Constitutive Modelling for Anisotropic Damage in Woven E-Glass Reinforcements
Ping Yang^{*}, Ying Tong^{}
Article Information
Identifiers and Pagination:
Year: 2017Volume: 11
First Page: 9
Last Page: 21
Publisher Id: TOMSJ-11-9
DOI: 10.2174/1874088X01711010009
Article History:
Received Date: 16/12/2015Revision Received Date: 17/05/2016
Acceptance Date: 25/06/2016
Electronic publication date: 28/04/2017
Collection year: 2017
open-access license: This is an open access article distributed under the terms of the Creative Commons Attribution 4.0 International Public License (CC-BY 4.0), a copy of which is available at: (https://creativecommons.org/licenses/by/4.0/legalcode). This license permits unrestricted use, distribution, and reproduction in any medium, provided the original author and source are credited.
Abstract
It is easy for composite laminates to be damaged by relative lower velocity impact which could give rise to internal delamination that will strongly weaken the compressive strength of laminates. In order to predict the occurrence of matrix failure, the elastic-brittle behaviors of fiber-reinforced composites were modeled constitutively by an anisotropic damage model. The dynamic tensile testing was performed at a constant velocity of 2 mm/min until the sample broke to achieve the mechanical parameters of E-glass reinforcements. The elastic constitutive equation and the constitutive damage model were obtained on basis of the fundamental theory of mechanics about the orthotropic constitutive of reinforcements. The methodology for this constitutive model which is developed by Hashin considered both the effect of fiber and matrix failure. Then, the developed constitutive equations were incorporated into the FE (finite element) codes, ABAQUS, through the user subroutine module to simulate the process of projectile impacting GFRP composite laminates. The results show that the material deformation reaches a maximum at 24 μs, then occurs rebound with the increase of the time. The stress of reinforcements traverse section linearly increases outward from 0 MPa to 509.8 MPa. Material damage area increases with the prolonging of time, and for a fixed time, material damage gradually increases from the edges to the center and reaches a constant value of 1, which means the rupture of the damage process.
1. INTRODUCTION
Fiber-reinforced composites have been widely used in some structural components in aircrafts on account of their multiple advantages such as lower thermal expansion and weight, higher specific stiffness, corrosion resistance and strength [1, 2]. It is well known that the properties of fiber-reinforced composites vary from matrix-dominant to fiber-dominant behavior [1], since they show strong anisotropic mechanical behavior according to their fiber orientations. Fiber-reinforced laminated composites are susceptible to transverse impact, especially transverse impact at low velocities which gives rise to significant damage inside composites in terms of matrix cracks and delamination, meanwhile inner damage is difficult to be detected with eyesight. The inner damage induces the obvious decrease in the stiffness and strength, and cumulative damage contributes most to the failure process of fibrous composite materials with non-ductile matrices. As a result, the damage of composite structure caused by the relative lower velocity impact inhibits their widespread applications in manufacturing [3]. In recent years, numerous investigations involving fiber-reinforced composites have been conducted on this subject, which contributes to the prediction of composite stiffness failure mechanisms, failure modeling, impact performance and non-orthogonal constitutive equation [4-16].
The relative lower velocity impact damage in laminates has been considered as a main threat for a long time [17]. A lot of efforts have been paid to analyzing the impact behaviors of laminate structures, but few efforts have been devoted to the damage analysis of velocity impact on composites so far. Hou et al. [18] constructed a 3D FE model including three criteria based on failure stresses in order to analyze the whole process of damage onset and propagation in velocity impacted laminates. Zheng et al. [19] proposed a double Mindlin type plate model involving a improved virtual crack closure method to analyze the lower velocity impact. Johnson et al. [2] proposed a model on the basis of continuum damage mechanics to analyze the inter-laminar and intra-laminar failures during the loading process of velocity impact.
The GFRP laminates consist of epoxy resins and glass-fiber, thus the main fracture mechanisms for GFRP laminates includes two aspects, fiber failure and matrix failure. However, few attention has been paid to the integrated effects of fiber failure and matrix failure in constitutive damage modelling for GFRP laminates. The methodology for this constitutive model was developed by Hashin (1980) in which fiber mode and matrix mode, two distinct fatigue failure modes, were considered and modelled. In Hashin’s mathematical model, five coefficients closely related to strength parameters can be obtained and dirived from simple uniaxial tensions and compressions. In the following sections, firstly, the uniaxial tensile tests were performed at a constant velocity of 2 mm/min until the samples broke to achieve the mechanical parameters of E-glass reinforcements. Secondly, the basic mechanics theory about the orthotropic constitutive modelling of reinforcements is used to construct the Hashin constitutive damage model and analyze the impact behavior of composite structures. Finally, the developed constitutive equation was incorporated into a finite element code by using finite element method (FEM) on ABAQUS software, and the simulation procedure of bullet impacting GFRP laminates was realized in this way.
2. EXPERIMENTAL PROGRAMS
2.1. Material
The glass fiber reinforced composite (GFRP) studied is composed of polyacrylonitrile derived glass fibers in a resin matrix. A plain weave was used as a basic single-layer element design for one-layer fabric because due to its excellent performance. GFRP having fiber packing possesses a higher density which results in a higher strength, meanwhile GFRP possesses long floats and thus a lower crimp. The diameter of an E-glass fiber is approximately 9 μm, and it has less than 1% alkali chemically. The E-glass fiber has tensile strength 3448 MPa, elastic modulus 72.4 GPa, elongation 4.8%. The E-glass plain weaves were prepared by interlacing warp thread and fill thread as shown in Fig. (1). The E-glass plain weave woven with reinforcement adopted has a specific mass of 600 g/m^{2} with approximately 6 warp ends per cm, 4.5 weft picks per cm, in another word it has a density of 2.54 g/cm^{3}. The matrix resin has Polyester mixed up with catalyst hardener ensuring a density of 1.21 g/cm^{3}. The basic structural element is a laminated plate containing cross-woven E-glass cloth consisting of continuous glass filaments. Panel of thirteen element layers of E-glass woven fabrics was laminated to a thickness of 8 mm under the pressure of 100 MPa on a vulcanizing machine for forty-eight hours. Fig. (2) shows the homogeneity of the structure obtained by mixture of E-glass cloth with the resin. In the material, the overall fiber volume fraction is approximately 40%, and the resin volume fraction is approximately 60%.
Fig. (1). Schematic drawing of plain weave E-glass fabric. |
Fig. (2). Structure of the laminated composite material tested. |
2.2. Sample Preparation for Tensile Tests
Specimen is important for a tensile test as it determines the measuring results of stress-strain relationships. The specimen must conform to exact physical dimensions and must be no wrinkles, precision cutting and free of burrs and nicks. Here a precision milling machine and hand finishing were adopted, then the required configurations were achieved. Laminated composite samples with thirteen element layers of E-glass woven fabrics were prepared in panel form for cutting into the appropriate pattern, or pattern plating of the appropriate form. Epoxy resin was used as the material matrix. Laminated composite samples were prepared through a hand lay-up process. The lay-up chosen of the laminate was [0°/90°] S which provided a fully symmetric arrangement. A [0°/90°] lay-up for the glass plies ensured that uncured epoxy resin and hardener were respectively infiltrated into the 0° and 90° plies.
The tensile samples may be in the form of “dog-bone” samples as described in Chinese Standard GB/T1446-2005, Type-1, and their plane geometry and dimensions are illustrated as Fig. (3a). Fig. (3b) shows the specimen dimensions for testing Poisson’s ratio with aluminum sheets adhered to its two ends as described in Chinese Standard GB/T1447-2005. The aluminum sheet strengthens the ends of composite specimen, and ensures the first crack to appear in the middle of specimen.
Fig. (3). Geometry and dimensions of (a) tensile specimen; (b) rectangular poison’s ratio specimen. |
2.3. Test Procedure
The setup of the dynamic tensile testing is presented in Fig. (4). Tensile testing aims to evaluate the ability of a material to sustain pulling forces and the stretching extent before breaking. In a tensile testing process, one end of the sample is clamped while another one is pulled at a constant velocity of 2 mm/min until the sample is broken. Strain represents the length change resulted from pulling per unit of beginning length. The output of such a tensile test is a load versus elongation curve as shown in Fig. (5a) which will be converted into a curve about engineering stress versus engineering strain as shown in Fig. (5b). The engineering stress and the engineering strain data can be obtained by dividing the load and elongation by some constant values such as geometry informations). Fig. (5b) represents a typical engineering stress versus engineering strain curve, from which it can be seen that stress increases continuously along with strain and linearly up to a sudden drop (i.e. fracture).
Fig. (4). Test set-up for high speed tensile testing. |
In addition, during a tensile test for Poisson’s ratio, the elastic lateral strains need to be measured accurately, while their values of laminated composite samples reinforced with E-glass woven fabrics in a tensile test are usually very small. Therefore, in order to perform the reasonably accurate measurement of Poisson’s ratio, a very sensitive extensometer (strain gages) is always used for lateral strains. Fig. (6) represents the lateral strain versus longitudinal strain curve which indicates a linear relationship.
3. RESULTS AND DISCUSSION
3.1. Linear Elastic Characteristics in Microstructures
Fig. (5b) shows that the engineering stress increases linearly and then exits when the engineering strain passes the maximum value, 0.018. Meanwhile, from Fig. (6), it can be seen that the lateral compressive strain increases linearly along with the longitudinal strain increasing up to 0.018. The linear elasticity is valid due to the fact that stress states do not produce yielding. In Fig. (7a) the observation by optical microscope reveal that the fracture of the laminated composite reinforced with E-glass woven fabrics is smooth, which indicates that the material has negligible ductility. Fig. (7b) shows that the E-glass woven fabrics in the laminated composite have been pulled out from their matrix, and the curved E-glass fibers have become straight under large pullout energy. The observations reveal that the laminated composite reinforced with E-glass woven fabrics is also a kind of linear elastic material.
Fig. (5). Tensile property in principal direction: (a) load versus elongation curve; (b) engineering stress versus engineering strain curve. |
Fig. (6). Lateral strain versus longitudinal strain curve. |
Fig. (7). Failure of specimen (a) fracture; (b) failure fiber. |
3.2. Elastic Constitutive Model
In the coordinate system of 2D woven reinforced composite layer plate shown in Fig. (8), x_{1} and x_{2} indicate the direction of laying fiber longitudinal and transverse directions while x_{3} represents the thickness direction.
Fig. (8). The coordinate system of woven reinforced composite layer plate. |
When the main direction x_{1} subjects to tensile effect, the global and local coordinate systems coincide. According to axial conversion formula, the following forms can be obtained.
(1) |
According to tensile test results, the elastic modulus and Poisson's ratio of the composite material can be expressed as:
(2) |
The elastic constant in z direction (perpendicular to the layer) is approximately equal to the resin matrix. The elastic modulus and Poisson's ratio of this resin can be expressed as E_{3}= 907.42MPa, v_{23}= 0.072. Main direction strength is calculated using the following equation:
σ=F/bd | (3) |
Main direction strength σ_{11} is about 670 MPa. Interlaminar shear modulus parameters are not independent and Eq. (4) shows the relationship of three projects elastic constants, E, G and V.
(4) |
Substituing Eq. (2) into Eq. (4), thus, interlaminar shear modulus can be expressed as G_{12} = G_{13} = 1325.892MPa, G_{23} = 423.237MPa.
According to the mechanical properties of the elastic plate, stress-strain relationship during loading conforms to the generalized Hooke's law and can be expressed as
(5) |
In the theory of elasticity, the majority of anisotropic materials have symmetrical internal structure. Suppose there are two orthogonal symmetric elastic material, taking X_{1}-X_{3} plane as symmetry plane, flexibility matrix can be expressed as
(6) |
Where E_{1}, E_{2}, E_{3} are Young's modulus, and G_{12}, G_{13}, G_{23} are shear modulus.
According to the flexibility coefficient and the relationships between the elastic constants of engineering, the flexibility matrix is solved.
Eq. (7) is obtained by substituting the experimental results of tensile test.
(7) |
Stiffness coefficient C_{ij} Eq. (8) is obtained by the flexibility matrix inversion.
(8) |
in which,
Substituting the above results into Eq.6, it can obtain the elastic constitutive model of glass fiber reinforced composite.
(9) |
3.3. Failure Criteria
The failure criteria based on failure mechanisms was established by Hashin who in 1973 proposed two failure criteria considering the quadratic interaction between tractions acting on failure plane based on his own experimental observations of tensile specimen failures, one related to fiber failure and another one related to matrix failure. After that, in 1980, he furthermore deduced the fiber and matrix failure criteria distinguished by tension and compression statuses. In the failure modes of lamina, the method of Hashin is best suited for determining failure criteria. The coefficients in the quadratic polynomials are related to a series of strength parameters Xt, Xc, Yt, S_{12}, and S_{23}, which can be obtained from simple uniaxial compressions and tensions. In a practical application, the transverse and axial shear strength parameters are proposed to be equal. As the plane stress assumptions have been conducted, the following four failure criteria are constructed as follows:
(10) |
Material parameters of the glass-epoxy laminae are expressed as Table 1. The damaging effect resulting from the shear stresses and normal stresses in matrix and fibers frequently occurs on matrix or fiber-matrix interface, which often leads to debonding. In common the bonding strength of fiber-matrix interface is the lower in comparison with the strength of single constituents. The cracks in matrix soon transmit into fiber-matrix interface and propagate along fibers without crossing into fiber material. In common, yield and longitudinal shear failure are the main two causes inducing longitudinal compressive failure of composite. In further the compressive strength can be characterized by two models, and the first one is tension or compression damage model, meanwhile the second one is shear damage. They are written as
E_{1} | E_{2} | E_{3} | v_{12} | v_{13} | v_{23} | G_{12} | G_{13} | G_{23} | X_{t} | σ_{f} | a_{k} | |
---|---|---|---|---|---|---|---|---|---|---|---|---|
3314.73 | 3314.73 | 907.42 | 0.25 | 0.25 | 0.072 | 1325 | 1325 | 423 | 670 | 101.4 | 15.7 | 23.4 |
(11) |
The longitudinal compressive strength of composite selects the smaller one, then X_{c} =666.59MPa can be obtained. Substituting Eq.7, Table 1 and X_{c} into the Eq. 10, the Failure criteria finally becomes
(12) |
3.4. Simulation of Impact Tests on Composite Plate
The established failure criteria are usually inserted into finite element method to predict and describe failure behaviors in composite materials. The developed constitutive equation is incorporated into a finite element code. It can simulate the actual production and the results can provide a theoretical reference. The simulations of trial impact with damage/delamination model in ABAQUS/Explicit solver on ideal GFRP laminates are modeled. The plates consist of 6 plies of E-glass fabric/epoxy, and their nominal dimensions are 80×80×4 mm. In the trial impact a steel sphere impactor with a diameter of 50 mm and an added density of 7.8 g/cm^{3} shown in Fig. (9) is often adopted. The dimension data of the composite is imported, and then the surfaces are meshed. As the material thickness is small, shell element is suite. The parameters of impactor are shown in Table 2.
Fig. (9). The projectile and laminated composite plate model. |
ρ (kg/m^{3}) | E (MPa) | v |
---|---|---|
7800 | 2.0×10^{5} | 0.33 |
Orthotropic elastic constitutive model and Hashin failure criteria are used in 2D woven E-glass laminate and the parameters of them are shown in Tables 3 and 4 respectively. The composite plate is impacted at its center with a rigid impactor, meanwhile it is supported over the frame. The simulation results corresponding to an impact velocity of 55 m/s are shown in Fig. (10). These figures show that with the increase of deformation time deformation gradually increases until rupture of composite panels. From the deformation process under the impact effect in Fig. (10), it can be seen that the deformation of plate is small in the initial stage. With the increasing of the impact load, the deformation of plate gradually increases. When the impact load reaches a critical material damage value (732N), the plate begins to break. After about 24 μs, material deformation reaches the maximum and reallocation occurs subsequently.
ρ (kg/m^{3}) | E_{1} | E_{2} | E_{3} | v_{12} | v_{13} | v_{23} | G_{12} | G_{13} | G_{23} |
---|---|---|---|---|---|---|---|---|---|
1100 | 3314.73 | 3314.73 | 907.42 | 0.25 | 0.25 | 0.072 | 1325 | 1325 | 423 |
X_{t} | X_{c} | Y_{t} | Y_{c} | S_{1} | S_{c} | G_{1+} | G_{1-} | G_{2+} | G_{2-} |
---|---|---|---|---|---|---|---|---|---|
67 | 60.3 | 67 | 60.3 | 84 | 84 | 5E-6 | 5E-6 | 6E-6 | 6E-6 |
Fig. (10). Deformation process under the impact effect. |
Fig. (11) shows the typical deformation plots and stress contours during this impact event at an impact velocity of 55 m/s. In the initial stage of the impact, the stress (as shown in Fig. (11a)) is “cross-petal-shaped” distribution, which is because that transverse and longitudinal of composite laminates are the main fiber direction and suffer the most of the tensile stress. As shown in Fig. (11a)~d, material damage area increases with the prolonging of time. From Fig. (11b), it can be seen that stress gradually spreads to the surrounding from 619.6 MPa to 0 MPa. Fig. (11d) shows that at the maximal deformation during the impact process stress gradually increases outwards and it can be seen that the stress value of composite with 0 MPa becomes greater to 254.9 MPa, 509.8 MPa respectively after 24 μs corresponding to three points of 1, 2, and 3. Throughout the entire process, the material damage decrease radially from the center to the edges. As shown in Fig. (11), for a fixed time, material damage gradually increases from the edges to the center and reaches a constant value of 1, which means that the rupture of the damage process.
Fig. (11). Stress distribution rule under the impact effect. |
CONCLUSION
The dynamic tensile testing was performed at a constant velocity of 2 mm/min until the sample breaks. Through analysis of the experiment results and simulation the process of projectile impacting GFRP composite laminates, the following conclusions were drawn.
- The observation by optical microscope reveal that the fracture of the laminated composite reinforced with E-glass woven fabrics is smooth, which indicates the material has negligible ductility. The E-glass woven fabrics in the laminated composite have been pulled out from their matrix, and the E-glass fibers as strengthen part have become straight under large pullout energy.
- A continuum damage model for predicting damage in GFRP laminates has been established, and it is suited for the applications in finite element method.
- The simulation results have showed that the material deformation reached a maximum after about 24 μs, then rebound occurred with the increase of the time. The stress of reinforcements traverse section gradually increased outward from 0 MPa to 509.8 MPa. Throughout the entire process, the material damage decrease radially from the center to the edges. When the damage value of the center reaches 1, surrounded damage value tends to 0.
CONFLICT OF INTEREST
The authors confirm that this article content has no conflict of interest.
ACKNOWLEDGEMENTS
This work was supported by the open funds of State Key Laboratory of Vehicle NVH and Safety Technology of China (NVHSKL-201101).