{'fraction_non_alphanumeric': 0.02971960201576431, 'fraction_numerical': 0.018520911401128482, 'mean_word_length': 4.9640380169535065, 'pattern_counts': {'":': 0, '<': 0, '<?xml version=': 0, '>': 0, 'https://': 0, 'lorem ipsum': 0, 'www.': 0, 'xml': 0}, 'pii_count': 0, 'substrings_counts': 0, 'word_list_counts': {'cursed_substrings.json': 1, 'profanity_word_list.json': 0, 'sexual_word_list.json': 0, 'zh_pornsignals.json': 0}}
Impact of Pretreatment of Metal Glass Fe70Cr15B15 on Anodization in 1-butyl-3-methylimidazolium Tetraﬂuoroborate Ionic Liquid

: The impact of preliminary treatment (mechanical abrasion; chemical etching and anodization in ionic liquid) on the surface structure and corrosion behavior of Fe70Cr15B15 metal glass was studied. The detachment of the anodic oxide ﬁlm from untreated Fe-amorphous alloy under anodization in ionic liquid was observed for the ﬁrst time. The formation of hexagonal nanostructures (cells) on the surface of the Fe70Cr15B15 alloy after mechanical abrasion and following anodization in 1-butyl-3-methylimidazolium tetraﬂuoroborate ([Bmim][BF 4 ]) ionic liquid was also detected for the ﬁrst time. Electrochemical corrosion of the initial and pretreated amorphous alloy was tested in a Na 2 SO 4 aqueous solution. The resistance to corrosion was found to be enhanced slightly after mechanical abrasion. The sample with hexagonal nanostructures obtained after anodization of the mechanically abraded sample demonstrated a more signiﬁcant anodic shift in the corrosion potential ( E corr = + 379 mV) compared with that for the initial alloy ( E corr = − 125 mV).


Introduction
In recent years, the chemistry of metal glasses (amorphous alloys) has been intensively developed owing to the discovery of new properties and applications of these materials. Compared with crystalline materials, the liquid-like atomic structure, with no grain boundaries, dislocations, and phase segregation confers bulk metallic glasses superior mechanical properties involving high fracture strength and large elastic deformation [1]. Fe-based metal glasses were found to exhibit a higher strength, hardness, and corrosion resistance than other amorphous and crystalline alloy materials [2]. Amorphous alloys are widely applied in micro-and nano-electromechanical devices due to their outstanding physical and electrochemical properties [3]. Amorphous alloys are of particular interest as medical materials, for which one of the requirements is resistance to various types of corrosion [4,5]. and non-aqueous media has been poorly studied to date and the formation of nanostructures on this solid has not been considered.
The aim of this work was to elucidate the effect of preliminary treatment (mechanical abrasion; chemical etching in an acetone solution of citric acid, benzoic buffer, sodium hydroxide) on the corrosive properties of amorphous alloy Fe70Cr15B15 in an aqueous 0.1 M Na 2 SO 4 solution (pH = 7) and the surface topographical texture of the pretreated samples after anodic oxidation in 1-butyl-3-methylimidazolium tetrafluoroborate ([Bmim] [BF 4 ]) ionic liquid (IL).

Materials and Methods
[Bmim] [BF 4 ] ionic liquid (purity 99.5%) (ABCR GmbH, Karlsruhe, Germany) was used as purchased. The content of water in IL was 5000 ppm (determined by titration according to Fischer by the 899 Coulometer (Metrohm)). Acetone, benzoic and citric acids, sodium hydroxide, sodium sulfate, and sodium benzoate (all with a purity of 99.9+%) were used as received.
The rotating-cylinder method has been applied for the preparation of the amorphous iron-chromium-boron alloy. The starting materials were B (purity 99.99%), Fe (purity 99.95%), and electrolytic Cr (purity 99.95%). The amorphous Fe70Cr15B15 alloy (AA) was prepared in an electric arc furnace in an argon atmosphere with the triple remelting procedure. Impinging a stream of molten alloy on the outer surface of a rotating cylinder in an argon atmosphere was used to convert the obtained crystalline sample to the amorphous state [22]. The ribbon parameters were: width 7-10 mm, thickness 10 µm. The preparation conditions were determined by the necessity to obtain the material in the amorphous state.
The surface morphology and composition of the samples were studied using a scanning electron microscope EVO-50 Zeiss with an EDX (Energy-dispersive X-ray spectroscopy) analyzer (Zeiss AG, Jena, Germany) and an inverted routine microscope for materials ZEISS Axio Vert.A1 (Zeiss AG, Jena, Germany).
The X-ray phase analysis was carried out by means of a DRON-3 diffractometer (Cu-K α ) (Bourevestnik, JSC, St. Petersburg, Russia). According to X-ray phase analysis, a blurred halo is observed. The blurred halo indicates the amorphous state of this alloy. The amorphous state of the alloy was confirmed by differential scanning calorimetry. DSC (Differential scanning calorimetry) measurements were carried out with a Jupiter STA 449 F1 apparatus (NETZSCH GmbH, Selb, Germany) in He. The temperature scanning rate was 20 K min −1 . The apparatus was calibrated by the melting temperatures of standard samples of metals (In, Sn, Bi, Zn, Al, Au) provided by the NETZSCH company. Calibration and experiment were performed under the same conditions.
The electrochemical experiments were carried out in three-electrode cells (the volume of the ionic liquid was 2 mL) with non-separated compartments under galvanostatic conditions (the current density i = 12.5 mA cm −2 ) using an AUTOLAB PGSTAT 302N potentiostat (Metrohm AG, Herisau, Switzerland). Electrochemical anodizing was carried out at room temperature in air for 100 s in The areas of the working and auxiliary AA electrodes were 0.4 and 0.6 cm 2 , respectively. The distances between the working and auxiliary electrodes, auxiliary and reference electrodes, and working and reference electrodes were 0.3-0.4, 0.5-0.6, and 0.3-0.4 cm, respectively. The electrodes were rinsed with acetone in an Elmasonic P 30H ultrasonic cleaning unit (Elma) at 37 kHz and dried in Ar until they reached constant weight. A silver wire was used as a quasi-reversible reference electrode. The potential of the silver wire was constantly calibrated vs. the standard fc/fc + electrode.
Corrosion tests were carried out under natural aeration in 0.1 M Na 2 SO 4 prepared by using reagent-grade chemicals and deionized water. The volume of the solution was 100 mL. The area of the working AA electrode was 0.4 cm 2 . The linear polarization curves were measured at room temperature with a potential sweep rate of 1·10 −3 V s −1 , starting from the cathodic region. An Ag/AgCl electrode was used as a reference electrode. The corrosion potential (E corr ) and polarization resistance (PR) were calculated using the standard procedure (Nova 2.1.3, Linear polarization, Corrosion rate analysis) for the AUTOLAB PGSTAT 302N potentiostat. Corrosion measurements were performed at least in duplicate to ensure the repeatability of the results.
Before anodizing, the samples were sonicated in acetone for 1 h at room temperature. Pretreatment of AA included mechanical abrasion, chemical etching with solutions of citric acid (0.013 and 1.6 M) and a benzoic acid buffer solution (BB) [benzoic acid (0.013 M) and sodium benzoate (0.013 M)] in acetone; sodium hydroxide in water (7.75 M) and in acetone (0.013 M). The samples being exposed to etching solutions for 1 h were rinsed with acetone and dried in air.
The working electrode was abraded with emery paper for 5 min, as in, e.g., [13]. The sample without preliminary treatment was anodized just after the treatment with acetone.

Anodic Oxidation of Fe70Cr15B15 in Ionic Liquid (IL)
Particularly interesting data were observed for electrochemical oxidation of AA in IL. The results of anodizing of the Fe70Cr15B15 amorphous alloy in IL were found to depend on the state of the electrode surface. Figure 1a demonstrates galvanostatic transients obtained for the untreated, mechanically abraded, and chemically pretreated samples, with the latter alloy being treated with citric acid, benzoic buffer, and NaOH acetone solutions. The samples were exposed to reagents in acetone for 1 h at room temperature to react with surface oxide films. It should be noted that anodization in IL influences the surface state differently depending on the pretreatment procedure. Only for the mechanically abraded sample, a peculiar pattern was found on the metal glass surface. Anodization of this sample in IL led to the generation of hexagonal nanostructures (cells) (Figure 2a).
The variations in the potential during anodization of the AA sample preliminarily etched with a solution of sodium hydroxide in water and acetone are in accordance with the results obtained for the samples preliminarily treated with citric acid. The preliminary treatment of AA with alkaline solutions leads to the pitting of the electrode surface in both cases. The solvent nature (acetone/water) does not influence the results of anodization in IL. The surface of AA also undergoes effective etching. The pretreatment of AA with citric acid and sodium hydroxide solutions in acetone results in the total or partial removal of the surface oxide films, inasmuch as the oxides and hydroxides of Fe and Cr are known to be amphoteric. The reagents presumably act as a mild acid and base in a nonaqueous solvent.
It is seen from the potential-time transients that there are nonmonotonic upward slopes in the potential (E) with time for the unpretreated AA electrode (see 1, Figure 1a). This feature may be accounted for by the occurrence of two processes:

•
The increase in the oxide film thickness on the surface of the electrode as a result of the electrochemical galvanostatic oxidation; • The discontinuity of the oxide film due to a loss of the adhesion with the metal surface (detachment) [23].
The increase in the oxide film thickness brings about an electrode potential growth. The following detachment of the anodic oxide film from the alloy results in the electrode potential drop due to the development of the oxide-free metal surface. Detachment of the anodic oxide films from the metal surface was observed for aluminum and its alloys, e.g. [24][25][26]. Detachment of the anodic oxide film from the amorphous Fe-alloy was detected for the first time. The surface state of the sample under consideration at this moment is shown in Figure 1b.
At the same time, no distinct transient drops in the potential for the samples pretreated with citric acid, a BB acetone solution, and NaOH solutions in acetone and water were detected (Figure 1a curves  3-7). The pretreatment of AA samples leads to the total or partial removal of the native oxide film. Therefore, the following anodization of the etched AA samples gives rise to the electrochemical oxide film and results in a monotonic potential increase.
It should be noted that anodization in IL influences the surface state differently depending on the pretreatment procedure. Only for the mechanically abraded sample, a peculiar pattern was found on the metal glass surface. Anodization of this sample in IL led to the generation of hexagonal nanostructures (cells) (Figure 2a). It should be noted that anodization in IL influences the surface state differently depending on the pretreatment procedure. Only for the mechanically abraded sample, a peculiar pattern was found on the metal glass surface. Anodization of this sample in IL led to the generation of hexagonal nanostructures (cells) (Figure 2a).
The variations in the potential during anodization of the AA sample preliminarily etched with a solution of sodium hydroxide in water and acetone are in accordance with the results obtained for the samples preliminarily treated with citric acid. The preliminary treatment of AA with alkaline solutions leads to the pitting of the electrode surface in both cases. The solvent nature (acetone/water) does not influence the results of anodization in IL. The surface of AA also undergoes effective etching.  The variations in the potential during anodization of the AA sample preliminarily etched with a solution of sodium hydroxide in water and acetone are in accordance with the results obtained for the samples preliminarily treated with citric acid. The preliminary treatment of AA with alkaline solutions leads to the pitting of the electrode surface in both cases. The solvent nature (acetone/water) does not influence the results of anodization in IL. The surface of AA also undergoes effective etching.
It is reasonable to connect the deterioration of the anticorrosive properties of AA after pretreatment with a change in the surface composition of the electrode due to its enrichment in Cr, as has been found for austenitic stainless steel [27,28]. The bulk Cr:Fe ratio for the initial alloy is 1: 4.67. The surface Cr:Fe ratio for the initial alloy according to EDX analysis is 1: 4.32 (Table 1). The change in the surface composition in comparison with the bulk composition of the electrode probably occurs due to some surface enrichment in Cr. According to the EDX data, there was no considerable enrichment on the surface of AA during anodizing in IL. This fact allowed us to exclude the contribution of this mechanism (Table 1). Table 1. EDX data for the surface composition of the initial sample and those obtained after anodizing of amorphous Fe70Cr15B15 alloy (AA) in ionic liquid (IL) used without pretreatment (untreated) and after pretreatment with benzoic acid buffer solution (BB) (etched), etched and anodized in IL.

Sample
Mean It is of particular interest to discuss the electrochemical behavior of the preliminarily abraded electrode during anodizing in IL. Lower electrode potentials for this sample are evidently connected, with more effective removal of the natural oxide films by mechanical treatment. However, a key difference was observed in the surface texture of AA after galvanostatic anodization in IL. In this case, according to the SEM data, nano-cells were detected on the surface of the electrode (Figure 2a). A similar phenomenon was observed earlier on the surface of various electrodes during anodization in ionic liquids [17][18][19] and other non-aqueous electrolytes [29][30][31].
Therefore, the galvanostatic anodic oxidation leading to self-organization of the surface (in the form of hexagonal nano-cells) was detected. The use of hydrophobic IL is a crucial point. A hydrophobic IL containing a low content of water (below 5000 ppm) is an excellent medium for the formation of cellular nanostructures [16]. The pretreatment procedure is of utmost importance as well.
Therefore, the preliminarily abraded amorphous Fe70Cr15B15 alloy is the only sample that reveals the formation of hexagonal nanostructures on its surface appearing after anodization in IL.

Electrochemical Corrosion in an 0.1 M Na 2 SO 4 Aqueous Solution
Iron and chromium are known to form solid solutions with unlimited solubility in the solid phase. This feature favors the production of binary alloys exhibiting high electrochemical corrosive stability in aqueous solutions. Indeed, crystalline Fe-Cr alloys show a significant electrochemical resistance to corrosion both with oxygen and hydrogen depolarizations.
The rate of electrochemical corrosion of single-phase systems drops dramatically with an increase in the atomic percentage of the alloying component (Cr) according to the n/8 Tammann's rule (n = 1, 2, 3, . . . , 7) [32]. This implies that Fe-Cr binary systems with concentrations of the alloying component close to the first (n = 1) or the second threshold (n = 2) of stability should reveal a significant increase in corrosion potential.
The anticorrosive features of iron alloys are also known to be dependent on the surface solid solution crystallinity. The crystalline single-phase alloys exhibit better anticorrosive properties due to the homogeneity of the crystalline phase. The anticorrosive properties of 303,304 steels alloyed with Cr and amorphous Fe-Cr alloys show significant stability with respect to electrochemical corrosion as a result of the passive oxide film development [33,34].
Amorphous iron alloys containing more than 8 at. % of chromium were reported to also show a high resistance to electrochemical pitting corrosion due to formation of a CrO x OH y ·nH 2 O protective film [34].
The composition and structural properties of the AA under study [35] are indicative of the high anticorrosive stability against aqueous solutions. Electrochemical oxidation of AA in aerated aqueous 0.1 M Na 2 SO 4 solutions was studied for:
Sample chemically etched and electrochemically treated in IL; 4.
Sample mechanically abraded and electrochemically treated in IL. The following anodization of this sample in IL results even in a much more pronounced decrease in the corrosion potential (−439 mV) (Figure 3a, curve 3). It is reasonable to note that the surface oxide film removal due to the treatment with the BB solution leads also to a decrease in the polarization resistance (Table 2).
Changes in the surface state of the sample after chemical etching with BB followed by electrochemical oxidation in the 0.1M Na2SO4 aqueous solution are depicted in Figure 3b,c. As seen in Figure 3c, anodic oxidation of the amorphous Fe70Cr15B15 alloy (preliminarily treated with BB) in an aqueous solution results only in deep pitting of the surface, as was observed for glassy Fe-40Ni-14P-6B alloy [36]. The following anodization of this sample in IL results even in a much more pronounced decrease in the corrosion potential (−439 mV) (Figure 3a, curve 3). It is reasonable to note that the surface oxide film removal due to the treatment with the BB solution leads also to a decrease in the polarization resistance (Table 2). Changes in the surface state of the sample after chemical etching with BB followed by electrochemical oxidation in the 0.1 M Na 2 SO 4 aqueous solution are depicted in Figure 3b,c. As seen in Figure 3c, anodic oxidation of the amorphous Fe70Cr15B15 alloy (preliminarily treated with BB) in an aqueous solution results only in deep pitting of the surface, as was observed for glassy Fe-40Ni-14P-6B alloy [36].
In contrast, the corrosion potentials after mechanical abrasion (−79 mV) and particularly after the subsequent electrochemical oxidation of the abraded electrode (+379 mV) in IL are significantly shifted to the anodic region. The PR value also decreases compared to that for the initial sample.
The substantial improvement in the anticorrosive properties of the abraded and anodized metal glass is accompanied by certain surface structure changes. This is clearly demonstrated in Figure 2b, in which hexagonal nanostructures are observed on the surface of the abraded Fe70Cr15B15 metal glass electrode after being anodized in IL.
It should be noted that self-organized hexagonal nano-cells are formed on the surface of the abraded Fe70Cr15B15 metal glass only after anodization in IL (Figure 2a). The following electrochemical oxidation of this sample in the 0.1 M Na 2 SO 4 aqueous solution brings about an oxide film growth on the background of the hexagonal nano-cells (Figure 2b).
The deterioration of the anticorrosive properties of AA after etching by BB originates from the partial removal of the incoherent oxide film. The subsequent anodization of the etched alloy electrode results in the detachment of the protective oxide film from the alloy and in the increase in the corrosion current due to the developing oxide-free metal surface. This phenomenon was also observed earlier for other samples [26,37].
In accordance with the results of polarization measurements, only the alloy covered with a natural passive oxide film demonstrates a relatively high corrosion potential and low current of corrosion (Table 2). Perhaps the protective effect of the surface oxide film is due to the homogeneity of the alloy surface texture and higher rate of the oxide growth connected with the highly active amorphous structure.
The natural oxide film formed on the AA surface is heterogeneous and consists of layers [33,37]. The presence of different oxide films is seen from the shape of the linear curves for the untreated amorphous Fe70Cr15B15 alloy (curve 1, Figure 3a). As compared with the similar curves obtained for the etched and anodized electrodes, there are some waves (at +0.32 and +0.82 V) on curve 1 for untreated AA attributed to the consecutive removal of the surface oxide layers [33,34].
The order of the removal of the oxide films from the AA surface and the sequence of the sudden potential changes obviously depend on the properties and types of oxide films. The differences in the corrosion potentials for the chemically etched (curve 2, Figure 3a) and etched and anodized (curve 3) electrodes point to the difference in the alloy surface composition. The larger cathodic shift in the corrosion potential in the case of the chemically etched and anodized AA ( Table 2) is likely due to the presence of a highly coherent oxide layer being left over the surface after chemical etching (curve 2). Otherwise, the corrosion potentials obtained for the etched (−293 mV) and for the etched and anodized (−439 mV) electrodes would be the same.
Thus, the chemical etching only results in a partial removal of the less cohered external oxide layer. The subsequent anodizing of the alloy that is preliminarily chemically etched in IL leads to the oxide-free surface and the following corrosion potential growth is connected with the electrochemical oxidation of the alloy.
In addition to the compact passive film, the nanostructure also plays a critical role in the excellent corrosion resistance of the eutectic high entropy alloy (EHEA). Pit nucleation is essentially an event of electrochemical instability and originates from the coupling of local anodic sites in the presence of perturbations in an electric field and the concentration of attacking ions [38].
Therefore, the untreated three-component amorphous alloy is stable enough relative to the corrosion compared with the amorphous Fe x Cr 1-x alloy studied earlier [34].

Conclusions
The influence of the preliminary treatment of the amorphous Fe70Cr15B15 alloy on the surface morphology and electrochemical behavior in aqueous solutions of Na 2 SO 4 and in IL 1-butyl-3-methylimidazolium tetrafluoroborate was established by means of linear polarization investigations and galvanostatic anodic oxidation studies.
The treatment of the amorphous Fe70Cr15B15 alloy with citric acid, benzoic acid buffer, and NaOH acetone solutions results in total removal of the natural oxide films. The total removal of the natural oxides before anodization in aqueous solutions and IL results only in etching (no cellular nanostructure) of the alloy surface. The decay of the continuity of the superficial oxide films (mechanical abrasion) favors the appearance of hexagonal nanostructures (cells) on the electrode surface after the subsequent anodization in IL. The sample with hexagonal nanostructures obtained after anodization of the mechanically abraded sample demonstrates a more significant anodic shift in the corrosion potential (E corr = + 379 mV) compared with that for the initial alloy (E corr = −125 mV). The formation of hexagonal nanostructures provides a better possibility to produce uniform oxide layers (due to the nanostructure) compared to the other samples. The significant anodic shift in the corrosion potential is observed for this reason. The detachment of the anodic oxide film from untreated Fe-amorphous alloy under anodization in ionic liquid was revealed for the first time.