CC BY
37
УДК 539.32
Оценка модуля упругости нанокомпозитов на основе сшитого полиэтилена и глины с памятью формы
Y. Zare1, K.Y. Rhee2
1 Институт рака Мотамеда, Тегеран, 14155-4364, Иран 2 Университет Кёнхи, Йонъин, 446-701, Республика Корея
В статье с использованием ряда моделей проведен анализ модуля упругости полимерных нанокомпозитов из сшитого полиэтилена и глины с памятью формы. Традиционные модели, такие как модель модифицированного правила смесей, модели Guth, Paul, Counto, Kerner-Nielsen и другие, дают заниженные значения модуля упругости, показывая, что при его оценке для нанокомпозитов с памятью формы следует учитывать упрочняющий эффект нанонаполнителя. В некоторых моделях определены необходимые параметры для корректного расчета модуля упругости. В соответствии с моделью Halpin-Tsai для наполнителей с неравномерным трехмерным распределением и моделью Hui-Shia среднее значение относительного удлинения для слоев наноглины равно 56. Результаты, полученные с помощью модели Takayanagi, не согласуются с экспериментальными данными, что указывает на существенное влияние межфазной границы между полимерной матрицей и наноглиной. Предложена модификация моделей Guth, Halpin-Tsai и Kerner-Nielsen для корректировки расчета модуля упругости наноком-позитов на основе сшитого полиэтилена и глины с памятью формы.
Ключевые слова: модуль упругости, нанокомпозиты с памятью формы, моделирование
DOI 10.24411/1683-805X-2020-14011
Estimation of tensile modulus for cross-linked polyethylene/clay shape memory nanocomposites
Y. Zare1 and K.Y. Rhee2
1 Biomaterials and Tissue Engineering Research Group, Department of Interdisciplinary Technologies, Breast Cancer Research Center, Motamed Cancer Institute, ACECR, Tehran, 14155-4364, Iran 2 Department of Mechanical Engineering, College of Engineering, Kyung Hee University, Yongin, 446-701, Republic of Korea
Many models are used for the analysis of tensile modulus in cross-linked polyethylene/clay shape memory polymer nanocomposites. The conventional models such as modified rule of mixtures, Guth, Paul, Counto, Kerner-Nielsen, etc. underestimate the modulus exhibiting that the reinforcing effect of nanofiller should be considered for the estimation of tensile modulus in the shape memory nanocomposites. In addition, the appropriate parameters in some models are indicated for proper prediction of tensile modulus. Several models such as Halpin-Tsai for fillers with random 3D distribution and Hui-Shia offer the average aspect ratio of 56 for nanoclay layers. The results obtained by the Takayanagi model are not fitted to the experimental results demonstrating the important effect of the interphase between polymer matrix and nanoclay. Some models such as Guth, Halpin-Tsai and Kerner-Nielsen are modified for better adjustment to tensile modulus of cross-linked polyethylene/clay shape memory nanocomposites.
Keywords: tensile modulus, shape memory nanocomposites, simulation
1. Introduction
Smart materials have attracted much attention in more studies. Shape memory materials are regarded by their potential to store a temporary deformed shape
and recover the originally permanent shape [1]. The shape memory behavior is introduced by a change in temperature, which is shown in metals, ceramics and polymers [2-4]. Shape memory polymers demonstrate
© Zare Y., Rhee K.Y., 2020
many advantages such as low density, high shape recovery, high recoverable strain, easy processing along with low cost. Especially, their recoverable strain is in order of 100%, while this term in shape memory metals and ceramics reaches to only about 10% and 1%, respectively [5].
All shape memory polymer structure retains two hard and soft phases. The hard segments keep the permanent shape and does not melt or soften in the transition temperature Tg of soft segments. These segments can be cross-linked as rigid local structures or entanglements, which will not separate in the recovery temperature. In another side, the soft part acts as a switch to remember the original shape of material. The shape memory polymers causing the large strains to recover in restricted environments are employed in many applications such as deployable aerospace structures, microsystems, heat-shrink tubing and biomedical tools [6-8].
A typical predeformation and recovery cycles for shape memory polymers were described as follows [9]. First, the shape memory polymer is heated to high temperature, which in this step, the sample is deformed to a desired strain. In the second step, shape memory polymer is cooled to fix the temporary shape. At the lower temperature, the shape memory polymer molecular segments are frozen in a temporary position and upon removing the restriction, the induced shape is recovered. In the last step, the shape memory polymer is heated up to transition temperature, which the original shape is recovered. The deformation, i.e., strain energy is amassed by a reversible morphological change or inhibition of molecular relaxation [10]. From the theoretical point of view, this stored energy can be converted to force, but to attain this, the rubbery modulus described as the elastic modulus above Tg should be increased [11]. Many types of fillers such as chopped carbon, glass or Kevlar fibers have been used to improve the rubbery modulus [11].
There is a growing attentiveness on the nanostruc-tures such as nanocomposites in recent years [12-26]. In the recent years, it has been found that the performance of shape memory polymers significantly improves using nanoparticles [2, 27, 28]. Koerner et al. [29] have revealed that the homogeneous dispersion of 1-5 vol % of carbon nanotubes can store and subsequently release more than 50% of recovery stress compared to the neat polymer. Most studies have made known that the addition of nanofillers to polymers affects the physical, mechanical, thermal and barrier properties of polymers [30-34]. In the case of shape memory polymer reinforced with traditional
microfillers, it frequently loses its shape memory effect due to the high weight portion of filler (20-30%). Nanofillers can overcome these disadvantages and the smart nanocomposites, even with small clay contents (0-8 wt %) show good mechanical properties and high physical properties such as high recovery force.
Although much investigation has focused on the experimental characterizations of shape memory polymer nanocomposites, their properties have not been analyzed so far. The theoretical analysis and modeling can offer valuable information, which facilitates the achievement of desired properties. Further, the evaluation of behavior makes possible to predict the behavior of shape memory polymer nanocomposites without requiring more experiments. The prediction of rubbery modulus is more helpful particularly to make an appropriate actuator with specified properties. In this article, the tensile modulus of cross-linked shape memory polymer/clay nanocomposites is analyzed using the composite theories. In addition, some equations are suggested for better prediction of tensile modulus in these samples.
2. Background
The simplest models to predict the tensile modulus of composites are parallel and series models [35]. For the rule of mixtures, the equivalent strain is assumed in both matrix and filler phases. This model is given by
E _ EmK + E f (1)
where Em and Ef are the Young's moduli of matrix and filler, and and are the volume fractions of the matrix and filler.
The inverse rule of mixtures presumes the same stress in the matrix and filler parts as
1 _ K + k
E E„
(2)
The rule of mixtures model was modified by Cox [36] as
E _ EmK +nEff (3)
, tanh m
n_1--, (4)
m
m _a.
2G
Ef ln(r/R)'
(5)
in which a is the aspect ratio of filler, a _ w/t, where w and t are the width and thickness of the filler, G is
the shear modulus of matrix, while R and r are the filler radius and the centre-to-centre distance of the fillers.
U =
1 Hf G
The rule of mixtures was modified as [37]:
E _ Em K + MRF^f Ef, (6)
MRF = 1 (7)
V E A (8)
a V Ef Am
Verbeek model [38] considers the porosity of the composite and the aspect ratio of the reinforcement as key factors influencing the Young's modulus. This model assumes the perfect adhesion between the phases and stress is transferred through a shear mechanism. Verbeek model is given by
E _ EmAm + ^Ef f
tanh m
À = 1 -
m
(9) (10)
m=a
(1 - X )3 G фf
Ef
X = ■
f ¥
1 ^f
v =
фт(1 -у )
(1 -фm)f фmax
(11)
(1f)
(13)
E = x( Em Фm + Ef фf) + (1 - x)-
Ef Em
(14)
Ef +
where x and (1 - x) represent the relative contributions of composite to the rule of mixtures and inverse rule of mixtures, respectively.
Authors of Ref. [41] considered that the consistent stress is created at the matrix-filler interface: 1 + (m - 1)f
E = Em
1 + (m- 1)f
m=
E
Em
(15)
(16)
In Ref. [42] under the assumption of the faultless adhesion in the matrix-filler boundary a model was suggested as
1 _ 1 — f
E
1
Em (1 -фГ)/фГ Em + Ef
(17)
Guth [43] believed the interaction between filler particles exploiting the Smallwood-Einstein approach. The Guth model is presented as
E _ Em(1 + 2.5Af + 14.1A2). (18)
The aspect ratio of filler was introduced to the Guth model in order to account the accelerated stiffening for rod-like filler [44] as
E _ Em[1 + 0.67aAf + 1.62(a^f)2]. (19)
Davies [45] suggested one of the most used model
as
E15 _ EmfAm + E15Af. (20)
Halpin and Tsai [46] proposed the most commonly used model as
1
E = Em ,
1 -пФ
Ef/Em -1 Ef/ Em +Ç'
(f1)
(ff)
1 — ^m^max
where ¥ is the voidage and Amax is the maximum volumetric packing fraction of the filler, Amax = true volume of the filler/apparent volume occupied by the filler, X is the modified void content as the modified porosity relative to the polymeric phase. The value of Amax was determined through the method proposed by McGeary [39] as 0.75.
Series and parallel models as we mixed [40]
= 2a. (23)
The tensile modulus for randomly oriented fillers can be calculated by laminate plate theory as
E = 0.49E1 + 0.51E2, (24)
E1 and E2 are the tensile moduli of the composite in the longitudinal and transverse directions, respectively. Both E1 and E2 are calculated from Eq. (9), but the aspect ratio of filler is assumed as 1 for E2 (a = 1).
Landel and Nielsen [47] modified the Halpin-Tsai model as
1 + AB<f
E = Em
A=
1 - фВф^? ' 7 - 5v
8 - 10v
в = Ef/Em - 1
P = 1 + ф:
Ef/ Em + A' f 1 -Kax
Ф„
(f5)
(f6)
(f7)
(f 8)
where v is the Poisson ratio of matrix.
In addition, Lewis and Nielsen [48] took account the maximum volumetric packing fraction of the filler in the Halpin-Tsai model as
1 +
E = Em
ф= 1 + фf
1 -фпф
1 -Ф„ЯК
ф„
(f9)
(3G)
Kerner [49] proposed a model, which was originally developed to calculate the shear modulus of composites. The model is expressed as
E _ Em
1-
15(1 -v) fc
(31)
8 - 10v 1 -fcf
Hui and Shia [50] developed a model assuming the perfect interfacial adhesion between the polymer matrix and particles as
-1
+
E _ Em
Em
1 -fcf f 1-
4 U C + AJJ
(32)
Ef - Em
-3(1 -fcf)(1 -g)a2 -g2, (33)
A _ (1 -f
a2 -1
n
g _ 2 a,
3(a 2 + 0.25) g - 2a 2
a 2 -1 '
(34)
(35)
Ji et al. [51] suggested a three-phase model (matrix, filler and interphase) as
a-p
E _ Em
1 -a
+
1 -a + a(k-1)/ln k
P
1 -a + 1/2(a-P)(k + 1) + PEf/ Em
a _
2ti
1+1|<f
(36)
(37)
(38)
where t and ti are the thickness of filler and interphase, respectively, k is the ratio of the interphase modulus on the surface of filler Ei and the Young's modulus of matrix as k _ EilEm. If the effects of interface are neglected (ti = 0), the Ji model changes to the two phase model of Takayanagi [52] as
P ^
E _ Em
1 -p-
1 -P + PEf/ Em
(39)
E _Em(1 -a)2 +a2 Em + Ef
2
Sato and Furukawa [53] developed a model for the tensile modulus of composites using an adhesion parameter Z as
f 1 (1 fcfv;
E _ Em
1+
2-2^ (1-
«f 1 + fc3 - fc/3
3 1-fc3 +fc23.
(1-fc13)fcf
(40)
(41)
The Z parameter of 0 indicates the good adhesion, while Z = 1 shows the poor adhesion.
3. Results and discussion
The experimental measurements of tensile modulus were provided from Rezanejad et al. [6] study on the cross-linked polyethylene/clay shape memory na-nocomposites. The results showed that the tensile modulus, the recovery temperature, the recovery force and force recovery rate increased with the addition of nanoclay to the shape memory polymer, due to their improved mechanical properties, but final recovery strain decreases slightly about 12%. The XRD and TEM characterizations illustrated the intercalated structure. The presence of clay layers caused the cross-link density to decrease and crystallinity to increase.
When experimental data and theoretical measurements of tensile modulus are compared, except the rule of mixtures model, other models underestimate the tensile modulus showing the poor predictability of these models. It gives an idea that more parameters such as the aspect ratio of nanofiller should be assumed for estimation of tensile modulus in shape memory polymer nanocomposites. Modified rule of mixtures model suggests the lowest predictions in which the various values of aspect ratio of nanoclay do not change the predicted data, significantly. The obtained results by Davies model are found to be some better than others. The Kerner-Nielsen and Kerner models calculate the inappropriately identical results and their predictions do not depend on the maximum volumetric packing fraction of the filler fcmax and the Poisson ratio of matrix v. Furthermore, the Takayanagi model, which does not consider the interphase shows the much inferior results. It demonstrates that the effect of interphase should be taken into account in the Ji model for the cross-linked polyethylene/clay shape memory nanocomposites.
Using the Ji model, the values of nanofiller and interphase thickness (t and ti) and k should be established, which are very hard to characterize. However, in the previous studies, the value of k was randomly chosen and its role has not be determined, obviously [51]. Parameter k is defined as the ratio of the interphase modulus on the surface of the platelets Ei and the tensile modulus of matrix as k _ Ei/Em by the assumption of linear dependence of the modulus on space variable from the matrix to the surface of particles. As a result, the possible values of interphase modulus are Ei (min) = Em and Ei (max) = Ef. Accordingly, the parameter k can be selected in the range of 1 to 4450 for the present nanocomposites. The values of
k can be chosen from this range and the t/ti ratio is calculated from the fitting process to the experimental results. It should be indicated that the reduced thickness of the dispersed clay platelets t/ti expresses the level of exfoliation. The broken silicate layers in matrix with small thickness is indicative to smaller t/ti? which confirm the superior dispersion of silicate layers, i.e. higher degree of exfoliation. Figure 1 shows the values of t/ti as a function of k parameter. For k values ranged from 0 to 800, the t/ti increases to 0.25 rapidly, but for greater k values, the t/ti remains constantly at 0.25. The results of t/ti show clearly that the interphase thickness is at least four times higher than that of silicate layers, which verify the good exfoliation and reinforcing effect of nanoparticles in the polyethylene matrix. Evidently, further research by microscopic measurements is necessary for accurate determination of these parameters.
The Hirsch model [40] is properly fitted to the experimental data at x value of 0.01. It corroborates that the tensile modulus of cross-linked polyethylene/clay shape memory nanocomposites follows the rule of mixtures model more than the inverse rule of mixtures, due to the much higher modulus of nanoclay platelets. The developed Guth and Halpin-Tsai models calculate the tensile modulus at smaller aspect ratio of nanoclay compared to other models. These models usually over predict the tensile modulus [54] may be due to the minor contribution of two dimensional filler to tensile modulus in comparison to one dimensional fillers. Due to this reason, they are fitted to the experimental data at lower aspect ratios. Other models such as Halpin-Tsai for 3D random platelets, LewisNielsen, Hui-Shia and Verbeek suggest the various aspect ratios from 40 to 88 for nanoclay layers, which provide the average aspect ratio of 56. Moreover, Sa-to-Furukawa model predicts the tensile modulus accurately at Z of -14, while the variation range of Z is specified at 0 to 1. It is possibly due to the much slighter
level of nanoclay contents in the cross-linked shape memory nanocomposites compared to the conventional microcomposites.
For calculating the tensile modulus by the Cox model, two parameters including the aspect ratio of nano-filler a and the ratio of centre-to-centre distance of the filler and filler radius r/R should be measured. However, in the silicate layer nanocomposites containing randomly dispersed platelets, the accurate values of these parameters are difficult to determine. Therefore, the value of aspect ratio of nanoclay as a function of r/R is provided based on the fitting procedure to the experimental data as observed in Fig. 2. The aspect ratio of nanoclay increases quickly to 26 at r/R values of 1 to 35, but further values of r/R up to 300 do not affect the value of aspect ratio, noticeably. The obtained results show that the Cox model can predict the tensile modulus at the logical values of parameters.
3.1. Development of modified rule of mixtures model
The different aspect ratios of silicate layers have been indicated that do not affect the predicted results, considerably. In addition, the variation of MRF and u (Eqs. (7), (8)) at different nanoclay contents are negligible. As a result, modified rule of mixtures model for cross-linked polyethylene/clay shape memory nano-composites can be developed into
E = Em 4 m + MRF^f Ef. (42)
This equation is more similar to Cox and Verbeek models (Eqs. (3) and (9)) in which the MRF is the filler orientation efficiency factor [55]. MRF has been found to be 0.38 for PVA-nanotube thin films [56]. However, the best fitted results are obtained at MRF value of 0.01 for the current nanocomposites as illustrated in Fig. 3.
3.2. Modification of the Guth model
As mentioned, the Guth and developed Guth models do not estimate the suitable results for tensile
0 2 4 6 8
Nanoclay, wt %
Fig. 3. The predictions of tensile modulus by the modified rule of mixtures, Guth and Halpin-Tsai models
--1-1-1-1-1-1-1-r-1
0 2 4 6 8
Nanoclay, wt %
Fig. 4. The predicted modulus by the developed KernerNielsen, Kerner and Sato-Furukawa models
E = Em
(44)
modulus of present shape memory polymer nanocom-posites. Therefore, because of overestimation of the developed Guth model, a modulus reduction factor (MRF) can be introduced as
E = Em[1 + 0.67MRFa4f +1.62(MRFa4f)2]. (43)
Figure 3 shows the predicted results by the proposed model with the MRF value of 0.35. Obviously, the best agreement between the experimental and the predicted data is demonstrated.
3.3. Modification of the Halpin-Tsai model
Like the developed Guth equation, the Halpin-Tsai model also overestimates the tensile modulus. So, a MRF can be taken into account in the model for improving the predictability. The Halpin-Tsai model after introducing the MRF is presented as
,= E 1 + MRF^f 1 "^f '
Figure 3 shows the calculations of the modified Halpin-Tsai model by MRF value of 0.4. The proposed results are extremely better fitted to the experimental data compared to the original model.
3.4. Modification of the Kerner-Nielsen and Kerner models
As mentioned, the Kerner-Nielsen model cannot predict the tensile modulus of present nanocomposite. It was noted that various 4max and v values do not alter the predicted results, due to the higher level of Young's modulus of nanoclay (about 178 GPa) compared to the matrix modulus of 40 MPa. Accordingly, A, P and B parameters (Eqs. (26)-(28)) can be removed from the Kerner-Nielsen model and regarding the fitting process, the modified Kerner-Nielsen model can be shown as
1 + 354f
The theoretical predictions by modified KernerNielsen model are shown in Fig. 4. The modified model presents a good ability for prediction of tensile modulus in the present shape memory polymer nano-composites. Most attention should be given to the simplicity of the suggested model in which more simple parameters are observed. Additionally, the Kerner model is not fitted to the experimental data properly. Furthermore, the different values of v in the long range of 0.33 to 0.5 do not play a key role in the calculations. As a result, v can be taken out from the Kerner model and the developed model is attained such as the modified Kerner-Nielsen model in Eq. (45).
3.5. Development of the Sato-Furukawa model
The value Z = -14 in the Sato-Furukawa model suggests the accurate calculations for tensile modulus of current nanocomposite. But, the typical range of Z is determined as 0 to 1. By assuming Z = 0 for a perfect adhesion between nanoclay and matrix and using the fitiing procedure, the Sato-Furukawa model can be modified into
' 8*r
E = Em
1+-
1 -41
13
(46)
E = Em
1 -4f
(45)
The predictions of the modified Sato-Furukawa model is observed in Fig. 4. More superior conformity between the experimental results and the predictions is provided using the modified model.
4. Conclusions
The tensile modulus of cross-linked polyethylene/clay shape memory nanocomposites was evaluated using many models. The conventional models such as Paul and Counto underestimate the modulus showing the requirement to more parameters such as the aspect ratio of nanofiller. For many models, the suitable values of parameters for proper prediction of tensile
modulus are indicated. The average aspect ratio of 56 for nanoclay layers is obtained according to several models such as the Halpin-Tsai model for randomly 3D fillers and the Hui-Shia model. Moreover, the Ta-kayanagi predictions demonstrate the significant effect of interphase on the present shape memory polymer nanocomposites. Lastly, the modified rule of mixtures, the Guth, Halpin-Tsai, Kerner-Nielsen, Kerner and Sato-Furukawa models are modified to better estimation of tensile modulus for cross-linked polyethylene/clay shape memory nanocomposites.
References
1. Panahi-Sarmad M., Abrisham M., Noroozi M., Amir-kiai A., Dehghan P., Goodarzi V., Zahiri B. Deep focusing on the role of microstructures in shape memory properties of polymer composites: A critical review // Eur. Polymer J. - 2019. - V. 117. - P. 280303.
2. Wu G, Gu Y, Hou X., Li R., Ke H, Xiao X. Hybrid nanocomposites of cellulose/carbon-nanotubes/po-lyurethane with rapidly water sensitive shape memory effect and strain sensing performance // Polymers. - 2019. - V. 11. - P. 1586.
3. Liu Y., Zhang F., Leng J., Wang L., Cotton C., Sun B., Chou T.-W. Synergistic effect enhanced shape recovery behavior of metal-4D printed shape memory polymer hybrid composites // Composites. B. Eng. - 2019. - V. 179. - P. 107536.
4. Zaeem M.A., Zhang N., Mamivand M. A review of computational modeling techniques in study and design of shape memory ceramics // Comput. Mater. Sci. - 2019. - V. 160. - P. 120-136.
5. Cho J.W., Lee S.H. Influence of silica on shape memory effect and mechanical properties of polyure-thane-silica hybrids // Eur. Polymer J. - 2004. -V. 40. - P. 1343-1348.
6. Rezanejad S., Kokabi M. Shape memory and mechanical properties of cross-linked polyethylene/clay na-nocomposites // Eur. Polymer J. - 2007. - V. 43. -P. 2856-2865.
7. Hassanzadeh-Aghdam M., Ansari R., Darvizeh A. Thermal expanding behavior of carbon nanotube-shape memory polymer nanocomposites // Mech. Adv. Mater. Struct. - 2018. - P. 1-12.
8. Hassanzadeh-Aghdam M., Mahmoodi M., Ansari R., Darvizeh A. Interphase influences on the mechanical behavior of carbon nanotube-shape memory polymer nanocomposites: A micromechanical approach // J. Intelligent Mater. Syst. Struct. - 2018. - doi 1045389X18812704
9. Liu Y., Gall K., Dunn M.L., McCluskey P. Ther-momechanics of shape memory polymer nanocom-
posites // Mech. Mater. - 2004. - V. 36. - P. 929940.
10. Di Prima M., Gall K., McDowell D, Guldberg R., Lin A., Sanderson T., Campbell D., Arzberger S. Cyclic compression behavior of epoxy shape memory polymer foam // Mech. Mater. - 2010. - V. 42. -P. 405-416.
11. Ohki T., Ni Q.-Q., Ohsako N., Iwamoto M. Mechanical and shape memory behavior of composites with shape memory polymer // Composites. A. Appl. Sci. Manufactur. - 2004. - V. 35. - P. 1065-1073.
12. Panin V.E., Surikova N.S., Panin S.V., Shugu-rov A.R., Vlasov I.V. Effect of nanoscale mesoscopic structural states associated with lattice curvature on the mechanical behavior of Fe-Cr-Mn austenitic steel // Phys. Mesomech. - 2019. - V. 22. - No. 5. -P. 382-391. - doi 10.1134/S1029959919050059
13. Golovnev I.F., Golovneva E.I., Utkin A.V. Effect of the nanorod size on energy absorption at the microlevel under cyclic loading // Phys. Mesomech. -2019. - V. 22. - No. 5. - P. 420-431. - doi 10.1134/ S1029959919050084
14. Bochkarev A.O., Grekov M.A. Influence of surface stresses on the nanoplate stiffness and stability in the Kirsch problem // Phys. Mesomech. - 2019. - V. 22. - No. 3. - P. 209-223. - doi 10.1134/S10299599 19030068
15. Golovnev I.F., Golovneva E.I. Numerical study of the kinetic aspects of fracture of metal nanocrystals // Phys. Mesomech. - 2019. - V. 22. - No. 3. -P. 195-202. - doi 10.1134/S1029959919030044
16. Korotaev A.D., Litovchenko I.Yu., Ovchinnikov S.V. Structural-phase state, elastic stress, and functional properties of nanocomposite coatings based on amorphous carbon // Phys. Mesomech. - 2019. -V. 22. - No. 6. - P. 488-495. - doi 10.1134/S 1029959919060055
17. Zare Y., Rhee K.Y., Park S.J. Simple model for hy-drolytic degradation of poly (lactic acid)/poly (ethylene oxide)/carbon nanotubes nanobiosensor in neutral phosphate-buffered saline solution // J. Biomed. Mater. Res. A. - 2019. - V. 107. - P. 2706-2717.
18. Zare Y., Rhee K.Y. Prediction of loss factor (tan 5) for polymer nanocomposites as a function of yield tress, relaxation time and the width of transition region between Newtonian and power-law behaviors // J. Mech. Behav. Biomed. Mater. - 2019. - V. 96. -P.136-143.
19. Zare Y., Rhee K.Y. Significances of interphase conductivity and tunneling resistance on the conductivity of carbon nanotubes nanocomposites // Polymer Composites. - 2020. - V. 41. - P. 748-756.
20. Li Z., Xu K., Pan Y. Recent development of superca-pacitor electrode based on carbon materials // Nano-technology Rev. - 2019. - V. 8. - P. 35-49.
21. Ventrapragada L.K., Creager S.E., Rao A.M., Podi-la R. Carbon nanotubes coated paper as current collectors for secondary Li-ion batteries // Nanotechno-logy Rev. - 2019. - V. 8. - P. 18-23.
22. Cherepanov G.P. Theory of superplasticity and fatigue of polycrystalline materials based on nanome-chanics of fracturing and failure // Phys. Meso-mech. - 2019. - V. 22. - No. 1. - P. 52-64. - doi 10. 1134/S1029959919010090
23. Beznosyuk S.A., Maslova O.A., Zhukovsky M.S. Quantum infrastructure of attosecond sensors and actuators of nonequilibrium physical media in smart materials // Phys. Mesomech. - 2019. - V. 22. -No. 5. - P. 432-438. - doi 10.1134/S10299599 19050096
24. Le J.-L., Xu Z. A simplified probabilistic model for nanocrack propagation and its implications for tail distribution of structural strength // Phys. Meso-mech. - 2019. - V. 22. - No. 2. - P. 85-95. - doi 10. 1134/S1029959919020012
25. DitenbergI.A., TyumentsevA.N., SmirnovI.V., Grin-yaev K.V., Chernov V.M. Thermal stability of nanos-tructured internally oxidized vanadium alloy with combined dispersion and substructural hardening // Phys. Mesomech. - 2019. - V. 22. - No. 6. -P. 496-503. - doi 10.1134/S1029959919060067
26. Tabatabaeian A., Ghasemi A.R. Curvature changes and weight loss of polymeric nano-composite plates with consideration of the thermal cycle fatigue effects and different resin types: An experimental approach // Mech. Mater. - 2019. - V. 131. - P. 69-77.
27. Hassanzadeh-Aghdam M., Ansari R. Thermal conductivity of shape memory polymer nanocomposites containing carbon nanotubes: A micromechanical approach // Composites. B. Eng. - 2019. - V. 162. -P.167-177.
28. Hassanzadeh-Aghdam M.K., Ansari R., Mahmoo-di M.J. Thermo-mechanical properties of shape memory polymer nanocomposites reinforced by carbon nanotubes // Mech. Mater. - 2019. - V. 129. - P. 8098.
29. Koerner H., Price G., Pearce N.A., Alexander M., Vaia R.A. Remotely actuated polymer nanocompo-sites—Stress-recovery of carbon-nanotube-filled thermoplastic elastomers // Nature Mater. - 2004. -V.3. - P. 115-120.
30. Zare Y., Rhee K.Y. A core-shell structure for interphase regions surrounding nanoparticles to predict the shear, bulk and Young's polymer moduli of par-ticulate nanocomposites // Phys. Mesomech. -2020. - V. 23. - No. 1. - P. 89-96. - doi 10.1134/S 1029959920010099
31. Zare Y., Rhee K.Y. A modeling approach for Young's modulus of interphase layers in polymer nanocomposites // Phys. Mesomech. - 2020. -
V. 23. - No. 2. - P. 176-181. - doi 10.1134/S 1029959920020095
32. Zare Y., Rhee K.Y., Park S.-J. Simple models for interphase characteristics in polypropylene/montmoril lonite/CaCO3 nanocomposites // Phys. Mesomech. -2020. - V. 23. - No. 2. - P. 182-188. - doi 10.1134 /S1029959920020101
33. Hassanzadeh-Aghdam M.K., Mahmoodi M.J., Ansari R., Mehdipour H. Effects of adding CNTs on the thermo-mechanical characteristics of hybrid titanium nanocomposites // Mech. Mater. - 2019. - V. 131. -P. 121-135.
34. Hasanzadeh M., Ansari R., Hassanzadeh-Agh-dam M. Evaluation of effective properties of piezoelectric hybrid composites containing carbon nano-tubes // Mech. Mater. - 2019. - V. 129. - P. 63-79.
35. Haghighat M., Zadhoush A., Khorasani S.N. Physi-comechanical properties of a-cellulose—filled sty-rene-butadiene rubber composites // J. Appl. Polymer Sci. - 2005. - V. 96. - P. 2203-2211.
36. Cox H. The elasticity and strength of paper and other fibrous materials // British J. Appl. Phys. - 1952. -V. 3. - P. 72.
37. Dong Y., Bhattacharyya D. Mapping the real mic-ro/nanostructures for the prediction of elastic moduli of polypropylene/clay nanocomposites // Polymer. -2010. - V. 51. - P. 816-824.
38. Verbeek C. The influence of interfacial adhesion, particle size and size distribution on the predicted mechanical properties of particulate thermoplastic composites // Mater. Lett. - 2003. - V. 57. -P. 1919-1924.
39. McGeary R. Mechanical packing of spherical particles // J. Am. Ceram. Soc. - V. 44. - 1961. - P. 513522.
40. Kalaprasad G., Joseph K., Thomas S., Pavithran C. Theoretical modelling of tensile properties of short sisal fibre-reinforced low-density polyethylene composites // J. Mater. Sci. - 1997. - V. 32. - P. 42614267.
41. Ahmed S., Jones F. A review of particulate reinforcement theories for polymer composites // J. Mater. Sci. - 1990. - V. 25. - P. 4933-4942.
42. Nunez A.J., Sturm P.C., Kenny J.M., Aranguren M.I., Marcovich N.E., Reboredo M.M. Mechanical characterization of polypropylene-wood flour composites // J. Appl. Polymer Sci. - 2003. - V. 88. - P. 14201428.
43. Guth E. On the hydrodynamical theory of the viscosity of suspensions // Phys. Rev. - 1938. - V. 53. -P.322-325.
44. Wu Y.-P., Jia Q.-X., Yu D.-S., Zhang L.-Q. Modeling Young's modulus of rubber-clay nanocomposites using composite theories // Polymer Test. - 2004. -V. 23. - P. 903-909.
45. Davies W. The theory of elastic composite materials // J. Phys. D. Appl. Phys. - 1971. - V. 4. - P. 1325.
46. Halpin J.C., Kardos J. The Halpin-Tsai equations: a review // Polymer Eng. Sci. - 1976. - V. 16. -P.344-352.
47. Landel R.F., Nielsen L.E. Mechanical Properties of Polymers and Composites. - CRC Press, 1993.
48. Lewis T.B., Nielsen L.E. Dynamic mechanical properties of particulate-filled composites // J. Appl. Polymer Sci. - 1970. - V. 14. - P. 1449-1471.
49. Kerner E. The elastic and thermo-elastic properties of composite media // Proc. Phys. Soc. B. - 1956. -V. 69. - P. 808.
50. Hui C., Shia D. Simple formulae for the effective moduli of unidirectional aligned composites // Polymer Eng. Sci. - 1998. - V. 38. - P. 774-782.
51. Ji X.L., Jiao K.J., Jiang W., Jiang B.Z. Tensile modulus of polymer nanocomposites // Polymer Eng. Sci. - 2002. - V. 42. - P. 983.
52. Cauvin L., Kondo D., Brieu M., Bhatnagar N. Mechanical properties of polypropylene layered silicate
nanocomposites: Characterization and micro-macro modelling // Polymer Test. - 2010. - V. 29. -P. 245-250.
53. Sato Y., Furukawa J. A molecular theory of filler reinforcement based upon the conception of internal deformation (a rough approximation of the internal deformation) // Rubber Chem. Technol. - 1963. -V. 36.- P. 1081-1106.
54. Sisakht Mohsen R., Saied N.K., Ali Z., Hosein E.M., Hasan P. Theoretical and experimental determination of tensile properties of nanosized and micron-sized CaCO3/PA66 composites // Polymer Composites. - 2009. - V.30. - P. 274-280.
55. Coleman J.N., Khan U., Gun'ko Y.K. Mechanical reinforcement of polymers using carbon nanotubes // Adv. Mater. - 2006. - V. 18. - P. 689-706.
56. Shaffer M.S., Windle A.H. Fabrication and characterization of carbon nanotube/poly (vinyl alcohol) composites // Adv. Mater. - 1999. - V. 11. - P. 937941.
Received 21.07.2020, revised 21.07.2020, accepted 03.08.2020
Сведения об авторах
Yasser Zare, PhD, Dr., Motamed Cancer Institute, Iran, y.zare@aut.ac.ir
Kyong Yop Rhee, PhD, Prof., Kyung Hee University, Republic of Korea, rheeky@khu.ac.kr
