Abstract
Non-dendritic microstructures are generally obtained in metals after semi-solid deformation (deformation during solidification); however, dendritic growth is preferred without deformation. The fragmentation of dendrites is recognized as an essential contributing factor to non-dendritic microstructures. However, the underlying mechanism of fragmentation needs to be clarified in depth. It is infamously hard for researchers to carry out a direct observation of this process. Moreover, a comprehensive numerical survey of this process is not trivial. The present research reported a new method to model dendritic growth during semi-solid deformation. The motion and deformation of the solid coupled with liquid flow in the melt were treated as the two-phase flow because plastic materials could be formulated as non-Newtonian fluids. The vector-valued phase-field formulation and the self-constructed Navier–Stokes solver made it possible to simulate the growth, motion, deformation, fragmentation and agglomeration of two dendrites coupled with liquid flow in the melt. Computational results suggest that fragmentation can occur when the grain boundary is wet and penetrated by the melt, giving new supporting evidence to a previously proposed mechanism for the fragmentation of dendrites.
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Acknowledgements
This work was supported by the National Key Research and Development Program [Grant No. 2016YFB0300401, 2018YFA0702900], the National Natural Science Foundation of China [Grant No. 51774265, 51701225], the National Science and Technology Major Project of China [Grant No. 2019ZX06004010, 2017-VII-0008-0101], the Strategic Priority Research Program of the Chinese Academy of Sciences [Grant No. XDC04000000], LingChuang Research Project of China National Nuclear Corporation, Program of CAS Interdisciplinary Innovation Team, Youth Innovation Promotion Association, CAS, the Special Scientific Projects of Inner Mongolia. The numerical calculations in this paper have been done on the supercomputing system in the Supercomputing Center of University of Science and Technology of China.
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Jian-kun Ren wrote original draft, Yun Chen helped in writing–review and editing, Yan-fei Cao and Bin Xu validated the study, Ming-yue Sun administrated the project, and Dian-zhong Li supervised the study.
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10853_2021_6026_MOESM3_ESM.gif
Supplementary file3 (GIF 1289 KB): two dendrites grew, moved, bent, broke, and agglomerated in Al-Cu alloy (the second row shows region with ϕ > 0).
Appendices
Appendix 1 Solution sensitivity with respect to step and mesh sizes
The solution sensitivity with respect to different step and mesh sizes was investigated in this section. Initially, a seed was placed at the center of the domain with a size of 1.4 × 1.4 mm2, which contained supersaturated Al-1 wt.% Cu alloy (Ω = 0.35). Solidification took place isothermally all the time, and ε4 was set as 0.05. The mesh size near the interface (ϕ = 0) was as 0.5 W0 (1.4 × 2–12 mm), and the step size was selected as 0.01 τ0. The result at t = 0.54 s is shown in Fig. 10(a1)–(a3).
Figure 10(b1) compares the contours of ϕ = 0 by only changing the step sizes (0.01 τ0, 0.005 τ0 and 0.0025 τ0). Little difference could be found unless with an extremely close look (Fig. 10b2). This indicates a step size as small as 0.01 τ0 guarantees a valid phase-field computation with this supersaturation.
Figure 10(a3) displays that the mesh size of 0.5 W0 ensures the phase field varies smoothly from solid to liquid. Figure 11 demonstrates the result with the mesh size a level coarser (1.4 × 2–11 mm = W0) near the interface (other conditions kept unchanged), and the phase field did not have a smooth transition across the interface any more (Fig. 11c).
Consequently, in the current study, the mesh near the interface kept a size of 0.5 W0. Considering the velocity computation (the step size Δt to solve Navier–Stokes equations should be limited by Δt ≤ h/|v| in every cell; h is the cell size [41]), the step size to solve phase-field equations should be adjusted dynamically (Sec. 2.4 in Ref. [41]) with an upper limit of 0.01 τ0 (this limit is based on the test of alloy. For the pure metal, the limit should be selected as 0.05 τ0, according to a similar test in Ref. [55]).
Appendix 2 Numerical procedures to solve Navier–Stokes equations
The techniques to solve v and p from Navier–Stokes equations [Eqs. (8)–(9)] have already been discussed in Ref. [41]. Unlike Ref. [41], in the present study, v and p were solved separately rather than as a whole to enable a simpler preconditioner [77].
Linear system and preconditioner (without scaling)
v and p are approximated by finite element method:
where v is discretized as a solution vector Zv with Nv degrees of freedom (Zjv is the jth element in Zv with the shape function ψjv), and a similar definition is applicable for p. Equations (8)–(9) are discretized into a linear system [readers can refer to Eqs. (A.1), (A.5) and (A.10) in Ref. [41] for the space and time discretization]:
with
where Δt is the step size. vold is the velocity field that has been solved at the last step. (·, ·)S and < ·, · > Γ2 denote the integrations over the computational domain S and “do-nothing” boundary Γ2 (pm on Γ2 is set as zero), respectively [Eqs. (A.2)-(A.3) in Ref. [41]]. If v has Dirichlet condition on the whole boundary, pressure is only defined up to a constant [41, 80, 94]. Here Mpp, Rp arise from the zero-pressure constraint at one point; therefore, MppZp = 0. Hence, Eq. (27) can be rewritten as
Equation (31) is equivalent to
Equations (32) and (33) lead to
Schur complement reads
S−1 can be approximated by (S*)−1 as [41]
where
Lwp should be assembled with the zero-pressure constraint at one point in the domain to ensure it is positive definite. Equation (34) is hard to solve in a straightforward way [77]; thus, it is preconditioned with Eq. (36):
After Yp is solved with the CG solver from Eq. (39), Zp can be recovered from Yp:
and then
Diagonal scaling
In the current study, the procedures described in “Linear system and preconditioner (without scaling)” of Appendix 2 cannot be directly applied. It is impractical to obtain the exact inverse of a matrix; thus, (Mvv)−1, (Lwp)−1 and (Qwp)−1 are represented by Cholesky decomposition. However, the variable viscosity in Eqs. (28) and (38) indicates that there are variations of orders of magnitude inside Mvv and Qwp. To guarantee effective decomposition, Mvv and Qwp are scaled with their diagonal elements, and the corresponding scaling vectors are defined as
respectively, with a diagonal matrix
The scaled linear system is
where
Subsequently, Eqs. (39)–(41) become
In Eq. (51),
where (MIvv)−1, (Lwp)−1 and (Qwp)I−1 are represented by Cholesky decomposition. Zv and Zp can be recovered by
Appendix 3 Principal symbols
Matrices, vectors, tensors are in boldface, while scalars are in lightface.
- ϕ:
-
Phase field
- α:
-
Orientation field
- α4:
-
4α
- c:
-
Solute concentration field
- a1, a2:
-
Constants in phase-field model (Table 2)
- as:
-
Anisotropy [Eq. (5)]
- T:
-
Temperature
- d0:
-
Capillary length (Table 1)
- W0:
-
Spatial scale
- τ0:
-
Time scale
- τϕ:
-
Phase-field relaxation time (Table 1)
- τα:
-
Orientation relaxation time
- UT:
-
Dimensionless temperature for pure metal (Table 1)
- Uc:
-
Dimensionless concentration for alloy [Eq. (3)]
- Y:
-
Thermal/solutal driving force (Table 1)
- λ:
-
Coupling constant
- ω:
-
Rotation rate
- F = (F1, F2):
-
Vector-valued phase field [Eq. (7)]
- W:
-
Diffuse interface thickness
- P:
-
Mobility function [Eq. (6)]
- v:
-
Velocity
- p:
-
Pressure
- σm:
-
Mean stress
- pm:
-
Mean pressure across the “do-nothing” boundary
- t:
-
Time
- c∞:
-
Initial concentration in the melt
- Tl–s:
-
Freezing range
- ρ:
-
Density
- I:
-
Unit diagonal tensor
- f:
-
External force acting on a unit mass [Eq. (8)]
- fs:
-
Local solid fraction: fs = (1 + ϕ)/2
- \(\dot{\boldsymbol\varepsilon }\):
-
Strain rate [Eq. (24)].
- \(\dot{\varepsilon }_{{{\text{eq}}}}\) , σeq:
- μ:
-
Dynamic viscosity
- μl, μs, μs–l:
-
Dynamic viscosity in the liquid, solid [Eq. (14)], and within the s-l interface [Eq. (16)]
- σy:
-
Yield strength
- σ:
-
Stress tensor
- s:
-
Deviatoric stress tensor
- μmax(s), μmax(s-l) :
-
Cutoff viscosity in the solid and within the s-l interface [Eq. (17)]
- ε4:
-
Anisotropic strength
- Ω:
-
Supersaturation
- θ:
-
Dimensionless undercooling for the alloy
- Tm:
-
Melting point
- D:
-
Diffusivity (Table 1)
- DT:
-
Thermal diffusivity
- Dcl:
-
Solute diffusivity in the liquid
- ν:
-
Kinematic viscosity
- k:
-
Solute partition coefficient
- m :
-
Liquidus slope
- μc, η, β, s:
-
Constants in the phase-field model, listed in Table 2
- Γ:
-
Gibbs-Thomson coefficient
- L:
-
Volumetric latent heat
- cp:
-
Volumetric specific heat
- σsl, σgb:
-
Interfacial tensions on the s-l interface and grain boundary
- ψjv, ψjp:
-
Shape functions for the jth degree of freedom in the finite element space of v and p [Eqs. (25)–(26)]
- Zv, Zp:
- Nv:
-
The number of degrees of freedom in the finite element space of v
- ZIv, ZIp:
- dv, dp:
- Λp:
-
Diagonal matrix constructed by dp [Eq. (44)]
- Mvv, Mvp, Mpv, Mpp:
- MIvv, MIvp, MIpv, MIpp:
- Rv, Rp:
-
Right hand sides in linear system Eq. (27)
- RIv, RIp :
- S:
-
Schur complement [Eq. (35)]
- (S*)−1:
-
Approximation to S-1 [Eq. (36)]
- Lwp, Qwp:
- (Qwp)I:
-
Scaled Qwp [Eq. (56)]
- Yp:
-
Solution vector in linear system Eq. (39)
- YIp:
-
Solution vector in scaled linear system Eq. (51)
- SI:
-
Scaled Schur complement [Eq. (54)]
- (SI*)-1:
-
Approximation to (SI)-1 [Eq. (55)]
- Δt:
-
Step size for solving the Navier–Stokes equations
- S:
-
Computational domain
- Γ2:
-
“Do-nothing” boundary
- N:
-
Outward unit normal to the boundary
- (·, ·)S, <·, ·>Γ2:
-
Integration over the domain and “do-nothing” boundary
- D(·):
-
Operator defined by Eq. (11)
- ::
-
Double dot product between two second-order tensors [Eq. (13)]
- (x1, x2), (X1, X2):
-
Axes of the local and global frame (Fig. 1 in Ref. [55])
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Ren, Jk., Chen, Y., Cao, Yf. et al. A phase-field study of the solidification process coupled with deformation. J Mater Sci 56, 12455–12474 (2021). https://doi.org/10.1007/s10853-021-06026-6
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DOI: https://doi.org/10.1007/s10853-021-06026-6