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BEGIN:VEVENT
DTSTAMP:20261006T220030Z
DTSTART;VALUE=DATE-TIME:20241125T130000
DTEND;VALUE=DATE-TIME:20241125T140000
SUMMARY:WCPM: Erik Bitzek\, Max-Planck-Institut für Eisenforschung
TZID:Europe/London
UID:20241125-8a1785d891c69ed40191cd6b9ef20f38@warwick.ac.uk
CREATED:20241125T084132Z
DESCRIPTION:Time: 13.00-14.00 Seminar location: A2.05B There will be an i
 nformal sandwich lunch outside D2.02 at 12.30. To join this meeting onli
 ne click here. Title: Atomistic Simulations of Dislocation – Precipitate
  Interactions in Ni-based Superalloys Abstract: The interaction between 
 dislocations and precipitates is one of the archetypical hardening mecha
 nisms in alloys and plays together with solid solution strengthening a c
 ritical role for the high (creep) strength of superalloys. Precipitation
  hardening in superalloys has been intensively studied\, e.g.\, through 
 TEM observations of interrupted creep tests\, and more recently by in-si
 tu micromechanical tests. Analytical and numerical models can successful
 ly describe many aspects of strengthening on the meso- and macroscale. H
 owever\, such models as discrete dislocation dynamics (DDD) simulations 
 require parameters\, which depend on the atomic-scale details of the dis
 location – precipitate interactions. Atomistic simulations can in princi
 ple provide such information but are currently severely limited by the l
 ack of accurate atomic interaction potentials for technologically releva
 nt\, multi-component alloys and by the difficulties to include diffusive
  processes. Therefore\, there are currently still relatively few atomist
 ic simulations of dislocation-precipitate interactions in superalloys. H
 ere we present an overview of our atomistic simulations in the Ni-Al-(Re
 ) system as model for γ/γ’ strengthened alloys. We show that while param
 eters like the cutting-stress for dislocations to enter γ’ precipitates 
 can be obtained from idealized geometries\, the details of the γ/γ’ inte
 rface structure\, the precipitate morphology and arrangement can severel
 y influence the dislocation-precipitate interactions. In particular the 
 curvature of the γ/γ’ interface can affect the misfit dislocation networ
 k\, as demonstrated using experimentally obtained γ/γ’ interface morphol
 ogies. The local interface orientation not only alters the misfit disloc
 ation core structure but can also facilitate the formation of ⟨100⟩ disl
 ocations at the interface. Furthermore\, the spatial arrangement and siz
 e-distribution of spherical γ’ precipitates\, e.g.\, in disk-alloys\, ca
 n lead to synergistic effects that are not present in the typical models
  of precipitate strengthening based on the interaction of straight dislo
 cations with a regular array of uniform precipitates. Certain Ni-base su
 peralloys furthermore form γ precipitates inside the cuboidal γ’ phase. 
 Our simulations suggest that the misfit stresses caused by the γ precipi
 tates reduce the yield stress of γ’ cubes subjected to nanomechanical co
 mpression tests. The situation is\, however\, different when the deforma
 tion is not controlled by the nucleation of dislocations\, e.g.\, when t
 he γ’ cubes are embedded in a dislocation-containing γ matrix. In this c
 ase\, the γ precipitates lead to an additional hardening that is also ob
 served experimentally.
LOCATION:A2.05B
CATEGORIES:WCPM
LAST-MODIFIED:20241125T084132Z
ORGANIZER;CN=Sarah Jarratt:
END:VEVENT
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