Journal of Chemistry
Volume 2016 (2016), Article ID 9542942, 11 pages
http://dx.doi.org/10.1155/2016/9542942

Research Article

Corrosion Performance of Cu-Based Coins in Artificial Sweat

J. Porcayo-Calderon,1,2 R. A. Rodríguez-Díaz,³ E. Porcayo-Palafox,¹ and L. Martinez-Gomez2,4

¹CIICAp, Universidad Autónoma del Estado de Morelos, Avenida Universidad 1001, 62209 Cuernavaca, MOR, Mexico
²Instituto de Ciencias Físicas, Universidad Nacional Autónoma de México, Avenida Universidad s/n, 62210 Cuernavaca, MOR, Mexico
³Universidad Politécnica del Estado de Morelos, Boulevard Cuauhnahuac 566, Col. Lomas del Texcal, 62574 Jiutepec, MOR, Mexico
⁴Corrosion y Protección (CyP), Buffon 46, 11590 Mexico City, Mexico

Received 8 July 2016; Revised 6 October 2016; Accepted 20 October 2016

Academic Editor: Stefano Caporali

Copyright © 2016 J. Porcayo-Calderon et al. This is an open access article distributed under the Creative Commons Attribution License, which permits unrestricted use, distribution, and reproduction in any medium, provided the original work is properly cited.

Abstract.

The performance of different Cu-based coins in artificial sweat was evaluated. The electrochemical behavior of the coins was determined by potentiodynamic polarization curves, linear polarization resistance, and electrochemical impedance spectroscopy. Regardless of the chemical composition of the Cu-based coins, they showed similar polarization curves; particularly, the observed similarity in the anodic zone suggests that the corrosion mechanism is the same in all cases. The presence of Ni and Zn does not appreciably affect the corrosion resistance of Cu. However, the presence of both elements affects the corrosion resistance of Cu. Electrochemical impedance spectroscopy measurements showed the presence of three time constants with very similar characteristics, again indicating that the main corrosion mechanism is the same in all cases. Equivalent circuits confirmed that the corrosion performance of the Ni-Zn-Cu coins depends on the Zn/Ni ratio, such that decreasing this value decreases the corrosion resistance of the alloy. In general, nickel has a detrimental effect due to the formation of highly soluble Ni-based corrosion products.

1. Introduction

Metallic corrosion originated by metal alloys in contact with human body has been assessed and studied in various researches. Frequently this problem is associated with the tarnishing of the metals as a consequence of the contact of the sweat generated by some parts of human body in contact with pieces of metals or alloys such as coins, jewels, piercing, and earrings. The contact of metals with human sweat can produce undesirable effects. The problem of the metallic corrosion resulting from the formation of corrosion products or liberation of metallic ions originated by the palmar sweat is typical to a great number of industrial occupations [1].

Besides the tarnishing that occurs in metals when exposed to artificial sweat, another aspect concerning human health, which cannot be disregarded, is the detrimental effects on human body that could induce the metal contact with human body. Metallic objects in long periods of contact with human skin may, in fact, produce a toxic effect usually attributed to the release of metal ions. For example, dermal hypersensitivity to Ni or Ni-based alloys is typical. In this case, contact dermatitis is not originated by nickel itself but by the nickel salts which are formed as a result of the contact of human sweat with a metallic object, for example, a necklace, ring, or watch. This phenomenon is developed simultaneously with the corrosion of the object. Once a person acquired nickel allergy, this illness lasts for life [2]. The metallic corrosion induced by human sweat has been known since a century approximately. Various researchers have stated that metals such as Mg, Ni, and stainless steels have experienced pitting and crevice corrosion and hence must be protected with appropriate passive layers for a better performance in service [3].

Human sweat is constituted of greatly variable quantities of primary electrolytes, organic acids and carbohydrates, ionic constituents, nitrogenous substances, amino acids, and vitamins and miscellaneous constituents. Sweat is composed of 99.0–99.5% water and 0.5–1.0% solids. The published literature describing synthetic sweat formulations is diverse and includes many different compounds. All of the published synthetic formulas differ in composition, concentration, and pH. Although there have been few reports concerning the allergy induced by cooper, recently this element has been increasingly recognized as an allergen. Despite the fact that Cu shows allergenic potential lower than the other metals, the allergy induced by this element has an undoubtful clinical importance. Corrosion studies of copper alloys in artificial sweat and in Ringer biological solution showed that, at low potentials, a thin oxide layer was produced but, at nobler potentials, a thick chloride or oxychloride layer was originated. The composition and thickness of the surface layers depended on the stability of complexes of the metal ions with the chloride ions and with the complexing agents present in the artificial sweat. The corrosion products were formed simultaneously with an increment of the dissolution rate of zinc and nickel, and this behavior augmented the allergen problem of nickel in contact with human skin [4–6].

Corrosion of the coins is a common phenomenon during the circulation process, which shortens its service life and reduces its collectable value. Coins come into contact with the skin during the usage process, and sweat left on them becomes a major reason for their tarnishing [7]. A lot of the current coins consist of a ring and an inner pill, and the bimetallic structure of these coins can be a problem because of the metallic enrichment of both pill and ring surfaces [5]. Due to prolonged contact with human skin, the metal dissolution is important because of potential allergic reactions [6].

Therefore, the purpose of this study is to evaluate the corrosion behavior of Cu-based coins in artificial sweat. The electrochemical performance of the coins was determined by potentiodynamic polarization curves, linear polarization resistance, and electrochemical impedance spectroscopy.

2. Experimental Procedure

A batch of 20 Cu-based coins from different countries was corrosion tested by means of electrochemical techniques. However, because in many cases the nominal chemical composition reported does not correspond to the actual chemical composition [8], it was decided to determine the elemental chemical composition by EDS (Energy Dispersive Spectroscopy) technique. Therefore, for electrochemical tests, only the coins with the chemical composition reported in Table 1 were selected. In addition, high-purity copper (99.99 wt.%) (Goodfellow) was evaluated for comparison purposes. The coins consisted of binary, ternary, and quaternary alloy systems, and, for analysis purposes, the alloys only will be referred to by the percentage of alloying elements. In general, Ni-Zn-Cu alloys are known as Alpaca, German Silver, Nickel Bronze, or Nickel Silver, and the Cu6Zn5Al1Sn alloy is known as Nordic Gold.

Table 1: Chemical composition of the Cu-based coins (wt.%).

Alloy
Ni
Zn
Al
Mn
Sn
Cu

Cu
<0.01
<0.01
<0.01
<0.01
<0.01
99.99

23Ni
23.0
—
—
—
—
Bal

32Zn
—
31.5
—
—
—
Bal

10Ni25Zn
9.7
25.5
—
—
—
Bal

13Ni17Zn
13.0
17.0
—
—
—
Bal

15Ni22Zn
14.5
22.0
—
—
—
Bal

8Ni27Zn
8.5
27.0
—
—
—
Bal

6Al2Ni
2.0
—
6.0
—
—
Bal

13Zn6Mn4Ni
3.6
13.3
—
6.0
—
Bal

6Zn5Al1Sn
—
6.0
5.5
—
1.2
Bal

Coins were cut into rectangular form in order to be used as electrode work. They were spot-welded to a Cu wire and then mounted in polyester resin. In this state, the coins were abraded with emery paper down to 1200 SiC, and once the surface of the specimens was metallographically prepared, samples were washed with distilled water and then by ethanol in an ultrasonic bath for 10 minutes.

Corrosive electrolyte used for the electrochemical essays was a synthetic sweat solution which was prepared according to ISO 3160-2 standard [9]. Table 2 shows the chemical composition of the artificial sweat.

Table 2: Chemical composition of artificial sweat (pH adjusted to 4.7 by NaOH).

Compound
Content [g/L]

NaCl
20.0

NH₄Cl
17.5

Acetic acid
5.0

Lactic acid
15.0

Electrochemical tests were performed in a Gamry Interface 1000 Potentiostat controlled by a personal computer and the Framework™ data acquisition software version 7.03. Experiments were performed in a three-electrode electrochemical cell (working electrode, saturated calomel electrode (SCE) as the reference electrode, and a high-purity graphite rod as the auxiliary electrode). In order to obtain the potentiodynamic polarization curves, coins were polarized from −400 mV to 800 mV from value at a scan rate of 1 mV/s. From potentiodynamic polarization curves the values of corrosion potential (), current density (), and Tafel slopes (ba, bc) were determined. Before starting the test, the system was allowed to stabilize for a period of 0.5 hours. For the purpose of obtaining the values of polarization resistance , the linear polarization resistance (LPR) was measured within the interval of ±20 mV from value with a scan rate of 1 mV/s. After determining value, the corrosion current density () was calculated by applying the Stern-Geary equation.

Measurements of electrochemical impedance spectroscopy (EIS) were performed in the frequency range of 0.01 Hz to 100,000 Hz with a perturbation of ±10 mV. In each test performed a new working electrode was used. The tests were performed in triplicate and the values reported are the average of the values obtained.

3. Results and Discussion

3.1. Potentiodynamic Polarization Curves

The polarization curves for Cu and binary alloys are displayed in Figure 1. The polarization curves for pure copper and binary alloys exhibited similar active-passive behavior; similar observations have been reported by other authors [5]. The addition of Ni and Zn to the copper generated a diminution of the corrosion rate; however, the Ni induces a shift of the corrosion potential towards the noble side and the Zn addition conversely. Also, Cu and 32Zn alloy showed a more defined passivation zone compared to 23Ni alloy, and they are passivated at lower overpotentials. The potentiodynamic behaviors of pure copper and the ternary alloys are presented in Figure 2. The variation in the composition of the coins influences the polarization and the passivation nature. The addition of both Ni and Zn induces a decrease of corrosion rate; however it seems that this decrease is dependent on the Zn/Ni ratio. Figure 3 shows the polarization curves for pure Cu together with the quaternary alloys. The anodic branch of Cu and quaternary alloys exhibits an active-passive behavior. Similarly to the polarization behavior of ternary alloys, the addition of the groups of triad elements, Zn-Al-Sn and Zn-Mn-Ni, to the pure Cu, induced a diminution of its corrosion rate. It is worth noticing that the quaternary Cu-Zn-Al-Sn alloys exhibited the lowest corrosion rate.

Figure 1: Polarization curves for the Cu-based binary alloys in artificial sweat at 37°C (dE/dt = 1.0 mV/s).

Figure 2: Polarization curves for the Cu-based ternary alloys in artificial sweat at 37°C (dE/dt = 1.0 mV/s).

Figure 3: Polarization curves for the Cu-based quaternary alloys in artificial sweat at 37°C (dE/dt = 1.0 mV/s).

Table 3 shows the electrochemical parameters of the Cu-based coins determined from polarization curves in the region of ±250 mV with respect to corrosion potential. Importantly, all tested coins show a similar anodic-cathodic behavior, with possible significant variations at overpotentials above 0 volts. The low value of the anodic slopes (60–70 mV) suggests a process of active dissolution due to the formation of soluble species (), and, on the other hand, the presence of the passive region is due to the Cu₂O formation as other authors have suggested [5]. The observed similarity in the anodic zone at potentials above value (up to 300 mV) suggests that the main corrosion mechanism is the same in all cases. Regardless of the number of alloying elements, various studies on copper-based alloys in artificial sweat confirm this assertion [4–7, 10, 11], such that the main corrosion product detected is the cuprous oxide (Cu₂O), besides copper chloride hydroxide (Cu₂(OH)₃Cl). This confirms that the sodium chloride (NaCl) present in the artificial sweat accelerates the anodic reaction process.

Table 3: Electrochemical parameters of the Cu-based coins evaluated in artificial sweat at 37°C.

Alloy

(mV)
ba
(mV/Dec)
bc
(mV/Dec)

(mA/cm²)
(Ohms-cm²)
Zn/Ni
ratio

Cu
−310
300
69
0.01110
2276
—

23Ni
−285
207
67
0.00734
3085
—

32Zn
−347
355
67
0.00854
2950
—

10Ni25Zn
−332
334
72
0.00941
3298
2.5

13Ni17Zn
−301
343
62
0.00810
3236
1.3

15Ni22Zn
−323
230
58
0.00573
2900
1.47

8Ni27Zn
−271
330
75
0.00406
4880
3.37

6Al2Ni
−344
244
70
0.00624
4708
—

13Zn6Mn4Ni
−346
333
68
0.00724
3350
3.25

6Zn5Al1Sn
−360
195
61
0.00362
4152
—

3.2. Linear Polarization Resistance Curves

The variation of corrosion rate in terms of as a function of the immersion time for pure copper together with the binary, ternary, and quaternary alloys exposed to artificial sweat is presented in Figure 4. values were obtained from the Stern-Geary equation, Tafel slopes (from polarization curves), and values. It can be seen that the alloy 15Ni22Zn displayed the highest corrosion rate after the two hours of exposure, while the 13Zn6Mn4Ni and 6Zn5Al1Sn exhibited the lower corrosion rate in terms of , besides the fact that the corrosion current density of these quaternary alloys remained almost constant during the 24 hours of immersion. Also, the corrosion rate of Cu tended to prevail more or less constantly during the whole exposure period. Besides, it is worth noticing that pure copper exhibited a lower corrosion rate than the binary and ternary alloys during the lapse of time from around the 8th hour of exposure up to the end of the linear polarization test. The fact that the corrosion rate of Cu remained more or less constant for 24 hours can be certainly related to the good stability of the Cu₂O passive film formed onto copper surface. It can be observed that the behavior of binary alloys was very similar to that of copper; this may indicate that in long exposures the presence of Ni and Zn does not appreciably affect the corrosion resistance of Cu. However, in the case of ternary alloys the presence of both elements affects the corrosion resistance of Cu, apparently at higher nickel content, and the corrosion rate is increased. Also, corrosion rate of binary and ternary alloys increased while the exposure time had elapsed. This trend could be ascribed to the detrimental effect induced in the protective nature of the copper oxide formed on surface of materials. Specifically, the formation of NiO and ZnO could have produced a reduction of the protective character of the passive film formed on the surface of the alloys. In this sense, Milošev and Kosec [4] studied the nickel ion release associated with nickel allergy which was released by the Cu18Ni20Zn alloy after an immersion period in artificial sweat solution for 30 days. In this research, the authors reported that the surface layer of the alloy was constituted predominantly by Cu₂O, but the presence of NiO and ZnO also was detected; on the other hand, they also found that the Ni concentration into electrolyte is two times higher than that of Cu and Zn, while the concentrations of Cu and Zn were similar, this being due to the formation of Ni-based corrosion products being highly soluble. This may also explain the poor performance of the 2Ni6Al ternary alloy, on one hand the presence of nickel may form soluble corrosion products, and, on the other hand, the formation of aluminum oxide provides little protection because of its low stability in halides-rich electrolytes [12, 13].

Figure 4: Change of values with time for Cu-based coins evaluated in artificial sweat at 37°C.

3.3. EIS Measurements

Impedance spectra for copper and bimetallic alloys after 24 hours of immersion in artificial sweat at 37°C are shown in Figure 5. The analysis of the Nyquist plot shows very similar characteristics for copper and bimetallic alloys, namely, the apparent presence of a capacitive semicircle and the formation of a “tail” of scattered points in the low frequency region, where this scattering may correspond to processes of either diffusion or adsorption of species. Generally the information provided or interpreted from the analysis of the Nyquist plot is limited and can lead to erroneous conclusions, this being mainly because it is impossible to define the frequency range where the surface phenomena are occurring [13–15]. It is therefore important to perform a complete analysis of impedance spectra, that is, taking into account the Bode plots. Furthermore, analysis of the Bode plot is simpler because the dispersion of the experimental data is minimized and the analysis can be performed by frequency range. In particular, the phase angle-frequency relationship clearly indicates how many time constants exist in the system under analysis, and this is impossible to observe from the analysis of the Nyquist plot, especially in the high frequency region. Bode diagrams can be analyzed for frequency ranges, regions of high, intermediate, and low frequency [13–17]. In the high frequency region (1 k–100 kHz), Bode plot shows a horizontal line (high frequency plateau) with the phase angle approaching 0°. This fingerprint is the characteristic response of the electrolytic resistance (solution resistance, ). In the intermediate frequency region (1000 to 10 Hz), the capacitive behavior of the passive oxide and its dielectric properties can be observed. In general, the spectra display a linear slope in log as log () decreases, and the maximum phase angle is reached, and, finally, in the low frequency region () is possible to detect a horizontal line (low frequency plateau with the phase angle approaching 0°) for charge-transfer processes or a deviation from the behavior described for other relaxation processes (mass transfer, adsoption, etc.) taking place at the film-electrolyte interface or into the pores of the surface film. The basic elements that could be observed from Bode diagrams are resistors R (high and low frequencies plateaus), in which and the phase angle is approaching 0°, capacitors C, in which log is a straight line with a −1 slope and the phase angle is approaching 90°, and elements associated with diffusion, in which log has a −0.5 slope and the phase angle is approaching 45°. This mode of interpretation of the impedance spectra is very useful in order to define reliably the equivalent circuits of the system.

Figure 5: Nyquist and Bode plots for the Cu-based binary alloys in artificial sweat at 37°C after 24 hours. Points are the experimental data, and the continuous lines are the fitting data.

Based on this Bode plot it can be observed again that the behavior of copper and bimetallic alloys is very similar. However, from the phase angle-frequency relationship, one can deduce the presence of three time constants (three maximums of phase angle). One of them is at the high-intermediate frequency region (phase angle approaching 0° and formation of the plateau at higher frequencies than 10,000 Hz) with a maximum phase angle of 53–58° at 300–400 Hz. This indicates that the time constant for the three materials has very similar characteristics and may correspond to the presence of a viscous film onto material surface [13, 14], and this may be associated with the formation of hydrides or metallic oxyhydrides as has been previously reported [4, 5, 7, 11]. The second time constant is observed in the region of intermediate-low frequency, where for the bimetallic alloys the maximum phase angle is located approximately 10 Hz and for copper around 2 Hz, in addition the phase angle is less in the case of copper (45°) compared to those of the bimetallic alloys (above 50°), and, on the other hand, the slope of the log |Z|-f relationship is smaller for the case of copper and similar in the case of the bimetallic alloys. These features indicate susceptibility to corrosion of materials in artificial sweat, that is, phase angle values smaller than 90° and slopes smaller than −1, and it means that the protective layer is not an effective insulating barrier and is permeable to ions from solution [18]. Finally, in the low frequency region the third time constant is observed,  Hz; however the phase angle does not tend to zero degrees and the plateau region is not developed. This behavior can be associated with mass transfer processes (diffusion) due to the presence of the viscous film defined by the first time constant [13, 19].

Liang et al. [7] have shown that the main corrosion products developed on a Cu30Zn alloy immersed in artificial sweat are copper chloride hydroxide (Cu₂(OH)₃Cl) and cuprous oxide (Cu₂O). Then it is possible that Zn-based corrosion products are completely soluble in the electrolyte. Similar observations have been reported for Cu-based alloys evaluated in artificial sweat, further indicating that copper chloride hydroxide (Cu₂(OH)₃Cl) is almost insoluble, in contrast to CuCl₂·2H₂O, which is very soluble [5]. Moreover, apparently the presence of nickel into alloy does not significantly improve its corrosion resistance, because Ni-based corrosion products formed are soluble in the electrolyte [11]. It has been reported that the amount of dissolved Ni is twice that of dissolved Cu, and, however, the amount of dissolved Zn is similar to that of dissolved Cu [4].

Figure 6 shows the impedance spectra for copper and ternary alloys in the Nyquist and Bode format after 24 hours of immersion in artificial sweat at 37°C. Analysis of the plots shows similar characteristics in all spectra, and the main differences are the diameter of the capacitive semicircles and the magnitude of the impedance module at low frequency region; this is apparently a function of alloy composition. Furthermore, from the phase angle-frequency relationship the presence of three time constants is also observed. The time constant observed in high-intermediate frequency region shows important differences; that is, the maximum phase angle of the ternary alloys is smaller than that observed for copper. This may indicate that the addition of Zn and Ni influences the corrosion resistance of the alloy, and this is a function of the Zn/Ni ratio added. The interpretation of the three time constants has the same meaning described for those of the bimetallic alloys. It has also been shown that the main corrosion products formed onto Cu-base ternary alloys are copper chloride hydroxide (Cu₂(OH)₃Cl) and cuprous oxide (Cu₂O) [4, 5, 7, 11]. The presence of both Zn- and Ni-based corrosion products is rarely detected because their corrosion products are soluble in the electrolyte, and the presence of chloride ions breaks down the passivation layer; in Cu-Zn-Ni alloys, the concentration of dissolved Ni is the highest one [11]. Therefore, it might be expected that increasing the concentration of nickel in the ternary alloy increases its corrosion rate. Cu-, Zn-, and Ni-based soluble corrosion products are formed according to [5]

On the other hand, corrosion performance of the 2Ni6Al alloy was better than that of both 13Ni15Zn and 15Ni22Zn alloys. This best performance can be associated with the formation of Al⁺ ions (metal/oxide interface) and their migration (oxide/solution interface) to be oxidized to Al³⁺ according to the following [13, 20]:

However, Al-based corrosion products are soluble in the electrolyte, and, on the other hand, in the presence of halides, the Al₂O₃ is frequently subjected to breakdown [12, 13].

Figure 6: Nyquist and Bode plots for the Cu-based ternary alloys in artificial sweat at 37°C after 24 hours. Points are the experimental data, and the continuous lines are the fitting data.

Figure 7 shows the impedance spectra for copper and quaternary alloys in Nyquist and Bode format after 24 hours of immersion in artificial sweat at 37°C. Again it is observed that the impedance spectra are very similar to those observed for copper and alloys both binary and ternary. In this case it is observed that the diameter of the capacitive semicircle as the magnitude of the impedance module at low frequency region of the ternary alloys is greater than those observed for copper. In addition, from the phase angle-frequency relationship the presence of three time constants with identical features is also observed. The corrosion resistance of these alloys was greater than the others previously described. Although the 13Zn6Mn4Ni alloy contains a high percentage of Zn and an appreciable amount of Ni, its performance was better than that of copper. This may be due to the presence of Mn since it is known that the addition of this element increases the pitting corrosion resistance in chloride-rich electrolytes [21]. On the other hand, 6Zn5Al1Sn alloy showed similar behavior to that of 13Zn6Mn4Ni alloy, and this may indicate that the aluminum addition enhances the corrosion performance of the alloy, contrary to that observed with the addition of nickel.

Figure 7: Nyquist and Bode plots for the Cu-based quaternary alloys in artificial sweat at 37°C after 24 hours. Points are the experimental data, and the continuous lines are the fitting data.

Based on that discussed above, it is possible to establish that the equivalent circuit shown in Figure 8 is suitable for modeling the electrochemical behavior of the Cu-based coins tested in artificial sweat at 37°C. Because in the impedance spectra (Figures 5–7) a nonideal frequency response was evident, a constant phase element (CPE) was used in the equivalent circuit. Typically, a CPE is used to compensate for surface irregularities such as roughness or nonuniform distribution of charge transfer. Its impedance value is a function of the frequency and the phase is independent of the frequency:

is a proportional factor which combines properties related to the surface and electroactive species, and it is independent of the frequency; is imaginary number ;   is the angular frequency (), being the frequency; and is related to the slope of the log versus log plot. If is equal to 1, the CPE is an ideal capacitor, where is equal to the capacitance; however, if then the CPE describes a distribution of dielectric relaxation times in frequency space, and if then the CPE represents a Warburg impedance with diffusional character.

Figure 8: Equivalent circuit for Cu-based coins evaluated in artificial sweat at 37°C.

As discussed previously, the impedance spectra indicate the presence of three time constants. The first time constant represents the surface layer (rich in copper chloride hydroxide and/or metallic hydroxides) through which the metal ions diffuse, the second time constant represents the charge-transfer process of the metal dissolution or the oxide dissolution, and the third one represents the diffusional effects due to the presence of the surface layer. From equivalent circuit, represents the CPE of the surface layer, is the resistance of the surface layer, represents the CPE of the double layer capacitor, is the resistance to the charge transfer, and is the element for the finite length Warburg (FLW) diffusion.

where , is the effective diffusion thickness, is the effective diffusion coefficient, and . The impedance spectra were modeled with the Zview software. The evolution of the main fitting parameters obtained is presented in Figures 9 and 10.

Figure 9: and variation against time for Cu-based coins evaluated in artificial sweat at 37°C.

Figure 10: and variation against time for Cu-based coins evaluated in artificial sweat at 37°C.

Figure 9 shows the variation of and for Cu-based coins evaluated in artificial sweat at 37°C. From plot it can be seen that both alloys, 13Ni17Zn and 15Ni22Zn, showed the lowest corrosion resistance, and the corrosion resistance of the quaternary alloys (13Zn6Mn4Ni and 6Zn5Al1Sn) was greater. On the other hand, values observed are lower with respect to those of . This is consistent because represents the resistance of the surface layer through which the metal ions diffuse.

Figure 10 shows plots of the capacitance ( and ) versus time for Cu-based coins evaluated in artificial sweat at 37°C. Capacitance values were obtained from values according to the following equation:

Values of are slightly lower than those of . For Cu and bimetallic alloys, values tend to decrease, and at the same time their values tend to increase. For the others alloys both values of and remain almost constant. This behavior indicates a more active corrosion process both for Cu and for the bimetallic alloys.

Figure 11 shows the variation of values versus time for the Cu-based coins evaluated in artificial sweat at 37°C. values were calculated from values obtained during the modeling process of the impedance spectra, using the same procedure as that employed from LPR values. It can be observed that both the performance ranking and values are similar to those observed from LPR measurements (Figure 4). This indicates that the proposed equivalent circuit is suitable to simulate the impedance spectra and is compatible with the surface processes described above.

Figure 11: variation against time for Cu-based coins evaluated in artificial sweat at 37°C ( values from values of EIS measurements).

Binary alloys have a similar behavior to that observed for copper. Apparently the corrosion resistance of the ternary alloys (mainly the Ni-Zn-Cu ones) depends on the Zn/Ni ratio, such that decreasing this value decreases the corrosion resistance of the alloy. Although the Zn is the the most electronegative element, its presence does not cause a detrimental effect as that observed by the presence of Ni; this could be due to the high solubility of the Ni-based corrosion products. Again it is observed that the 13Zn6Mn4Ni quaternary alloy showed the best performance. It appears that the presence of Mn improved its corrosion performance, regardless of whether the Zn/Ni ratio was similar to that of the 8Ni27Zn alloy. In the case of the 2Ni6Al ternary and 6Zn5Al1Sn quaternary alloys, both have a similar aluminum content; however their corrosion performance was different; again it appears that high corrosion rate of the ternary alloy was due to its Ni content. These observations indicate that nickel has a detrimental effect because it increases the corrosion rate of Cu-based coins, and this is due to the formation of soluble Ni-based corrosion products which cause defect points in the protective layer. Also, this may increase the risk to the health of people allergic to Ni.

4. Conclusions

The corrosion performance of Cu-based coins in artificial sweat was studied by potentiodynamic polarization curves, linear polarization resistance, and electrochemical impedance spectroscopy. The main results showed that the polarization curves of pure copper and Cu-based coins are similar, suggesting that the main corrosion mechanism is the same, regardless of the number of alloying elements. It was found that the impedance spectra are very similar, again regardless of the number of alloying elements; however, the main differences were the diameter of the capacitive semicircles and the magnitude of the impedance module at low frequency region. Impedance spectra indicated the presence of three time constants, where the first one represents a surface layer (rich in copper chloride hydroxide and/or metallic hydroxides) through which the metal ions diffuse, the second one represents the charge-transfer process (metal dissolution or the oxide dissolution), and the third one represents the diffusional effects due to the presence of the surface layer. The agreement of the obtained results of modeling of the impedance spectra with those of the linear polarization resistance measurements indicates that the proposed equivalent circuit is compatible with the surface processes described. In general, binary alloys have a similar performance as copper; however, corrosion resistance of ternary alloys depends on the Zn/Ni ratio and by increasing the Ni content increases the corrosion rate. Ni causes a detrimental effect due to the high solubility of the Ni-based corrosion products. Quaternary alloys showed the best performance; results showed that the Mn enhanced the corrosion performance and that the Al addition does not cause a negative effect as that observed by the Ni addition.

Competing Interests

The authors declare that there is no conflict of interests regarding the publication of this paper.

Acknowledgments

Financial support from Consejo Interinstitucional de Ciencia y Tecnología (CONACYT, México) (Projects 196205, 159898, and 159913) is gratefully acknowledged. The authors acknowledge the support of I. S. Arizmendi-Carbajal and E. Y. Bautista-Flores (Universidad Politécnica del Estado de Morelos).

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