Design and development of an experimental wrought aluminum alloy for use at elevated temperatures

Polmear, I. J.; Couper, Malcolm J.

doi:10.1007/bf02628387

Cited by 223 publications

(75 citation statements)

References 3 publications

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“…EC measurements were used to determine the amount of solute in solid solution; their relationship can be expressed as [3,11,29]: 1/EC=0.0267+0.032Fess%+0.033Mnss%+0.0068Siss%+0.003Mgss%+0.0021particle% (2) Where, Fess%, Mnss%, Siss% and Mgss% and particle% are weight percentage. As shown in Eq.…”

Section: Evolution Of Properties During Precipitation Treatmentmentioning

confidence: 99%

“…However, the strength of traditional precipitation strengthening alloys, such as 2xxx, 6xxx and 7xxx alloys, can be seriously deteriorated due to the rapid coarsening of precipitates at elevated temperature (i.e., the overaging effect) [1,2]. Conversely, dispersoid strengthening is reported to be an important hardening mechanism at elevated temperature in aluminum alloys [3][4][5][6][7][8].…”

Section: Introductionmentioning

confidence: 99%

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Development of Al–Mn–Mg 3004 alloy for applications at elevated temperature via dispersoid strengthening

2015

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In this study, the potential applications of Al-Mn-Mg 3004 alloy at elevated temperature have been evaluated through the systematic study of the precipitation behavior of α-Al(MnFe)Si dispersoids and their effect on material properties during precipitation treatment and long-term thermal holding. The results demonstrate a significant dispersion strengthening effect caused by the precipitation of fine uniformly distributed dispersoids during precipitation treatment. The peak compression yield strength (YS) at 300°C of the experimental 3004 alloy can reach as high as 78 MPa due to a large volume fraction (~2.95 vol. %) of α-Al(MnFe)Si dispersoids. The dispersoids are found to be thermally stable at 300°C for up to 1000 h of holding, leading to consistently high mechanical performance and creep resistance. The superior and stable YS and creep resistance at 300°C enables the 3004 alloy to be applied to weight-sensitive applications at elevated temperatures.

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Section: Evolution Of Properties During Precipitation Treatmentmentioning

confidence: 99%

Section: Introductionmentioning

confidence: 99%

Development of Al–Mn–Mg 3004 alloy for applications at elevated temperature via dispersoid strengthening

2015

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“…It has been reported that the age-hardening response in the Al-4Cu-0.3Mg (mass%) alloy is significantly enhanced by trace additions of Ag in sample aged at 150 and 200 C. 27,28) Similar enhancement of hardness was observed in the alloys of the Al-Mg alloy system as a result of microalloying with Ag. 24) The maximum hardness value of the Al-10Mg-0.5Ag alloy is slightly higher than that of the Al-4Cu-0.3Mg-0.4Ag alloy when both alloys are under the same ageing condition, 24) but the time required to achieve maximum hardness in Al-10Mg-0.5Ag alloy is longer than that of the Al-4Cu-0.3Mg-0.4Ag alloy.…”

Section: Methodsmentioning

confidence: 74%

Effect of Trace Additions of Ag on Precipitation in Al–Mg Alloys

Kubota

Muddle

2005

Mater. Trans.

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Effect of Ag additions on the precipitate microstructures of the Al-10Mg alloys has been investigated using transmission electron microscopy (TEM) and electron diffraction.In the Al-10Mg alloy aged at 240 C, age-hardening response is attributable initially to an array of coarse-scale, sparsely distributed rodlike and/or plate-like 0 precipitate (particles). At the maximum hardness, the microstructure contained an increased volume fraction of coarsescale 0 and precipitate particles. In a well over-aged condition, the microstructure exhibited very coarse-scale precipitate particles. However, in the Al-10Mg-0.5Ag alloy aged at 240 C, fine-scale and uniformly distributed icosahedral quasicrystalline precipitates were observed in the early stages of ageing, and it was to be replaced by the metastable crystalline T phase after the alloy is aged for 2 h at 240 C. The T phase formed as faceted rods parallel to h110i directions appeared to be the primary strengthening constitute exhibiting maximum hardness. The globular precipitate particles were observed to be replaced by the metastable rod-like T precipitate particles after the alloy was aged 72 h at 240 C, and the phase is confirmed to be the equilibrium constitute phase in the over-aged ternary Al-10Mg-0.5Ag alloy.

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“…Also, it will be of interest to compare the present results with the behavior of Al 7075, which is one of the high strength aerospace aluminum alloys, at high temperatures. Polmear and Couper [23] showed that the yield strength of this alloy at room temperature is about 500 MPa, while at 190 and 250 ∘ C the yield strength is 200 and 50 MPa, respectively. Thus, the performance of this alloy is catastrophic at high temperatures.…”

Section: Design Of Experiments (Doe)mentioning

confidence: 92%

Statistical Model for the Mechanical Properties of Al-Cu-Mg-Ag Alloys at High Temperatures

Al-Obaisi

El‐Danaf

Ragab

et al. 2017

Advances in Materials Science and Engineering

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Aluminum alloys for high-temperature applications have been the focus of many investigations lately. The main concern in such alloys is to maintain mechanical properties during operation at high temperatures. Grain coarsening and instability of precipitates could be the main reasons behind mechanical strength deterioration in these applications. Therefore, Al-Cu-Mg-Ag alloys were proposed for such conditions due to the high stability of Ω precipitates. Four different compositions of Al-Cu-Mg-Ag alloys, designed based on half-factorial design, were cast, homogenized, hot-rolled, and isothermally aged for different durations. The four alloys were tensile-tested at room temperature as well as at 190 and 250 ∘ C at a constant initial strain rate of 0.001 s −1 , in two aging conditions, namely, underaged and peak-aged. The alloys demonstrated good mechanical properties at both aging times. However, underaged conditions displayed better thermal stability. Statistical models, based on fractional factorial design of experiments, were constructed to relate the experiments output (yield strength and ultimate tensile strength) with the studied process parameters, namely, tensile testing temperature, aging time, and copper, magnesium, and silver contents. It was shown that the copper content had a great effect on mechanical properties. Also, more than 80% of the variation of the high-temperature data was explained through the generated statistical models.

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Design and development of an experimental wrought aluminum alloy for use at elevated temperatures

Cited by 223 publications

References 3 publications

Development of Al–Mn–Mg 3004 alloy for applications at elevated temperature via dispersoid strengthening

Development of Al–Mn–Mg 3004 alloy for applications at elevated temperature via dispersoid strengthening

Effect of Trace Additions of Ag on Precipitation in Al–Mg Alloys

Statistical Model for the Mechanical Properties of Al-Cu-Mg-Ag Alloys at High Temperatures

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Design and development of an experimental wrought aluminum alloy for use at elevated temperatures

Cited by 223 publications

References 3 publications

Development of Al–Mn–Mg 3004 alloy for applications at elevated temperature via dispersoid strengthening

Development of Al–Mn–Mg 3004 alloy for applications at elevated temperature via dispersoid strengthening

Effect of Trace Additions of Ag on Precipitation in Al&ndash;Mg Alloys

Statistical Model for the Mechanical Properties of Al-Cu-Mg-Ag Alloys at High Temperatures

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Effect of Trace Additions of Ag on Precipitation in Al–Mg Alloys