Cahit
Benel
a,
Arne
Fischer
a,
Anna
Zimina
bc,
Ralph
Steininger
d,
Robert
Kruk
a,
Horst
Hahn
*aef and
Aline
Léon‡
*d
aInstitute of Nanotechnology, Karlsruhe Institute of Technology, Hermann-von-Helmholtz-Platz 1, 76344 Eggenstein-Leopoldshafen, Germany
bInstitute of Catalysis Research and Technology, Karlsruhe Institute of Technology, Hermann-von-Helmholtz-Platz 1, 76344 Eggenstein-Leopoldshafen, Germany
cInstitute for Chemical Technology and Polymer Chemistry, Karlsruhe Institute of Technology, Engesserstr. 18/20, 76128 Karlsruhe, Germany
dInstitute for Photon Science and Synchrotron Radiation, Karlsruhe Institute of Technology, Hermann-von-Helmholtz-Platz 1, 76344 Eggenstein-Leopoldshafen, Germany. E-mail: aline.leon@Kit.edu
eJoint Research Laboratory Nanomaterials at Technische Universität Darmstadt, 64287 Darmstadt, Germany
fHerbert Gleiter Institute of Nanoscience, Nanjing University of Science and Technology, Nanjing, China
First published on 9th January 2019
The potential to control the structure of amorphous materials and establish correlations with their properties would constitute an extraordinary step in formulating new pathways to design and tailor amorphous structures, which correspondingly would exhibit novel properties. Towards achieving this goal, a bottom-up approach is proposed here. In the present study, cluster-assembled Fe80Sc20 metallic glasses are used as the model systems to illustrate this potentially groundbreaking approach. Accordingly, Fe80Sc20 amorphous films are nanofabricated under well-defined conditions with precise control over cluster size and impact energy. Their local atomic structures are characterized by X-ray absorption spectroscopy around both constituent metals, i.e., Fe and Sc. The capability of controlling the local structure by controlling the deposition energy (i.e., the clusters’ impact energy) has resulted in substantial changes in the magnetic Curie temperature. In fact, the Curie temperature changes by as much as 60 K when the deposition energy is increased from 50 eV per cluster (the lowest deposition energy) to 500 eV per cluster (the highest deposition energy). This remarkable result, clearly establishing a structure–property relationship, observed for the first time in cluster-assembled metallic glasses, opens up new pathways for synthesizing novel amorphous materials with engineered structures and accompanying new properties.
Conceptual insightsIn this manuscript, we demonstrate an effective method to synthesise cluster-assembled metallic glasses with full control over their atomic structure and magnetic properties. Growth of metallic glass films is performed by means of a novel experimental technique using the energetic impact of size-selected clusters on substrates. Experimental evidence for the correlation between the atomic structures of the constituent atoms (Fe and Sc herein), determined by XANES and EXAFS studies, and the magnetic properties in amorphous materials of Fe80Sc20 is provided. Our work demonstrates that the amorphous structure can be drastically different from the known structure of rapidly quenched metallic glasses and, furthermore, can be controlled by the impact energy of the clusters during assembly. In addition, a selected magnetic property, the Curie temperature, is shown to scale with the different local structures, potentially opening new ways to control the properties of the metallic glasses. Therefore, novel amorphous structures exist with distinct structural differences and they are stable over a certain temperature range. The discovery of the different local structures of metallic glasses, combined with the possibility of controlling the structures and magnetic (and potentially other physical) properties in binary metallic glasses, opens new horizons for the design of tailormade amorphous structures. |
Based on theoretical modeling,9ab initio molecular dynamics simulation,10 synchrotron high energy X-ray diffraction,11 and nano-beam electron diffraction,12 the atomic arrangements within metallic glasses have been described in terms of local motifs (a number of other terms have been used in the respective references, such as local atomic configurations, short-range order, clusters, etc.). It has been predicted that the relative population of local motifs can be used to control the properties of metallic glasses.13 However, experimental evidence for establishing relationships between the local atomic structure and macroscopic properties is missing due to the limitations of the existing synthesis routes, which are largely based on rapid quenching from either the gaseous (i.e. thin film deposition methods) or the liquid state (i.e., melt spinning techniques). An alternative method, mechanical deformation techniques (i.e., ball milling) occurring solely in the solid state, also does not provide the exact control of the experimental parameter to tailor the local atomic structure and to control the physical properties. In an attempt to control local motifs, Kartouzian et al.14 deposited particles in the size range of the local motifs (10–16 atoms) by cluster beam deposition. The amorphous nature of Cu50Zr50 films with different coverages per area (film thicknesses) was confirmed by synchrotron X-ray diffraction but the influences of the impact energy on the short-range order or any structure–property relationships were not investigated.14 Our technique of cluster ion deposition builds on the basic concept of synthesizing metallic glass samples utilizing a controlled bottom-up approach, in which small amorphous clusters, in the size range of a few hundred atoms, are assembled into metallic glass film samples. This tight control over cluster size has paved the way for developing a new and unique capability that makes it possible to change the local motifs by means of controlling the cluster deposition energy. It is precisely this unique capability that differentiates our innovative approach from other cluster synthesis and processing techniques that have been previously used.
The binary metallic system Fe100−xScx has been chosen as the model system for the present study, since it fulfils the prerequisites for easy glass formation,15 requiring both low eutectic points (at x = 9 at% and 80 at%) and different sizes of the constituent atoms (the radius of the Sc atom is 1.65 Å, whereas the radius of the Fe atom is 1.24 Å). Herein, the production of Fe80Sc20 clusters was performed using a custom-designed and -built cluster ion beam deposition system.16 The cluster size, determined by in situ time of flight mass spectrometry, shows a log-normal size distribution with an average value of 800 atoms per cluster and a sigma-value of 0.54. In this way, solid amorphous particles, consisting of a few hundred atoms with narrow size distribution, are deposited on a substrate and the impact energy of the particles is varied from 50 to 500 eV per cluster. The local atomic arrangements (local motifs) around the iron and scandium atoms were probed using X-ray absorption spectroscopy on samples deposited at 50, 100, 200 or 500 eV per cluster. As it will be shown, the size of the local motifs of the cluster-assembled metallic glasses systematically varies with variation in the clusters’ impact energy. This interesting result points out to the possibility that by varying the impact energy one can control the atomic structure of the resulting amorphous phase. It will be further shown that this possibility, of being able to vary the local structure by means of the deposition energy, results in a drastic change in the Curie temperature of the Fe100−xScx cluster-assembled amorphous films by as much as 60 K when the deposition (impact) energy is increased from 50 eV (the lowest value) to 500 eV (the highest value).
Fig. 1 Cross-sectional view of the deposition stage within the cluster ion beam deposition system that includes simulated ion trajectories, reproduced with the permission of AIP Publishing.1 The sample holder (a) for the deposition of ionized clusters is shown along with the deflection electrode (b). |
Fig. 2 displays the normalized Sc K-edge XANES spectra (and Fig. S2 – the Fe K-edge XANES, ESI†) of cluster-assembled metallic glasses with 50, 100, and 500 eV impact energy/cluster compared to the spectra of the corresponding metals, Sc2O3, and FeSc amorphous ribbon. Analysis of the valence states of Sc and Fe in the cluster-assembled metallic glass samples indicates that Sc and Fe are in the metallic state (as verified by the analysis of the energy positions of the absorption edges; refer to Table S1, ESI†), with an emphasis on the observation that a strong electron correlation effect is present around Sc, which enhances the screening of the Sc nuclear charge in these samples. Comparison to the Sc2O3 K-edge position and its fine structure clearly shows that the cluster-assembled samples are not oxidized for all impact energies. Moreover, the shapes of the Sc and Fe K-edge XANES spectra of the cluster-assembled samples are significantly different, when compared either to the corresponding metal foil or to the ribbon, suggesting different local atomic environments in these samples.
The fading of the EXAFS oscillations around Sc and Fe centers in the cluster-assembled metallic glasses, compared to metallic scandium shown in Fig. 3 (and see Fe K-EXAFS data in Fig. S3, ESI†), clearly confirms the amorphous structure of the cluster-assembled samples. The scattering profiles of the three cluster-assembled glass samples at the Sc and Fe K-edges are independent of the impact energy but they exhibit significant differences in shape/amplitude, compared to the corresponding metal, indicating different local structures in the cluster-assembled samples. It can be seen that the amplitudes of the oscillations around Sc are significantly lower compared to the amplitudes of the amorphous ribbon or the Sc metal, indicating a sizeable decrease in the number of neighboring atoms around the Sc absorbers. Further information on the local atomic structure around Sc and Fe atoms in the Fe80Sc20 cluster-assembled metallic glasses is derived from the detailed analysis of EXAFS spectra. Fig. 4 displays the magnitude of the Fourier transform k3-weighted EXAFS χ(k) function of the samples at the Sc and Fe K-edges. A significant reduction of the number of higher order shells, relative to the first order, is observed. This is consistent with the lack of long-range order in the Fe80Sc20 cluster-assembled metallic glass samples, irrespective of the impact energy. To quantify the evolution of the structural parameters around Fe and Sc centers, in terms of coordination numbers (N) and interatomic distances (R), with the impact energy, fits of the experimental spectra were performed using single scattering paths generated from theoretical models. The spectrum of the Fe metallic foil can be fitted using the crystallographic data of Fe in the bcc phase (a = b = c = 2.93 Å, space group Imm, 8 Fe atoms in the first coordination shell). However, the data of the cluster-assembled samples can only be fitted with a modified Fe structure, assuming an fcc phase (a = b = c = 3.64 Å, space group Fmm, 12 and 6 Fe atoms in the first and second coordination shells), where 3 Sc replace Fe in the first and second shells (see the fit of the 500 eV impact energy sample, Fig. S4 and S5, ESI†). A summary of the structural parameters around Fe and Sc atoms, obtained from the least-squares fitting, can be found in Fig. 4 (see also Table S2, ESI†). The scattering process involved in these materials was determined by the intensities and shapes of the scattering profiles of Fe and Sc atoms. It should be mentioned that the scattering around the Fe absorber in the cluster-assembled metallic glasses is largely dominated by the scattering of the surrounding iron atoms in the Fe80Sc20 structure and less so by the scandium surroundings. By contrast, the scattering at the Sc K edge is sensitive to the presence of the Sc–Fe bond, which can be easily distinguished from the Sc–Sc neighbors. It is evident from the experimental results that the size of the local motifs depends critically on the impact energy of the clusters on the substrate surface. But the Fe–Fe and Fe–Sc distances within the local motifs do not appear to be affected (in fact, these distances remain constant, within the error bar of the experimental data). For the lowest impact energy of 50 eV per cluster, the local motifs consist of only 5 atoms. By contrast, the local motifs of the sample deposited with an impact energy of 500 eV per cluster are substantially larger in size, consisting of 14 atoms per cluster and thus being comparable to those of the rapidly quenched sample.
Fig. 3 k 3 × χ(k) Sc K EXAFS spectra of the RQ ribbon and cluster assembled metallic glasses deposited with energies of 50, 100 and 500 eV per cluster. The Sc metal is shown for comparison. |
Fig. 4 The magnitudes of the Fourier transform of k3-weighted EXAFS signals at the Sc and Fe K-edges of the ribbon reference sample and of the cluster-assembled samples deposited with impact energies of 500, 100, and 50 eV per cluster (no phase correction). N represents the coordination number and R is the interatomic distance in Å for each experimental data resulting from the IFEFFIT fitting procedure (see Table S2 in the ESI†). |
From the structural characterization, it is evident that identical clusters in the cluster beam can lead to different amorphous structures with significantly different magnetic features and Curie temperatures, depending on the impact energy of the clusters. At present, to explain the change in the local motifs as a function of impact energy, it is assumed that the clusters with an average size of 800 atoms per cluster consist of local motifs of similar sizes and compositions to that of the RQ reference sample. The structural modifications, giving rise to the effects seen by EXAFS, may occur in the interfacial regions between the colliding clusters during their assembly into films, with a massive introduction of free volume and changes in the chemical composition during their energetic impact on the substrate.
Fig. 6 shows the observed changes in the Curie temperature, as a function of impact energy, together with one possible graphical representation of the local motifs based on the results of the EXAFS analysis, in terms of the number of neighboring atoms and their interatomic distances. Additional information on the local motifs such as the spatial arrangements of the atoms cannot be extracted from EXAFS data. The lower Curie temperatures, measured on the samples deposited at the lower impact energies (50, 100, 200 eV per cluster), are in line with the reduced number of spatially correlated nearest neighbors in the respective local motifs. Of course, to fully unravel the physical origins of this correlation, more information is needed on the geometrical configurations of Fe and Sc atoms along with the possible relative orientations of the neighboring local motifs. However, one can notice right away that the Fe–Fe distances between the nearest neighbors are virtually independent of the cluster impact energy. Consequently, when considering the trend in Curie temperature versus impact energy, the Fe–Fe distance dependence of the magnetic exchange interactions can be neglected in the first approximation. Thus, the observed increase in the Curie temperature with increasing size of cluster local motifs can be explained within the context of a standard mean-field approximation, strongly suggesting that increasing the number of the Fe nearest neighbors strengthens the magnetic exchange interactions and thus shifts the Curie temperature to the correspondingly higher values.
Footnotes |
† Electronic supplementary information (ESI) available. See DOI: 10.1039/c8mh01013g |
‡ Current address: European Institute for Energy Research, Emmy Noether Straße 11, 76131 Karlsruhe, Germany. E-mail: aline.leon@eifer.org |
This journal is © The Royal Society of Chemistry 2019 |