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Electrolytic accelerated corrosion morphology for structural steel based on an improved solution

  • Qi Si , Yang Ding and Liang Zong EMAIL logo
Published/Copyright: June 18, 2021
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Corrosion Reviews
From the journal Corrosion Reviews Volume 39 Issue 4

Abstract

Atmospheric corrosion degrades the mechanical properties of steel structures mainly because of stress concentrations caused by an uneven corrosion topography. Electrolytic corrosion is regarded as one of the most efficient indoor accelerated corrosion approaches, while, the uneven atmospheric corrosion topography usually cannot be well simulated by electrolytic corrosion. This study aims to introduce an electrolytic corrosion solution suitable for simulating atmospheric corrosion. The surface morphologies of the structural steel specimens after electrolytic corrosion in three different solutions under various electrification time and magnitude of the current were compared. The surface characteristics of the corroded steel plates were measured by a 3D noncontact surface topography scanner, and analyzed based on surface roughness theory and fractal theory. The results showed that the mixed solution of 0.5% CH3COONa and 0.2% NaCl will produce pitting corrosion on the steel surface, and the surface morphologies of the steel specimens after electrolytic corrosion were consistent with that of neutral salt spray accelerated corrosion test. It is verified that the electrolytic accelerated corrosion in such a solution can simulate actual atmospheric corrosion reasonably.

Keywords: accelerated corrosion; corrosion morphology; electrolytic corrosion; fractal theory; structural steel; surface roughness theory

1 Introduction

Most corrosion of metallic materials occurs in the natural environment, primarily in the atmosphere, water, and soil, with atmospheric corrosion being the most severe. The amount of steel used in the atmosphere worldwide exceeds 60% of its total production, and metal losses due to atmospheric corrosion account for more than 50% of total corrosion losses (Ke 2004). Extensive studies have been carried out on atmospheric corrosion (Dai et al. 2015; Garbatov et al. 2014; Li et al. 2020; Wu et al. 2019), where a variety of tests involving atmospheric corrosion have been conducted. Generally, the main test methods of atmospheric corrosion can be divided into atmospheric exposure tests and indoor accelerated tests.

An atmospheric exposure test is conducted in a natural environment, with the metal specimens placed in a natural atmospheric environment according to certain requirements. It is the most direct test approach for studying atmospheric corrosion (Asami and Kikuchi 2003; Beeharry and Surnam 2018). However, corrosion in a natural environment usually develops extremely slowly and takes years. It is difficult to conduct a continuous test for such a long period of time. Therefore, accelerated corrosion methods have been extensively adopted in academic research. Common accelerated corrosion methods include salt spray test, wet thermal corrosion, cyclic wet–dry immersion corrosion, compound environmental corrosion, artificial spray accelerated corrosion and electrolytic corrosion. Draẑić (1989) has carried out two accelerated corrosion tests (immersions in aerated 3% NaCI and a salt chamber) on two low alloyed Cr-Mo steels and two nonalloyed steels in parallel with long-term (5 year) tests on an atmospheric corrosion station, the results showed that long-term atmospheric corrosion behavior can be predicted based on accelerated corrosion tests only. Three kinds of steel [soft steel (SPHC), carbon steel (SS400), and weathered steel (A588)] were prepared for cyclic wet–dry accelerated corrosion and atmospheric corrosion tests, the results of the atmospheric corrosion test are similar to the accelerated corrosion test, indicating the validity of the accelerated corrosion method (Lin and Wang 2005). Manivannan et al. (2015) studied the corrosion performance of cast Mg–6Al–1Zn + XCa alloy under salt spray test (ASTM-B117). Chen et al. (2020) used the copper-accelerated acetic acid salt spray (CASS) test to study corrosion behavior of different cables of large-span building structures in different environments. Nishikata et al. (1995) studied the atmospheric corrosion of steels in a cyclic wet–dry condition. Papadopoulos et al. (2007) studied the effect of salt spray corrosion exposure on the mechanical performance of reinforcing steel bars of different technical classes. Katayama et al. (2005) used a spraying-system to simulate airborne sea salt to study the corrosion of carbon steels in atmospheric environment. The corrosion behavior of galvanized sheets in neutral salt spray test, cyclic immersion, and wet thermal corrosion test was investigated (Feng et al. 2017) to clarify the effect of different accelerated corrosion test environments on the corrosion behavior of galvanized sheets, the results showed that the corrosion process of galvanized sheets was basically the same in the three accelerated corrosion test, the corrosion of the material was most serious in the neutral salt spray test, followed by the cyclic immersion test, and the lightest in the wet thermal corrosion test. These existing studies have shown that, it is feasible to study the corrosion mechanism of steel by short-term tests, but metal specimens with high atmospheric corrosion degrees cannot be obtained quickly. For salt spray corrosion, wet thermal corrosion, cyclic wet–dry immersion corrosion, compound environmental corrosion, and artificial spray accelerated corrosion, the corrosion of metal can be accelerated by adjusting the composition and content of the corrosion solution, but the test period is still considerable, 10% corrosion degree may need 2–4 months.

Regarding electrolytic corrosion, this method was mostly used for accelerated corrosion of pipeline steel buried in soil or rebars corrosion in reinforced concrete. Electrolytic corrosion is not an ordinary immersion test, it is a process of accelerated corrosion. In this process, a metallic surface is continuously corroded by other metal it is in contact with, due to an electrolyte and the flow of an electrical current between the two metals, caused from an external source of electromotive force. Yadav et al. (2004) conducted an electrochemical impedance study on galvanized steel corrosion under cyclic wet–dry conditions to determine the influence of the time of wetness. Yuan et al. (2006) used an artificial climate environment and galvanostatic method to accelerate corrosion on reinforced concrete beams, and the test showed that the surface corrosion characteristics and corrosion products of rebar obtained by the galvanostatic method were significantly different from those under an artificial climate environment. Xiao et al. (2020) conducted an experimental study to compare the deterioration of mechanical properties of 460D steel specimens with two kinds of corrosion, and the geometric features of the specimens were evaluated by using 3D scanning. Although electrolytic accelerated corrosion method can quickly reach the predetermined amount of corrosion and greatly shorten the time required for the test, the resulting corrosion morphology is significantly different from atmospheric corrosion. The formation of stress concentrations in steel due to uneven surface corrosion is the main reason for the reduction in the plasticity, fracture toughness and fatigue performance of rusted steel structures, which makes the method of electrolytic corrosion greatly restricted when studying atmospheric corrosion.

To improve the feasibility of the electrolytic corrosion method, an electrolytic corrosion solution suitable for simulating atmospheric corrosion is proposed in this study. The surface morphology of structural steel after electrolytic corrosion in this solution and other two solutions was compared. The surface characteristics of corroded steel plates were measured by a 3D noncontact surface topography scanner, and the effects of the electrification time and magnitude of the current on the corrosion morphology of structural steel were studied. Surface roughness theory and fractal theory were used to characterize and analyze the surface morphology of the steel after electrolytic corrosion, and the feasibility of the proposed solution was verified by comparing the corrosion morphology of the steel in a neutral salt spray environment.

2 Electrolytic corrosion tests

For electrolytic accelerated corrosion test, NaCl solution is the most widely used solution. Nevertheless, it is revealed by numerous studies that the corrosion surface of steel is homogeneous after the electrolytic accelerated corrosion in NaCl solution (Yuan et al. 2006), which differs from the surface morphologies of the real atmosphere, and cannot reflect the evolution process of corrosion morphology of steel surface from local pitting to overall corrosion in real atmospheric (Bhandari et al. 2015; Zhang et al. 2012). Pitting corrosion often occurs on metals with a passivated or protective film on the surface (Szklarska Smialowaka 1981). A distinctive feature of the metal oxidation process in the CH3COONa solution is the formation of a dense oxidation product layer on the electrode surface (Usoltseva et al. 2014). To produce pitting on a steel surface during the electrolytic corrosion process that has a corrosion morphology close to that of actual atmospheric corrosion, this study proposes the electrolytic corrosion solution – a mixed solution of NaCl and CH3COONa.

Four specimens, labeled by S1–S4, are designed in this study. Specimens S1 and S2 are placed in a 3.5% NaCl solution (mass %), S3 is placed in a 0.2% NaCl solution, and S4 is placed in a mixed solution of 0.5% CH3COONa and 0.2% NaCl. The corrosion morphologies of the steel specimens after electrolytic corrosion in the different solutions are then compared and analyzed as follows.

2.1 Test material

The specimens comprise Q355B structural steel, and its chemical composition is shown in Table 1. The specimen size is 30 × 30 × 8 mm. Before the test, the bottom of the test piece is connected to a wire, and it is wrapped with waterproof tape. The working electrode area is 16 cm2. The surface of the specimen is treated as follows. First, 800#–1200# waterproof sandpaper is used to polish the surfaces of the specimens to a mirror-like finish. Next, the surface of the specimen is cleaned with acetone. Graphite is used to connect to the negative electrode of the power supply and is twice the length and width of the specimen. The two electrodes are 80 mm apart. The specimen and graphite are arranged symmetrically in a test container.

Table 1:

Chemical composition of the Q355B steel (wt.%).

Material C Si Mn P S Alt Fe
Q355B 0.19 0.107 0.42 0.009 0.002 0.023 Balance

2.2 Test apparatus

The initial weight of the specimen before the test and the weight after rust removal are measured and recorded with a precision electronic balance that is accurate to 0.001 g. The mass of the specimen before the test is recorded as m1, and the mass of the specimen after electrolytic corrosion is recorded as m2.

The test container is composed of acrylic, and the DC current is transmitted through the SS-305 DC power supply to ensure voltage stability, as shown in Figure 1a. The room is well ventilated, and the average temperature is approximately 28 °C. The specimen and graphite were placed in the container to form a circuit of positive power supply specimen solution – negative power supply, as shown in Figure 1b.

Figure 1: Electrolytic corrosion test.
Figure 1:

Electrolytic corrosion test.

2.3 Analysis of results

After the process is initiated according to standard GB/T 16545-2015, 500 ml HCl (ρ = 1.19 g/ml), 3.5 g hexamethylenetetramine and 500 ml distilled water are used to remove the rust. After rust removal, the surfaces of the specimens are observed, and the rust pits are observed by optical microscopy at 50 times magnification. The test results are shown in Table 2 and Figure 2.

Table 2:

Results of electrolytic corrosion of specimens S1–S4.

Specimens m 1 (g) m 2 (g) I (A) J (A/m2) T (min) Δm (g) η 0 (%)
S1 50.348 49.846 0.5 284.09 60 0.502 1.00
S2 51.949 51.413 1.0 568.18 30 0.536 1.03
S3 52.674 52.169 0.5 284.09 60 0.505 0.96
S4 49.277 48.784 0.5 284.09 60 0.493 1.00

  1. I, electron flow; J, current density; T, electrification time; Δm, mass loss; η0, mass loss; η0 = Δm/m1.

Figure 2: Macroscopic and microscopic corrosion morphologies of specimens S1-S4.
Figure 2:

Macroscopic and microscopic corrosion morphologies of specimens S1-S4.

According to Figure 2a–c, the electrolytic corrosion of the steel specimens in the NaCl solution, current magnitude, and NaCl concentration have a low influence on the corrosion morphology; uniform corrosion and no pitting of the steel specimens occurs. Figure 2d shows that in the solution of 0.5% CH3COONa and 0.2% NaCl presented in this paper, steel pitting occurs and pits are formed. This behavior is closer to that of actual atmospheric corrosion.

A sulfide-induced pitting corrosion model is used to analyze the pitting corrosion phenomenon caused by electrolytic corrosion in the proposed mixed solution. Electrolysis of steel in a sodium acetate solution forms a passivation film on its surface. The continuity and integrity of the passivation film can be disrupted by the exposure of nonmetallic inclusions on the surface. At the interface between the inclusions and the steel matrix, the arrangement of iron atoms is disordered; in a high-energy state, its thermodynamic stability is poor, and the ionization trend is strong. This part of the surface is also the thinnest passivation film and therefore provides very weak protection. The steel specimens’ potential is positively shifted, and aggressive anions, such as Cl−, adsorb at the interface between the inclusions and the steel matrix, as shown in Figure 3a. Aggregated chloride ions react with the oxide film to form a soluble chloride of iron, with local dissolution of the surface film and local activation of the steel substrate surface during electrolytic corrosion. Destruction of the passivated film on the steel surface alternates with its repair. As long as there is activation on the surface, some of the iron atoms are ionized and produce hydrolytic acidification, which enhances the acidity of localized microspot regions and causes a small amount of dissolution to occur at the edges of the inclusions to form some sort of dissolution product, as shown in Figure 3b. With the destruction of the passivation film by the chloride ions and the increasing ionization of the iron, the passivation film cannot be repaired, and pitting corrosion is induced. The passivation film at the interface between the inclusions and the iron matrix is completely destroyed, the iron matrix is dissolved, and the inclusions continue to be dissolved, as shown in Figure 3c. As corrosion proceeds, localized acidification of the steel surface occurs, inclusions continue to dissolve, and the damaged area of the passivation film expands. These factors promote the development of pitting, and eventually a pitting pattern is formed on the steel surface, as shown in Figure 3d.

Figure 3: Schematic diagram of the pitting mechanism.
Figure 3:

Schematic diagram of the pitting mechanism.

3 Corrosion morphology scanning

For electrolytic accelerated corrosion testing of steel, the magnitude of the current and the duration of the energization may have an effect on its corrosion morphology. To study the specific corrosion morphology of the steel specimens in a mixture of 0.5% CH3COONa and 0.2% NaCl, 15 specimens are designed for electrolytic accelerated corrosion and numbered A11–A53, as shown in Figure 4. The specimens are de-rusted after the corrosion test, and the specific data for each specimen are listed in Table 3.

Figure 4: Design of the specimens.
Figure 4:

Design of the specimens.

Table 3:

Results of the electrolytic corrosion of specimens A11–A53.

Specimens m 1 (g) m 2 (g) I (A) J (A/m2) T (min) Δm (g) η 0 (%) η (%)
A11 49.277 48.784 0.50 284.09 60 0.493 1.00 0.95
A12 52.536 52.059 0.75 426.14 40 0.477 0.91
A13 51.701 51.209 1.00 568.18 30 0.492 0.95
A21 51.539 50.536 0.50 284.09 120 1.003 1.95 2.01
A22 49.699 48.683 0.75 426.14 80 1.016 2.04
A23 49.853 48.842 1.00 568.18 60 1.011 2.03
A31 50.486 48.820 0.50 284.09 200 1.666 3.30 3.33
A32 52.642 50.906 0.75 426.14 137 1.736 3.30
A33 52.591 50.809 1.00 568.18 100 1.782 3.39
A41 52.543 49.41 0.50 284.09 450 3.133 5.96 6.07
A42 52.539 49.346 0.75 426.14 300 3.193 6.08
A43 52.195 48.974 1.00 568.18 225 3.221 6.17
A51 52.551 46.283 0.50 284.09 900 6.268 11.93 11.84
A52 52.539 46.417 0.75 426.14 600 6.122 11.65
A53 52.37 46.12 1.00 568.18 450 6.25 11.93

  1. I, electron flow; J, current density; T, time; Δm, mass loss; η0, mass loss, η0 = Δm/m1; η, average mass loss.

3.1 Surface topography

A three-dimensional noncontact surface ST-400 profilometer by NANOVEA is used for the 15 specimens after rust removal, as shown in Figure 5. The topography of the surface is scanned with a scan step of 0.05 mm. The three-dimensional appearances of the specimens are shown in Figure 6.

Figure 5: The ST-400 surface profilometer.
Figure 5:

The ST-400 surface profilometer.

Figure 6: Three-dimensional topography of specimens A11–A53.
Figure 6: Three-dimensional topography of specimens A11–A53.
Figure 6: Three-dimensional topography of specimens A11–A53.
Figure 6:

Three-dimensional topography of specimens A11–A53.

The three-dimensional surface topography obtained from the scan consists of the real image, a color scale and an indication of the height based on the color scale. From the three-dimensional surface topography, it can be seen that at the beginning of electrolytic corrosion, the pits on the surface of the specimen are mostly round and oval. As the power-on time increases, the range of corrosion gradually expands, and circular pits begin to combine to form long strips and large round pits. With the development of corrosion, corrosion pits continue to develop and expand, and corrosion formed by the pits combine with the formation of secondary rust pits all over the surface of the specimen. corrosion A uniform corrosion state is then developed.

3.2 Contour line scanning

The midline of the scan fields was selected for the contour lines to analyze the pit shape of each specimen in its depth direction. Due to the large number of specimens, only the scan results for A1–A52 are listed, as shown in Figure 7. Length in the figure is the scan range of the contour line and Pt is the height difference between the peaks and troughs of the wave.

Figure 7: Contour scanning diagrams for specimens A22–A52.
Figure 7:

Contour scanning diagrams for specimens A22–A52.

The trends for the rust pits on the steel surface in the depth direction can be observed from the contour line scanning diagrams. The contour lines show that a large number of pinhole-shaped rust pits appear on the surface of the test piece, and the corrosion is vertical in the initial stage of electrolytic corrosion. With an increase in corrosion degree, the corrosion extends to the whole surface. Due to the slow connection of the pinholes, deeper and larger holes appear, such as U-shaped corrosion pits and conical corrosion pits. In the late stages of corrosion, the pits continue to develop and expand, and some of them produce secondary pits, which form a complex morphology.

4 Corrosion morphology analysis

4.1 Theory and calculation

At present, there is no unified method for the morphological characterization of corroded steel structure surfaces (Xu et al. 2016). In this paper, surface roughness theory and fractal theory are adopted to characterize and analyze the surface characteristics of structural steel after electrolytic corrosion.

The surface roughness refers to the characteristics of the micro-geometry and shows small spacings and peaks and valleys on the surface (Alvarez et al. 2010; Hotar and Hotar 2018; Toloei et al. 2013). According to standard ISO 25178, the arithmetic mean height (Sa), the root mean square height (Sq) and the maximum height (Sz) of each specimen surface after electrolytic corrosion are calculated from the three-dimensional topographic scan data (ISO 2012).

The fractal dimension (D) in fractal theory is a mathematical concept to classify certain sets in more detail than the topological dimension can. Many scientists in the life sciences and materials sciences use the fractal dimension as a parameter to characterize rough lines or surfaces. In other words, the fractal dimension is a measure of the morphology, texture, and roughness of a surface. The fractal dimension can numerically characterize the variation in the surface structure caused by corrosion (Costa et al. 1991; Pidaparti et al. 2010). The fractal dimension is calculated using the box counting method (Sarkar and Chaudhuri 1994; Xu and Weng 2006). The specific formula for each parameter is shown in Eqs. (1)–(4), and the results are shown in Table 4 and Figure 8.

(1)Sa=1A∭D|z(x,y)|dxdy
(2)Sq=1lxly∫0l∫0lz2(x,y)dxdy
(3)SZ=Sp+Sv
(4)N(ϵi)=Vϵi/ϵi3=∑m=1lx/ϵi∑n=1ly/ϵiVϵi,m,n/ϵi3=∑m=1lx/ϵi∑n=1ly/ϵi(max(max(Zm,n))−min(min(Zm,n)))/ϵi

where Z (x, y) is the scanning surface of the specimen; lx and ly are the side lengths of the sampling area; Sp and Sv are the maximum peak height and valley depth, respectively; Vϵi,m,n is the volume of a square column with a base of ϵi×ϵi at position (m, n); and Zm,n is a matrix formed by the coordinate values of the scanning points in the thickness direction of the square column.

Table 4:

Surface morphological characteristics of specimens A11–A53.

Specimen S a (μm) S q (μm) S z (μm) D
A11 23.405 29.211 207.032 2.539
A12 24.397 33.550 194.145 2.480
A13 28.204 33.832 151.589 2.584
A21 41.100 49.793 282.138 2.472
A22 42.448 48.417 248.505 2.553
A23 41.555 48.016 240.840 2.547
A31 53.465 66.848 389.662 2.454
A32 50.637 53.447 266.730 2.389
A33 48.577 51.164 253.862 2.497
A41 78.055 96.771 595.685 2.320
A42 67.340 84.128 499.170 2.303
A43 56.282 71.034 426.080 2.325
A51 138.414 172.798 999.458 2.224
A52 104.674 128.449 729.373 2.292
A53 92.851 115.184 636.752 2.253
Figure 8: Surface morphology parameters of the specimens.
Figure 8:

Surface morphology parameters of the specimens.

Figure 8 shows that during electrolytic accelerated corrosion, the values of Sa, Sq and Sz show an overall decreasing trend with increasing current for the same amount of corrosion. The greater the degree of corrosion is, the more pronounced the decrease in the values of Sa, Sq and Sz. Sa, Sq and Sz are proportional to the amount of corrosion when the magnitude of the current is the same, with the values of Sa, Sq and Sz increasing the longer the current is applied. The variation pattern between the fractal dimension of the specimen surface and the magnitude of the current is not evident for the same amount of corrosion. As the corrosion degree increases, the fractal dimension (D) of the corroded surface gradually decreases, in agreement with the findings (Kong and Xu 2011; Xu and Weng 2006).

4.2 Comparison and verification

The Sa, Sq and Sz of the corroded surface are fitted by a power function, and the formula is shown in Table 5. A comparison of the fitted formula with the results obtained by neutral salt spray accelerated corrosion test (Qin et al. 2016) is conducted to verify the feasibility and accuracy of simulating atmospheric corrosion by electrically accelerating corrosion in the mixed solution. The results of the comparison are shown in Figure 9.

Table 5:

Formulas for Sa, Sq and Sz.

I (A) S a (μm) S q (μm) S z (μm)
0.5 S a  = 22.655 × η0.725 (R2 = 0.995) S q  = 27.535 × η0.736 (R2 = 0.995) S z  = 179.046 × η0.690 (R2 = 0.997)
0.75 S a  = 26.192 × η0.555 (R2 = 0.993) S q  = 32.366 × η0.552 (R2 = 0.998) S z  = 179.223 × η0.567 (R2 = 0.998)
1.0 S a  = 26.954 × η0.483 (R2 = 0.974) S q  = 31.613 × η0.509 (R2 = 0.984) S z  = 156.899 × η0.565 (R2 = 0.999)
Figure 9: Comparison chart of surface morphology parameters.
Figure 9:

Comparison chart of surface morphology parameters.

From the comparative results, the relationship between Sa, Sq and Sz of the rusted surface and the amount of corrosion can be fitted with a power function model, and R2 values are all greater than 0.9, indicating that the fitting effect is improved. Different current magnitudes have an effect on the Sa, Sq and Sz of the rusted surface, but the general pattern is approximately the same and proportional to the corrosion degree. When the current is 0.75 A, the variation curves of the relationship of Sa, Sq and Sz with the corrosion degree are closest to the results of the artificial spray corrosion. A comparison with the formula proposed by Qin et al. (2016) indicates that the surface morphology of the steel specimens after electrolytic accelerated corrosion in a mixed solution of CH3COONa and NaCl is similar to the corrosion morphology development pattern during artificial spray corrosion, indicating that the electrolytic accelerated corrosion in this solution can better simulate atmospheric corrosion in the actual environment.

5 Conclusion

This study was focused on a new electrolytic corrosion solution which can simulate the real atmospheric corrosion and the corrosion morphology of structural steel. Some conclusions relating to the electrolytic accelerated corrosion test can be drawn from this research.

  1. For electrolytically accelerated corrosion of steel in NaCl solutions, the current size and NaCl concentration have little effect on the corrosion morphology. The steel is corroded uniformly without pitting. For electrolytic accelerated corrosion of steel in the mixed solution of 0.5% CH3COONa and 0.2% NaCl, pitting corrosion occurs on the steel specimens, forming corrosion pits.

  2. The relationship between Sa, Sq and Sz and the corrosion degree on the steel surface after electrolytic corrosion can be expressed as a power function model. For the same amount of corrosion, the values of Sa, Sq and Sz show an overall decreasing trend with increasing current. For the same magnitude of current, Sa, Sq and Sz are proportional to the amount of corrosion; that is, the longer the energization time is, the greater the value of Sa, Sq and Sz. As the corrosion degree increases, the fractal dimension of the corroded surface gradually decreases.

  3. The surface morphology of the steel in a CH3COONa and NaCl mixed solution after electrolytic corrosion and the results obtained by neutral salt spray accelerated corrosion test are in good agreement. The curves for Sa, Sq and Sz with the amount of corrosion at a current of 0.75 A are closest to the results for neutral salt spray accelerated corrosion test, showing that electrolytic accelerated corrosion in this solution can better simulate actual atmospheric corrosion.

Corresponding author: Liang Zong, School of Civil Engineering, Key Laboratory of Coast Civil Structure Safety, Ministry of Education, Tianjin University, Tianjin300072, China, E-mail:

Funding source: The National Key Research and Development Program of China 10.13039/501100012166

Award Identifier / Grant number: 2018YFC1504304

Funding source: The Postgraduate Innovation Research Project of Tianjin

Award Identifier / Grant number: 2019YJSB166

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

  2. Research funding: The reported research work was sponsored by the National Key Research and Development Program of China (2018YFC1504304) and The Postgraduate Innovation Research Project of Tianjin (2019YJSB166).

  3. Conflicts of interest: The authors declare no conflicts of interest regarding this article.

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Received: 2020-11-24
Accepted: 2021-05-14
Published Online: 2021-06-18
Published in Print: 2021-08-26

© 2021 Walter de Gruyter GmbH, Berlin/Boston

Articles in the same Issue

  1. Frontmatter
  2. In this issue
  3. Reviews
  4. Ferrous materials degradation: characterisation of rust by colour – an overview
  5. Recent progress on the corrosion behavior of metallic materials in HF solution
  6. Original articles
  7. Study on the corrosion resistance of sulfonated graphene/aluminum phosphate composites in waterborne polyurethane coatings
  8. Microstructural evolution and corrosion behaviour of friction stir-processed QE22 magnesium alloy
  9. Preparation and characterization of Nd-doped double-layer silane anticorrosion coating on AZ91D magnesium alloy surface
  10. Electrolytic accelerated corrosion morphology for structural steel based on an improved solution
https://doi.org/10.1515/corrrev-2020-0108
Keywords for this article
accelerated corrosion; corrosion morphology; electrolytic corrosion; fractal theory; structural steel; surface roughness theory

Articles in the same Issue

  1. Frontmatter
  2. In this issue
  3. Reviews
  4. Ferrous materials degradation: characterisation of rust by colour – an overview
  5. Recent progress on the corrosion behavior of metallic materials in HF solution
  6. Original articles
  7. Study on the corrosion resistance of sulfonated graphene/aluminum phosphate composites in waterborne polyurethane coatings
  8. Microstructural evolution and corrosion behaviour of friction stir-processed QE22 magnesium alloy
  9. Preparation and characterization of Nd-doped double-layer silane anticorrosion coating on AZ91D magnesium alloy surface
  10. Electrolytic accelerated corrosion morphology for structural steel based on an improved solution
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