Abstract:We examine experimental and theoretical results on the cold-work (Snoek-Köster) peak in bcc Fe due to H using density functional theory (DFT). We reaffirm that Seeger's interpretation of the H cold-work peak (Hcwp), involving motion of H with kinks on non-screw dislocations associated with the intrinsic-dislocation α peak, has experimental backing. Use of the solute-dragging theory of Schoeck suggests a H-mixed dislocation binding energy of 0.3 eV. The theory of Hirth, that the Hcwp involves H-screw dislocatio… Show more
“…where u i and r i are the polar coordinates defined in [41] with the extra plane of the edge dislocation above the glide plane and b = (mb e /3p)((1 + n)/(1 − n)Dv) where μ and ν are the elastic constants, b e is the norm of the Burgers vector and Dv represents a local volume change related to the insertion of the H atom at position (u i , r i ). With Dv equal to 20% of the atomic volume, the segregation energy at (u i = −p/2, r i = b e ) is −0.13 eV, a reasonable value for searching an upper bound of the elastic trapping effect (for DFT calculations on H at a screw dislocation in Fe, see [44]). Furthermore, stress also affects the energy in the saddle configuration, also in a linear way [43].…”
This paper studies the effect of a plastic shear on the tetrahedral vs. octahedral site stability for hydrogen, in aluminium. Based on Density Functional Theory calculations, it is shown that the tetrahedral site remains the most stable site. It transforms into the octahedral site of the local hexagonal compact structure of the intrinsic stacking fault. The imperfect stacking is slightly attractive with respect to a regular lattice site. It is also shown that the shearing process involves a significant decrease of the energetic barrier for hydrogen jumps, at half the value of the Shockley partial Burgers vector, but not in the intrinsic stacking fault. These jumps involve a displacement component perpendicular to the shearing direction which favours an enhancement of hydrogen diffusion along edge dislocation cores (pipe diffusion). The magnitude of the boost in the jump rate in the direction of the dislocation line, according to Transition State Theory and taking into account the zero point energy correction, is of the order of a factor 50, at room temperature. First Passage Time Analysis is used to evaluate the effect on diffusion which is significant, by only at the nanoscale. Indeed, the common dislocation densities are too small for these effects (trapping, or pipe diffusion) to have a signature at the macroscopic level. The observed drop of the effective diffusion coefficient could therefore be attributed to the production of debris during plastic straining, as proposed in the literature.
“…where u i and r i are the polar coordinates defined in [41] with the extra plane of the edge dislocation above the glide plane and b = (mb e /3p)((1 + n)/(1 − n)Dv) where μ and ν are the elastic constants, b e is the norm of the Burgers vector and Dv represents a local volume change related to the insertion of the H atom at position (u i , r i ). With Dv equal to 20% of the atomic volume, the segregation energy at (u i = −p/2, r i = b e ) is −0.13 eV, a reasonable value for searching an upper bound of the elastic trapping effect (for DFT calculations on H at a screw dislocation in Fe, see [44]). Furthermore, stress also affects the energy in the saddle configuration, also in a linear way [43].…”
This paper studies the effect of a plastic shear on the tetrahedral vs. octahedral site stability for hydrogen, in aluminium. Based on Density Functional Theory calculations, it is shown that the tetrahedral site remains the most stable site. It transforms into the octahedral site of the local hexagonal compact structure of the intrinsic stacking fault. The imperfect stacking is slightly attractive with respect to a regular lattice site. It is also shown that the shearing process involves a significant decrease of the energetic barrier for hydrogen jumps, at half the value of the Shockley partial Burgers vector, but not in the intrinsic stacking fault. These jumps involve a displacement component perpendicular to the shearing direction which favours an enhancement of hydrogen diffusion along edge dislocation cores (pipe diffusion). The magnitude of the boost in the jump rate in the direction of the dislocation line, according to Transition State Theory and taking into account the zero point energy correction, is of the order of a factor 50, at room temperature. First Passage Time Analysis is used to evaluate the effect on diffusion which is significant, by only at the nanoscale. Indeed, the common dislocation densities are too small for these effects (trapping, or pipe diffusion) to have a signature at the macroscopic level. The observed drop of the effective diffusion coefficient could therefore be attributed to the production of debris during plastic straining, as proposed in the literature.
“…[ 42,43 ] Alternatively, using Hirth's interpretation, the binding of hydrogen to a screw dislocation could be estimated to be 0.2–0.3 eV based on the shift of the γ‐peak toward lower temperatures, [ 61 ] which is in correspondence to binding energies obtained by DFT calculations. [ 41–44 ] But although the H‐CW peak in bcc iron has been investigated quite extensively, [ 42,65,66,69–78 ] only limited studies have been made linking this peak to the hydrogen trapping capacity and HE. Kikuta et al [ 79 ] observed a correlation with the height of the H‐CW peak and the decrease of the notch tensile strength for pure iron and a high‐strength steel.…”
Section: The Interaction Of Microstructural Defects With Hydrogen Revealed By Ifmentioning
confidence: 92%
“…For example, using the Schoeck model, the binding energy of hydrogen to mixed dislocations can be determined to be 0.3 eV, [ 69 ] which is rather similar to the values obtained by TDS [ 17,21,22,61 ] and DFT results. [ 42,43 ] Alternatively, using Hirth's interpretation, the binding of hydrogen to a screw dislocation could be estimated to be 0.2–0.3 eV based on the shift of the γ‐peak toward lower temperatures, [ 61 ] which is in correspondence to binding energies obtained by DFT calculations. [ 41–44 ] But although the H‐CW peak in bcc iron has been investigated quite extensively, [ 42,65,66,69–78 ] only limited studies have been made linking this peak to the hydrogen trapping capacity and HE.…”
Section: The Interaction Of Microstructural Defects With Hydrogen Revealed By Ifmentioning
confidence: 95%
“…[ 62 ] Nevertheless, a combined action of both the Hirth and Seeger mechanisms was proposed by Gibala. [ 42 ] In this case, the Hirth and Seeger mechanisms are considered to be operating more or less simultaneously and the H‐CW peak temperature is determined by the extent at which the H‐edge/mixed dislocations and the H‐screw interactions meet in IF space and allow for Schoeck‐like bowing. Furthermore, the H‐CW peak has also been mentioned to consist of two peaks, one at 120 K and one at 150 K. One way of interpretation is that the first peak is related to the interaction of hydrogen with the nonscrew dislocations and the second peak is related to the interaction with screw dislocations.…”
Section: The Interaction Of Microstructural Defects With Hydrogen Revealed By Ifmentioning
confidence: 99%
“…Various authors [ 34–39 ] have reported DFT calculations indicating that hydrogen can lower the vacancy formation energy and, as such, enhance vacancy formation, which is one of the cornerstones of the HESIV mechanism. Furthermore, the binding energy of hydrogen to dislocations is shown to be strongly dependent on the position of hydrogen at the dislocation [ 40–42 ] and the dislocation type. [ 43,44 ] Typically, the maximum binding energy at an edge dislocation core is ≈0.4–0.5 eV, [ 44 ] whereas the maximum binding energy to a screw dislocation is considerably lower, i.e., ≈0.2–0.3 eV.…”
Hydrogen embrittlement of steels is known to have considerable impact in many engineering sectors. To be able to mitigate the hydrogen embrittlement problem, a profound comprehension of the interaction of hydrogen with the steel microstructure is required. Especially the interaction of hydrogen with dislocations and vacancies is very relevant as these defects are known to play an important role in hydrogen embrittlement. At present, thermal desorption spectroscopy is mostly used to study hydrogen–defect interactions. However, information obtained solely by this technique is insufficient to obtain a full understanding of the interaction of hydrogen with these defects in the steel microstructure. Herein, the use of internal friction, as a complementary technique to thermal desorption spectroscopy, to reveal the interaction of hydrogen with dislocations and vacancies, is reviewed based on the present understanding in the literature. Furthermore, the opportunities to use internal friction to characterize the interaction between hydrogen and these defects and to give more insight into the hydrogen embrittlement mechanism are discussed. It is demonstrated that internal friction has not yet been used to its full potential for this purpose, although it entails the opportunity to develop fundamental insights into the hydrogen embrittlement phenomenon.
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