Despite being studied for nearly 50 years, smallest chemically stable moieties in the metallic glass (MG) could not be found experimentally. Herein, we demonstrate a novel experimental approach based on electrochemical etching of amorphous alloys in inert solvent (acetonitrile) in the presence of a high voltage (1 kV) followed by detection of the ions using electrolytic spray ionization mass spectrometry (ESI MS). The experiment shows stable signals corresponding to Pd, PdSi and PdSi2 ions, which emerges due to the electrochemical etching of the Pd80Si20 metallic glass electrode. These fragments are observed from the controlled dissolution of the Pd80Si20 melt-spun ribbon (MSR) electrode. Annealed electrode releases different fragments in the same experimental condition. These specific species are expected to be the smallest and most stable chemical units from the metallic glass which survived the chemical dissolution and complexation (with acetonitrile) process. Theoretically, these units can be produced from the cluster based models for the MG. Similar treatment on Pd40Ni40P20 MSR resulted several complex peaks consisting of Pd, Ni and P in various combinations suggesting this can be adopted for any metal-metalloid glass.
Most structural, physical and chemical properties of polycrystalline alloys depend directly on the crystallographic structure, characterized by long range order, and the microstructure, i.e., the ensemble of all defects within the material. The microstructure of alloys can be tailored by means of the processing steps resulting in control of properties. In contrast, the amorphous structure of metallic glasses with similar compositions that exhibit only short- and medium range order results in maze-like pattern in high resolution transmission electron microscopy (TEM) without any discernible microstructural information1,2,3. In view of their distinct physical and chemical properties, metallic glasses have gained popularity in several scientific disciplines. Advanced synthesis and processing methods have been employed to modify the local structure of these glassy systems by the controlled introduction of defects, such as interfaces and precipitates4,5,6,7,8,9,10,11,12,13,14. The absence of long range ordering in metallic glasses complicates the understanding of their local structure3. The smallest building blocks (structural local motifs or clusters) and the direct chemical bonding between the constituents have been determined in several experiments and predicted by theoretical models. Information on the bond length as well as nearest and next-nearest neighborhood has been provided by a variety of experiments15,16,17,18. Current research on the structure of metallic glasses has revealed favored and unfavoured local atomic packing (structural motifs) and a significant diversity in the short-range ordering of metallic glasses14.
Several structural models have been introduced to describe the local structure and to understand the origin of the unusual properties of metallic glasses compared to their crystalline counterparts4,10. In addition to long studied dense random packing of hard spheres and ‘solid-like’ and ‘liquid-like’ regions in MGs, cluster-based local ordering is a widely accepted model for structurally disordered, yet macroscopically homogeneous systems11,19. Tailoring the population of local structural motifs (or building blocks) in a controllable manner may help to improve and engineer selective properties of metallic glasses. Hence deciphering the structural dissimilarity among the local motifs is necessary to establish a causal link between the key local structures and macroscopic properties2,3,14,20,21. Experimentally, the process is far more challenging as it requires high-end instrumental facility such as aberration corrected transmission electron microscopy (TEM) or synchrotron radiation sources16.
The understanding of the unusual mechanical/magnetic properties and the manipulation of the structure to optimize and improve properties of metallic glasses is directly related at the atomic level to the chemical bonding between the constituent elements15,20,22.
In search of the most stable configuration in metal-metalloid type metallic glasses, we introduce a novel method to visualize the chemical building blocks of single phase complex amorphous materials using a combination of easily accessible mass spectrometry (MS) additionally supported by Raman spectroscopy. The metallic glasses are de-alloyed or dissolved by electrochemical corrosion. In a process known as “Electrolytic Spray”, which is a fairly recent technique, introduced and described by Cooks and co-workers, electrospray ionization is employed to form ions for further characterization23,24. We have adopted this technique to determine the immediate local chemical bonds among the constituents of a metallic glass. It is the principal idea of the experiment that the strongest bonds between the constituent elements will remain stable and can be considered as the elemental building blocks of the metallic glass, stabilizing the amorphous structure. The combination of two techniques (mass spectrometry and Raman spectroscopy) can be employed to determine the bonding and the active constituents, which are responsible for the stabilization of the amorphous phase in the model systems Pd80Si20 and Pd40Ni40P20.
Results and discussion
Electrolytic spray ionization mass spectrometry
In electrolytic spray ionization mass spectrometry, metals are electrochemically etched with acetonitrile (ACN) in the presence of a high voltage. The solvated metal ions are directed to a mass spectrometer for analysis. Up to now, the etched ions have been deposited in desired shapes on preferred substrates in the form of nanoparticles as described by Cooks et al.23,24 in the past and Spolenak et al. more recently25. In both cases, the sacrificial metal electrode acts as an anode. In the current work, the electrolytic spray process has been used in a completely different perspective where a MSR was used as an electrode. Electrochemical reaction between the MSR and ACN produced solvated ions in the spray plume which were subsequently detected using a Waters Synapt G2S mass spectrometer. Electrolytic spray was achieved and calibrated by modifying an existing nano-electrospray ionization (NESI) setup as shown in Fig. 1A.
Electrochemical etching and dealloying from polycrystalline metal alloys
When a pure polycrystalline metal M was used, only M+ and M(CH3CN)n+ and a few M(H2O)+ species were observed. This was observed previously as the pure metal can have only one type of metal–metal bonding (see Fig. S1 for polycrystalline Cu)23,24. A Pt-wire (99.99% purity) was used as an electrode to optimize the experimental parameters. Close to 1 kV voltage was applied to generate a stable ion current during the electrolytic spray. During initial spray period, a strong signal at m/z 107 and 109 was observed along with a peak envelope at m/z 194–198. The peaks were assigned as Ag+ and Pt+. Upon careful examination, a peak for Au+ at m/z 197 was also found. Ag and Au are present as common impurities in the commercial Pt-wire and are etched out first as those are more reactive than Pt. The intensity of Ag+ and Au+ decreased with time (0–10 min) as the impurity was removed from the electrode as per their electrochemical reactivity and consequently, the Pt+ signal became stronger. The data are presented in Fig. 1B.
This is an example of dealloying during electrolytic spray26 and demonstrates the sensitivity of the process. It should be noted that non-reactive organic solvent acetonitrile was used for electrochemical etching here instead of strong acid like hydrofluoric acid, sulphuric acid etc. (or alkali in some cases).
Building blocks of Pd80Si20 MSR
Armed with the idea, we have selected a well-studied single phase glassy Pd80Si20 melt-spun ribbon (MSR)27,28,29 as an electrode and followed the above mentioned process. It should be noted here that electrochemical etching from any metallic glass using ACN has not been attempted before. The data are shown in Fig. 2 [corresponding X-ray diffraction (XRD) in Fig. S2]. During electrolytic etching using NESI MS, the main constituents detected in the mass spectra are Pd+ (m/z 102–110), PdSi+ (m/z 132–138) and PdSi2+ (m/z 158–168) with a few water adducts in the positive ion mode. This observation indicate that electrochemical etching is happening without selectively following the electrochemical reactivity of Pd and Si. Simultaneous release of Pd+, PdSi+ and PdSi2+, all of which has different reactivity, is possible only if they are part of the same microscopic unit in the Pd80Si20 MSR alloy.
Considering the dissolution process of the alloy, these species can be considered as the active chemical building blocks in the Pd80Si20 amorphous phase and, thus, are the smallest stable and predominant entities. The entity PdSi has been predicted from measurements of the radial distribution function (RDF) on the same system but the existence of PdSi2+ was not known28,29,30,31. The ratio of Pd and Si in the MSR was found to be ~ 3.8:1 from mass spectrometric intensity, which is very close to the actual ratio 4:1. In order to ensure that the reaction is not just a reflection of the surface activity of the MSR, more than 30 h of experiment was performed on randomly selected days with the same experimental parameters using the same MSR (in triplicate). In all cases, similar intensity ratios among the detected species were found. Additionally, the triatomic PdSi2+ species can possess different structures (linear or triangular), which can be separated using ion mobility (IM) coupled with regular MS. When these ions were allowed to pass through the ion mobility drift cell, PdSi2+ showed two isomeric peaks in the extracted ion mobilogram indicating two different types of PdSi2+ geometry. Ion geometries were optimized using density functional theory (DFT) with TPSS functional and def2-TZVPP basis set as implemented in the TURBOMOLE package. The triangular structure (77% population from IM-MS) is found to be more stable compared to the linear one (23% population from IM-MS) which was further confirmed by IM-MS.
Identification of the structural motifs
The existence of these particular species can be understood following the cluster based models generally used for the metallic glass. A plausible electrochemical fragmentation mechanism involving a Pd10Si3 (microscopic part of Pd80Si20 MSR) icosahedron cluster is shown for clarity (Fig. 3). The icosahedron geometry is a suggested local structural model for metallic glass and was chosen to represent 4:1 overall atomic ratio. While non-icosahedron solute centered quasi-equivalent coordination polyhedra is predicted for such Pd-Si system32,33, a simpler icosahedron model is used here to understand the possible pathway which can lead to PdSi2+ as seen in the current experimental condition shown in Fig. 2. Existence of the moieties (PdSi and PdSi2) in the Pd80Si20 MSR is additionally confirmed by Raman spectroscopy (see later).
Apart from mass spectrometry, Raman spectroscopy can help in understanding the materials. The optical phonon (ΓO) signal at 520 cm−1 of pure crystalline Si is generally used as a standard for Raman spectroscopy. Raman spectra in the range of 200–550 cm−1 are shown in Fig. S3. Amorphous Si shows a broad hump at ~ 480 cm−1. When the amorphous and crystalline (see later for the preparation) Pd80Si20 alloys were analyzed by Raman spectroscopy, none of the samples showed any peak at 520 cm−1 or hump around ~ 480 cm−1. This confirms the absence of amorphous and crystalline Si in the samples. This is in agreement with the previous RDF calculation which predicted no long range Si–Si bonding. Two peaks at ~ 190 cm−1 and ~ 210 cm−1 in the amorphous specimen are due to PdSi type of structure. Other peaks at 280, 332, 358 cm1 are attributed to the disordered PdSi while diffused and broad peaks in the range of 200–450 cm−1 are due to disordered PdSi2. No sharp signal comprising of pure PdSi or PdSi2 were observed, which can be understood to disorder induce Raman scattering from the amorphous alloy34,35,36,37,38,39. Results of the Raman spectroscopy confirm the presence of PdSi and PdSi2 in the Pd80Si20 MSR sample. These components are also seen during NESI MS measurement. Raman spectroscopy has been implemented here as a complementary method to the NESI MS.
Difference between amorphous and crystalline phase
Amorphous to crystalline phase transformation has been carried out upon heating the amorphous material well above its crystallization temperature. Previously reported results show that the crystallization temperature of Pd80Si20 MSR is 648 K where pure Pd is formed in majority along with Pd3Si. To obtain a fully crystallized sample, the MSR was heated at 673 K for 3 h in vacuum and the annealed ribbon was subsequently analyzed.
Mass spectra arising from the annealed ribbon visibly differ from that of amorphous analogue. It shows only the characteristic feature of Pd ions with H2O and CH3CN complexes of Pd. No signal for PdSi or PdSi2 were found after annealing (Fig. S4). The other component Pd3Si was not seen which is probably inert to such electrochemical treatment and hence was not etched out. The other reason is surface segregation of Pd after annealing leading to dealloying as discussed in Fig. 1. Presence of nanosized Pd was further confirmed by surface enhanced Raman spectroscopy (SERS) (see Note 1 and Fig. S5 in supplementary information for details). Raman spectroscopy also could not identify Pd3Si at the surface of the annealed ribbon.
Building blocks of Pd40Ni40P20 MSR
To extend the feasibility of the process to differentiate other amorphous systems, the ternary glassy alloy Pd40Ni40P20 was analyzed following identical methods as discussed above. This glass has also been studied extensively40,41,42,43,44,45. In this case, the material is composed of Pd–Ni metallic bonds and both Pd-P and Ni–P covalent bonds as reported in the previous studies. When the amorphous Pd40Ni40P20 ribbon was subjected to electrolytic spray at 1 kV potential (NESI MS), multiple pure Ni, Pd and a few water and ACN adducts were seen (see Fig. 4). The small quantity of crystalline Cu present on the surface is an impurity in the system being etched simultaneously. The presence of Cu arises most likely from the synthesis, when the molten mixture of Ni2P and Pd is collected on a water-cooled Cu surface. The Ni–P type bonds in the metallic glass are confirmed from the NiP2 and NiP containing ions in the mass spectrum. A strong and stable signal was found at m/z 309.8 which is assigned as PdNiPO(OH)(ACN)2+. Presence of these ion was further confirmed by tandem mass spectrometry (MS/MS) where Ni and solvent loss peaks were observed (Fig. S6). Initial loss of Ni was observed and the resulting species PdPO(OH)(ACN)2+ was seen at m/z 251.9. With increasing collision energy (0 eV to 30 eV, laboratory collision energy), other components were also lost and at the highest collision energy, only signal of Pd+ fragment was detected. After careful examination, the peak due to Ni+ was also seen (inset of Fig. 4B and Fig. S6B) in low mass region but the intensity was far lower compared to Pd+ intensity. Probably the most favored fragmentation pathway (in MS/MS) is by neutral Ni loss and hence Ni+ is not seen at higher intensity. The Pd–Ni unit was not seen in the current MS process but due to the presence of P in the system species containing both Pd and Ni with P were observed.
After the NESI MS analysis, the MSR was heated at 693 K in vacuum for 2 h above its reported glass transition temperature (575 K) and the crystalline alloy was analyzed again using NESI MS. The mass spectral signal from the crystalline sample is completely different from the amorphous one. The strong signal at m/z 148.5 was assigned at Ni2P, which is known to be a stable phase in the crystalline alloy and preformed Ni2P was used as Ni and P source during the synthesis of the glass (Fig. S7). Previous reports suggest the existence of Ni3P, which was not observed in the present experimental condition. After crystallization, Pd–P bonds were not observed and only free Pd+ with a few ACN and water adducts were found in the mass spectrum. Apart from free Ni and Pd, Ni2Pd2P phase is also known for the crystalline phase, absence of which can be explained by similar metallic bond breaking during electrospray analysis.
A direct method, based on electrolytic spray ionization mass spectrometry and Raman spectroscopy, to understand the most stable structural components and local bonding in amorphous materials namely, in Pd80Si20 and Pd40Ni40P20 metallic glasses is presented here. An inert solvent, acetonitrile was used for electrochemical etching during mass spectrometric experiment and subsequently for carrying the ions to the mass spectrometer. While electrochemical dealloying is evident for polycrystalline metals, single phase glassy alloys showed distinct ions with various combination of the constituent elements. Amorphous Pd80Si20 MSR showed signals for Pd, PdSi and PdSi2 ions, which are further supported by Raman spectroscopy. After crystallization, only Pd containing ions were seen in positive ion mode. Absence of other entities in the crystalline sample could be understood from the surface segregation of nano-Pd on the surface as seen from Raman spectroscopy. A simple cluster based structural model has been used to understand the most stable building blocks for such materials. Irrespective of the nuclearity and geometry of the clusters, only these three species (for Pd80Si20) are possible as the smallest stable building blocks which are now experimentally proven. A similar study on Pd40Ni40P20 glass showed characteristic peaks containing Ni–P and Pd–P in different complex combination. Understanding the difference of the local structure of different forms of amorphous materials with similar chemical composition would allow to tune their physical properties such as high mechanical strength, enhanced magnetism etc. Detailed theoretical calculations of the proposed phases and their three dimensional projection in voxel by voxel fashion will reveal more about the chemical structure of the materials.
Synthesis of Pd80Si20 and Pd40Ni40P20 MSR
Both the glasses were synthesized following conventional melt quenching technique and was spun on a rotating Cu disc. For Pd40Ni40P20, preformed Ni2P was used as Ni and P source.
All mass spectrometric studies were performed in positive ion nano-electrospray ionization (NESI) mode in a Waters’ Synapt G2S high definition mass spectrometer (MS) equipped with travelling wave ion mobility (IM) separation (TWIMS) and time of flight mass analyzer. About 1 kV DC high voltage was applied on the borosilicate glass capillary containing the metal/glassy alloy electrode and pure acetonitrile (ACN) from Sigma Aldrich was used as spray solvent. Cone voltage and source offset were set at 20 and 30 V, respectively. For ion mobility separation, IMS velocity and wave height were set at 650 m/s and 40 V, respectively.
All Raman spectroscopic measurements were performed using a Renishaw in via confocal Raman spectrometer equipped with 532 and 785 nm laser with maximum laser power of 50 mW. Most of the measurements were performed with 532 nm laser. Only SERS study was performed with 785 nm laser to avoid emission from the analyte.
Structure of the isomeric PdSi2 ions were optimized using density functional theory (DFT) with TPSS functional and def2-TZVPP basis set as implemented in the TURBOMOLE package. Coordinates of the optimized triangular and linear PdSi2+ structures are in supplementary information.
Greer, A. L. Metallic glasses. Science (Washington, D C) 267, 1947–1953 (1995).
Ma, E. Tuning order in disorder. Nat. Mater. 14, 547–552 (2015).
Miracle, D. B. A structural model for metallic glasses. Nat. Mater. 3, 697–702 (2004).
Ye, J. C., Lu, J., Liu, C. T., Wang, Q. & Yang, Y. Atomistic free-volume zones and inelastic deformation of metallic glasses. Nat. Mater. 9, 619–623 (2010).
Wang, Q. et al. Unusual fast secondary relaxation in metallic glass. Nat. Commun. 6, 7876 (2015).
Demetriou, M. D. et al. A damage-tolerant glass. Nat. Mater. 10, 123–128 (2011).
Wang, Q. & Jain, A. A transferable machine-learning framework linking interstice distribution and plastic heterogeneity in metallic glasses. Nat. Commun. 10, 5537 (2019).
Plummer, J. Is metallic glass poised to come of age?. Nat. Mater. 14, 553–555 (2015).
Liu, Y. et al. Metallic glass nanostructures of tunable shape and composition. Nat. Commun. 6, 7043 (2015).
Laws, K. J., Miracle, D. B. & Ferry, M. A predictive structural model for bulk metallic glasses. Nat. Commun. 6, 8123 (2015).
Zhu, F., Song, S., Reddy, K. M., Hirata, A. & Chen, M. Spatial heterogeneity as the structure feature for structure-property relationship of metallic glasses. Nat. Commun. 9, 1–7 (2018).
Sun, Y., Concustell, A. & Greer, A. L. Thermomechanical processing of metallic glasses: Extending the range of the glassy state. Nat. Rev. Mater. 1, 16039 (2016).
Ketov, S. V. et al. On cryothermal cycling as a method for inducing structural changes in metallic glasses. NPG Asia Mater. 10, 137–145 (2018).
Wu, Z. W., Li, M. Z., Wang, W. H. & Liu, K. X. Hidden topological order and its correlation with glass-forming ability in metallic glasses. Nat. Commun. 6, 6035 (2015).
Wagner, H. et al. Local elastic properties of a metallic glass. Nat. Mater. 10, 439–442 (2011).
Hirata, A. et al. Direct observation of local atomic order in a metallic glass. Nat. Mater. 10, 28–33 (2011).
Chen, N., et al. Direct observation of fast surface dynamics in sub-10-nm nanoglass particles. Appl. Phys. Lett.114, 043103/043101–043103/043105 (2019).
Liu, W.-H. et al. Nanoscale structural evolution and anomalous mechanical response of nanoglasses by cryogenic thermal cycling. Nano Lett. 18, 4188–4194 (2018).
Howe, J. M. Direct observation of order in the liquid at a solid-liquid interface by high-resolution transmission electron microscopy. Philos. Mag. A 74, 761–775 (1996).
An, Q. et al. How the toughness in metallic glasses depends on topological and chemical heterogeneity. Proc. Natl. Acad. Sci. USA 113, 7053–7058 (2016).
Anon. Crystallizing glassy issues. Nat. Mater.14, 541 (2015).
Mitrofanov, Y. P., Peterlechner, M., Divinski. S. V., & Wilde, G. Impact of plastic deformation and shear band formation on the boson heat capacity peak of a bulk metallic glass. Phys. Rev. Lett.112, 135901/135901–135901/135905 (2014).
Li, A. et al. Using ambient ion beams to write nanostructured patterns for surface enhanced Raman spectroscopy. Angew. Chem. Int. Ed. 53, 12528–12531 (2014).
Li, A., Luo, Q., Park, S.-J. & Cooks, R. G. Synthesis and catalytic reactions of nanoparticles formed by electrospray ionization of coinage metals. Angew. Chem. Int. Ed. 53, 3147–3150 (2014).
Reiser, A. et al. Multi-metal electrohydrodynamic redox 3D printing at the submicron scale. Nat. Commun. 10, 1–8 (2019).
Li, X. et al. Dealloying of noble-metal alloy nanoparticles. Nano Lett. 14, 2569–2577 (2014).
Adjaoud, O. & Albe, K. Interfaces and interphases in nanoglasses: Surface segregation effects and their implications on structural properties. Acta. Mater. 113, 284–292 (2016).
Durandurdu, M. Ab initio modeling of metallic Pd80Si20 glass. Comput. Mater. Sci. 65, 44–47 (2012).
Deng, Y. H., Wen, D. D., Li, Y., Liu, J. & Peng, P. Local atomic structures of amorphous Pd80Si20 alloys and their configuration heredity in the rapid solidification. Philos. Mag. 98, 2861–2877 (2018).
Alamgir, F. M., Jain, H., Schwarz, R. B., Jin, O. & Williams, D. B. Electronic structure of Pd-based bulk metallic glasses. J Non-Cryst. Solids 274, 289–293 (2000).
Faruq, M., Villesuzanne, A. & Shao, G. Molecular-dynamics simulations of binary Pd-Si metal alloys: Glass formation, crystallization and cluster properties. J. Non-Cryst. Solids 487, 72–86 (2018).
Cheng, Y. Q. & Ma, E. Atomic-level structure and structure-property relationship in metallic glasses. Prog. Mater. Sci. 56, 379–473 (2011).
Sheng, H. W., Luo, W. K., Alamgir, F. M., Bai, J. M. & Ma, E. Atomic packing and short-to-medium-range order in metallic glasses. Nature (London, U K) 439, 419–425 (2006).
Karabko, A. O., Dostanko, A. P., Kong, J. F., & Shen, W. Z. Phase transition and phonon dynamics in NiPdSi: An annealing study by temperature-dependent Raman spectroscopy. J. Appl. Phys.105, 033518/033511–033518/033515 (2009).
Prasad, A. & Saxena, N. S. Phonons in Pd80Si20 glass. Mater. Sci. Forum 223–224, 83–86 (1996).
Wang, X. L. et al. Plasticity of a scandium-based nanoglass. Scr. Mater. 98, 40–43 (2015).
Donthu, S. K., Tripathy, S., Chi, D. Z. & Chua, S. J. Raman scattering probe of anharmonic effects in NiSi. J. Raman Spectrosc. 35, 536–540 (2004).
Zhang, S-L., Wang, X., Ho, K-s., Li. J., Diao, P., & Cai, S. Raman spectra in a broad frequency region of p-type porous silicon. J. Appl. Phys.76, 3016–3019 (1994).
Thompson, M. J., Johnson, N. M., Nemanich, R. J. & Tsai, C. C. Silicide formation in palladium-a-silicon:hydrogen Schottky barriers. Appl. Phys. Lett. 39, 274–276 (1981).
Kai, W., Wu, Y. H., Jen, I. F., Ho, T. H., & Hsieh, H. H. Air-oxidation of a Pd40Ni40P20 bulk glassy alloy at 250–420 °C. J. Alloys Compd.586, S24–S30 (2014).
Drehman, A. J., Greer, A. L. & Turnbull, D. Bulk formation of a metallic glass: Palladium-nickel-phosphorus (Pd40Ni40P20). Appl. Phys. Lett. 41, 716–717 (1982).
Wang, W., Xu, Y., & Huang, X. Crystal nucleation and formation of bulk metallic glass in undercooled palladium-nickel-phosphorus (Pd40Ni40P20) melt under high pressure. Sci. China Ser A35, 1017–1024 (1992).
Kui, H. W. Formation of bulk palladium-nickel-phosphorus (Pd40Ni40P20) glass. Appl. Phys. Lett. 62, 1224–1226 (1993).
Yingfan, X., Xinming, H., Hong, G. & Wenkui, W. Formation of palladium-nickel-phosphorus (Pd40Ni40P20) bulk metallic glass. J. Mater. Sci. Lett. 9, 850–851 (1990).
Guan, P. F., Fujita, T., Hirata, A., Liu, Y. H., & Chen, M. W. Structural origins of the excellent glass forming ability of Pd40Ni40P20. Phys. Rev. Lett.108, 175501/175501–175501/175505 (2012).
We acknowledge Prof. Gerhard Wilde Institute of Materials Physics, University of Münster for generously providing Pd40Ni40P20 MSR. A.B. and S.B. gratefully acknowledge Karlsruhe Institute of Technology for guest scientist fellowships. A.B. thanks Prof. Manfred M. Kappes for his valuable comments and suggestions. A.B. thanks Dr. Jean Francois Greisch for initial NESI mass spectrometric experiments and data analysis. A.B. thanks Erik Karsten Schneider for helping with DFT calculation. H.H. and S.H.N. acknowledge for the financial support provided by the Deutsche Forschungsgemeinschaft under grant HA 1344/30-2. We thank Karlsruhe Nano-Micro Facility for mass spectrometry facility. We acknowledge the support of KIT publication fund.
Open Access funding enabled and organized by Projekt DEAL.
The authors declare no competing interests.
Springer Nature remains neutral with regard to jurisdictional claims in published maps and institutional affiliations.
About this article
Cite this article
Baksi, A., Bag, S., Kruk, R. et al. Structural insights into metal-metalloid glasses from mass spectrometry. Sci Rep 10, 17467 (2020). https://doi.org/10.1038/s41598-020-74507-w