The influence of grain boundary inclination on the structure and energy of σ = 3 grain boundaries in copper

Wolf, U.; Ernst, F.; Muschik, T.; Finnis, Michael W.; Fischmeister, H. F.

doi:10.1080/01418619208248003

Cited by 201 publications

(86 citation statements)

References 27 publications

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“…Although the materials and temperature differ, it is also interesting to compare the present observations to a previous combined experimental and theoretical study of R3 grain boundaries in Cu, with boundary plane orientations in the h1 1 0i zone [10]. The common feature between Cu and Ni is that they share the fcc crystal.…”

Section: Discussionmentioning

confidence: 57%

“…In general, the grain boundary energy can vary as a function of all five macroscopic crystallographic parameters (three for lattice misorientation and two for grain boundary plane orientation) that are used to classify a grain boundary. Because of the large number of different grain boundaries, past measurements of grain boundary energies in face-centered cubic (fcc) metals have been made over a limited range of the crystallographic parameters [2][3][4][5][6][7][8][9][10][11][12][13][14][15][16]. In this paper, we report the relative grain boundary energies of nickel as a function of all macroscopic five crystallographic parameters, a quantity that will be referred to as the grain boundary energy distribution (GBED).…”

Section: Introductionmentioning

confidence: 99%

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Relative grain boundary area and energy distributions in nickel

2009

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The three-dimensional interfacial network of grain boundaries in polycrystalline nickel has been characterized using a combination of electron backscatter diffraction mapping and focused ion beam serial sectioning. These data have been used to determine the relative areas of different grain boundary types, categorized on the basis of lattice misorientation and grain boundary plane orientation. Using the geometries of the interfaces at triple lines, relative grain boundary energies have also been determined as a function of lattice misorientation and grain boundary plane orientation. Grain boundaries comprising (1 1 1) planes have, on average, lower energies than other boundaries. Asymmetric tilt grain boundaries with the R9 misorientation also have relatively low energies. The grain boundary energies and areas are inversely correlated.

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Section: Discussionmentioning

confidence: 57%

Section: Introductionmentioning

confidence: 99%

Relative grain boundary area and energy distributions in nickel

2009

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“…This is in accordance with the calculated boundary energy as a function of the boundary orientation for the <011> tilt twin boundary. Two minima are found, one for the coherent twin, the other for a boundary inclined at 82° with respect to the coherent twin boundary (Wolf et al 1992). Since the ledges are introduced to compensate for a deviation from the exact {111}/{111} boundary orientation, it would be expected that they are spaced rather regularly.…”

Section: Initiation and Propagation Of Cleared Channelsmentioning

confidence: 99%

Initiation and propagation of cleared channels in neutron-irradiated pure copper and a precipitation hardened CuCrZr alloy

Edwards

Singh

Bilde-Sørensen

2005

Journal of Nuclear Materials

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(max. 2000 char.):The phenomenon of plastic flow localization in the form of "cleared" channels has been frequently observed in neutron irradiated metals and alloys for more than 40 years. So far, however, no experimental evidence as to how and where these channels are initiated during postirradiation deformation has emerged. Recently we have studied the problem of initiation and propagation of cleared channels during post-irradiation tensile tests of pure copper and a copper alloy irradiated with fission neutrons. Tensile specimens of pure copper and a precipitation hardened copper alloy (CuCrZr) were neutron irradiated at 323 and 373K to displacement doses in the range of 0.01 to 0.3 dpa (displacement per atom) and tensile tested at the irradiation temperature. The stress-strain curves clearly indicated the occurrence of a yield drop. The post-deformation microstructural examinations revealed that the channels are formed already in the elastic regime and their density increases with increasing plastic strain. The channels appear to have been initiated at grain boundaries, twin boundaries, at relatively large inclusions and even at the previously formed cleared channels. Even though the channels are produced throughout the whole tensile test, no clear evidence has been found for the operation of Frank-Read sources in the volume between the channels. Channels have been observed to penetrate through annealing twins, in some cases stopping at the opposite twin boundary and in other cases penetrating even through the opposite twin boundary and continuing further into the grain. In some cases channels have been found to penetrate through grain boundaries too. It is suggested that the high stress levels reached during deformation of the irradiated specimens activate dislocation sources at the sites of stress concentration at the boundaries and inclusions. The propagation of these newly generated dislocations in the matrix causes the formation of cleared channels. Implications of these results are discussed with specific reference to the origin and consequences of plastic flow localization.

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“…Early work examined the grain boundary structures and energies of fcc metals in symmetric and asymmetric tilt grain boundaries. [190][191][192] In general, these studies have shown that the grain boundary has a minimum energy structure that is composed of combinations of structural units (i.e., grain boundary dislocations) from particular low-order coincident site lattice boundaries (low R boundaries, such as the R3 coherent twin boundary). For the interested reader, some recent works have calculated the structures and energies for symmetric/asymmetric tilt/twist/ mixed character grain boundaries in Cu, Ni, and/or Al; [193][194][195] in particular, Olmsted et al 193 explored 388 distinct Ni and Al boundaries to ascertain relationships with grain boundary energy and grain boundary mobility.…”

Section: Grain Boundary (Bicrystal) MD Simulationsmentioning

confidence: 99%

“Bulk” Nanocrystalline Metals: Review of the Current State of the Art and Future Opportunities for Copper and Copper Alloys

Tschopp

Murdoch

Kecskes

et al. 2014

JOM

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It is a new beginning for innovative fundamental and applied science in nanocrystalline materials. Many of the processing and consolidation challenges that have haunted nanocrystalline materials are now more fully understood, opening the doors for bulk nanocrystalline materials and parts to be produced. While challenges remain, recent advances in experimental, computational, and theoretical capability have allowed for bulk specimens that have heretofore been pursued only on a limited basis. This article discusses the methodology for synthesis and consolidation of bulk nanocrystalline materials using mechanical alloying, the alloy development and synthesis process for stabilizing these materials at elevated temperatures, and the physical and mechanical properties of nanocrystalline materials with a focus throughout on nanocrystalline copper and a nanocrystalline Cu-Ta system, consolidated via equal channel angular extrusion, with properties rivaling that of nanocrystalline pure Ta. Moreover, modeling and simulation approaches as well as experimental results for grain growth, grain boundary processes, and deformation mechanisms in nanocrystalline copper are briefly reviewed and discussed. Integrating experiments and computational materials science for synthesizing bulk nanocrystalline materials can bring about the next generation of ultrahigh strength materials for defense and energy applications.

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The influence of grain boundary inclination on the structure and energy of σ = 3 grain boundaries in copper

Cited by 201 publications

References 27 publications

Relative grain boundary area and energy distributions in nickel

Relative grain boundary area and energy distributions in nickel

Initiation and propagation of cleared channels in neutron-irradiated pure copper and a precipitation hardened CuCrZr alloy

“Bulk” Nanocrystalline Metals: Review of the Current State of the Art and Future Opportunities for Copper and Copper Alloys

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