Dislocation modelling in Ti<sub>2</sub>AlN MAX phase based on the Peierls–Nabarro model

Gouriet, Karine; Carrez, Philippe; Cordier, Patrick; Guitton, Antoine; Joulain, Anne; Thilly, L.; Tromas, C.

doi:10.1080/14786435.2015.1066938

Cited by 27 publications

(12 citation statements)

References 41 publications

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“…violation of Schmid's law has been readily observed in bcc metals [20][21][22][23][24], and it has been postulated that it is due to the non-planar spreading of the screw dislocation core in the presence of stresses other than the resolved shear stress [23]. In MAX phases, dislocation glide is confined to the basal plane [5][6][7], and in ref. [6], it was shown that this results in strong interactions and dislocation alignments along specific orientations that may lead to elevated lattice friction.…”

Section: Resultsmentioning

confidence: 99%

“…While MAX phases have only two independent basal slip systems [5][6][7], the existence of additional deformation and failure mechanisms facilitated by their CONTACT Ankit Srivastava ankit.sri@tamu.edu nanolayered structure distinguishes them from other materials with an insufficient number of slip systems. The weakly bonded MX-A interlayers in the MAX phases not only facilitate crystallographic slip but also cleavage, buckling of layers, ripplocations and kinking [3,4,[8][9][10][11][12].…”

Section: Introductionmentioning

confidence: 99%

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Non-classical crystallographic slip in a ternary carbide – Ti₂AlC

Zhan

Chen

Radović

et al. 2020

Materials Research Letters

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Herein, we report on mechanical deformation of single-crystal Ti 2 AlC MAX phase using compression testing of micropillars with a range of crystallographic orientations. Our results show that depending on the crystallographic orientation, the Ti 2 AlC micropillars either undergo only non-classical (non-Schmid) crystallographic slip, non-classical crystallographic slip followed by cleavage or cleavage without any appreciable crystallographic slip. The non-classical crystallographic slip is found to be a result of the strong dependence of crystallographic slip on both, the resolved shear stress and the stress normal to the slip plane.

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Section: Resultsmentioning

confidence: 99%

Section: Introductionmentioning

confidence: 99%

Non-classical crystallographic slip in a ternary carbide – Ti₂AlC

Zhan

Chen

Radović

et al. 2020

Materials Research Letters

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“…The calculation of the GSFE surface involves the quantification of the response to shearing of specific crystal planes along specific slip directions. One of the first instances in which the GSFE surface for MAX phases was calculated was the work by Gouriet et al [15]. In that case, the GSFE was calculated by sliding (0001) planes at different cutting levels (i.e.…”

Section: Introductionmentioning

confidence: 99%

Effect of A mixing on elastic modulus, cleavage stress, and shear stress in the Ti3(SixAl1−

et al. 2017

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Solid solution MAX phases offer the opportunity for further tuning of the thermo-mechanical and functional properties of MAX phases, increasing their envelope of performance. Previous experimental results show that the lattice parameters of Ti 3 (Si x Al 1−x)C 2 decrease, while the Young's modulus increases with increased Si content in the lattice. In this work, we present a computational investigation of the structural, electronic, and mechanical properties of Ti 3 (Si x Al 1−x)C 2 (x= 0, 0.25, 0.5, 0.75, and 1). The solid solutions were modeled using special quasirandom structures (SQS) and calculated using Density Functional Theory (DFT), which is implemented in the Vienna Ab initio Simulation Package (VASP). The SQS structures represent random mixing of Al and Si in the A sublattice of 312 MAX phase and their structural, electronic, and mechanical properties were calculated and compared with experiments. We study the cleavage and slip behavior of Ti 3 (Si x Al 1−x)C 2 to investigate the deformation behavior in terms of cleavage and shear. It has been shown that the cleavage between M and A layers results in increasing cleavage stress in Ti 3 (Si x Al 1−x)C 2 as a function of Si content in the lattice. In addition, the shear deformation of hexagonal close packed Ti 3 (Si x Al 1−x)C 2 under 2110 {0001} and 0110 {0001} results in increasing unstable stacking fault energy (USFE) and ideal shear strength (ISS) in Ti 3 (Si x Al 1−x)C 2 as the system becomes richer in Si.

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“…[78,79] However, in crystals with large unit cells and especially where repeating sub-units are also large, the use of ab initio approaches is limited by the size of the required cell. Other modeling approaches, such as atomistic modeling requiring suitable interatomic potentials [80] and novel methods for extraction of dislocation core structure [81] and lattice resistance [9] are advancing continuously.…”

Section: Extracting General Principles Of Plasticitymentioning

confidence: 99%

Microcompression of brittle and anisotropic crystals: recent advances and current challenges in studying plasticity in hard materials

Korte‐Kerzel

2017

MRS Communications

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Recent years have seen an increased application of small-scale uniaxial testing-microcompression-to the study of plasticity in macroscopically brittle materials. By suppressing fast fracture, new insights into deformation mechanisms of more complex crystals have become available, which had previously been out of reach of experiments. Structurally complex intermetallics, metallic compounds, or oxides are commonly brittle, but in some cases extraordinary, though currently mostly unpredictable, mechanical properties are found. This paper aims to give a survey of current advances, outstanding challenges, and practical considerations in testing such hard, brittle, and anisotropic crystals.While the origin of mechanical strength, toughness, and creep resistance is well studied in most metals, much less is known about the properties of more complex crystal structuresdespite their wide use as reinforcement phases and the undiscovered potential in their sheer number and variability. A major challenge in plasticity research of the next years will therefore be to close this gap in knowledge. Small-scale testing techniques have been demonstrated as a key enabling technique for such studies. Most prominent is microcompression, which helps overcome the fundamental challenge of studying plasticity in materials, which suffer from extreme brittleness in conventional testing. [1,2] Their plastic properties may, at first glance, appear to be of only academic interest: aiming to deduce fundamental relationships of crystal plasticity and structure to enable knowledge-guided search and data mining for new structural materials. However, they are in fact essential to performance at the microstructural scale of many advanced and highly alloyed materials and to understanding the effects of alloying strategies aimed at inducing deformability as baseline or reference information. Investigating plasticity in hard crystalsA deep understanding of plasticity and dislocation motion exists in most metallic crystals and strategies to engineer different aspects, for example by adjustment of the stacking fault energy, have been very successful. [3,4] These are being applied-with great effect-to hexagonal metals [3] which in spite of their closely related atomic packing show strongly anisotropic deformation and are therefore much more difficult to deform at low temperatures. In BCC metals, fundamental aspects of dislocation core structure, stress tensor dependence, and resulting non-Schmid behavior, are also still under investigation. [5,6] However, in all of these materials, the availability of large-grained or single crystals with sufficient purity has scarcely been a problem, nor has the ability to deform such samples under carefully controlled conditions. Suitable investigations by conventional, analytical and high-resolution microscopy techniques have also been carried out whenever new methods have allowed researchers to dive deeper into the physics of their plastic deformation.In intermetallics, ceramics, and compounds we face challeng...

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Dislocation modelling in Ti₂AlN MAX phase based on the Peierls–Nabarro model

Cited by 27 publications

References 41 publications

Non-classical crystallographic slip in a ternary carbide – Ti₂AlC

Non-classical crystallographic slip in a ternary carbide – Ti₂AlC

Effect of A mixing on elastic modulus, cleavage stress, and shear stress in the Ti3(SixAl1−

Microcompression of brittle and anisotropic crystals: recent advances and current challenges in studying plasticity in hard materials

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Dislocation modelling in Ti2AlN MAX phase based on the Peierls–Nabarro model

Cited by 27 publications

References 41 publications

Non-classical crystallographic slip in a ternary carbide – Ti2AlC

Non-classical crystallographic slip in a ternary carbide – Ti2AlC

Effect of A mixing on elastic modulus, cleavage stress, and shear stress in the Ti3(SixAl1−

Microcompression of brittle and anisotropic crystals: recent advances and current challenges in studying plasticity in hard materials

Contact Info

Product

Resources

About

Dislocation modelling in Ti₂AlN MAX phase based on the Peierls–Nabarro model

Non-classical crystallographic slip in a ternary carbide – Ti₂AlC

Non-classical crystallographic slip in a ternary carbide – Ti₂AlC