Grain size stabilization and strengthening of cryomilled nanostructured Cu 12 at% Al alloy

Chakravarty, Somraj; Sikdar, Koushik; Singh, Sudhanshu S.; Roy, Debdas; Koch, Carl C.

doi:10.1016/j.jallcom.2017.05.093

Cited by 31 publications

(8 citation statements)

References 52 publications

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“…Выбор сплавов на основе Сu-Al с твердорастворным упрочнением для исследования был обусловлен рядом соображений. Во-первых, сплавы Сu-Al являются перспективными как материалы с оптимальным сочетанием прочности и пластичности [6][7][8]. Вовторых, в сплавах Сu-Al обнаружена положительная температурная зависимость скалярной плотности дислокаций, что является необычным [9].…”

Section: Introductionunclassified

Influence of Composition on the Evolution of Dislocation Substructure in the Low-Stability State Polycrystalline Cu-Al Alloys under Plastic Deformation

Trischkina¹,

Klopotov²,

Potekaev³

et al. 2021

Известия АлтГУ

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New concepts of dislocation physics of plasticity and strength are considered using quantitative methods of transmission diffraction electron microscopy. New concepts of dislocation physics of plasticity and strength are considered using quantitative methods of transmission diffraction electron microscopy. The analysis of changes in the parameters of the dislocation substructure (DSS) is given on the example of alloys Cu-0.5 and 14 аt. % Al and the influence of these parameters on the change in the substructure of the material at a temperature T=293 K is considered. It is shown that at each stage of deformation, there are usually two substructures ("old" and "new"). The blurring of the transition from stage to stage is associated with the presence of weakly stable pre-transition structural-phase States at certain degrees of deformation of several types of substructures simultaneously, i.e., a weakly stable structural-phase state of the system. Against the background of the "old" substructure, a "new" one is born, which in the process of deformation becomes the main one, and then the "old" one, in the depths of which another substructure is formed. Experimental evidence of this regularity is obtained for FCC alloys. The presence of grain boundaries complicates the diagrams: a third substructure is formed near the grain boundaries, which corresponds to the following substructures (later) in the sequence of DSS transformations.

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Section: Introductionunclassified

Influence of Composition on the Evolution of Dislocation Substructure in the Low-Stability State Polycrystalline Cu-Al Alloys under Plastic Deformation

Trischkina¹,

Klopotov²,

Potekaev³

et al. 2021

Известия АлтГУ

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“…They pointed out that the AL 2024 T6 material is stronger than the AL 2024 T351 alloy, and it has lower ductility, as well. In study [26] 4,1 % Cu, 12 % Cu [27,28] and [29,30] carried out studies on Al alloys containing 4,8% Cu. In study [31] acquired the current and voltage data of a three phase induction motor by using the LabVIEW based measuring system, which is also used by [32] in order to receive the power data of arc furnace that is used for metal melting processes in the industrial areas both on their own studies and on this study.…”

Section: Introductionmentioning

confidence: 99%

Cost analysis of T6 induction heat treatment for the aluminum-copper powder metal compacts

Taştan

Gökozan

Çavdar³

et al. 2020

SCI SINTER

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This work compares an energy cost and an energy consumption results of the 4 wt.% cupper mixed aluminum based powder metal (PM) compacts processing under induction or furnace heating. Total power and energy consumptions and total energy costs per kilogram and compact have been analyzed. T6 precipitation heat treatment applications have been applied with two different methods, one with 2.8 kW, 900 kHz ultra-high frequency induction heating system (UHFIHS), other with 2 kW chamber furnace. In the first method, Al-Cu PM compacts have been heated by induction at 580 °C in one minute and then cooled down by water. Afterwards, the samples have been heated 170, 180, 190 and 200 °C respectively for artificial ageing and cooled naturally. In the second treatment, unlike the first study, Al-Cu PM compacts are heated by chamber furnace at 540 °C in 5 hours and cooled by water. Then PM compacts are artificially aged at 190 °C in 10 hours with same furnace. During both processes, energy and power consumptions for each defined process have been measured. Optimum heat treatment of the induction is determined. The cheaper energy cost is obtained by the induction heat treatment.

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“…[20][21][22][23][24][25][26][27][28] That is why the purpose of this paper is to develop a model for thermodynamic stability of such NG alloys. Although there is plenty of previous literature on both the synthesis [29][30][31][32][33][34][35][36][37][38][39][40][41][42][43][44][45][46][47] and on modeling the stabilization of NG alloys ) (see also reviews [89][90][91][92][93] ), the present paper is novel as it puts this question into a wider framework of the nano-Calphad method, [94,95] i.e., into the thermodynamic framework originally developed by Gibbs. [96] All previous models on GB stability apply the simplest Langmuir-McLean model [97,98] (see also Reference 99) for modeling grain boundary (GB) energy.…”

Section: Introductionmentioning

confidence: 99%

Thermodynamic Stability of Nano-grained Alloys Against Grain Coarsening and Precipitation of Macroscopic Phases

Kaptay

2019

Metall Mater Trans A

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Thermodynamic conditions are derived here for binary alloys to have their grain boundary (GB) energies negative, ensuring the stability of some nano-grained (NG) alloys. All binary alloys are found to belong to one of the following three types. Type 1 is the unstable NG alloy both against grain coarsening and precipitation of a macro-phase. Type 2 is the partly stable NG alloy, stable against coarsening but not against precipitation. Type 3 is the fully stable NG alloy, both against coarsening and precipitation. Alloys type 1 have negative, or low-positive interaction energies between the components. Alloys type 2 have medium-positive interaction energies, while alloys type 3 have high-positive interaction energies. Equations are derived for critical interaction energies separating alloys type 1 from type 2 and those from type 3, being functions of the molar excess GB energy of the solute, temperature (T) and composition of the alloy. The criterion to form a stable NG alloy is formulated through a new dimensionless number (Ng), defined as the ratio of the interaction energy to the excess molar GB energy of the solute, both taken at zero Kelvin. Systems with Ng number below 0.6 belong to alloy type 1, systems with Ng number between 0.6 and 1 belong to alloy type 2, while systems with Ng number above 1 belong to alloy type 3, at least at T = 0 K. The larger is the Ng number, the higher is the maximum T of stability of the NG alloy. By gradually increasing temperature alloys type 3 convert first into type 2 and further into type 1. The Ng number is used here to evaluate 16 binary tungsten-based (W-B) alloys. At T = 0 K type 3 NG alloys are formed with B = Cu, Ag, Mn, Ce, Y, Sc, Cr; type 2 is formed in the W-Ti system, while type 1 alloys are formed with B = Al, Ni, Co, Fe, Zr, Nb, Mo and Ta. For the WAg system the region of stability of the NG alloys is shown on a calculated phase diagram, indicating also the stable grain size.

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Grain size stabilization and strengthening of cryomilled nanostructured Cu 12 at% Al alloy

Cited by 31 publications

References 52 publications

Influence of Composition on the Evolution of Dislocation Substructure in the Low-Stability State Polycrystalline Cu-Al Alloys under Plastic Deformation

Influence of Composition on the Evolution of Dislocation Substructure in the Low-Stability State Polycrystalline Cu-Al Alloys under Plastic Deformation

Cost analysis of T6 induction heat treatment for the aluminum-copper powder metal compacts

Thermodynamic Stability of Nano-grained Alloys Against Grain Coarsening and Precipitation of Macroscopic Phases

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