Evaluation of 4-Year Atmospheric Corrosion of Carbon Steel, Aluminum, Copper and Zinc in a Coastal Military Airport in Greece

Atmospheric corrosion seriously affects the working life of construction metals. The quantitative knowledge of the corrosion effects helps the maintenance and the materials’ logistics. In this work, in a military airport located by the sea, the corrosion damage equations of carbon steel, aluminum, zinc and copper are determined after outdoor exposure for four years. Exposure started in 2014, at two different periods of the year, in summer and in winter, for all cases. Weight loss measurements were performed as well as characterization of the exposed metal coupon surfaces by microscopy: optical, electron and atomic force, by X-ray diffraction and Fourier Transform Infrared Spectroscopy. Atmospheric conditions and pollutants were also evaluated. The derived corrosion equations of all tested metals for the exposure have been employed for the 30-year projection of expected corrosion. A parallel 12-month exposure of steel and aluminum—the most common airport metals—have been evaluated for five consequent years to designate the rating of the airport, according to ISO and ASTM Standards. The results showed that there is not a good correlation between the predictions of the Corrosion Damage Algorithm and the Europe Corrosion Map and the actual measurements on steel and aluminum at the site.


Introduction
Atmospheric corrosion is the main parameter in degradation of metallic materials. According to Simillion et al. [1], a corrosion cost at the range of 3-6% of the Gross Domestic Product (GDP) of the economies of the industrialized countries can be considered as common grounds of different studies [2][3][4]. Atmospheric corrosion constitutes a considerable part of this corrosion cost [5]. This has led to an extensive international effort to investigate it, aiming towards minimizing its effects. In 1980, the ISOCORRAG, ICP/UNECE and MICAT programs were launched in order to investigate in depth and understand the phenomenon of corrosion, and at the same time to proceed to a systematic development of prediction models of the corrosivity of the environment. As a result, Dose Response Functions (DRF) were established, based on meteorological data, SO 2 concentration and chloride (from NaCl) deposition rate. A general methodology for the classification of the atmospheric aggressivity started to emerge, based on the similarities of the methodologies of these programs. A major step for the atmospheric aggressivity determination was the publication of ISO Standards 9223-9226 [6][7][8][9] in 1992, based on a relatively small spectrum of experimental data, concerning climatological and pollution conditions. In addition, extensive studies were presented on the DRF and the corrosion aggressivity. In an extensive research by Morcillo et al. [10], no improvement in the correlation

Materials and Methods
Aluminum, zinc, copper and unalloyed carbon steel specimens have been exposed in outdoor atmospheric conditions, on the roof of a maintenance hangar, at a distance of approximately 0.2 km from the seashore at the LGMG for a 4-year exposure period. Exposure started in 2014 at two different periods of the year, in summer and in winter, in order to determine the seasonal effects on the initial corrosion stage and eventually the long-term effects on the metal surface, as well as the evolved corrosion rates. The standard specimens of commercially pure Al (>99.5% minimum), unalloyed carbon steel, Zn (>95% minimum) and Cu (>94% minimum) were flat coupons with dimensions 100 × 100 × 1 mm 3 , as described in ISO 9226 [9]. Table 1 shows the detailed composition of the tested carbon steel samples as analyzed by an ARL3460 automatic Optical Emission Spectrometer (OES) at Halyvourgiki Inc. laboratories. Table 1. Average chemical composition (wt.%) of unalloyed carbon steel specimens. The LGMG (37 58 52.01" N, 023 21 55.52" E) [44] was selected as the exposure site due to (i) the observation of macroscopic corrosion in aircraft subassemblies and of the construction materials in helicopters, after technical inspection, and (ii) the proximity of the rural test site to the seacoast and to the surrounding industrial area of Elefsina.
Four test pieces were used for each metal and period of exposure on a rack at 45 • to the horizontal facing south, as seen in Figures 1 and 2. The metal structures were designed with the use of "3D CAD Design Software SOLIDWORKS", according to standard ISO 9225 [8] and constructed in the Laboratory of the Manufacturing Technology of NTUA. Three specimens, for each metal and period of exposure, were weighted before and after the exposure in order to measure the weight loss. The preparation, cleaning of the metal coupons (and the mass loss of the exposed metal samples) was determined after sequential pickling as per ISO 8407 [32] and the ASTM norm, G1-90 [33]. Chemical cleaning procedures for the removal of the corrosion products are described in Table 2.    The fourth test specimen for each metal was employed for the surface analysis of the corrosion products formed. Test work was carried over 4 years, with samples taken for analysis after 3, 6, 12, 24 and 48 months during the two periods of exposure. "TableCurve 2D v5.01.01" and "Microsoft Excel" software were used for the determination of the power equations and for plotting the data relative to the corrosion loss. Corrosion rates of the tested metals were determined from the weight loss of specimens in accordance to ISO 9226 [9].
The corrosion products formed on the metal surfaces have been characterized by: (i) A FEI Quanta 200 Scanning Electron Microscope/Energy Dispersive Spectrometer (SEM/EDS, Thermo Fisher Scientific, Waltham, MA, USA) coupled with Energy Dispersive X-Ray Analysis (EDAX). The SEM images were analyzed by means of the computer program EDGE.EXE [45]. (ii) A Siemens D-500 X-ray diffractometer (with a graphite crystal monochromator and a Cu anticathode, (Siemens, Munich, Germany) based on an automatic adjustment and analysis system, with Diffract-EVA quality analysis software [46]. (iii) A Leica DMR Optical Microscope (OM, Leica Microsystems, Wetzlar, Germany). (iv) For the Al surface morphology examination, an Atomic Force Microscope Scanner (AFM, Semilab Germany GmbH, Braunschweig, Germany) DUALSCOPE 95-50 of DME was employed. (v) Examination of the presence of amorphous corrosion products on steel coupons'     The fourth test specimen for each metal was employed for the surface analysis of the corrosion products formed. Test work was carried over 4 years, with samples taken for analysis after 3, 6, 12, 24 and 48 months during the two periods of exposure. "TableCurve 2D v5.01.01" and "Microsoft Excel" software were used for the determination of the power equations and for plotting the data relative to the corrosion loss. Corrosion rates of the tested metals were determined from the weight loss of specimens in accordance to ISO 9226 [9].
The corrosion products formed on the metal surfaces have been characterized by: (i) A FEI Quanta 200 Scanning Electron Microscope/Energy Dispersive Spectrometer (SEM/EDS, Thermo Fisher Scientific, Waltham, MA, USA) coupled with Energy Dispersive X-Ray Analysis (EDAX). The SEM images were analyzed by means of the computer program EDGE.EXE [45]. (ii) A Siemens D-500 X-ray diffractometer (with a graphite crystal monochromator and a Cu anticathode, (Siemens, Munich, Germany) based on an automatic adjustment and analysis system, with Diffract-EVA quality analysis software [46]. (iii) A Leica DMR Optical Microscope (OM, Leica Microsystems, Wetzlar, Germany). (iv) For the Al surface morphology examination, an Atomic Force Microscope Scanner (AFM, Semilab Germany GmbH, Braunschweig, Germany) DUALSCOPE 95-50 of DME was employed. (v) Examination of the presence of amorphous corrosion products on steel coupons' The fourth test specimen for each metal was employed for the surface analysis of the corrosion products formed. Test work was carried over 4 years, with samples taken for analysis after 3, 6, 12, 24 and 48 months during the two periods of exposure. "TableCurve 2D v5.01.01" and "Microsoft Excel" software were used for the determination of the power equations and for plotting the data relative to the corrosion loss. Corrosion rates of the tested metals were determined from the weight loss of specimens in accordance to ISO 9226 [9].
The corrosion products formed on the metal surfaces have been characterized by: (i) A FEI Quanta 200 Scanning Electron Microscope/Energy Dispersive Spectrometer (SEM/EDS, Thermo Fisher Scientific, Waltham, MA, USA) coupled with Energy Dispersive X-Ray Analysis (EDAX). The SEM images were analyzed by means of the computer program EDGE.EXE [45]. (ii) A Siemens D-500 X-ray diffractometer (with a graphite crystal monochromator and a Cu anticathode, (Siemens, Munich, Germany) based on an automatic adjustment and analysis system, with Diffract-EVA quality analysis software [46]. (iii) A Leica DMR Optical Microscope (OM, Leica Microsystems, Wetzlar, Germany). (iv) For the Al surface morphology examination, an Atomic Force Microscope Scanner (AFM, Semilab Germany GmbH, Braunschweig, Germany) DUALSCOPE 95-50 of DME was employed. (v) Examination of the presence of amorphous corrosion products on steel coupons' surface was performed by Fourier Transform Infrared Spectrometer FT-IR4200 of Jasco (Jasco, Cremella, Italy).
A temperature (T • C) and relative humidity (RH%) data logger «Tinytag» PLUS2 (TGP-4500) was used in order to obtain the parameters of air temperature and of relative humidity, for a year, at the exact field site, as seen in the frame of Figure 1. T and RH data obtained by the data logger are also used for calculating the Time of Wetness (TOW). The TOW is calculated as the length of time when the relative humidity is greater than 80% at a temperature greater than 0 • C [6]. In order to determine the airborne salinity, the chloride measurements were conducted by the Wet Candle Method for the airport according to ISO 9225 [8] and ASTM G140-02 [31] Standards. Sampling was performed every 30 days, while a new sample was positioned for further exposure. The amount of chlorides, in every sample, was measured by both the Mohr and Volhard titration methods, as well as by AgNO 3 test. Chloride measurements of the atmosphere were not feasible; however, an approximate environmental calibration based on corrosion rates' determination and corrosion products' characterization and literature is attempted.
In addition, three specimens of the commercially pure Al (>99.5% minimum) and the unalloyed carbon steel are also exposed for a one-year period, for two initial times of exposure. After one year, the first set of the exposed specimens was removed and another set was exposed. This process was repeated from 2014 to 2019, according to ISO and ASTM standards. A classification of the atmospheric aggressivity based on the environmental data and the corrosion rate measurements of steel and Al was conducted. The obtained gravimetric data were also used in order to examine the reliability of the CDA, and the Europe and Asia Corrosion Map at the LGMG environment.

Pollutants
The mean annual concentration of the O 3 over the Attica region, during the period 2000-09, is almost constant at approximately 55 µg/m 3 [47,48]. In a distance of 20 km from the LGMG area, where the country's industrial core is located in the area of Elefsina, the annual mean concentration of SO 2 is at approximately 7 µg/m 3 [47,49,50]. In the LGMG area, there has never been made any pollutant concentration measurements. Regarding the concentration of sulfur dioxide at the LGMG, the annual maximum concentration of the pollutant is estimated at [SO 2 ] max = 2 µg/m 3 , according to the European Monitoring and Evaluation Program (EMEP) and several sources [47,[49][50][51][52][53][54][55][56].

Meteorological Data
The meteorological data at LGMG area are presented in Table 3. The monthly variation of the temperature-humidity data and the time of wetness are presented in Figure 3.
The time of wetness expressed in hours per year has been estimated to 2439 h/year, as reported in a previous work [60]. The RH-TOW factor is expected to affect the atmospheric corrosion of metals in a major degree. The influence of temperature on the atmospheric corrosion of many metals has a maximum at about 9-11 • C. The mean annual temperature at the airport has been 20.9 • C, as previously reported [60]. Due to the NW prevailing wind at Megara area, from inland to the seashore, and the mean annual wind speed, the salinity is expected to affect the corrosion of metals to a lesser degree than what is generally expected for a coastal site [47].
Corros. Mater. Degrad. 2020, 1 FOR PEER REVIEW 6 Figure 3. Monthly variation of T (°C) and RH (%) data at the Pachi Military Airport (LGMG) [60]. The black line represents the mean monthly temperature and its standard deviation at the LGMG. The red bar marks the hours per month where RH is over 80% and the blue bar marks the hours per month that RH is less than 80%. The numbers at the bottom are the TOW hours for each month. The numbers at the top are the hours where there is no wetness.
The time of wetness expressed in hours per year has been estimated to 2439 h/year, as reported in a previous work [60]. The RH-TOW factor is expected to affect the atmospheric corrosion of metals in a major degree. The influence of temperature on the atmospheric corrosion of many metals has a maximum at about 9-11 °C. The mean annual temperature at the airport has been 20.9 °C, as previously reported [60]. Due to the NW prevailing wind at Megara area, from inland to the seashore, and the mean annual wind speed, the salinity is expected to affect the corrosion of metals to a lesser degree than what is generally expected for a coastal site [47].

The 4-Year Corrosion Assessment of the Tested Metals and the Anticipated 30-Year Corrosion Loss
For modeling the corrosion loss with exposure time, the (power) kinetic Equation (1) was employed in the form: where a: constant, t: time of exposure in days and b: time exponent. The validity of the equation and its reliability to predict long-term corrosion has been demonstrated by many authors [16,23,[61][62][63][64][65][66][67]. Both "a" and "b" are dependent on the climatic parameters and on the type of the metal. The constant "a" represents the corrosion loss during the first year, while the time exponent "b" represents the multi-year loss yield [68]. The higher the time exponent "b" term is the less protective is the corrosion product layer on the metal surface [69]. The statistical coefficient of determination, R 2 , is a measure of the goodness of fit of the experimental data [69]. The representation of the corrosion data versus time and the 30-year anticipated corrosion evolution are depicted in Table 4 and in the power plots and Figures 4-7 for each one of the tested metals. Table 4 shows the mass loss data for 1, 2 and 4 years, determined experimentally and the model equation parameters and the estimation of 30-year corrosion by the projection of the model  [60]. The black line represents the mean monthly temperature and its standard deviation at the LGMG. The red bar marks the hours per month where RH is over 80% and the blue bar marks the hours per month that RH is less than 80%. The numbers at the bottom are the TOW hours for each month. The numbers at the top are the hours where there is no wetness.

The 4-Year Corrosion Assessment of the Tested Metals and the Anticipated 30-Year Corrosion Loss
For modeling the corrosion loss with exposure time, the (power) kinetic Equation (1) was employed in the form: where a: constant, t: time of exposure in days and b: time exponent. The validity of the equation and its reliability to predict long-term corrosion has been demonstrated by many authors [16,23,[61][62][63][64][65][66][67]. Both "a" and "b" are dependent on the climatic parameters and on the type of the metal. The constant "a" represents the corrosion loss during the first year, while the time exponent "b" represents the multi-year loss yield [68]. The higher the time exponent "b" term is the less protective is the corrosion product layer on the metal surface [69]. The statistical coefficient of determination, R 2 , is a measure of the goodness of fit of the experimental data [69]. The representation of the corrosion data versus time and the 30-year anticipated corrosion evolution are depicted in Table 4 and in the power plots and Figures 4-7 for each one of the tested metals. Table 4 shows the mass loss data for 1, 2 and 4 years, determined experimentally and the model equation parameters and the estimation of 30-year corrosion by the projection of the model equations. Table 5 shows the corrosion rate of Cu for 1, 2 and 4 years, determined experimentally, expressed in µm/year, given by the Equation: where ∆m is the mass loss of Cu in g, A is the surface area in m 2 , t is the exposure time in years and ρ is the density of Cu ρ cu = 8.96 g/cm 3 [9]. Figures 4-7 show the experimental gravimetric curves and the fitted model equations obtained for the four metals tested.
where Δm is the mass loss of Cu in g, A is the surface area in m 2 , t is the exposure time in years and ρ is the density of Cu ρcu = 8.96 g/cm 3 [9]. Figures 4-7 show the experimental gravimetric curves and the fitted model equations obtained for the four metals tested.

Characterization of the Metals' Surfaces After Four Years of Exposure
It is observed that, in an area with low values of pollutants' concentration, the corrosion attack on the downward side of the metal specimens is significantly lower than on the upward side [70]. This is also observed, both macroscopically and microscopically, in the metal specimens tested. That observation confirms (i) the low concentration of pollutants in the LGMG, especially of SO2, and (ii) reveals the significant role of rainfall in the corrosivity of its atmosphere.
The corrosion products' development on the steel surface observed by OM, after four years of exposure, for both initial time of exposure, is presented in Figure 8.

Characterization of the Metals' Surfaces After Four Years of Exposure
It is observed that, in an area with low values of pollutants' concentration, the corrosion attack on the downward side of the metal specimens is significantly lower than on the upward side [70]. This is also observed, both macroscopically and microscopically, in the metal specimens tested. That observation confirms (i) the low concentration of pollutants in the LGMG, especially of SO2, and (ii) reveals the significant role of rainfall in the corrosivity of its atmosphere.
The corrosion products' development on the steel surface observed by OM, after four years of exposure, for both initial time of exposure, is presented in Figure 8.

Characterization of the Metals' Surfaces After Four Years of Exposure
It is observed that, in an area with low values of pollutants' concentration, the corrosion attack on the downward side of the metal specimens is significantly lower than on the upward side [70]. This is also observed, both macroscopically and microscopically, in the metal specimens tested. That observation confirms (i) the low concentration of pollutants in the LGMG, especially of SO 2 , and (ii) reveals the significant role of rainfall in the corrosivity of its atmosphere.
The corrosion products' development on the steel surface observed by OM, after four years of exposure, for both initial time of exposure, is presented in Figure 8.
C, S and traces of chlorides, attributed to aircraft fuel emissions, the emissions of the vehicles traveling on the nearby motorway (0.9 km) and the proximity to the sea (0.2 km) are detected from the carbon steel specimens' surface analysis by SEM/EDS. Carbon steel exhibits the highest concentration of O among the tested metals due to the oxides and hydroxides formed on both sides. The surface analysis by SEM/EDS on steel, after four years of exposure, is presented in Figure 9. C, S and traces of chlorides, attributed to aircraft fuel emissions, the emissions of the vehicles traveling on the nearby motorway (0.9 km) and the proximity to the sea (0.2 km) are detected from the carbon steel specimens' surface analysis by SEM/EDS. Carbon steel exhibits the highest concentration of Ο among the tested metals due to the oxides and hydroxides formed on both sides. The surface analysis by SEM/EDS on steel, after four years of exposure, is presented in Figure 9.  C, S and traces of chlorides, attributed to aircraft fuel emissions, the emissions of the vehicles traveling on the nearby motorway (0.9 km) and the proximity to the sea (0.2 km) are detected from the carbon steel specimens' surface analysis by SEM/EDS. Carbon steel exhibits the highest concentration of Ο among the tested metals due to the oxides and hydroxides formed on both sides. The surface analysis by SEM/EDS on steel, after four years of exposure, is presented in Figure 9. Growth of oxides and hydroxides is observed, both on skyward and downward sides, already from the 1st semester of the exposure, by X-ray diffraction (XRD). Lepidocrocite [γ-FeO(OH)] and traces of goethite [α-FeO(OH)] are identified after two years of exposure of carbon steel specimens' surface in the atmosphere, independent from the initial time of exposure (summer or winter) and the side of the specimens (skyward or downward). Magnetite (Fe 3 O 4 ) is identified on the coupons' skyward surface, exposed during winter, after two years of exposure [46]. After four years, lepidocrocite [γ-FeO(OH)], goethite [α-FeO(OH)], magnetite (Fe 3 O 4 ), akagenaite (β-FeOOH) and traces of hematite (Fe 2 O 3 ) are identified on both sides of the steel specimens for both initial times of exposure. No amorphous corrosion products on steel surface were detected after examination of carbon steel specimens by XRD ( Figure 10) and FTIR ( Figure 11) and also mentioned by other studies [71][72][73][74][75][76][77][78][79]. The corrosion products identified by XRD and FTIR, after four years of exposure, are presented in Figures 10 and 11. the elements detected by SEM/EDS after 4 years of exposure. Initial time of exposure: (a) summer; (b) winter.
Growth of oxides and hydroxides is observed, both on skyward and downward sides, already from the 1st semester of the exposure, by X-ray diffraction (XRD). Lepidocrocite [γ-FeO(OH)] and traces of goethite [α-FeO(OH)] are identified after two years of exposure of carbon steel specimens' surface in the atmosphere, independent from the initial time of exposure (summer or winter) and the side of the specimens (skyward or downward). Magnetite (Fe3O4) is identified on the coupons' skyward surface, exposed during winter, after two years of exposure [46]. After four years, lepidocrocite [γ-FeO(OH)], goethite [α-FeO(OH)], magnetite (Fe3O4), akagenaite (β-FeOOH) and traces of hematite (Fe2O3) are identified on both sides of the steel specimens for both initial times of exposure. No amorphous corrosion products on steel surface were detected after examination of carbon steel specimens by XRD ( Figure 10) and FTIR ( Figure 11) and also mentioned by other studies [71][72][73][74][75][76][77][78][79]. The corrosion products identified by XRD and FTIR, after four years of exposure, are presented in Figures 10 and 11.  In the case of the Cu specimens tested, both macroscopically and microscopically, cuprite (Cu 2 O) prevalence as the main corrosion product is found. The corrosion products on Cu by OM after four years of exposure, are shown in Figure 12.
In the case of Cu, increased concentrations of O and Cl − are detected by SEM/EDS. Cu exhibits the highest concentration of chlorides among the tested metals and the second higher concentration of C. On the skyward side of Cu specimens (×100), after four years of exposure, the % atomic concentration of chloride is 10.3%, independent of the initial time of exposure. The surface analysis by SEM/EDS on Cu surface, after four years of exposure, is presented in Figure 13.
Growth of Cu 2 O on both the upper and lower sides of the Cu specimens has been observed since the first semester of exposure. Cu 2 O is identified as the only corrosion product during the first two years of exposure by XRD. After four years of exposure, on both sides of the specimens (i) Cu 2 O is identified as the main corrosion product, (ii) atacamite [Cu 2 Cl(OH) 3 ] is also identified, as a result of the salinity on the specimens' surface. The corrosion products identified by XRD, after four years of exposure, for both initial times of exposure, are presented in Figure 14.
In the case of Zn, no significant corrosion impact is microscopically observed during the four years of exposure. The low S concentration detected in Zn specimens by EDS, with the simultaneous absence of an S-containing corrosive product by XRD, proves a low SO 2 concentration in the LGMG area. Zn surface also measures the highest concentration of C among the tested metals, caused by aircraft fuel emissions, and the second higher concentration of oxygen, after carbon steel specimens, probably due to the synthesis of the corrosion products detected on its surface, after four years of exposure.
Chlorides are detected on the specimens' surface, after four years of exposure, due to the proximity to the seacoast. The relative high TOW favors the dissolution of Zn chlorides in the moisture film.
Corros. Mater. Degrad. 2020, 1 FOR PEER REVIEW 12 Figure 11. Examination of carbon steel specimens-initially exposed during winter-by FTIR, after 4 years of exposure at the LGMG. FTIR absorption bands correspond to chemical bonds which can be attributed to the crystal phases presented in the figure.
In the case of the Cu specimens tested, both macroscopically and microscopically, cuprite (Cu2O) prevalence as the main corrosion product is found. The corrosion products on Cu by OM after four years of exposure, are shown in Figure 12. In the case of Cu, increased concentrations of O and Cl − are detected by SEM/EDS. Cu exhibits the highest concentration of chlorides among the tested metals and the second higher concentration Figure 11. Examination of carbon steel specimens-initially exposed during winter-by FTIR, after 4 years of exposure at the LGMG. FTIR absorption bands correspond to chemical bonds which can be attributed to the crystal phases presented in the figure. Figure 11. Examination of carbon steel specimens-initially exposed during winter-by FTIR, after 4 years of exposure at the LGMG. FTIR absorption bands correspond to chemical bonds which can be attributed to the crystal phases presented in the figure.
In the case of the Cu specimens tested, both macroscopically and microscopically, cuprite (Cu2O) prevalence as the main corrosion product is found. The corrosion products on Cu by OM after four years of exposure, are shown in Figure 12.  Corros. Mater. Degrad. 2020, 1 FOR PEER REVIEW 13 of C. On the skyward side of Cu specimens (×100), after four years of exposure, the % atomic concentration of chloride is 10.3%, independent of the initial time of exposure. The surface analysis by SEM/EDS on Cu surface, after four years of exposure, is presented in Figure 13. Growth of Cu2O on both the upper and lower sides of the Cu specimens has been observed since the first semester of exposure. Cu2O is identified as the only corrosion product during the first two years of exposure by XRD. After four years of exposure, on both sides of the specimens (i) Cu2O is identified as the main corrosion product, (ii) atacamite [Cu2Cl(OH)3] is also identified, as a result of the salinity on the specimens' surface. The corrosion products identified by XRD, after four years of exposure, for both initial times of exposure, are presented in Figure 14. In the case of Zn, no significant corrosion impact is microscopically observed during the four years of exposure. The low S concentration detected in Zn specimens by EDS, with the simultaneous absence of an S-containing corrosive product by XRD, proves a low SO2 concentration in the LGMG area. Zn surface also measures the highest concentration of C among the tested metals, caused by aircraft fuel emissions, and the second higher concentration of oxygen, after carbon steel specimens,      In the case of Al, no significant corrosion impact is observed by OM, even after four years of exposure. O, S, C and traces of chlorides are detected by SEM (Figure 17), after a 4-year exposure period, despite the background pollution, the proximity to the sea, and the Al susceptibility to pitting corrosion.
Corros. Mater. Degrad. 2020, 1 FOR PEER REVIEW 16 In the case of Al, no significant corrosion impact is observed by OM, even after four years of exposure. O, S, C and traces of chlorides are detected by SEM (Figure 17), after a 4-year exposure period, despite the background pollution, the proximity to the sea, and the Al susceptibility to pitting corrosion. No products, at both sides of the specimens, are identified by X-ray diffraction analysis on the Al surface, probably due to the small thickness of the corrosion layers.
By AFM, the mean roughness Sa (arithmetical mean height) of the 400 μm 2 projected areas of the skyward side of the Al 1050, before the exposure, after two and four years of exposure during summer and winter, is presented in Table 6. After two years of exposure: (i) the Sa doubles and the rolling lines appear to be filled with corrosion products and (ii) no seasonal deviations are observed regarding the roughness evolution of the Al surface. After four years of exposure, the Sa and the highest pitting depth Sv of the 400 μm 2 projected areas (1.157 μm during summer and 1.035 μm during winter) reveal a higher impact on the surface of the specimens exposed during summer, mainly due to the effect of higher concentration of chlorides and particulate matters (PM). The surface morphology development of the skyward side of Al 1050 by AFM, after four years of exposure is presented in Figure 18. No products, at both sides of the specimens, are identified by X-ray diffraction analysis on the Al surface, probably due to the small thickness of the corrosion layers.
By AFM, the mean roughness S a (arithmetical mean height) of the 400 µm 2 projected areas of the skyward side of the Al 1050, before the exposure, after two and four years of exposure during summer and winter, is presented in Table 6. After two years of exposure: (i) the S a doubles and the rolling lines appear to be filled with corrosion products and (ii) no seasonal deviations are observed regarding the roughness evolution of the Al surface. After four years of exposure, the S a and the highest pitting depth S v of the 400 µm 2 projected areas (1.157 µm during summer and 1.035 µm during winter) reveal a higher impact on the surface of the specimens exposed during summer, mainly due to the effect of higher concentration of chlorides and particulate matters (PM). The surface morphology development of the skyward side of Al 1050 by AFM, after four years of exposure is presented in Figure 18. Pitting is detected on Al specimen's surface, but in a much smaller extent than theoretically expected and only after two years of exposure, due to (i) the pollution of the area (low concentration Pitting is detected on Al specimen's surface, but in a much smaller extent than theoretically expected and only after two years of exposure, due to (i) the pollution of the area (low concentration of SO 2 and chloride deposition rate at the range of 0-20 mg/m 2 d, as described in a following paragraph); (ii) the existing particulate matters in the area, augmented seasonally by the North African dust; (iii) the meteorology of the area during summer (low RH-TOW, absence of precipitation, high temperatures and low wind speed or calm) and (iv) the presence of the aircraft in the area. During the transition spring and autumn periods, the impact of African dust reaches its peak and increases the particulate matters' concentrations in the Greek region [80]. The mean monthly concentration of PM, during the transition spring and autumn periods, is 25-40 µg/m 3 [80]. The continuous take-offs/landings and technical tests, during summer (driest months), provoke the maximization of the concentration of the pollutants locally, the continuous resuspension and dry re-deposition of the contaminated by the pollutants and by chlorides' (due to the proximity to the sea) particulate matters, on their peak concentration. These effects lead to a relatively higher pitting, in density and depth, of the Al exposed, starting in summer, in relation to the Al exposed, starting in winter, as it is presented in Table 7. The rating system for the evaluation of pitting corrosion on Al was performed in accordance with ISO 8993 [81], after 2 and four years of exposure. The ISO rating has been conducted visually and the estimation of the average pitting depth in µm by OM. Due to the combustion of fossil fuels at the airport region, an atomic concentration of at least 11.5% of C is detected to all metal specimens' surfaces by SEM, after the first two years of exposure.

Classification of the Corrosivity of the Pachi Airport Atmosphere
With a view to the development and the specification of optimized corrosion evolution and protection for manufactured products, data on the corrosivity of the atmosphere are considered essential. The corrosivity category is a technical characteristic which provides a basis for the selection of materials and, consequently, protective measures in atmospheric environments subject to the demands of the specific application, particularly with regard to service life [9].
The airport atmosphere is classified by S-containing substances represented by SO 2 , in accordance with ISO 9223 [6], in pollution category P 0 ([SO 2 ] < 12 µg/m 3 ), which is accounted to be background pollution by SO 2 and insignificant from the view point of corrosion. The TOW is estimated in 2439 h/year. As a result, the atmosphere is classified of TOW as «T3», according to ISO 9223:1992 [6].
Considering the (i) the corrosion rate of Cu, (ii) the development of corrosion products on the tested metals' surface, (iii) the pitting corrosion of Al and (iv) the atomic Cl concentration on the tested metals' surface, during the first four years of exposure, it is estimated that the salinity deposition rate at the LGMG does not exceed the threshold of 20 mg/(m 2 d), which is the threshold deposition rate that would result in significant material deterioration [82]. Thus, the deposition rate of chlorides expected at the range of 0-20 mg/(m 2 d), seems to be better related to the observed corrosive environment. Therefore, the atmosphere of the airport, in relation to airborne salinity pollution, is rated as pollution category S 0 , chloride deposition rate lower than 3 mg/(m 2 d), or as pollution category S 1 , chloride deposition rate in mg/(m 2 d): 3 < S < 60, in accordance with the standard ISO 9223 [6].
The characterization of an outdoor test site with respect to its corrosivity can be accomplished by determining the corrosion rate of standard specimens exposed for one year to the atmosphere at the respective location (direct corrosivity evaluation). The average chemical composition of Al (>99.5% minimum) and carbon steel (Table 1) specimens used at this study meet the requirements described by ISO 9226 [9]. The corrosion rate of carbon steel and Al for the first year of exposure for the five different corrosion categories, according to ISO9223, is presented in Table 8. The classification of the atmospheric corrosivity, for carbon steel and Al is presented in Table 9. The higher first-year corrosion rate of carbon steel specimens, exposed during summer, is primarily caused by the background pollution of the area and the high conductivity of the steel specimens' surface due to the existing PM in the area enriched by the North African dust (PM) during the initial time of exposure. The higher corrosion rate for the first-year of Al, exposed during winter, can be attributed to an easier Al 3+ diffusion through the formed oxide with the humidity presence. The critical parameters taken into consideration in order to evaluate the atmosphere aggressivity, according to the CDA, are presented in Table 10.

Corrosion Patterns Related to Each Metal Type
The main findings assessed by the 4-year atmospheric corrosion experiments at the LGMG can be summarized as follows: In the case of carbon steel, the high RH-TOW during the period December-March, the decisive influence of the rainfall during winter and of temperature, during January and February, increase the corrosion of steel. Multi-year corrosion evolution shows that the sea chlorides, from natural airborne salinity, have an accelerating effect on the corrosion rate of steel, that is also observed by other researchers [83,84]. Taking into account the zero influence of sulfur-containing substances on atmospheric corrosion of the tested metals at the LGMG microclimate, the low corrosion rate of steel specimens also indicates a relatively low chloride deposition rate. The O 3 pollutant has little effect in steel corrosion rate [85]. Unalloyed carbon steel showed increased corrosion among the tested metals.
During the 30-year corrosion projection, the factors which led to a relatively high corrosion rate of the steel samples are: (i) The high relative humidity, the atmospheric precipitation (rain) and the temperature play the primary role. (ii) Salinity and particulate matters play a secondary role to the corrosion rate. (iii) Finally, the synergy of the above factors with the air pollutants (aircraft emissions, etc.).
In the case of Al, S compounds and salinity affect the "a" value much less than the other three metals [68]. Al exhibits the lowest "a" value than the other tested metals (Table 4). Al also exhibits the lowest time exponent "b" values than the other metals tested, which verifies the corrosion protectiveness of the corrosion product layer of Al 2 O 3 on the metal surface. The "b" values are not strongly affected by environmental variations, due to the Al 2 O 3 spontaneous formation upon exposure in the environment, which protects the metal substrate. However, despite the low exponent values observed, the "b" shows higher values in the specimens starting exposure in the summer than those in winter, which shows the following: (i) In the summer months, under the influence of airborne salinity and particulate matters, the corrosion product layer on Al surface is less protective than its counterpart in the winter months, where higher TOW and rainfall prevail. (ii) Airborne salinity and PM are anticipated to play the dominant role in the corrosion of aluminum in these atmospheres (Figure 5b).
During the four first years of exposure, relative high RH-TOW and rainfall, during the period December-March, and the mean monthly temperature, during January and February, also guide to the relatively higher corrosion attack. During the 4-year corrosion, evolution is observed that the corrosion values of Al specimens is less than 0.30 g/m 2 a, mainly due to the metal attack by the chemical solution used during chemical removal of the alumina film during cleaning in order to calculate the gravimetric weight loss rather than by the aggressivity of the atmosphere [84]. After 5.5 years of exposure, the corrosion rate of the Al specimens, exposed during summer, is anticipated to be higher than those exposed during winter, mainly due to the impact of salinity, because of the proximity to the sea, and the effect of the particulate matters, as it is also observed by other researchers [83]. Al corrosion rate is the lowest among the tested metals, two orders of magnitude lower than that of steel.
During the 30-year corrosion evolution, the factors which lead to a relatively high corrosion rate of the Al surfaces are: (i) Chlorides and PM are anticipated to be the most important causes of corrosion of Al alloys in the specific atmosphere. (ii) The high RH, the atmospheric precipitation (rain) and the temperature play a secondary role. (iii) Finally, the synergy of the above factors with the pollutants.
In the case of Cu, salinity and TOW strongly affect both the time exponent and the "a" values [68]. During the multi-year corrosion projection, Cu corrosion rate is an order of magnitude lower than that of steel and independent of the initial period of exposure. Cu has lower corrosion rate than steel because of its low thermodynamic tendency to react (noble potential compared to iron). Cu also exhibits the highest coefficient of determination value (R 2 = 0.99). The corrosion rate of Cu, which is less than 2 µm/year (Table 5) in the first four years of exposure, indicates that salinity is less than 20 mg/(m 2 d) Cl − [83]. Moisture, salinity, precipitation (rainfall) and O 3 are the factors playing a decisive role in corrosion of Cu in the airport area.
During the 30-year corrosion projection, the factors which led to a relatively high corrosion rate of the Cu samples are: (i) The high relative humidity, the atmospheric precipitation (rain) and the concentration of O 3 in the atmosphere are the dominant factors in the long-term corrosion of Cu. (ii) Chloride deposition rate has a secondary, but significant, role in corrosion rate.
In the case of Zn, the environmental variables do not significantly affect the protectivity of the corrosion product layer on the metal surface. In more detail, TOW and chlorides influence the time exponents to a small extent [68].
During the four years of exposure: (i) From the first year of exposure, Zn exhibits a corrosion rate dependent of the period initially exposed and an order of magnitude lower than steel, a fact that has been observed by other researchers [86]. Higher RH, during the initial time of exposure, plays a catalytic role in the corrosion rate of Zn [86], especially during the first four years of exposure. The synergistic effect of the relatively high moisture with SO 2 [56] and relatively high O 3 concentration [87] in the atmosphere increases its corrosion rate. (ii) The exponent "b" shows values far higher for the specimens exposed in the summer. The corrosion layer of the specimens exposed during the summer, under the influence of the airborne salinity, the particulate matters and the maximizing of concentration of the pollutants (mainly CO 2 and O 3 ) is less protective than its counterpart of the specimens exposed during the winter months, where high humidity and, especially, atmospheric precipitations (rainfall) provoke a washing out of the chlorides and pollutants from the metal surfaces.
In a marine atmosphere, the corrosion of Zn is a direct function of TOW and the chloride pollution level [88]. After 5.5 years of exposure, the anticipated corrosion evolution shows that Zn specimens exposed during summer exhibit a steadily higher corrosion rate, than those exposed during winter, in contrary with the first years of exposure. The 30-year corrosion evolution of Zn shows that the specimens initially exposed during summer are anticipated to have twice the weight of metal loss than those exposed during winter (Table 4), mainly due to the effect of: (i) Higher salinity deposition rate. (ii) Higher concentration of PM (African dust, particle resuspension and redeposition due to aircraft take-offs and landings, etc.). (iii) Higher concentration of pollutants, especially of CO 2 , mainly from the combustion fuels of aircraft. (iv) Higher O 3 concentration.
(v) The decisive effect of the rain on washing out the chlorides and the pollutants from the tested metals' surface during winter.

Aspects of Gravimetric Data Analysis and Interpretation
The gravimetric data acquired for the exposure starting at winter showed that higher weight loss values are obtained during the first three months for Al, steel and Zn causing deviations from fitted curves. This can be attributed to the water-solubility of the initial corrosion products. From the 6-month experimental data, it is evident that both corrosion film dissolution and water-insoluble corrosion products' accumulation takes place.
The chloride deposition rate in the LGMG is estimated on the basis of the: (i) The corrosivity of the atmosphere regarding carbon steel and Al classification as C2 "low", according to ISO 9223. (ii) The low concentration of chlorides on the Al, Zn and steel surfaces.
(iii) The pitting corrosion observed on Al surface, with maximum depth of 2 µm, after four years of exposure, at a distance of approximately 0.2 km from the seacoast. (iv) The average annual loss of Cu, less than 2 µm/year during the first four years of exposure.
Concerning the results of gravimetric analysis on carbon steel and aluminum specimens, after the first year of exposure, with initial time of exposure the 25th of May and the 25th of November of each year from 2014 to 2019: (i) The higher first-year corrosion rate of carbon steel specimens, exposed during summer, is primarily caused by the salinity and the background pollution of the area. The high conductivity of the steel surface by particulate matters acts as seeding for the water vapors to form water droplets.
The seasonal presence of the African dust increases the effect. (ii) The higher first-year of aluminum, exposed during winter, can be attributed to an easier Al 3+ diffusion through the formed oxide with the humidity presence.

Comparison of Three Different Approaches for Corrosive Environment Classification
The classification of atmospheric aggressivity and the expected corrosion damage to carbon steel and Al alloy components of the aircrafts at the Airport, according to the ISO and the CDA [18,19] methodologies and the Europe and Asia Corrosion Map [89], are presented in Figures 19 and 20.
Corros. Mater. Degrad. 2020, 1 FOR PEER REVIEW 22 (i) The higher first-year corrosion rate of carbon steel specimens, exposed during summer, is primarily caused by the salinity and the background pollution of the area. The high conductivity of the steel surface by particulate matters acts as seeding for the water vapors to form water droplets. The seasonal presence of the African dust increases the effect.
(ii) The higher first-year of aluminum, exposed during winter, can be attributed to an easier Al 3+ diffusion through the formed oxide with the humidity presence.

Comparison of Three Different Approaches for Corrosive Environment Classification
The classification of atmospheric aggressivity and the expected corrosion damage to carbon steel and Al alloy components of the aircrafts at the Airport, according to the ISO and the CDA [18,19] methodologies and the Europe and Asia Corrosion Map [89], are presented in Figures 19 and  20. Figure 19. Section of the Corrosion Damage Algorithm that considers distance to salt water, leading either to the very severe AA rating (site of exposure: red path) or a consideration of the moisture and the pollutants and the expected corrosion damage to carbon steel and Al components of aircraft at the LGMG [18,19]. Figure 19. Section of the Corrosion Damage Algorithm that considers distance to salt water, leading either to the very severe AA rating (site of exposure: red path) or a consideration of the moisture and the pollutants and the expected corrosion damage to carbon steel and Al components of aircraft at the LGMG [18,19]. The results of the three methodologies employed for the classification of the corrosivity of the LGMG atmosphere are presented in Table 11: Table 11. Synoptic comparison of the results of the classification of the corrosivity of the LGMG atmosphere according to ISO [6-9] and CDA [18,19] methodologies, and Europe and Asia Corrosion Map [89].

Site of Exposure
Classification of the Corrosivity of LGMG Atmosphere According to:

Carbon Steel Aluminum
LGMG ISO C2 «LOW» C2 «LOW» CDA AA «very severe» «Europe and Asia Corrosion Map» «SEVERE» After a comparison of the results of the meteorological and pollution data, and of the gravimetric results on carbon steel and Al specimens exposed at the coastal site of Pachi to the The results of the three methodologies employed for the classification of the corrosivity of the LGMG atmosphere are presented in Table 11: Table 11. Synoptic comparison of the results of the classification of the corrosivity of the LGMG atmosphere according to ISO [6-9] and CDA [18,19] methodologies, and Europe and Asia Corrosion Map [89].

Site of Exposure
Classification of the Corrosivity of LGMG Atmosphere According to:

Carbon Steel Aluminum
LGMG ISO C2 «LOW» C2 «LOW» CDA AA «very severe» «Europe and Asia Corrosion Map» «SEVERE» After a comparison of the results of the meteorological and pollution data, and of the gravimetric results on carbon steel and Al specimens exposed at the coastal site of Pachi to the expected corrosion damage, estimated by the CDA and the Europe and Asia Corrosion Map, it is proved that both the CDA and Europe and Asia Corrosion Map do not provide a good correlation between the predicted and the actual corrosion damage at the LGMG. On the contrary, the ISO classification methodology provides a good correlation among corrosivity of atmosphere and actual carbon steel and Al corrosion damage in the specific atmosphere.

1.
LGMG atmosphere is classified, according to the ISO 9223: TOW was characterized as T3. The area has been classified in pollution category P 0 , which is considered to be background pollution by SO 2 and insignificant from the point of view of corrosion attack. The corrosivity of the atmosphere, regarding carbon steel and Al, has been classified as C2 "low". The chloride deposition rate in the LGMG is estimated at the range of the values 0 < S < 20 mg/m 2 d, and the area has been classified in pollution category S 0 or S 1. 2. The 4-year experimental weight loss curves show that: The corrosion rates at the coastal site of Pachi are ranked in order of decline: carbon steel > Cu> Zn > Al. No seasonal deviations are observed regarding the corrosion rates of Cu specimens during the exposure. Corrosion rate of Al is two orders lower than steel. The corrosion value of Al specimens is partially due to the metal attack by the chemical reagent used during chemical cleaning in order to calculate the gravimetric weight loss. Corrosion rate of Zn and Cu is an order lower than steel.
During the first four years of exposure, the specimens exposed during winter show higher corrosion rates than those exposed during summer. RH is identified as the major factor of corrosion of the tested metals. Precipitation and temperature are also recognized as main corrosion factors. Depending on the metal, these factors, in combination with: (i) Airborne salinity, PM and the high concentration of O 3 lead to a relatively high corrosion rate of Cu. (ii) Airborne salinity and CO 2 lead to a higher corrosion rate of Zn. (iii) Airborne salinity and PM lead to a higher corrosion rate of steel and Al alloy. Uniform corrosion is observed on the surface of the steel specimens and pitting corrosion is observed on the surface of the Al. 3. During the 30-year corrosion evolution: In the case of carbon steel, the specimens exposed during winter show higher corrosion rates than those exposed during summer. The steel corrosion rate is the highest among the metals tested.
In the case of Cu, the metal specimens exposed during winter show higher corrosion rates than those exposed during summer.
In the case of Zn, the metal specimens exposed during summer are expected to show higher corrosion rates than those exposed during winter, after 5.5 years of exposure. Zinc specimens, exposed during summer, are expected to have double metal loss than those exposed during winter, after 30 years of exposure.
In the case of Al, the metal specimens exposed during summer are anticipated to show higher corrosion rates than those exposed during winter, after 5.5 years of exposure. The corrosion rate of Al is expected to remain the lowest among the tested metals and by two orders lower than steel. The corrosion curves, as well as the evolution of the maximum pitting depth, indicate the self-stopping nature of pitting corrosion of aluminum. 4. After a comparison of the results of gravimetric analysis on carbon steel and Al specimens to the expected corrosion damage estimated by the CDA and the classification of atmospheric aggressivity according to the Europe and Asia Corrosion Map, it is proved that the CDA and the Europe and Asia Corrosion Map do not provide a good correlation between the predicted and the actual corrosion damage at the LGMG, regarding carbon steel and Al. The ISO classification methodology provides a good correlation among corrosivity of atmospheres and actual carbon steel and aluminum corrosion damage in the specific atmosphere.