1 Introduction
Electropolishing is an efficient polishing process for metal materials in concentrated electrolytes; it generates a damage-free surface because the material is removed through anodic dissolution [1–3]. Atomic and close-to-atomic scale accuracy is possible with the electrochemical machining and electropolishing method because the material is removed atom by atom in the anodic dissolution [4–6]. Electropolishing of the surfaces fabricated by laser powder bed fusion (L-PBF) has been reported as an effective method to improve the surface roughness [7–9] and remove the outmost layer with residual stress without causing thermal and mechanical stress [10,11]. Lyczkowska-Widlak et al. [12] compared the electropolished and ground 316L SS samples fabricated by L-PBF and reported that electropolishing increased the corrosion resistance of sample considerably compared with grinding. Zhang et al. [13] studied the electropolishing of L-PBF-fabricated Inconel 718 part surfaces and found that the electropolishing enables to dissolve the hardening phase and relieve residual stress, resulting in lower nanohardness and elastic modulus. Urlea and Brailovski [14,15] studied the electropolishing of L-PBF-fabricated Ti-6Al-4V and IN625 multiple surfaces, which were oriented with respect to the power bed under different angles from 0° to 135°. All the surfaces were electropolished to a lower surface roughness independent of the different surface roughness caused by the changed angle. L-PBF-fabricated components suffer from process-induced imperfections, such as high residual stresses and micropores [16,17]. Residual stresses and micropores are the main reasons for the failure and low performance of some alloys fabricated by L-PBF under fatigue loading. Electropolishing was used to measure residual stresses with different depths generated by the L-PBF process to remove the sample surface layer [10,11,18]. This condition is due to the material removal performed by anodic dissolution, which generates a damage-free surface in the absence of thermal and mechanical stress [3].
Mechanical properties of 316L SS fabricated by L-PBF show anisotropic characterization and have greatly attracted the interest of researchers [19–22]. Alsalla et al. [20] fabricated 316L SS with different building orientations, measured the fracture toughness, and found that the presented defects, such as pores and cracks, were influenced by the different building orientations, thereby affecting fracture toughness, strength, and total elongation. Mertens et al. [19] performed uniaxial tensile testing on samples fabricated with different main orientations with respect to the same orientation direction. The mechanical behavior showed a strong anisotropy, which was related to the microstructures and processing conditions. Ni et al. [23] clarified the mechanical properties of 316L SS fabricated by L-PBF using tensile experiments and reported the anisotropy properties closely related to the grain sizes and boundaries, which were dissimilar in the different surfaces with respect to the building orientation. Kong et al. [21] reported that a lower resistance to deformation along the building orientation of 316L SS fabricated by L-PBF was confirmed because most grain boundaries were parallel to the loading direction.
The corrosion behavior of 316L SS fabricated by L-PBF is influenced by the microstructures, which can be optimized by adjusting the process parameters, such as the scanning speed and laser power. Voids or international porosities are generally formed in the L-PBF process under two completely different conditions of insufficient [24,25] and excessive heat input [26]. The insufficient heat input leads to lack-of-fusion voids, and the excessive heat input leads to keyhole-induced pores. A lower energy density or large scanning space causes less overlap or even no overlap between scanning lines, resulting in changes in the wetting and thermal conditions of the melt pool. If the molten material fails to wet the previous layer and/or hatch line, lack-of-fusion voids form because the molten material is insulated by surrounding powder [24]. Keyhole-induced porosities are mostly formed due to occurrence of local cod zones with higher surface tension and insignificant recoil pressure, and a parametric study has shown that a keyhole is formed when exceeding a certain threshold of input power [27]. Finer microstructures and minimum manufacturing defects could be obtained during the L-PBF of 316L SS by adjusting the scanning speed, thereby leading to better biocompatibility due to the increase in corrosion resistance and decrease in toxicity ion release [28]. In general, fast scanning speeds generated more voids, inside of which oxide power and nonmelt silicon were found. Therefore, the number of pitting sites increased with increasing scanning speed due to pits that occurred preferentially at the voids [29]. 316L SS showed improved corrosion resistance and biocompatibility when fabricated by L-PBF at high laser power, and more subgrain boundary and dislocation were found in the L-PBF-fabricated sample than the wrought 316L SS, thereby promoting the formation of passive film to better corrosion resistance [30]. The influence of L-PBF parameters on the anisotropic properties of fabricated parts has been widely studied [31,32], and many studies [33,34] focused on the mechanical properties and corrosion behavior of L-PBF parts. However, reports about the influence of orientation effect on the electropolishing process of L-PBF 316L SS parts were few.
The distinction in electropolishing characteristics on different surfaces of 316L SS fabricated by selective laser melting is studied. Different surfaces corresponding to the building orientation are electropolished, and the surface finish, surface composition of the passive oxide layer, and corrosion resistance are investigated. This study can be used to understand the anisotropy in corrosion resistance on different surfaces of 316L SS fabricated by L-PBF although the sample is electropolished. Thus, the knowledge gap in the anisotropy study on the different surfaces of 316L SS fabricated by L-PBF is filled.
2 Experimental approach
316L SS samples were fabricated by L-PBF with the stainless-steel CL 20ES powders (316L) (Concept Laser, Lichtenfels, Germany). The laser power was 100 W, and the scanning speed was 600 mm/s. The layer thickness was 25 μm. The laser spot size and scanning space were 50 and 84 μm, respectively. The sample size was designed as 10 mm × 20 mm × 2 mm for electropolishing. The unpolished surface of the sample was insulated from the electrolyte by coating with an aerosol conformal coating (RS Components, Ltd., UK). The study on electropolishing original 316L SS surface fabricated by L-PBF is presented separately. This study is focused on the electropolishing characteristics of the different surfaces corresponding to the orientation direction. Therefore, the polishing side was uniformly ground with 600 grit abrasive sandpaper to smoothen the rough surface obtained from L-PBF. The electrolyte for electropolishing consisted of H2SO4 (98%), H3PO4 (85%), and glycerol in the volume ratio of 5:4:1, which has shown good electropolishing effect for 316L SS in the previous research [1,35]. All the electrolyte compositions were purchased from the Mistral Industrial Chemicals, UK. The NaCl solution in the concentration of 3 mol/L was used for all the electrochemical analysis at room temperature. Each electrochemical measurement was repeated at least three times for higher credibility. Figure 1 shows the experimental setup, and the details can be found in the previous research [1,35]. The electropolishing potential was supplied by a potentiostat/galvanostat CS310, which was also used for the electrochemical analysis. The hotplate stirrer was used to heat the electrolyte and cooperated with a thermal sensor to control the electrolyte temperature. A magnetic stir bar was used to stir the electrolyte with the speed range of 100–2000 r/min. The samples were cleaned using distilled water and ethanol in sequence in an ultrasonic agitation bath for 3 min before the electropolishing process. The electrochemical impedance measurement was carried out on the potentiostat/galvanostat CS310, and the measured spectra were fitted with the accessory software. VHX-5000 digital microscope, 3D optical profiler (NPFLEX), and Omicron NanoTechnology MXPS system with a dual X-ray anode (Omicron DAR 400) were used for the surface characterization.
3 Results and discussion
3.1 Electropolishing different surfaces
Figure 2 shows the schematic of the L-PBF of 316L SS, in which the building orientation is the Z-axis. The horizontal surface is perpendicular to the building orientation, and the vertical surface is in parallel with the building orientation. Both surfaces, horizontal and vertical surface, were electropolished in an H2SO4-based electrolyte, and the electrochemical analysis of electropolished surface was performed in NaCl solution.
Figure 3 shows the polarization curves of different plans at the electrolyte temperature of 28 °C and 66 °C. Under the electrolyte temperature of 28 °C, the current density increases with increasing the applied potential in the range of 1.4 to 3 V with the vertical surface. However, a limiting current density plateau region (LCDPR) [3], where the best electropolishing effect can be obtained, can be observed evidently with the horizontal surface. In the LCDPR, the passive oxide film on the workpiece surface increases with increasing applied potential, slight change in the current density. On the contrary, the thickness of passive oxide film on the vertical surface does not change with increasing applied potential under the electrolyte temperature of 28 °C, thereby increasing the current density with the potential. Under the electrolyte temperature of 66 °C, the LCDPR can be observed on the horizontal and vertical surface, as shown in Fig. 3(b). Hence, the thickness of passive oxide film on the vertical surface increases along with the applied potential in the LCDPR when the electrolyte temperature is increased to 66 °C. The potential width of the LCDPR with the vertical surface is much narrower than the horizontal surface, indicating that the stability of the passive oxide film on the horizontal surface is higher than the vertical surface. Figure 4 shows the current density transients with different plans at the electrolyte temperature of 28 °C and 66 °C with the electropolishing duration of 20 min. The applied potential of 2 V was determined by the LCDPR shown in Fig. 3 to obtain the best electropolishing effect. The current density with the vertical surface is slightly higher than the horizontal surface, which coincides with the polarization curves in Fig. 3. The current density decreases at the initial stage of electropolishing, which agrees with a traditional electropolishing process because a passivation process occurs on the sample surface [3]. A high electrolyte temperature is necessary for electropolishing vertical surface to obtain better electropolishing effect because the polarization curves of the vertical surface only show the critical LCDPR at the electrolyte temperature of 66 °C.
Figure 5 shows the electropolished horizontal and vertical surfaces with the electrolyte temperature of 66 °C. Smooth surfaces can be obtained due to the sufficient electropolishing effect, and the surface roughness Sa was decreased to 35 and 55.7 nm with the horizontal and vertical surface, respectively. Moreover, many defects generated by the electropolishing are shown in Fig. 5. The defects in electropolishing are normally generated by corrosion, and corrosion pits have different appearances with the defects in Fig. 5. Hence, the defects are generated in the L-PBF process. L-PBF is a significantly complicated process because the performance is influenced by many parameters, such as laser power, layer thickness, and chamber environment. Therefore, defects are easily generated when these parameters could not be optimized effectively. Zhang et al. [36] classified the common defects in three types: Porosities, incomplete fusion, and cracks. The common defects have also been categorized in equipment-related, power-related, and processing-related defect formations [37]. Liverani et al. [38] summarized that mainly three types of defects are observed in the 316L SS fabricated by L-PBF, namely, 1) binding defects, 2) pores, and 3) layered voids. On the basis of the previous reports and the defects that appeared in this study, the observed defects are classified into two types, namely, process-related defects and gas-related defects. The defects related to the lack of fusion of powder particles are process-related defects. The particle fusion can be influenced by many processes, such as the quality and cleanness of the mirrors, laser power, and scanning speed. Unmelted particles are caused by insufficient fusion, which could result in low junction quality between adjacent layers and adjacent melt pools. The process-related defects are characterized by irregular shape and unmelted particles inside. The unmelted particle can be observed clearly in the ellipse marked as “A” in Fig. 5(b). The defects are considered gas-related defects when the formation process is related to the included gas during the solidification process. The gas between the powder particles may dissolve in the molten pool, especially when the packing density of metal powders is low. In addition, the gas solubility in the molten pools can be high because of the high molten pool temperature generated by the intense laser power. The gas-related defects are typically smaller with a spherical shape. The two types of defects can be observed on electropolished surfaces in Fig. 5. Moreover, the number of defects on the electropolished vertical surface is greater than the horizontal surface, as shown in Fig. 5. The gas-related defects are normally generated in one laser scanning layer, and the process-related defects can be generated not only in a single layer but also the interface of adjacent layers. Defect size, shape, and densification can be varied by changing the melting pool size and overlapping between neighboring melt pools during the L-PBF process [39]. For example, a shallow melt pool can be formed by changing the laser transforms from the Gaussian beam to the flat-top beam due to the uniform distribution of the energy and decreased power density [40]. This condition causes weak layer-to-layer bonds, resulting in more unfused defects.
Figures 5(a) and 5(b) show that the defect edges were smoothened by the electropolishing because the electropolishing current density concentrates on the defect edges, resulting in a higher material removal rate. To compare the original and electropolished defect edges, 316L SS fabricated by L-PBF was uniformly ground with 600, 1200, and 2500 grit abrasive sandpaper in sequence, and then mechanical polished using the colloidal silica polishing suspension with micro sizes of 3 and<1 µm. Figure 6 shows the different surfaces after grinding and mechanical polishing. The edges of defects are significantly shaped compared with the defects shown in Figs. 5(a) and 5(b), especially on the vertical surface, because electropolishing rounds the defect edges due to the higher electrochemical dissolution rate. In addition, Fig. 6 also shows that the number of defects on the vertical surface is higher than the horizontal surface, and the process-related defects are the dominant defects on the vertical surface, which are the same as the electropolished surfaces shown in Fig. 5. Therefore, electropolishing enables modifying the defect edges but not eliminating the defects. Figure 7 shows the electropolished surface roughness Sa from the horizontal and vertical surface with different electrolyte temperatures. The vertical surface shows a higher surface roughness Sa than the horizontal place because the electropolished vertical surface has a greater number of defects, as shown in Fig. 5.
Fig.5 Electropolished horizontal and vertical surface with the electrolyte temperature of 66 °C. The applied potential was 2 V, and the stirrer speed was 667 r/min. The electropolishing duration was 1200 s. Optical microscope image of the electropolished (a) horizontal and (b) vertical surfaces; contour image of the electropolished (c) horizontal and (d) vertical surfaces; and topography of the electropolished (e) horizontal and (f) vertical surfaces. The ellipse and square indicate the process-related defects and gas-related defects, respectively. |
3.2 X-ray photoelectron spectroscopy (XPS) spectra analysis
The compositions of different electropolished surfaces were investigated by XPS spectra. Figure 8 shows the XPS survey spectra of the electropolished different surfaces with the electrolyte temperature of 66 °C. Table 1 shows the corresponding chemical composition of the different electropolished surfaces. The O 1s element was the dominant composition for electropolished surfaces because a thick passive oxide film is formed after removing the air-formed oxide film on the workpiece surface during electropolishing [3]. The atomic percentage of the O 1s element was 29.12% on the outmost surface of the electropolished vertical surface; it was lower than the electropolished horizontal surface of 34.43%. Therefore, the electropolished horizontal surface has a thicker passive oxide film due to the higher percentage of O 1s element than the vertical surface. Moreover, the element ratio of Cr/Fe seriously affects the corrosion resistance of the electropolished surface, and higher corrosion resistance corresponds to the higher ratio of Cr/Fe [41,42]. The element ratios of Cr/Fe were 0.84 and 0.72 with the electropolished horizontal and vertical surface, respectively. Therefore, the higher corrosion resistance of the electropolished horizontal surface is expected. This finding coincides with the percentages of O 1s element on the outmost surfaces of different surfaces shown in Table 1.
Tab.1 Chemical compositions of the different electropolished 316L SS surfaces with the electrolyte temperature of 66 °C |
| Component name | Position | Electropolished horizontal surface | Electropolished vertical surface | ||
|---|---|---|---|---|---|
| Area | Atom% | Area | Atom% | ||
| O 1s | 531.0 | 21236.09 | 34.43 | 20111.01 | 29.12 |
| C 1s | 284.0 | 9975.37 | 47.38 | 10812.08 | 45.87 |
| Mn 2p | 640.0 | 6217.98 | 2.12 | 2416.12 | 0.74 |
| Si 2p | 91.0 | 163.97 | 0.95 | 2221.74 | 11.54 |
| Cr 2p | 576.0 | 11634.10 | 4.74 | 9421.14 | 3.43 |
| Ni 2p | 853.0 | 1735.94 | 0.37 | 2051.38 | 0.39 |
| Mo 3d | 231.0 | 796.24 | 0.40 | 1056.07 | 0.47 |
| P 2p | 133.0 | 436.72 | 1.74 | 471.20 | 1.68 |
| S 2p | 168.0 | 195.94 | 0.55 | 29.73 | 0.08 |
| N 1s | 399.0 | 642.21 | 1.69 | 729.21 | 1.72 |
| Fe 2p | 711.0 | 19430.15 | 5.62 | 19231.32 | 4.79 |
Figure 9 shows the high-resolution XPS spectra of Cr and Fe elements. The Cr element exists in the forms of Cr(0), Cr2O3, Cr(OH)3, and CrO3 on the outmost surface of the electropolished horizontal surface. Cr(O) was obtained from the original workpiece composition, and other compositions were generated from electropolishing because a passive oxide film was generated on the workpiece instead of the original film formed in the air. The dominant distribution of Cr element is in the form of Cr(OH)3, which has the binding energy of 577.3 eV, for the different electropolished surfaces. This phenomenon has been reported in the previous study on electropolishing 316L SS [35]. Furthermore, CrO3 was only measured on the electropolished horizontal surface. The CrO3 was reported to exist in the passive oxide film of 316L SS, which is related to a high electrolyte pH and a potential drop across the oxide film [43]. The horizontal and vertical surfaces were electropolished under the same conditions. Thus, the generation of CrO3 in the passive oxide film is also associated with the anisotropy characteristics of the workpiece. Cr6+ is harmful to the environment due to its toxicity property [41]. Therefore, the electropolishing of vertical surface should focus on the eco-friendly environment. High XPS resolution spectra of Iron exists in the forms of Fe(0), FeS, FeO, Fe2O3, and FeOOH on the different electropolished surfaces, indicating that the similar anodic dissolution reactions occur during the electropolishing of different surfaces. The peaks at a binding energy of 710.9 and 711.8 eV in Fig. 9(b) are considered the composition of Fe2O3 and FeOOH, respectively. The dominant Fe2O3 and FeOOH have similar area percentage in the high XPS spectrum of iron from the electropolished horizontal and vertical surfaces, as shown in Fig. 10. This finding verified the occurrence of similar anodic dissolution reactions in the electropolishing of different surfaces. The area percentage of Fe2O3 composition was much higher than that obtained from the electropolishing of commercial 316L SS [35]. This condition is due to the different manufacturing processes of the workpiece that result in the difference in the composition of the oxide film formed on electropolished surfaces.
Figure 11 shows the high-resolution spectra of oxygen on different electropolished surfaces. The measured spectra and the simulated spectra coincide with each other effectively. The O element exists in the forms of O2‒, M-O, Me-OH, H2O, and OH‒. Me-OH is the dominant form of the O element, which agrees with the high-resolution XPS spectra of Cr and Fe element shown in Fig. 9. The electropolishing process has the advantage of forming a new thick passive oxide film on the polished surface, and Fig. 11 shows that the oxidized metal elements mainly existed in the form of Me-OH instead of Me-O, which was observed on the electropolished vertical surface. The M-O composition on the electropolished vertical surface might be from the formation of chromium oxide and/or iron oxides.
3.3 Corrosion resistance
Figure 12 shows the open circuit potentials (OCPs) of the electropolished horizontal and vertical surfaces measured in the 3 mol/L NaCl solution. The OCPs decreased at the initial stage because the thick passive oxide film, which was formed on the workpiece by electropolishing, was dissolved, thereby decreasing the OCP. The OCP reached a stable condition after 50 min. The OCP decreased slowly from 10 to 50 min because the rates of generation and dissolution of passive oxide film on the anode surface are close, and even the dissolution rate was slightly higher. The final stable stage could be obtained when the two rates obtain a balance, in which the generation and dissolution rates are equal. Then, the OCP shows no change even when some electrochemical reactions occur in the passive oxide film. The stable OCP is slightly higher with the electropolished horizontal plan than the vertical surface. Therefore, the electropolished horizontal surface shows slightly higher corrosion resistance than the vertical surface.
Figure 13 shows the anodic polarization scans of the electropolished horizontal and vertical surfaces measured in the NaCl solution. The corrosion potentials were −0.322 and −0.239 V with the electropolished horizontal and vertical surfaces, respectively. Therefore, the electropolished vertical has higher corrosion resistance in the 3 mol/L NaCl solution. A current hump is shown with each curve, thereby implying oxidation of workpiece in the NaCl solution. The current density decreased with increasing applied potential in the current hump because the thickness of passive oxide film increased. A passivation region can be seen after the current hump, and the current density is stable with increasing potential due to an increase in the thickness of passive oxide film. The current density is lower in the passivation region with the electropolished horizontal region than the vertical surface. This finding indicates that the passive oxide layer is thicker on the electropolished horizontal surface. Furthermore, Figs. 5 and 6 show that more pores are found on the vertical surface, and the defects also reduce the corrosion resistance of the electropolished vertical surface. The electropolished surfaces shown in Fig. 5 indicate that the edges of defect have a higher dissolution rate during electropolishing because the current density concentrates on the defect edges. Therefore, the corrosion resistance is reduced by the defect edges due to similar reasons. Moreover, the irregular-shaped lack-of-fusion voids have a detrimental effect on corrosion initiation and propagation compared with the keyhole-induced properties, and this effect is likely due to their crevice-like geometry [44,45]. Few lack-of-fusion voids are observed on the electropolished horizontal surface, as shown in Fig. 5, thereby also causing higher corrosion resistance of the horizontal surface.
Figure 14 shows the electrochemical impedance spectroscopy (EIS) plots of the electropolished horizontal and vertical surface measured in the NaCl solution. The workpiece was immersed in the NaCl solution for 90 min to obtain stable OPCs based on the OCPs shown in Fig. 12. Then, the EIS plots were measured and repeated three times with each workpiece. The EIS Nyquist plots show two capacitive semicircles, and the diameter is smaller with the electropolished horizontal surface in the high-frequency region. The EIS Bode plots show two time constants due to the two peaks. The first time constant is closely related to the passive oxide film on the workpiece surface, and the second one is formed due to the electric double layers between the workpiece and electrolyte. Therefore, the electrical equivalent circuit, as shown in Fig. 15, is used to simulate the measured EIS spectra with two time constants. A constant phase element (CPE) is used instead of a capacitor to simulate the EIS spectrum, considering that the capacitors in the EIS measurements are difficult to fit the spectra accurately. The CPE is expressed in Eq. (1), as follows:
where Q is a constant, n is a constant phase between 0 and 1, i is the imaginary unit, and ω is the angular frequency (ω = 2πf, f being the frequency) [46]. CPE is widely used to obtain a better agreement between the theoretical and the experimentally measured EIS spectra. Rs is the electrolyte resistance, Rct is the charge transfer resistance, and Rct is associated with the high-frequency part of the EIS spectrum. CPE1 and CPE2 represent the capacitances corresponding to high and low frequency, respectively. CPE1 is related to high-speed activities, such as the movement of charge in electric double layers. CPE2 is mainly affected by slow processes, such as the movement of charged species through the oxide film, and Rf is the corresponding resistance [47]. The parameter values in the electrical equivalent circuit were fitted based on the measured EIS spectra, and Table 2 shows the results. The corrosion resistance can be expressed as the total resistance Rtotal, which equals to Rct + Rf, and higher corrosion resistance is expected with larger Rtotal [48]. They were 130.157 and 104.172 kΩ‧cm2 with the electropolished horizontal and vertical surface, respectively. Therefore, the electropolished horizontal surface has higher corrosion resistance than the electropolished vertical surface.
Tab.2 Fitting results of the electrical equivalent circuit. |
| Samples | Rs/Ω | CPE1×10−4 /(Ω−1∙sn∙cm−2) | n1 | Rct/(kΩ∙cm2) | CPE2×10−3 /(Ω−1∙sn∙cm−2) | n2 | Rf/(kΩ∙cm2) | Rtotal/(kΩ∙cm2) |
|---|---|---|---|---|---|---|---|---|
| Electropolished horizontal surface | 3.184 | 3.050 | 0.793 | 4.057 | 1.921 | 0.850 | 126.100 | 130.157 |
| Electropolished vertical surface | 4.829 | 2.069 | 0.599 | 4.582 | 3.080 | 0.896 | 99.590 | 104.172 |
3.4 Discussion
The different electropolished surfaces in Fig. 5 show that the surface finish is influenced by the L-PBF process significantly. More defects are generated on the vertical surface in L-PBF; thus, the finish of the electropolished vertical surface has higher surface roughness Sa than the horizontal surface, as shown in Fig. 7. Therefore, the distinction in electropolishing characteristics on different surfaces of 316L SS fabricated by L-PBF should be considered when electropolishing is selected as the post surface treatment. The XPS analysis shows that the Cr/Fe ratio, which has critical importance for the corrosion resistance of electropolished 316L SS [49], is higher on the electropolished horizontal surface than the vertical surface. The compositions of the passive oxide film on different electropolished surfaces do not have significant difference according to the high-resolution spectra of chromium, iron, and oxygen element, as shown in Figs. 9 and 11. The electrochemical analysis in the NaCl solution investigated the corrosion resistance of different electropolished surfaces through measuring the OCPs, anodic polarization, and EIS plots. According to the measured OCPs and corrosion potentials and the fitted electrical equivalent circuit for the experimental EIS, the electropolished horizontal surface has higher corrosion resistance than the vertical surface. The defects on the electropolished vertical surface, as shown in Fig. 5, may decrease the corrosion resistance in the NaCl. The defects have shown a faster anodic dissolution rate on the defect edges by comparing the electropolished and mechanical polished surfaces in Figs. 5 and 6. Moreover, the higher Cr/Fe ratio on the electropolished vertical surface, which has been verified by the XPS spectra in Section 3.2, also contributes to the higher corrosion resistance of the electropolished horizontal surface.
4 Conclusions
The distinction in electropolishing characteristics on different surfaces of the 316L SS fabricated by selective laser melting is studied by focusing on the polarization curve measurement during the electropolishing process and electrochemical analysis of the electropolished surfaces. The following conclusions can be drawn.
The electropolishing of different surfaces is affected by the electrolyte temperature significantly, especially for the vertical surface. A high electrolyte temperature is necessary for the optimized electropolishing effect to be obtained in the limiting current density plateau region.
The surface finish of different electropolished surfaces is affected by the defects generated in the L-PBF process, and the electropolished vertical surface has higher surface roughness Sa than the horizontal surface. This finding is caused by a greater number of processed-related defects generated on the vertical surface during L-PBF process.
The electropolished horizontal surface has a higher percentage of oxygen element and Cr/Fe element ratio, indicating that the electropolished horizontal surface has higher corrosion resistance than the vertical surface.
The anodic polarization curves of the electropolished horizontal and vertical surfaces show that the corrosion potential of the horizontal surface is higher than the vertical surface. Therefore, higher corrosion resistance is expected on the electropolished horizontal surface.
The EIS analysis verifies that the electropolished horizontal surface has higher corrosion resistance than the vertical surface by fitting the electrical equivalent circuit diagram of the experimental EIS.
The higher corrosion resistance of electropolished horizontal surface could be determined by a smaller number of defects and higher Cr/Fe ratio than the electropolished vertical surface.