP-strained specimens, which are related to the microstructural transition from a severely deformed state to a static recovery state of dislocations, and to recrystallized state. Along with the disappearance of the P1 peak, another relaxation internal friction peak P2 is observed during the second heating run only in Fe-18wt.%Cr alloy, and it does not disappear even during subsequent third heating run. This peak is not observed in T91 steel and W. The P2 peak is likely associated with a process of grain boundary (GB) sliding. Unlike T91, no abundant carbide precipitates distribute on GBs to pin GB and repulse GB sliding, thus, the P2 peak only occurs in Fe-18wt.%Cr alloy. It is concluded that high-temperature internal friction measurements are required to detect the grain boundary peak in pure W.

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“…The casting Al-Si and Al-Mg alloys are having many important applications in automotive and aerospace industry because of their light weight can help reduce the vehicle weight and improve fuel economy and good mechanical properties [18][19][20]. Therefore, it is worthy to study the properties of Al-Si and Al-Mg alloys.…”

Section: Introductionmentioning

confidence: 99%

FABRICATION OF CAST ALUMINIUM-SILICON (Al-Si) AND ALUMINIUM-MAGNESIUM (Al-Mg) ALLOYS AND THEIR PROPERTIES

Akkera¹,

Reddy²,

Poloju³

et al. 2016

Acta Metall Slovaca

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In the present investigation, three distinct aluminium-silicon (Al-Si) containing 7 wt.%, 12 wt.%, 14 wt.% of silicon and two different aluminium-magnesium (Al-Mg) alloys containing 2.5 wt.%, 4.5 wt.% of magnesium were prepared by casting route method. The prepared Al-Si and Al-Mg alloys have homogeneous distribution of the second rich phase throughout the cast. The microstructural analysis was done by using both optical and scanning electron microscope. Hardness values were measured with a Vickers hardness tester and tensile properties were determined by using Instron universal testing machine. Further, the wear properties were studied by using a ball-on-plate wear tester. The obtaining results highlight the hardness, tensile properties and wear resistance are increases with increasing percentage of second rich phase in aluminium. The worn surfaces of these alloys revealed that the surfaces have cracks, grooves, scoring marks and debris.

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Role of the β-phase in grain boundary and dislocation anelasticity in binary Al–Mg alloys

Cited by 47 publications

References 35 publications

Study on Mechanical Relaxations of 7075 (Al–Zn–Mg) and 2024 (Al–Cu–Mg) Alloys by Application of the Time-Temperature Superposition Principle

Study on Mechanical Relaxations of 7075 (Al–Zn–Mg) and 2024 (Al–Cu–Mg) Alloys by Application of the Time-Temperature Superposition Principle

Mechanical Spectroscopy Of Equal-Channel Angular Pressed Fe-Cr Alloys And Tungsten

FABRICATION OF CAST ALUMINIUM-SILICON (Al-Si) AND ALUMINIUM-MAGNESIUM (Al-Mg) ALLOYS AND THEIR PROPERTIES

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