Grain Boundary Plane Distributions in Modified 316 LN Steel Exposed at Elevated and Cryogenic Temperatures

Downey, S.; Bembridge, Nicholas; Kalu, Peter N.; Miller, Herbert M.; Rohrer, Gregory S.; Han, Ke

doi:10.1007/s10853-007-1959-1

Cited by 19 publications

(19 citation statements)

References 8 publications

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“…It is also possible to calculate the GBCD through the stereological analysis of two‐dimensional orientation maps 22 . Because this is much easier than serial sectioning, it has been more widely adopted 8,23–44 . The main limitation of stereology is that, in its current form, it can not be applied to materials with significant orientation texture.…”

Section: The Emergence Of New Techniques To Measure Gb Distributimentioning

confidence: 99%

Measuring and Interpreting the Structure of Grain‐Boundary Networks

Rohrer

2011

Journal of the American Ceramic Society

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Recently developed techniques to measure the structure of interfacial networks in three dimensions have the potential to revolutionize our ability to control the microstructures of polycrystals and interface-dominated materials properties. This paper reviews recent findings from two-and three-dimensional orientation mapping studies. The observations confirm a strong inverse correlation between the relative energies of grain boundaries and the frequency with which they occur in microstructures. The observations also show that during microstructure evolution, relatively higher energy grain boundaries are more likely to be shrinking while lower energy interfaces are more likely to be growing. These processes can lead to a steady-state distribution of grain boundaries that is influenced as much by the relative grain-boundary energies as by the exact processing conditions. Recent findings and emerging opportunities for grainboundary characterization are reviewed in the final section of the paper.Automated EBSD, which makes it possible to accumulate a map of orientations on a surface, has had a transformative effect on the study of grain boundaries in polycrystals (see Panel B). 10 It is Panel A. Description of multidimensional representations of grain boundary character distributions.Three different representation of the distribution of relative areas of different types of grain boundaries, using the same data. This example is for a hexagonal material, WC. (a) This is a single-parameter disorientation distribution. Each boundary is classified by its minimum misorientation angle, without consideration of the misorientation axis. Compared with the random distribution, there is an enhancement of grain boundaries with 301 and 901 disorientation. (b) When one considers the axis and angle of the misorientation, there are three independent parameters for each boundary, two for axis direction and one for the rotation angle. Therefore, each position in a three-dimensional space corresponds to a different grain boundary. In each layer of the axis angle space, all possible axis are represented; the rotation angle varies along the vertical direction. Note that the peak for 301 in (a) is concentrated at [0001], indicating that these are mostly 301 rotations about [0001], and the peak at 901 is concentrated at [10-10], indicating that this is the dominant misorientation axis. For any particular axis angle combination, there is a distribution of grain-boundary planes, as shown for the examples in (c) and (d). Note that when the misorientation axis, the misorientation angle, and the grain-boundary planes are specified, there are five independent parameters. The grainboundary plane distributions (c) and (d) are the relative areas of different grain-boundary planes at for the misorientation of 901 about [10-10] (c) 301 about [0001]. The plots are stereographic projections. The maxima show that the 901 [10-10] misorientation boundaries are concentrated on [10-10] planes, indicating that they are also pure twist boundaries. The local max...

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Section: The Emergence Of New Techniques To Measure Gb Distributimentioning

confidence: 99%

Measuring and Interpreting the Structure of Grain‐Boundary Networks

Rohrer

2011

Journal of the American Ceramic Society

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“…The coincident site lattice (CSL) model is one of the important methods to describe the grain boundary characteristics. The CSL boundaries, Σ3 n ( n = 1, 2, 3) including primary twins Σ3 (60°/<111>), higher order twins Σ9 (38.9°/<101>), [ 45 ] Σ27a (31.6°/<110>), [ 46 ] and Σ27b (35.4°/<210>) [ 47 ] play a significant role in the DRX process. [ 26 ] The interactions between Σ3 n boundaries are described as the following relationships [ 48 ]

\sum 3 + \sum 3 \to \sum 9, \sum 3 + \sum 9 \to \sum 3, \sum 3 + \sum 9 \to \sum 27

…”

Section: Resultsmentioning

confidence: 99%

“…(60 /<111>), higher order twins Σ9 (38.9 /<101>), [45] Σ27a (31.6 /<110>), [46] and Σ27b (35.4 /<210>) [47] play a significant role in the DRX process. [26] The interactions between Σ3 n boundaries are described as the following relationships [48]…”

Section: Arrhenius-type Constitutive Modelingmentioning

confidence: 99%

Hot Deformation Characteristics and Dynamic Recrystallization Mechanisms of a Novel Nickel‐Based Superalloy

Jia

et al. 2020

Adv Eng Mater

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The hot deformation characteristics of a novel nickel‐based superalloy is investigated via the isothermal compression test in temperature range of 1000–1150 °C and strain rate of 0.001–10 s−1 under the true strain of 0.8. The hot deformation characteristics of GH4065 alloy are studied here for the first time. Based on the flow stress data, it is observed the typical features of flow curves exhibit the occurrence of dynamic recrystallization (DRX) during the hot deformation process. The constitutive equation in the Arrhenius‐type model is established, and activation energy (Q) is determined as 844.787 kJ mol−1. The microstructure evolution and DRX mechanism are investigated by electron backscatter diffraction (EBSD) and transmission electron microscopy (TEM) technique. The results reveal that the fraction of low angle grain boundaries (LAGBs) decrease gradually with the increase in deformation temperature, whereas the fraction of Σ3 boundaries increase first and then decrease. For γ + γ′ dual‐phase region, the particle‐induced DRX (PIDRX), characterized by the generation of sub‐grains accelerated by γ′ precipitates pinning dislocations, and discontinuous dynamic recrystallization (DDRX) are the dominant nucleation mechanism of DRX. For γ quasi‐phase region and γ single‐phase region, the occurrence of bulged grain boundaries with twins further illustrates that DDRX plays a more significant role.

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“…A typical structural conduit material used for these CICC operating at cryogenic temperatures down to 4.2 K is the austenitic stainless steel 316LN [7]. Especially the high-nitrogen austenitic steel, 316LN was qualified for that temperature by numerous experiments in the past [8][9][10][11][12][13][14][15]. 316LN has a wide application for cryogenic components and an excellent combination of mechanical and physical properties such as resistance to neutron radiation and corrosion [7].…”

Section: Introductionmentioning

confidence: 99%

Effect of Aging on Mechanical Properties of 316ln at 4.2 K for Fusion Applications

Sas

Kauffmann-Weiss

Weiss

2018

Acta Metall Slovaca

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Within the fusion magnet technology the low-temperature superconductor Nb3Sn is usually used for high magnetic field in the range of 12 T and 4.5 K. These superconductors are produced as round strands. Here Nb3Sn filaments are embedded in a round copper matrix with a diameter of about 0.8 mm. To allow magnet windings of several Mega-Ampere to produce the needed magnetic field, about 900 superconducting strands are cabled and compacted in a stainless steel conduit resembling the so-called cable-in-conduit-conductor (CICC). However, the mechanically brittle Nb3Sn superconducting phase is produced by the diffusion reaction by a long-term heat treatment. Therefore, the magnet winding containing the superconducting strands together with the stainless steel jacket has to undergo this heat treatment. In order to simulate the magnet manufacturing process, seamless tubes were compacted, bend and straightened and tensile stretched by 2.5 % at room temperature followed by the heat treatment necessary for the Nb3Sn formation. The aim of this study was to compare the microstructures and tensile properties at cryogenic operation temperature of two modified 316LN austenitic stainless steels with very-low carbon (≤0.013) in the as built conditions and after heat treatments. Scanning Electron Microscopy (SEM), Electron Backscatter Diffraction (EBSD) and X-ray diffraction were used to study microstructure. Deformation behaviour was investigated by tensile test at 4.2 K.

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Grain Boundary Plane Distributions in Modified 316 LN Steel Exposed at Elevated and Cryogenic Temperatures

Cited by 19 publications

References 8 publications

Measuring and Interpreting the Structure of Grain‐Boundary Networks

Measuring and Interpreting the Structure of Grain‐Boundary Networks

Hot Deformation Characteristics and Dynamic Recrystallization Mechanisms of a Novel Nickel‐Based Superalloy

Effect of Aging on Mechanical Properties of 316ln at 4.2 K for Fusion Applications

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