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Effects of C and heat treatment on microstructure, mechanical, and tribo-corrosion properties of VAlTiMoSi high-entropy alloy coating

  • Zhengyi Fu , Sansan Ding EMAIL logo , Aiqin Tian , Dawei Chen , Xu Chen , Huaqiang Lin , Zhongwen Li , Xiaohong Sun , Xiangjian Meng and Wei Zhou EMAIL logo
Published/Copyright: June 10, 2024
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REVIEWS ON ADVANCED MATERIALS SCIENCE
From the journal REVIEWS ON ADVANCED MATERIALS SCIENCE Volume 63 Issue 1

Abstract

High-entropy alloy (HEA) coatings have demonstrated great potential in anti-wear applications. To further improve the mechanical and tribo-corrosion properties of the HEA coatings, the VAlTiMoSi, (VAlTiMoSi)80C20, and (VAlTiMoSi)60C40 coatings were successfully deposited by DC magnetron sputtering. The microstructure, mechanical, and tribo-corrosion properties of as-deposited and heat-treated coatings were analyzed. All the as-deposited HEA coatings were BCC + amorphous phases. The thermal effect promoted the formation of intermetallic compounds, and the C inhibited the formation of Mo3Si and Ti5Si4. The hardness and elastic modulus of the heat-treated VAlTiMoSi coating were 20.1 and 294.0 GPa, respectively. The heat-treated (VAlTiMoSi)60C40 coating showed the lowest wear rate, namely 5.2 × 10−14 m3·Nm−1, and the best formation ability of passive film in 3.5 wt% NaCl solution.

Keywords: high-entropy carbides; mechanical performance; wear resistance; heat treatment; magnetron sputtering

1 Introduction

The marine economy and resource exploration have gained significant attention in various countries. The ocean engineering equipment plays a momentous role in the ocean development. However, friction and corrosion in the seawater environment severely reduce the operating stability and service life of components [1]. Therefore, the protection of the sea-related components, such as ocean platforms, pumps, and lifting systems, come as a worldwide issue. The tribo-corrosion resistance coating coated on the component is an economical and effective fashion to improve the wear resistance and corrosion resistance. Nowadays, nitride and carbide coating are the main protective coatings for marine components [2,3]. However, cracking and peeling have not yet been properly resolved, and research bottlenecks began to appear for conventional protective coatings [4,5]. For this reason, a novel material system may inspire some unexpected achievement for the marine protective coatings.

High entropy alloy (HEA) coating has a great potential in structural design and performance modulation due to the unique lattice distortion, high entropy effect, cocktail effect, and sluggish effect. Therefore, quite a few material systems and structures are designed to fulfill the excellent tribo-corrosion resistance. For the corrosion resistance, it is suggested that the passive film derived from HEA coating has a low donor density and a high ability to inhibit ions adsorption [6]. The reduced point-defect density in the passive film also plays a decisive role in corrosion resistance [7]. Wang et al. [6] assessed the tribo-corrosion resistance of the (TiZrNbTaMo)C HEA coating in 3.5 wt% NaCl solution, impressively, the self-corrosion current density of the HEA coating was one order of magnitude lower than that of bare CP-Ti. For the wear resistance, the phase modification [8], elemental type/content [9], carbonization/nitriding [10], heat treatment [11], etc., feature in enhancing the hardness of the coating and likewise contribute to reducing wear loss. Niu et al. [12] evaluated that the doping of carbon in HEA coating effectively made the structure dense, and higher content of C benefited in improving the tribo-corrosion resistance. In particular, the N-doped CrNbTiAlV coating obtained an extremely low wear rate (∼4.4 × 10−7 mm3·N−1·m−1) in 3.5 wt% NaCl solution [13]. Wang et al. [14] proved that the heat treatment at 300°C would obviously enhance the wear resistance of (TiVCrAlMo)N coating. And the thermal stability of coating must be considered because of the transient temperature generated during the wear process [15]. From the literature, the HEA and C containing HEA exhibit a good thermal stability [16,17]. As aforementioned, the introduction of non-metallic elements (C or N) and heat treatment can effectively improve the tribo-corrosion resistance of the coating. However, there is a lack of systematic study about the effect of C/N and heat treatment simultaneously on the mechanical property and tribo-corrosion resistance of HEA coating.

From the previous literature on the VAlTiCrCu [18], VAlTiCrMo [19], and VAlTiCrSi [20] coating, remarkable results on tribo-corrosion or corrosion resistance were reported. Therefore, V, Al, Ti, Mo, and Si were selected as the principal element of the HEA coating. In this work, to investigate the effect of C and heat on the microstructure, mechanical, and tribo-corrosion properties, 20 and 40 at% of C were introduced into the HEA coatings by magnetron sputtering. The hardness and elastic modulus of the as-deposited and heat-treated coating were tested at the ambient temperature. The friction and corrosion experiments were operated simultaneously in 3.5 wt% NaCl solution.

2 Experiment

2.1 HEA coatings preparation

The HEA coatings were deposited on 304 stainless steel and Si (100) substrates by a Hauzer Flexicoat 850 DC magnetron sputtering system. The rectangular metal blocks with target sizes of 125 mm × 10 mm × 12 mm, that is high purity (≥99 %) V, Al, Ti, Mo, and Si, were stacked in the vertical direction in the order of V–Al–Ti–Mo–Si from top to bottom, forming a total of 12 target cycles. A monolithic graphite target (600 mm × 125 mm × 12 mm) is utilized to introduce carbon into the coatings. Before fixing the substrates into tunable sample racket, the substrates were subsequently ultrasonically cleaned with acetone and ethanol for 30 min, respectively. When the chamber vacuum pressure value is lower than 1.0 × 10−4 Pa, the targets were etched by argon ions bombardment to remove the oxides and contaminants. During the deposition process, the sputtering power of V–Al–Ti–Mo–Si composite target was 2,000 W, the graphite targets were 0, 1,000, and 2,500 W, the substrate bias was −50 V, the rotation speed of sample racket was 2 rpm, and the substrate temperature was around 100°C. The abovementioned parameters were maintained for 7 h to prepare the VAlTiMoSi and VAlTiMoSiC x coatings.

2.2 Heat treatment of the HEA coatings

The HEA coatings on 304 stainless steel were put into a vacuum tube furnace. Prior to heat treatment, the residual oxygen in the quartz tube was extracted. According to the result of the phase transformation, 700°C was selected as the temperature of heat treatment, and argon gas was used as a protective gas. The heating rate is 10 °C·min−1 and the holding time is 1 h at 700°C, then all the samples were cooled to ambient temperature in the furnace.

2.3 Mechanical and tribo-corrosion tests

The Nanoidenter (G200, MTS) was conducted to characterize the mechanical properties of the coatings at room temperature in a mode of fixed 1,000 nm depth. The six test points for a sample ensure the convince data. The hardness and elastic modulus were calculated by Nanosuit software that embedded the method of Oliver-Pharr. The tribological properties of the HEA coatings were performed on a friction tester (Rtec MFT5000) in 3.5 wt% NaCl solution, simultaneously, the corrosion resistance of the coatings was measured by a Modulab analyzer. Three-electrode electrochemical method was used to obtain the open circuit potential (OCP) result, the Ag/AgCl worked as reference electrode, a platinum wire as a counter electrode, and the HEA coatings as working electrode. With regard to the obtained friction curve, the applied load is 1 N, grinding pair is Si3N4 ball with a diameter of 6 mm, the sliding frequency is 1 Hz, and the sliding speed is 1 cm·s−1. The wear rate was calculated using the following formula:

(1) w = Sl FL ,

where S is the area of the wear scar, l is the length of grinding track (5 mm), F is the applied load, and L is the total sliding length (18 m). The detailed experimental process can be referred to in the literature [18].

2.4 Characterization methods

The surface and cross-sectional morphologies of the as-prepared and heat-treated coatings were analyzed by scanning electron microscope (SEM; Verios G4 UC). The wear scar morphologies of the tested coatings were observed by Verios G4 UC, likewise. To precisely collect the chemical composition of the as-deposited coatings, the glow-discharge optical emission spectrometry (GDA 750HP) was used. The crystal structure was detected by X-ray diffractometer (XRD; D8 Advance Davinci) with Cu-Kα source (λ = 0.154 nm), and the scanning angle ranged from 10° to 90°. The profile of the wear scar that is perpendicular to the wear scar direction was obtained by a Profilometer (ASTQ, America). To analyze the effect of the heat treatment on the structure and elemental distribution, transmission electron microscope (TEM; Talos F200x) was operated to characterize the cross-sectional morphology and mapping. Additionally, the sample was pretreated by focused ion beam (Carl Zeiss Auriga).

3 Results and discussion

3.1 Microstructure and morphologies of the coatings

Table 1 gives the chemical composition of the as-deposited coating. It indicates that the atomic percentage of elemental constant covers the range from 5 to 35 at% of the HEA. The difference in sputtering yield of the target caused various relative atomic percent [21]. The C content in the coatings increased with the increased sputtering power. For the purpose of concise description, the as-deposited HEA coatings were named as VAlTiMoSi, (VAlTiMoSi)80C20, and (VAlTiMoSi)60C40 according to the atomic percentage of C.

Table 1

Chemical composition of the as-prepared HEA coatings (at%)

Sample V Al Ti Mo Si C
VAlTiMoSi 15.90 25.77 19.12 10.38 28.83 —
(VAlTiMoSi)80C20 13.74 16.67 14.38 10.87 20.94 23.36
(VAlTiMoSi)60C40 10.04 13.42 11.10 10.79 14.67 39.98

Figure 1 illustrates XRD patterns of the as-deposited and heat-treated HEA coatings. The peak located at 43.7°, 50.8°, and 74.7° corresponds to the 304 stainless steel. The as-deposited VAlTiMoSi HEA coating and carbonized VAlTiMoSi HEA coating exhibited an amorphous structure as shown in Figure 1(a). The introduction of carbon into the coating further promoted the amorphization of the coating. Considering that the XRD diffraction peak position of the amorphous phase overlaps with the BCC phase, the microstructure of the coatings will be further characterized later [22]. For the heat-treated coatings, it can be obviously observed from Figure 1(b) that heat treatment has a positive effect on crystallization of the HEA coatings on 304 stainless steel. After heat treatment, the crystallization of VAlTiMoSi coating was promoted, resulting in the formation of Mo3Si, Ti5Si4, TiSi2, and AlV3. Comparing the XRD patterns of the heat-treated coatings, higher C content inhibited the formation of the Mo2C and Ti5Si4.

Figure 1 XRD patterns of the (a) as-prepared and (b) heat-treated HEA coatings.
Figure 1

XRD patterns of the (a) as-prepared and (b) heat-treated HEA coatings.

The microstructure of the VAlTiMoSi, (VAlTiMoSi)80C20, and (VAlTiMoSi)60C40 coatings is presented in Figure 2. As shown in Figure 2(a), all the as-deposited coatings showed a smooth and compact surface morphology. The introduction of C has minimal effect on the surface morphology of the VAlTiMoSi coating. And the thickness of the VAlTiMoSi, VAlTiMoSi, and VAlTiMoSi coatings was 2.89, 2.29, and 2.65 μm, respectively. The cross-sectional structure showed a columnar shape, which is a typical morphology for magnetic sputtering coatings [23,24]. For the heat-treated HEA coatings, white and small particle in SEM view existed in all the heat-treated HEA coatings. Comparing with the as-deposited coatings, the grain size of the heat-treated coatings became larger. Additionally, the thermal effect has a significant effect on the grain growth of the C-included HEA coatings [25]. A noticeable difference can also be found on the surface morphology. The number of the white and large grain was less and more for VAlTiMoSi, VAlTiMoSi, and VAlTiMoSi coatings, respectively. From a rough statistical result of the crystal cluster size, the size of as-deposited coatings was in the range from 50 to 110 nm, and larger size ranged from 120 to 240 nm and can be found for annealed coatings. The thickness of the heat-treated coatings was 2.73, 3.38, 3.22 μm, respectively.

Figure 2 Surface and cross-sectional morphologies of the HEA coatings before heat treatment: (a) VAlTiMoSi, (b) (VAlTiMoSi)80C20, (c) (VAlTiMoSi)60C40, and after annealing at 700°C (d) VAlTiMoSi, (e) (VAlTiMoSi)80C20, (f) (VAlTiMoSi)60C40.
Figure 2

Surface and cross-sectional morphologies of the HEA coatings before heat treatment: (a) VAlTiMoSi, (b) (VAlTiMoSi)80C20, (c) (VAlTiMoSi)60C40, and after annealing at 700°C (d) VAlTiMoSi, (e) (VAlTiMoSi)80C20, (f) (VAlTiMoSi)60C40.

To further analyze the effect of carbon and heat treatment on the microstructure of the coatings from a high-resolution view, the TEM result of the as-deposited and heat-treated HEA coatings is shown in Figures 3 and 4, respectively. As shown in Figure 3, the compact and columnar cross-sectional morphologies of the as-deposited coatings can be obviously observed. (VAlTiMoSi)80C20 coating almost has the same size as the columnar structure with VAlTiMoSi coating. However, higher content of C may promote a little coarser columnar structure as shown in Figure 3(c). From the corresponding elemental mapping of the coatings, all the as-deposited HEA coatings have a uniform element distribution. Furthermore, combined with XRD patterns in Figure 1(a) and corresponded selected area electron diffraction (SAED) patterns in Figure 3, it can be seen that all the coatings are mainly composed of BCC polycrystalline and amorphous.

Figure 3 TEM images of the cross-sectional morphologies, corresponding elemental mapping, and SAED patterns of the as-deposited coatings: (a) VAlTiMoSi, (b) (VAlTiMoSi)80C20, and (c) (VAlTiMoSi)60C40.
Figure 3

TEM images of the cross-sectional morphologies, corresponding elemental mapping, and SAED patterns of the as-deposited coatings: (a) VAlTiMoSi, (b) (VAlTiMoSi)80C20, and (c) (VAlTiMoSi)60C40.

Figure 4 TEM images of the cross-sectional morphologies, corresponding elemental mapping, and SAED patterns of the heat-treated coatings: (a) VAlTiMoSi, (b) (VAlTiMoSi)80C20, and (c) (VAlTiMoSi)60C40.
Figure 4

TEM images of the cross-sectional morphologies, corresponding elemental mapping, and SAED patterns of the heat-treated coatings: (a) VAlTiMoSi, (b) (VAlTiMoSi)80C20, and (c) (VAlTiMoSi)60C40.

For the heat-treated HEA coatings, the columnar structure of the VAlTiMoSi disappeared and formed large size grains as shown in Figure 4. Contrarily, the thermal effect is unfavorable in modification of the columnar structure of the C-included HEA coatings, and the compact and columnar cross-sectional morphologies were almost the same as the as-prepared C-included coatings, correspondingly. As for the elemental mappings, there is a slice of element segregation in the VAlTiMoSi coating. (VAlTiMoSi)80C20 and (VAlTiMoSi)60C40 coatings have outstanding ability in anti-segregation. From the corresponding SAED patterns, the crystallization degree of C-included coatings was lower than that of VAlTiMoSi coating, which is consistent with the XRD results in Figure 1(b).

3.2 Mechanical and tribo-corrosion properties

The hardness and elastic modulus of the as-deposited and heat-treated HEA coatings are presented in Figure 5. As can be seen in Figure 5(a), the hardness and elastic modulus of VAlTiMoSi coating were 10.4 and 200.1 GPa, respectively. The hardness of C-included HEA coatings was higher than VAlTiMoSi coating, and the hardness and elastic modulus of the (VAlTiMoSi)80C20 coating were 12.6 and 215.6 GPa, respectively, because of the solid-solution strengthening of C. However, higher C content coating is inferior in the mechanical property compared with (VAlTiMoSi)80C20 coating, which is mainly attributed to the increased content of amorphous carbon [26]. For the heat-treated HEA coatings, the mechanical properties of all the coatings significantly improved, as shown in Figure 5(b). The VAlTiMoSi and (VAlTiMoSi)60C40 coatings shared almost the same hardness, around 20.1 and 19.6 GPa, respectively. And the hardness of the heat-treated VAlTiMoSi coating is almost twice that of the as-prepared VAlTiMoSi coating. Comparing Figure 1(a) and (b), the intermetallic compounds Mo3Si, Mo2C, AlV3, etc., contributed to the higher hardness. It is widely shared that the value of H/E is closely related to the damage resistance and elastic strain capacity of the coating, and the ratio of H3/E2 can represent the ability of the film to resist crack initiation and propagation to a certain extent [27,28]. Consequently, the higher ratio of H/E and H3/E2 means the higher wear resistance [29]. The (VAlTiMoSi)60C40 coating gained the highest H/E and H3/E2 value when compared with as-deposited or heat-treated VAlTiMoSi and (VAlTiMoSi)80C20 coatings, respectively. And the heat treatment promoted the wear resistance, since the value of H/E and H3/E2 were higher than as-deposited coatings.

Figure 5 Hardness and elastic modulus, the ratio of H/E and H3/E2 of the HEA coatings: (a) as-prepared coatings and (b) heat-treated coatings.
Figure 5

Hardness and elastic modulus, the ratio of H/E and H3/E2 of the HEA coatings: (a) as-prepared coatings and (b) heat-treated coatings.

The friction curve in a reciprocating friction mode of the coatings is shown in Figure 6. For the as-prepared coatings, the coefficient of friction (COF) of the VAlTiMoSi coating was lower than C-included coatings. The average COF of the VAlTiMoSi coating was 0.79, which is higher than most of the HEA coatings [7,30,31]. The higher C content did not reduce the COF of the (VAlTiMoSi)60C40 coating, the COF of (VAlTiMoSi)80C20 and (VAlTiMoSi)60C40 coating was approximately equal. However, the heat-treated HEA coatings had a relative lower COF than as-prepared coatings. The average COF of all the heat-treated coatings was not higher than 0.6, and the lowest average COF was 0.42, belonging to the (VAlTiMoSi)80C20 coating.

Figure 6 COF and OCP curves of the HEA coatings tested in 3.5 wt% NaCl solution: (a and c) as-deposited coatings and (b and d) heat-treated coatings.
Figure 6

COF and OCP curves of the HEA coatings tested in 3.5 wt% NaCl solution: (a and c) as-deposited coatings and (b and d) heat-treated coatings.

The OCP evolution of the working electrode contributes to obtain the qualitative information of electrochemical state during the tribo-corrosion test. The OCPs of the tested HEA coatings, during, and after the tribo-corrosion tested in 3.5 wt% NaCl solution are shown in Figure 6(c) and (d). In terms of static corrosion resistance, the OCP value of the as-deposited VAlTiMoSi and (VAlTiMoSi)80C20 coatings was relatively higher than (VAlTiMoSi)60C40 coating. However, the OCP value of the heat-treated VAlTiMoSi coating is the lowest, which means that thermal effect failed to enhance VAlTiMoSi coating in static corrosion resistance. Upon commencing the friction test, it is observed that all the coatings exhibited a significant negative deviation in their OCP curves. This deviation is derived from the mechanical destruction of the passive film. During the friction process, the OCP curves of the coating fluctuate. The fluctuation can be mainly attributed to the formation and destruction of the passive film during the reciprocating motion of the grinding pair. After the friction test, the OCP value almost returned back to its original state, indicating the reformation of the complete passive film. Additionally, as shown in Figure 6(d), the C-included coatings had a better formation ability of the passive film. And the complete passive film of the (VAlTiMoSi)60C40 coating has been formed before the end of the friction process.

The wear rate is an evaluation index of wear duration, and the wear rate of the coatings is depicted in Figure 7. As shown in Figure 7(a), the wear rate of the as-prepared (VAlTiMoSi)80C20 and (VAlTiMoSi)60C40 coatings was lower than 3.5 × 10−13 m3·Nm−1, while the VAlTiMoSi coating was higher than 1.0 × 10−12 m3·Nm−1. Introducing C into the HEA coating significantly improved the wear resistance. Comparing with the as-prepared coatings, the wear resistance of the heat-treated coating improved constructively. The wear rate of the heat-treated VAlTiMoSi coating reduced by more than one order of magnitude, and the (VAlTiMoSi)60C40 coating had the lowest wear rate, i.e., 5.2 × 10−14 m3·Nm−1. Particularly, the as-prepared and heat-treated (VAlTiMoSi)60C40 coating obtained the lowest wear rate among the tested coatings.

Figure 7 Wear rate of the tested HEA coatings.
Figure 7

Wear rate of the tested HEA coatings.

To analyze the wear mechanism of HEA coatings, the morphologies of the wear track were collected. As can be seen in Figure 8(a), furrows obviously distributed along the sliding direction, which means abrasive wear dominated in the wear track of the as-deposited coatings. Especially, for the VAlTiMoSi and (VAlTiMoSi)80C20 coatings, delamination on the edge of the wear track appeared, it indicates that delamination wear also existed, that is why these two kinds of coatings had higher wear rate than (VAlTiMoSi)60C40 coating. After heat treatment, the plowing effect of VAlTiMoSi and (VAlTiMoSi)60C40 coatings decreased significantly, and the delamination of VAlTiMoSi and (VAlTiMoSi)80C20 coatings disappeared. Additionally, known from the wear track marked by yellow dash lines, the width of wear track of heat-treated coatings is narrower than as-deposited coatings. Therefore, the wear rate of all the heat-treated HEA coatings decreased. However, the furrows in the wear track of (VAlTiMoSi)80C20 coating were conspicuous, which can elaborate the higher wear rate compared with VAlTiMoSi coating. Abrasive wear is the main wear mechanism of these heat-treated coatings. Considering the mechanical and tribo-corrosion properties, the heat-treated (VAlTiMoSi)60C40 coating has the best application prospect.

Figure 8 Morphologies of the wear track of the tested coatings: (a and d) VAlTiMoSi, (b and e) (VAlTiMoSi)80C20, and (c and f) (VAlTiMoSi)60C40.
Figure 8

Morphologies of the wear track of the tested coatings: (a and d) VAlTiMoSi, (b and e) (VAlTiMoSi)80C20, and (c and f) (VAlTiMoSi)60C40.

3.3 Effect of C and heat treatment on the HEA coatings

For the as-deposited coatings, a slice of C enhanced the mechanical properties of the HEA coating by solid-solution strengthening, and the excessive C cannot further improve the hardness of the coating due to the formation of amorphous carbon. Known from the XRD patterns of heat-treated coatings, that the C inhibited the formation of Si-containing intermetallic compounds (Mo3Si and Ti5Si4), and C replaced Si to form Mo2C.

Heat treatment released the internal stress of the coatings and induced the existence of intermetallic compounds. After heat treatment, the bigger grain size of the (VAlTiMoSi)60C40 coating reduced the number of grain boundaries, which contributed to the corrosion resistance. Comparing the OCPs of the heat-treated coatings, unlike Mo2C, Mo3Si was hardly able to promote the formation of passive film.

4 Conclusions

To address the effect of C and heat treatment on the microstructure, mechanical, and tribo-corrosion properties of HEA coating, the VAlTiMoSi, (VAlTiMoSi)80C20, and (VAlTiMoSi)60C40 coatings were successfully prepared by DC magnetron sputtering.

All the as-deposited coatings were composed of BCC and amorphous phases. Heat treatment significantly improved the mechanical and tribo-corrosion properties of the HEA coatings. The hardness of the heat-treated coatings was increased by 36–93%, and the values of H/E and H3/E2 of (VAlTiMoSi)60C40 coating were up to 0.07 and 0.11, respectively. In particular, the wear rate of the heat-treated VAlTiMoSi coating reduced by more than one order of magnitude compared with as-deposited VAlTiMoSi coating. The COF of the heat-treated coatings is lower than 0.6. Abrasive wear dominated the wear mechanism after heat treatment. The improvement in tribo-corrosion resistance and mechanical properties of the coatings is mostly due to the reduction of residual stress and the generation of intermetallic compounds.

Acknowledgments

The authors thank the teachers, leaders and colleagues who provided the necessary support for the implementation of the project, in addition to the anonymous reviewers for their productive suggestions for improving the article.

  1. Funding information: The authors state no funding involved.

  2. Author contributions: Zhengyi Fu: conceptualization, methodology, formal analysis, writing – original draft, data curation, visualization, validation; Sansan Ding: data curation, visualization, validation, supervision. Aiqin Tian: methodology; Dawei Chen: investigation; Xu Chen: methodology, supervision; Huaqiang Lin: methodology, supervision; Zhongwen Li: methodology; Xiaohong Sun: methodology, supervision; Xiangjian Meng: investigation, methodology; Wei Zhou: conceptualization, supervision, funding acquisition. All authors have accepted the responsibility for the entire content of this manuscript and approved its submission.

  3. Conflict of interest: The authors state no conflict of interest.

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Received: 2023-12-08
Revised: 2024-03-14
Accepted: 2024-04-10
Published Online: 2024-06-10

© 2024 the author(s), published by De Gruyter

This work is licensed under the Creative Commons Attribution 4.0 International License.

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https://doi.org/10.1515/rams-2024-0018
Keywords for this article
high-entropy carbides; mechanical performance; wear resistance; heat treatment; magnetron sputtering
Creative Commons
BY 4.0

Articles in the same Issue

  1. Review Articles
  2. Effect of superplasticizer in geopolymer and alkali-activated cement mortar/concrete: A review
  3. Experimenting the influence of corncob ash on the mechanical strength of slag-based geopolymer concrete
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  108. Modeling the strength parameters of agro waste-derived geopolymer concrete using advanced machine intelligence techniques
  109. Promoting the sustainable construction: A scientometric review on the utilization of waste glass in concrete
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  111. Investigation of nano-basic oxygen furnace slag and nano-banded iron formation on properties of high-performance geopolymer concrete
  112. Effect of incorporating ultrafine palm oil fuel ash on the resistance to corrosion of steel bars embedded in high-strength green concrete
  113. Influence of nanomaterials on properties and durability of ultra-high-performance geopolymer concrete
  114. Influence of palm oil ash and palm oil clinker on the properties of lightweight concrete
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