Observations on the interaction of dislocations with a migrating interphase boundary

Baró, G.B.; Perepezko, John H.

doi:10.1016/0025-5416(77)90177-x

Cited by 12 publications

(7 citation statements)

References 17 publications

Supporting

Mentioning

Contrasting

Order By: Relevance

“…The authors accordthe Ag-Al system was observed by Baro et al [3] and Baro ingly decided to assemble an overview of both experimental and Perepezko. [4] The dislocation emission occurred when observations on this internal structure and explanations the undercooling below the congruent transformation temadvanced for its formation, and to offer their own contribuperature was greater than ϳ50 K. This emission appeared tions to these explanations. Concepts evolved from studies of to occur by the "peeling off" of a portion of the growth internal structure produced during grain boundary migration ledge into the ␤ matrix, where it became a lattice dislocation.…”

Section: Introduction II Experimental Observations On Internal Stmentioning

confidence: 91%

“…We envisage that slip dislocations observed in the matrix Brown et al [14] found that proeutectoid ferrite precipitatahead of the parent:MT interfaces in Cu-Ga [2] and Ag-Al ing on austenite twin boundaries in Fe-C-Mo is "clean," i.e., alloys [3,4] may arise at least in part due to one or more of it is relatively dislocation-free. On the other hand, ferrite the foregoing sources.…”

Section: Introduction II Experimental Observations On Internal Stmentioning

confidence: 98%

“…and both experimental observations and explanations develGrowth ledges have been repeatedly observed in this oped during counterpart studies on proeutectoid ferrite fortransformation. [3,5] mation in steel, wherein the interstitial solute diffuses but Baro and Perepezko [4] found that at undercoolings in the substitutional solutes do not, will also be utilized. As a byrange of 10 to 100 K, some dislocations at the ␤: m boundproduct of this effort, a suggestion will be made that the aries were left behind in MT product phase as the boundaries defects left behind by the massive transformation interface moved forward, a result consistent with the optical microscan in at least one case provide important clues to the interfacopy observations of Kittl and Massalski [2] on the ␤ → m cial structure and the operative boundary migration process.…”

Section: Introduction II Experimental Observations On Internal Stmentioning

confidence: 99%

“…They also showed Cu-(19.5 to 20.5) pct Ga [6,28,29] ␤ → ␣ m bcc → fcc dislocations slightly split* Cu-(20.5 to 25.5) pct Ga [6,28,29] ␤ → m bcc → hcp profuse twinning, widely split dislocations Cu-37.6 Pct Zn [7] ␤ → ␣ m bcc → fcc large twins and microtwins, high densities of aligned dislocations Ag-24.5 Pct Al [3,4] ␤ → m bcc → hcp twins and well split dislocations Fe [8][9][10][11] ␥ → ␣ m fcc → bcc dislocations only MnAl(C) [26] → m hcp → L1 o twins, microtwins, split dislocations *The ␣ m / m duplex structure is not considered here.…”

Section: Introduction II Experimental Observations On Internal Stmentioning

confidence: 99%

“…Hence loops of varying frequency the larger the driving force for the massive transsizes appear, depending upon when an individual massive formation and the proeutectoid ferrite reaction in an crystal was nucleated as well as the structural details of its Fe-C-Mo alloy. [2,3,4,7,49] growth kinetics. These loops can interact and thereby A reviewer has brought to our attention papers by Yanar become no longer distinguishable.…”

Section: Introduction II Experimental Observations On Internal Stmentioning

confidence: 99%

See 4 more Smart Citations

Origins of internal structure in massive transformation products

Aaronson

Mahajan

Purdy

et al. 2002

Metall Mater Trans A

View full text Add to dashboard Cite

The internal structure in massive phases formed during six massive transformations has been reviewed. A counterpart review has also been made for the proeutectoid ferrite reaction, mainly in alloy steels in which bulk partition of alloying elements between austenite and ferrite has not occurred. Both dislocations and twins comprise this structure unless the stacking fault energy is too high to permit twin formation. Volume and shape changes associated with transformation can explain dislocation loops through stress-induced displacement and multiplication of misfit dislocations into the softer phase by means of either a dissociation reaction followed by Ashby-Johnson prismatic looping or emanation of glide loops from Frank-Reed sources. Following Gleiter et al., the "growth accidents" concept used to explain dislocation and twin formation during grain growth proves equally suitable for explaining formation of the same features during the massive and other diffusional transformations. Climb of interfaces produced by edge-to-edge rather than the usual plane-to-plane matching, introduced by Kelly and Zhang and experimentally supported by Nie and Muddle and by Howe et al. for the ␣ → ␥ m transformation in near-TiAl alloys, is proposed as another source of dislocations in the product phase.

show abstract

Section: Introduction II Experimental Observations On Internal Stmentioning

confidence: 91%

Section: Introduction II Experimental Observations On Internal Stmentioning

confidence: 98%

Section: Introduction II Experimental Observations On Internal Stmentioning

confidence: 99%

Section: Introduction II Experimental Observations On Internal Stmentioning

confidence: 99%

Section: Introduction II Experimental Observations On Internal Stmentioning

confidence: 99%

See 3 more Smart Citations

Origins of internal structure in massive transformation products

Aaronson

Mahajan

Purdy

et al. 2002

Metall Mater Trans A

View full text Add to dashboard Cite

show abstract

Spreading of extrinsic grain boundary dislocations in austenitic steel

Varin

1979

Phys. Stat. Sol. (a)

View full text Add to dashboard Cite

The dependence of the spreading process of extrinsic grain boundary dislocations (EGBD's) on grain boundary state and misorientation, and spreading kinetics in austenitic steel is investigated. Spreading of EGBD's at non‐equilibrium grain boundaries obtained by successive cold rolling and annealing treatments at a temperature much lower than 0.8Tm is found to occur at approximately 450 °C. EGBD's in specimens annealed at 0.8Tm however spread at about 550 to 600 °C. This observation seems therefore to indicate that at approximately 0.8Tm an irreversible change in grain boundary structure takes place. It is also found that EGBD's lying at special and incoherent twin boundaries spread at 700 °C compared with 550 to 600 °C for equilibrium, random boundaries in the same material. Observations of spreading kinetics indicate that the latter is not solely controlled by grain boundary diffusion.

show abstract

Growth kinetics and mechanism of the massive transformation

Perepezko

1984

Metall Trans A

View full text Add to dashboard Cite

Observations on the interaction of dislocations with a migrating interphase boundary

Cited by 12 publications

References 17 publications

Origins of internal structure in massive transformation products

Origins of internal structure in massive transformation products

Spreading of extrinsic grain boundary dislocations in austenitic steel

Growth kinetics and mechanism of the massive transformation

Contact Info

Product

Resources

About