Pseudo-subgrain-boundaries in stainless steel

Bollmann, W.; Michaut, B.; Sainfort, G.

doi:10.1002/pssa.2210130236

Cited by 125 publications

(19 citation statements)

References 9 publications

(1 reference statement)

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“…An example in stainless steel was discussed by Bollmann, Michaut & Sainfort (1972). The fact that crystal dislocations can act as secondary dislocations seems to be related to the low stacking-fault energy of stainless steel.…”

Section: The Secondary Level 321 the Conservation Of A Coincidencementioning

confidence: 99%

Continuous distribution of dislocations in intercrystalline boundaries

Bollmann¹

1977

Acta Cryst Sect A

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The structure of a dislocation network in a crystal boundary depends, among other parameters, on the two crystal structures and their relation, i.e. the linear transformation leading from one crystal lattice to the other. For the same transformation, the structure of the network is related to the crystal structure. The link between the transformation and the many possible dislocation networks is described by a theorem which states that the displacement field of the linear transformation in the boundary can be described in an infinite number of ways by continuous dislocation distributions. The discrete dislocations are then obtained by grouping the continuous dislocations. The O-lattice theory is discussed in relation to these new aspects, particularly with respect to the features which tend to be conserved in the boundary. A special discussion is given of the case where a common crystallographic axis, without the relaxation pattern being periodic, represents the preferred state.

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Section: The Secondary Level 321 the Conservation Of A Coincidencementioning

confidence: 99%

Continuous distribution of dislocations in intercrystalline boundaries

Bollmann¹

1977

Acta Cryst Sect A

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“…Burgers vector (Bollmann, 1970;Bollmann, Michaut & Sainfort, 1972) and step height (King & Smith, 1980) must be conserved. A lattice dislocation can also be transmitted through a grain boundary by creating a lattice dislocation in the other grain and yielding a residual perfect DSC dislocation in the grain boundary.…”

Section: Fu-rong Chen and A H King 421mentioning

confidence: 99%

“…Also of importance in describing the grain-boundary geometry is the so-called DSC lattice, which is a lattice made up of vectors which represent displacements of one crystal with respect to the other which leave the boundary structure shifted, but complete: DSC vectors thus define the allowable Burgers vectors of perfect grain-boundary dislocations. The existence of DSC dislocations in high-angle grain boundaries, conserving structures of high lattice coincidence through small changes in misorientation, has been confirmed by various transmission electron microscope investigations; most of these observations were made in materials with cubic crystal structures (Bollmann, Michaut & Sainfort, 1972;Clark & Smith, 1978;Sun & Balluffi, 1982). The behavior of grain boundaries, in many cases, has also been linked to the properties of grain-boundary dislocations, although this frequently requires that further geometrical concepts be brought into consideration.…”

Section: Introductionmentioning

confidence: 95%

The further geometry of grain boundaries in hexagonal close-packed metals

Chen¹,

King²

1987

Acta Crystallogr Sect B

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A technique is given for finding partial DSC vectors appropriate to crystals with more than one atom per lattice site. The DSC lattice is made up of vectors that represent displacements of one crystal with * Now at Department of Materials Science and Engineering, Massachusetts Institute of Technology, Cambridge, MA 02139, USA.respect to the other that leave the boundary structure shifted, but not complete. A new, rapid method for finding the step vectors associated with perfect DSC dislocations is described. Partial DSC vectors and step vectors for perfect DSC dislocations in hexagonal close-packed crystals are determined. The availability of reactions between lattice partial dislocations and grain boundaries in hexagonal closepacked crystals is also assessed.0108-7681/87/050416-07501.50 (~ 1987 International Union of Crystallography FU-RONG CHEN AND A. H. KING 417 IntroductionGeometrical models of the structures of grain boundaries have received a great deal of attention since the early 1970's, with considerable emphasis being placed upon understanding the principles which govern structure, and the ways in which structure influences the grain-boundary properties (Smith & Pond, 1976;Sutton, 1984). Grain-boundary geometry has been described in terms of the coincidence-site lattice (CSL), and its generalization called the O lattice (which is the lattice of possible origins of the transformation which produces crystal 2 from crystal 1). Also of importance in describing the grain-boundary geometry is the so-called DSC lattice, which is a lattice made up of vectors which represent displacements of one crystal with respect to the other which leave the boundary structure shifted, but complete: DSC vectors thus define the allowable Burgers vectors of perfect grain-boundary dislocations. The existence of DSC dislocations in high-angle grain boundaries, conserving structures of high lattice coincidence through small changes in misorientation, has been confirmed by various transmission electron microscope investigations; most of these observations were made in materials with cubic crystal structures (Bollmann, Michaut & Sainfort, 1972;Clark & Smith, 1978;Sun & Balluffi, 1982). The behavior of grain boundaries, in many cases, has also been linked to the properties of grain-boundary dislocations, although this frequently requires that further geometrical concepts be brought into consideration. Two important geometrical features have been identified beyond the usual CSL, O lattice and DSC lattice: the first of these is the step vector associated with a DSC dislocation, which is used in determining the height of the step in the grain-boundary plane that is associated with the core of a grain-boundary dislocation. The definition of the step vector and an extensive description of its properties was given by King & Smith (1980) and step vectors for grainboundary dislocations in cubic materials were tabulated by King (1982). Quantitative confirmation of the importance of step vectors in determining the behavior of grain b...

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“…With regard to the diffusional phase transformation of twophase alloys, many researchers have reported on the morphology of a precipitate to elucidate the rule for determining its shape from both experimental 1) and theoretical 2) viewpoints because the shape affects the macromechanical properties. These studies are roughly classified into two categories-interphase energy 3) and elastic strain.…”

Section: Introductionmentioning

confidence: 99%

Prediction of Precipitate Morphology by Atomic Matching Model and FEM Analysis with Consideration of Anisotropy Elastic Strain in a BCC/HCP system

et al. 2008

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This study focuses on the entire shape of the precipitate in Ti-22V-4Al in terms of the interphase and elastic strain energies generated between the precipitate and matrix. In order to consider a transformation strain, the volumetric strain and strain relaxation by a misfit dislocation on the interphase boundary are calculated. Firstly, the atomic matching model is employed for determining the preferred habit planes by evaluating the results of geometrical atomic matching. Subsequently, the precipitate configuration that consists of the preferred habit plane is determined by the elastic strain with the minimum value. Then, the elastic strain surrounding and within the predicted precipitate is examined by an FEM analysis, which can be used to calculate the anisotropic elastic strain depending on the shape of the precipitate. A comparison of these results with regard to the precipitate observed by TEM elucidates the determination of the ideal shape of the precipitates in BCC/HCP systems; the optimum configuration of the precipitate that consists of the preferred habit plane is determined by the tradeoff relationship of two factors; one is the strain relaxation due to an increment in the broad face plane, and the other is the decrease in the total elastic strain as the surface ratio approaches a regular square.

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Pseudo-subgrain-boundaries in stainless steel

Cited by 125 publications

References 9 publications

Continuous distribution of dislocations in intercrystalline boundaries

Continuous distribution of dislocations in intercrystalline boundaries

The further geometry of grain boundaries in hexagonal close-packed metals

Prediction of Precipitate Morphology by Atomic Matching Model and FEM Analysis with Consideration of Anisotropy Elastic Strain in a BCC/HCP system

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