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Nanoscale Effect of Zirconia Filler Surface on Mechanical Tensile Strength of Polymer Composites
Nanoscale Research Letters volume 15, Article number: 51 (2020)
A characteristic effect of a nano-concave-convex structure of a zirconia nanoparticle assembly with an inherent porous structure and huge surface area enabled us to introduce systematic surface modification by thermal treatment to smooth surface and polymer impregnation to mask the nano-concave-convex structure of the zirconia nanoparticle assembly. A polymer composite prepared from 30 wt% poly(N-isopropylacrylamide) containing 0.02 wt% zirconia nanoparticle assembly with the inherent nano-concave-convex surface structure showed the highest tensile strength in mechanical tensile testing. However, both sintered zirconia nanoparticle assembly with smooth surface and zirconia nanoparticle assemblies with polymer masked surface showed lower strength with longer elongation at break in mechanical tensile testing.
Nanomaterials are some of the most intriguing advanced materials in many research and application fields [1,2,3,4,5], since their intrinsic physical/chemical properties are so different from those of bulk materials [6,7,8,9]. When nanomaterials are applied as fillers of polymer composites, minute differences in the fillers, such as surface area, surface structure, and particle morphology of the nanomaterials, lead to drastic changes in the macro-scale properties of the composites .
For instance, incorporation of inorganic components into polymers improved physical and chemical properties, such as thermal stability, mechanical strength, dispersibility, and solubility [11,12,13,14].
However, a systematic study failed to clarify the relationship between the nanoscale properties of the nanomaterials, i.e., structure, morphology, and surface area, and the macro-scale physical and mechanical ones of the composites.
Porous metal oxide nanomaterials such as silicon dioxide [15,16,17], titanium dioxide [18,19,20], zirconium dioxide [21,22,23], cerium dioxide [24,25,26], and other materials [27,28,29] with large surface areas have been applied in chemical catalysis, gas absorption, separation, drug delivery, and energy storage materials [30,31,32,33,34,35]. In this context, our group developed unique metal oxide nanoparticle assemblies with submicron-sized spherical morphologies by a simple one-pot and single-step solvothermal approach . We named these materials micro/mesoporously architected roundly integrated metal oxides (MARIMOs). These produce nanometer-scale surface roughness and wide surface area. For instance, TiO2 MARIMO has a nano-concave-convex surface due to its inherent numerous fine primary particles with diameters of ca. 5 nm and high specific surface area (400 m2 g−1) . In previous research, we applied these unique materials to support inhomogeneous nanometal catalysts and anode materials for rechargeable batteries. In the catalyst supports, highly dispersed Au nanoparticles on the TiO2 MARIMO support surface enhanced the catalytic activity and improved the durability of the catalyst at high temperature . In the anode material, Nb2O5-TiO2 MARIMO increased the current capacity and lifetime of the batteries . Additionally, TiO2 nanofiber bundles with a cheek brush morphology enhanced the mechanical strength of a polymer hydrogel when used as a filler .
The nano- and micro-scale anchoring effect is most significant in the adhesive mechanism. We consider that these MARIMOs with nano-concave-convex surface structures, huge surface areas, and porous structures would be appropriate for clarifying the relationship between nanoscale surface properties and macro-scale material properties, since the surface properties of MARIMO can be easily tuned by thermal treatment and polymer decoration (Fig. 1). For instance, thermal treatment of MARIMO creates a smooth surface with a decreased surface area and lower porosity. Impregnation  of monomers or polymers into MARIMO pores should mask the nano-concave-convex surface of the MARIMO. Thus, in this paper, a new method of filler surface modification by impregnation of polymers to mask the nano-concave-convex shape of MARIMO was studied to demonstrate the nano-anchoring effect of the filler surface. Here, we selected a zirconia (ZrO2) MARIMO as a filler to enhance the mechanical properties of polymer composites, since ZrO2 filler exhibits better properties such as chemical resistance especially for acids, mechanical strength, and thermal stability, which would be favorable for the polymeric matrix to lead durable polymer composites [41,42,43]. Monomers, 2-hydroxyethyl methacrylate (HEMA), benzyl methacrylate (BMA), and cyclohexyl methacrylate (CHMA), and their polymers were selected to modify the nano-concave-convex surface of ZrO2 MARIMO fillers. Poly(N-isopropylacrylamide) (PNIPAM) hydrogel was chosen as a matrix for the polymer composites.
There are several approaches to estimate physical and chemical interactions between filler surfaces and polymer chains in polymer composites. Thermogravimetry, UV–visible spectroscopy, FT-IR spectroscopy, and microscopy are their representatives. Here, we adopted mechanical tensile testing as an alternative technique that is relatively simple, easy, and rapid. There are a few reports on mechanical property of the hydrogels with graphene oxide and ZrO2 powder [44, 45], which is different from ours with respect to a simple system which consisted of only zirconia and polymer matrix. To the best of our knowledge, no report on the relationship between nanostructural changes in filler surfaces and polymer chains in polymer composites has been published.
N-isopropylacrylamide (NIPAM), N,N,N',N'-tetramethylethylenediamine (TMEDA), potassium persulfate (KPS), and commercial zirconia (commercial ZrO2) were purchased from FUJIFILM Wako Pure Chemical Corporation. HEMA, BMA, CHMA, and 1-hydroxycyclohexyl phenyl ketone (HCPK) were purchased from Tokyo Chemical Industry Co., Ltd. All reagents were used as received. ZrO2 MARIMO was obtained from UJIDEN Chemical Industry Co., Ltd.
Preparation of HEMA-, NIPAM-, BMA-, and CHMA-Impregnated ZrO2 MARIMO Fillers
An impregnation method for supported nanometal catalyst preparation  was applied to obtain HEMA-impregnated ZrO2 MARIMO filler. ZrO2 MARIMO was dried at 80 °C under vacuum for 12 h. Then, 20 μL of a HEMA/HCPK (20/1, mol/mol) mixture was added to 200 mg of vacuum-dried ZrO2 MARIMO, and the mixture was manually mixed well with a mortar and pestle. It was then irradiated with UV light for 1 h with intermittent mixing every 15 min. Similar procedures were used to prepare NIPAM-, BMA-, and CHMA-impregnated ZrO2 MARIMO fillers.
Preparation of PNIPAM Hydrogels with ZrO2 Fillers
Hydrogels consisting of PNIPAM and ZrO2 fillers were prepared according to a previously reported method . ZrO2 MARIMO (24 mg, 0.02 wt%) was dispersed in 115 mL of reverse osmosis water with N2 bubbling before adding NIPAM (36 g, 30 wt%) to the solution. The mixture was stirred for 30 min and then KPS (0.18 g, 0.67 mmol) in water (5 mL) and TMEDA (1.8 mL, 12 mmol) were successively added. The mixture was carefully transferred to several glass tubes with an inner diameter of 1.0 cm. The upper dead volume of the tubes was purged with N2 and the glass tubes were closed tightly with screw caps then left at 25 °C. After 3 days, the glass tubes were cut and the polymer hydrogels were removed. The obtained hydrogel rods with a diameter of 1.0 cm and length of 3.0 cm were used for mechanical strength measurements. Similar procedures afforded PNIPAM composites with HEMA-, NIPAM-, BMA-, and CHMA-impregnated ZrO2 MARIMO fillers.
Mechanical Tensile Testing of Polymer Composites
Mechanical tensile testing was applied to the specimens in the axial direction. The deformed length of the composite (strain) and the applied force (stress) were measured using a tensile tester (AND MCT-2150) with a crosshead speed of 50 mm min−1 at room temperature. On the tensile tests of all composite samples, the percent elongation, 930%, is the limitation of the tensile tester machine. Ten composite samples were used for the mechanical tensile testing, and at least seven samples were used for data analysis. We note that composites containing bubble, cracked by glass, and cracked by grip of tensile testing machine were omitted from the data analysis to guarantee the data quality. The results are presented as mean ± standard deviation.
Scanning electron microscopy (SEM) was performed on a Hitachi SU8020 FE-SEM microscope. Transmission electron microscopy (TEM) images were obtained with a JEOL JEM-2100F microscope. STEM-EDX mapping was taken by bright-field (BF) mode and performed on an Oxford INCA X-max 80 EDX spectrometer. X-ray diffractometry (XRD) was performed on a Rigaku SmartLab diffractometer (Cu Kα radiation, D/teX Ultra 250 detector). Nitrogen adsorption–desorption isotherms were obtained using a BEL Japan Inc. Belsorp Mini (II) instrument. Specific surface areas were calculated using the Brunauer–Emmett–Teller (BET) method, and pore size distribution was derived by the Barrett–Joyner–Halenda (BJH) method. Differential scanning calorimetry (DSC) was performed with DSC7000X from Hitachi High-Tech Science Corporation at a scanning rate of 10 °C min-1 from 0 to 100 °C in a nitrogen atmosphere in three scans. Size exclusion chromatography (SEC) was performed using a JASCO PU-2080 Plus pump with two gel columns (KF-804L and KF-806L) and an RI-2031 Plus Intelligent RI detector in chloroform calibrated with polystyrene standards at 40 °C. Diffuse reflectance infrared Fourier transform spectroscopy (DRIFTS) was performed on a FT/IR-4600 from JASCO Corporation, and the spectra were performing Kubelka-Munk transformations.
Results and Discussion
Surface Properties of ZrO2 MARIMOs
Physical properties of ZrO2 fillers were evaluated by the BET method, XRD, and SEM. A reference material, commercial ZrO2 nanoparticles, showed roughly aggregated morphology (Fig. 2a,b) with a specific surface area of 20 m2 g−1 (Table 1). Conversely, ZrO2 MARIMO exhibited a spherical mesoporous morphology (Fig. 2c,d) with a huge specific surface area (283 m2 g−1), which is 14 times larger than that of the commercial ZrO2 nanoparticles. Sintered ZrO2 MARIMO obtained by heating at 700 °C for 3 h in air exhibited a low specific surface area of 6 m2 g−1 as expected (Fig. 2e,f). The extreme reduction in the specific surface area indicates that the primary particle size of the sintered ZrO2 MARIMO was increased by heating, which was confirmed by primary particle size estimation from the XRD peak width using the Scherrer equation and BJH method from the nitrogen adsorption–desorption isotherm analysis (Table 1). Thus, tiny primary particles in the ZrO2 MARIMO brought huge surface area as well as porous structure with the nano-concave-convex surface. Therefore, much amount of materials will interact with the nano-concave-convex surface and pores of the ZrO2 MARIMO.
DSC is a powerful tool to demonstrate the interaction between ZrO2 filler surface and organic molecules through endo- or exo-thermal phenomena . Prior to surface decollation of ZrO2 MARIMO fillers by polymers, we selected NIPAM monomer as probe molecules to investigate the interaction between the ZrO2 filler surface and organic probe molecules by means of DSC, since melting point of NIPAM monomer is sensitive to the crystallinity of NIPAM solid . If NIPAM solid is embedded in pores of host materials, its melting point would shift to lower temperature, since the crystallinity of the embedded nano-sized NIPAM solid with nano-size in the pores of the host materials would be easily disturbed by some perturbation from boundary pore wall.
The DSC profiles of NIPAM itself, a mixture of commercial ZrO2 nanoparticles and NIPAM monomer (commercial ZrO2/NIPAM), a mixture of ZrO2 MARIMO and NIPAM monomer (ZrO2 MARIMO/NIPAM), and a mixture of sintered ZrO2 MARIMO and NIPAM monomer (sintered ZrO2 MARIMO/NIPAM) with different ZrO2/NIPAM ratio in weight are shown in Fig. S1, Fig. S2, and Fig. S3, respectively. NIPAM monomer itself showed an endothermal peak ascribed to its melting point at 67.7 °C. In the case of commercial ZrO2/NIPAM, a simple gradual peak shift of DSC profiles from 67.7 °C (NIPAM) to 64.8 °C was observed in accordance with the higher ZrO2 contents (Fig. S1, Table S1). The endothermal peaks at 64.8 °C can be ascribed to the melting point of NIPAM solid situated between the commercial ZrO2 primary particles.
On the contrary, the larger temperature shifts from 67.7 to 62.4 °C were recognized in accordance with the higher ZrO2 MARIMO contents up to ZrO2 MARIMO/NIPAM = 50/50 (wt%) in the case of ZrO2 MARIMO/NIPAM (Fig. S2, Table S1). These large shifts clearly demonstrate that the ZrO2 MARIMO has some positive effect on solid state of NIPAM monomer embedded in the MARIMO pores, where the larger shift of the endothermal peaks could correspond to the stronger interaction between the ZrO2 filler surface and NIPAM monomer. However, the endothermal peaks were shifted to opposite direction of higher temperature of 65.2 °C at the ZrO2/NIPAM ratio ranging from 50/50 to 80/20 (wt%). It is difficult to put forward a conclusive discussion, but the endothermal peaks at 62.4 and 65.2 °C might be ascribed to the melting points of NIPAM solid embedded deep pores and much amount of shallow pores in ZrO2 MARIMO, respectively. As for the sintered ZrO2 MARIMO/NIPAM with the smooth surface, quite similar simple lower temperature shifts of endothermal peaks were shown in proportion to sintered ZrO2 MARIMO contents (Fig. S3, Table S1) similar to the results of commercial ZrO2/NIPAM in Fig. S1.
Thus, the positive interaction found between the ZrO2 MARIMO and NIPAM monomer would be advantageous to polymer decollation onto the ZrO2 MARIMO surface.
Preparation of PNIPAM Hydrogels with ZrO2 Fillers
To evaluate the effect of surface structure of the ZrO2 fillers further, PNIPAM hydrogels with the ZrO2 fillers were chosen, since strength of PNIPAM hydrogels were sensitive to the properties of the fillers. PNIPAM hydrogels were prepared from aqueous solutions containing different amounts (20, 25, and 30 wt%) of NIPAM, KPS as a radical initiator, and TMEDA. When the gel obtained from 20 wt% of NIPAM was left at room temperature, it changed to sol within 60 min (Fig. S4a). Conversely, no structural deformation of the hydrogel shape was observed with the gels obtained from 25 and 30 wt% NIPAM solutions (Fig. S4b–c). The stress and strain were 2.7 ± 0.2 kPa and above 930% for 25 wt% PNIPAM hydrogels, and 7.8 ± 0.2 kPa and 716 ± 106% for 30 wt% PNIPAM hydrogels, respectively (Fig. S5 and Table S2). Then, we selected the stronger 30 wt% PNIPAM hydrogel as a polymer matrix to evaluate the effect of the ZrO2 fillers.
The ZrO2 filler content in PNIPAM hydrogels was then optimized by changing the amount of the commercial ZrO2 filler (0.002 (2a), 0.02 (2b), and 0.04 wt% (2c)) in 30 wt% of PNIPAM hydrogel. Consequently, composite 2a showed the highest tensile strength (9.5 ± 0.7 kPa), while composite 2b showed the highest elongation (902 ± 28%) among all composites (Fig. S6 and Table S3). From these results, it is difficult to judge which one (high tensile strength or long elongation) is suitable for the filler amount to prepare polymer hydrogel. Then, the profile areas were calculated to estimate how much work was necessary to break these composites. Consequently, composite 2b showed the highest work among all the composites (Table S3).
Thus, the conditions of 30 wt% of NIPAM and 0.02 wt% of ZrO2 filler were fixed throughout the experiments.
Mechanical Tensile Testings of the Polymer Composites
The mechanical tensile strength obtained from stress–strain curves is shown in Fig. 3. The maximum stress and strain of each composite estimated from mechanical tensile testings are summarized in Table 2. The effect of the surface morphology of ZrO2 filler on polymer composites can be clarified by measuring the tensile strength [41,42,43] of composites prepared with commercial ZrO2 (2b), with nano-concave-convex ZrO2 MARIMO (3), with and sintered ZrO2 MARIMO (4) with the smooth surface. As a result, composite 3 containing MARIMO with the nano-concave-convex surface showed the highest ultimate tensile strength (9.2 ± 0.2 kPa) and the lowest elongation (746 ± 37%). However, composite 4 containing sintered MARIMO with a smooth surface exhibited a poor tensile strength of 6.6 ± 0.3 kPa. Elongation capacities of 2b (902 ± 28%) and 4 (903 ± 19%) were almost the same. Generally, the anchor effect of filler surface on polymer chains and slippage of polymer chains can be estimated from the maximum stress and maximum strain, respectively, obtained from mechanical tensile testing . The obtained results clearly indicate that the nano-concave-convex surface played a critical role in the tensile strength of the polymer composites as expected, which can be an anchoring effect between the nano-concave-convex surface and the polymer chains in the polymer composites. In order to know the microstructure and distribution of ZrO2 fillers, we used freeze-dried polymer composites for direct SEM observation. As a result, we confirmed the uniform polymer network of hydrogel but no aggregation nor agglomeration of ZrO2 fillers was observed (Fig. S7).
Effect of Surface Properties of Polymer-Impregnated ZrO2 MARIMO
To complete the systematic study on the relationship between the nano-concave-convex surface of the ZrO2 MARIMO filler and polymer chains, we modified the ZrO2 MARIMO filler surface by polymer impregnation to mask the nano-concave-convex surface. Herein, we selected vinyl monomers such as HEMA, NIPAM, BMA, and CHMA to be impregnated into pores of ZrO2 MARIMO. Polymerization of the impregnated monomers in ZrO2 MARIMO was achieved by UV irradiation in the presence of a photoinitiator (HCPK). The progress of polymerization was checked by SEC of the supernatant of the impregnated ZrO2 MARIMO/chloroform dispersion (Table S4). All the samples had molecular weights of around 1000. On DRIFTS experiments, there is no significant peak indicating interaction between the polymer and ZrO2 MARIMO (Fig. S8). In this meaning, we studied SEM and STEM-EDX analysis to confirm impregnation. As shown in Fig. 4, the spherical MARIMO morphologies were retained even after the impregnation treatments. STEM-EDX analysis (Fig. 5) clearly shows that Zr, C, O, and (N) atoms were homogeneously distributed throughout the ZrO2 MARIMO fillers. These results indicate that the monomers were uniformly impregnated and polymerized in the nanocavities and pores of the MARIMO.
Mechanical Tensile Testings of Polymer Composites
Existence of the anchoring effect of the nano-concave-convex surface of ZrO2 MARIMO was studied through mechanical tensile testings. Polymer composites with HEMA-impregnated ZrO2 MARIMO (5), with NIPAM-impregnated ZrO2 MARIMO (6), with BMA-impregnated ZrO2 MARIMO (7), and with CHMA-impregnated ZrO2 MARIMO (8) were prepared according to the similar procedures to that employed for composites 2b, 3, and 4. As shown by the mechanical tensile strengths obtained from stress–strain curves in Fig. 6, all composites 5–8 with vinyl polymer impregnated ZrO2 MARIMO fillers showed lower tensile strength as compared to composite 3 with the nano-concave-convex ZrO2 MARIMO filler (Table 3), suggesting the anchoring effect of the surface reduced in all cases of the polymer impregnated ZrO2 MARIMO fillers. Instead, higher elongation of all composites 5–8 with the polymer impregnated ZrO2 MARIMO fillers was clearly observed, which can be ascribed to slippage of the matrix polymer chains on the polymer-impregnated MARIMO filler surfaces. Thus, polymer-impregnated ZrO2 MARIMO fillers in polymer composites induced lower tensile strength and improved elongation capacity of the composites. Turning to the protopype ZrO2 MARIMO, the nano-concave-convex surface played a positive role in the tensile strength of the polymer composites.
Surface modification of a ZrO2 MARIMO filler with a nano-concave-convex structure revealed importance of nanoscale anchoring interactions between the filler surface and matrix polymer chains via mechanical tensile testings. To investigate the effect of the nano-concave-convex structure, we modified the ZrO2 MARIMO filler surface by (i) calcination of the ZrO2 MARIMO to smooth the nano-concave-convex surface and (ii) impregnation of polymers into the ZrO2 MARIMO pores to mask the nano-concave-convex surface. Mechanical tensile testing was applied to estimate the interaction between the surface of the fillers and the polymer chains in the polymer composites. The polymer composites containing a nano-concave-convex ZrO2 MARIMO filler showed the highest tensile strength, while polymer-impregnating the ZrO2 MARIMO fillers caused the large elongation. Thus, the nano-concave-convex surface of the ZrO2 MARIMO filler positively interacted with the matrix polymer chains to improve the tensile strength capacity, while polymer-masking the nano-concave-convex surface of the ZrO2 MARIMO fillers improved the elongation capacity. Consequently, rational design of the filler surface enabled us to understand the nanoscale interaction of filler surface with the polymer matrix through macro-scale mechanical tensile testings. Different kinds of monomers or polymers, such as ionic, hydrophilic, and hydrophobic monomers or polymers, can be incorporated into the MARIMO fillers by the simple impregnation technique to control properties of MARIMO fillers. Further studies on better dispersion of ZrO2 filler into aqueous media is now in progress.
Availability of Data and Materials
All relevant data that support the findings of this study are available from the corresponding author on request.
Diffuse reflectance infrared Fourier transform spectroscopy
Differential scanning calorimetry
1-Hydroxycyclohexyl phenyl ketone
Micro/mesoporously architected roundly integrated metal oxide
Size exclusion chromatography
Scanning electron microscopy
Transmission electron microscopy
- ZrO2 :
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The authors also thank Ujiden Chemical Industry Co., Ltd. for providing them with ZrO2 MARIMO.
This work was supported by the financial support from the Creation of New Business and Industry Program through the Kochi Prefectural Industry Academia Government Collaboration Research Promotion Operation.
The authors declare that they have no competing interests.
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Kan, K., Moritoh, D., Matsumoto, Y. et al. Nanoscale Effect of Zirconia Filler Surface on Mechanical Tensile Strength of Polymer Composites. Nanoscale Res Lett 15, 51 (2020). https://doi.org/10.1186/s11671-020-3282-6
- Surface modification
- Polymer composite