Rejuvenation is the configurational excitation of amorphous materials and is one of the more promising approaches for improving the deformability of amorphous metals that usually exhibit macroscopic brittle fracture modes. Here, we propose a method to control the level of rejuvenation through systematic thermal processing and clarify the crucial feasibility conditions by means of molecular dynamics simulations of annealing and quenching. We also experimentally demonstrate rejuvenation level control in Zr55Al10Ni5Cu30 bulk metallic glass. Our local heat-treatment recipe (rising temperature above 1.1Tg, followed by a temperature quench rate exceeding the previous) opens avenue to modifying the glass properties after it has been cast and processed into near component shape, where a higher local cooling rate may be afforded by for example transient laser heating, adding spatial control and great flexibility to the processing.
Amorphous metals1,2,3 have excellent properties such as high corrosion resistance4, high strength5 and large elastic elongation6. At room temperature, however, plastic deformation localizes into narrow band region and sudden fracture occurs exhibiting almost no macroscopic plastic deformation under uniaxial tensile and compressive loadings7,8,9. This brittle nature is the most serious flaw of amorphous metals for use as structural materials. Therefore, improvement and moreover tuning of the deformability has been the largest challenge of the decades in the field of amorphous metals10,11,12,13. Rejuvenation14,15,16,17 is the structural excitation of amorphous solids accompanied by an increase in the enthalpy and free volume and is thus the inverse of aging. Since rejuvenation has to change the elastic and plastic deformation behavior17 of amorphous metals, it is a new but promising approach for tuning the deformability of amorphous metals. It has recently been reported that shot-peening16 and sever plastic deformation17 can mechanically induce the rejuvenation. On the other hand, structural excitation driven by a thermal loading process18,19 also has potential application for practical usage, because the thermal loading process realizes a local rejuvenation control, which is more difficult by mechanical processing. However, the feasibility rejuvenation driven by thermal annealing and quenching is still controversial because of few experimental evidence18 and a lack of clear knowledge of the nonequilibrium glass properties.
In this work, we theoretically propose a recipe to control the level of rejuvenation through systematic thermal processing and clarify the crucial feasibility conditions by means of molecular dynamics (MD) simulations and figure out a rejuvenation map with respect to annealing temperature and quenching rate. Our rejuvenation map provides temperature-cooling rate conditions to achieve desired level of rejuvenation while avoiding crystallization and/or gross shape change. Based on the rejuvenation map we also experimentally demonstrate the realization of rejuvenation level control in Zr55Al10Ni5Cu30 bulk metallic glass, which evidences our rejuvenation map and recipe do work well even for typical experimental cooling rates. Moreover, the internal structural features and mechanical properties of rejuvenated amorphous metals are revealed.
For all of the MD simulations described here, we use the Lennard-Jones (L-J) potentials20 developed for the Cu-Zr amorphous alloy and a 30,000-atom simulation box with three-dimensional (3D) periodic boundary conditions. We consider alloys with atomic compositions of Cu50Zr50, Cu30Zr70 and Cu57Zr43 to ensure composition-independent generality (see Supplementary Information in regard to the latter two). The MD time step was set to 1 fs and we employed the NPT ensemble for which the temperature and pressure are controlled by the Nose-Hoover21 and Parrinello-Rahman methods22, respectively. An amorphous model was constructed via a melt-quenching process as follows (Fig. 1). We first arranged the atoms randomly in the simulation box and melted the structure by keeping the model at a high temperature of 3000 K for 20 ps (Fig. 1; process AB). The melted model was then quenched at a constant cooling rate of ( K/s) from 3000 K to 0 K (process BD). This quenched product is referred to as the “as-quenched model” hereafter and we use a tilde to represent the initial quenching process. By monitorinng the specific volume change during the rapid quenching process with a cooling rate of , the glass transition temperature was determined to be approximately 900 K from the kink in volume-temperature curve. Since generally depends on the cooling rate23, we also determined a set of temperatures for five different cooling rates (): K/s, K/s, K/s, K/s and K/s (see Supplementary Information, Fig. S1).
We conducted successive thermal loading simulations of the as-quenched model as follows. First, the as-quenched model was reheated at a heating rate of K/s up to a temperature (process DE) and then annealed for a time period (=2000 ps) under constant and zero external pressure conditions (process EF). Isothermal annealing processes with =500 and 1000 ps were also conducted and revealed that the annealing time had a small effect on our simulation results (see Supplemental Information, Fig. S2). We assumed various values ranging from to to examine the effect of the annealing temperature on the level of thermal rejuvenation. After isothermal annealing at for , the model was quenched again at five different cooling rates, () (), from to 0 K (process FG). This final product is referred to as the “annealed model” hereafter.
Results and Discussion
Figure 2(a) shows the generated excess potential energy due to the thermal loading process from state D to G for different and values. If any aging occurs during the thermal loading process, then the excess potential energy value should fall below zero. On the other hand, if thermal rejuvenation occurs, then the excess potential energy value should remain positive. Thus, the excess potential energy can represent the level of rejuvenation or aging depending on the sign. As we see in Fig. 2(a), significant aging is observed whenever the cooling rate is less than , regardless of the annealing temperature , whereas thermal rejuvenation is observed in the opposite case. Thus, a higher cooling rate after isothermal annealing than that of the initial quenching process is a necessary condition for thermal rejuvenation, but this alone is insufficient. Thermal rejuvenation is only realized when the annealing temperature is above a certain critical temperature . Thus, the two conditions, and , are crucial conditions for feasible thermal rejuvenation. We also found that a higher and a higher result in a higher level of rejuvenation under these conditions. Figure 2(a) can then be used as a rejuvenation map to identify conditions for controlling the rejuvenation level. It should be noted that is not an intrinsic material property but depends on both and as follows: 1) Since a higher leads to a thermodynamically unstable as-quenched state, further aging proceeds easily during later thermal loading and the value is shifted to a higher temperature. 2) Since a higher does not allow a more thermodynamically stable state to be found during the final quenching process, limited aging proceeds and the value is shifted to a lower temperature (Fig. 2(a)).
The levels of aging and rejuvenation are relative quantities and depend on the choice of reference amorphous state. Thus, if we choose a perfectly rejuvenated amorphous state as the reference amorphous state, which is supposedly constructed through melt quenching at an infinitely fast cooling rate, then further rejuvenation will not occur. In reality, however, it is impossible to realize such a perfectly rejuvenated state; even though a near-perfectly rejuvenated state can be realized, we would not be able to observe it because of the extremely short lifetime of the highly excited state. For this reason, the discussions above are valid for actual glass systems in general, in which both aging and rejuvenation can be realized.
It is worth noting that evaluating the level of aging and rejuvenation based on the volume change (i.e., mass density change) yields qualitatively similar results to those in Fig. 2(a) (see Supplementary Information, Fig. S3).
Based on the above findings, we demonstrate thermal rejuvenation experimentally in a Zr55Al10Ni5Cu30 bulk glassy alloy ( K at a heating rate of 0.33 K/s). The as-quenched Zr55Al10Ni5Cu30 alloy rod was sliced into 0.5-mm-thick disc samples that were initially annealed at 685 K for 120 s at heating and cooling rates of 0.17 K/s, denoted as R∗Exp. The fully relaxed samples were then annealed again at 735 K () for 120 s at a heating rate of 0.33 K/s and then quenched at cooling rates of = 0.33, 0.83, 1.7, 3.2, or 4.4 K/s (Ref. 24). The excess enthalpy generated during the second annealing process is calculated as , where RT is the room temperature. and are the specific heats of the sample reheated to 723 K and the as-secondary annealed state, respectively. The specific heat measurement was conducted with a heating and cooling rates of 0.33 K/s using DSC. Figure 2(b) shows the change in the potential energy calculated by the MD simulation compared to the change in the enthalpy obtained from the experiment. The cooling rates after annealing employed in the MD simulation and experiment are normalized by the typical cooling rates, ( K/s) and R∗Exp. (=0.17 K/s), respectively. Note that due to the different alloy chemistries, the MD and the experimental curves in Fig. 2(b) are not directly comparable; yet the basic trend and the order of magnitude roughly match. The enthalpy obtained from the experiment increases with increasing cooling rate after annealing and the positive enthalpy of the plots for = 0.83, 1.7, 3.2 and 4.4 K/s indicate that thermal rejuvenation was achieved. This is clear evidence of the feasibility of thermal rejuvenation via thermal loading, provided the necessary conditions are satisfied. The rough matching between MD and experimental curves in Fig. 2(b) implies that the level of rejuvenation is dominated by a cooling rate ratio between initial melt-quenching and final quenching, rather than the absolute magnitude of the cooling rate.
Figure 3 shows a schematic of the energy/volume change during the initial melt-quenching (AD) and subsequent thermal loading processes (DG). (1) If the annealing temperature is much higher than (), then an amorphous metal may quickly “relax” to an equilibrium liquid state within the heating stage (green curve in Fig. 3, top and bottom left) before the annealing process starts. As the equilibrium liquid is cooled (FG), sooner or later the liquid deviates from the equilibrium liquid state and eventually the structure is frozen into a glass. A cooling rate higher than induces an earlier deviation from the equilibrium liquid and leads to a rejuvenated glass with a higher energy/volume (red curve in Fig. 3, top left), while a cooling rate lower than leads to an aged glass (blue curve in Fig. 3, bottom left). (2) If is slightly above , then the annealing time becomes a key factor in addition to the cooling rate because the relaxation time to the equilibrium liquid is considerable compared with the heating and annealing times. Thus, during isothermal annealing the energy/volume increases to approach that of the equilibrium liquid. We actually observed the energy increase during the isothermal annealing process under conditions (see Supplementary Information, Fig. S4). As shown in Fig. 3 (top right), a longer annealing time leads to a larger energy/volume increase during isothermal annealing and eventually to a rejuvenated glass after cooling (solid red curve), while a shorter annealing time may lead to an aged glass (dotted red curve). Therefore, there is a critical minimum annealing time for rejuvenation ; rejuvenation is realized only if . (3) If is below (), then the annealing-cooling process always leads to aged glass as shown in Fig. 3 (bottom right). In Fig. 3 (top and bottom left), the fictive temperature (Ref. 25) is also indicated, at which the extrapolated glass line intersects the equilibrium liquid line. In a similar manner to , glass produced at a higher cooling rate from a high temperature liquid has a higher fictive temperature and vice versa26.
Change in the topological order by rejuvenation
We investigated the change in the topological order induced by the thermal loading process. The internal structures of amorphous metals, such as the short-range order (SRO) and medium-range order (MRO) have been attracted much attention, because they are correlated with the intrinsic properties of amorphous metals. Figure 4(a) shows the change in the fraction of icosahedral SRO, which has an energetically stable, high packing structure and is known to be a core amorphous metal structure. The figure shows clearly that aging increases and rejuvenation decreases icosahedral SRO.
Figure 4(b) shows the topological MRO composed of icosahedra. To characterize the MRO network structure, we employ the MRO clustering coefficient parameter , which was employed in our previous work27. For the center atom of the icosahedron , the clustering coefficient parameter can be defined as, , where is the icosahedral bond number and is the number of triangular geometries. As is the average clustering coefficient parameter over all icosahedra in an amorphous model, a large value implies a highly developed MRO network structure. As shown in Fig. 4(b), increases during the thermal loading process (DG) when the annealing temperature is below or the cooling rate is below . In contrast, although some fluctuation is observed, decreases when is above and the cooling rate is above .
Together with Fig. 2(a) and Fig. 4, we conclude that aging increases and rejuvenation decreases the topological SRO and MRO, which are typical characteristics of glass structures. The clear correspondence between the potential energy profile in Fig. 2(a) (and the volume profile in Supplementary Information, Fig. S3) and the SRO and MRO in Fig. 4 indicates that aging and rejuvenation change the macroscopic structural properties of amorphous metals, such as the free volume, by changing the internal topological order.
Change in the mechanical properties by rejuvenation
To demonstrate the possibility of controlling the mechanical properties via aging and rejuvenation, the change in elastic stiffness due to thermal loading (process DG) was investigated. The elastic stiffness coefficients of the as-quenched model with a cooling rate (state D in Fig. 1), and , were calculated from the second spatial derivative of the total potential energy ; these and values are taken as the reference. The elastic stiffness coefficients of the models annealed at and with a final cooling rate (state G) were also calculated and the change in the elastic stiffness coefficients due to thermal loading (process DG), and , are shown Fig. 5(a). Both and increase in the case of aging, while they decrease in the case of rejuvenation. Moreover, both values saturate in the high region and take values of and , respectively, which are the elastic stiffness coefficients of the as-quenched model with a cooling rate of (). The clear correspondence between the potential energy profile () in Fig. 2 and the elastic stiffness coefficient profile in Fig. 5(a) shows the possibility of controlling the elastic properties of amorphous metals via thermally induced rejuvenation and aging. The correlation between SRO in Fig. 4(a) and elastic stiffness in Fig. 5(a) in this study agrees with that found in our previous studies27,28, where the elastic constant increases with increasing icosahedral SRO.
Plastic deformation behavior of the “aged model” and “rejuvenated model” was also investigated by simple shear MD deformation tests, in which the models were applied incremental affine shear strain at 0 K. At each strain step, the atomic structure and simulation box were relaxed using the conjugate gradient method. Figure 5(b) shows the shear stress change during the shear deformation tests for four models; two as-quenched models (state D) with different cooling rates, and () and two annealed models (state G) with different annealing temperatures, (aged model) and (rejuvenated model) with the same cooling rate of after annealing, (). All the model shows a maximum shear stress at around engineering shear strain and the peak shear stress increases by the thermal loading process DG with the annealing at and decreases with the annealing at . The two figures of atomic structure in Fig. 5(b) represent snapshots of the annealed models at engineering shear strain, in which atoms are colored by Mises strain29. The aged model shows an inhomogeneous deformation, in which Mises strain is localized into band region parallel to shear direction, while the rejuvenated model shows more homogeneous deformation. The clear difference in deformation mode between the aged and rejuvenated models demonstrates that the aging and rejuvenation can change the plastic behavior of amorphous metals. It is well known that deformation at uniaxial strain of well-aged amorphous metals at room temperature is severely localized into narrow band region, so called shear banding and the shear banding severely limits the macroscopic deformability of amorphous metals because of the local melting30,31,32,33. The homogeneous deformation in the rejuvenated model suggests that the rejuvenation conduces better macroscopic deformability to amorphous metals. Tensile ductility of amorphous metal induced by mechanical rejuvenation has been reported in a recent experimental study34.
We also experimentally observed the change in the mechanical properties via rejuvenation through a micro Vickers hardness test (see Supplementary Information, Fig. S5).
Recently, the critical fictive temperature concept for plasticity in amorphous metals has been proposed13. The critical fictive temperature is a characteristic of amorphous metals: an amorphous metal is ductile in the case of and brittle in the case of . Since rejuvenation increases as schematically shown in Fig. 3, it would improve the ductility of amorphous metals through the prevention of catastrophic shear localization behavior such as shear banding. We actually demonstrated that rejuvenation enhances more homogenous deformation in Fig. 5(b), which supports a fictive-temperature-based discussion of ductility in amorphous metals.
In summary, we have conducted thermal loading MD simulations of an already-formed amorphous metals subjected to heating, isothermal annealing and second quenching and have produced a rejuvenation map with respect to the annealing temperature and second quenching rate that allows conditions to be found to control the level of rejuvenation. We found that thermal rejuvenation occurs via a thermal processing of isothermal annealing at temperatures above and subsequent quenching at a cooling rate that is higher than that of the initial quenching process. The level of rejuvenation increases with increasing annealing temperature and quenching rate. We also experimentally demonstrated control of the level of thermal rejuvenation in Zr55Al10Ni5Cu30 bulk glassy alloy. The above results are qualitatively consistent with analytical models of fictive temperature evolution in quenching and heating glass DSC analysis26, but now adding a constructive notion of applying the heating-quenching process multiple times to engineer glass properties, with quantitative proofs that the scheme actually works.
The fact that rejuvenation is realized via annealing even slightly above and subsequent quenching is important for modifying the glass properties after the material has been cast and processed into near component shape because amorphous metals are easy to handle at temperatures slightly above because of their high resistance to shape changes and/or crystallization.
One would have the flexibility of applying the thermal rejuvenation very locally, using for example transient laser heating; if the laser-heated spot is very small, the local cooling rate afterwards could be much higher than with the entire glassy block cooling down from melt. In practical thermal loading, the achieved level of rejuvenation will vary across the sample because heterogeneous heat transfer and heat conduction over time and space are expected. If we need to demonstrate the details of the heterogeneity in an actual heat treatment process, then we could employ a coarse-grained heat transfer and temperature distribution analysis such as FEM in combination with our rejuvenation map. This analysis framework could be a useful engineering tool for predicting heterogeneous rejuvenation and engineering the desired rejuvenation distribution while avoiding crystallization and/or gross shape changes with certain boundary conditions. Recently, nanoimprinting of metallic glass35 has been developed using a thermoplastic forming process slightly above , which allows the realization of low-cost fabrication of micro- and nanodevices. Our study proposes that a thermoplastic forming process consisting of annealing slightly above and then rapid cooling before the glass relaxes into equilibrium liquid would avoid embrittlement by aging in the thermoplastic forming process.
How to cite this article: Wakeda, M. et al. Controlled Rejuvenation of Amorphous Metals with Thermal Processing. Sci. Rep. 5, 10545; doi: 10.1038/srep10545 (2015).
Greer, A. L. Metallic Glasses. Science 267, 1947–1953 (1995).
Inoue, A. Stabilization of metallic supercooled liquid and bulk amorphous alloys. Acta Mater. 48, 279–306 (2000).
Schuh, C. A., Hufnagel, T. C. & Ramamurty, U. Mechanical behavior of amorphous alloys. Acta Mater. 55, 4067–4109 (2007).
Asami, K., Kawashima, A. & Hashimoto, K. Chemical Properties and Applications of Some Amorphous Alloys. Mater. Sci. Eng. 99, 475–481 (1988).
Masumoto, T. & Maddin, R. The mechanical properties of palladium 20 a/o silicon alloy quenched from the liquid state. Acta Metall. 19, 725–741 (1971).
Ashby, M. F. & Greer, A. L. Metallic glasses as structural materials. Scr. Mater. 54, 321–326 (2006).
Lewandowski, J. J. & Lowhaphandu, P. Effects of hydrostatic pressure on the flow and fracture of a bulk amorphous metal. Phil. Mag. A 82, 3427–3441 (2002).
Zhang, Z. F., Eckert, J. & Schultz, L. Fatigue and Fracture Behavior of Bulk Metallic Glass. Metall. Mater. Trans. A 35, 3489–3498 (2004).
Conner, R. D., Yim, H. C. & Johnson, W. L. Mechanical properties of Zr57Nb5Al10Cu15.4Ni12.6 metallic glass matrix particulate composites. J. Mater. Res. 14, 3292–3297 (1999).
Sarac, B. & Schroers, J. Designing tensile ductility in metallic glasses. Nat. Comm. 4, 2158 (2013).
Das, J. et al. “Work-Hardenable” Ductile Bulk Metallic Glass. Phys. Rev. Lett. 94, 205501 (2005).
Zheng, N. et al. Design of ductile bulk metallic glasses by adding “soft” atoms. Appl. Phys. Lett. 100, 141901 (2012).
Kumar, G., Neibecker, P., Liu, Y. H. & Schroers, J. Critical fictive temperature for plasticity in metallic glasses. Nat. Comm. 4, 1536 (2013).
Hodge, I. M. Physical Aging in Polymer Glasses. Science 267, 1945–1947 (1995).
Utz, M., Debenedetti, P. G. & Stillinger, F. H. Atomistic Simulation of Aging and Rejuvenation in Glasses. Phys. Rev. Lett. 84, 1471–1474 (2000).
Concustell, A. et al. Structural relaxation and rejuvenation in a metallic glass induced by shot-peening. Phil. Mag. Lett. 89, 831–840 (2009).
Meng, F., Tsuchiya, K. S. II. & Yokoyama, Y. Reversible transition of deformation mode by structural rejuvenation and relaxation in bulk metallic glass. Appl. Phys. Lett. 101, 121914 (2012).
Kumar, G., Rector, D., Conner, R. D. & Schroers, J. Embrittlement of Zr-based bulk metallic glasses. Acta Mater. 57, 3572–3583 (2009).
Kumar, G., Prades-Rodel, S., Blatter, A. & Schroers J. Unusual brittle behavior of Pd-based bulk metallic glass. Scr. Mater. 65, 585–587 (2011).
Kobayashi, S., Maeda, K. & Takeuchi, S. Computer Simulation of Deformation of Amorphous Cu57Zr43 . Acta Metall. 28, 1641–1652 (1980).
Nòse, S. A unified formulation of the constant temperature molecular dynamics methods. J. Chem. Phys. 81, 511–519 (1984).
Parrinello, M. & Rahman, A. Polymorphic transitions in single crystals: A new molecular dynamics method. J. Appl. Phys. 52, 7182–7190 (1981).
Moynihan, C. T., Easteal, A. J., Wilder, J. & Tucker, J. Dependence of the glass transition temperature on heating and cooling rate. J. Phys. Chem. 78, 2673–2677 (1974).
Saida, J., Yamada, R. & Wakeda, M. Recovery of less relaxed state in Zr-Al-Ni-Cu bulk metallic glass annealed above glass transition temperature. Appl. Phys. Lett. 103, 221910 (2013).
Tool, A. Q., Relation between inelastic deformability and thermal expansion of glass in its annealing range. J. Am. Ceram. Soc. 29, 240–253 (1946).
Moynihan, C. T., Easteal, A. J. & Debolt, M. A., Tucker J. Dependence of the Fictive Temperature of Glass on Cooling Rate. J. Am. Ceram. Soc. 59, 12–16 (1976).
Wakeda, M. & Shibutani, Y. Icosahedral clustering with medium-range order and local elastic properties of amorphous metals. Acta Mater. 58, 3963–3969 (2010).
Wakeda, M., Shibutani, Y., Ogata, S. & Park J. Relationship between local geometrical factors and mechanical properties for Cu-Zr amorphous alloys. Intermetallics 15, 139–144 (2007).
Li, J. AtomEye: an efficient atomistic configuration viewer. Modelling Simul. Mater. Sci. Eng. 11, 173–177 (2003).
Wada, T., Inoue, A. & Greer, A. L. Enhancement of room-temperature plasticity in a bulk metallic glass by finely dispersed porosity. Appl. Phys. Lett. 86, 251907 (2005).
Sergueeva, A. V. et al. Shear band formation and ductility of metallic glasses. Mater. Sci. Eng. A 383, 219–223 (2004).
Shimizu, F., Ogata, S. & Li, J. Yield point of metallic glass. Acta Mater. 54, 4293–4298 (2006).
Shimizu, F., Ogata, S. & Li, J. Theory of Shear Banding in Metallic Glasses and Molecular Dynamics Calculations. Mater. Trans. 48, 2923–2927 (2007).
Wang, Q. et al. Superior Tensile Ductility in Bulk Metallic Glass with Gradient Amorphous Structure. Sci. Rep. 4, 4757 (2014).
Kumar, G., Tang, H. X. & Schroers, J. Nanomoulding with amorphous metals. Nature 457, 868–872 (2009).
This work was supported by Grants-in-Aid for Challenging Exploratory Research (Nos. 23656418 and 25630013), Scientific Research (A) (No. 23246025) and the Elements Strategy Initiative for Structural Materials (ESISM). J.L. acknowledges support by NSF DMR-1240933 and DMR-1120901.
The authors declare no competing financial interests.
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Wakeda, M., Saida, J., Li, J. et al. Controlled Rejuvenation of Amorphous Metals with Thermal Processing. Sci Rep 5, 10545 (2015). https://doi.org/10.1038/srep10545
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