(PDF) Rapid solidification of non-stoichiometric intermetallic compounds: Modeling and experimental verification

(pdf) rapid solidification of non-stoichiometric intermetallic compounds: modeling and experimental verification

for undercooled Co-53at.%Si and Co-55at.%Si alloys, solute

drag was concluded to be signicant upon rapid solidica-

tion of non-stoichiometric intermetallic compounds. Solute

drag is signicant over the entire range of undercooling

except for the late stage of the second sluggish stagewhere

complete solute trapping happens and the early stage of the

second abrupt growth stage where invert partitioning

occurs.

Acknowledgements

The authors would like to thank theNatural Science Foundation

of China (Nos. 51371149 and 51671075), the Huo Yingdong Young

Teacher Fund (No. 151048), theAeronauticalScienceFoundation of

China (No. 2021ZF53066), and the Free Research Fund of State Key

Lab. of Solidication Processing (No. 92-QZ-2021).

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(pdf) time-resolved in situ measurements during rapid alloy solidification: experimental insight for additive manufacturing

consequence of heat extraction due to variations in

the local curvature of the solid–liquid interface. In

both alloys, after an initial incubation time of

several microseconds, a columnar microstructure

developed during acceleration of the solid–liquid

interface. In the Al–Si alloy, columnar growth of

supersaturated primary a-Al phase persisted to the

end of the rapid solidification process. In the Al–Cu

alloy, columnar growth of a non-equilibrium eutec-

tic solidification product proceeded to the point of

absolute stability at the solid–liquid interface,

where a banded morphology common to many

rapidly solidified alloys developed. In situ imaging

provided the first direct observations of the evolu-

tion of this banded microstructure at this instability

point.

These types of in situ measurements have broad

implications for additive manufacturing through

integration with predictive modeling capabilities.

The results can both inform and validate models

with the goal of understanding processing–mi-

crostructure–properties/performance relationships

in additive manufacturing and non-equilibrium

materials processing.

ACKNOWLEDGEMENTS

This work was performed under the auspices of

the U.S. Department of Energy, by Lawrence

Livermore National Laboratory (LLNL) under

Contract No. DE-AC52-07NA27344. Activities and

personnel at LLNL were supported by the U.S.

Department of Energy, Office of Science, Office of

Basic Energy Sciences, Division of Materials Sci-

ence and Engineering under FWP SCW0974.

Activities and personnel at the University of Pitts-

burgh received support from the National Science

Foundation, Division of Materials Research, Metals

& Metallic Nanostructures program through Grant

No. DMR 1105757. Work at Los Alamos National

Laboratory (LANL) was performed under the aus-

pices of the U.S. Department of Energy by Los

Alamos National Security, LLC, under Contract No.

DE-AC52-06NA25396. Activities and personnel at

LANL were supported by AJC’s Early Career Award

from the U.S. Department of Energy, Office of Sci-

ence, Office of Basic Energy Sciences, Division of

Materials Science and Engineering. DTEM sample

preparation at LANL was performed at the Center

for Integrated Nanotechnologies, an Office of Sci-

ence User Facility operated for the U.S. Department

of Energy, Office of Science.

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998

Rapid solidification processing | request pdf

This book has developed the subject of solidification kinetics and interfacial processes at crystal-melt interfaces by considering near-equilibrium phenomena occurring over a few layers of atoms, some temporally associated with the crystal, and some temporally associated with the melt. This thin microscopic zone of transition was usually approximated mathematically as a ‘sharp’ interface of zero thickness. Also, the rate-limiting kinetic processes that were considered thus far acted both separately and simultaneously, and consisted of heat conduction and solute diffusion. Both of these transport mechanisms normally develop fields over macroscopic distances, as compared to the near-atomic interface thickness. Moreover, the dynamic interchanges among the host and solute atoms at sharp interfaces were considered to occur rapidly enough, and to repeat frequently enough, to approximate closely the condition of local interfacial thermodynamic equilibrium. Global, i.e. total, thermodynamic equilibrium, was shown to be inoperative, as it is precluded for virtually all crystal-melt processes on the basis that the relevant length scales over which heat transfer and solute diffusion operate on practical time scales for the motion of the interface are much too small to allow total equilibrium to be achieved.

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