scholarly journals Revealing the Subsurface Basal 〈a〉 Dislocation Activity in Magnesium Through Lattice Rotation Analysis

2020 ◽  
Vol 51 (9) ◽  
pp. 4414-4421
Author(s):  
Bijin Zhou ◽  
Leyun Wang ◽  
Wenjun Liu ◽  
Xiaoqin Zeng ◽  
Yanjun Li
Keyword(s):  
Slip System ◽  
Pole Figure ◽  
Trace Analysis ◽  
Basal Slip ◽  
Lattice Rotation ◽  
Burgers Vector ◽  
Dislocation Activity ◽  
Complementary Method ◽  
Dislocation Behavior ◽  
Basal Dislocation

Abstract A method was proposed in this study to reveal the subsurface basal dislocation activity in Mg-Y alloy and determine the corresponding Burgers vector. This is achieved by correlating the slip directions of dislocations to the lattice rotation represented by the {0001} pole figure. The identified basal slip system by this approach was verified by micro-Laue diffraction. This method can be applied as a complementary method to the conventional slip trace analysis to study the dislocation behavior of Mg alloys.

Formation of Whisker in Pure Sn under Tensile Stress and a Method of its Suppression

2012 ◽  
Vol 706-709 ◽  
pp. 751-756 ◽  
Author(s):  
Kiyomichi Nakai ◽  
Tatsuaki Sakamoto ◽  
Takeaki Miyamoto ◽  
Sengo Kobayashi
Keyword(s):  
Heat Treatment ◽  
Tensile Stress ◽  
Slip System ◽  
Edge Dislocation ◽  
Pipe Diffusion ◽  
Sn Whisker ◽  
Screw Dislocations ◽  
Burgers Vector ◽  
Dislocation Behavior ◽  
Pure Sn

Effect of dislocation behavior on formation of whisker in pure Sn has been investigated. Slip system in β-Sn was determined; slip plane is , and Burgers vector b is . The magnitude of Burgers vector is larger than the smallest interatomic spacing in β-Sn. This means that there is broad space under the extra half plane of edge dislocation. It sould be noted that pipe diffusion along the edge dislocation is enhanced in β-Sn, resulting in easy supply of Sn atoms at the root of Sn whisker [1, 2]. Si-bearing particles, which precipitate on surface of bulk Sn by heat-treatment in quartz tube, suppress the accumulation of both edge and screw dislocations to same area. It is greatly effective for the suppression of the nucleation of Sn whisker.

Dislocations in alumina deformed by prismatic slip

1978 ◽  
Vol 36 (1) ◽  
pp. 606-607
Author(s):  
J. Cadoz ◽  
J. Castaing ◽  
J. Philibert
Keyword(s):  
Electron Microscopy ◽  
Transmission Electron Microscopy ◽  
Basal Slip ◽  
Prismatic Slip ◽  
Compression Tests ◽  
Thin Sections ◽  
Burgers Vector ◽  
Maximum Deformation ◽  
Transmission Electron ◽  
Mechanical Thinning

Plastic deformation of alumina has been much studied; basal slip occurs and dislocation structures have been investigated by transmission electron microscopy (T.E.M.) (1). Non basal slip has been observed (2); the prismatic glide system <1010> {1210} has been obtained by compression tests between 1400°C and 1800°C (3). Dislocations with <0110> burgers vector were identified using a 100 kV microscope(4).We describe the dislocation structures after prismatic slip, using high voltage T.E.M. which gives much information.Compression tests were performed at constant strainrate (∿10-4s-1); the maximum deformation reached was 0.03. Thin sections were cut from specimens deformed at 1450°C, either parallel to the glide plane or perpendicular to the glide direction. After mechanical thinning, foils were produced by ion bombardment. Details on experimental techniques can be obtained through reference (3).

scholarly journals Quantitative study of the effect of grain boundary parameters on the slip system level Hall-Petch slope for basal slip system in Mg-4Al

2020 ◽  
Vol 200 ◽  
pp. 148-161 ◽  
Author(s):  
Mohsen Taheri Andani ◽  
Aaditya Lakshmanan ◽  
Veera Sundararaghavan ◽  
John Allison ◽  
Amit Misra
Keyword(s):  
Grain Boundary ◽  
Slip System ◽  
Quantitative Study ◽  
Basal Slip ◽  
System Level

Deformation banding in single crystal with predominant activity of basal slip system

2018 ◽  
Vol 2018 (0) ◽  
pp. OS0107
Author(s):  
Tsuyoshi MAYAMA ◽  
Kousuke TAKAGI ◽  
Yoji MINE ◽  
Kazuki TAKASHIMA
Keyword(s):  
Slip System ◽  
Single Crystal ◽  
Basal Slip ◽  
Deformation Banding

scholarly journals Mobility of Edge Dislocations in the Basal‐Slip System of Zinc

1967 ◽  
Vol 38 (10) ◽  
pp. 4011-4018 ◽  
Author(s):  
D. P. Pope ◽  
T. Vreeland ◽  
D. S. Wood
Keyword(s):  
Slip System ◽  
Basal Slip ◽  
Edge Dislocations

Simulation of Dislocation Dynamics in the Continuum Limit

1998 ◽  
Vol 538 ◽  
Author(s):  
K. W. Schwarz
Keyword(s):  
Slip System ◽  
Strong Interaction ◽  
Continuum Limit ◽  
Dislocation Dynamics ◽  
The Self ◽  
Burgers Vector ◽  
Strained Layer ◽  
The Continuum

AbstractPeach-Koehler theory is implemented to simulate the motion of three-dimensionally interacting dislocations, located on various glide planes and having any allowed Burgers vector. The self-interaction is regularized by a modified Brown procedure, which remains stable and loses accuracy in a well-controlled manner as atomic dimensions are approached. The method is illustrated by applying it to several problems involving interacting dislocations in an fcc slip system. The strong interaction of two dislocations on intersecting glide planes is investigated with a view towards developing a set of rules to describe the outcome of such interactions. The effect of Frank-Read sources in relaxing a strained layer are illustrated, both for sources on parallel and on intersecting glide planes.

The Slip Transfer Process Through Grain Boundaries in HCP Ti

1993 ◽  
Vol 319 ◽  
Author(s):  
J. Shirokoff ◽  
I.M. Robertson ◽  
H.K. Birnbaum
Keyword(s):  
Grain Boundary ◽  
Slip System ◽  
Grain Boundaries ◽  
Slip Systems ◽  
Boundary Dislocation ◽  
Burgers Vector ◽  
Slip Transfer ◽  
Transmission Electron ◽  
Fcc Materials

AbstractInformation on the mechanisms of slip transfer across grain boundaries in an HCP α-Ti alloy has been obtained from deformation experiments performed In situ in the transmission electron microscope. Initially, lattice dislocations are accommodated within the grain boundary until a critical local dislocation density is reached. The boundary then responds by activating slip in the adjoining grain on the slip system experiencing the highest local resolved shear stress and producing the residual grain-boundary dislocation with the smallest Burgers vector. Slip on secondary slip systems may be initiated provided they reduce the magnitude of the Burgers vector of, or eliminate, the residual grainboundary dislocation. The selection rules used to predict the slip system activated by the grain boundary are the same as apply in ordered and disordered FCC materials.

Universal Scaled Strength Behaviour for Micropillars and Nanoporous Materials

2009 ◽  
Vol 1185 ◽  
Author(s):  
Brian Derby ◽  
Rui Dou
Keyword(s):  
Shear Modulus ◽  
Slip System ◽  
Strong Correlation ◽  
Nanoporous Materials ◽  
Nanoporous Gold ◽  
Burgers Vector ◽  
Fcc Metals ◽  
Specimen Diameter ◽  
Bcc Structure ◽  
Fcc Structure

AbstractThe strength of submicron FCC structure metal columns, σ, fabricated by FIB machining or electrodeposition, shows a strong correlation with specimen diameter, d, with σ/μ = A(d/b)−0.63, where A is a constant, μ is the single crystal shear modulus resolved onto the slip system and b is the Burgers' vector. The strength of BCC structure metals does not show such a well defined correlation with size across different metals but the data occupies the same region of parameter space as with the FCC metals. Nanoporous gold specimens show a similar size-correlated behaviour but with an exponent of −0.5. This may indicate different mechanisms operating in each case.

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