( 2019 2018 2017 )
Tracing fcc iron in ODS steel. — The crystal structure, the magnetic properties, and the valence band density of states of an oxide dispersion strengthened (ODS) steel with nominal composition of Fe–18%Cr–13%Ni-2.5%Mo-3.2%Si-0.1%C +1 wt% Y2O3 was investigated applying volumetric and surface sensitive methods. The sample volume contained majority fcc and minority bcc phases according to XRD and volumetric magnetic measurements, while the surface layer of the grains contained only the paramagnetic fcc phase, which was revealed by conversion electron Mössbauer spectrometry (CEMS) and by photoelectron measurements. The valence band photoelectron emission spectra reflected well the average distribution of the theoretically expected DOS, however, there were no signs of abrupt peaks in the region of 0–4 eV below the Fermi level that could have been attributed to 3d Fe states (bcc phase). It was demonstrated that the photoelectron emission can be utilized to distinguish the Fe atoms located in different crystallographic structures. The valence band data of the ODS steel was compared to those of a bcc iron based magnetic alloy .
Interface properties of nanoscale layers. — The behavior of the atomically sharp Al-on-Fe and the chemically mixed Fe-on-Al interfaces under heat treatment up to 300 oC were studied in Al/Fe/Al trilayers by conversion electron Mössbauer spectroscopy. The samples were prepared by high vacuum evaporation and the heat treatments were made ex-situ in an ultrahigh vacuum of 10−8 Pa. The preliminary results undoubtedly show that alloying and the formation of a paramagnetic alloy phase starts at higher temperature at the Al-on-Fe interface.
α-synuclein protein – new interpretation. — The potential barriers governing the motions of α-synuclein (αS) variants’ hydration water (Fig. 1) was in the focus, which yielded essential information about distributions and heights of them . All of the αS variants possess secondary structural elements, although monomers are intrinsically disordered. Monomers have 33% secondary structure, and therefore they are more compact than a random coil. At the lowest potential barriers with mobile hydration water, monomers are already functional, a monolayer of mobile hydration water is surrounding them. The solvent-accessible surface of the oligomers is ordered or homogenous in its interactions with water to 66%. As a contrast, αS amyloids are disordered or heterogeneous to 75% of their solvent accessible surface. Mobile water molecules in the first hydration shell of amyloids are the weakest bound compared to other forms.
Figure 1. α-synuclein (a) monomers, (b) oligomers and (c) amyloids, wild type (dark blue open up triangles, dark blue dot-dashed lines) and A53T mutant (cyan solid down triangles, dotted cyan lines) variants dissolved in pure water, melting diagrams. Data are given for 50 mg ml-1 protein concentration.
Molecular motions and interactions in solutions of proteins and their 1:1 complex. — Wide-line 1H NMR measurements were extended and all results were interpreted in a thermodynamics based new approach on aqueous solutions of thymosin-β4 (Tβ4), stabilin C-terminal domain (CTD) and their 1:1 complex ,. Energy distributions of potential barriers controlling the motion of protein-bound water molecules were determined. Heterogeneous and homogeneous regions were found in the protein-water interface. The measure of heterogeneity of this interface gives quantitative value for the portion of disordered parts in the protein. Ordered structural elements were found extending up to ~20% of the individual whole proteins. About 40% of the binding sites of free Tβ4 get involved in bonds holding the complex together. The complex has the most heterogeneous solvent accessible surface (SAS) in terms of protein-water interactions. The complex is more disordered than Tβ4 or stabilin CTD. The greater SAS area of the complex is interpreted as a clear sign of its open structure.
Interface properties of nanoscale layers. — Our work aimed to study the buried interfaces ex situ in polycrystalline trilayer structures by Mössbauer spectroscopy. In a structurally perfect and chemically sharp layered structure it is only two monolayers of Fe atoms at the interface which “feel the presence of other kind of atoms”, since hyperfine parameters of the Mössbauer atom are basically determined by atoms located in its first two coordination shells even in case of metallic systems. This allows us to reveal differences in width and chemical composition of the bottom and top interfaces of nanoscale Fe layers. For this purpose the Mössbauer parameters of trilayer pairs of equal Fe layer thickness are compared, for example Nb/Fe/Nb and Nb/Fe/Ag pairs. (The layer sequence is given as starting from the bottom, i.e. from the substrate side.) The Mössbauer parameters of the Fe-on-Nb interface can be derived from the Nb/Fe/Ag samples, since the Ag-on-Fe interface is chemically very sharp and the Mössbauer parameters of two monolayers of Fe atoms at the Fe-Ag interface are well known from the literature. The Mössbauer parameters of the Nb-on-Fe interface can be derived from the comparison of the Nb/Fe/Nb and Nb/Fe/Ag sample pairs of equal Fe layer thickness, as the fitted parameters and the intensity of the different components are compared. For example, if the bottom and top interfaces of the Fe layer are similar, then the hyperfine parameters of the Fe-Nb interface components remain unaltered and the intensity of the Nb-Fe interface sub-spectrum is halved when the top Nb layer is replaced by Ag.
In case of Nb/Fe/Nb vacuum evaporated trilayers on top of Si(111) substrate our Mössbauer analysis indicated that the chemical mixing forms less than 1 nm thick Fe-rich interfaces at both sides of the Fe layer. It is in accordance with our x-ray reflectometry and Rutherford backscattering spectrometry measurements , where the evaluations provided slightly larger - around 2 nm wide and symmetric - interface layers indicating that chemical mixing and geometrical roughness equally contribute to the element distribution across the layers.
The different interface width and alloy composition of the Fe-on-Ti and Ti-on-Fe interfaces was shown to result different evolution of the phase compositions at the two interfaces in Ti/Fe/Ti trilayers (Fig. 1) under heat treatments below 300 °C. At the Ti-on-Fe interface the amount of both the paramagnetic and magnetic alloy components increase, while at the Fe-on-Ti interface the amount of the paramagnetic alloy increases at the expense of the magnetic alloy component. The results are explained by the different thickness of the magnetic alloy at the two interfaces and the consequently different degree of layer formation.
Characterization of protein molecules by 1H NMR — To characterize aqueous protein solutions, a novel thermodynamic method was applied. It is based on the two-component wide line 1H NMR signal and provides direct experimental data on the potential energy surface of protein molecules. The temporal behavior of the wide line 1H NMR signal component coming from mobile hydration water proves clearly that during heating the internal energy changes. The amount of mobile hydration water as a function of temperature gives a melting diagram. Melting diagrams provide special characterization of the proteins.
The usefulness and merits of our approach are demonstrated through four globular structured protein examples . Quantitative conclusions could be deduced about the ratios of the globular (ordered) and the more solvent exposed (disordered) regions of the protein molecules and also about the energy relations of the protein-water interactions. These “globular” proteins are disordered to some definite, though small degree. The extent of disorder ranges from 0.14% to 0.49% in these proteins.
Hydration properties of folded and unfolded/disordered miniproteins were monitored in frozen solution . The amount of mobile water as function of T was found characteristically different for folded, semi-folded and disordered variants. Comparing results of wide-line 1H-NMR and molecular dynamics simulations, it was found that both the amount of mobile water, as well as the miniproteins’ thaw profiles differ significantly as function of the compactness and conformational heterogeneity of their structure.
Parkinson’s disease is connected with abnormal α-synuclein (αS) aggregation. Energetics of potential barriers governing motions of hydration water is examined . Information about the distributions and heights of potential barriers is gained by a thermodynamical approach. The αS monomer contains 33% secondary structure and is more compact than a random coil. αS monomers realize all possible hydrogen bonds. Oligomers are ordered by 66%. Wild type and A53T amyloids show identical, low-level hydration, and are considered as disordered to 75%.
Magnetic properties of nanoscale Fe-Ag multilayers. — The aim of our work was to give a broad-range map on the variation of the blocking temperature as a function of the Fe-layer (tFe) and Ag-layer (tAg) thickness and the number (n) of the bilayers in Fe-Ag granular multilayers. The magnetic relaxation of Fe-Ag multilayers with tFe in the few monolayers range was first recognized in epitaxial single-crystal multilayers. The relaxation was first attributed to the two-dimensional nature of the ferromagnetic layers but the observation of a linear temperature dependence of the magnetic hyperfine field gave way to explanations based on the island structure of the Fe layers. The deviation of the magnetization of the field-cooled (FC) and zero-field cooled (ZFC) sample undoubtedly indicates a small particle behavior of Fe islands in polycrystalline multilayers. The superparamagnetic properties of such so-called discontinuous or granular multilayers have been the subject of several investigations, similarly to granular alloys prepared by co-deposition. The superparamagnetic properties were shown to be determined by the magnetic anisotropy and the size distribution of the ferromagnetic grains and the strength of the exchange and dipolar interactions between the grains within and between the layers. Our work pointed to the role of the grain-size variation along the subsequent ferromagnetic layers.
The dependence of the blocking temperature (TB) on the bilayer number is shown in Fig. 1, where solid and open symbols denote two series of samples with tAg = 50 and 70Å and TB is measured by the maximum value of the ZFC magnetization curve. It is evident at a first glance that the scatter of the TB values is significant, which is basically due to the relatively large error of the nominal layer thickness in the few Å layer-thickness range. In spite of the large experimental errors, one can make two definite observations; (i) the blocking temperature increases monotonically with the bilayer number, showing a tendency to saturation and (ii) the tAg= 70 Å points (open symbols) lie systematically below the tAg= 50 Å points (closed symbols). Observation (ii) can evidently be explained by the decrease of magnetic interactions between the ferromagnetic layers as the distance between them increases. Dipolar interactions may also contribute to observation (i) as some previous works have already shown in the literature, but the observed changes were smaller.
Figure 1. Blocking temperature (TB) of (4 Å Fe + tAg)n multilayers as a function of bilayer number for tAg = 50 Å (solid symbols) and 70 Å (open symbols). The solid and dashed lines are guides to the eye for the solid and open symbols, respectively.
Another possible cause, namely that the grain size may vary along the multilayer stack, has been demonstrated by our experiment shown in Figs 2 and 3. A composite multilayer pair with bilayer number of n = 20 was fabricated which contained only one Fe-Ag bilayer, the rest being composed of non-magnetic Nb-Ag bilayers, as shown in Fig. 2. The multilayer with the Fe layer on the top has a higher blocking temperature (TB = 80 K) than that with the Fe layer on the bottom (TB = 25 K), but the increase is smaller than that what can be seen in Fig. 1. These results suggest that the dipolar interactions between the magnetic layers and the grain-size variation along the layer structure might equally play a role in the relation between TB and the bilayer number. The respective role of these factors should be further studied.
Figure 2. Schematic view of a special Fe-Ag/Nb-Ag composite multilayer pair with bilayer number of n = 20, containing one Fe layer of 4 Å either in the bottom bilayer (left panel) or in the top bilayer (right panel). The equal thickness of the bottom and top Fe layers was ensured by the simultaneous deposition of the layers.
Figure 3. Magnetization as a function of temperature measured at 10 Oe for the Si/70 Å Ag + 4 Å Fe + (70 Å Ag + 4 Å Nb)19 (bottom) and Si/(70 Å Ag + 4 Å Nb)19 + 70 Å Ag + 4 Å Fe) (top) multilayer. For each sample, the lower curve (with the maximum) belongs to the ZFC condition while the upper curve to the FC condition.
Melting diagram of protein solutions and its thermodynamic interpretation — NMR characteristics of frozen aqueous solutions provide direct information on the immobile and partially or fully mobile parts of the molecules. The purpose is the thermodynamic characterization of protein systems. The studies were focused on the proteins ubiquitin (UBQ) and early response to dehydration 10 (ERD10). These proteins are representatives of distinct structural classes, UBQ is a globular protein and ERD10 is intrinsically disordered protein (IDP). The melting diagrams (MDs) of the protein solutions are the amount of the mobile hydration water as a function of temperature or potential barrier for this motion (Fig. 1). The amount of mobile hydration water is measured by the amplitude of the slowly decaying 1H NMR signal component expressed as a fraction of the total water amount. Temperature is measured as normalized functional temperature Tfn = T/273.15 K (T is absolute temperature) and the potential barrier for the motion of water is Ea = Tfn·6.01 kJ/mol, where Tfn is multiplied with the heat of fusion of water. Hydration is grams water/grams protein.
Figure 1. Melting diagram of proteins ubiquitin (UBQ, green circles) and early response to dehydration 10 (ERD 10, red stars), both dissolved in water (50 mg/mL) and that of frozen water under identical conditions (blue squares).
In aqueous solutions, melting (i.e. beginning of molecular motion) of protein-bound water begins at a much lower temperature than the melting of bulk ice. Each protein has a unique MD that results from its individual thermodynamic characteristics. The MD of globular and ID proteins vastly differ. They can be characterized by temperature-independent sections (globular proteins) or without them (IDPs) or can have a small such section (partly IDP).
For UBQ, at melting (-46 °C), the steep step shows that there are water molecules in the first hydrate shell that are bound almost identically, so the relevant molecular surface is equipotential. The potential field of nearly identical elements resembles the feature of hydrogen bridges. The next wide region is a plateau, in this excitation energy region no new water molecules begin to move, because there are no water molecules that are bound by corresponding energy to the protein. The hydrogen bridges here link the bulk of the molecule to a globule. The water molecules, which are bound to surface areas more accessible to water, begin to move at higher potential barriers. For ERD10, the melting occurs at higher temperature (-42 °C) what it is common in IDPs. The plateau after the melting step is significantly narrower than that observed in globular proteins. Then, a phase of continuous rise in MD is observed indicating that a much larger part of the protein surface is accessible to water in ERD10, in an IDP, than in globular proteins. This means that the solvent-accessible surface of ERD10 is highly heterogeneous energetically which is characteristic to IDPs.
Interface properties of nanoscale multilayers. — Artificial multilayers and hetero-structures of nanoscale layers are essential parts of information technology as well as many other technical applications. Since these multilayers are prepared by depositing layer by layer the appropriate amount of different atoms, the interface structure is determined by stochastic processes taking place at the actual, continuously changing surface of the structure. This way the width, the crystal structure, the atomic composition and the associated physical properties of the interface can be largely different when A atoms are deposited over a layer of B atoms or, vice versa, when B is deposited over A.
Figure 1. Concentration profiles across the Fe-on-Ti and Ti-on-Fe interfaces as calculated from MD simulations for different orientations of the substrate layer. The substrate orientations which belong to the different curves and the thickness of the respective interface alloy are indicated in the inset.
In our study, a significant difference of the Ti-on-Fe and the Fe-on-Ti interfaces are undoubtedly revealed both by molecular dynamics simulations of the layer growth (in collaboration with the Research Institute for Materials Science, Centre for Energy Research, HAS) and by experimental investigations. The calculated concentration depth profiles for different substrate orientations are displayed in Fig. 1. The Fe-on-Ti interfaces are slightly intermixed and the interface broadening depends on the orientation of the substrate, although the variation is small. In the Ti-on-Fe case, no atomic mixing can be seen for the Fe(001) substrate orientation, but the interface is slightly wavy which results in a 0.3 nm intermixing in the concentration depth profile. The largest intermixing takes place in case of the Fe(111) substrate orientation, but the interface width (0.7 nm) still remains below the Fe-on-Ti values. Altogether, from the simulations we can conclude that the intermixing is asymmetric with respect to the interchange of the constituents of the film and the substrate.
The experimental studies were made by conversion electron Mössbauer spectroscopy (CEMS) complemented by cross-sectional transmission electron microscopy (TEM) and X-ray reflectometry (XRR). The Ti/Fe/Ti trilayer samples were prepared by evaporation in high vacuum onto Si single crystal substrate using iron metal highly enriched in the 57Fe Mössbauer resonant isotope. In order to determine the phase fractions within the top (Ti-on-Fe) and bottom (Fe-on-Ti) Fe interface, Ti/57Fe/Ti/Si and Ag/57Fe/Ti/Si sample pairs were compared by exploiting the non-mixing property of Fe and Ag. Analyzing the spectra of Ag/57Fe/Ti samples provides information on the Fe-on-Ti interface, since the Ag/Fe interface is chemically sharp and the Ag layer causes only a small and well documented change in the hyperfine parameters of 57Fe within the atomic layers nearest and next-nearest to the Fe-Ag interface. Additional spectral components appearing in the Mössbauer spectra of Ti/57Fe/Ti samples reveal the specific properties of the Ti-on-Fe interface.
Figure 2. Room temperature Mössbauer spectra of Ti/57Fe/Ti and Ag/57Fe/Ti sample pairs with varying thickness of the 57Fe layer, as indicated in the figure. The sub-spectra belonging to paramagnetic amorphous alloy and ferromagnetic crystalline alloy components are indicated by blue and red lines, respectively.
From the Mössbauer results shown in Fig. 2 one can conclude that the bottom and the top interface of a Fe layer in between Ti layers are very different both in the extent and in the ratio of the amorphous and the crystalline alloys appearing at the interface. The Fe-on-Ti interface is about three times thicker than the Ti-on-Fe interface and the ratio of the Fe-rich bcc alloy is larger than that of the Ti-rich amorphous alloy. The Ti-rich amorphous alloy has a higher ratio than the crystalline alloy in the thin Ti-on-Fe interface, which probably does not form a continuous layer.
Surprisingly, the TEM experiments do not show the marked asymmetry of the Fe interfaces, probably due to the averaging of the signal across the specimen thickness in the view direction and a possible modest heating in spite of all the care taken during the sample thinning, but the XRR measurements also indicate a significant asymmetry. The fitted roughness values of 0.86 nm and 0.23 nm result in 2.0 and 0.54 nm “10-90” interface widths for the Fe-on-Ti and Ti-on-Fe interfaces, respectively. The scaling of the interface width may be model dependent, but a strong asymmetry of the Ti-on-Fe and the Fe-on-Ti interface widths is undoubtedly experimentally verified by the Mössbauer and the X-ray reflexivity (XRR) data. The TEM and XRR studies have been carried out in collaboration with the Peter Grünberg Institut, Forschungszentrum Jülich (Jülich, Germany).