Effect of Negative Bias Voltage on Tribological Properties under High Relative Humidity Environment and Corrosion Resistance of Boron Carbide Coatings

: Humid air is a very important service environment, in which metal friction parts should be enhanced to offer excellent corrosion resistance and wear resistance. The B 4 C coating is an excellent candidate material to enhance the corrosion resistance and tribological behaviors. The purpose is to investigate the effect of negative bias voltages on the tribological properties of B 4 C coatings under a high relative humidity environment. Amorphous B 4 C coatings were successfully prepared by closed ﬁeld unbalanced magnetron sputtering technology and its microstructure, hardness, elastic modulus, adhesive force and tribological properties were systematically studied. Results demonstrate that the B 4 C coatings deposited at each negative bias voltage have a columnar structure and the surface roughness remained unchanged (about 1.0 nm), while the thickness, hardness, elastic modulus and adhesion force increase ﬁrst and then decrease with the negative bias voltage increasing. Among them, the B 4 C ( − 50 V) coating showed the best mechanical properties. It should be noted that the B 4 C ( − 50 V) coating with an excellent corrosion resistance also exhibits the lowest friction coefﬁcient (~0.15) and wear resistance (7.2 × 10 − 7 mm 3 · N − 1 · m − 1 ) under humid air (85% RH). This is mainly due to the tribochemical reaction of B 4 C during a sliding process to produce boric acid at the sliding interface. B 4 C coatings can provide an excellent corrosion resistance and high wear resistance due to their high chemical stability and high hardness.


Introduction
Metal friction pairs face various atmosphere environments during service, such as high temperature, methane, dry nitrogen, dry air and humid air [1][2][3][4]. In particular, humid air is a very important service environment, and the surface of metal friction parts should be modified to have a high hardness and high chemical inertness in order to offer an excellent corrosion resistance and wear resistance. The ultra-high hardness of boron carbide (B 4 C) ceramics is second only to the hardness of diamond and cubic boron nitride in nature [5][6][7]. At the same time, it also possesses excellent chemical stability [8,9]. Therefore, the B 4 C coating is an excellent candidate material under high humidity conditions to enhance the corrosion resistance and tribological performances [10].
The development of magnetron sputtering sources over recent years has attracted extensive attention to the B 4 C coating deposited by closed field unbalanced magnetron sputtering technology [11][12][13][14]. The magnetron sputtering technology can produce high kinetic energy and density plasma, which has the advantages of a faster deposition rate, larger deposition area, lower deposition voltage and lower deposition temperature and easy industrial production. In addition, the prepared B 4 C coatings by closed field unbalanced magnetron sputtering technology have excellent physical and chemical properties, such as excellent mechanical properties, a high adhesion, uniform and compact surface and small roughness [7]. If a suitable negative bias is applied during the deposition process, the sample can be cleaned and activated in the deposition chamber, which is conducive to improving the coating bonding strength, increasing the coating nucleation density in the nucleation stage and the coating density in the growth process, increasing the surface heat energy and introducing lattice defects in the surface area of the interlayer, so as to promote diffusion and reaction and improve the bonding force [15]. Based on the above advantages, closed field unbalanced magnetron sputtering deposition technology has been widely concerned and applied.
The appropriate negative bias voltage can effectively increase the energy and flow of sputtered ions, and then improve the mechanical properties such as hardness and adhesive force, as well as the tribological properties. Therefore, B 4 C coatings were prepared by unbalanced closed field magnetron sputtering equipment, and the effects of negative bias voltage on the cross-section and surface morphology, thickness, microstructure and bonding strength of B 4 C coatings were systematically investigated. At the same time, the tribological properties of B 4 C coatings in humid air were investigated. The results of this paper have an important guiding significance for the deposition of B 4 C coatings with excellent mechanical properties, low friction and high wear resistance by closed field unbalanced magnetron sputtering technology.

Materials and Methods
An unbalanced closed field magnetron sputtering device-UPD 650 (Teer, Droitwich, UK) was used to sputter one B 4 C target and two Cr targets in argon (Ar) atmosphere and polish (Ra ≤ 0.03 µm). Amorphous B 4 C coatings were successfully fabricated on 304 L stainless steel. Before deposition, the samples were ultrasonically cleaned with acetone and ethanol for 30 min to remove pollutants, and then dried with dry nitrogen. After being introduced into the deposition chamber, the samples were firstly etched by Ar + under a bias voltage of −500 V for 30 min to further remove the residual organic matter and other impurities on the surface. Subsequently, a chromium (Cr) intermediate layer of 200 nm was deposited by sputtering a high-purity Cr target in Ar atmosphere for 10 min to improve the bonding force. Finally, B 4 C coatings with different properties were successfully deposited on the substrate by adjusting the negative bias voltage (0 V, −50 V, −100 V, −150 V). The specific deposition conditions were reported in our previous publications [16].
The cross-section and surface morphology of B 4 C coatings were observed by SEM-JSM-6701F (JEOL, Tokyo, Japan). The surface morphology of the coatings was observed by atomic force microscopy-AFM (CSPM4000, Ben Yuan Nanometer Instrument Co., Ltd., Beijing, China), with a scanning area of 10 µm × 10 µm.The crystal structures of B 4 C coatings and B 4 C target were studied by the X-ray diffractometer-XRD (D/Max-2400X, Rigaku, Tokyo, Japan) with Cu Kα X-ray of monochromatic source. The Raman spectra of the coating in the range of 100-1800 cm −1 were studied by the Lab-RAM HR Evolution Raman spectrometer. A nano indentation device (TTX-NHT2, Anton Paar, Graz, Austria), equipped with a diamond indenter tip, was used to measure hardness and Young's modulus of the deposited coatings, and the indentation depth did not exceed 10% of the coating thickness to minimize the effect of substrate. The adhesions of B 4 C coatings were measured with a CSM scratch instrument equipped with a diamond tip.
The tribological properties of deposited B 4 C coatings in humid air (85% RH) were evaluated by CSM tester in pin-on-disk reciprocating mode. The friction and wear experiments were carried out at room temperature. The GCr15 ball with a radius of 3 mm was used as mating ball, normal load was 2 N, amplitude was 5 mm, sliding frequency was 5 Hz, and each sliding revolution was set to 10,000 cycles. In order to reduce the experimental error and obtain reliable experimental results, the friction test under each test condition was repeated at least three times. After the friction test, 3~5 positions were randomly selected on the wear tracks by two-dimensional optical profiler to measure wear loss; then, wear rates were obtained according to the formula: Wear rate = Wear loss/(Applied load × rubbing distance). Moreover, the sliding interfaces after friction tests were analyzed by Optical microscope and Scanning electron microscope. An electrochemical workstation (PGSTAT302, Metrohm Autolab, Utrecht, The Netherlands) was used to perform the potentiodynamic polarization tests to measure the corrosion resistance of 304 L steel sheet and B 4 C coating. A standard three electrode system was used and immersed in 3.5 wt.% NaCl solution for 30 min to obtain a stable open circuit potential (OCP). The action potential polarization experiments were carried out at a scanning rate of 2 mV/s at room temperature, and the applied potential was increased from −0.5 V below the stable OCP. Figure 1 shows the SEM section morphology and AFM surface morphology of B 4 C coatings. It was observed that the coating was composed of a Cr bonding layer and B 4 C layer, in which the thickness of the Cr bonding layer was about 0.22 µm. The thickness of the B 4 C layer was 1.40 µm, 1.46 µm, 1.59 µm and 1.52 µm, respectively, when the negative bias voltage was 0 V, −50 V, −100 V and −150 V. The reason why the coating thickness decreased slightly when the negative bias voltage was −150 V may be that the energy of the deposited atomic clusters was too large due to the high bias voltage. As shown in the illustration in Figure 1, the surface of the B 4 C coating under different negative bias voltages was smooth, flat and dense, and the surface roughness was 1.2 nm (0 V), 0.9 nm (−50 V), 1.0 nm (−100 V) and 1.10 nm (−150 V), respectively, showing a trend of first decreasing and then increasing. In addition, it was observed that, except for depositing the B 4 C coating with a bias voltage of 0 V, B 4 C under other bias voltages showed an obvious columnar structure, and the higher the negative bias voltage, the more obvious the columnar structure was. Combined with the analysis of the surface roughness, the application of an appropriate negative bias voltage (−50 V) could make the microstructure of the film more compact and the surface roughness decrease. However, with the further increase in the bias to −150 V, the columnar structure became coarser and the roughness increased slightly, indicating that the high bombardment energy of Ar + ions would increase the surface roughness of the film. dition was repeated at least three times. After the friction test, 3~5 positions were randomly selected on the wear tracks by two-dimensional optical profiler to measure wear loss; then, wear rates were obtained according to the formula: Wear rate = Wear loss/(Applied load × rubbing distance). Moreover, the sliding interfaces after friction tests were analyzed by Optical microscope and Scanning electron microscope. An electrochemical workstation (PGSTAT302, Metrohm Autolab, Utrecht, Netherlands) was used to perform the potentiodynamic polarization tests to measure the corrosion resistance of 304 L steel sheet and B4C coating. A standard three electrode system was used and immersed in 3.5 wt.% NaCl solution for 30 min to obtain a stable open circuit potential (OCP). The action potential polarization experiments were carried out at a scanning rate of 2 mV/s at room temperature, and the applied potential was increased from −0.5 V below the stable OCP. Figure 1 shows the SEM section morphology and AFM surface morphology of B4C coatings. It was observed that the coating was composed of a Cr bonding layer and B4C layer, in which the thickness of the Cr bonding layer was about 0.22 μm. The thickness of the B4C layer was 1.40 μm, 1.46 μm, 1.59 μm and 1.52 μm, respectively, when the negative bias voltage was 0 V, −50 V, −100 V and −150 V. The reason why the coating thickness decreased slightly when the negative bias voltage was −150 V may be that the energy of the deposited atomic clusters was too large due to the high bias voltage. As shown in the illustration in Figure 1, the surface of the B4C coating under different negative bias voltages was smooth, flat and dense, and the surface roughness was 1.2 nm (0 V), 0.9 nm (−50 V), 1.0 nm (−100 V) and 1.10 nm (−150 V), respectively, showing a trend of first decreasing and then increasing. In addition, it was observed that, except for depositing the B4C coating with a bias voltage of 0 V, B4C under other bias voltages showed an obvious columnar structure, and the higher the negative bias voltage, the more obvious the columnar structure was. Combined with the analysis of the surface roughness, the application of an appropriate negative bias voltage (−50 V) could make the microstructure of the film more compact and the surface roughness decrease. However, with the further increase in the bias to −150 V, the columnar structure became coarser and the roughness increased slightly, indicating that the high bombardment energy of Ar + ions would increase the surface roughness of the film.  The Raman spectrum of the B 4 C coating is shown in Figure 2a. Obvious characteristic peaks of amorphous carbon were not observed, namely the D peak and G peak, which indicated that the B 4 C coating did not contain free carbon. Therefore, according to the boron carbide phase diagram [17], we suggest that the deposited coating was mainly composed of B 4 C. By comparing the Raman spectrum and XRD spectrum of the B 4 C coating and B 4 C target (Figure 2b), it was concluded that the deposited B 4 C coating was amorphous. The Raman spectrum of the B4C coating is shown in Figure 2a. Obvious characteristic peaks of amorphous carbon were not observed, namely the D peak and G peak, which indicated that the B4C coating did not contain free carbon. Therefore, according to the boron carbide phase diagram [17], we suggest that the deposited coating was mainly composed of B4C. By comparing the Raman spectrum and XRD spectrum of the B4C coating and B4C target (Figure 2b), it was concluded that the deposited B4C coating was amorphous.

Mechanical Properties of B4C Coatings
As shown in Figure 3a, the microhardness and elastic modulus of the B4C coating increased first and then decreased with the increase in a negative bias voltage. In particular, when the negative bias voltage was −50 V, the microhardness and elastic modulus of the B4C coating were the largest, about 32.4 GPa and 280 GPa, respectively. Figure 3b shows the bonding strength of B4C coatings under different negative bias voltages, measured by a CSM scratch tester and showing the results. With the increase in a negative bias voltage, the bonding strength of the B4C coatings first increased and then decreased, and reached the maximum at −50 V, which was 15.5 N (0 V), 20.5 N (−50 V), 20.2 N (−100 V) and 17.2 N (−150 V), respectively. Applying an appropriate negative bias voltage can effectively increase the energy and density of deposited clusters, which would lead to a strong bombardment, resulting in a more dense structure, higher microhardness and bonding force. However, if the negative bias voltage were to rise to −150 V, the energy and density of the deposited clusters could be too large. On the one hand, too large, deposited clusters would destroy the dense structure of the coating; on the other hand, too energetically deposited clusters would sputter out the atoms in the coating and cause back splashing, which would also destroy the dense structure of the coating; thus, weakening the mechanical properties of the B4C coating.

Mechanical Properties of B 4 C Coatings
As shown in Figure 3a, the microhardness and elastic modulus of the B 4 C coating increased first and then decreased with the increase in a negative bias voltage. In particular, when the negative bias voltage was −50 V, the microhardness and elastic modulus of the B 4 C coating were the largest, about 32.4 GPa and 280 GPa, respectively. Figure  Applying an appropriate negative bias voltage can effectively increase the energy and density of deposited clusters, which would lead to a strong bombardment, resulting in a more dense structure, higher microhardness and bonding force. However, if the negative bias voltage were to rise to −150 V, the energy and density of the deposited clusters could be too large. On the one hand, too large, deposited clusters would destroy the dense structure of the coating; on the other hand, too energetically deposited clusters would sputter out the atoms in the coating and cause back splashing, which would also destroy the dense structure of the coating; thus, weakening the mechanical properties of the B 4 C coating.
The Raman spectrum of the B4C coating is shown in Figure 2a. Obvious characteristic peaks of amorphous carbon were not observed, namely the D peak and G peak, which indicated that the B4C coating did not contain free carbon. Therefore, according to the boron carbide phase diagram [17], we suggest that the deposited coating was mainly composed of B4C. By comparing the Raman spectrum and XRD spectrum of the B4C coating and B4C target (Figure 2b), it was concluded that the deposited B4C coating was amorphous.

Mechanical Properties of B4C Coatings
As shown in Figure 3a, the microhardness and elastic modulus of the B4C coating increased first and then decreased with the increase in a negative bias voltage. In particular, when the negative bias voltage was −50 V, the microhardness and elastic modulus of the B4C coating were the largest, about 32.4 GPa and 280 GPa, respectively. Figure 3b shows the bonding strength of B4C coatings under different negative bias voltages, measured by a CSM scratch tester and showing the results. With the increase in a negative bias voltage, the bonding strength of the B4C coatings first increased and then decreased, and reached the maximum at −50 V, which was 15.5 N (0 V), 20.5 N (−50 V), 20.2 N (−100 V) and 17.2 N (−150 V), respectively. Applying an appropriate negative bias voltage can effectively increase the energy and density of deposited clusters, which would lead to a strong bombardment, resulting in a more dense structure, higher microhardness and bonding force. However, if the negative bias voltage were to rise to −150 V, the energy and density of the deposited clusters could be too large. On the one hand, too large, deposited clusters would destroy the dense structure of the coating; on the other hand, too energetically deposited clusters would sputter out the atoms in the coating and cause back splashing, which would also destroy the dense structure of the coating; thus, weakening the mechanical properties of the B4C coating.   Figure 4a shows the friction curves of B 4 C coatings prepared by different negative bias voltages under a high relative humidity (85% RH). It was observed from Figure 4a that each B 4 C coating had a low friction coefficient and a common feature: these friction curves started from a high value, then, gradually, decreased to a steady-state value accompanied by large fluctuations. It was found from Figure 4b that both the friction coefficient and wear rate first decreased and then increased with the increase in a negative bias voltage. When the negative bias voltage was 0 V, −50 V, −100 V and −150 V, the friction coefficient of the B 4 C layer was 0.21, 0.15, 0.28 and 0.28, respectively; the specific wear rates were 9.65, 7.24, 7.57 and 10.49 × 10 −7 mm 3 ·N −1 ·m −1 , respectively. Figure 4a shows the friction curves of B4C coatings prepared by different negative bias voltages under a high relative humidity (85% RH). It was observed from Figure 4a that each B4C coating had a low friction coefficient and a common feature: these friction curves started from a high value, then, gradually, decreased to a steady-state value accompanied by large fluctuations. It was found from Figure 4b that both the friction coefficient and wear rate first decreased and then increased with the increase in a negative bias voltage. When the negative bias voltage was 0 V, −50 V, −100 V and −150 V, the friction coefficient of the B4C layer was 0.21, 0.15, 0.28 and 0.28, respectively; the specific wear rates were 9.65, 7.24, 7.57 and 10.49 × 10 −7 mm 3 ·N −1 ·m −1 , respectively.  Figure 5 shows the optical morphology of disc wear tracks of the B4C coating under different negative bias voltages under humid air. It was observed that the wear tracks of the B4C coating were relatively similar-there were many wear particles around the wear tracks, the interior of the wear tracks was very smooth with small cracks and obvious furrows were also observed. This indicated that fatigue wear and abrasive wear occurred in the friction process. Figure 6 shows the wear scar morphology of the GCr15 steel balls under different negative bias voltages. It was seen that the morphology of each wear scar was also relatively similar-the wear scars were a regular circular, many wear particles were scattered around and there were deep furrows inside.

Tribological Performances and Corrosion Resistance of B4C Coatings
In order to further analyze the reasons for the best tribological properties of the B4C (−50 V) coating, the wear track surface of the B4C (−50 V) coating was investigated by SEM and EDS. As shown in Figure 7, there were some abrasive particles at the edge of the wear track of the B4C (−50 V) coating and small furrows inside the wear track, which indicated that abrasive wear occurred during the friction process. In the corresponding EDS diagram, it was observed that the O element obviously accumulated on the wear debris at the edge of the wear track, which indicated that the B4C coating was oxidized during friction and then reacted with water vapor to generate boron oxide (B2O3) or boric acid (H3BO3) [16]. This was why the B4C coating obtained low friction in a high humidity atmosphere.
In conclusion, the B4C (−50 V) coating showed the best tribological properties at a high relative humidity (85% RH), and its friction coefficient was about 0.15 and the wear rate was about 7.24 × 10 −7 mm 3 ·N −1 ·m −1 . Hardness was the main factor to evaluate wear resistance by the classical wear theory [18]: the harder the material, the more wear-resistant it is. In addition, the high elastic modulus, adhesion and denser microstructure can play a better bearing role. Therefore, the B4C (−50 V) coating with the highest hardness, elastic modulus, adhesion and a denser columnar structure, had excellent friction and wear performances.  Figure 5 shows the optical morphology of disc wear tracks of the B 4 C coating under different negative bias voltages under humid air. It was observed that the wear tracks of the B 4 C coating were relatively similar-there were many wear particles around the wear tracks, the interior of the wear tracks was very smooth with small cracks and obvious furrows were also observed. This indicated that fatigue wear and abrasive wear occurred in the friction process. Figure 6 shows the wear scar morphology of the GCr15 steel balls under different negative bias voltages. It was seen that the morphology of each wear scar was also relatively similar-the wear scars were a regular circular, many wear particles were scattered around and there were deep furrows inside.   In order to further analyze the reasons for the best tribological properties of the B 4 C (−50 V) coating, the wear track surface of the B 4 C (−50 V) coating was investigated by SEM and EDS. As shown in Figure 7, there were some abrasive particles at the edge of the wear track of the B 4 C (−50 V) coating and small furrows inside the wear track, which indicated that abrasive wear occurred during the friction process. In the corresponding EDS diagram, it was observed that the O element obviously accumulated on the wear debris at the edge of the wear track, which indicated that the B 4 C coating was oxidized during friction and then reacted with water vapor to generate boron oxide (B 2 O 3 ) or boric acid (H 3 BO 3 ) [16]. This was why the B 4 C coating obtained low friction in a high humidity atmosphere. Considering that metal friction parts were prone to serious corrosion in a high humidity environment, we further compared and evaluated the corrosion resistance of a 304 L steel sheet and B4C (−50 V) coating with an electrochemical workstation (PGSTAT302, AutoLab). It is well known that the resistance of corrosion can be estimated according to the corrosion current density (Icorr) and corrosion potential (Ecorr) [19][20][21]. It was observed In conclusion, the B 4 C (−50 V) coating showed the best tribological properties at a high relative humidity (85% RH), and its friction coefficient was about 0.15 and the wear rate was about 7.24 × 10 −7 mm 3 ·N −1 ·m −1 . Hardness was the main factor to evaluate wear resistance by the classical wear theory [18]: the harder the material, the more wearresistant it is. In addition, the high elastic modulus, adhesion and denser microstructure can play a better bearing role. Therefore, the B 4 C (−50 V) coating with the highest hardness, elastic modulus, adhesion and a denser columnar structure, had excellent friction and wear performances.
Considering that metal friction parts were prone to serious corrosion in a high humidity environment, we further compared and evaluated the corrosion resistance of a 304 L steel sheet and B 4 C (−50 V) coating with an electrochemical workstation (PGSTAT302, AutoLab). It is well known that the resistance of corrosion can be estimated according to the corrosion current density (I corr ) and corrosion potential (E corr ) [19][20][21]. It was observed from Figure 8 that the I corr value of the B 4 C coating was about 7.0 × 10 −8 A·cm −2 , and the I corr value of the 304 L steel sheet was about 3.0 × 10 −6 A·cm −2 . Moreover, the E corr value of the B 4 C (−50 V) coating positively increased from −0.51 V of the 304 L sheet to −0.31 V of the B 4 C (−50 V) coating. In short, the B 4 C (−50 V) coating showed a lower corrosion current and higher corrosion potential than the 304 L steel substrate; that is, the B 4 C coating significantly improved the corrosion resistance of the 304 L steel substrate. In addition, as shown in Figure 8b,c, the surface of the B 4 C (−50 V) coating after the corrosion attack before the test had no obvious change compared with that before the corrosion attack. It was seen that the B 4 C (−50 V) coating on the inner wall of the 6063 Al pipe could maintain stability in the corrosive medium, effectively prevent the penetration of corrosive medium and play a good protective role for the 6063 Al pipe. Considering that metal friction parts were prone to serious corrosion in a high humidity environment, we further compared and evaluated the corrosion resistance of a 304 L steel sheet and B4C (−50 V) coating with an electrochemical workstation (PGSTAT302, AutoLab). It is well known that the resistance of corrosion can be estimated according to the corrosion current density (Icorr) and corrosion potential (Ecorr) [19][20][21]. It was observed from Figure 8 that the Icorr value of the B4C coating was about 7.0 × 10 −8 A·cm −2 , and the Icorr value of the 304 L steel sheet was about 3.0 × 10 −6 A·cm −2 . Moreover, the Ecorr value of the B4C (−50 V) coating positively increased from −0.51 V of the 304 L sheet to −0.31 V of the B4C (−50 V) coating. In short, the B4C (−50 V) coating showed a lower corrosion current and higher corrosion potential than the 304 L steel substrate; that is, the B4C coating significantly improved the corrosion resistance of the 304 L steel substrate. In addition, as shown in Figure 8b,c, the surface of the B4C (−50 V) coating after the corrosion attack before the test had no obvious change compared with that before the corrosion attack. It was seen that the B4C (−50 V) coating on the inner wall of the 6063 Al pipe could maintain stability in the corrosive medium, effectively prevent the penetration of corrosive medium and play a good protective role for the 6063 Al pipe.

Conclusions
In view of the serious corrosion and wear of metal friction parts under high relative humidity conditions, B4C coatings with excellent friction and wear properties were suc-

Conclusions
In view of the serious corrosion and wear of metal friction parts under high relative humidity conditions, B 4 C coatings with excellent friction and wear properties were successfully prepared on 304 L steel sheets by closed field unbalanced magnetron sputtering equipment, and the effect of a negative bias voltage on mechanical properties and tribological properties under a high relative humidity environment were investigated. The main conclusions were as follows: • The surface of the amorphous B 4 C coatings under different negative bias voltages was smooth, dense and columnar. With the increase in a negative bias voltage, the thickness, microhardness, elastic modulus and bonding force of the coatings first increased and then decreased. Overall, the mechanical properties of the B 4 C coating were the best when the negative bias voltage was −50 V. • B 4 C coatings showed excellent tribological properties in humid air with 85% RH, and the tribological performances increased first and then decreased with the increase in a negative bias voltage. When the negative bias voltage was −50 V, the B 4 C coating showed the best friction reduction and wear resistance in humid air with 85% RH; the friction coefficient of the B 4 C coating was as low as 0.15 and the wear rate was 7.2 × 10 −7 mm 3 ·N −1 ·m −1 .

•
The corrosion current density (I corr ) of 304 L steel substrate was about three orders of magnitude higher than the B 4 C (−50 V) coating. The corrosion potential (E corr ) value positively increased compared with that of the 304 L steel substrate. Therefore, the B 4 C coating remarkably enhanced the resistance to corrosion of the 304 L steel substrate.
Funding: This research received no external funding.
Data Availability Statement: Data presented in this article are available at request from the corresponding author.

Conflicts of Interest:
The authors declare no conflict of interest.