Effect of Multiwalled Carbon Nanotubes on Improvement of Fracture Toughness of Spark-Plasma-Sintered Yttria-Stabilized Zirconia Nanocomposites

Abstract

Highly dense yttria-stabilized zirconia (YSZ) nano-ceramics reinforced with TC-CVD-synthesized multiwall carbon nanotubes (MWCNTs) were fabricated using spark plasma sintering at a temperature of 1350°C, the heating rate of 100 °C/min and pressure of 50MPa with a dwell time of 10 minutes. The identical parameters were utilized for fabricating composites with a varying weight ratio of YSZ and MWNCTs. The samples were characterized for their phase transformation, microstructure and elemental composition using x-ray diffraction (XRD), scanning electron microscopy (SEM) and energy-dispersive spectroscopy (EDS). The physical and mechanical properties such as density, porosity, hardness, fracture toughness and wear were also investigated. The increase in the MWCNTs concentration has resulted in the deterioration of the hardness due to CNT agglomerations. The wear resistance of the composites revealed MWNCTs enhanced wear resistance of YSZ nanocomposite by undergoing MWNCTs pull-out and crack branching mechanisms. Further indentation method and single-beam V-notch beam (SEVNB) methods were utilized to study the effect of MWCNTs on the fracture toughness of the nanocomposites. The fracture toughness of YC1 (6.58 ± 0.3 MPa m1/2) was 21% higher than the YSZ (5.21 ± 0.2 MPa m1/2) due to the toughening mechanisms attributable to crack deflection, branching and bridging of MWCNTs.

Introduction

Over the decades, ageing has been a common issue for the human being who involves degenerative issues of human joints, musculoskeletal diseases and dental problems. Along with these issues, the increase in traffic accidents has also increased the need for artificial implants that can be used by humans for a lifetime without any maintenance or failure. Researchers have been trying to find a permanent solution using biomaterials with properties compatible with medical research. Since the 1960s, Ti-based alloys have been acting as a prominent biomaterial in orthopaedics such as artificial joints and dental plants due to their higher strength, good corrosion resistance and higher biocompatibility (Ref 1). However, the Ti-based alloys undergo excessive wear which could result in loosening in the implants and have harmful side effects on the human body which include tissue blacking and metallosis. The ions and particles of Titanium alloys are deposited in different parts of tissues leading to toxic reactions that could result in yellow nail syndrome. Furthermore, hypersensitivity reactions can lead to implant failure and allergic reactions (Ref 2). Recently, advanced ceramics and their composites have expanded their applications in various fields such as biomedical, structural and aerospace industries. Among advanced ceramics, YSZ (yttria-stabilized zirconia) has been a keen interest to researchers in the field of biomedical applications such as dental implants, femoral ball head, prosthetic heart valves and ligaments owing to its excellent properties like high fracture toughness, biocompatibility, high wear resistance and low plaque affinity (Ref 3,4,5,6). Being a well-studied ceramic, the excellent properties of YSZ have led its path into thermal/environmental barrier coatings in aerospace industries and composites in biomedical and structural areas (Ref 7,8,9,10). The YSZ-based biomaterials could have a predominant advantage over the Ti alloys as the material does not pose issues of corrosion or leaching and does not cause the metal allergic patients (Ref 11). However, ageing poses vulnerability toward the reduction in fracture toughness and complete failure of YSZ composites implants in humid environments (Ref 12, 13). Many researchers have investigated the ageing resistance of YSZ by modifying process conditions, confining phase and microstructural transformations and by grain size controlling (Ref 14, 15). To circumvent this problem, materials like SiC and Al2O3 were added as composites and a material like Y2O3 was coated but these changes resulted in a minimal increase in fracture toughness (Ref 16, 17). A high ductile material like CNTs which has been the core of research from its discovery by Iijima owing to its excellent mechanical, thermo-chemical stability and biocompatibility could act as reinforcement for YSZ for biomedical (Ref 18,19,20). The CNT has been used as a strengthening aid in composites and coating along with material to improve their properties. Mehdi et al. studied the effect of 10 vol.% CNT onto the ZrB2 and concluded that the CNT was responsible for improved fracture toughness of the composites (Ref 21). Likewise, Chen et al. also noted an improvement in tensile and fracture toughness on spark-plasma-sintered TiB2/CNT composites where the presence of additional CNTs could have led to toughening mechanisms such as crack deflection and bridging (Ref 22). Whereas Oleksii et al. investigated the hot-pressed composites of TiB2/CNT and concluded that the fracture toughness was not improved whereas the hardness of the samples reduced drastically (Ref 23). The addition of CNT into TiN composites fabricated using spark plasma sintering led to reduced density in the composites with finer microstructure (Ref 24). In most cases, the use of MWCNTs has resulted in the control of composite grain coarsening by binding the grains together leading to increased mechanical properties. However, many researchers stated that the addition of CNT to YSZ could result in a decrease or minimal increase in fracture toughness depending on the percentage of CNT employed. Duszov et al. and Sun et al. reported that the reinforcing CNT with YSZ did not lead to an increase in fracture toughness whereas Garmendia et al, Mazaheri et al, Kasperski et al and Melk et al reported a slight increase in fracture toughness (Ref 25,26,27,28,29). The contradiction in the results may have been due to (i) Increased MWCNTs content may reduce the interfacial bonding between composites resulting in high porosity (ii) Improper sintering methods/temperature/pressure could damage the material causing non-homogenization, agglomeration and impaired/degraded CNT with YSZ (iii) Improper testing methods like indentation fracture toughness cause inconsistency in toughness values (iv) Unsuitable ultrasonication medium and/or pre-treatment may cause inhomogeneous dispersion and impurity of CNT. Therefore, the need for further research to focus on a comprehensive investigation into the effects of MWCNTs on YSZ and resolve the above-mentioned inadequacies. In recent times, spark plasma sintering (SPS) is used for composite preparations due to the rapid sintering process, high densification and minimal material damage, etc (Ref 30,31,32,33).

Altogether, the reinforcement of CNT with different material led to increase or decrease in mechanical properties as investigated in numerous studies, but there is no systematic study on the precise quantity of MWCNTs which could simulate the mechanical properties of the material. Also, several controversial fracture toughness values have reported earlier due to various parameter as mentioned above. Therefore, the purpose of this work is to comprehensive study of MWCNT-reinforced YSZ composite prepared by spark plasma sintering method and accomplishes the contentious fracture toughness values.

Materials and Methods

MWCNTs were used as reinforcement material with 8YSZ for the fabrication of ceramic matrix composite. In previous work, MWCNTs were synthesized using thermo-catalytic chemical vapor deposition (TC-CVD) with an outer diameter ranging from 20 to 30 nm and purity greater than 97% (Ref 34). The commercial 50 nm YSZ (99% purity, MK industries, Canada) was used as the raw material for the fabrication of composite using spark plasma sintering process (Ref 35). Ceramic matrix composite was fabricated with different percentages of MWCNTs (0.5 ~ 5 wt.%). The nanocomposites of different compositions (as shown in Table 1) were fabricated by dispersing the MWCNTs into a mixture of ethanol and water in a ratio of 3:2 with a 0.5 wt.% sodium hexametaphosphate as dispenser agent and ultrasonicated using a probe-ultrasonicator (OSCAR, PR600MP) with a frequency of 50KHz for 20 minutes. Then the YSZ powder was added and stirred vigorously using a magnetic stirrer for uniform blending between YSZ and MWCNTs. Subsequently, the obtained slurry was balled milled (SPEX 8000D, Ukraine) at a constant speed of 300rpm for 5 hours in presence of 12 tungsten carbide balls and further dried using a rotary evaporator (Buchi India Pvt Ltd, India) at a temperature of 100 °C for 12 hours. The attained powder was sintered using a spark plasma sintering process with graphite die of 20mm diameter lined with graphite foil and press. The sintering was performed at a temperature of 1350 °C with a heating rate of 100 °C/min and pressure of 50 MPa and dwell time of 10 minutes (Ref 36).

Table 1 Composition of samples

The phase composition of the sintered composites was studied using an x-ray diffractometer (smart lab-RIGAKU, Japan). The XRD was carried out at room temperature with 2θ value ranging from 0 to 90° and wavelength of 1.54056 Å with a step of 0.05° s−1 and operational target voltage and tube current of 30KV and 100 mA (Ref 37, 38). Surface topographies of the samples were obtained using a scanning electron microscope method (ZEISS SUPRA 55), and simultaneously quantitative elemental analysis was conducted (ASTM D4541) (Ref 39). The EDAX analysis was made at different spots on the samples to ensure the homogenous distribution of MWCNTs. The density of the samples was measured using Archimedes liquid displacement method with water as the immersion medium. Apparent density is the product of water density and ratio between dry sample weight and a difference in weights of dry sample and soaked immersed sample. Likewise, bulk density is the product of water density and ratio between dry sample weight and a difference in weights of soaked sample and soaked immersed sample. Those samples with high porosity were immersed into a mixture of water and lubricant for at least 3 days to ensure filling up of the pores. Then apparent porosity in percentage is the ratio of the difference in weights of soaked and dry samples to a difference in weights of soaked and soaked immersed samples (Ref 40). The Vickers hardness test (Krystal Elmec, India) was conducted as per ASTM C1327 standards with sample dimensions of 4 mm thickness, 30 mm diameter and 1µm surface finish. Further, the diamond indenter is used to make an impact on the sample with a load of 10 N and a dwell time of 20 seconds. The diagonal lengths of the indentation were measured using scanning electron microscopy for further utilization in the calculation of fracture toughness as per Evans and Charles equation (1) where ‘a’ is average half-length of the diagonal, ‘c’ is the average half-crack length from the diagonal and Hv represents Vickers hardness.

$$\mathrm{Fracture toughness }(\mathrm{Indentation }) {K}_{\mathrm{IC}}=0.203{\mathrm{ H}}_{\mathrm{V}} \times {\mathrm{a}}^{\left(\frac{1}{2}\right)}\times {\left\{\frac{\mathrm{c}}{\mathrm{a}}\right\}}^{-\left(\frac{3}{2}\right)}$$
(1)

Likewise, the single edge v-notch beam method (SEVNB method) was utilized to evaluate the fracture toughness of the composites. The required notch was machined using a diamond saw and tapered with help of a razor blade with 3µm diamond paste. The ASTM C1421 standard is followed for the SEVNB method with a dimension of test specimens being 40×3×4 mm. The SEVNB test was conducted in a four-point bending system with inner (S2) and outer (S1) span length of 10mm and 20mm, notch depth ‘a’ of ~ 0.5mm, ‘W’ and ‘B’ are width and thickness of specimens, ‘F’ being fracture load obtained through computerized method and α being ratio of notch depth to width of specimens (α = a/W) and ‘Y’ being stress intensity factor which was calculated through equation (2). With ‘Y’, the fracture toughness of specimens was calculated using equation (3) (Ref 41).

$$Y=1.9887-1.326\alpha -\frac{(3.49-0.68\alpha +1.35{\alpha }^{2})\alpha (1-\alpha ) }{{\left(1+\alpha \right)}^{2}}$$
(2)
$$\mathrm{Fracture toughness }\left(\mathrm{SEVNB}\right){K}_{\mathrm{IC}}= \frac{F}{B \sqrt{W}} \times \frac{{S}_{1}-{S}_{2}}{W} \times \frac{3\surd \alpha }{{2(1-\alpha )}^{1.5}}\times Y$$
(3)

The wear performance of the samples was investigated using a pin on disc tester (DUCOM TR-20LE-PHM-400-ASTM G99) (Ref 42, 43) under the ambient room temperature with a constant sliding speed of 0.523 m/s with varying load (5 N and 10 N) and sliding distance (100 and 400 m). Then the specific wear rate is calculated from the ratio between volume loss and the product of applied load and sliding distance.

Results and Discussion

Density and Porosity

The apparent and bulk densities of the samples are slightly varying due to the addition of MWCNT as shown in Fig. 1. The apparent density of YC1 is 6.23 g/cm3 which is highest and followed by YC0.5 is 5.92 g/cm3, YSZ is 5.83 g/cm3, YC2 is 5.38 g/cm3 and YC5 is 4.41 g/cm3. It is shown that the apparent density values are slightly increasing with the addition of MWCNT (up to 1%) and dropped from thereon, which may have been a result of CNT filling up the voids inside the composite by slipping away during the compaction process while sintering. However, a higher concentration of MWCNTs in the composite could lead to agglomeration that increases the open pores network resulting in density drop (Ref 44). Nisar et al. reported that CNT forms a continuous network layer on the samples due to agglomeration which leads to a decrease in the Joule heating by providing low resistance during the SPS process (Ref 45). Inversely the bulk density decreases with the addition of MWCNT. The bulk density of YSZ, YC0.5, YC1, YC2 and YC5 are 5.85, 5.72, 5.64, 5.48 and 4.72 g/cm3, respectively. The extreme decrease in bulk density at a higher amount of MWCNTs may be due to the additional pores volume between and within the particles taken into consideration during its assessment.

Fig. 1
figure1

Apparent and bulk densities along with porosity of the samples

Furthermore, the apparent porosity of YC1 is determined to be the lowest compared with other samples. The YC1 acted as the middle range between the porosity values of the composites. Considering the range of porosity, all the five composites could be classified into two categories of closed and open pores (cite 8ysz article). The composites YSZ, YC5 are said to be open pores with porosity values ranging from 30% or more whereas the other composites YC0.5, YC1 and YC2 is said to be closed pores. By observing the transition from open pores to closed pores between YSZ and YC2, it is evident that the composite which undergoes at high temperature leads to solid-state diffusion of the material which closes up the pores formed on the surface. A study conducted on spark plasma sintering of alumina concluded that the transition of open pores to closed pores occurs at a temperature above 1050°C which has been a result of the formation of isolated pores (Ref 46). It is evident that the material undergoes a transition from open to closed pores until an accumulation of 2% MWCNT, after that the composites again behave as open pores due to the presence of excess MWCNTs which led to weak interfacial bonding forming gaps between the composites resulting in increased porosity. Inversely, when lower amount MWCNT (< 0.5%) may degrade the carbon content during the sintering process. Thus, fracture propagation at grain boundaries was prevented due to the homogeneous distribution of the precise amount of MWCNT ( ~ 1%), which act as a barrier and reduced the apparent porosity.

Phase Analysis and Surface Morphology

The phase examination of YSZ mixed with various MWCNT composite powder is shown in Fig. 2. The XRD peaks revealed the presence of tetragonal and cubic phases in all the samples (YSZ & composites); however, monoclinic phases are present only in composites (YC1, YC2 and YC5) due to a superior amount of MWCNT (ICDD JCPDS 2003 database) (Ref 47). By contrast, a carbon nanotube is unexploited in the YC0.5 sample due to the lower amount of MWCNT decomposed in sintering which is confirmed from elemental analysis (Fig. 5b). Besides, the strongest peak of this phase diagram is a cubic phase appearing at 2theta of 30.25°. Other peaks of cubic phases were perceived at 2theta of 35.02°, 62.73° and 81.95°. Also, tetragonal phases were found at 2theta of 50.12°, 59.91°, 74.51° and 83.5°, respectively. The monoclinic phases of YSZ were perceived only in a higher amount of MWCNT with YSZ (YC1, YC2 and YC5) samples at 2theta of 28.53°. The high intensity was found at YC2 and YC5, and it indicates the high crystallite nature of composites. The present investigation revealed that the phase transition from cubic to tetragonal was found in the YSZ sample, and tetragonal phases were gradually decreased in YC0.5, YC1, YC2 and YC5 samples. The slight monoclinic phases appeared in a higher amount of MWCNT in composites due to the tetragonal phase transition (Ref 48).

Fig. 2
figure2

X-ray diffraction peaks obtained for the specimens sintered at 1350 °C

Besides, SEM is (Fig. 3) performed on the cross section of polished samples to analyze pores concerning grain size. The surface morphology of YC1 (Fig. 3b) exhibits the close pores, uniform distribution of MWCNT and high interfacial bonding resulting in microstructure refinement. On the other hand, the surface morphology of YC5 (Fig. 3c) shows a deep superficial pore, de-agglomeration of MWCNT and poor interfacial bonding due to a higher amount of MWCNT with YSZ. Furthermore, YSZ, YC0.5 and YC5 samples revealed a coarse structure with an average grain size of 25 ~ 32 nm, which is higher than YC1 and YC2 samples average grain size of 10 ~ 15 nm. However, in Fig. 3(b) sharp grains seem at the edge reflecting well-pinned CNT along grain boundaries. Thus, fracture propagation at grain boundaries was presented and acted as a barrier due to the high aspect ratio and strong Van der Waals’ force of attraction among CNTs, also leads the homogeneous distribution (Fig. 4) and reduced the apparent porosity (YC1 is 17.01%). Furthermore, the quantitative elemental values of samples are shown in Fig. 5. Initially, the base material (YSZ) was characterized by quantitative analysis to verify the purity of YSZ. Figure 5(a) confirms the 7.45% yttria and 92.55% ZrO2 presence. As expected, the carbon was identified for YC1, YC2 and YC5 (Fig. 5c, d, e) samples and confirmed the MWCNT presence. But in the YC0.5 sample (Fig. 5b), carbon content was unexploited which may be due to the decomposition of a lower amount of MWCNT during the sintering process.

Fig. 3
figure3

Scanning electron microscopy image representing (a) open pores of YSZ, (b) closed pores of YC1, (c) open pores of YC5 at same sintering temperature

Fig. 4
figure4

The entangled CNTs in YC1 sample

Fig. 5
figure5

Quantitative analysis of (a) YSZ, (b) YC0.5, (c) YC1, (d) YC2, (e) YC5 samples

Mechanical Properties

Vickers hardness test was carried, out and the diagonal length (Fig. 7a) was calculated from FESEM. The variation of Vickers hardness was uniform and reached a higher value of 13.52 ± 0.4 GPa for YSZ, 13.58± 0.3 GPa for YC0.5 and 12.96 ± 0.3 GPa for YC1 (Fig. 6). The high values may have been a result of better suspension of MWCNTs into the matrix and also the grain size reduction by pinning effect of CNTs which inhabits the grain growth. On the other side, hardness of YC2 and YC5 samples decreased successively (10.81± 0.5 and 8.85 ± 0.7 GPa, respectively) due to a higher amount of MWCNT. The Vickers hardness of the nanocomposites shows that the hardness is highly dependent on the CNT content (Ref 49). The increase in MWCNTs contents led to agglomeration and the aggolmated CNTs contained nano pores which were responsible for deterioration in hardness along with weak interfacing bonding between aggolmated CNT and YSZ which is evident from Fig. 3. Nevertheless, the hardness values achieved are higher than the other reported values suggesting that the prolonged ultrasonification of the CNTs led to a homogenous mixture which resulted in increased hardness (Ref 50, 51).

Fig. 6
figure6

Hardness and fracture toughness (SEVNB and indentation method) for the samples

The indentation fracture toughness (Fig. 6) of YSZ is 5.21 ± 0.2 MPa m½ which further increases by ~ 21% in YC1 (6.58 ± 0.3 MPa m½), 12% in YC0.5 (5.93 ± 0.2 MPa m½), 9% in YC2 (5.78 ± 0.4 MPa m½) and then decreases by 4% in YC5 (4.98 ± 0.2 MPa m½). Though, many authors have disputed the reports obtained through the indentation method reporting the method as indirect fracture measurement through cracks propagated (Ref 52). So, another method namely single edge v-notch beam was employed to understand the fracture toughness behavior of the composites. From SEVNB method, the fracture toughness of YSZ is 4.41 ± 0.4 MPa m½ which is further increased by 15% in YC1 (5.22 ± 0.3 MPa m½), 6% in YC0.5 (4.72 ± 0.2 MPa m½), 5% in YC2 (4.65 ± 0.2 MPa m½) and then decreases by 9% in YC5 (4.01 ± 0.2 MPa m½). Furthermore, the KIC values of both the methods are similar trends which are increasing with CNT content after that it has been decreased successively. The precise amount of CNT controls the grain growth, well dispersion along grain boundaries which led fracture toughness higher than YSZ in both methods. However, fracture toughness of YC5 is reduced from YSZ due to porosity and weakened interfacial bonding in composite introduced by a higher amount of MWCNT. As reported in the open literature on fiber-reinforced composites undergoes toughening mechanism such as fiber pull-out, crack deflection and crack bridging could also be responsible for enhanced toughness in the composites. Figure 7 shows the fractographic SEM images of cracks formed after the indentation fracture toughness method on the surface of nanocomposites showing crack deflection, bridging and pull-out mechanisms. The propagation of cracks after applied fracture load results in uncoiling of the entangled CNTs present in the composites leading to a bridging mechanism. With further propagation of cracks, the uncoiled CNTs stretch by anchoring into one side of the grains of the composites until the ceramic interface. The further cracks propagation in the high porosity samples leads to failure of CNT stretching resulting in reduced fracture toughness (Ref 53). Figure 7(a) clearly shows that the crack was deflected in multiple directions due to the encircling of YSZ with CNT particles. This crack deflection is consistent with the residual stresses at interfaces due to the difference in thermomechanical properties between YSZ and CNT. These manifold crack deflection in the composite increases energy-dissipation during crack propagation, leading to increased fracture toughness (Ref 54). Besides, the contribution of crack deflection to raising composite fracture toughening usually depends on the angle of deflection amount. The more twisting crack path is a qualitative sign that more energy was absorbed during crack spreading. The crack bridging and crack branching (Fig. 7b, c, d) mechanisms cause energy dissipation and are related to increased fracture toughness (Ref 55). Overall, experimental values have shown that the indentation fracture toughness values are ~ 20% higher than SEVNB method. From these comparisons, it is revealed that the indentation test can be considered only for relative toughness measurement purposes. Hence, it can be concluded that the various controversial KIC values reported earlier using the indentation method may be due to parameters chosen like insufficient crack length and grain size values (Ref 56).

Fig. 7
figure7

Fractographic images of crack (a) deflection, (b) branching, (c) bridging and (d) worn surfaces pull out

The specific wear rates of the samples at a constant sliding speed of 0.523 m/s, varying applied load (5 and 10 N) and varying sliding distance (100 and 400 m) are presented in Fig. 8. The wear rate was found to be increased with a load for fixed sliding velocity, but the effect of sliding distance is more pronounced specific wear in all samples (Ref 57). The wear rate of YSZ is 1.72 × 10−9 m3/N m (5 N & 100 m) which further increases their wear resistance by 70% in YC1 (0.482 × 10−9 m3/N m), 40% in YC0.5 (1.01 × 10−9 m3/N m), 13% in YC2 (1.49 × 10−9 m3/N m) and then decreases by 8% in YC5 (1.86 × 10−9 m3/N m). Likewise, the wear resistance of the remaining samples is increased with loads and sliding distances. However, YC5 samples drastically reduce their wear resistance up to 80% at a 400 m sliding distance. The outstanding wear resistance in the YC1 sample is promising with uniform tribofilm on worn surfaces. On the other side, the YC5 sample has an irregular form and does not protect from a fracture due to de-agglomeration/porosity; in fact, the wear resistance was closely similar (up to ~ 2% of MWCNT). However, pull out of MWCNT was found near wear tracks which are acting as an intrinsic lubricant to improve the wear resistance. Therefore, YC1 composite, i.e., precise quantity of MWCNT, has superior wear resistance among all types of samples.

Fig. 8
figure8

Specific wear rate of composites

Conclusion

This contemporary research explored the precise amount of MWCNT with 8YSZ on the improvement in structural and mechanical properties. Besides, precise amount of MWCNT controlled the grain growth, well-distributed along grain boundaries and led fracture toughness higher than YSZ in both the methods. The fracture toughness values obtained from indentation are higher (15-20%) than the SEVNB method. Hence, it can be concluded that the various controversial KIC values reported earlier using the indentation method may be due to parameters chosen like insufficient crack length and grain size values. Altogether, this present study revealed that the indentation method is advisable only for relative toughness measurements purpose. Further, the pull out of MWCNT was found near wear tracks act as an intrinsic lubricant to improve the wear resistance. Therefore, MWCNT plays a significant role to influence the wear behavior of composites by energy dissipating mechanisms such as crack–deflection, bridging and branching.

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Arunkumar, T., Anand, G., Subbiah, R. et al. Effect of Multiwalled Carbon Nanotubes on Improvement of Fracture Toughness of Spark-Plasma-Sintered Yttria-Stabilized Zirconia Nanocomposites. J. of Materi Eng and Perform (2021). https://doi.org/10.1007/s11665-021-05562-1

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Keywords

  • energy dissipating mechanisms
  • fracture toughness
  • multiwalled carbon nanotubes (MWCNTs)
  • spark plasma sintering (SPS)
  • yttria-stabilized zirconia (YSZ)