Next Article in Journal
Reactivity of Metakaolin in Alkaline Environment: Correlation of Results from Dissolution Experiments with XRD Quantifications
Previous Article in Journal
Effect of Ti Content on the Microstructure and Corrosion Resistance of CoCrFeNiTix High Entropy Alloys Prepared by Laser Cladding
 
 
Search for Articles:
Title / Keyword
Author / Affiliation / Email
Journal
Article Type
 
 
Advanced Search
 
Section
Special Issue
Volume
Issue
Number
Page
 
Journals
Materials
Volume 13
Issue 10
10.3390/ma13102213
materials-logo
Submit to this Journal Review for this Journal Propose a Special Issue
► Article Menu

Article Menu

share Share announcement Help format_quote Cite question_answer Discuss in SciProfiles thumb_up
...
Endorse textsms
...
Comment
first_page
settings
Order Article Reprints
Font Type:
Arial Georgia Verdana
Font Size:
Aa Aa Aa
Line Spacing:
Column Width:
Background:
Article

Manufacturing ZrB2–SiC–TaC Composite: Potential Application for Aircraft Wing Assessed by Frequency Analysis through Finite Element Model

by
Behzad Mohammadzadeh
1,2,†,
Sunghoon Jung
3,4,†,
Tae Hyung Lee
3,†,
Quyet Van Le
5,*,
Joo Hwan Cha
6,
Ho Won Jang
3,
Sea-Hoon Lee
7,*,
Junsuk Kang
1,2,* and
Mohammadreza Shokouhimehr
3,*
1
Department of Landscape Architecture and Rural Systems Engineering, Seoul National University, Seoul 08826, Korea
2
Research Institute of Agriculture and Life Sciences, Seoul National University, Seoul 08826, Korea
3
Department of Materials Science and Engineering, Research Institute of Advanced Materials, Seoul National University, Seoul 08826, Korea
4
Advanced Nano Surface Department, Surface Technology Division, Korea Institute of Materials Science, Changwon 51508, Korea
5
Institute of Research and Development, Duy Tan University, Da Nang 550000, Vietnam
6
Innovative Enterprise Cooperation Center, Korea Institute of Science & Technology, Hwarangro 14-gil, Seongbuk-gu, Seoul 02792, Korea
7
Division of Powder/Ceramics Research, Korea Institute of Materials Science, Changwon 51508, Korea
*
Authors to whom correspondence should be addressed.
†
These authors contributed equally in this work.
Materials 2020, 13(10), 2213; https://doi.org/10.3390/ma13102213
Submission received: 6 April 2020 / Revised: 2 May 2020 / Accepted: 8 May 2020 / Published: 12 May 2020
Browse Figures
Versions Notes

Abstract

:
This study presents a new ultra-high temperature composite fabricated by using zirconium diboride (ZrB2), silicon carbide (SiC), and tantalum carbide (TaC) with the volume ratios of 70%, 20%, and 10%, respectively. To attain this novel composite, an advanced processing technique of spark plasma sintering (SPS) was applied to produce ZrB2–SiC–TaC. The SPS manufacturing process was achieved under pressure of 30 MPa, at 2000 °C for 5 min. The micro/nanostructure and mechanical characteristics of the composite were clarified using X-ray diffraction (XRD), field-emission scanning electron microscopy (FESEM), and nano-indentation. For further investigations of the product and its characteristics, X-ray fluorescence (XRF) analysis and X-ray photoelectron spectroscopy (XPS) were undertaken, and the main constituting components were provided. The composite was densified to obtain a fully-dense ternary; the oxide pollutions were wiped out. The mean values of 23,356; 403.5 GPa; and 3100 °C were obtained for the rigidity, elastic modulus, and thermal resistance of the ZrB2–SiC–TaC interface, respectively. To explore the practical application of the composite, the natural frequency of an aircraft wing considering three cases of materials: (i) with a leading edge made of ZrB2–SiC–TaC; (ii) the whole wing made of ZrB2–SiC–TaC; and (iii) the whole wing made of aluminum 2024-T3 were investigated employing a numerical finite element model (FEM) tool ABAQUS and compared with that of a wing of traditional materials. The precision of the method was verified by performing static analysis to obtain the responses of the wing including total deformation, equivalent stress, and strain. A comparison study of the results of this study and published literature clarified the validity of the FEM analysis of the current research. The composite produced in this study significantly can improve the vibrational responses and structural behavior of the aircraft’s wings.

1. Introduction

Ultra-high temperature ceramics (UHTCs) are refractory materials presenting outstanding mechanical properties at elevated temperatures beyond 2000 °C [1,2,3]. They have been used for possible thermal protection systems, coating of objects exposed to high temperatures, and biomedical applications [4,5,6,7]. A few natural elements exist having ultra-high melting points over 3000 °C such as carbon, rhenium, osmium, tungsten, and tantalum [8,9,10]. Also, limited chemical compounds having high-temperature resistance have been achieved and utilized for various applications, e.g., thorium dioxide (ThO2), tantalum diboride (TaB2), zirconium diboride (ZrB2), tantalum carbide (TaC), hafnium carbide (HfC), zirconium carbide (ZrC), titanium carbide (TiC), etc. [11,12,13,14].
The huge demand for high-temperature resistant materials for industries, especially aerospace, has motivated the Air Force Materials Laboratory to develop a new class of materials tolerating the harsh environment of proposed hypersonic vehicles such as Dyna-soar and the Space Shuttle at Man Labs Incorporated [15]. Assessment of the refractory properties of binary ceramics showed that the metal borides, carbides, and nitrides possessed the significant thermal conductivity and oxidation resistance as well as appropriate mechanical strength in the case of using small grain size. Among the aforementioned materials, ZrB2 and HfB2 in composites comprising ~20% volume SiC have presented the most efficient and practical applications. A significant number of research studies reported in the literature dealt with improving the performance of ZrB2 and HfB2 despite having numerous works that have been undertaken to characterize the nitrides, oxides, carbides, etc. [16,17,18,19,20]. There are several documented studies presenting the diborides utilization for high thermal conductivity and low melting points. These unique properties of such ceramics provide significant thermal resistance making them ideal candidates for elevated-thermal applications [21,22,23]. Among the UHTCs, the Zr-based diborides have been developed with the aim of tolerating ambient loads and elevated temperatures which can be experienced by leading vehicle edges in sustained hypersonic flight [24,25]. The surfaces of aircraft vehicles are exposed to drastically elevated temperatures and high flow-rate oxidation. It has been documented that ZrB2-based UHTCs can retain shape under high-temperature surroundings because of their significant oxidation resistance and high melting point [26,27,28].
ZrB2 has been considered one of the most promising thermal protection materials and employed for a wide range of structural and industrial applications [29,30,31]. From the results given in the literature, it has been figured out that ZrB2-based UHTCs possess an outstanding oxidation resistance, rigidity, and fracture toughness. It was observed that the oxidation resistance of ZrB2–SiC composite was supreme in the air up to 1500 °C boosting the strength by healing the surface flaws [32,33]. The significant oxidation resistance of ZrB2–SiC beyond 1800 °C has been also reported presenting outstanding integrity of the underlying microstructure under specific situations [34,35]. Furthermore, huge efforts have been assigned to the assessment of high-temperature mechanical properties of ZrB2-based ceramics, particularly by incorporating various additives. In this regard, several studies have been reported on the investigation of the flexure strength of ZrB2-based ceramics at high temperatures by employing the three-point bending test. The results showed that the flexure strength, stiffness, thermal, and corrosion resistance were relatively decreased with increasing the temperature [36,37,38]. Among various additives included to UHTCs for improving their properties, TaC is unique because of its high melting point (~3880 °C) which is among the highest for binary compounds. Furthermore, TaC has a microhardness of 1600–2000 kg/mm2, and an elastic modulus of 285 GPa.
This study focuses on the production of a new type of UHTCs having superior characteristics to the existing conventional counterparts and newly manufactured ZrB2-based materials [39,40,41,42,43,44,45,46,47,48,49]. Based on the investigations through the characteristics of different additives, this study employed TaC nanopowder to enhance the mechanical properties of ZrB2–SiC for industrial and structural applications. Thereafter, to visualize the practical application of the presented manufactured composite, it was adopted for the aerospace applications. For this aim, the finite element (FE) method which has been frequently used as an outstanding tool for a wide range of applications such as modeling materials, and structural and mechanical components, vibration analysis, buckling analysis, crack propagation, and blast analysis of structures and materials, was taken into account [50,51,52,53,54,55,56,57,58,59,60]. In this regard, the FE package ABAQUS was adopted to evaluate the natural frequencies of an aircraft wing of aluminum 2024-T3 and the leading edge made of the ZrB2–SiC–TaC.

2. Experimental Setup

2.1. The Manufacturing Process of ZrB2–SiC–TaC

To manufacture the ZrB2–SiC–TaC composite, ZrB2, SiC, and TaC were mixed in the form of powder with the volume fractions of 70%, 20%, and 10%, respectively. The purity of ZrB2 was greater than 99.8% with the particle size smaller than 2 μm. SiC had a particle size of <3 μm with a purity of 99.2%, while the TaC powder size was smaller than 100 nm having a purity of 99.5%. The mixing of the starting materials was carried out inside an ultrasonic bath with ethanol lasting for 80 min. The admixture was completely dried using a magnetic hot plate and a stove. When the mixture was thoroughly loaded in the mold, the sintering process was carried out by spark plasma sintering (SPS) subjected to 2000 °C under 30 MPa pressure for 5 min. The obtained pallet with a thickness of 6 mm and a diameter of 2.4 mm was unfolded by grinding using a diamond grinding disk and eliminating its graphite foil cover.

2.2. Analysis and Characterization

To characterize the crystal structure of the prepared composite, a high-resolution X-ray diffractometer (XRD) was performed on a Bruker D8 Advance instrument (Bruker, Billerica, MA, USA). To obtain the mechanical characteristics of the composite the instrumented nano-indentation test was adopted by employing the Berkovich indenter. ZrB2–SiC–TaC was investigated by the Oliver-Pharr method to reveal its mechanical and thermal properties such as modulus of elasticity (E), Poisson’s ratio (ν), rigidity, and fracture toughness, and the load-displacement relationship. For this aim, XRD, and nano-indentation were utilized. Field-emission scanning electron microscopy (FESEM) images were attained using a SUPRA 55VP and Sigma Carl Zeiss (Zeiss, Oberkochen, Germany) instrument equipped with energy-dispersive X-ray spectroscopy (EDS). X-ray photoelectron spectroscopy (XPS) was carried out using an Al Kα source (Sigma probe, VG Scientifics). The field emission-electron probe microanalyzer (FE-EPMA) was acquired using a JXA-8530F, JEOL (Tokyo, Japan). X-ray fluorescence (XRF) spectroscopy was achieved by an XRF-1800, Shimadzu (Kyoto, Japan).

3. Potential Applications and Computational Model

The prominent requirements of mechanical, thermal, and corrosion properties for the materials used for aerospace applications limits the choice of materials to carbides, borides, nitrides of the transition metals, etc. Among the available materials, TaC is unique because of its high melting point over 3000 °C. Moreover, the TaC-based composites provide enhanced mechanical characteristics compared with other UHTCs. The composite of this study, ZrB2–SiC–TaC, can be an appropriate alternative for current commercial materials for long-term aerospace applications. The components of the leading edge and nose cap of aircraft are exposed to temperatures higher than 2000 °C and subjected to complex stresses. The illustration of the possible applications of the materials of this research in aircraft wings is provided in Figure 1a.
Furthermore, the refractory property and high toughness of ZrB2–SiC–TaC enable it to be used for car engines and brakes, nuclear reactors, and coating on wooden structures. It can also be used for electric and electronic devices because ZrB2 acts as an electrical conductor, while SiC functions as an electrical ceramic. Figure 1b illustrates the potential application of this ceramic for the car industry used as an internal coating of the combustion chamber. Due to the high fracture toughness, corrosion, and oxidation resistance of the presented ceramic, it can also be utilized for biomedical applications, e.g., knee joints (Figure 1c). Furthermore, it can be applied for stent fabrication to keep the arteries passageway open. Figure 1d shows the possible biomedical applications for the ZrB2–SiC–TaC in artificial knee replacement and stent used to open clogged arteries.
To examine the practical applications of ZrB2–SiC–TaC, this study adopted the commercially available finite element package ABAQUS to investigate the natural frequencies of the aircraft wing with a leading edge made of the ceramic. The solid elements were adopted for the geometrical modeling of the wing. There are two models in terms of the materials: i) the case that the aluminum 2024-T3 was specified to the global body of the wing while the composite of this study was allocated to the leading-edge; and ii) the wing made totally with aluminum 2024-T3. It is worth noting that in the case of having a wing made of both materials, the volume fraction of the ZrB2–SiC–TaC used for leading-edge is ~18%, and for aluminum used in the rest of the wing is ~72%. The mechanical properties of the materials used for the wing are provided in Table 1.
There are two commonly used elements for meshing 3D models: the brick element and the tetrahedron element. It has been documented that brick elements can show better performance compared with the tetrahedron. However, for the cases of complex geometries, the probability of geometry degradation exists when meshing the model with brick elements. In addition, the number of nodes of brick elements is higher than the number of elements which significantly increases the computational time. Re-meshing of the brick elements is difficult and hence may not be suitable for large deformation problems. Therefore, the tetrahedron element, the 10-node quadratic tetrahedron (C3D10), was adopted for the numerical model of this study. To find the appropriate mesh size, the convergence study was performed and the corresponding graph is illustrated in Figure 2a.
It can be seen from Figure 2a that as the size of elements increases the convergence of the results decreases such that after the size of 3.0, the rate of divergence exponentially increases. In this study, to achieve reliable results, the global size of 0.5 was adopted for the mesh size. The geometry of the wing model in ABAQUS is illustrated in Figure 2b while the open-view of the wing showing the airfoils inside the wing is provided in Figure 2c. The boundary conditions shown on the wing end which are connected to aircraft fuselage is provided in Figure 2d, and the meshed model is given in Figure 2e.

4. Results

4.1. Characterization of ZrB2–SiC–TaC

To provide a better insight into the crystal structure and determine the characteristics of ZrB2–SiC–TaC, several methods were employed, namely nano-indentation, XRD, XRF, FE-EPMA, and FESEM. The XRD pattern of the prepared ceramic is shown in Figure 3.
XPS analysis of the elements existing in ceramic and the composition of ZrB2–SiC–TaC is illustrated in Figure 4.
The graph showing the XRF of the composite of this study is given in Figure 5 while the nano-indentation of ZrB2–SiC–TaC showing the load-displacement relationship of this composite is provided in Figure 6.
Furthermore, the non-destructive analytical technique of XRF was used to determine the elemental composition of ZrB2–SiC–TaC. The characteristics of the ZrB2–SiC–TaC are provided in Table 2.
Table 2 shows that ZrB2–SiC–TaC has very high rigidity, elastic modulus, and thermal resistance. These outstanding properties together with its high thermal and oxidation resistance expands its utilization for industrial and structural applications. Figure 7 shows the FESEM images of ZrB2–SiC–TaC composite.
The EDS elemental map of the composite presenting zirconium, boron, carbon, silicon, and tantalum is provided in Figure 8.
FE-EPMA was employed to explain and illustrate the carboniferous dopant existence in terms of primary graphite as well as recently-created zirconium diboride composite after sintering procedure (Figure 9).

4.2. Computational Results

To evaluate the applicability of the material of this study, we applied it to the leading edge of the aircraft wing and total body of the wing. The aim was to investigate the natural frequency of the wing by employing the finite element model (FEM) method through ABAQUS.

4.2.1. Method Validity

To evaluate the validity of the computational method of this study, the results given in the literature [50] dealing with the analysis of an aircraft wing was adopted to be compared with the current study. The example problem given in the aforementioned reference was modeled in this study. The Aluminum 2024-T3 was considered for the material of the wing and static analysis was performed to obtain the total deformation, equivalent stress, and equivalent strain. For the static analysis, the pressure force of 500 Pa was applied to the bottom surface of the wing at the center of the pressure. One end of the wing was completely constrained for all the degrees of freedom as it is embedded inside the fuselage while the other end was left free with six degrees of freedom. Thereafter, the results were compared with those of literature as provided in Table 3.
The last row of Table 3 shows the variation of the results of the current study and literature. The small amount of variation shows that the numerical model of this study could provide an acceptable prediction of the results and was in good agreement with literature. Therefore, the validity of the FEM analysis of the current study employing ABAQUS was approved. It can be adopted for further analysis to evaluate the natural frequencies of the aircraft wing considering the material produced in this study, ZrB2–SiC–TaC.

4.2.2. The Natural Frequency of the Wing

The illustrations of the first two modes of natural frequencies of wings are provided in Figure 10 for three cases: (i) ZrB2–SiC–TaC as the leading edge and aluminum for the rest of the wing-body, (ii) ZrB2–SiC–TaC used for all the body of wing, and (iii) aluminum used for the wing. As can be seen from Figure 10, the maximum displacement was observed at the free end of the wing. Similar mode shapes were obtained for the wings made of pure aluminum and ZrB2–SiC–TaC.

5. Discussions

5.1. Experiments

Performing a set of experimental works resulted in the production of a refractory material called ZrB2–SiC–TaC to provide superior thermal and mechanical properties for potential applications in structural, mechanical, aerospace, and biomedical areas. Thereafter, the composite was characterized by employing nano-indentation, XRD, XRF, and XPS. The densification of the material was completely achieved through the SPS process. Only peaks of zirconium and boron could be obtained allocated to the matrix of ZrB2. The peaks of silicon and carbon could be only detected as SiC additive. Figure 3 provides XRD of the ZrB2–SiC–TaC. Small values of the sedentary shaped ZrB2 phase enhanced the assumption indicating the bounded reaction between TaC and the face contamination of zirconium diboride–silicon carbide. Results revealed that the intensity of the TaC top point in the sintered compound was smaller than the powder admixture. The relative density of ZrB2–SiC–TaC was 98.5% through the SPS process under the temperature of 2000 °C and 30 MPa pressure for 5 min. Despite achieving the theoretical density for the composite of this study, the remaining 1.5% porosity in the as-sintered experimental sample could be attributed to insufficient sintering temperature or the absence of any metallic, carbonaceous, or other types of sintering aids. However, because of the negative effects of employing the sinter additives or higher sintering temperatures on the mechanical performance of sintered parts, a value of 98.5% would be admissible.
The XPS images of the composite and constituent compounds are provided in Figure 4. Having the XPS analysis of the materials, as a very advanced and accurate analysis tool, it was found that the purity of the composite is excellent, and no other compound was produced. Similar results were obtained by XRF analysis (Figure 5). Among the constituent materials, the highest intensity belonged to ZrB2 corresponding to the binding energy of approximately 178 (eV). The lowest intensity attributed to TaC with a magnitude of 2300 which occurred on the binding energy equal to 23 (eV).
It has been documented that there is a possibility of the creation of new compounds as well as the desired main composite during the manufacturing process. For example, Ghassemi Kakroudi and co-workers [38] detected two other compounds including ZrC and TaSi2 during the hot process manufacturing of ZrB2–SiC–TaC. They explained that it could be because of the formation of oxide impurity on the surface of ZrB2 powders as the main component of the mixture. They suggested the chemical reaction formula given in Equation (1) for the verification of this outcome [38]:
2SiC + TaC + ZrO2 → TaSi2 + ZrC + 2CO
However, from the outcomes obtained from XRD, XPS analysis of the current study, no extra in situ formation of new compounds was observed except the main composite of desire. This superior result was achieved due to employing the advanced SPS manufacturing process which is preferable to the other existent manufacturing processes.
Figure 6 shows the load-displacement relation of the material obtained from the nano-indentation technique. As can be seen, the result was achieved through five loading-unloading processes. After each cycle, the amount of displacement increased with respect to the same loading amounts which shows the slight reduction in the rigidity of the material. By using the nano-indentation graphs, the characteristics of the composite of this study were attained. The mechanical and thermal characteristics of the composite and ZrB2–SiC–TaC interface are given in Table 2 shows a substantial reduction in the minimum and mean rigidity and modulus of elasticity of the interface with respect to those of zirconium diboride, silicon carbide, and tantalum carbide phases. It was observed that the existence of residual porosities and oxides could result in a decrease in rigidity and modulus of elasticity at the interface. It was found that SiC dominated in the regarding indent because of the indentation head position. For example, the case can be considered as the principal segment of the projected region positioned within silicon carbide for which the force-displacement relation tended to that of SiC. By contrast, when the indentation was positioned within the ZrB2 phase, the properties of the force-displacement relationship tended to ZrB2. The same pattern was also observed for the TaC for which the material characteristics presented those of TaC when the indentation placed within TaC.
FESEM images of the surface of the composite are shown in Figure 7 comprising grey, dark, and bright areas correspondence to ZrB2, SiC, and TaC grains, respectively. There is a good consistency with the volume ratios of each phase in the powder mixture. Besides, this microstructural result was in good agreement with the relative density value of 98.5% for the sintered bulk. EDS of the composite also confirms the integrity and presence of the constituent elements in the ZrB2–SiC–TaC (Figure 8). The FE-EPMA map also shows the areal information on the properties of the composite and its chemical components provided in Figure 9. These results demonstrated the distribution map of each component and the whole composition of ZrB2–SiC–TaC.

5.2. Finite Element Method

The numerical analysis of the aircraft wing was performed to investigate the effect of the application of ZrB2–SiC–TaC on the natural frequency of the aircraft wing. The first two shape modes of the wings corresponding to different cases from the viewpoint of the material are provided in Figure 10. As can be seen from Figure 10, the free end of the wing sustained the highest displacement. To provide a better understanding of the efficiency of the material of this study, the amounts of natural frequencies corresponding to the first three mode shapes, the most important modes, are provided and compared in Table 4.
According to the results given in Table 4, the natural frequency of the aircraft wing is changed by using ZrB2–SiC–TaC. It was observed that employing the material of this study for the leading edge of the wing increased the natural frequency by over 50%. Moreover, it was seen that having used the presented composite instead of aluminum for the wing resulted in a small increase in natural frequencies. Using the composite of this study significantly enhances the stiffness of the wing as well as its thermal resistance.

6. Conclusions

This presented a new type of ultra-high temperature ceramic, ZrB2–SiC–TaC, having the thermal resistance beyond 3000 °C, and superior mechanical properties. The purpose of the study was to produce new material for structural and aerospace applications. The designed composite was produced by combining zirconium diboride, silicon carbide, and tantalum carbide sintered by spark plasma sintering. This new composite was characterized through the nano-indentation, X-ray diffractometer, X-ray fluorescence spectrometer, field emission-electron probe microanalyzer, and field-emission scanning electron microscopy. This composite possesses a melting point beyond 3000 °C, elastic modulus, and rigidity. Its possible application in aerospace was illustrated. To depict the workability and applicability of the material of this study, the computational method was adopted to model the aircraft wing through finite element model analysis employing ABAQUS. In this regard, three cases were considered from the viewpoint of specifying ZrB2–SiC–TaC in the wing: i) only applied to the leading edge of the wing, ii) considered for the wing as a whole, and iii) only aluminum 2024-T3 applied to the wing without consideration of ZrB2–SiC–TaC. Comparison studies between the results showed that employing ZrB2–SiC–TaC enhances the structural performance of the wing and changes its natural frequency substantially when it is considered as a leading edge of the wing. When ZrB2–SiC–TaC was applied to the wing as a whole, a small variation was observed with the case of wing fully made of aluminum 2024-T3. It can be concluded that the best case is to apply this composite for the leading edge of the wing.

Author Contributions

Conceptualization, B.M.; J.K. and M.S.; methodology, B.M. and M.S.; software, B.M. and J.K.; validation, B.M.; J.K.; Q.V.L.; S.-H.L. and M.S.; formal analysis, B.M. and M.S.; investigation, B.M.; S.J.; T.H.L.; J.H.C.; H.W.J.; and M.S.; resources, B.M.; S.J.; T.H.L.; J.H.C.; H.W.J.; and M.S.; data curation, B.M.; S.J.; T.H.L.; and M.S.; writing—original draft preparation, B.M.; S.J.; T.H.L. and M.S.; writing—review and editing, B.M.; J.K. and M.S.; visualization, B.M.; S.J.; T.H.L. and M.S.; supervision, J.K.; Q.V.L.; S.-H.L.; project administration, S.J.; T.H.L. and M.S.; funding acquisition, J.K.; Q.V.L.; S.-H.L., and M.S. All authors have read and agreed to the published version of the manuscript.

Funding

This work was funded by the grant (19CTAP-C144787-02) of the Ministry of Land, Infrastructure, and Transport (MOLIT) of the Korean Agency for Infrastructure Technology Advancement (KAIA). In addition, the financial supports of Future Material Discovery Program (2016M3D1A1027666), and the Basic Science Research Program (2017R1A2B3009135) through the National Research Foundation of Korea.

Conflicts of Interest

The authors declare no conflict of interest. The funders had no role in the design of the study; in the collection, analyses, or interpretation of data; in the writing of the manuscript, or in the decision to publish the results.

References

  1. Fahrenholtz, W.G.; Hilmas, G.E.; Chamberlain, A.L.; Zimmermann, J.W. Processing and characterization of ZrB2-based ultra-high temperature monolithic and fibrous monolithic ceramics. J. Mater. Sci. 2004, 39, 5951–5957. [Google Scholar] [CrossRef]
  2. Dai, F.; Zhou, Y. Reducing the ideal shear strengths of ZrB2 by high efficient alloying elements (Ag, Au, Pd and Pt). Sci. Rep. 2017, 7, 43416. [Google Scholar] [CrossRef] [PubMed] [Green Version]
  3. Shahedi Asl, M.; Nayebi, B.; Ahmadi, Z.; Parvizi, S.; Shokouhimehr, M. A novel ZrB2–VB2–ZrC composite fabricated by reactive spark plasma sintering. Mater. Sci. Eng. A 2018, 731, 131–139. [Google Scholar] [CrossRef]
  4. Feng, X.; Wang, X.; Liu, Y.; Guo, Y.; Zhang, M.; Zhang, L.; Jian, X.; Yin, L.; Xie, J.; Deng., L. Oxidation behaviour of plasma-sprayed ZrB2-SiC coatings. Ceram. Int. 2019, 45, 2385–2392. [Google Scholar] [CrossRef]
  5. Zoli, L.; Vinci, A.; Galizia, P.; Melandri, C.; Sciti, D. On the thermal shock resistance and mechanical properties of novel unidirectional UHTCMCs for extreme environments. Sci. Rep. 2018, 8, 9148. [Google Scholar] [CrossRef] [PubMed]
  6. Oliveros, A.; Coletti, C.; Saddow, S.E. Carbon based materials on SiC for advanced biomedical applications. In Silicon Carbide Biotechnology; Elsevier: Waltham, MA, USA, 2012; Volume 12, pp. 431–458. [Google Scholar] [CrossRef]
  7. Guo, S.Q. Densification of ZrB2-based composites and their mechanical and physical properties: A review. J. Eur. Ceram. Soc. 2009, 29, 995–1011. [Google Scholar] [CrossRef]
  8. Wuchina, E.; Opila, E.; Opeka, M.; Fahrenholtz, W.; Talmy, I. UHTCs: Ultra-high temperature ceramic materials for extreme environment applications. Electrochem. Soc. Interface 2007, 16, 30. [Google Scholar]
  9. Cedillos-Barraza, O.; Manara, D.; Boboridis, K.; Watkins, T.; Grasso, S.; Jayaseelan, D.D.; Konings, R.J.; Reece, M.J.; Lee, W.E. Investigating the highest melting temperature materials. A laser melting study of the TaC-HfC system. Sci. Rep. 2016, 6, 37962. [Google Scholar] [CrossRef] [Green Version]
  10. Silvestroni, L.; Kleebe, H.; Fahrenholtz, W.; Watts, J. Super-strong materials for temperatures exceeding 2000 °C. Sci. Rep. 2017, 7, 40730. [Google Scholar] [CrossRef]
  11. Zhang, G.J.; Guo, W.M.; Ni, D.W.; Kan, Y.M. Ultrahigh temperature ceramics (UHTCs) based on ZrB2 and HfB2 systems: Powder synthesis, densification and mechanical properties. J. Phys. Conf. Ser. 2009, 176, 012041. [Google Scholar] [CrossRef]
  12. Nisbet, H.; Migdisov, A.A.; Williams-Jones, A.E.; Xu, H.; van Hinsberg, V.J.; Roback, R. Challenging the thorium-immobility paradigm. Sci. Rep. 2019, 9, 17035. [Google Scholar] [CrossRef] [PubMed]
  13. Jiang, M.; Zheng, J.W.; Xiao, H.Y.; Liu, Z.J.; Zu, X.T. A comparative study of the mechanical and thermal properties of defective ZrC, TiC and SiC. Sci. Rep. 2017, 7, 9344. [Google Scholar] [CrossRef] [PubMed] [Green Version]
  14. Smith, C.J.; Ross, M.A.; Leon, N.D.; Weinberger, C.R.; Thompson, G.B. Ultra-high temperature deformation in TaC and HfC. J. Eur. Ceram. 2018, 38, 5319–5332. [Google Scholar] [CrossRef]
  15. Lawson, J.W.; Murray, S.D.; Charles, W. Bauschlicher. Lattice thermal conductivity of ultra high temperature ceramics ZrB2 and HfB2 from atomistic simulations. J. Appl. Phys. 2011, 110, 083507. [Google Scholar] [CrossRef] [Green Version]
  16. Ma, H.B.; Man, Z.Y.; Liu, J.X.; Xu, F.F.; Zhang, G.J. Microstructures, solid solution formation and high-temperature mechanical properties of ZrB2 ceramics doped with 5 vol.% WC. Mater. Des. 2015, 81, 133–140. [Google Scholar] [CrossRef]
  17. Guo, W.M.; Zhang, G.J. Reaction processes and characterization of ZrB2 powder prepared by boro/carbothermal reduction of ZrO2 in vacuum. J. Am. Ceram. Soc. 2009, 92, 264–267. [Google Scholar] [CrossRef]
  18. Hu, P.; Wang, Z. Flexural strength and fracture behavior of ZrB2–SiC ultra-high temperature ceramic composites at 1800 °C. J. Eur. Ceram. Soc. 2010, 30, 1021–1026. [Google Scholar] [CrossRef]
  19. Shen, Y.; Jiang, J.C.; Zeman, P.; Šímová, V.; Vlček, J.; Meletis, E.I. Microstructure evolution in amorphous Hf-B-Si-C-N high temperature resistant coatings after annealing to 1500 °C in air. Sci. Rep. 2019, 9, 3603. [Google Scholar] [CrossRef] [Green Version]
  20. Šímová, V.; Vlček, J.; Zuzjaková, Š.; Houška, J.; Shen, Y.; Jiang, J.; Meletis, E.I.; Peřina, V. Magnetron sputtered Hf–B–Si–C–N films with controlled electrical conductivity and optical transparency, and with ultrahigh oxidation resistance. Thin Solid Film. 2018, 653, 333–340. [Google Scholar] [CrossRef]
  21. Gild, J.; Zhang, Y.; Harrington, T.; Jiang, S.; Hu, T.; Quinn, M.C.; Mellor, W.M.; Zhou, N.; Vecchio, K.; Luo, J. High-entropy metal diborides: A new class of high-entropy materials and a new type of ultrahigh temperature ceramics. Sci. Rep. 2016, 6, 37946. [Google Scholar] [CrossRef]
  22. Wu, P.; Lv, H.; Peng, T.; He, D.; Mu, S. Nano conductive ceramic wedged graphene composites as highly efficient metal supports for oxygen reduction. Sci. Rep. 2015, 4, 3968. [Google Scholar] [CrossRef] [PubMed] [Green Version]
  23. Zapata-Solvas, E.; Jayaseelan, D.D.; Lin, H.T.; Brown, P.; Lee, W.E. Mechanical properties of ZrB2- and HfB2-based ultra-high temperature ceramics fabricated by spark plasma sintering. J. Eur. Ceram. 2013, 33, 1373–1386. [Google Scholar] [CrossRef]
  24. Tan, W.; Petorak, C.A.; Trice, R.W. Rare-earth modified zirconium diboride high emissivity coatings for hypersonic applications. J. Eur. Ceram. Soc. 2014, 34, 1–11. [Google Scholar] [CrossRef]
  25. Neuman, E.W.; Hilmas, G.E.; Fahrenholtz, W.G. Mechanical behavior of zirconium diboride–silicon carbide ceramics at elevated temperature in air. J. Eur. Ceram. Soc. 2013, 33, 2889–2899. [Google Scholar] [CrossRef]
  26. Neuman, E.W.; Hilmas, G.E.; Fahrenholtz, W.G. Mechanical behavior of zirconium diboride–silicon carbide–boron carbide ceramics up to 2200 °C. J. Eur. Ceram. Soc. 2015, 35, 463–476. [Google Scholar] [CrossRef]
  27. D’Angio, A.; Zou, J.; Binner, J.; Ma, H.B.; Hilmas, G.E.; Fahrenholtz, W.G. Mechanical properties and grain orientation evolution of zirconium diboride-zirconium carbide ceramics. J. Eur. Ceram. Soc. 2018, 38, 391–402. [Google Scholar] [CrossRef] [Green Version]
  28. Silvestroni, L.; Mungiguerra, S.; Sciti, D.; Martino, G.D.D.; Savino, R. Effect of hypersonic flow chemical composition on the oxidation behavior of a super-strong UHTC. Corros. Sci. 2019, 159, 108125. [Google Scholar] [CrossRef]
  29. Shahedi Asl, M.; Nayebi, B.; Ahmadi, Z.; Jaberi Zamharir, M.; Shokouhimehr, M. Effects of carbon additives on the properties of ZrB2–based composites: A review. Ceram. Int. 2018, 44, 7334–7348. [Google Scholar] [CrossRef]
  30. An, Y.; Han, W.; Han, J.; Zhao, G.; Zhou, S.; Zhang, X. Synergistic effect on the mechanical behaviors of ternary graphene oxide-zirconium diboride-poly(vinyl alcohol) papers. Mater. Des. 2016, 112, 275–281. [Google Scholar] [CrossRef]
  31. Sonber, J.K.; Raju, K.; Murthy, T.C.R.C.; Sairam, K.; Nagaraj, A.; Majumdar, S.; Kain, V. Friction and wear properties of zirconium diboride in sliding against WC ball. Int. J. Refract. Met. Hard Mater. 2018, 76, 41–48. [Google Scholar] [CrossRef]
  32. Shahedi Asl, M.; Nayebi, B.; Shokouhimehr, M. TEM characterization of spark plasma sintered ZrB2–SiC–graphene nanocomposite. Ceram. Int. 2018, 44, 15269–15273. [Google Scholar] [CrossRef]
  33. Nayebi, B.; Ahmadi, Z.; Shahedi Asl, M.; Parvizi, S.; Shokouhimehr, M. Influence of vanadium content on the characteristics of spark plasma sintered ZrB2–SiC–V composites. J. Alloys Compd. 2019, 805, 725–732. [Google Scholar] [CrossRef]
  34. Chakraborty, S.; Das, P.K.; Ghosh, D. Spark plasma sintering and structural properties of Zrb2 based ceramics: A review. Rev. Adv. Mater. Sci. 2016, 44, 182–193. [Google Scholar]
  35. Zhang, X.; An, Y.; Han, J.; Han, W.; Zhao, G.; Jin, X. Graphene nanosheet reinforced ZrB2–SiC ceramic composite by thermal reduction of graphene oxide. RSC Adv. 2016, 5, 47060–47065. [Google Scholar] [CrossRef]
  36. Thimmappa, S.K.; Golla, B.R.; Prasad, V.V.B.; Majumdar, B.; Basu, B. Phase stability, hardness and oxidation behavior of spark plasma sintered ZrB2-SiC-Si3N4 composites. Ceram. Int. 2019, 45, 9061–9073. [Google Scholar] [CrossRef]
  37. Sha, J.J.; Li, J.; Lv, Z.Z.; Wang, S.H.; Zhang, Z.F.; Zu, Y.F.; Flauder, S.; Krenkel, W. ZrB2-based composites toughened by as-received and heat-treated short carbon fibers. J. Eur. Ceram. Soc. 2017, 37, 549–558. [Google Scholar] [CrossRef]
  38. Ghassemi Kakroudi, M.; Dehghanzadeh Alvari, M.; Shahedi Asl, M.; Pourmohammadie Vafa, N.; Rabizadeh, T. Hot pressing and oxidation behavior of ZrB2–SiC–TaC composites. Ceram. Int. 2020, 46, 3725–3730. [Google Scholar] [CrossRef]
  39. Sharifianjazi, F.; Pakseresht, A.H.; Shahedi Asl, M.; Esmaeilkhanian, A.; Nargesi Khoramabadi, H.; Jang, H.W.; Shokouhimehr, M. Hydroxyapatite consolidated by zirconia: Applications for dental implant. J. Compos. Compd. 2020, 2, 26–34. [Google Scholar] [CrossRef] [Green Version]
  40. Rafiaei, S.M.; Bahrami, A.; Shokouhimehr, M. Influence of Ni/Co binders and Mo2C on the microstructure evolution and mechanical properties of (Ti0.93W0.07)C-based Cermets. Ceram. Int. 2018, 44, 17655–17659. [Google Scholar] [CrossRef]
  41. Maleki, M.; Beitollahi, A.; Shokouhimehr, M. Template-free synthesis of porous boron nitride using a single source precursor. RSC Adv. 2015, 5, 6528–6535. [Google Scholar] [CrossRef] [Green Version]
  42. Vajdi, M.; Sadegh Moghanlou, F.; Sharifianjazi, F.; Shahedi Asl, M.; Shokouhimehr, M. A review on the COMSOL Multiphysics studies of heat transfer in advanced ceramics. J. Compos. Compd. 2020, 2, 35–44. [Google Scholar] [CrossRef]
  43. Ahmadi, Z.; Nayebi, B.; Parvizi, S.; Shahedi Asl, M.; Shokouhimehr, M. Phase transformation in spark plasma sintered ZrB2–V–C composites at different temperatures. Ceram. Int. 2020, 46, 9415–9420. [Google Scholar] [CrossRef]
  44. Shokouhimehr, M.; Mahmoudi Gom-Yek, S.; Nasrollahzadeh, M.; Kim, A.; Varma, R.S. Palladium nanocatalysts on hydroxyapatite: Green oxidation of alcohols and reduction of nitroarenes in water. Appl. Sci. 2019, 9, 4183. [Google Scholar] [CrossRef] [Green Version]
  45. Vajdi, M.; Sadegh Moghanlou, F.; Ranjbarpour Niari, E.; Shahedi Asl, M.; Shokouhimehr, M. Heat transfer and pressure drop in a ZrB2 microchannel heat sink: A numerical approach. Ceram. Int. 2020, 46, 1730–1735. [Google Scholar] [CrossRef]
  46. Shahedi Asl, M.; Nayebi, B.; Ghassemi Kakroudi, M.; Shokouhimehr, M. Investigation of hot pressed ZrB2–SiC–carbon black composite by scanning and transmission electron microscopy. Ceram. Int. 2019, 45, 16759–16764. [Google Scholar] [CrossRef]
  47. Ramezanalizadeh, H.; Emamy, M.; Shokouhimehr, M. Wear behavior of Al/CMA-type Al3Mg2 Nanocomposites fabricated by mechanical milling and hot extrusion. Tribol. Trans. 2016, 59, 219–228. [Google Scholar] [CrossRef]
  48. Nayebi, B.; Shahedi Asl, M.; Ghassemi Karoudi, M.; Shokouhimehr, M. Temperature dependence of microstructure evolution during hot pressing of ZrB2–30 vol% SiC composites. Ceram. Int. 2016, 54, 7–13. [Google Scholar] [CrossRef]
  49. Nayebi, B.; Shahedi Asl, M.; Ghassemi Kakroudi, M.; Farahbakhsh, I.; Shokouhimehr, M. Interfacial phenomena and formation of nano-particles in porous ZrB2–40 vol% B4C UHTC. Ceram. Int. 2016, 42, 17009–17015. [Google Scholar] [CrossRef]
  50. Das, S.K.; Roy, S. Finite element analysis of aircraft wing using carbon fiber reinforced polymer and glass fiber reinforced polymer. IOP Conf. Ser. Mater. Sci. Eng. 2018, 402, 012077. [Google Scholar] [CrossRef]
  51. Mohammadzadeh, B.; Choi, E.; Kim, D. Vibration of sandwich plates considering elastic foundation, temperature change and FGM faces. Struct. Eng. Mech. 2019, 70, 601–621. [Google Scholar] [CrossRef]
  52. Mohammadzadeh, B.; Noh, H.C. Analytical method to investigate nonlinear dynamic responses of sandwich plates with FGM faces resting on elastic foundation considering blast loads. Compos. Struct. 2017, 174, 142–157. [Google Scholar] [CrossRef]
  53. Mohammadzadeh, B.; Noh, H.C. Numerical analysis of dynamic responses of the plate subjected to impulsive loads. Int. J. Civ. Environ. Struct. Constr. Archit. Eng. 2015, 9, 1148–1151. [Google Scholar]
  54. Mohammadzadeh, B.; Noh, H.C. An analytical and numerical investigations on the dynamic responses of steel plates considering the blast loads. Int. J. Steel Struct. 2018, 19, 603–617. [Google Scholar] [CrossRef]
  55. Mohammadzadeh, B.; Noh, H.C. Investigation into central-difference and Newmark’s beta method in measuring dynamic responses. Adv. Mater. Res. 2014, 831, 95–99. [Google Scholar] [CrossRef]
  56. Mohammadzadeh, B.; Bina, M.; Hasounizadeh, H. Application and comparison of mathematical and physical models on inspecting slab of stilling basin floor under static and dynamic forces. Appl. Mech. Mater. 2012, 147, 283–287. [Google Scholar] [CrossRef]
  57. Mohammadzadeh, B.; Noh, H.C. Investigation into buckling coefficients of plates with holes considering variation of hole size and plate thickness. Mechanika 2016, 22, 167–175. [Google Scholar] [CrossRef] [Green Version]
  58. Mohammadzadeh, B.; Noh, H.C. Use of buckling coefficient in predicting buckling load of plates with and without holes. J. Korean Soc. Adv. Compos. Struct. 2014, 5, 1–7. [Google Scholar] [CrossRef]
  59. Mohammadzadeh, B.; Choi, E.; Kim, W.J. Comprehensive investigation of buckling behavior of plates considering effects of holes. Struct. Eng. Mech. 2018, 68, 261–275. [Google Scholar] [CrossRef]
  60. Whally, R.; Ebrahimi, M. Vibration and control of aircraft wings. Proc. Inst. Mech. Eng. Part G J. Aerosp. Eng. 1998, 212, 353–365. [Google Scholar] [CrossRef]
Materials 13 02213 g001 550
Figure 1. Potential applications of ZrB2–SiC–TaC for (a) aerospace, (b) combustion cylinder of the car engine, (c) artificial knee joint, and (d) stent.
Figure 1. Potential applications of ZrB2–SiC–TaC for (a) aerospace, (b) combustion cylinder of the car engine, (c) artificial knee joint, and (d) stent.
Materials 13 02213 g001
Materials 13 02213 g002 550
Figure 2. The mesh size evaluation and model of the aircraft wing in ABAQUS: (a) convergence study evaluating the appropriate mesh size for the wing, (b) wing dimensions, (c) internal view of wing showing the inside construction, and (d) clamped boundary conditions applied on the wing end, (e) meshed model.
Figure 2. The mesh size evaluation and model of the aircraft wing in ABAQUS: (a) convergence study evaluating the appropriate mesh size for the wing, (b) wing dimensions, (c) internal view of wing showing the inside construction, and (d) clamped boundary conditions applied on the wing end, (e) meshed model.
Materials 13 02213 g002
Materials 13 02213 g003 550
Figure 3. X-ray diffraction (XRD) pattern of ZrB2–SiC–TaC.
Figure 3. X-ray diffraction (XRD) pattern of ZrB2–SiC–TaC.
Materials 13 02213 g003
Materials 13 02213 g004 550
Figure 4. X-ray photoelectron spectroscopy (XPS) of ZrB2–SiC–TaC and its constituent compounds.
Figure 4. X-ray photoelectron spectroscopy (XPS) of ZrB2–SiC–TaC and its constituent compounds.
Materials 13 02213 g004
Materials 13 02213 g005 550
Figure 5. X-ray fluorescence (XRF) spectroscopy of ZrB2–SiC–TaC.
Figure 5. X-ray fluorescence (XRF) spectroscopy of ZrB2–SiC–TaC.
Materials 13 02213 g005
Materials 13 02213 g006 550
Figure 6. Nano-indentation of ZrB2–SiC–TaC.
Figure 6. Nano-indentation of ZrB2–SiC–TaC.
Materials 13 02213 g006
Materials 13 02213 g007 550
Figure 7. Different magnification of field-emission scanning electron microscopy (FESEM, left), and corresponding secondary electron detector (right) images of ZrB2–SiC–TaC.
Figure 7. Different magnification of field-emission scanning electron microscopy (FESEM, left), and corresponding secondary electron detector (right) images of ZrB2–SiC–TaC.
Materials 13 02213 g007
Materials 13 02213 g008 550
Figure 8. Energy-dispersive X-ray spectroscopy (EDS) map of ZrB2–SiC–TaC.
Figure 8. Energy-dispersive X-ray spectroscopy (EDS) map of ZrB2–SiC–TaC.
Materials 13 02213 g008
Materials 13 02213 g009 550
Figure 9. Field-emission-electron probe microanalysis (FE-EPMA) of ZrB2–SiC–TaC and its constituent compounds.
Figure 9. Field-emission-electron probe microanalysis (FE-EPMA) of ZrB2–SiC–TaC and its constituent compounds.
Materials 13 02213 g009
Materials 13 02213 g010 550
Figure 10. First two modes of wing natural frequency of (a) ZrB2–SiC–TaC for the leading edge (model I), (b) ZrB2–SiC–TaC for the leading edge (model II), (c) ZrB2–SiC–TaC for the body of the wing (model I), (d) ZrB2–SiC–TaC for the body of wing (model II), (e) aluminum for the body of wing (model I), and (f) aluminum for the body of wing (model II).
Figure 10. First two modes of wing natural frequency of (a) ZrB2–SiC–TaC for the leading edge (model I), (b) ZrB2–SiC–TaC for the leading edge (model II), (c) ZrB2–SiC–TaC for the body of the wing (model I), (d) ZrB2–SiC–TaC for the body of wing (model II), (e) aluminum for the body of wing (model I), and (f) aluminum for the body of wing (model II).
Materials 13 02213 g010
Table
Table 1. Rigidity and elastic modulus of each phase.
Table 1. Rigidity and elastic modulus of each phase.
Mechanical PropertyMaterialValue
Elastic modulus (GPa)ZrB2–SiC–TaC403.5
Aluminum 2024-T373.1
Poisson’s ratioZrB2–SiC–TaC0.29
Aluminum 2024-T30.33
Density (kg/m3)ZrB2–SiC–TaC3000
Aluminum 2024-T32780
Table
Table 2. Mechanical and thermal properties of the material interface.
Table 2. Mechanical and thermal properties of the material interface.
Mechanical PropertyPhaseMinMaxMean
Rigidity (GPa)ZrB2–SiC–TaC Interface162182612523356
Elastic modulus (GPa)ZrB2–SiC–TaC Interface359.4460.1403.5
Thermal resistance (°C)ZrB2–SiC–TaC Interface300032003100
Table
Table 3. Comparison between the results of static analysis of aircraft wing obtained from the current study and literature [50].
Table 3. Comparison between the results of static analysis of aircraft wing obtained from the current study and literature [50].
EntryTotal Deformation (mm)Equivalent Stress (MPa)Equivalent Strain
Reference [50]6.737716.0340.00023
Current6.889316.4880.00075
Variation%2.252.752.26
Table
Table 4. First three modes corresponding to the aircraft wing natural frequencies.
Table 4. First three modes corresponding to the aircraft wing natural frequencies.
MaterialMode I (Cycle/Time)Mode II (Cycle/Time)Mode III (Cycle/Time)
ZrB2–SiC–Tac2.67 × 10−3 1.13 × 10−21.14 × 10−2
Al2.56 × 10−39.91 × 10−31.08 × 10−2
ZrB2–SiC–Tac + Al5.79 × 10−32.24 × 10−22.44 × 10−2
Variation% (Al/Zr)4.1212.305.26
Variation% (Al/Zr–Al)55.7955.7655.74

Share and Cite

MDPI and ACS Style

Mohammadzadeh, B.; Jung, S.; Lee, T.H.; Le, Q.V.; Cha, J.H.; Jang, H.W.; Lee, S.-H.; Kang, J.; Shokouhimehr, M. Manufacturing ZrB2–SiC–TaC Composite: Potential Application for Aircraft Wing Assessed by Frequency Analysis through Finite Element Model. Materials 2020, 13, 2213. https://doi.org/10.3390/ma13102213

AMA Style

Mohammadzadeh B, Jung S, Lee TH, Le QV, Cha JH, Jang HW, Lee S-H, Kang J, Shokouhimehr M. Manufacturing ZrB2–SiC–TaC Composite: Potential Application for Aircraft Wing Assessed by Frequency Analysis through Finite Element Model. Materials. 2020; 13(10):2213. https://doi.org/10.3390/ma13102213

Chicago/Turabian Style

Mohammadzadeh, Behzad, Sunghoon Jung, Tae Hyung Lee, Quyet Van Le, Joo Hwan Cha, Ho Won Jang, Sea-Hoon Lee, Junsuk Kang, and Mohammadreza Shokouhimehr. 2020. "Manufacturing ZrB2–SiC–TaC Composite: Potential Application for Aircraft Wing Assessed by Frequency Analysis through Finite Element Model" Materials 13, no. 10: 2213. https://doi.org/10.3390/ma13102213

Note that from the first issue of 2016, this journal uses article numbers instead of page numbers. See further details here.

Article Metrics

Back to TopTop