Home Corrosion behavior of GH3535 alloy in KCl–MgCl2 eutectic salts purified with magnesium
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Corrosion behavior of GH3535 alloy in KCl–MgCl2 eutectic salts purified with magnesium

  • Na Li , Qi Liu EMAIL logo , Huiqin Yin , Changjian Ling , Yang Wang and Zhongfeng Tang EMAIL logo
Published/Copyright: June 26, 2023
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Corrosion Reviews
From the journal Corrosion Reviews Volume 41 Issue 5

Abstract

The corrosion behavior of GH3535 alloys in KCl–MgCl2 eutectic salts with or without magnesium (Mg) was investigated using the static immersion tests. The effect of purification treatment on the corrosion of GH3535 specimens was also evaluated by the different analysis. The KCl–MgCl2 salts purified with Mg and reducing service temperature can slow down the corrosion rate of GH3535 specimens. Infrared spectra results showed that purification treatment reduced the content of crystal water in the KCl–MgCl2 salts. The difference of hydrate content in KCl–MgCl2 salts and the diffusion rate of Cr in alloy are the main reasons for the change of GH3535 specimens corrosion rate.

Keywords: corrosion; GH3535 alloy; KCl–MgCl2; molten salt; purification

1 Introduction

As a kind of medium with low price, good high temperature stability, and excellent heat transfer performance, KCl–MgCl2 salts have a wide application prospect in the next-generation concentrated solar power (CSP) and molten salt reactor (MSR) (Liang et al. 2021; Magnusson et al. 2020; Xu et al. 2018, 2022, 2023), and it was identified as heat transfer candidates for use in the intermediate loop (Lin et al. 2020; Lu et al. 2023). However, most of chloride salts have strong corrosivity at high temperature, and corrosion of structural materials has hence been recognized as the main challenge for realizing their commercial application (Guo et al. 2018; Li et al. 2022; Villada et al. 2021). In recent years, the corrosion behavior of structural materials (mainly commercial metal alloys) in contact with molten chloride salts at high temperatures has been widely investigated (Ding and Bauer 2021; Lambrecht et al. 2022; Liu et al. 2017; Sarvghad et al. 2018). Fe-based and Ni-based alloys have been selected as the candidate materials for next generation CSP because of their good high temperature strength and corrosion resistance (Li et al. 2023; Lu et al. 2023). The corrosion behavior of Fe-based alloy (SS347/310/316/P91) and Ni-based alloy (Hastelloy N, C-276, C-22, Incoloy 800 H, GH4033 and GH4169, Inconel 625, 600, 702, Haynes230, 224) in chlorine salts has been investigated (Ding et al. 2018; Grégoire et al. 2020; Lambrecht et al. 2022; Peng and Reddy 2019; Sun et al. 2018). Results showed Ni-based alloys had relatively better corrosion resistance than Fe-based alloys. It is generally recognized that the corrosion of the alloys in molten chloride salt was attributed to the selective dissolution and/or oxidation of the element Cr in alloy (Guo et al. 2020; Liu et al. 2021; Ong et al. 2020; Yang et al. 2020), the chromium content in the alloy is an important factor affecting the corrosion resistance of alloys in molten salts (Liu et al. 2017; Sun et al. 2018). Sun et al. (2018) found that the performance sequence of four commercial nickel-based alloys in NaCl–KCl–MgCl2 salt is Hastelloy N>C276>C22>Haynes 230. After 400 h corrosion at 700 °C, the corrosion depth of Hastelloy N is about 15 μm, while that of Haynes 230 is as high as 100 μm. The corrosion rate of metals in NaCl–KCl–MgCl2 salt increases with the increase of Cr content.

In addition to the composition and structure of the alloy, it was found that the corrosion behavior of the alloy in the salts is closely related to the quality of the molten salt (Ding et al. 2018; Guo et al. 2018; Lambrecht et al. 2022; Ong et al. 2020). The type and concentration of impurities have a great influence on the corrosion performance of salt. Metallic impurities, such as FeCl3 and CrCl3, will accelerate the corrosion rate in Fe–Cr–Ni alloys (Ghaznavi et al. 2022). For KCl–MgCl2 salt, Since MgCl2 is very sensitive to moisture, the hydration of MgCl2 at ambient temperature and the further hydrolysis reactions during heating are inevitable (Guo et al. 2020; Liu et al. 2021; Sun et al. 2018; Yang et al. 2020). Water and oxygen impurities in salt and secondary products of chemical reactions, such as HCl, Cl2, H±, OH−, and magnesium-hydroxy ions will aggravate the corrosion of chloride salts to the alloy (D’Souza et al. 2021; Lehmusto et al. 2021; Li et al. 2021; Wu et al. 2020). Therefore, reducing the concentration of impurities in salt and controlling the content of water and oxygen are helpful to reduce the corrosiveness of salt (Mortazavi et al. 2022). It is found that the concentration of metal impurity ions in salt can be reduced by adding reducing metal elements and electrochemical control potential method (Ding et al. 2021; Lambrecht et al. 2022), utilization of an inert atmosphere (e.g. Ar or N2) as ullage gas and including a drying step upon heating of the salt mixture can reduce the dehydrolysis reaction to produce the corrosive impurities and limit the corrosivity of chloride melt (Guo et al. 2020; Ong et al. 2020).

For CSP equipment, higher operating temperatures can realize more efficient conversion of thermal energy to electrical energy (Lambrecht et al. 2022; Villada et al. 2021). However, using molten chloride salts at higher temperatures will increase corrosiveness of containers and structural materials. The dissolution rate of Cr in Incoloy 800H in LiCl–KCl salt at 700 °C is more than twice that at 650 °C (Mortazavi et al. 2022). When the working temperature of chloride salt (e.g., ZnCl2/KCl/NaCl) is setting too high, such as 800 °C, Even materials with excellent corrosion resistance, such as Hastelloys C-22 and C-276, cannot meet the requirements of industrial applications (Ding et al. 2018).

A great deal of work has been done on the corrosion of alloys in chloride salt, but most of them only study the influence of a certain factor on its corrosion behavior. In practice, various factors are often coupled together.

In this work, in order to evaluate the effect of molten salt purity and temperature on chloride corrosion, GH3535 (UNS N10003) alloy with good corrosion resistance is taken as the representative, and static immersion corrosion tests were undertaken to compare the corrosion behavior of alloy in KCl–MgCl2 eutectic salts with different temperatures and purification degrees. Scanning electron microscope (SEM) was used to analyze the micro-structures of corroded GH3535 alloy. The related salt chemistry was characterized by the inductively coupled plasma emission spectroscopy (ICP-OES) and infrared spectrum (IR). The mechanism of corrosion temperature and purification treatment was discussed affecting the corrosion behavior of the GH3535 specimens in KCl–MgCl2 salts. The systematic study of the corrosion behavior of alloy in different environments is helpful to understand its corrosion mechanisms and accelerates the application of Ni–Mo–Cr alloy in CSP and MSR with KCl–MgCl2 as heat transfer medium.

2 Materials and methods

2.1 Materials

Unpurified KCl–MgCl2 eutectic salts (A, 62.5–37.5 wt%) were prepared by melting after blending with commercial KCl and MgCl2 (greater than 99.5 wt% purity) (Guo et al. 2020), supplied by Sinopharm Chemical Reagent Corporation (Shanghai, China). Purified KCl–MgCl2 eutectic salts (B, 62.5–37.5 wt%) were prepared by Mg metal reduction method at 600 °C for 24 h under Ar gas (inside the glove box), then filtered with a Ni net. ICP-OES and ion chromatography were used to determine cationic and anion impurities concentration in KCl–MgCl2 eutectic salts, respectively, and the main impurities concentration in unpurified KCl–MgCl2 eutectic salts (A) and purified KCl–MgCl2 eutectic salts (B) were shown in Table 1. The residual free H2O and oxygen in KCl–MgCl2 eutectic salts were determined through the Karl–Fischer titration and LECO oxygen analyzer, and the concentrations of residual H2O and oxygen in A salts were 300 ppm and 1520 ppm.

Table 1:

The main impurities in A and B salts pre-corrosion tests (mg/kg).

Salts Impurity
Fe Cr Ni Mn Si SO42− NO3− NO2− PO43−
A 24.69 0.38 0.32 0.36 1.35 155.3 188.1 152.4 130.6
B 0.12 – – – 0.02 – – – –

  1. “−” is in concentrations below the quantitative limits of detection for ICP-OES.

The Ni–Mo–Cr alloy named as GH3535 in China was provided by Shanghai Institute of Applied Physics, Chinese Academy of Science, and the chemical composition was shown in Table 2. The 15.0 mm × 10.0 mm × 3.0 mm specimens were abraded with an emery paper to 1500 grit and polished with 0.05 μm Al2O3 powder, followed by cleaning with deionized water and alcohol and then drying.

Table 2:

Chemical compositions of GH3535 alloy (wt.%).

Alloy Fe Cr Ni Mn Si Al Co Cu Mo C
GH3535 4.24 6.96 Bal. 0.51 0.27 0.15 <0.01 0.06 17.00 0.06

2.2 Static corrosion test

High temperature static corrosion of GH3535 specimens in A or B salts was conducted on a furnace connected with the glove box in Ar (99.995 %) and the content of water and oxygen were controlled below 10 ppm by a gas purification system. The schematic diagram of the experimental set up is shown in Figure 1. Static corrosion of GH3535 specimens were carried out in KCl–MgCl2 eutectic salts at 500 °C, 600 °C, and 700 °C for 100 h in Ar. The corroded GH3535 specimens were cleaned using deionized water and dried with cold air. In order to reduce the deviation, three specimens were placed in each crucible, and three corroded specimens were analysed and the average value of them was taken as the result.

Figure 1: Schematic diagram of the corrosion experimental test.
Figure 1:

Schematic diagram of the corrosion experimental test.

2.3 Characterization methods

Weight changes caused by corrosion of the GH3535 specimens could be got by the following Equation (1) (Lambrecht et al. 2022).

(1)Δm=ma−mbS

where Δm is the mass change per unit area (unit: mg/cm2), ma and mb stand for the mass of GH3535 specimens pre- and post-corrosion, respectively. S is the surface area of alloy pre-corrosion. Weight change is the mean of three parallel GH3535 specimens.

The microstructure morphology changes of the corroded GH3535 specimens were analyzed using SEM (Merlin Compact) coupled with an energy dispersive X-ray spectrometer (EDS), The alloy specimens were embedded in epoxy resin to form a module, which was then ground and polished to obtain sequential cross-sections. The cationic impurities of salts were analyzed using ICP-OES. Additionally, specimens of various salts were analyzed by IR spectra to determine the chemical composition and structure of the salts. IR spectroscopy acquisition was performed with a PerkinElmer Frontier FT-IR/NIR spectrometer. The salt specimens for IR spectra analysis were ground into powders in an agate mortar and then spread on a diamond window.

3 Results

3.1 Weight change

All alloy specimens have weight loss after static corrosion test. The weight change of GH3535 specimens in unpurified KCl–MgCl2 eutectic salts (A) and purified KCl–MgCl2 eutectic salts (B) at 500, 600 and 700 °C for 100 h under Ar were shown in Figure 2. It was found that the purification of salt and the change of corrosion temperature would affect the weight loss of GH3535 specimens. Weight loss of corroded GH3535 specimens in B salts was lower than that A salts at a given temperature. At the same time, it could be found that the corrosion weight loss of the alloy increased with the increase of temperature, whether purified or not. Weight loss of GH3535 specimens immersed in A and B salts were 0.35 mg/cm2 and 0.09 mg/cm2 at 500 °C, respectively. When the temperature is 600 °C, the weight loss of GH3535 specimens is 1.01 mg/cm2 for A salts and 0.67 mg/cm2 for B salts, respectively. While the weight loss of GH3535 specimens immersed in A and B salts were 2.97 mg/cm2 and 2.44 mg/cm2 at 700 °C, respectively.

Figure 2: Weight changes of GH3535 specimens immersed in unpurified KCl–MgCl2 salts (A) and purified KCl–MgCl2 salts (B) at 500, 600, and 700 °C under Ar for 100 h.
Figure 2:

Weight changes of GH3535 specimens immersed in unpurified KCl–MgCl2 salts (A) and purified KCl–MgCl2 salts (B) at 500, 600, and 700 °C under Ar for 100 h.

3.2 Microscopic morphology analysis

The cross-sectional SEM images of the corroded GH3535 specimens in A and B salts for 100 h at three different temperatures were shown in Figure 3. All alloys suffered corrosion attack. The increase of temperature intensifies the corrosion of the alloy, while the purification treatment weakens the corrosion of KCl–MgCl2 eutectic salts to the alloy. When the GH3535 specimens were corroded in the unpurified KCl–MgCl2 (A1, A2, and A3) for 100 h, the surface of corroded GH3535 specimens began to appear uneven and a few corrosion holes began to appear at 500 °C. At 600 °C, the number of corrosion holes in the surface area increased, and the diffusion depth of holes within the matrix also increased. When the corrosion temperature rises to 700 °C, many large holes appear on the cross section, and the holes formed by corrosion extend to the matrix along the grain boundary more obviously. Microscopic investigations indicated that the corrosion hole depth is 1.8 µm and 6.8 µm respectively at 500 °C and 600 °C, while it has reached 20.9 µm after 100 h of corrosion at 700 °C. When the GH3535 specimens were corroded in the purified KCl–MgCl2 (B1, B2, B3) for 100 h. The corrosion of the GH3535 also intensified with the increase of KCl–MgCl2 salt temperature and the depths of corrosion holes were about 0.9 µm, 4.5 µm and 17.3 µm respectively at 500 °C, 600 °C and 700 °C. When judging from the hole size or the depth distribution of the corrosion holes, the corrosivity of the purified KCl–MgCl2 salts is weaker than that of the untreated KCl–MgCl2 salts.

Figure 3: Cross-sectional SEM images of corroded GH3535 specimens exposed in A salts (A1, A2, A3) and B salts (B1, B2, B3) under Ar for 100 h at 500 °C (A1, B1), 600 °C (A2, B2), and 700 °C (A3, B3).
Figure 3:

Cross-sectional SEM images of corroded GH3535 specimens exposed in A salts (A1, A2, A3) and B salts (B1, B2, B3) under Ar for 100 h at 500 °C (A1, B1), 600 °C (A2, B2), and 700 °C (A3, B3).

3.3 Cr depletion distance analysis

In line-scanning mode, SEM-EDS was used to analyze the Cr depletion depths in the surface layer of corroded GH 3535 alloy. It corresponds to the depth when the Cr concentration is lower than that in the alloy. The results are shown in Figure 4. The Cr depletion depths of the corroded GH3535 exposed in the unpurified KCl–MgCl2 salts (A) is 1.9 µm, 7.1 µm and 21.6 μm at 500 °C, 600 °C, and 700 °C, respectively. While the Cr depletion depths of the corroded GH3535 exposed in the purified KCl–MgCl2 salts is 0.9 µm, 4.6 µm and 17.8 μm at 500 °C, 600 °C, and 700 °C, respectively. The influence trend of molten salt temperature and salt purification on the depletion depth of Cr is similar to the distribution law of holes on the surface of the alloy. With the increase of salt temperature, the depletion depth of Cr in the corroded GH3535 increases, and salt purification can reduce the depletion depth of Cr on the GH3535 alloy surface.

Figure 4: Cr depletion depths of corroded GH3535 exposed in (A) and (B) salts under Ar for 100 h at 500 °C, 600 °C, and 700 °C.
Figure 4:

Cr depletion depths of corroded GH3535 exposed in (A) and (B) salts under Ar for 100 h at 500 °C, 600 °C, and 700 °C.

3.4 ICP-OES analysis

The content of alloy elements selectively dissolved into molten salt can be used to characterize the degree of corrosion of the alloy. Researches showed that among chromium containing alloys, chromium atom was the most vulnerable to selective corrosion by high-temperature molten salt (Guo et al. 2020; Liu et al. 2021; Sun et al. 2018; Yang et al. 2020). Cr ions contents in the unpurified and purified KCl–MgCl2 salts after corrosion were determined and shown in Figure 5. Since the raw materials for preparing KCl–MgCl2 salts were analytical pure reagents, the Cr ions content was only about 0.38 mg/kg even in the unpurified KCl–MgCl2 salts (A). After purification, the content of Cr ions in purified KCl–MgCl2 salts (B) were even lower (Table 1). When GH3535 specimens were immersed in high-temperature molten KCl–MgCl2 salts, Cr atoms in the alloy would be selectively dissolved and entered the molten KCl–MgCl2 salts. The analysis of molten KCl–MgCl2 salts after corrosion test showed that the Cr ions concentrations in the unpurified (A) and purified KCl–MgCl2 salts (B) increased by 0.018 mg/kg and 0.013 mg/kg at 500 °C after 100 h, respectively. The Cr ions concentrations in the unpurified and purified KCl–MgCl2 salts post-corrosion increased by 0.045 mg/kg and 0.033 mg/kg at 600 °C after 100 h, respectively. When the KCl–MgCl2 salts temperature rises to 700 °C, the Cr ions concentration in the unpurified KCl–MgCl2 salts has reached 0.177 mg/kg, while the Cr ions concentration in the purified KCl–MgCl2 salts is only 0.094 mg/kg. To some extent, the concentration of Cr in the GH3535 specimens corroded into KCl–MgCl2 salts increased exponentially with the increase of molten salt temperature.

Figure 5: Concentrations of dissolved Cr elements from the GH3535 in the KCl–MgCl2 eutectic salts under Ar at different temperatures for 100 h through ICP-OES analyses.
Figure 5:

Concentrations of dissolved Cr elements from the GH3535 in the KCl–MgCl2 eutectic salts under Ar at different temperatures for 100 h through ICP-OES analyses.

3.5 IR spectra analysis

To further investigate the effect of purification treatment on the KCl–MgCl2 salt, the IR spectra of the unpurified KCl–MgCl2 salts(A) and purified KCl–MgCl2 salts(B) were characterized as shown in Figure 6. The IR spectra of unpurified KCl–MgCl2 salts showed a significant broad absorption peak at 1025 cm−1, which was the characteristic peak due to water molecules of hydration (Angelis et al. 2022). While that of purified KCl–MgCl2 salts(B) showed small fluctuation around 1025 cm−1. It showed that high temperature purification treatment can greatly reduce the trace crystal water in unpurified KCl–MgCl2 salts.

Figure 6: IR spectra of the (A) unpurified KCl–MgCl2 salts and (B) purified KCl–MgCl2 salts.
Figure 6:

IR spectra of the (A) unpurified KCl–MgCl2 salts and (B) purified KCl–MgCl2 salts.

4 Discussion

The corrosion of alloy in high-temperature molten chloride salts is mainly manifested by the selective dissolution of Cr and other elements in the alloy into the molten salts (Guo et al. 2020; Liu et al. 2021; Sun et al. 2018; Yang et al. 2020). In molten salt, the corrosion rate of the Hastelloy N alloy depends on the reaction rate of Cr at the interface between molten salt and alloy, and the outward diffusion rate of Cr in the alloy (Guo et al. 2020; Liu et al. 2021).

The reaction rate of Cr at the interface between molten salt and GH3535 is mainly related to the type and concentration of impurities in the KCl–MgCl2 salt. Although the raw materials of analytical purity were used for the unpurified KCl–MgCl2 salts, because MgCl2 salt was easy to absorb water to form hydrate, the crystal water could not be completely removed by high-temperature mixing melting under Ar (Ding et al. 2018; Mortazavi et al. 2022; Wu et al. 2020). The signal of the existence of crystal water in unpurified KCl–MgCl2 salts could still be detected by IR. It is known that the decompose of hydrates of MgCl2 at high temperature would form HCl, H2O, MgOHCl as shown in Reactions 1 and 2 (Li et al. 2022; Sun et al. 2020; Zhang et al. 2019). Cr on the surface of GH3535 will react with these corrosive impurities, so that chromium in the surface layer will be corroded and dissolved into molten salt, as shown in Reactions 3 and 4 (Sun et al. 2020; Wu et al. 2020).

Metal Mg reduction method is used for the purification of KCl–MgCl2 salts (Hanson et al. 2022; Li et al. 2022; Sun et al. 2020; Zhang et al. 2019). As showed in Reactions 5, 6, and 7 in the purification process, Mg atom will react with these corrosive impurities in unpurified KCl–MgCl2 salts After purification, the concentration of highly corrosive substances such as HCl, H2O, and MgOHCl in salts were reduced, which greatly weakened the corrosion of KCl–MgCl2 salts to the GH3535, Therefore, after 100 h of corrosion at three temperatures, the concentration of Cr ions in all purified magnesium chloride salts was lower than that of the unpurified salt.

MgCl2·xH2O = MgOHCl + HCl + (x − 1) H2OReaction 1
MgOHCl = MgO +HClReaction 2
Cr + 2HCl = CrCl2+H2Reaction 3
Cr + 2MgOHCl = 2MgO + CrCl2 + H2Reaction 4
Mg + 2HCl = MgCl2 + H2Reaction 5
Mg + H2O = MgO + H2Reaction 6
Mg + 2MgOHCl = 2MgO + MgCl2 + H2Reaction 7

During the corrosion process, due to the concentration difference between the surface and GH3535 substrate, Cr will continuously diffuse from the inside to the outside of the alloy, and the outward diffusion rate of chromium in GH3535 is directly related to the diffusion coefficient. Based on Fick’s law of diffusion, the diffusion distance (x) in the cross-section could be expressed empirically as (Ai et al. 2021; Sun et al. 2018).

(2)x=2Deff×t

where Deff is the effective diffusion coefficient of alloying elements, and t is the immersion time for corrosion.

The Deff near the GBs could be calculated by a weighted mean of the diffusion coefficient at alloy matrix lattice DV and that at GBs DB, Investigation showed that the lattice and grain boundary diffusion coefficients of Cr in GH3535 are expressed as, respectively (Sun et al. 2018).

DV=1.8×10−2exp(−340KJmol−1RT)m2s−1
DB=8.2×10−8exp(−335KJmol−1RT)m2s−1

The grain boundary diffusion coefficient of Cr in GH3535 alloy is much higher than the lattice diffusion coefficient. In this way, the chromium at the grain boundary diffuses outward faster, and the surrounding elements cannot diffuse in time, so that holes are formed at the grain boundary. DB increases exponentially with temperature, so does Deff and distribution depth of surface holes. For the maximum Cr depletion layer in purified salt, the effective diffusion coefficient (DCr-eff) of Hastelloy N is estimated. At 500 °C, 600 °C, and 700 °C, the Deff of Cr in the Hastelloy N alloy are 5.6 × 10−19 m2/s, 1.5 × 10−17 m2/s, and 2.2 × 10−16 m2/s, respectively.

Because the raw material of KCl–MgCl2 eutectic salt is AR grade, the whole preparation process and corrosion test of KCl–MgCl2 eutectic salt are carried out in high purity argon, and the impurity content of unpurified KCl–MgCl2 salt is not high. Therefore, at a lower temperature (500 °C), the concentration of Cr ion in corroded KCl–MgCl2 salt is not high, but with the increase of salt temperature, the concentration of Cr ion in corroded KCl–MgCl2 salt increases rapidly, which is the same as the depth of Cr depleted layer in corroded alloy, and increases exponentially with the increase of temperature. It can be inferred that the whole corrosion process was controlled by the diffusion rate of Cr in GH3535, and the influence of temperature change on the GH 3535 corrosion is greater than the purity of salt.

5 Conclusions

The high temperature corrosion resistance of the GH3535 alloy in unpurified and purified KCl–MgCl2 salts was studied through static immersion corrosion under Ar at 500 °C, 600 °C, 700 °C for 100 h. Mg reduction and purification treatment reduced the concentrations of impurities in the unpurified KCl–MgCl2 salt and weakened its corrosion effect to GH3535 specimens. The outward diffusion of Cr atoms in the GH3535 is the controlling factor of corrosion in the KCl–MgCl2 salts, and it increased with the temperature from 500 °C to 700 °C.

Corresponding authors: Qi Liu and Zhongfeng Tang, Shanghai Institute of Applied Physics, Chinese Academy of Sciences, Shanghai201800, China, E-mail: ,

Funding source: National Key R&D Program of China

Award Identifier / Grant number: 2021YFB3700603

Funding source: DNL Cooperation Fund, CAS

Award Identifier / Grant number: DNL202012

  1. Author contributions: All the authors have accepted responsibility for the entire content of this submitted manuscript and approved submission.

  2. Research funding: Supported by the National Key R&D Program of China (2021YFB3700603) and DNL Cooperation Fund, CAS (DNL202012).

  3. Conflicts of interest: The authors declare that they have no known competing financial interests or personal relationships that could have appeared to influence the work reported in this paper.

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Received: 2022-07-05
Accepted: 2023-05-07
Published Online: 2023-06-26
Published in Print: 2023-10-26

© 2023 Walter de Gruyter GmbH, Berlin/Boston

Articles in the same Issue

  1. Frontmatter
  2. Review
  3. The role of acid–base interactions in the pitting corrosion of aluminum: a review
  4. Original Articles
  5. The effect of Pd and Ni coatings on hydrogen permeation experiments of as-quenched martensitic steel
  6. Effect of surface machining on the environmentally-assisted cracking of Alloy 182 and 316L stainless steel in light water reactor environments: results of the collaborative project MEACTOS
  7. Microbiologically influenced corrosion behavior of 304 stainless steel in ZnO nanofluids
  8. Hairy bamboo leaf extract as an eco-friendly corrosion inhibitor for L245N steel in CO2-saturated oilfield produced water
  9. Using electrochemical testing and modeling to assess the efficiency of a water-soluble inhibitor on the corrosion of 6061Al-15 % (v) SiC (p) composite
  10. Corrosion behavior of GH3535 alloy in KCl–MgCl2 eutectic salts purified with magnesium
  11. Erratum
  12. Erratum to: Long-term state-driven atmospheric corrosion prediction of carbon steel in different corrosivity categories considering environmental effects
https://doi.org/10.1515/corrrev-2022-0058
Keywords for this article
corrosion; GH3535 alloy; KCl–MgCl2; molten salt; purification

Articles in the same Issue

  1. Frontmatter
  2. Review
  3. The role of acid–base interactions in the pitting corrosion of aluminum: a review
  4. Original Articles
  5. The effect of Pd and Ni coatings on hydrogen permeation experiments of as-quenched martensitic steel
  6. Effect of surface machining on the environmentally-assisted cracking of Alloy 182 and 316L stainless steel in light water reactor environments: results of the collaborative project MEACTOS
  7. Microbiologically influenced corrosion behavior of 304 stainless steel in ZnO nanofluids
  8. Hairy bamboo leaf extract as an eco-friendly corrosion inhibitor for L245N steel in CO2-saturated oilfield produced water
  9. Using electrochemical testing and modeling to assess the efficiency of a water-soluble inhibitor on the corrosion of 6061Al-15 % (v) SiC (p) composite
  10. Corrosion behavior of GH3535 alloy in KCl–MgCl2 eutectic salts purified with magnesium
  11. Erratum
  12. Erratum to: Long-term state-driven atmospheric corrosion prediction of carbon steel in different corrosivity categories considering environmental effects
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