Low-energy ion-assisted control of interfacial structures in metallic multilayers
Introduction
Metallic thin-film multilayers can possess high strength and hardness [1], [2], [3], [4], [5] and sometimes exhibit unusual electron transport properties such as giant magnetoresistance [6], [7], which is utilized for magnetic field sensing [8] and other spin-based devices [9]. Metal superlattice structures also have tunable high reflectivity that has led to their use in X-ray, soft X-ray, and extreme ultraviolet (EUV) telescopes for solar physics and astronomical research [10], [11], [12]. These applications utilize multilayers that are composed of many metal layers ranging from a few monolayers to several nanometers in thickness.
The roughness and degree of intermixing at the interfaces between the metal layers in multilayer films can greatly affect their properties [13], [14], [15]. While the role of interface structures upon the magnetotransport [6], [7], [13], [14], [15] and optical properties [10], [11] of thin films has been extensively studied, the mechanisms that control interfacial roughness and intermixing during multilayer growth have only recently begun to be addressed. Several experimental studies have sought to understand the kinetic and thermodynamic factors controlling the growth of thin films and multilayers by changing the growth temperature or using plasma-based methods to increase adatom mobility [10], [16], [17], [18]. The best metal superlattices are usually grown at relatively low homologous temperatures to avoid interdiffusion across interfaces. However, these conditions can result in the formation of rough interfaces and other defects [19].
Ion beams [17] and plasmas [10], [20] are widely used to induce inert gas ion impacts with growth surfaces. This results in local energy transfer to surface atoms and enhanced surface atom mobility and enables use of a low epitaxial growth temperature to avoid interlayer diffusion in the subsurface region [21], [22], [23]. However, conventional ion beam-assisted deposition processes utilize high-energy ion fluxes in the 50 eV to 5 keV range during metal deposition. While these have been successfully used to create flat surfaces on thick monolithic films [21], [22], these ion energies exceed the damage threshold energy for multilayers with nanoscopic layer thicknesses and result in significant interlayer mixing [24], [25].
Molecular dynamics (MD) simulations have been used to explore the atomic assembly mechanisms during the vapor deposition of metallic multilayers [26], [27], [28], [29]. The structures predicted by these accelerated deposition rate simulations are surprisingly similar to those observed by three-dimensional atomic probe techniques [30]. The predicted misfit dislocation structures are also similar to those observed by high-resolution transmission electron microscopy [31], [32]. Recent simulations of ion interactions with a model Co-on-Cu bilayer system indicate that low (5–10 eV) energy impacts can be highly effective at flattening small (10 atoms) cobalt clusters on (1 1 1) copper surfaces without inducing interfacial alloying [24], [33], [34]. They also reveal that appropriate combinations of ion species (mass), ion energy, ion fluence, and ion incident angle can be used to selectively activate either atom recoil, atomic exchange, or direct jumping mechanisms to flatten surface asperities [24], [33]. These studies further indicate that nearly perfect multilayer structures can be vapor deposited using ion assistance if the ion energy is maintained between the critical energies for flattening and intermixing. These energies and the energy gap depend on the ion incident angle and ion mass. The widest critical energy gap is achieved for an ion incident angle around 50° from surface normal (which avoids easy atom penetration in crystal channeling directions) using an ion mass comparable to that of the metals [33].
There are many ways, in which a low-energy ion assistance method could be used to control the assembly of a metal multilayer thin film. In the example above, constant energy ion bombardment was used simultaneously with the deposition process. However, the ion energy could also be varied (modulated) during the metals deposition, or the ion bombardment could be applied only after each metal layer had been deposited (sequential assistance). Here, we utilize MD simulations to investigate these three ion assistance approaches for controlling the interfacial structures of a model Cu/Co/Cu trilayer system. Several near-optimal processes for the growth of metallic superlattices with chemically sharp, planar interfaces are identified.
Section snippets
Molecular dynamics simulation
In MD simulations, a computational crystal is created by assigning the positions of atoms to an assembly of lattice sites. An interatomic potential is then used to calculate the forces between atoms, and Newton's equations of motion are used to calculate the velocities and positions of all atoms. This approach dynamically solves for atom vibration around the occupied lattice sites. It also naturally incorporates the energy barriers for the various jump paths and correctly simulates the
Simultaneous ion assistance with metal flux deposition
In conventional ion beam assistance methods, continuous inert gas ion irradiation of the growth surface accompanies metal deposition [21]. Numerous simulations of a Cu/Co/Cu trilayer structure deposition with argon ion assistance were conducted with ion incident energies between 0 and 30 eV and different ion incidence angles. Details of the atomic reassembly mechanisms using simultaneous ion assistance can be found in previous papers [24], [33]. Fig. 1 shows examples of the atomic structures
Effects of interface depth
It has been shown that quite chemically sharp, almost flat interfaces can be fabricated using an optimized ion energy simultaneous ion-assisted deposition scheme. However, the optimum ion energy is sensitive to underlying/overlying materials. Both Fig. 1, Fig. 3 indicate that the mixing and roughness of the Cu-on-Co and Co-on-Cu interfaces are different when the same growth conditions are used. This arises because the energy barriers for cobalt migration over terrace edges and the atomic
Discussion
The results discussed above indicate that optimum ion energy (to achieve the lowest combination of interfacial roughness and mixing) in a Cu/Co/Cu multilayer structure depends on the ion assistance method. For example, the optimized argon ion energy for simultaneous assistance is around 8 eV, whereas for modulated energy or sequential ion assistance, it is either 20 eV or more than 30 eV, respectively. This difference arises in part because the size of asperities that must be smoothed is different
Conclusion
An MD method has been used to explore low-energy argon ion-assisted deposition approaches for the fabrication of Cu/Co multilayers. The study indicates that:
- 1.
During continuous ion assistance, the ion energy significantly affects the interfacial structure of multilayer structures. High-ion energies promote migration of surface atoms over Ehrlich–Schwoebel barriers and promote flattening of the film surface. However, during multilayer growth they can also result in interlayer mixing by an atom
Acknowledgments
We are grateful to the Defense Advanced Research Projects Agency and Office of Naval Research for support of this work under ONR Grant N00014-03-C-0288 monitored by Drs. Carey Schwartz and Julie Christodoulou.
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