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Journal articles on the topic 'Al-Mg-Si-Cu alloys'

Author: Grafiati

Published: 4 June 2021

Last updated: 19 February 2022

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1

Tokuda, Momoko, Kenji Matsuda, Takeshi Nagai, Junya Nakamura, Tokimasa Kawabata, and Susumu Ikeno. "TEM Observation of Cu and Ag Addition Al-Mg-Si Alloys." Advanced Materials Research 409 (November 2011): 81–83. http://dx.doi.org/10.4028/www.scientific.net/amr.409.81.

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It has been known that Cu-and Ag-addition Al-1.0mass%Mg2Si alloys (Al-Mg-Si-Cu alloy and Al-Mg-Si-Ag alloy) have higher hardness and elongation than those of Al-1.0mass%Mg2Si alloy. In this study, the aging behaviour of Al-Mg-Si-Cu alloy, Al-Mg-Si-Ag alloy and (Cu+Ag)-addition Al-1.0 mass% Mg2Si alloy (Al –Mg –Si-Cu-Ag alloy) has been investigated by hardness test and TEM observation. The Al-Mg-Si-Cu-Ag alloy has the fastest age-hardening rate in the early aging period and the finest microstructure at the peak hardness among three alloys. Therefore the microstructure of the precipitate in Al–Mg–Si-Cu-Ag alloy has been investigated by HRTEM observation to understand the effect of Cu and Ag addition on aging precipitation.

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2

Tokuda, M., K. Matsuda, T. Nagai, T. Kawabata, J. Nakamura, and S. Ikeno. "Hrtem Observation of the Precipitates in Cu and Ag Added Al-Mg-Si Alloys." Archives of Metallurgy and Materials 58, no. 2 (June 1, 2013): 363–64. http://dx.doi.org/10.2478/v10172-012-0200-7.

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It has been known that Cu- and Ag-added Al-1.0mass%Mg2Si alloys (Al-Mg-Si-Cu alloy and Al-Mg-Si-Ag alloy) have higher hardness and elongation than those of Al-1.0mass%Mg2Si alloy. In this study, the aging behaviour of Al-Mg-Si-Cu alloy, Al-Mg-Si-Ag alloy and (Cu+Ag)-addition Al -1.0 mass% Mg2Si alloy has been investigated by hardness test and TEM observation. The Al-Mg-Si-Cu-Ag alloy has the fastest age-hardening rate in the early aging period and the finest microstructure at the peak hardness among three alloys. Therefore the microstructure of the precipitate in Al-Mg-Si-Cu-Ag alloy has been investigated by HRTEM observation to understand the effect of Cu and Ag addition on aging precipitation.

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3

Zhao, Jing Rui, Yong Du, Li Jun Zhang, Shu Hong Liu, Jin Huan Xia, and Jin Wei Wang. "Thermodynamic Calculation of the Liquidus Projections of the Al-Cu-Fe-Mg, Al-Cu-Mg-Si, and Al-Fe-Mg-Si Quaternary Systems on Al-Rich Corner." Materials Science Forum 993 (May 2020): 1031–42. http://dx.doi.org/10.4028/www.scientific.net/msf.993.1031.

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The thermodynamic calculations of Al-Cu-Fe-Mg, Al-Cu-Mg-Si and Al–Fe–Mg–Si quaternary systems were carried out using CALPHAD method, based on the Al–Cu–Fe–Mg–Si thermodynamic database. The liquidus projection of Al–Cu–Fe–Mg, Al–Cu–Mg–Si and Al–Fe–Mg–Si quaternary systems at Al-rich corner were constructed, and the solidification structures of Al-12Cu-7Mg-1Fe, Al-14Cu-2Mg-4Si, Al-0.3Fe-6Mg-12Si (wt.%) alloys were analyzed by the Scheil solidification simulation. The calculated results agree well with the previous experimental data. The liquidus projections of three quaternary aluminum alloys at the Al-rich corner were accurately plotted, which could be helpful for the analysis of solidification process of multicomponent alloy systems, and provide an important theoretical basis for the material design of aluminum alloys.

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4

Kovacheva, R. "Metallographic Investigation of Al-Si-Mg and Al-Si-Cu Alloys/ Metallographische Untersuchung von Al-Si-Mg- und Al-Si-Cu- Legierungen." Practical Metallography 30, no. 2 (February 1, 1993): 68–81. http://dx.doi.org/10.1515/pm-1993-300203.

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5

Lech-Grega, Marzena, and Sonia Boczkal. "Iron Phases in Model Al-Mg-Si-Cu Alloys." Materials Science Forum 674 (February 2011): 135–40. http://dx.doi.org/10.4028/www.scientific.net/msf.674.135.

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Iron phases present in alloys from the 6xxx series affect the workability behaviour of these alloys. Iron in these alloys occurs in the form of intermetallic phases and AlFe, α-AlFeSi, β- AlFeSi eutectics. The homogenisation treatment is carried out to induce the transformation of  phase into phase The aim of the studies was EDX and EBSD analysis by scanning microscopy of iron phases present in model alloys based on 6061 system, characterised by the silicon-iron ratio Si/Fe=0,5 and 1, examined in as-cast condition and after homogenisation, followed by a comparison of the detected phases with phases present in industrial ingots. In 6061 alloy, copper in the amount of 0,4wt.% occurred in the solid solution of aluminium. The EDX analysis proved that copper atoms were embedded also in iron precipitates, and scarce phases of an AlxCuy type were being formed. Different content of magnesium in the examined alloys (0,8 and 1,2wt.%) affected not only the quantitative content of Mg2Si phases, but also the presence of AlFe phases in alloy with small content of Si (0,4wt.%) and high content of Mg (1,2wt.%).

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6

Ber, L. B. "Accelerated artificial ageing regimes of commercial aluminium alloys. II: Al–Cu, Al–Zn–Mg–(Cu), Al–Mg–Si–(Cu) alloys." Materials Science and Engineering: A 280, no. 1 (March 2000): 91–96. http://dx.doi.org/10.1016/s0921-5093(99)00661-9.

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7

Lacaze, Jacques, Gérard Lesoult, and Ibrahim Ansara. "Rosettes in Al-Cu-Mg-Si Aluminium Alloys." Materials Science Forum 217-222 (May 1996): 171–76. http://dx.doi.org/10.4028/www.scientific.net/msf.217-222.171.

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8

Chakrabarti, D. J., and J. L. Murray. "Eutectic Melting in Al-Cu-Mg-Si Alloys." Materials Science Forum 217-222 (May 1996): 177–82. http://dx.doi.org/10.4028/www.scientific.net/msf.217-222.177.

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9

Yao, Ji Yong, Geoffrey A. Edwards, Li-Hui Zheng, and D. A. Graham. "Directional Solidification of Al-Si-Cu-Mg Alloys." Materials Science Forum 217-222 (May 1996): 183–88. http://dx.doi.org/10.4028/www.scientific.net/msf.217-222.183.

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10

Kim, A., S. S. Cho, and H. J. Lee. "Foaming behaviour of Al–Si–Cu–Mg alloys." Materials Science and Technology 20, no. 12 (December 2004): 1615–20. http://dx.doi.org/10.1179/026708304x11297.

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11

Zhao, Jing Rui, Yong Du, Li Jun Zhang, Shu Hong Liu, Jin Huan Xia, and Jin Wei Wang. "Thermodynamic Calculation of the Liquidus Projections of the Al-Cu-Fe-Si and Al-Cu-Fe-Mg-Si Multicomponent Systems on Al-Rich Side." Materials Science Forum 993 (May 2020): 984–95. http://dx.doi.org/10.4028/www.scientific.net/msf.993.984.

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The thermodynamic calculations of Al–Cu–Fe–Si quaternary system and Al–Cu–Fe–Mg–Si quinary system were carried out using CALPHAD approach based on the Al–Cu–Fe–Mg–Si thermodynamic database. The liquidus surface projection of Al–Cu–Fe–Si quaternary system at the Al-rich corner was constructed, and then the solidification structures of four Al–Cu–Fe–Si alloys were analyzed by the Gulliver-Scheil solidification simulation. The calculated results were in good agreement with the previous experimental data. The liquidus surface projections of A1–Cu–Fe–Mg–Si quinary system at the region of Al-Cu, Al-Si and Al-Mg were constructed, respectively. The liquidus projection of the multicomponent aluminum alloy system at the Al-rich side was accurately drawn, which could accurately predict the primary phase in the solidification process of the alloy. This work has an important guiding significance for the design of the aluminum alloys.

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12

Karlík, Miroslav, Jiri Faltus, Jitka Nejezchlebová, Petr Haušild, and Petr Harcuba. "Characterisation of Al-Cu and Al-Mg-Si Free-Cutting Alloys." Materials Science Forum 794-796 (June 2014): 1181–86. http://dx.doi.org/10.4028/www.scientific.net/msf.794-796.1181.

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Free cutting alloys of Al-Cu (AA2011 and AA2111B) in T6 temper and Al-Mg-Si system (AA6023 and AA6262) in tempers T6 and T8 were subjected to Charpy U - notch impact testing at the temperatures ranging from 20°C to 350°C. The microstructure of the materials was characterized by light metallography, fracture surfaces were observed using scanning electron microscope (SEM). The alloys showed a significant decrease in the impact energy KU at temperatures ~125°C (AA2011, AA2111B), ~170°C (AA6023), and ~250°C (AA6262), respectively. This decrease of KU was caused by melting of disperse phases containing low-melting point metals (Pb, Sn, Bi), which was confirmed by differential scanning calorimetry. Additional annealing of the AA6262-T8 alloy for 2h at 400°C followed by slow cooling led to the transformation of Pb + Bi particles accompanied by the shift of the melting temperature from ~250 to ~310 °C. Higher temperature solution annealing of the AA6023 alloy for 30 min at 540°C (as a replacement of common 30 min at 520°C) resulted in a partial transformation of Sn + Bi particles accompanied by melting point shift from ~170 to ~200°C. Chemical composition of the corresponding phases was monitored by energy dispersive X-ray spectroscopy in SEM.

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13

Nishikubo, Masaya, Kenji Matsuda, Yoshihisa Oe, Jyunya Nakamura, and Susumu Ikeno. "Aging Precipitation of Al-Mg-Si Alloys with Additions of Ag and Cu." Materials Science Forum 794-796 (June 2014): 981–84. http://dx.doi.org/10.4028/www.scientific.net/msf.794-796.981.

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In this study, the aging behaviour of several Al-Mg-Si alloys (Al-Mg-Si-Cu , Al-Mg-Si-Ag and Al-Mg-Si-Cu-Ag) has been investigated by hardness tests and TEM observations. Comparing the age-hardening rate in the early period of these alloys, the alloys with Cu or/and Ag addition are faster than that of the base alloy, and the aging time to reach the maximum hardness of the alloys with Cu or/and Ag addition is shorter than that of the base alloy.Therefore the aging behaviour of that alloys has been investigated by TEM observations to understand the effect of Cu, Ag and Cu+Ag additions on aging precipitation.

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14

TANAKA, Takio. "Lubricated wear resistance of Al-Cu-Mn-Mg-Si and Al-Si-Cu-Mn-Mg alloys to ADC12 die cast alloy." Journal of Japan Institute of Light Metals 42, no. 3 (1992): 161–67. http://dx.doi.org/10.2464/jilm.42.161.

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15

Alexopoulos, Nikolaos D., Vangelis Migklis, Stavros K. Kourkoulis, and Zaira Marioli-Riga. "Fatigue Behavior of Aerospace Al-Cu, Al-Li and Al-Mg-Si Sheet Alloys." Advanced Materials Research 1099 (April 2015): 1–8. http://dx.doi.org/10.4028/www.scientific.net/amr.1099.1.

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In the present work, an experimental study was performed to characterize and analyze the tensile and constant amplitude fatigue mechanical behavior of several aluminum alloys, namely 2024 (Al-Cu), 2198 (Al-Li) and 6156 (Al-Mg-Si). Al-Li alloy was found to be superior of 2024 in the high cycle fatigue and fatigue endurance limit regimes, especially when considering specific mechanical properties. Alloy 6156 was found to have superior constant amplitude fatigue performance that the respective 6xxx series alloys; more than 15% higher endurance limit was noticed against 6061 and almost 30% higher than 6082. Alloy 6156 presented only a marginal increase in fatigue life for the HCF regime.

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16

Pan, Yan Peng, Zhi Feng Zhang, Bao Li, Bi Cheng Yang, and Jun Xu. "Effect of Alloying Elements on Mechanical Properties of Al-Si-Cu-Mg Cast Alloys." Materials Science Forum 817 (April 2015): 127–31. http://dx.doi.org/10.4028/www.scientific.net/msf.817.127.

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To develop Al-Si cast alloys with high performance is important for lightweighting vehicles. In this study, the effects of the alloying elements such as Si, Cu, Mg contents (5%-7% Si, 1%-3%Cu, 0.3%-0.9%Mg) on mechanical properties of a test Al-Si-Cu-Mg cast alloy was studied to achieve a specific composition. The experimental results show that the Al-6%Si-3%Cu-0.3%Mg alloy has better comprehensive mechanical properties after T6 heat treatment, which indicates a remarkable interaction of the alloying elements for improving performance.

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17

Liu, Meng, Calin Daniel Marioara, Randi Holmestad, and John Banhart. "Ageing Characteristics of Al-Mg-(Ge,Si)-Cu Alloys." Materials Science Forum 794-796 (June 2014): 971–76. http://dx.doi.org/10.4028/www.scientific.net/msf.794-796.971.

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In order to elucidate some of the differences between Al-Mg-Si and Al-Mg-Ge alloys and the role of Cu, a series of Al-Mg-Ge, Al-Mg-Si and Al-Mg-Ge-Si alloys, some of them containing Cu, are investigated by positron annihilation lifetime spectroscopy during natural ageing. Al-Mg-Ge alloys show qualitatively the same evolution of positron lifetime τ1Cwith time as Al-Mg-Si alloys, namely an initial decrease, followed by a re-increase, after which τ1Cdrops to an equilibrium value. However, for alloys with equal Mg contents, Ge gives rise to a notably slower ageing kinetics than Si, pointing at effects of atomic size or solute-vacancy binding energies. Adding Cu to both Al-Mg-Ge and Al-Mg-Si alloys slows down the initial formation of clusters but promotes their further growth.

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18

Han, Yi, Chu Yan Wang, Tong Guang Zhai, and Hiromi Nagaumi. "Morphology of Si Phase in Al-Mg-Si-Cu Alloys with Excess Si Addition." Materials Science Forum 783-786 (May 2014): 161–67. http://dx.doi.org/10.4028/www.scientific.net/msf.783-786.161.

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The morphology of Si phase and its growth manner in the Al-Mg-Si-Cu alloys with amounts of excess silicon were investigated using by a combination of the higher magnification microstructure and DSC measurements. Solidification characteristics of the alloys were predicted by thermodynamic calculation and compared to the experimental results. It was found that addition of higher amount of excess silicon led to the formation of the evidently morphological Si phase, especially when the silicon content was beyond 1.35 wt.%. The Si phase was one of the dominant phases in the alloys and its reaction peak was identified with the onset temperature of 550.43oC in the DSC curves. These experimental results were in good agreement with the thermodynamic calculations by the Gulliver-Scheil model. Keywords: Al-Mg-Si-Cu alloy; morphology; thermodynamic calculation; excess Si

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19

Sjölander, E., and S. Seifeddine. "Artificial ageing of Al–Si–Cu–Mg casting alloys." Materials Science and Engineering: A 528, no. 24 (September 2011): 7402–9. http://dx.doi.org/10.1016/j.msea.2011.06.036.

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20

Kozlov, A., and R. Schmid-Fetzer. "Growth restriction factor in Al-Si-Mg-Cu alloys." IOP Conference Series: Materials Science and Engineering 27 (January 12, 2012): 012001. http://dx.doi.org/10.1088/1757-899x/27/1/012001.

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21

Tavitas-Medrano, F. J., A. M. A. Mohamed, J. E. Gruzleski, F. H. Samuel, and H. W. Doty. "Precipitation-hardening in cast AL–Si–Cu–Mg alloys." Journal of Materials Science 45, no. 3 (February 2010): 641–51. http://dx.doi.org/10.1007/s10853-009-3978-6.

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22

Lacaze, Jacques, Gerard Lesoult, Olivier Relave, Ibrahim Ansara, and Jean Pierre Riquet. "Thermodynamics and Solidification of Al-Cu-Mg-Si Alloys." International Journal of Materials Research 78, no. 2 (February 1, 1987): 141–50. http://dx.doi.org/10.1515/ijmr-1987-780211.

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23

Achiţei, Dragoş Cristian, Petrică Vizureanu, Mirabela Georgiana Minciună, Mohd Mustafa Al Bakri Abdullah, and Ioan Gabriel Sandu. "Study on Al-Si Alloys Properties Enhancement." Applied Mechanics and Materials 754-755 (April 2015): 634–38. http://dx.doi.org/10.4028/www.scientific.net/amm.754-755.634.

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The paper presents a study about aluminum alloy, allied with Si, Cu, Mn, Mg. The Al-Si-Cu-Mg alloys for foundry are used for parts strongly required and which work at high temperatures, due to their good wear resistance. The industrial Al-Cu alloys contain 12 % cooper, are hipo-eutectic and may be for foundry or deformable. By alloying with magnesium, the Al-Cu alloys become with remarkable properties of resistance and plastic deformation processing. The improvement of mechanical characteristics for Al-Si alloys is realized with metals which forms the intermediate phases with silicon or aluminum, with variable solubility in solid state and which permits the structural hardening by heat treatments (quenching and ageing). From the analysis of dilatogramms, grouped for each sample, with the specific initial length, subjected to successive heating, from ambiance temperature up to 500°C, it is found that, with the appearance of ageing phenomena, on the samples aren’t significant modifications for elongation (few microns), only different may be the form of elongation-temperature curve. This analysis permits the determination of experimental data, regarding the behavior of Al-Si alloy subjected to heat treatments and repeated warming. Therefore, the Al-Si-Cu-Mg alloys, for foundry, are used for manufacture the parts strong required and which work at high temperatures, like pistons for engines with internal burn, parts for machines and reinforcements construction, due to their high usage resistance.

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24

Dong, Zhong-Qiang, Jin-Guo Wang, Zhi-Ping Guan, Pin-Kui Ma, Po Zhao, Zhu-Jin Li, Tian-Shi Lu, and Rui-Fang Yan. "Effect of Short T6 Heat Treatment on the Thermal Conductivity and Mechanical Properties of Different Casting Processes Al-Si-Mg-Cu Alloys." Metals 11, no. 9 (September 13, 2021): 1450. http://dx.doi.org/10.3390/met11091450.

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The thermal conductivity of alloys is gradually becoming appreciated. It is often assumed that heat treatment can improve the thermal conductivity of Al-Si-Mg-Cu alloys, but there has been little relevant research. This paper studies the effects of different casting processes and short T6 heat treatment (ST6) on the thermal conductivity and mechanical properties of Al-Si-Mg-Cu alloys. The results show that a microstructure with fine α-Al crystal grains can be obtained by semi-solid die casting (SSDC), improving the mechanical properties of the Al-Si-Mg-Cu alloy in the as-cast state. After SSDC, the size and aspect ratio of eutectic silicon can be reduced by ST6 treatment, effectively improving the thermal conductivity and mechanical properties of the alloy. Finally, the influence of eutectic silicon on electron transport is analyzed in detail. With the SSDC + ST6 processing technology, Al-Si-Mg-Cu alloys with excellent thermal conductivity and mechanical properties can be obtained.

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25

Liu, Hai Jun, Lie Jun Li, Jian Wei Niu, Ji Xiang Gao, and Chuan Dong Ren. "Effect of Mg and Cu Additions on Microstructure and Mechanical Properties of Squeeze Casting Al-Si-Cu-Mg Alloy." Materials Science Forum 850 (March 2016): 511–18. http://dx.doi.org/10.4028/www.scientific.net/msf.850.511.

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The effects of Mg and Cu additions with different contents on the mechanical properties of Al-Si alloy prepared by indirect squeeze casting have been experimentally investigated. The microstructure and mechanical properties of as-cast and T6-treated Al-Si-Cu-Mg alloys were tested by OM, SEM, DSC and tensile measurement, where the samples were produced by artificial aging at 180°C for 8 h after solution treatment at 540°C for 4 h. It has been found that for the as-cast alloys, with increasing contents of Mg and Cu the tensile strength (UTS) and yield strength (YS) increased, while the percentage elongation (El) decreased. And the optimal mechanical properties of Al-Si-Cu-Mg alloys were obtained under the content ratio of Cu/Mg within 4, where the UTS and El reached 426 MPa and 6.3% after T6 treated, respectively.

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26

Bae, Chul-Hong, Seong-Ho Ha, Bong-Hwan Kim, Young-Ok Yoon, Hyun-Kyu Lim, Shae K. Kim, and Young-Jig Kim. "Correlation of Surface Oxidation and Mg-Based Intermetallic Phases in Grain Boundaries of Al–Mg Alloys Containing Third Elements." Journal of Nanoscience and Nanotechnology 21, no. 3 (March 1, 2021): 2055–58. http://dx.doi.org/10.1166/jnn.2021.18948.

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In this study, the correlation of surface oxidation and Mg-based intermetallic phases in the grain boundary in Al–Mg alloys containing third elements was investigated. The experimental results were examined by phase diagrams plotted as a function of oxygen partial pressure determined by thermodynamic calculation. The addition of Si and Cu as third elements into the Al–7 mass%Mg alloy formed Mg-based secondary phases during solidification. The 1 mass% Cu addition formed three different types of Mg-based intermetallic compounds. From weight gains by oxidation, all samples exhibited their weight gains depending on time. The Si-added alloy showed a considerably lower weight gain and maintained a nearly constant weight, while the weight gain of the Al–7 mass%Mg–1 mass%Cu alloy was significantly greater than those of other alloys. MgO and MgAl2O4− spinel were the main oxides that formed the oxide scale in all examined alloys. Si addition formed the multi-element oxide including Mg and Si.

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27

Matsuda, Kenji, and Susumu Ikeno. "Microstructure and Nano-Segregation of Cu in Al-Mg-Si-Cu Alloys." Materia Japan 42, no. 12 (2003): 860. http://dx.doi.org/10.2320/materia.42.860.

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28

Chauke, Levy, Heinrich Möller, Ulyate Andries Curle, and Gonasagren Govender. "Anodising of Al-Mg-Si-(Cu) Alloys Produced by R-HPDC." Materials Science Forum 765 (July 2013): 658–62. http://dx.doi.org/10.4028/www.scientific.net/msf.765.658.

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Anodising of aluminium alloys can be used to improve corrosion resistance during application or it can be simply for decorative purposes. In this research, anodising of 6111 (Cu containing) and 6082 (without Cu) alloys produced by Rheo-High Pressure Die Casting (R-HPDC) was studied. R-HPDC components suffer from surface liquid segregation (SLS), the surface layer of the casting is enriched in alloying elements and it is expected to have different properties than the bulk material. An advantage of R-HPDC is that traditional wrought alloys such as the 6xxx series can be cast into near-net shape. Therefore, in order to commercialise R-HPDC of certain wrought alloy components, the anodisibility of the SLS is of importance. The two alloys, in the T6 condition, were anodised in a 250 g/l sulphuric acid solution. The anodisability of the alloys with and without SLS was studied by using a scanning electron microscope coupled with energy dispersive spectroscopy (SEM/EDS). The thickness of the sample with SLS and without the SLS was measured. The intermetallic phases in the alloys and their influence on anodising were analysed using SEM/EDS.

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29

Hida, Shintaro, Šárka Mikmeková, Kenji Matsuda, and Susumu Ikeno. "Observation of large Equilibrium Phase of Al-Mg-Si Alloys." Materials Science Forum 794-796 (June 2014): 977–80. http://dx.doi.org/10.4028/www.scientific.net/msf.794-796.977.

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The precipitation sequence in Al-Mg-Si alloy is generally accepted as supersaturated solid solution GP-zone β β β (Mg2Si). The effect of Ag or Cu in Al-Mg-Si alloy was reported in our previous work. There is little report about effect of Ag or Cu on the metastable phase and equilibrium phase in this alloy the system. Hexagonal plate like β-phase and Q-phase were observed the Cu added alloy. This hexagonal-shaped β-phase has unique orientation relationship to the Al matrix. This work was performed to compare the shape of effect of the additional elements on the equilibrium phase. The hexagonal shape precipitate was observed in Cu or Ag added alloys aged at 673K.

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30

Ibrahim, Mohamed F., Agnes M. Samuel, Herbert W. Doty, and Fawzy H. Samuel. "Effect of Aging Conditions on Precipitation Hardening in Al–Si–Mg and Al–Si–Cu–Mg Alloys." International Journal of Metalcasting 11, no. 2 (May 23, 2016): 274–86. http://dx.doi.org/10.1007/s40962-016-0057-z.

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31

Ghosh, K. S. "Calorimetric studies of 2024 Al–Cu–Mg and 2014 Al–Cu–Mg–Si alloys of various tempers." Journal of Thermal Analysis and Calorimetry 136, no. 2 (September 3, 2018): 447–59. http://dx.doi.org/10.1007/s10973-018-7702-0.

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32

Yu, Si Rong, Jun Xu, Xiao Hua Zhang, Qiang Yao, and Shu Miao Xu. "Al-Si-Mg-Cu Heat Storage Alloys and their Heat Storage Properties." Materials Science Forum 743-744 (January 2013): 24–28. http://dx.doi.org/10.4028/www.scientific.net/msf.743-744.24.

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The problems such as poor oxidation resistant properties at high temperatures and abated thermal storage capacities after repeated thermal cycles still exist in heat storage alloys. In order to alleviate these problems, orthogonal experiment was used to design nine Al-Si-Mg-Cu alloys in this work. An SII TG/DTA6300 differential thermal analyzer was used to determine the heat storage properties of these alloys. After integrating a series of factors, Al-12Si-2Mg-15Cu alloy was selected as the heat storage alloy. The oxidation test of this alloy at the temperature of 650 °C for 300 h was carried out, and the oxidation kinetics curve was obtained. The results showed that the oxide film was of good protection. This alloy exhibited a good thermal stability in view of the latent heat of fusion decreased 3.53%, the initial phase transition temperature decreased 0.1 °C, and terminated phase transition temperature increased 3.1 °C after 150 times of thermal cycles. The photomicrograph was used to discuss the reasons of the performance changes of this alloy.

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33

Kang, H. G., M. Kida, H. Miyahara, and K. Ogi. "Age hardening behaviour of alumina continuous fibre reinforced Al-Si-Cu and Al-Si-Cu-Mg alloys." International Journal of Cast Metals Research 15, no. 1 (July 2002): 1–7. http://dx.doi.org/10.1080/13640461.2002.11819457.

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34

Curle, Ulyate Andries, Heinrich Möller, and Gonasagren Govender. "R-HPDC in South Africa." Solid State Phenomena 192-193 (October 2012): 3–15. http://dx.doi.org/10.4028/www.scientific.net/ssp.192-193.3.

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The history of semi-solid metal forming and in particular rheo-high pressure die casting at the Council for Scientific and Industrial Research in South Africa is discussed. Processing flexibility is demonstrated on the Al-Si-Mg, Al-Mg-Si, Al-Cu-Mg and Al-Zn-Mg-Cu casting and wrought alloy systems as well as on high purity aluminium, unmodified Al-Si binary eutectic, metal matrix composites and magnesium alloys. Material properties are highlighted.

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35

Pan, X., J. E. Morral, and H. D. Brody. "Predicting the Q-Phase in Al-Cu-Mg-Si Alloys." Journal of Phase Equilibria and Diffusion 31, no. 2 (January 6, 2010): 144–48. http://dx.doi.org/10.1007/s11669-009-9640-9.

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36

Hutchinson, C. R., and S. P. Ringer. "Precipitation processes in Al-Cu-Mg alloys microalloyed with Si." Metallurgical and Materials Transactions A 31, no. 11 (November 2000): 2721–33. http://dx.doi.org/10.1007/bf02830331.

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37

Sjölander, Emma, and Salem Seifeddine. "The heat treatment of Al–Si–Cu–Mg casting alloys." Journal of Materials Processing Technology 210, no. 10 (July 2010): 1249–59. http://dx.doi.org/10.1016/j.jmatprotec.2010.03.020.

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38

Wang, Xiaoguo, Jian Qin, Hiromi Nagaumi, Ruirui Wu, and Qiushu Li. "The Effect of α-Al(MnCr)Si Dispersoids on Activation Energy and Workability of Al-Mg-Si-Cu Alloys during Hot Deformation." Advances in Materials Science and Engineering 2020 (May 20, 2020): 1–12. http://dx.doi.org/10.1155/2020/3471410.

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Abstract:

The hot deformation behaviors of homogenized direct-chill (DC) casting 6061 aluminum alloys and Mn/Cr-containing aluminum alloys denoted as WQ1 were studied systematically by uniaxial compression tests at various deformation temperatures and strain rates. Hot deformation behavior of WQ1 alloy was remarkably changed compared to that of 6061 alloy with the presence of α-Al(MnCr)Si dispersoids. The hyperbolic-sine constitutive equation was employed to determine the materials constants and activation energies of both studied alloys. The evolution of the activation energies of two alloys was investigated on a revised Sellars’ constitutive equation. The processing maps and activation energy maps of both alloys were also constructed to reveal deformation stable domains and optimize deformation parameters, respectively. Under the influence of α dispersoids, WQ1 alloy presented a higher activation energy, around 40 kJ/mol greater than 6061 alloy’s at the same deformation conditions. Dynamic recrystallization (DRX) is main dynamic softening mechanism in safe processing domain of 6061 alloy, while dynamic recovery (DRV) was main dynamic softening mechanism in WQ1 alloy due to pinning effect of α-Al(MnCr)Si dispersoids. α dispersoids can not only resist DRX but also increase power required for deformation of WQ1 alloy. The microstructure analysis revealed that the flow instability was attributed to the void formation and intermetallic cracking during hot deformation of both alloys.

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39

Ólafsson, P., and R. Sandström. "Calculations of electrical resistivity for Al–Cu and Al–Mg–Si alloys." Materials Science and Technology 17, no. 6 (June 2001): 655–62. http://dx.doi.org/10.1179/026708301101510528.

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Cheng, Xiao Min, Xin Chen, Yuan Yuan Li, and Yong Gang Tan. "Research on the Properties of the Thermal Storage and Corrosion of Al-Si-Cu-Mg-Zn Alloy." Advanced Materials Research 197-198 (February 2011): 1064–72. http://dx.doi.org/10.4028/www.scientific.net/amr.197-198.1064.

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In this paper, various kinds of high-temperature phase change thermal storage Al-Si-Cu-Mg-Zn alloys were prepared, and the thermal properties were studied through integrated thermal analysis. Then the corrosion kinetics of Cr20Ni80 alloy in Al-7% Si alloy and Al-Cu-Mg-Zn alloy at 700°C in thermal cycles were obtained. The microstructures, element concentration and phases in the interface were analyzed by means of metallographic microscope, EPMA and XRD. The results show that all materials phase transition temperatures are during 450°C ~650°C . The total thermal energies of the materials are higher than 900J/cm3. Quaternary alloys and quinary alloys show much more advantages when applying for solar thermal power generation systems. The latent heat depends strongly upon the composition and percentage of elements and the phase composition. Besides, experimental results show that the corrosion rate of Cr20Ni80 alloy in Al-7%Si alloy at 700°C is 0.167mm/h. Under thermal cycling conditions, the corrosion rate of Cr20Ni80 alloy in Al-Cu-Mg-Zn alloy is a little lower and the reaction interface layer does not significantly affect the rate of further corrosion. The corrosion of Al-Si-Cu-Mg-Zn phase change thermal storage materials depends on the content of aluminum element, and nickel-based alloys are not suitable for use as packaging materials.

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Matsuda, Kenji, Junya Nakamura, Tokimasa Kawabata, Susumu Ikeno, Tatsuo Sato, Calin D. Marioara, Sigmund J. Andersen, and Randi Holmestad. "Effect of Additional Elements (Cu, Ag) on Precipitation in 6xxx (Al-Mg-Si) Alloys." Materials Science Forum 706-709 (January 2012): 357–60. http://dx.doi.org/10.4028/www.scientific.net/msf.706-709.357.

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It has been known that Cu- or Ag-addition Al-1.0mass%Mg2Si (balanced) alloys shows higher hardness and elongation than Cu-free or Ag-free balance alloy. In this study, the alloys with Cu or Ag addition and the alloys with Si / Mg in excess have been investigated by hardness and tensile tests and HRTEM observation. Cu addition is effective for higher hardness, and Ag-addition is useful for improvement of elongation for peak-aged samples. Precipitates in peak aged these alloys have been confirmed by HRTEM. Cu-addition alloy almost includes Q’-phase, and Ag-addition alloy includes b’-phase. The precipitation sequence of Ag- or Cu addition Al-Mg-Si alloy was investigated using HRTEM, SAED, and EDS. The precipitates obtained in the two alloys were classified into several kinds by HRTEM images and SAED patterns. The relative frequencies of precipitates were also investigated and compared with that in the alloy.

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42

Okubo, Michinori, and Yoshihiro Kohisa. "Dissimilar aluminium weldability of SiC particle reinforced aluminium alloy to Al–Si, Al–Mg, Al–Mg–Si, Al–Zn–Mg–Cu alloys by electron beam welding." Welding International 23, no. 1 (January 2009): 15–20. http://dx.doi.org/10.1080/09507110802348967.

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43

Cayron, C., and P. A. Buffat. "Structural Phase Transition in Al-Cu-Mg-Si and Al-Mg-Si Alloys: Ordering Mechanisms and Crystallographic Structures." Materials Science Forum 331-337 (May 2000): 1001–6. http://dx.doi.org/10.4028/www.scientific.net/msf.331-337.1001.

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Aguilera-Luna, I., M. J. Castro-Román, J. C. Escobedo-Bocardo, F. A. García-Pastor, and M. Herrera-Trejo. "Effect of cooling rate and Mg content on the Al–Si eutectic for Al–Si–Cu–Mg alloys." Materials Characterization 95 (September 2014): 211–18. http://dx.doi.org/10.1016/j.matchar.2014.06.009.

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Belov, Nikolay A., A. V. Koltsov, and Dmitry G. Eskin. "The Al-Cu-Fe-Mg-Si Phase Diagram in the Range of Al-Cu Alloys." Materials Science Forum 396-402 (July 2002): 929–34. http://dx.doi.org/10.4028/www.scientific.net/msf.396-402.929.

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46

Liu, D., H. V. Atkinson, and H. Jones. "Thermodynamic prediction of thixoformability in alloys based on the Al–Si–Cu and Al–Si–Cu–Mg systems." Acta Materialia 53, no. 14 (August 2005): 3807–19. http://dx.doi.org/10.1016/j.actamat.2005.04.028.

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47

Raghavan, V. "Al-Cu-Mg-Si (Aluminum-Copper-Magnesium-Silicon)." Journal of Phase Equilibria and Diffusion 28, no. 2 (May 8, 2007): 198–200. http://dx.doi.org/10.1007/s11669-007-9046-5.

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48

Meyer, B. C., E. Lectard, N. Serrano, E. Zschech, T. Hirsch, and P. Mayr. "Laserstrahlschweißen der Al-Mg-Si-Cu-Legierung 6013." HTM Journal of Heat Treatment and Materials 52, no. 5 (September 1, 1997): 291–97. http://dx.doi.org/10.1515/htm-1997-520508.

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49

Cáceres, C. H., and J. A. Taylor. "Enhanced ductility in Al-Si-Cu-Mg foundry alloys with high Si content." Metallurgical and Materials Transactions B 37, no. 6 (December 2006): 897–903. http://dx.doi.org/10.1007/bf02735011.

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Sivarupan, Tharmalingam, Carlos H. Caceres, and John A. Taylor. "Alloy Composition and Dendrite Arm Spacing in Al-Si-Cu-Mg-Fe Alloys." Metallurgical and Materials Transactions A 44, no. 9 (May 9, 2013): 4071–80. http://dx.doi.org/10.1007/s11661-013-1768-x.

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