Corrosion resistance and glass forming ability of Fe47Co7Cr15M9Si5B15Y2 (M=Mo, Nb) amorphous alloys

Corrosion resistance and glass forming ability of Fe₄₇Co₇Cr₁₅M₉Si₅B₁₅Y₂ (M=Mo, Nb) amorphous alloys

Carlos Alberto Caldas de SouzaI, ^*; Claudomiro Bolfarini^II; Walter José Botta Jr.^II; Luiz Rogério Pinho de Andrade Lima^I; Marcelo Falcão de Oliveira^III; Claudio S. Kiminami^II

^IDepartment of Materials Science and Technology, Federal University of Bahia - UFBA, Rua Aristides Novis, 2, CEP 40210-630, Salvador, BA, Brazil

^IIDepartment of Materials Engineering, Federal University of São Carlos - UFSCar, Rod. Washington Luis, Km 235, CEP 13565-905, São Carlos, SP, Brazil

^IIIDepartment of Materials Engineering, Aeronautics and Automotive, São Paulo University - USP, Av. Trabalhador São Carlense, 400, Centro, CEP 13566-590, São Carlos, SP, Brazil

ABSTRACT

In the present work the effect of substituting Mo with Nb on the glass forming ability and corrosion resistance of Fe-Co-Cr-M-Si-B-Y (M=Mo, Nb) ribbons with high corrosion resistance is investigated. The X-ray powder diffraction pattern indicates that the alloy containing both Nb and Mo presented greater glass forming ability than the alloy containing either of these elements separately. The results obtained indicate that Mo is more effective in enhancing corrosion resistance than the Nb in 4.0 M HCl solution. The alloy containing both Nb and Mo presented greater overall corrosion resistance than the alloy containing only one of these elements.

Keywords: amorphous alloys; corrosion; glass forming ability

1. INTRODUCTION

The presence of a higher molybdenum content in Fe-based amorphous alloys enables the production of nickel free alloys with a high corrosion resistance. This is important due to the fact that nickel released as a result of wear or corrosion may cause environmental and health concerns^1,2.

In recent studies³ it has been reported that a Fe-based bulk metallic glass (BMG) (Fe₄₁Co₇Cr₁₅Mo₁₄C₁₅B₆Y₂) with a diameter of 5mm exhibits high corrosion resistance in simulated body fluids. However, the commercial application of Fe-based bulk metallic glass with a high Mo content is expensive. Therefore it is important to carry out studies to analyze the effect of Mo substitution with other elements for corrosion resistance and glass forming ability. BMG with the greatest corrosion resistance should have a high glass forming ability (GFA), because it has to have a big enough diameter for use in applications such as medical implants. Therefore a study of these alloys should analyze the effect of alloying elements on the GFA.

It has been reported in the literature that the addition of Nb to Fe-Cr-Mo based amorphous alloys is effective in enhancing corrosion resistance. The addition of 2% Nb to an Fe-Cr-Mo-(Nb)-C-B alloy (Fe₄₅Cr₁₆Mo₁₆C₁₈B₅ and Fe₄₅Cr₁₆Mo₁₄Nb₂C₁₈B₅) is effective in enhancing the corrosion resistance in HCl solution⁴ and that an alloy containing both Nb and Mo (0.15 wt.% Mo and 0.15 wt.% Mo) presented greater corrosion resistance than an alloy containing only Mo (0.15 wt.% Mo) in HCl and H₂SO₄ solution⁵. However, the effect of Mo compared to Nb on the corrosion resistance of alloys that present a typical composition of BMG with high corrosion resistance is not clear. Moreover, the effect of Mo compared with Nb on the GFA of these BMGs is not clear.

Si has been added to several Fe-based BMGs such as Fe_57.6C_7.1Si_3.3B_5.5P₈.₇Cr_12.3Mo_2.5Al_2.0Co_1.0^[6] and Fe₅₉.₁C₇.₁Si₄.₄B₆.₅P₈.₆Cr_12.3Al_2.0^[7]. In the latter alloy, it was found that the Si content is high enough to form SiO₂ phases in the passive film which promotes corrosion resistance.

A possible approach to investigate the effect of composition on the GFA and the corrosion resistance of BMG is to make amorphous ribbons of different compositions from the melt-spinning technique and then use the results obtained to design a BMG with high corrosion resistance⁸. In the present study the effect of the substitution of Mo with Nb on the glass forming ability and corrosion resistance of Fe₄₇Co₇Cr₁₅M₉Si₅B₁₅Y₂(M=Mo,Nb) ribbons alloy is investigated.

2. EXPERIMENTAL PROCEDURE

Ribbons of 20 to 30 ∝m thick were produced using melt spinning equipment with a copper wheel rotating at a speed of 55 m/s in an argon atmosphere.

The structure of the melt-spun ribbons was characterized by X-ray diffraction (XRD) using Cu-Kα radiation. The thermal stability of the melt spun sample was characterized by differential scanning calorimetry (DSC). The DSC scans were performed under continuous heating from room temperature to 1273 K with a heating rate of 40 K min ^{- 1}.

The mixing enthalpy values, ∆H, of the alloys analyzed were obtained from the mixing enthalpies of atomic pairs among the elements present in the alloy⁹. The ∆H values of the alloys were calculated considering the stoichiometry of the alloy. To perform these calculations we used the software MSExel.

Corrosion resistance was evaluated by weight loss corrosion tests and potentiodynamic polarization curves in aerated solutions of 4.0 M HCl at room temperature.

The samples for weight-loss measurements were mechanically ground using emery SiC paper (600 grit). Subsequently, the samples were ultrasonically cleaned in acetone for 5 min, rinsed with distilled water and dried. After their initial weight and surface area were measured, they were immersed in the test solution. After being immersed for 13 hours, the samples were cleaned, rinsed and dried. Subsequently the samples were weighed. For the weight measurements a Mettler AB2004 analytical balance was used. Each test was performed with the samples immersed in the solution and the weight loss corrosion test was repeated three times for each condition.

The polarization curves were carried out at a scan rate of 2 mV/s using the alloy ribbons as the working electrode, which was electrically connected to an isolated wire. The auxiliary electrode was a graphite cylinder, and a saturated calomel electrode (SCE) was used as reference. Before each experiment, the sample surface was ground with emery SiC paper (600 grit). A potenciostat-galvanostat AUTOLAB model PGSTAT 100 was used.

3. RESULTS AND DISCUSSION

3.1. Glass forming ability

Figure 1 shows the XRD patterns of the as-cast melt spun ribbons. For Fe₄₇Co₇Cr₁₅Mo_4.5Nb_4.5Si₅B₁₅Y₂ ribbon alloy, as shown in this figure, there is one diffuse intensity peak indicating the formation of an amorphous structure. However, for alloys containing only Nb or Mo, as well as the diffuse intensity peak, there is also the presence of several sharp Bragg peaks, indicating the presence of crystalline phases. Therefore, according to the XDR obtained, the alloy containing both Nb and Mo presented greater glass forming ability than the alloy containing either of these elements.

The glass forming ability, GFA, is a function of liquid phase stability and crystalline resistance⁸. The high supercooled liquid region results in low temperature nucleation, therefore the nucleation kinetics of the crystalline phase is inhibited. The high supercooled liquid region is a consequence of the formation of a highly dense random packed structure¹⁰, which occurs when three empirical rules are satisfied: (1) multi-component alloy systems consist of more than three elements, (2) significantly different atomic radius ratios above about 12% among the main constituent elements are present, and (3) the heats of mixing among their elements are negative. More negative values of mixing enthalpies of atomic par make the bonding nature stronger between these atoms, which results in increased GFA. In the present paper the effect of composition on the GFA of alloys analyzed is discussed in the framework of these three empirical rules.

The atomic radius of the elements Nb and Mo and their difference from the atomic radius of Fe are listed in Table 1. The difference in the atomic radius of Nb with Fe is the greatest. The greater different atomic size ratios among the main constituent elements lead to more efficient packing, thus stabilizing the liquid stability, which favors GFA¹⁰. Therefore, because of the atomic size difference the addition of Nb to Mo can improve the GFA. A larger number of alloying elements could lead to an increase in GFA because the tendency of forming all crystalline phases can be difficult. Thus, from this point of view the addition of Nb to Mo could also improve the GFA.

Table 2 shows the mixing enthalpy values, ∆H, of the alloys analyzed. The Fe₄₇Co₇Cr₁₅Mo_4.5Nb_4.5Si₅B₁₅Y₂ alloy presents a higher negative value of ∆H in comparison with the Fe₄₇Co₇Cr₁₅Mo₉Si₅B₁₅Y₂ alloy, which is coherent with the higher GFA of the alloy containing Nb and Mo. However, the alloy containing only Nb, despite having more negative values of mixing enthalpies compared to the other alloys, has a lower GFA in comparison with the alloys containing Nb and Mo. Therefore, this indicates that as well as the three empirical rules which are related to the liquid phase stability, there are other factors that affect the stability of the alloys analyzed related to the crystalline resistance.

To compare the GFA of Fe₄₇Co₇Cr₁₅Mo_4.5Nb_4.5Si₅B₁₅Y₂ alloy with amorphous alloys obtained as BMG cited in literature, the DSC curve of this alloy was obtained. Figure 2 shows the DSC curve of the Fe₄₇Co₇Cr₁₅Mo_4.5Nb_4.5Si₅B₁₅Y₂ amorphous ribbon. The presence of a glass transition temperature, T_g, characterizes this sample as a "glassy metallic alloy". Apart from T_g, the temperature of crystallization, T_x, and the liquidus temperature, T_l, are given in Table 3, where the γ parameter corresponds to the relationship between T_x and T_g+T_1. This table also shows the values of T_g, T_x, T_l, and the γ of BMG, cited in literature^3,11,12 which has a thickness greater than 1mm. The γ parameter is effective in evaluating the GFA because it incorporates both the liquid phase stability and the crystalline resistance effects⁸. It can also be seen in Table 3 that the γ parameter of the Fe₄₇Co₇Cr₁₅Mo_4.5Nb_4.5Si₅B₁₅Y₂ alloy is higher than several alloys which are obtained as BMG^3,11,12. In future studies the making of Fe₄₇Co₇Cr₁₅Mo_4.5Nb_4.5Si₅B₁₅Y₂ alloy as BMG will be investigated.

3.2. Corrosion resistance

The effect of substituting Mo with Nb on the corrosion resistance of the alloys was evaluated from mass loss measurements. The results, which were obtained in 4.0 M HCl aerated solution, are shown in Table 4.

The results obtained from mass loss indicate that the alloy containing Mo presented a more uniform corrosion resistance than the alloy containing Nb. However, the highest corrosion resistance was observed in the alloy containing both Nb and Mo in relation to the alloy containing either of these elements alone.

Figure 3 shows the potentiodynamic polarization curves of the as-cast alloy in 4.0 M HCl solution. Note that under an applied potential larger than a value about 0.1 V vsHg/Hg₂Cl₂, the current density of the alloy shows a slight variation with potential, which indicates the formation of a passive film. The lower values of current density in passive region, i_p, are related to a higher protective capacity of the passive film. The alloys have different current density values in passive region passivity, i_p, indicating that the passive film of these alloys exhibits different protective ability against corrosion. The i_p values indicate that in relation to the protective ability of the passive film, the alloys can be put in the following ascending order: Fe₄₇Co₇Cr₁₅Nb₉Si₅B₁₅Y₂, Fe₄₇Co₇Cr₁₅Mo₉Si₅B₁₅Y₂ and Fe₄₇Co₇Cr₁₅Mo_4.5Nb_4.5Si₅B₁₅Y₂, alloys. These results are consistent with measures of loss mass indicating that the corrosion resistance of the alloys analyzed is related to the protective ability of the passive film.

Table 5 shows the corrosion potential, E_cor, of as cast alloys obtained from Figure 3. The highest corrosion potential of the alloy contain Nb and Mo, indicating a higher corrosion resistance of this alloy, while the lowest corrosion potential of the alloy contains only Nb which indicates the lower corrosion resistance of this alloy.

The high corrosion resistance of Fe-Cr based amorphous alloys is usually attributed to the formation of the passive film composed mainly of chromium-enriched oxyhydroxide. The effect of other alloying elements such Mo and Nb on corrosion resistance is related to the behavior of chromium-enriched oxyhydroxide film or with the formation of another film.

The effect of Nb in enhancing the corrosion resistance can be attributed to the presence of Nb₂O₅ in the passive film. The presence of this oxide, which was detected by XPS analysis of the passive film in FeNbZrCuB amorphous alloy¹³, increases the susceptibility to passivation and the protective capacity of passive film. In a Fe-Cr based amorphous alloy immersed in 1 M HCl open to air it was found¹⁴ that the addition of Mo promotes the enrichment of the chromium ion in the film greatly. Furthermore, it has been observed that¹⁵ in 6M HCl solution the addition of Mo promotes the corrosion resistance of glassy Fe - Cr based alloys by the formation of Mo oxide film.

The results obtained in this work indicate that the presence of Mo was more favorable than that of Nb for the passivation and inhibition of corrosion in the HCl solution analyzed. However, in presence of both Mo and Nb the corrosion resistance of the alloy is higher than the alloy content only Mo, suggesting a synergetic effect between these elements.

It has been reported¹⁶ for 30Cr-2Mo ferritic stainless steel in HCl solution that in the passive region the inner MoO₂ film is protected by the outer chromium-enriched oxyhydroxide film. This outer film inhibits the dissolution of Mo, and the MoO₂ film acts as an effective barrier against the diffusion of matter through the film. Therefore it is possible that the presence of Nb₂O₅ has the effect of increasing the protective capacity of the outer film and decreasing the active dissolution of the MoO₂ film. However, the occurrence of this behavior for amorphous Fe-Cr based alloys should be evaluated using surface analysis techniques.

It is also possible that the presence of a crystalline phase in samples containing only Mo or Nb affects the corrosion resistance of these alloys. The presence of a crystalline phase in an amorphous matrix can result in the occurrence of galvanic corrosion between these phases. The presence of galvanic corrosion decreases the corrosion resistance in relation to the sample containing Mo and Nb. However, in order to identify the presence of galvanic corrosion it is necessary to determine the composition and the fraction of the crystalline phase. In previous work¹⁷ it was found that the partially crystalline structure favors Si diffusion resulting in a more protective SiO₂ passive film. Therefore it is possible that the partially crystallization has a positive effect on the corrosion resistance. The composition, the fraction of crystalline phase and the effect of crystallization on the Si diffusion will be evaluated in future work.

4. CONCLUSIONS

In the present paper Fe₄₇Co₇Cr₁₅M₉Si₅B₁₅Y₂(M=Mo,Nb) ribbons were obtained. The XDR pattern indicates that the alloy containing both Nb and Mo presents a greater glass forming ability than the alloy containing either of these elements. The presence of these two elements causes the alloy Fe₄₇Co₇Cr₁₅Mo_4.5Nb_4.5Si₅B₁₅Y₂ to exhibit an amorphous structure and high glass forming ability. The results indicate that in the alloys analyzed Mo is more effective in corrosion resistance than Nb in 4.0 M HCl solution. However, the alloy containing both Nb and Mo presents a greater overall corrosion resistance than the alloys containing either of these elements alone.

Received: February 08, 2013

Revised: May 15, 2013

• ¹
  Ruff CA and Belsito DV. The impact of various patient factors on contact allergy to nickel, cobalt, and chromate. Journal of the American Academy of Dermatology 2006; 55:32-39. PMid:16781289. http://dx.doi.org/10.1016/j.jaad.2006.04.015
• ²
  Bal W, Kozøowski H and Kasprzak KS. Molecular models in nickel carcinogenesis. Journal of Inorganic Bichemistry. 2000; 76:213-218. http://dx.doi.org/10.1016/S0162-0134(99)00169-5
• ³
  Wang YB, Li HF, Cheng, Wei SC and Zheng YF. Corrosion performances of a Nickel-free Fe-based bulk metallic glass in simulated body fluids. Electrochemistry Communications. 2009; 11:2187-2190. http://dx.doi.org/10.1016/j.elecom.2009.09.027
• ⁴
  Pang SJ, Zhang T, Asami K and Inoue A. New Fe-Cr-M0-(Nb,Ta)-C-B. Glassy Alloys with High Glass-Forming Ability and Good Corrosion Resistance. Materials Transactions Japan Institute of Metals. 2001; 42:376-379.
• ⁵
  Kiminami CS, Souza CAC, De Andrade LRP, Surinach S, Baro MD, Bolfarini, Botta WJ. Partial crystallization and corrosion resistance of amorphous Fe-Cr-M-B (M = Mo, Nb) alloys. Journal of Non-Crystalline Solids 2010; 356:2651. http://dx.doi.org/10.1016/j.jnoncrysol.2010.04.051
• ⁶
  Wang SL, Li HX, Zhang XF, Yi S. Effects of Cr contents in Fe-based bulk metallic glasses on the glass forming ability and the corrosion resistance. Materials Chemistry and Physics 2009;113:878-883. http://dx.doi.org/10.1016/j.matchemphys.2008.08.057
• ⁷
  Wang SL, Yi S. The corrosion behaviors of Fe-based bulk metallic glasses in a sulfuric solution at 70 °C, Intermetallics. 2010;18:1950-1953. http://dx.doi.org/10.1016/j.intermet.2010.01.020
• ⁸
  Lu ZP, Liu Y, Liu CT. Evaluation of Glass-Forming Ability. In: Bulk Metallic Glasses. Burlington: Elsevier; 2006.
• ⁹
  Inoue A, Takeuchi. Mixing enthalpy of liquid phase calculated by miedemas's scheme and approximated with sub-regular solution model for assessing forming ability of amorphous and glassy alloys. Intermetallics. 2010; 18:1779-1789. http://dx.doi.org/10.1016/j.intermet.2010.06.003
• ¹⁰
  Ma LA, Inoue A. On glass-forming ability of Fe-based amorphous alloys. Materials Letters1999; 38:58-61. http://dx.doi.org/10.1016/S0167-577X(98)00132-3
• ¹¹
  Hidal K, Sekido N, Perepezko JH. Critical coocling rate for Fe₄₈Cr₁₅Mo₁₄Y₂C₁₅B₆ bulk metallic glass formation. Intermetallics. 2006; 14:898-902. http://dx.doi.org/10.1016/j.intermet.2006.01.036
• ¹²
  Ponnambalam V, Poon SJ, Shifet GJ, Keppens VM, Taylor R, Petculescu G. Synthesis of Bulk Metallic Glasses as Nonferromagnetic Amorphous Steel Alloys. Applied Physics Letters 2003;83:1131-1133. http://dx.doi.org/10.1063/1.1599636
• ¹³
  Souza CAC, De Oliveira MF, May JE, Botta FWJ, Mariano NA, Kuri SE, Kiminami CS. Corrosion resistance of amorphous and nanocrystalline Fe-M-B (M=Zr, Nb) alloys. Journal Non Crystalline solids 2000; 273:282-288. http://dx.doi.org/10.1016/S0022-3093(00)00174-5
• ¹⁴
  Tan MW, Akiyma E, Kawashima A, Asami K, Hashimoto K. The effect of air exposure on the corrosion behavior of amorphous Fe-8Cr-Mo-13P-7C Alloys in 1M HCl. Corrosion Science. 1995; 37:1289-1301. http://dx.doi.org/10.1016/0010-938X(95)00035-I
• ¹⁵
  Asami K, Naka M, Hashimoto K, Masumoto T. Effect of molybdenum on the anodic behavior of amorphous Fe-Cr-Mo-B alloys in hydrochlori-acid. Journal Electrochemical Society. 1980;127:2130-2138. http://dx.doi.org/10.1149/1.2129359
• ¹⁶
  Hashimoto K, Asami K, Kawashima A, Habazaki H, Akiyama E.The role of corrosion-resistant alloying elements in passivity. Corrosion Science 2007; 49:42-52. http://dx.doi.org/10.1016/j.corsci.2006.05.003
• ¹⁷
  Souza CAC, Kuri SE, Politti FS, May JE, Kiminami CS. Corrosion resistance of amorphous and polycrystalline FeCuNbSiB alloys in sulphuric acid solution. Journal Non Crystalline solids 1999; 247:69-73. http://dx.doi.org/10.1016/S0022-3093(99)00034-4

Publication Dates

• Publication in this collection
  23 July 2013
• Date of issue
  Dec 2013

History

• Received
  08 Feb 2013
• Reviewed
  15 May 2013