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Article

Yttria-Stabilized Zirconia Composite Coating as Barrier to Reduce Hydrogen Permeation into Steel

by
Jianmeng Wu
,
Jiaqi **e
,
Mengyuan He
,
**gyi Zhang
and
Songjie Li
*
School of Chemical Engineering, Zhengzhou University, Zhengzhou 450001, China
*
Author to whom correspondence should be addressed.
Materials 2024, 17(12), 3017; https://doi.org/10.3390/ma17123017
Submission received: 14 April 2024 / Revised: 31 May 2024 / Accepted: 15 June 2024 / Published: 20 June 2024
(This article belongs to the Special Issue Corrosion and Crack Behavior of Metallic Materials in High-Temperature Environment)
Browse Figures
Versions Notes

Abstract

:
Hydrogen atoms can enter into metallic materials through penetration and diffusion, leading to the degradation of the mechanical properties of the materials, and the application of hydrogen barrier coatings is an effective means to alleviate this problem. Zirconia coatings (ZrO2) have been widely studied as a common hydrogen barrier coating, but zirconia undergoes a crystalline transition with temperature change, which can lead to volumetric changes in the coating and thus cause problems such as cracking and peeling of the coating. In this work, ZrO2 coating was prepared on a Q235 matrix using a sol-gel method, while yttria-stabilized zirconia (YSZ) coatings with different contents of rare earth elements were prepared in order to alleviate a series of problems caused by the crystal form transformation of ZrO2. The coating performances were evaluated by the electrochemical hydrogen penetration test, pencil hardness test, scratch test, and high-temperature oxidation test. The results show that yttrium can improve the stability of the high-temperature phase of ZrO2, alleviating the cracking problem of the coating due to the volume change triggered by the crystalline transition; improve the consistency of the coating; and refine the grain size of the oxide. The performance of YSZ coating was strongly influenced by the yttria do** mass, and the coating with 10 wt% yttria do** had the best hydrogen barrier performance, the best antioxidant performance, and the largest adhesion. Compared with the matrix, the steady-state hydrogen current density of the YSZ coating decreased by 72.3%, the antioxidant performance was improved by 65.8%, and the ZrO2 coating hardness and adhesion levels were B and 4B, respectively, while YSZ coating hardness and adhesion were upgraded to 2H and 5B. With the further increase in yttrium do** mass, the hardness of the coating continued to improve, but the defects of the coating increased, resulting in a decrease in the hydrogen barrier performance, antioxidant performance, and adhesion. In this work, the various performances of ZrO2 coating were significantly improved by do** with the rare earth element, which provides a reference for further development and application of oxide coatings.

1. Introduction

As the most widely distributed substance in nature, hydrogen energy is regarded as the clean energy with the most development potential in the 21st century for its high calorific value, lack of pollution, and abundant sources [1,2,3]. Hydrogen energy is conducive to promoting the clean and efficient use of traditional fossil energy and supporting the large-scale development of renewable energy [4,5]. However, for metal materials in a hydrogen environment, due to the small radius and high permeability of hydrogen atoms, their entry into the metal material leads to a decline in the mechanical properties of the material. The plasticity of the material especially is reduced, triggering the occurrence of hydrogen damage or even fracture phenomena, resulting in huge economic losses or even a disaster [6,7,8].
American scholar Flowler first proposed the concept of hydrogen permeation barrier coatings at the end of the 1970s [9]. Many studies have shown that hydrogen barrier coatings on the surface of metal materials can effectively slow down the diffusion of hydrogen into the metal materials, which can reduce the occurrence of hydrogen damage phenomena and improve the safety of the whole process of hydrogen energy utilization [10,11,12]. According to the type, the hydrogen barrier coating can be divided into oxide coatings [13,14], carbide coatings [15,16], and metal alloy coatings [17]. Among them, the oxide coating has the advantages of stable chemical properties, good wear resistance, low solubility and permeability of hydrogen, low cost, etc.; oxide coatings are the most widely studied type of coating, including chromium oxide coating [18,19], alumina coating [20], and so on. For example, He et al. [21] prepared a Cr2O3 coating on 316L stainless steel by the metal–organic decomposition (MOD) method, using chromium acetylacetonate as the precursor. The hydrogen permeation results show that the hydrogen permeability of Cr2O3 coating can be reduced by 24–117 times at 823–973 K. Feng et al. [22] deposited Al2O3 as a hydrogen barrier coating on a 316L matrix by plasma electrolytic oxidation, and the results of gas-phase hydrogen permeation tests showed that the alumina coating was able to reduce the rate of hydrogen permeation by three orders of magnitude concerning the pure matrix. However, the thermal expansion coefficient between the metal matrix and the oxide coating differs greatly, and there is an obvious thermal mismatch problem, which is highly likely to lead to problems such as cracks and coating peeling. Zhang et al. [23] prepared an Al2O3 coating on a 316L matrix by the MOD method, but due to the difference in thermal expansion coefficients, cracks and defects appeared in the Al2O3 coating during the drying and annealing process, and the protective effect of the coating on the matrix was improved by sealing and densifying the coating with aluminum phosphate.
Certainly, the selection of an oxide material with a coefficient of thermal expansion similar to that of the matrix is an important means of improving the hydrogen barrier properties of the coating. In recent years, zirconia (ZrO2) has been widely studied as a new type of hydrogen permeation barrier coating material with a coefficient of thermal expansion much closer to those of various types of steel materials [24,25], and the diffusion coefficient of hydrogen in zirconia is low [26,27,28]. Hatano et al. [29] prepared ZrO2 coatings on ferrite steel by the sol-gel method and electrolytic deposition technique, and the coatings showed a good hydrogen barrier effect at 300–550 °C according to the gas phase hydrogen permeation test. However, ZrO2 is a polycrystalline oxide, and as the temperature changes, the crystalline form will shift, which will lead to changes in the volume of ZrO2 and thus cause cracking and peeling of the ZrO2 coating [30]. Therefore, adopting reasonable preparation methods and processes to inhibit the transformation of the ZrO2 crystal type and reduce the cracking phenomenon of the coating is an important means to promote the wide application of ZrO2 in the field of hydrogen permeation barrier coating [31,32]. The radius difference between yttrium (Y) ions and zirconium ions is smaller than that of other metals, so yttrium has been used to stabilize zirconium oxide crystals in many studies, and excellent results have been achieved [33].
Based on the above viewpoints, in this work, ZrO2 coatings were prepared on a Q235 mild steel matrix by the sol-gel method. Meanwhile, in order to alleviate the problems of coating cracking and peeling caused by the crystalline transformation of ZrO2, as well as to improve the hydrogen barrier performance and other comprehensive properties of the coatings, yttrium nitrate with different contents was introduced into the coating preparation process. The effects of the addition of the Y element on the surface morphology, hardness, bonding force, antioxidant performance, and hydrogen barrier performance of the coatings were investigated.

2. Experimental Procedures

2.1. Materials

n-propanol (>99.5 wt%), n-propanol zirconium (70 wt% in n-propanol), acetylacetone (>99.0 wt%), and yttrium nitrate (>99.5 wt%) were supplied by Shanghai Macklin Biochemical Technology Co., Ltd. (Shanghai, China). Sodium sulfide (>99.0 wt%) and sodium hydroxide (>95.0 wt%) were purchased from Shanghai Aladdin Reagent Co., Ltd. Acetone (>99.0 wt%) and anhydrous ethanol (>99.5 wt%) were obtained from Sinopharm Chemical Reagent Co., Ltd. (Shanghai, China). The dimension of Q235 steel used in this work was 35 mm × 45 mm × 0.3 mm, and its specific composition is shown in Table 1.

2.2. Pretreatment of Matrix Q235 Mild Steel

The Q235 matrix was sequentially polished using 1200, 2400, and 4000 mesh sandpaper, followed by polishing of the matrix using a 5 μm diamond polish. Prior to the preparation of the coating, the matrix needed to be ultrasonically cleaned in anhydrous ethanol and acetone sequentially for 20 min and dried to remove oils and impurities from the matrix surface [34,35].

2.3. Preparation of ZrO2 Coating and Yttria-Stabilized Zirconia Coating

Precursor sols of ZrO2 were prepared using n-propanol zirconium as the zirconium source, n-propanol as the solvent, acetylacetone as the complexing agent, and yttrium nitrate as the stabilizer, with a molar ratio of n-propanol zirconium, n-propanol, acetylacetone, and deionized water of 1:10:2:2.5. The contents of yttrium nitrate added (calculated as the mass ratio of Y2O3 relative to ZrO2) were 5 wt%, 10 wt%, and 15 wt%. Firstly, n-propanol zirconium was dissolved in the n-propanol solvent and stirred well. After that, acetylacetone and deionized water were added sequentially and mixed well. After stirring and reacting for 24 h, the resulting sol was placed in a beaker, and the precursor sol of yttria-stabilized zirconia (YSZ) was obtained by sealing and static aging for 48 h at room temperature.
The prepared sol was uniformly coated onto the treated matrix, which was subsequently placed in a drying oven at 85 °C for 20 min to evaporate excess water and solvent in the wet gel. At the end of drying, the specimen was taken out to be coated with the sol again, and the process was repeated three times. The dried specimen was placed in a muffle furnace and heated up to 300 °C at a heating rate of 1 °C/min, and it was taken out after pre-sintering for 35 min; then, the coating and drying process was carried out again, which was repeated three times. Finally, the specimen was placed in a muffle furnace and heated up to 550 °C for heat treatment; the specific process of heat treatment is shown in Table 2. The ZrO2 and YSZ coatings were obtained after heat treatment and natural cooling to room temperature in the furnace. The YSZ coatings were named 5YSZ, 10YSZ, and 15YSZ based on the order of Y do** mass from 5 wt% to 15 wt%.

2.4. Characterization of Materials

The TG-DTG-DSC curves of the gels were measured using a Differential Thermo-Thermogravimetric Simultaneous Analyzer (Netzsch STA449F5, Bavaria, Germany). With N2 as the protective gas, the test temperature range was from room temperature to 800 °C, and the heating rate was 10 °C/min. The physical phase composition of the coatings was analyzed using a X-ray diffractometer (PANalytical Empyrean, Almelo, the Netherlands), which uses a Cu target with a test angle range of 20–80° and a scanning speed of 1°/min. The scanning electron microscope (ZEISS sigma 500, Oberkochen, Germany) was used to observe the microscopic morphology and cross-sectional morphology of the coatings, and a energy dispersive spectrometer (BRUKER XFlash 6130, Billerica, MA, USA) was used to perform surface scanning of the coating surfaces to analyze the composition and ingredients of the film layers.

2.5. Hydrogen Barrier Performance Testing of Coatings

In this work, electrochemical hydrogen permeation was used to evaluate the hydrogen barrier performance of the coatings. The schematic diagram of the electrochemical hydrogen permeation test setup is shown in Figure 1. The main experimental setup consisted of a Devanathan–Stachurski double electrolytic cell, which contained a cathode chamber and an anode chamber, with the sample to be tested sandwiched between the two chambers. The electrolyte in the cathode chamber was a mixed solution of 0.2 mol/L NaOH and 1 g/L Na2S, and the electrolyte in the anode chamber was a 0.2 mol/L NaOH solution. The platinum sheet electrode acted as the auxiliary electrode in the cathode and anode chambers, the Hg/HgO electrode was used as the reference electrode in the anode chamber, and the specimen acted as a double working electrode, both as an anode and cathode. During the experiment, the side with the coating faced the cathode chamber, which was connected to the constant current apparatus, and the anode chamber was connected to the electrochemical workstation. Five parallel tests were performed for each type of coating, and coating specimens whose experimental results varied within 5% were selected as the raw data for electrochemical hydrogen permeation curve plotting.

2.6. Hardness and Adhesion Testing of Coatings

The hardness of a coating is one of the most important properties indicating the mechanical strength of the coating and is also an important indicator of the quality of the coating [36]. The coating hardness test was conducted with the Sichuan Strubic BK636 pencil hardness tester (Chengdu, China); the hardness level from low to high was divided into 6B-B, HB, and H-6H, for a total of 13 levels. A vertical pressure of 1 kg was applied to the surface of the coating at an oblique angle of 45° for a length of 3 cm and repeated 3 times. The hardness of the pencil corresponds to the hardness of the coating when the pencil fails to make a scratch.
The strength of the bond between the coating and the matrix largely determines the service life of the coating. The adhesion test was carried out by the Sichuan Strubic BK218 scribe(Chengdu, China), and the adhesion was categorized into six grades from 0B to 5B. The test was conducted with a 218/4 cutter head and a 10 × 10 mm grid of 100 squares. The results were observed using 3 M adhesive tape and a magnifying glass.

2.7. Antioxidant Performance Test of Coatings

In addition to the effects of hydrogen atoms on the material, the material is also susceptible to attack by ambient oxygen. In this study, the oxidation resistance of the coated specimens was evaluated by measuring the weight change in the samples before and after they were heated to 500 °C in air and held for different times.

3. Results and Discussion

3.1. Thermal Transition Temperature Analysis of Different Types of Gel

The results of the TG-DTG analysis of the dried ZrO2 gel powder and YSZ gel powder are shown in Figure 2. From the TG curves in Figure 2a, it can be found that the overall mass loss of the two gels was about 36%, and the mass loss process was divided into three stages. The ZrO2 gel lost weight slowly in the range from room temperature to 190 °C, with a mass loss of about 5.7%. In the range of 190–450 °C, the gel lost weight significantly, with a mass loss of 26.2%, and the rate of weight loss was fast. In the range of 450–800 °C, the change in gel mass was small, only 4.6%. YSZ sol had a faster rate of weight loss than ZrO2 sol between 190 °C and 450 °C, mainly due to the decomposition of yttrium nitrate.
Combined with the DTG curves in Figure 2b, it can be found that both gels showed obvious weight loss peaks near 90 °C, which were mainly attributed to the evaporation of the residual free water and solvent in the gels. Between 190 and −400 °C, the DTG curves showed multiple weight loss peaks. The weight loss peak near 220 °C was mainly attributed to the removal of bound water, and the weight loss peak appeared near 290 °C when the decomposition of organic matter mainly occurred. The weight loss peaks of the DTG curve of ZrO2 sol appeared at 400 °C and 511 °C, which was mainly due to the transformation of the ZrO2 gel, and the oxides were gradually formed at this stage [37,38]. From the DTG curve of YSZ sol, oxide was formed at a lower temperature and at an accelerated rate, and there was no obvious weight loss peak after 400 °C, which also indicates that Y do** has a positive effect on stabilizing the crystal form of oxides, and the crystalline form of oxides remains stable after formation. From the DSC curves in Figure 3c, it can be seen that the phase transition temperature from the amorphous to the crystalline state of ZrO2 gel decreased after the addition of Y element, which indicates that Y can promote the phase transition of ZrO2 and stabilize the crystalline form of the oxide to some extent.

3.2. Surface Morphology Analysis of Coatings

Figure 3 shows the SEM morphology of the ZrO2 coating and the YSZ coating, and Figure 4 shows the elemental distribution on the surface of the YSZ coating. From Figure 3a, it can be seen that there are more defects on the surface of the ZrO2 coating. The smooth lumpy ZrO2 ceramics are uniformly distributed on the surface of the matrix, and a small amount of needle-like iron oxide exists on the surface due to the partial oxidation of the coating during the preparation process [39]. With the do** of Y into the coating, the volume change effect due to the crystallographic transition is suppressed and the cracking of the coating is reduced, but when the do** mass of Y is further increased to 15 wt%, the stability of the crystallographic structure of the oxides deteriorates again. The 10YSZ coating has the densest surface condition with the least number of cracks and defects on the surface.
As can be seen in Figure 4, the YSZ coating is mainly composed of Zr, Y, and O elements; the elements are uniformly distributed in the coating. This indicates that the coating is mainly composed of oxides of Zr and Y, which further indicates the successful do** of element Y into the coating.

3.3. Phase Composition Analysis of Coatings

Figure 5 shows the XRD patterns of the ZrO2 coating and YSZ coatings. It can be seen that the ZrO2 coating is mainly composed of a large amount of monoclinic phase (m-ZrO2) and a small amount of tetragonal phase (t-ZrO2), along with the Y do**. The monoclinic phase in the ZrO2 coatings gradually disappeared, and the coatings mainly contained Y-doped t-ZrO2(t-Zr1−xYxO2−0.5x, 0 < x < 1) and a small amount of t-ZrO2 [40], which indirectly proves the successful do** of the Y element.
Meanwhile, at 2θ = 30°, 35°, and 50°, the diffraction peak patterns show a diffuse broadening phenomenon, and the peak intensity decreases, which implies that the YSZ material has a smaller grain size [41,42]. As a whole, the YSZ coating is mainly dominated by tetragonal phase oxides, and the Y do** amount does not have much effect on the physical phase type of the coating, but with the gradual increase in the Y do** content, more and more Y atoms form a composite oxide with Zr atoms, and the content of t-ZrO2 decreases gradually while the content of t-Zr1−xYxO2−0.5x rises gradually. Diffraction peaks of iron oxide appeared at Y do** levels of 5 wt% and 15 wt%, indicating that there were some defects in the coating during the preparation process under these two do** levels, resulting in oxidation of the matrix when exposed to air. The peak widths of the main diffraction peaks showed a significant reduction in the oxide grain size. It can be calculated from the Scherrer formula that as the Y do** increased from 5 wt% to 15 wt%, the average grain size of the oxides decreased by about 31%, 37%, and 60%, respectively.

3.4. Evaluation of Physical Properties of Coatings

Figure 6 shows the results of the pencil hardness tester for ZrO2, 5YSZ, 10YSZ, and 15YSZ coatings. The results show that the hardness level of the ZrO2 coatings is B. The hardness of the coatings gradually increases with the increase in Y do** mass, and the hardness level increases from B to 4H. The reason is that with the increase in Y do**, the increase in viscosity and density of the sol makes the thickness of the coating increase under the same coating process. On the one hand, the oxide particles are of high hardness, so the hardness of the coating is enhanced with the increase in the thickness [43]; on the other hand, due to the Y do** making the grain size of the oxide smaller, the effect of grain refinement can effectively improve the hardness and wear resistance of the coating, so the YSZ coating has a greater hardness and enhanced wear resistance compared with the ZrO2 coating.
The results of the adhesion test of the ZrO2 coating and the YSZ coating are shown in Figure 7, and the bonding strength of the coatings can be visualized by observing the shedding of the coatings in the scratch test. The scratches were carefully observed with an optical microscope, and it was found that the ZrO2 coating had a small amount of separation between the coating and the matrix at the intersection of the scratches and the peeling phenomenon. The overall affected area was less than 5%, and the adhesion test grade was 4B. The 5YSZ coating showed a small amount of the separation and peeling phenomenon between the coating and the matrix at the intersection of the scratches; the overall affected area was less than 5%, and the adhesion test grade was 4B. 10YSZ coating had almost no peeling phenomena at the edge of the scratch; the adhesion test grade was 5B. 15YSZ coating showed a partial peeling phenomenon at the edge of the scratch; the overall impact area was more than 5% but less than 15%, and the test grade was 3B.
The results of adhesion and hardness tests of the coatings show that the addition of Y at a low do** amount can inhibit the transformation of the ZrO2 crystal type and greatly alleviate the decrease in bonding force caused by the volume change in the coatings. The bonding force between the coatings and the matrix is gradually strengthened with the increase in the Y do** amount, and the adhesion gradually improves [44]. However, too-high Y do** will lead to the stabilization effect of the crystalline form being poor, while the increase in the thickness of the coating and the increase in the brittleness of the coating will also make the coating densification poor and decrease the bonding force with the matrix, resulting in cracking or even peeling phenomena. Therefore, when the Y do** amount is 10 wt%, the coating has the best comprehensive physical properties, and the 10YSZ coating has the strongest bonding force with the matrix and a high hardness level.

3.5. Antioxidant Behavior of Coatings

From Figure 8a, it can be seen that the oxidation kinetic curves of both matrix specimens and coated specimens show parabolic shapes, and Figure 8b shows that the square of the weight gain of the specimens shows a linear relationship with time. The above results indicate that the oxides generated during the heating process can cover the surface densely and will not crack due to excessive internal stress, and the thickening of the oxide film on the surface of the matrix and the coating have a blocking effect on the oxidation, which prevents further oxidation of the matrix. This also indicates that there is a better bonding force between the coating and the matrix [45,46].
With the increase in Y do** in the coatings, the mass of the sample weight gain first decreased and then increased at the same time, and the oxidation rate of the samples first slowed down and then accelerated. This indicates that the antioxidant protection ability of the coating increases and then decreases with the increase in Y do**, and the 10YSZ coating has the best antioxidant performance, while the 15YSZ has the worst antioxidant performance, and even the performance is not as good as that of the ZrO2 coating. Combined with the SEM morphology of the coatings and the results of the bonding test, it can be found that the 10YSZ coating has the best densification and bonding; the weight gain of the specimen is mainly attributed to the oxidation of the matrix, and the dense coating can slow down the rate of the oxidation of the matrix at high temperatures, so the dense 10YSZ coating has the best antioxidant performance.

3.6. Electrochemical Hydrogen Permeation Performance of Coatings

From the electrochemical hydrogen permeation curves in Figure 9a, it can be seen that both the ZrO2 coating and the YSZ coating have a good protection effect on the matrix. The steady-state hydrogen permeation current density of the samples protected with the coatings decreased significantly relative to the steady-state current density of 33.0 μA/cm2 for the pure matrix. Comparing the electrochemical hydrogen permeation curves of YSZ coatings with different Y do** amounts, it is seen that the hydrogen barrier performances of the coatings are not linearly correlated with the Y do** amount, and the hydrogen barrier performance of the coatings shows an increasing and then decreasing trend as the do** amount increases. The variation in steady-state hydrogen permeation flux for different samples is shown in Figure 9b, and the data related to the hydrogen permeation test are shown in Table 3, which indicate that the coating can effectively reduce the permeation and diffusion of hydrogen into the matrix. The 10YSZ coating had the lowest steady-state hydrogen permeation current density of 9.13 μA/cm2, and the steady-state hydrogen permeation current density decreased by 26.1% compared to the ZrO2 coating, while the steady-state hydrogen permeation current densities of 5YSZ and 15YSZ were 15.34 μA/cm2 and 12.84 μA/cm2, respectively. Compared to the matrix, the 5YSZ, 10YSZ, and 15YSZ coatings resulted in a 61.1%, 72.3%, and 53.5% improvement in the hydrogen barrier performance of the specimens, respectively.
From the theory related to Y do** to stabilize the crystal shape, the do** of Y3+ produces oxygen vacancies, causing lattice deformation, and the combination of oxygen ion vacancies and Zr4+ cations is the main reason for making the tetragonal phase stable at room temperature [40,47]. It has been shown that the stabilization of the tetragonal phase is only controlled by oxygen ion vacancies, and a small concentration of oxygen ion vacancies associated with Zr ions can be effectively generated by do** appropriate amounts of Y ions. However, with the further increase in Y do**, the continuous increase in the oxygen vacancy concentration will lead to increase in the distortion of the coordination layer of ZrO2 crystals, and at this time, the local coordination number inside the crystals may appear to be much lower than eight, which is not conducive to the stabilization of the ZrO2 crystalline form. From the analysis of the physical properties of the sol, the continuous increase in the viscosity of the sol with the excess increase in Y do** affects the coating quality and thickness of the coating, which ultimately leads to an increase in coating defects and cracks and a decrease in the bonding of the coating to the matrix [48,49]. The hydrogen barrier performance of the coatings decreases as H atoms preferentially pass through the defects of the coatings. There is a high degree of consistency between the changes in antioxidant performance and hydrogen barrier performance of coatings with different Y contents, as both are more sensitive to the densities and integrity of the coatings.

4. Conclusions

In this study, composite coatings YSZ with different do** amounts of Y element were prepared by the sol-gel method, and the results through multifaceted characterization and performance evaluation are as follows.
(1)
XRD and SEM-EDS analyses show that the rare earth element Y was successfully doped into the ZrO2 coating. Y can stabilize the tetragonal phase zirconia existing at high temperatures to a room temperature environment, alleviate the cracking problem of the coating due to the volume change triggered by the crystalline transition, and improve the densification of the coating. Meanwhile, the addition of yttrium can refine the grain size of the oxide; as the Y do** increased from 5 wt% to 15 wt%, the average grain size of the oxides decreased by about 31%, 37%, and 60%, respectively.
(2)
Compared with the ZrO2 coating, the hardness, adhesion, and antioxidant performances of the YSZ coating show a tendency to increase and then decrease with the increase in Y do**, and the YSZ coating with a Y do** of 10 wt% has the best overall performance. When the Y do** amount was lower than 10 wt%, the uniformity and continuity of the coating surface gradually improved with the increase in yttrium do**, and the hardness was improved, with the hardness level increasing from B to 2H and the adhesion increasing from 4B to 5B level. The surface quality of the coating decreased and cracks and defects increased after the Y do** exceeded 10 wt%. Although the hardness level was further increased to 4H, the coating was more brittle at this time and was prone to peeling off, and the adhesion level decreased to 3B.
(3)
After heating at 500 °C for 12 h, the antioxidant performance of the ZrO2 coatings was enhanced by 60% compared to the pure substrate, and the antioxidant performance of the 5YSZ, 10YSZ, and 15YSZ coatings was enhanced by 61.9%, 65.8%, and 53.5%, respectively. Meanwhile, the steady-state hydrogen permeation current density of the ZrO2 coating was reduced by 62.5% compared to the matrix, and the steady-state hydrogen current density of the 5YSZ, 10YSZ, and 15YSZ coatings was reduced by 61.1%, 72.3%, and 53.5%, respectively.
In conclusion, this study demonstrates that the addition of the appropriate amount of Y element can effectively improve the hydrogen barrier property and other comprehensive properties of ZrO2 coating. This provides an experimental basis and theoretical reference for further industrialized application of oxide coatings in many fields in the hydrogen energy industry chain, especially in nuclear energy and aerospace, which require hydrogen permeation protection at high temperatures.

Author Contributions

Conceptualization, J.W. and J.X.; methodology, M.H.; software, J.X.; validation, J.W. and J.Z.; formal analysis, J.W.; investigation, J.Z.; resources, J.X.; writing—original draft preparation, J.W.; writing—review and editing, M.H.; visualization, J.X.; supervision, S.L.; project administration, S.L.; funding acquisition, S.L. All authors have read and agreed to the published version of the manuscript.

Funding

This work was partially supported by grants from the National Natural Science Foundation of China (52071297), the Natural Science Foundation of Henan Province (212300410082), and Project Funding for Young Backbone Teachers in Colleges and Universities of Henan Province (2020GGJS013). These grants are gratefully acknowledged.

Institutional Review Board Statement

Not applicable.

Informed Consent Statement

Not applicable.

Data Availability Statement

The raw data supporting the conclusions of this article will be made available by the authors on request.

Conflicts of Interest

The authors declare that the research was conducted in the absence of any commercial or financial relationships that could be construed as a potential conflict of interest.

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Materials 17 03017 g001
Figure 1. Schematic diagram of electrochemical hydrogen penetration test device.
Figure 1. Schematic diagram of electrochemical hydrogen penetration test device.
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Materials 17 03017 g002
Figure 2. TG (a), DTG (b), and DSC (c) curves of ZrO2 and YSZ sol.
Figure 2. TG (a), DTG (b), and DSC (c) curves of ZrO2 and YSZ sol.
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Materials 17 03017 g003
Figure 3. SEM images of (a) ZrO2 coating, (b) 5YSZ, (c) 10YSZ and (d) 15YSZ coatings surface.
Figure 3. SEM images of (a) ZrO2 coating, (b) 5YSZ, (c) 10YSZ and (d) 15YSZ coatings surface.
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Materials 17 03017 g004
Figure 4. Element distribution on the surface of YSZ coating: (a) morphology, (b) Zr element distribution, (c) O element distribution, (d) Y element distribution.
Figure 4. Element distribution on the surface of YSZ coating: (a) morphology, (b) Zr element distribution, (c) O element distribution, (d) Y element distribution.
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Materials 17 03017 g005
Figure 5. XRD patterns of ZrO2 and YSZ coating.
Figure 5. XRD patterns of ZrO2 and YSZ coating.
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Materials 17 03017 g006
Figure 6. Pencil hardness statistics of ZrO2 coating and YSZ coating.
Figure 6. Pencil hardness statistics of ZrO2 coating and YSZ coating.
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Materials 17 03017 g007
Figure 7. Topography of the (a) ZrO2 coating, (b) 5YSZ, (c) 10YSZ and (d) 15YSZ coating after scratch test. (Note: The dashed circles in the figure represent the locations where the coating was peeling off).
Figure 7. Topography of the (a) ZrO2 coating, (b) 5YSZ, (c) 10YSZ and (d) 15YSZ coating after scratch test. (Note: The dashed circles in the figure represent the locations where the coating was peeling off).
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Materials 17 03017 g008
Figure 8. Graph of antioxidant property test results of samples: (a) weight gain as a function of time, (b) weight gain squared as a function of time.
Figure 8. Graph of antioxidant property test results of samples: (a) weight gain as a function of time, (b) weight gain squared as a function of time.
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Materials 17 03017 g009
Figure 9. (a) Electrochemical hydrogen permeation curves and corresponding (b) hydrogen permeation flux curves of the matrix and coatings.
Figure 9. (a) Electrochemical hydrogen permeation curves and corresponding (b) hydrogen permeation flux curves of the matrix and coatings.
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Table 1. Chemical composition of Q235 mild steel.
Table 1. Chemical composition of Q235 mild steel.
ElementCSiMnPSFe
Contents (wt%)0.160.180.720.0160.018Bal.
Table 2. Heat treatment process parameters for coatings.
Table 2. Heat treatment process parameters for coatings.
Temperature Range (°C)Heating Rate (°C/min)Terminal Holding Time (min)
RT–200135
200–400190
400–5503120
Table 3. Summary of hydrogen permeation results of the matrix, ZrO2, and YSZ coatings.
Table 3. Summary of hydrogen permeation results of the matrix, ZrO2, and YSZ coatings.
SampleQ235ZrO25YSZ10YSZ15YSZ
Iss (μA/cm2)33.0112.3612.849.1315.34
J∞ (mol/cm2·s)3.42 × 10−61.28 × 10−61.33 × 10−60.95 × 10−61.59 × 10−6
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MDPI and ACS Style

Wu, J.; **e, J.; He, M.; Zhang, J.; Li, S. Yttria-Stabilized Zirconia Composite Coating as Barrier to Reduce Hydrogen Permeation into Steel. Materials 2024, 17, 3017. https://doi.org/10.3390/ma17123017

AMA Style

Wu J, **e J, He M, Zhang J, Li S. Yttria-Stabilized Zirconia Composite Coating as Barrier to Reduce Hydrogen Permeation into Steel. Materials. 2024; 17(12):3017. https://doi.org/10.3390/ma17123017

Chicago/Turabian Style

Wu, Jianmeng, Jiaqi **e, Mengyuan He, **gyi Zhang, and Songjie Li. 2024. "Yttria-Stabilized Zirconia Composite Coating as Barrier to Reduce Hydrogen Permeation into Steel" Materials 17, no. 12: 3017. https://doi.org/10.3390/ma17123017

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