Numerical description for the recalescence of bulk-undercooled Cu70Ni30 alloy

Non-equilibrium transformation path for bulk undercooled hypereutectic Fe–B alloy

“…This criterion is compatible with Hindmarsh et al's conclusion that T R should depend on the solute concentration in the remaining liquid [22]. On this basis, a mathematically simple and physically realistic numerical procedure was proposed to describe the recalescence behavior for Cu-Ni solid solution alloy [19], where an extended dendrite growth model and solute trapping model were adopted [23,24].…”

“…Meanwhile, great progresses have also been made in the related theoretical investigations, such as homogeneous or heterogeneous nucleation theory [6][7][8], dendrite growth model [9][10][11][12][13] and metastable phase formation mechanism [14][15][16], in order to understand the physical essence underlying such rapid transformation process. Generally, solidification of undercooled melts consists of two distinctive regimes [17][18][19], i.e., rapid solidification accompanying recalescence, which can be experimentally observed as the abrupt rising of liquid temperature, and the subsequent near-equilibrium solidification controlled solely by external heat extraction to the environment. Up to now, it has been accepted from a thermodynamic view that the occurrence of non-equilibrium solidification is caused by the liquid/solid (L/S) Gibbs energy difference [2,8].…”

“…Regarding this point, the aim of the present paper is to extend the previous numerical method to the bulk undercooled Fe-B hypereutectic alloy, where the intermetallic phase Fe 2 B with defined stoichiometry forms primarily during recalescence [25,26]. In such a case, the solid concentration can be determined directly, without resorting to the dendrite growth model and solute trapping model [23,24] as applied for the previous solid solution alloy [19]. By doing this, it can be expected to largely reduce the computation complexity.…”

Determination of Solid Fraction from Cooling Curve

“…[1] and [2] are generally used to describe the event such as the baseline for cooling curve upon solidification.…”

“…UPON rapid solidification of undercooled melts, such as by melt fluxing or electromagnetic levitation, [1] the transformed fraction can be directly measured using differential thermal analysis, differential scanning calorimetry, synchrotron diffraction, or dilatometry experiments. [2] For solidification with negligible undercooling, all the preceding techniques can be used, whereas, for rapid solidification, delicately and repeatedly treating the sample is essential for achieving a high undercooling; in this case, most of the above techniques are limited due to the expensive facilities and the high sensitivity for measuring heat release.…”