Effect of Cu<sup>2+</sup> on Corrosion Behavior of A106B Carbon Steel and 304L Stainless Steels in Seawater

Fang, Kewei; Li, Chengtao; Dong, Shuai; Zhang, Dubao; Wu, Xiangfeng; Hu, Hongxiang

doi:https://doi.org/10.1155/2021/6661872

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Abstract Introduction Results and Discussion Conclusion Data Availability Conflicts of Interest Acknowledgments References Copyright Related Articles

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Volume 2021 | Article ID 6661872 | https://doi.org/10.1155/2021/6661872

Effect of Cu²⁺ on Corrosion Behavior of A106B Carbon Steel and 304L Stainless Steels in Seawater

Kewei Fang,¹Chengtao Li,¹Shuai Dong,¹Dubao Zhang,¹Xiangfeng Wu,¹and Hongxiang Hu²

Academic Editor: Jian Chen

Received05 Aug 2021

Accepted24 Aug 2021

Published06 Oct 2021

Abstract

The corrosion behaviors of A106B carbon steel and 304L stainless steel (SS) in seawater with different Cu²⁺ concentrations were studied by the immersion test and the potentiodynamic polarization test. The results showed that with the increasing Cu²⁺ concentration, the mass lot rates of A106B and 304L SS all increased in the immersion test, and compared with A106B, the mass lot rates of 304L SS were all smaller. In the potentiodynamic polarization test, following the concentration of Cu²⁺ increased, the corrosion potential of A106B firstly shifted negatively; then, when Cu²⁺ increased to 100 ppm, the polarization curve moved to the upper right direction; namely, both the corrosion potential and corrosion electrical density increased. The corrosion potential of 304L SS increased with the increasing Cu²⁺, and the passive region was reduced; the pitting sensitivity improved.

1. Introduction

The important plant water system (SEC system), i.e., the safety plant water system, function was to transfer the heat from the structures, systems, and components related to safety to the final sink-seawater under normal operation and accident conditions. The system consisted of SEC pumps, shellfish traps, various values and pipes, and RRI/SEC plate heat exchangers [1].

In the existing nuclear power plants, the SEC pipes were made of stainless steel [2, 3], carbon steel lined with coating, rubber, plastic or cement mortar, and resin pipes. During the service of the SEC pipes, the addition of the cupric fungicide to prevent microbial corrosion, the corrosion of copper components, or other reasons could lead to the local enrichment of Cu²⁺ in the SEC system and the precipitation of Cu on the surface of components; the interaction between Cu²⁺ and seawater may accelerate the corrosion of SEC system material, even leading to the breaking of the components and inducing the addition of Cu²⁺ into the secondary circuit system.

Presently, the corrosion of steels in seawater had been widely investigated all over the world [4–20], and the influence of Cu²⁺ on material corrosion is mainly focused on different materials in nonseawater environment, such as steel [21–30], aluminum alloy [31, 32], 690 alloy [33], and copper alloy [34]. However, the works focused on the corrosion behavior of steels in seawater containing Cu²⁺ and the influence of the Cu²⁺ and copper oxides on the corrosion of the equipment in the secondary circuit system were little reported [35]. Therefore, the corrosion behaviors of steels in seawater containing Cu²⁺ were studied by the immersion test, potentiodynamic polarization, and SEM observation, which could provide a certain basis and guidance for the operation of nuclear power stations.

2. Experimental Detail

The materials used in the present work were A106B carbon steel and 304L stainless steel (SS). The chemical compositions (wt.%) of A106B and 304L SS are listed in Table 1. As shown in Figure 1(a), the optical microstructure (OM) of A106B was ferrite and pearlite biphasic structure, among which the black lamellar structure was pearlite phase. The microstructure of 304L SS is listed in Figure 1(b), which was a typical austenitic structure with twins. A106B was eroded by 4% nitrate alcohol and ethanol, respectively; then, they were analyzed by an optical microscope. 304L SS was electrolytically etched in 10% oxalic acid reagent at 10 V for 60 s for the microstructural observations.

(a)

(b)

The materials were cut into sheets with a dimension of . Prior to the experiment, the surface of the samples was polished to 800# with sandpaper, then cleaned with deionized water, acetone, and anhydrous ethanol, then air-dried. The quality was weighted and size measured after the samples. The test solutions were seawater solutions with different concentrations of Cu²⁺; the concentrations of Cu²⁺ were 10, 50, 100, 500, and 1000 ppm, respectively; the test period was 168 h, and the test temperature was 50°C. Before and after the immersion tests, the specimen was weighed using an electronic balance with an accuracy of 0.01 mg. The corrosion rate () was calculated based on the mass loss, , using Equation (1) after a given period [1]:

where represent the mass loss of the five samples used (mg), is the surface area of the sample (10.4 cm²), and is the total test duration (168 h).

The exposed area of the sample in the test of the potentiodynamic polarization was 1 cm². Before the experiment, the surface of the samples was polished down to 800# with sandpaper and then cleaned using deionized water, acetone, and anhydrous ethanol. The potentiodynamic polarization test was carried out using the CS310 electrochemical workstation; the detailed introduction of the electrochemical experimental design methods was presented in the literature [1, 2]. The test solution was consistent with the immersion test, and the test temperature was 25°C. Before the test, the working electrode was immersed in the solution for 30 min and then −400 mV below the corrosion potential and terminated when the current density of 10 mA/cm² was reached with a scanning rate of 20 mV/min.

3. Results and Discussion

3.1. Corrosion Morphologies of A106B

Figure 2 presents the corrosion morphologies of A106B after the immersion test in tested solutions. A106B presented uniform corrosion in seawater of different concentrations of Cu²⁺. After the test in solution without Cu²⁺, the matrix surface of the sample was relatively flat; with the addition of Cu²⁺, small and shallow pits appeared, and with the increase of the concentration of Cu²⁺, the amount of the pits increased. After the test, a small number of tan corrosion products adhered to the matrix surface.

(a)

(b)

(c)

(d)

(e)

(f)

Figures 3 and 4 present the corrosion morphologies of 304L SS after the immersion test. The corrosion pits all appeared on the matrix surface of the samples; without the Cu²⁺, there were only few shallow pits, and the size of the pits were small, with a few microns; with the increase of the concentration of Cu²⁺, the amount and size of the pits both increased; the maximum depth of the pits in seawater of 500 ppm and 1000 ppm Cu²⁺ could be as deep as 1000 and 1500 microns, respectively.

(a)

(b)

(c)

(d)

(e)

(f)

(a)

(b)

3.2. Corrosion Rate of A106B and 304L SS

Figure 5 presents the mass loss rate of A106B and 304L SS after the immersion test. As is seen in Figure 5, the mass loss rate of A106B largely increased with the increase of the concentration of Cu²⁺. The mass loss rate in seawater without the Cu²⁺ was 0.163 g·m^–2·h^–1; the mass loss rate in seawater of 10, 50, 100, 500, and 1000 ppm Cu²⁺ increased by 0.23, 0.97, 2.14, 4.12, and 8.47 times, respectively. The mass loss rate of 304L SS in seawater without the Cu²⁺ is about 0.0012 g·m^–2·h^–1. However, the mass loss rate in seawater of 10 ppm, 50 ppm, 100 ppm, 500 ppm, and 1000 ppm Cu²⁺ increased by 6, 67, 139, 404, and 591 times, respectively. The presence of Cu²⁺ significantly increased the corrosion rate of 304L SS in seawater.

3.3. Corrosion Morphologies of A106B and 304L SS

Figure 6 presents the SEM surface morphologies of A106B after the immersion test in seawater solution of different concentrations of Cu²⁺. The morphologies of different concentrations of Cu²⁺ had no significant difference; the matrix was relatively flat with some small particles. The EDS analysis showed that the matrix surface mainly consisted of Fe and a small amount of O, the content of Cu was little, which indicated that the precipitated Cu and other corrosion products were very loose, and there were basically no residual corrosion products attached on the matrix. Figure 7 presents the EDS result on the surface of A106B, which indicated that the surface of A106B was rich in Fe and O elements.

(a)

(b)

(c)

(d)

(e)

(f)

Figure 8 shows the SEM microscopic morphology of 304L stainless steel after the corrosion test in seawater of different concentrations of Cu²⁺. Without the Cu²⁺, the pitting corrosion initiation formed, the concentration of Cu²⁺ increased to 10 ppm, and a small number of corrosion pits with a few microns to tens of micron in size appeared; with the increase of the concentration of Cu²⁺, the size of the corrosion pits increased; when the concentration of Cu²⁺ increased to 100 ppm, the size of the corrosion pits had been more than 100 microns, which indicated the sample suffered from heavy pitting corrosion.

3.4. Potentiodynamic Polarization

Figure 9 shows the potentiodynamic polarization curves of A106B in tested solutions. As is seen in Figure 10, the concentration of Cu²⁺ had a significant influence on the corrosion behavior of A106B. With the increase of the concentration of Cu²⁺, the corrosion potential decreased and the corrosion current density increased firstly; compared with that without Cu²⁺, of A106B in tested solutions initially shifted to a more negative potential and then subsequently increased to negative potential when the concentration of Cu²⁺ is higher than 100 ppm. The corrosion potential () for A106B in seawater without Cu²⁺ is -648 mV_SCE; when the concentration of Cu²⁺ increased to 10 ppm, decreased by about 10 mV; when increased to 50 ppm, it decreased by 65 mV_SCE; when increased more than 100 ppm, the potentiodynamic polarization curves moved significantly up to the right; namely, both the corrosion potential and the corrosion current density largely increased. Meanwhile, with the increase of the concentration of Cu²⁺, the cathode control became the diffusion control of Cu²⁺.

The corrosion potential was a mixed potential formed by the coupling of anodic dissolution reaction and cathode depolarizer reduction reaction, which was between the anodic reaction equilibrium potential and cathode reduction reaction equilibrium potential. In seawater solution without Cu²⁺, the cathode reaction was the reduction of O₂, as the equilibrium potential of electrode reaction was higher than that of ; when the Cu²⁺ was added, the cathode reactions on the surface of A106B included both the reduction reactions of O and Cu²⁺; namely, in the seawater containing Cu²⁺, there were two depolarizing agents, O₂ and Cu²⁺, which made the A106B suffer from corrosion.

The equilibrium potential (for standard hydrogen potential) of electrode reaction could be calculated through the Nernst equation: where is the equilibrium potential of electrode reaction and is the standard potential of electrode reaction , where is ideal gas constant, 8.314 J/(K·mol), is thermodynamic temperature (K), is Faraday constant, 96500 C, and is the concentration of Cu²⁺ (mol/cm³).

As known, was known as 0.345 V (SHE), was 0.401 V (SHE), so when the concentration of Cu²⁺ was low, the cathode reaction was mainly the reduction of O₂; the two intercoupling cathode reactions accelerated the anodic dissolution reaction rate; meanwhile, a small amount of Cu was precipitated on the surface of the sample, which formed the Fe-Cu corrosion galvanic cells and also accelerated the anodic dissolution reaction. With the increase of the concentration of Cu²⁺, increased constantly and finally increased higher than , the cathode reaction was changed from mainly the reduction of O₂ to mainly the reduction of Cu²⁺, a large amount of Cu was precipitated on the surface, and a large number of Fe-Cu corrosion galvanic cells were formed, which largely increased the anodic dissolution rate. This was also the reason why there were many small corrosion pits on the surface, but the macroscopic corrosion morphology was characterized by uniform corrosion.

Figure 10 shows the potentiodynamic polarization curves of 304L SS in tested solutions. As can be seen, with the increase of the concentration of Cu²⁺, the potentiodynamic polarization curves moved up to the right; the corrosion potential and corrosion current density increased. Due to the existence of the pass passivation film, the anodic dissolution rate was quite low and the anode reaction equilibrium potential had no significant change; with the increase of the concentration of Cu²⁺, the cathode reaction rate was accelerated and the cathode reaction equilibrium potential increased, and an anode reaction and two cathodic reactions coupled and polarized each other, finally leading to the increase of the corrosion potential and corrosion current density. Meanwhile, a small amount of Cu was precipitated on the surface of the sample, which also formed the Fe-Cu galvanic cells, making the stability of the passivation film decreased; the more the number of Fe-Cu galvanic cells increased, the more obvious the stability of the passivation film decreased; thus, the passivation zone significantly narrowed, and the pitting corrosion sensitivity significantly increased; once the passivation film was broken locally, the fresh metal substrate was exposed; the corrosion pits formed and developed under the combined action of Cl^- and Cu²⁺.

4. Conclusion

(1)The results of the immersion test showed that A106B presented uniform corrosion in seawater of different concentrations of Cu²⁺; with the increase of the concentration of Cu²⁺ to 10 ppm, 50 ppm, 10 0 ppm, 500 ppm, and 1000 ppm, the corrosion weight loss rate increased by 0.23, 0.97, 2.14, 4.12, and 8.47 times, respectively(2)304L SS presented pitting corrosion in seawater of different concentrations of Cu²⁺; with the increase of the concentration of Cu²⁺ to 10 ppm, 50 ppm, 100 ppm, 500 ppm, and 1000 ppm, the corrosion weight loss rate increased by 6, 67, 139, 404, and 591 times, respectively; the amount and size of the corrosion pits both increased. Compared with the behaviors of A106B in the immersion test, the mass lot rates of 304L SS were all lower(3)The results of potentiodynamic polarization curves of A106B showed that with the increase of the concentration of Cu²⁺, the corrosion potential decreased firstly; when increased to more than 100 ppm, both the corrosion potential and the corrosion current density largely increased. Meanwhile, the cathode reaction was altered from mainly the reduction of O₂ to mainly the reduction of Cu²⁺(4)The results of potentiodynamic polarization curves of 304L showed that with the increase of the concentration of Cu²⁺, the corrosion potential and corrosion current density increased, the passivation zone significantly narrowed, and the pitting corrosion sensitivity significantly increased

Data Availability

The data used to support the findings of this study are available from the corresponding authors upon request.

Conflicts of Interest

The authors declare that they have no conflict of interest.

Acknowledgments

The authors acknowledge the financial support of the National key research and development program (No. 2016YFB0700404).

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Copyright © 2021 Kewei Fang 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.

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Characterization of the Corroding Interface using Scanning Techniques 2021

Effect of Cu2+ on Corrosion Behavior of A106B Carbon Steel and 304L Stainless Steels in Seawater

Abstract

1. Introduction

2. Experimental Detail

3. Results and Discussion

3.1. Corrosion Morphologies of A106B

3.2. Corrosion Rate of A106B and 304L SS

3.3. Corrosion Morphologies of A106B and 304L SS

3.4. Potentiodynamic Polarization

4. Conclusion

Data Availability

Conflicts of Interest

Acknowledgments

References

Copyright

Effect of Cu²⁺ on Corrosion Behavior of A106B Carbon Steel and 304L Stainless Steels in Seawater