Open access peer-reviewed chapter - ONLINE FIRST

Micromechanical Failure Analysis of Unidirectional Composites

By Zheng-Ming Huang

Submitted: April 2nd 2018Reviewed: August 8th 2018Published: November 5th 2018

DOI: 10.5772/intechopen.80807

Downloaded: 201

Abstract

Internal stresses in the fiber and matrix of a unidirectional (UD) composite obtained by any micromechanics model are homogenized quantities. They must be converted into true values before an effective specifically failure and strength property of the composite can be predicted in terms of the fiber and matrix properties only. As elastic property of a material does not depend on the magnitude of its stresses, the predictions of an elastic property of the composite based on the homogenized and true stresses of the constituents are the same, concealing the fact that the elastic property should be predicted based on the true stresses as well. The conversion of all of the internal stress components has been shown in this chapter. Predictability of a total number of 12 micromechanics models for the stiffness and strength of a UD composite is assessed against the experimental data of the 9 UD composites provided in three worldwide failure exercises (WWFEs). Bridging Model exhibits overall the best accuracy in both the stiffness and the strength predictions. Further, the smallest fiber volume in a RVE (representative volume element) for an FE (finite element) approach plays a much more dominant role than other issues such as a random fiber arrangement pattern to achieve the highest simulation accuracy. Finally, consistency of a micromechanics model in calculating the internal stresses of a composite is an issue that should be taken into account. Only Bridging Model is consistent. A non-consistency implies that a full three-dimensional (3D) model should be used to predict an effective property, e.g., failure behavior of a composite even though it is only subjected to a uniaxial load, and a 3D RVE geometry should be discretized if a numerical micromechanics approach is applied.

Keywords

  • composites
  • micromechanics
  • stress concentration factors
  • interface crack
  • failure analysis
  • strength prediction
  • consistency
  • fiber arrangement arrays

1. Introduction

Fiber-reinforced composites have been used as a primary-load carrying structural material in many engineering areas especially in aerospace industry. Due to their anisotropy, the mechanical properties of the composites are difficult or expensive to understand through experiments. Establishment of mathematical models to link the overall behaviors of the composites with their constituent structures and properties is an objective of micromechanics. As any continuous fiber-reinforced composite structure can be subdivided into a combination of a series of unit cells or RVEs [1], which can be considered as UD composites in their local coordinate system, a micromechanics analysis of a UD composite is fundamental.

So far, numerous micromechanical models have been developed to predict elastic properties of the composites from those of the constituent fiber and matrix materials [2, 3, 4]. On the other hand, very few of them have been applied to estimate failure and strength behaviors of the composites only based on the original constituent data measured independently with a reasonable accuracy [5]. This is attributed to that the internal stresses in the fiber and matrix of a composite obtained by a micromechanics theory are homogeneous quantities. They must be converted into true values before an effective property of the composite is predicted in terms of the original consituent properties. An elastic property (modulus, stiffness, etc.) of a material does not depend on the magnitude of the stresses in it, as long as they do not exceed the elastic limit of the material. Hence, the predictions of an elastic property of the composite based on the homogenized and true stresses of the constituents are the same, concealing the fact that the composite elastic property should also be predcited based on the true stresses. The stress field of the fiber is uniform [6, 7]. Its homogenized and true stresses are the same. A true stress of the matrix is obtained by multiplying its homogeneous counterpart with a stress concentration factor (SCF) of the matrix in the composite. This is because a plate with a hole generates a stress concentration if subjected to an in-plane tension. When the hole is filled with a fiber of different proerties, a stress concentration occurs as well.

The most significant feature is that such an SCF cannot be defined, following a classical approach, as a maximum point-wise stress divided by the overall applied one. Otherwise, the resulting SCF would be infinite if there is an interface crack or debonding on a fiber and matrix interface, since at the crack tip, a matrix stress is singular. All of the SCFs of the matrix in a composite have been obtained [8, 9, 10, 11] and are summarized in this chapter.

Another objective of this chapter is to make a critical assessment for the predicability of 12 well-known micromechanical models for the stiffness and mainly failure and strength of a UD composite, based on the original fiber and matrix properties and the fiber volume fraction. By “original,” it is meant that the properties are either measured independently using monolithic material, e.g., matrix specimens or documented in a recognized material database. The previous comparisons, e.g., Refs. [12, 13, 14], were made essentially for the stiffness predictions by different models. Seldom have been found for the strength predictions. The models considered in this chapter are Eshelby’s method [6, 15], Bridging Model [16], Mori-Tanaka method [17, 18], rule of mixture method [19], Chamis model [20], modified rule of mixture method [19], Halpin-Tsai formulae [21], Hill-Hashin-Christensen-Lo model [22], self-consistent method [15], generalized self-consistent method [15, 23], double inclusion method [4], and finite element method (FEM) [24] with different fiber arrangement patterns in a unit cell or RVE. The measured stiffness and strength data of all of the nine independent UD composites adopted in three WWFEs [25, 26, 27] are used as benchmark to judge the prediction accuracy of each model. An accuracy ranking is made based on the overall correlation errors between the models’ predictions and the experiments.

Numerical micromechanics such as FE approaches are popular in the current literature. What kind of fiber arrangement pattern should be chosen in a RVE? By definition, the RVE geometry, on which a homogenization is made, should be infinitesimal. In reality, however, a finite volume for a RVE has to be used. Thus, various choices exist. Many people [28, 29, 30] deemed that a random arrangement pattern with quite a number of fibers, e.g., 30 [31], 40 [32], or even 120 [33], should be contained in the RVE. It is shown among the four different patterns considered in this chapter the one with the smallest fiber volume results in the highest prediction accuracy.

Finally, consistency in the internal stress calculation deserves an attention. Any micromechanics model can result in two sets of formulae, i.e., two-dimensional (2D) and three-dimensional (3D) formulae, for homogenized internal stresses in the fiber and matrix of a composite. When the composite is subjected to a planar load, either the 2D or the 3D formulae can be applied to calculate the internal stresses. If the stress components in the fiber and matrix by the 2D and the 3D formulae are exactly the same, the model is said to be consistent in the internal stress calculation. It is shown in the chapter that among the 12 theories considered, only Bridging Model is consistent. Thus, if any other models specifically the numerical micromechanics method is applied to determine the internal stresses, its full 3D formulae should be made in use, even though the composite is subjected to only a uniaxial load.

In short, the topics addressed in this chapter are important to the micromechanical analysis of an effective mechanical property of a composite. If one would like to estimate its failure and strength behavior under an arbitrary load condition only from its constituent information, the true stress theory as described in this chapter is inevitable.

2. Fundamental for internal stresses

A composite is heterogenous by nature. Any stress and strain should be defined upon averaged quantities with respect to its RVE of a volume V' through.

σi=V'σ˜idV/V'=Vfσif+Vmσim,E1
εi=V'ε˜idV/V'=Vfεif+Vmεim.E2

It must be realized that by definition V' should be infinitesimal, and a resulting stress or strain, with ∼ on head, represents a point-wise quantity. If V' is finite, the corresponding one is called a homogenized quantity. In Eqs. (1) and (2), V is a volume fraction with Vf + Vm = 1. A super-/subscript f or m refers to the fiber or matrix, whereas a quantity without any suffix is related to the composite.

Using a bridging equation, σim=Aijσjf, and the constitutive relationships, εif=Sijfσjf, εim=Sijmσjm, and {εi} = [Sij]{σj}, the internal stresses in the fiber and matrix together with the compliance tensor of the composite are found to be [16]

σif=VfI+VmAij1σj,E3
σim=AijVfI+VmAij1σj.E4
Sij=VfSijf+VmSijmAijVfI+VmAij1.E5

Sijfand Sijmare the compliance tensors of the fiber and matrix, respectively, and [I] is a unit tensor. From Eq. (5), the bridging tensor is solved as

Aij=VfSijSijm1SijfSij/Vm.E6

The prediction of elastic moduli is equivalent to the calculation of internal stresses in the fiber and matrix of the same composite.

3. Highlight on micromechanics models

A different micromechanics model corresponds to a different bridging tensor. Perhaps the most compact bridging tensor is given by Bridging Model [16], of which the non-zero bridging tensor elements are expressed as follows:

a11=Em/E11f,E7.1
a12=a13=νmE11fEmν12fEmE11fa11a22,E7.2
a22=a33=a44=0.3+0.7EmE22f,E7.3
a55=a66=0.3+0.7GmG12f.E7.4

E11f, E22f, and G12fare longitudinal, transverse, and in-plane shear moduli of the fiber, respectively. ν12fis its longitudinal Poisson’s ratio. Em and Gm are Young’s and shear moduli of the matrix. Substituting the so-defined bridging tensor into Eqs. (3) and (4) leads to

σ11f=σ110Vf+Vma11Vma12σ220+σ330Vf+Vma11Vf+Vma22,E8.1
σ11m=a11σ110Vf+Vma11+Vfa12σ220+σ330Vf+Vma11Vf+Vma22,E8.2
σijf=σij0Vf+Vma22,ij=22,33,and23,E8.3
σijm=a22σij0Vf+Vma22,ij=22,33,and23,E8.4
σijf=σij0Vf+Vma66,ij=12and13,E8.5
σijm=a66σij0Vf+Vma66,ij=12and13,E8.6

{σ110, σ220, σ330, σ230, σ130, and σ120} are any arbitrary loads applied on the composite.

The other analytical models are summarized in Appendix A. However, numerical micromechanics methods are even more widely applied in the current literature [34, 35, 36]. Among, an FE approach is the most common. In this approach, the fiber and matrix in a RVE geometry are discretized, respectively, into a number of elements with prescribed boundary conditions. After the stresses (i.e., point-wise quantities) in the fiber and matrix of the RVE under any load are obtained through an FE package such as ABAQUS, they are homogenized as per Eq. (1) and the bridging tensor is determined following a method of Ref. [37]. The specification of the boundary conditions has become standard [36]. Thus, different solutions only come from different RVE geometries used.

In this chapter, four kinds of RVE geometries with the same boundary conditions are chosen for the comparison. They are square fiber array [38] (Figure 1a), hexagonal array [36] (Figure 1b), square-diagonal array [39] (Figure 1c), and random array with 30 fibers involved [28, 31] (Figure 1d). Our solutions are the same as those in Ref. [36] for Figure 1b, in Ref. [39] for Figure 1c, and in Ref. [31] for Figure 1d, respectively.

Figure 1.

Different RVEs for a UD composite used in FE approach: (a) square fiber array, (b) hexagonal fiber array, (c) square-diagonal fiber array, and (d) random fiber array.

4. Assessment on stiffness prediction

Hinton et al. organized three WWFEs to judge efficiency of the current theories for composites [5]. A total number of nine independent material systems were used. Mechanical properties of the fibers and matrices as well as fiber volume fractions of the nine UD composites were provided [25, 26, 27] and cited in Table B.1 (see Appendix B). Measured effective properties of the composites from the exercise organizers [25, 26, 27], which are used as a benchmark to assess the predictability of the 12 models, are listed in Table B.2. Predictions for the five effective elastic moduli of each of the 9 composites by the 12 models are made and are summarized in Table B.3. Relative error of each predicted result in comparison with the measured counterpart (Table B.2) is calculated. The overall averaged errors by the 12 models are indicated in Table 1, in which FE-square, FE-hexagonal, FE-square-diagonal, and FE-random stand for the FEM solutions based on Figure 1ad, respectively.

ModelNAveraged error*Error ratioRankModelNAveraged error*Error ratioRank
Bridging model4510.38%1.01Halpin-Tsai formulae4519.24%1.859
FE-square4513.08%1.262Modified rule of mixture4519.35%1.8610
Double inclusion method4513.6%1.313Mori-Tanaka method4519.59%1.8911
Chamis model4514.09%1.364FE-square diagonal4521.48%2.0712
Hill-Hashin-C-L model3317.22%1.665Self-consistent method4521.82%2.113
FE-random4517.57%1.696Rule of mixture method4528.4%2.7414
Generalized self-consistent4518.14%1.757Eshelby’s method4530.72%2.9615
FE-hexagonal4519.05%1.848

Table 1.

Overall averaged errors in prediction of the elastic moduli of the nine UD composites by different models.

=1Ni=1Nabserrori.


It is seen from the table that Bridging Model exhibits overall the highest accuracy in the stiffness prediction, with an overall correlation error of 10.48%. The second smallest error, 13.06%, is achieved by the FE-square array. The FE approach with a random fiber array of 30 fibers results in a correlation error of 17.57%, which is 34.5% less accurate than the FE approach with the square fiber array. The other two fiber arrangement patterns, the hexagonal and the square-diagonal fiber arrays, make the correlation even poorer than the random fiber arrangement. Although the four kinds of fiber arrangement patterns considered in this work may be limited, compared to unlimited possibilities in fiber arrangements, the present study confirms that the minimum fiber volume in the RVE geometry for a composite is the most dominant factor to influence the simulation accuracy, as long as suitable boundary conditions have been equally specified. Table 1 also indicates that three analytical micromechanics models, Bridging Model, double inclusion method, and Chamis model, possess sufficient accuracy in modeling of composite stiffness.

The largest correlation error, 30.7%, is assumed by Eshelby’s method. In addition to it, there are three other models attaining an averaged correlation error of more than 20% in the stiffness prediction. They are the FE-square diagonal fiber array, self-consistent method, and rule of mixture method.

5. SCFs of the matrix in a composite

5.1 Background

Let the E-glass/LY556 UD composite in Table B.1 be subjected to only a transverse tension, σ220, which will fail from a matrix failure. The only non-zero internal stresses of the matrix from Eqs. (8.2), (8.4), and (8.6) are σ11m=0.134σ220and σ22m=0.442σ220. Thus, the transverse tensile strength of the composite is σ22u,t= Ym/0.422, where Ym is the in situ transverse tensile strength of the matrix in the composite. Setting Ym = σu,tm= 80 MPa (Table B.2), where σu,tmis the original tensile strength of the matrix, one obtains σ22u,t= 181 MPa, which is more than 5.2 times greater than 35 MPa, the measured counterpart of the composite (Table B.2). A similar conclusion can be drawn no matter which other composite is considered or another micromechanics theory is employed. This implies that the homogenized internal stresses evaluated through Eqs. (3) and (4) must be converted into “true” values before a failure assessment can be made against the original strength data of the constituents. As point-wise strains in the fiber are uniform [6], its homogenized and true stresses are the same. However, those in the matrix are not. Each of its true stresses is obtained by multiplying the homogenized counterpart with a factor, which is agreed to call an SCF of the matrix in the composite.

5.2 Definition

The most significant feature, as aforementioned, is that such an SCF is no longer obtainable from a classical approach. Thus, the new definition must be made on an averaged stress. But with respect to which kind of geometry the averaging should be performed? A classical SCF was obtained by a point-wise (something like zero-dimensional) stress divided by an overall applied one, which is in fact a 2D quantity averaged with respect to the boundary surface. By similarity, a present SCF must be defined as a line-averaged (one-dimensional) stress of the matrix divided by a volume-averaged (3D) one since three is the maximum attainable dimension in the denominator. An SCF of the matrix subjected to a transverse load is derived through [10]

K22φ=1RφbRφaRφaRφbσ˜22mσ22mBMdRφ,E9

in which σ˜22mis a point-wise stress of the matrix determined on a concentric cylinder assemblage (CCA) model along the loading direction; σ22mBMis given by Bridging Model, i.e., by Eq. (8.4), φ is the inclined angle of the outward normal to a failure surface under the given load, and Rφaand Rφbare the vectors of Rφat the surfaces of the fiber and matrix cylinders within the RVE, respectively, where b=a/Vf.

5.3 Transverse SCFs

In such a load case, the explicit integration of Eq. (9) leads to [8, 9, 10]

K22(φ)={1+A2Vfcos2φ+B2(1Vf)[Vf2cos4φ+4Vfcos2φ(12cos2φ)+Vf(2cos2φ+cos4φ)]}(Vf+a22Vm)/a22,E10.1
A=2E22fEmν12f2+E11fEmν23f1E22f2νm2+νm1E11fE22f+Em1ν23f+E22fνm2E22fEmν12f2,E10.2
B=Em1+ν23fE22f1+νmE22fνm+4νm23Em1+ν23f.E10.3

Under a transverse tension, the failure surface of the composite is perpendicular to the loading and hence φ = 0 (Figure 2a). When a transverse compression is applied, the failure surface of the composite has an inclined angle with the loading [31]. The inclined angle, φ = ϕ (Figure 2b), between the outward normal to the failure surface and the loading, can be determined by virtue of Mohr’s theory as [9]

ϕ=π4+12arcsinσu,cmσu,tm2σu,cm.E11

Figure 2.

Schematic of a RVE used in defining SCF of matrix in a composite subjected to (a) a transverse tension and (b) a transverse compression.

The transverse tensile, transverse compressive, and transverse shear SCFs of the matrix in the composite are given as [9, 10, 11]

K22t=K220,E12.1
K22c=K22ϕ,E12.2
K23=2σu,smK22tK22cσu,tmσu,cm,E12.3

σu,tm, σu,cm, and σu,smare the original tensile, compressive, and shear strengths of the matrix, respectively.

5.4 SCF under longitudinal shear

A longitudinal shear SCF of the matrix is given by [11]

K12=1VfG12fGmG12f+GmπVf14Vf41282512Vf54096Vf213Vf+a66Vma66,E13

5.5 SCFs under equally biaxial transverse loads

Eq. (9) designates a general rule to determine any SCF of the matrix in the composite. Under an equally biaxial transverse tension or compression (Figure 3), a point-wise stress of the matrix in the x2-direction is obtained through a coordinate transformation:

σ˜22m=σ˜ρρmσ220+σ˜ρρmσ330cos2φ+σ˜φφmσ220+σ˜φφmσ330sin2φσ˜ρφmσ220+σ˜ρφmσ330sin2φ,E14

Figure 3.

Any biaxially transverse loads can be separated into superposition of an equally biaxial load and a uniaxial transverse tension either along x3-direction (a), if σ330−σ220 > 0, or along x2-direction (b), if σ220−σ330 > 0.

where [41]

σ˜ρρmσ220=σ22021+Aa2ρ2+1+B4a2ρ23a4ρ4cos2φ,E15.1
σ˜φφmσ220=σ22021Aa2ρ213Ba4ρ4cos2φ,E15.2
σ˜ρφmσ220=σ22021B2a2ρ23a4ρ4sin2φ.E15.3

The stresses σ˜ρρmσ330, σ˜φφmσ330, and σ˜ρφmσ330are also given by Eqs. (15.1)(15.3), respectively, as long as the σ220in them is replaced by σ330and φ by φ = φ + π/2. Substituting Eqs. (14) and (8.4) into Eq. (9), a biaxial transverse SCF of the matrix, K22Biφ, is derived as

K22Biφ=σ220σ22mBM+AVfσ220+σ3302σ22mBMcos2φ+Bσ220σ33021Vfσ22mBMVf2cos4φ+4Vfcosφ212cos2φ+Vf2cosφ+cos4φ

However, the failure surface orientation of a UD composite under an equally biaxial transverse tension or compression is indeterminate. For this reason, we can assume that the failure surface orientation under an equally biaxial transverse load is the same as that under a uniaxial transverse load. In other words, we have (σ220=σ330).

K22Bi,t=K33Bi,t=Vf+0.3VmE22f+0.7VmEm0.3E22f+0.7Em1+AVf,ifσ330>0,E16.1
K22Bi,c=K33Bi,c=Vf+0.3VmE22f+0.7VmEm0.3E22f+0.7Em1AVfσu,cmσu,tm2σu,cm,ifσ330<0.E16.2

5.6 SCFs subjected to any biaxial transverse loads

When the matrix is subjected to any biaxial transverse loads, we can always separate the loads into an equally biaxial transverse tension or compression plus a uniaxial transverse tension (Figure 3). The SCFs of the matrix are then determined accordingly.

5.7 Longitudinal normal SCF

No SCF exists in such a load case, since the resulting stresses in the matrix are uniform [7, 41].

6. Assessment on strength prediction

6.1 True stresses of the matrix

Let σim=σ11mσ22mσ33mσ23mσ13mσ12mTbe the homogenized stresses of the matrix in a UD composite calculated from a micromechanics model. The true stresses of the matrix, σ¯im=σ¯11mσ¯22mσ¯33mσ¯23mσ¯13mσ¯12mT, are determined as follows:

σ¯im=σ11mK33Biσ33m+K22tσ22mσ33mK33Biσ33mK23σ23mK12σ13mK12σ12mT,ifσ22m×σ33m0andσ22mσ33m0,E17.1
{σ¯im}={σ11m,K22Biσ22m,K22Biσ22m+K22t(σ33mσ22m),K23σ23m,K12σ13m,K12σ12m}T,ifσ22m×σ33m0and(σ33mσ22m)0,E17.2
σ¯im=σ11mK22σ22m0K23σ23mK12σ13mK12σ12mT,ifσ33m=0,E18.1
σ¯im=σ11m0K33σ33mK23σ23mK12σ13mK12σ12mT,ifσ22m=0,E18.2
K22Bi=K22t,Bi,ifσ22m>0K22c,Bi,ifσ22m<0,E19.1
K33Bi=K22t,Bi,ifσ33m>0K22c,Bi,ifσ33m<0,E19.2
K22=K22t,ifσ22m>0K22c,ifσ22m<0,E19.3
K33=K22t,ifσ33m>0K22c,ifσ33m<0.E19.4

6.2 Uniaxial strength formulae

Bridging tensor elements of a micromechanics model for each of the nine UD composites can be calculated through Eq. (6), using the corresponding elastic moduli given in Table B.3.

Under a uniaxial load, only the internal stress component of a constituent (fiber or matrix) along the loading direction is dominant. The other stress components, if any, are negligibly small. This can be realized from the explicit Eqs. (8.1)(8.6). Accordingly, a longitudinal failure of the composite is controlled mostly by a fiber failure, whereas all of the other failures are resulted from matrix failures. We only need to determine the following relationships:

σ11f=λ1σ110,σ22m=λ2σ220,σ23m=λ3σ230,σ12m=λ4σ120.E20

where λis are dependent on the bridging tensor and σ110, σ220, σ230, and σ120are external loads applied individually to the composite once at a time. For each of the 9 composites, the λis calculated by the 12 models are summarized in Table B.4.

In terms of the data in Table B.4, the longitudinal tensile and compressive, transverse tensile and compressive, transverse shear, and longitudinal shear strengths of a UD composite are estimated through.

σ11u,t=σu,tf/λ1,σ11u,c=σu,cf/λ1,σ22u,t=σu,tm/(K22tλ2),σ22u,c=σu,cm/(K22cλ2),σ23u=σu,sm/(K23λ3),andσ12u=σu,sm/(K12λ4)E21

where K22t, K22c, K12, and K23 are the transverse tensile, transverse compressive, longitudinal shear, and transverse shear SCFs of the matrix in the composite.

6.3 Prediction assessment

Using the constituent data of Table B.1, all of the SCFs of the matrices in the nine composites are calculated as per Eqs. (12), (13), and (16). They are listed in Table 2. All of the SCFs only depend on the constituent properties and fiber volume fraction of a composite, since a perfect interface bonding has been implicitly assumed. Table 2 shows that the transverse tensile SCF of the matrix is generally the biggest in a composite, whereas the transverse shear SCF is the second biggest or even bigger than all of the remaining SCFs in some composite. Further, the transverse tensile SCF can be greater than 3, implying that the classical SCF of a plate with a hole is not the upper limit for that of the matrix when the hole is filled with a fiber.

E-glass
LY556
E-glass
MY750
AS4
3501–6
T300
BSL914C
IM7
8511–7
T300
PR319
AS
epoxy
S2-glass
epoxy
G400–800
5260
K121.521.4911.4241.431.4751.511.4491.51.483
K233.022.9361.3372.4212.0342.1671.9992.9822.469
K22t3.3393.2532.0982.1432.3273.1232.3393.3172.464
K22c2.2492.1811.4691.571.7612.0351.7432.1721.732
K22Bi,t2.7472.671.7431.7591.9052.551.9162.7192.08
K22Bi,c2.1822.1321.5621.6011.7122.051.7092.1481.74

Table 2.

SCFs of the matrices in the nine composites.

The predicted results are compared with the experimental measurements shown in Table B.2, and the averaged relative correlation errors for all of the 12 models are summarized in Table 3. It shows that Bridging Model is still overall the most accurate, although the accuracy difference between Bridging Model and the other top three models is insignificant. Compared Table 3 with Table 1, the ranking order of the top four theories for both the stiffness and strength predictions is essentially the same, with only a minor difference in the ranking order from stiffness and strength predictions by the FE-square and double inclusion method.

ModelNAveraged error*Error ratioRankModelNAveraged error*Error ratioRank
Bridging model5321.1%1.01Mori-Tanaka method5330.2%1.438
Double inclusion (Digimat)5321.9%1.042Modified rule of mixture5330.7%1.4510
FE-square5323.1%1.093FE-square diagonal5331.9%1.5111
Chamis model5325.4%1.204FE-hexagonal5332%1.5212
FE-random5328.5%1.305Self-consistent method5332.7%1.5413
Hill-Hashin-C-L model1830.1%1.436Rule of mixture method5344.5%2.1114
Halpin-Tsai formulae5330.1%1.436Eshelby’s method5345.1%2.1415
Generalized self-consistent5330.2%1.438

Table 3.

Overall averaged errors in prediction of the uniaxial strengths of the nine UD composites by different models.

=1Ni=1Nabserrori.


The largest correlation error in the strength prediction is still assumed by Eshelby’s method, which is 45.1%. Another model gaining a correlation error of more than 40% is rule of mixture method. All of the theories under consideration for the strength predictions can be classified into three classes, according to their accuracies attained. The first class exhibits the highest accuracy. It consists of four methods, which are Bridging Model, double inclusion method, the FE-square, and Chamis model, with a correlation error in between 21.1% and 25.4%. The second class is moderate in accuracy performance. Most of the models, i.e., the FE-random, Hill-Hashin-Christensen-Lo model, Halpin-Tsai formulae, generalized self-consistent method, Mori-Tanaka method, modified rule of mixture method, the FE-square diagonal, the FE-hexagonal and self-consistent method, are within this class. Their correlation errors vary from 27.4% to 32.7%. The third class possesses the lowest prediction accuracy, consisting of two models, i.e., rule of mixture method and Eshelby’s method. Looking back at Table 1, the classification of the three classes of the micromechanics models for the stiffness predictions is also valid.

If no SCFs of the matrix are taken into account, i.e., if K22t= K22c= K12 = K23 ≡ 1 are assumed in Eq. (21), the overall correlation error by a model from the first or the second class is much greater. Consider, e.g., Bridging Model. Without the SCFs, the correlation error between the predicted and measured transverse tensile, transverse compressive, transverse shear, and longitudinal shear strengths of the 9 composites is 115.3%, 5.22 times greater than that when the SCFs are taken into account. It is noted that the longitudinal strength predictions have been excluded in this latter comparison. Hence, the most critical factor to influence the overall strength prediction is the SCFs of the matrix in the composite.

7. Additional comments

7.1 Consistency

Eqs. (1)(6) are valid for both 2D and 3D stress states. Any micromechanics model can result in two sets of internal stress formulae, i.e., 2D and 3D formulae, respectively. Let the composite be subjected to a planar stress state {σ110, σ220, σ120}. The resulting internal stresses in the fiber and matrix by the 2D formulae are represented as {σ11f,2D, σ22f,2D, σ33f,2D, σ23f,2D, σ13f,2D, σ12f,2D} and {σ11m,2D, σ22m,2D, σ33m,2D, σ23m,2D, σ13m,2D, σ12m,2D}, where σ33f,2D= σ23f,2D= σ13f,2D= σ33m,2D= σ23m,2D= σ13m,2D= 0. On the other hand, using the 3D stress formulae and applying a load combination {σ110, σ220, 0, 0, 0, σ120}, the internal stresses thus obtained are denoted as {σ11f,3D, σ22f,3D, σ33f,3D, σ23f,3D, σ13f,3D, σ12f,3D} and {σ11m,3D, σ22m,3D, σ33m,3D, σ23m,3D, σ13m,3D, σ12m,3D}. If σijf,2D= σijf,3Dand σijm,2D= σijm,3Dfor all i and j, the corresponding micromechanics model is said to be consistent in the internal stress calculation.

A necessary and sufficient condition for a micromechanics model to be consistent is that its bridging tensor is always in an upper triangular form. If, e.g., A32≠0, we will get from Eqs. (3) and (4) that σ33f=B32σ220≠ 0 and σ33m=A32σ22f+A33σ33f≠ 0, where [Bij] = (Vf[I] + Vm[Aij])−1. The bridging tensor of Bridging Model, by definition, is always upper triangular, even when a constituent, e.g., matrix undergoes a plastic deformation [16]. On the other hand, the bridging tensors of all of the other models for the nine composites are not upper triangular. Hence, all of the other models are not consistent. The non-consistency implies that the homogenized internal stresses should be calculated using the full 3D stress formulae, even though the composite is subjected to a uniaxial load. To apply an analytical model, other than Bridging Model, the 3D compliance tensors of the fiber, matrix, and the composite should be used in Eq. (6) to obtain the 3D bridging tensor. If a numerical method is applied to predict a composite property, a 3D rather than 2D RVE geometry should be discretized.

7.2 Accuracy estimation

It is known that the elasticity of UD composites is essentially matured. This means that the accuracy in both experimental measurement and micromechanics prediction for the elastic properties of a UD composite is likely not improvable significantly, unless a revolutionary change in the processing technology for a composite occurs. Considering the measurement deviations for the fiber, matrix, and composite properties as well as for the fiber volume fraction and in light of Table 1, it can draw a conclusion that an overall correlation error of 10% would be the one attainable in the composite stiffness prediction if only the original constituent information is available. As more than double of the constituent data together with more other information are required in a strength prediction, a reasonable correlation error in this latter case that can be expected should be more than 10% and mostly up to 20%.

The individual correlation error for each of the uniaxial strengths of the nine UD composites by Bridging Model is calculated and is shown in Table 4. Evidently, the predictions by the current theory for the longitudinal tensile, longitudinal shear, and transverse shear strengths of the composites are good enough, whereas those for the other three strength properties are either bad or not very satisfactory. Improvement in the prediction accuracy for the latter three uniaxial strengths is expected.

Longitudinal tensile strengthLongitudinal compressive strengthLongitudinal shear strengthTransverse tensile strengthTransverse compressive strengthTransverse shear strengthOverall
11%25.1%13.1%39.2%23.2%14.3%21.1%

Table 4.

Averaged correlation errors of Bridging Model for the individul uniaxial strengths of the nine UD composites.

7.3 Improvement in strength prediction

From Table 4, the largest correlation error comes from the prediction of a transverse tensile strength. This is attributed to a crack occurred in between the fiber and matrix interface. There must be some composites in which the fiber and matrix interfaces were already debonded before an ultimate failure under a transverse tensile load. Many researches in the literature have confirmed that an interface debonding has the greatest influence on the transverse tensile strength of a composite [42, 43, 44]. Therefore, a true stress component of the matrix corresponding to a transverse tension must take an interface debonding into account [11].

The second largest error is in the prediction of a longitudinal compressive strength. Only a strength failure has been considered in this work for a composite subjected to a longitudinal compression. Existing evidences show that a longitudinal compressive failure is frequently caused by a kink-band or microbuckling [45, 46, 47], due to an initial fiber misalignment. A micromechanics approach for a kink-band failure only using the original fiber and matrix properties together with the initial fiber misalignment angle has been achieved very recently [48]. However, a fiber misalignment angle is in most cases an in situ parameter and is difficult to be accurately measured. A more suitable way is to retrieve it from a measured longitudinal compressive strength parameter of the composite. On the other hand, this parameter can also be used to adjust the fiber compressive strength to improve the correlation accuracy.

The third correlation error, which is greater than 20%, occurs in the prediction for the transverse compressive strengths of the composites. Most probably, this error is attributed mainly to an inaccurate measurement/determination of a matrix compressive strength. It is known that among the three uniaxial strength parameters of a matrix especially a ductile polymer or metal matrix material, the compressive strength is the most difficult to be measured. Sometimes, one even cannot obtain a fracture load when a cylinder sample is compressively tested. Further study is needed to determine a matrix compressive strength.

An interesting phenomenon behind Table 4 is that either longitudinal or transverse shear strength can be sufficiently well predicted based on a perfect interface bonding assumption. Undoubtedly, an interface debonding may occur when the composite is subjected to a shear load. But the interface debonding has insignificant effect on the shear as well as on any other kind of load carrying ability of a composite except for the transverse tension, as seen in the subsequent section.

8. Failure prediction with a debonded interface

8.1 Transverse tensile SCF of the matrix after interface crack

All of the SCFs presented in the preceding section are based on an assumption that the fiber and matrix interface has a perfect bonding up to a composite failure. In other words, the point-wise displacements and the point-wise stresses of the fiber and matrix on their common boundary are continuous. In most cases, an interface debonding or crack can occur before an ultimate failure of the composite. However, Table 4 suggests that only the transverse tensile load sustaining ability of the composite is influenced heavily by the interface crack or debonding. The transverse tensile SCF of the matrix after the interface crack (Figure 4) must be taken into account in a failure prediction, in general. This SCF has been derived in Ref. [11], which is summarized below.

Figure 4.

(a) Schematic failure of a transverse tensile-loaded composite with an interface crack, (b) failure locus of a composite after interface cracks [42].

K̂22t=K̂22tψ=Ree2Mbea2/bbeN2N1a2be
+ e2+e2NbeN3Vf+0.3VmE22f+0.7VmEm2ba0.3E22f+0.7Em,E22.1
Nz=Fz+a2kzzae0.5+zae0.5F0.5Da2z,E22.2
N1z=Fz+a2kz+1ξzae0.5+zae0.5F0.5Da2z,E22.3
N2=aFe+ake,N3=Fae+eak,E22.4
Mz=Fa2kz2F0.5z+H+Cz+Dz2χz,E22.5
F=1cosψ+2λsinψexp2λπψ+1k1+4λ2sin2ψ4k22cosψ+2λsinψexp2λπψ,E22.6
H=acosψ+2λsinψ0.5F,E22.7
C=k1cosψ2λsinψa2exp2λψπ,E22.8
D=1ka3exp2λψπ,E22.9
χz=zae0.5+zae0.5,E22.10
k=Gm(1+κ2)(1+ξ)(Gm+κ1G23f),λ=(lnξ)/(2π),ξ=(G23f+κ2Gm)/(Gm+κ1G23f),κ1=34vm,κ2=3ν23f4ν12fν21f1+ν23f,E22.11
b=a/Vf.E22.12

In the above, ψ is the half of the crack angle, which is determined from

ReG01k21kkexpexp2λψπReφ=ψγ=0,E23.1
Rexp=expiφe0.5+expiφe0.5expiφ,E23.2
G0=1cosψ+2λsinψexp2λπψ+1k1+4λ2sin2ψ2kkcosψ+2λsinψexp2λπψ,E23.3
γ=2λJ12+J22J12+J222J2J3,ifξ<12λJ12+J22J12+J222J2J3,ifξ>1,E23.4
J1=kG0121kξexp2λψcosψ,E23.5
J2=21kξexp2λψsinψ,E23.6
J3=21kξexp2λψJ1cosψJ2sinψ/J2.E23.7

If ξ = 1, no solution for ψ is obtainable from Eq. (23). The corresponding interface crack is called a singular crack. But one can always adjust the fiber or the matrix properties involved so that ξ ≠ 1, since experimental deviations exist in measurement of them.

8.2 Interface crack detection

Let a UD composite be subjected to a transverse tension, σ220, up to an ultimate failure. The measured transverse tensile strength of the composite is Y. Suppose that the fiber/matrix interface of the composite is initially bonded perfectly. When the load is increased to a critical level, e.g., σ̂220, a stable crack with a central angle of 2ψ occurs on the interface. Many reports have pointed out that an unstable propagation from an initial interface crack to the last stable angle is short [42, 49, 50], with no significant change in the applied load. Thus, we can safely assume that at a transverse load level smaller than σ̂220the interface is in perfect bonding.

From Eq. (8.4), the transverse stress in the matrix when the crack occurs reads

σ̂22m=0.3E22f+0.7EmVf+0.3VmE22f+0.7VmEmσ̂220.E24.1

Further, the longitudinal stress of the matrix at the critical load level is obtained from Eq. (8.2) as

σ̂11m=Vfa12Vf+Vma11Vf+Vma22σ̂220.E24.2

No other stress in the matrix exists. Supposing that the transverse matrix stress corresponding to the composite failure is denoted by σ¯¯22m, one has.

K̂22tσ¯¯22mσ̂22m+K22tσ̂22m=σu,tm,E25.1

where

σ¯¯22mσ̂22m=0.3E22f+0.7EmVf+0.3VmE22f+0.7VmEmYσ̂220.E25.2

From Eqs. (24.1), (25.1), and (25.2), the critical transverse tensile load is found to be

σ̂220=K̂22tYK̂22tK22tVf+0.3VmE22f+0.7VmEm0.3E22f+0.7EmK̂22tK22tσu,tm.E26

If it is equal to or greater than the transverse tensile strength, Y, the fiber and matrix system is said to have a perfect interface bonding up to failure. Otherwise, the system will undergo an earlier interface crack and a further interface modification is preferred.

Under any arbitrary load condition, an interface crack occurs in the composite if and only if

σ¯m1l>0E27.1

and

σ¯emlσ̂em,E27.2

where

σ̂em=σ̂11m2+K22tσ̂22m2K22tσ̂11mσ̂22mE28

is the critical Mises stress. σ¯emland σ¯m1lare the Mises and the first principal stresses of the matrix obtained from the current load-step true stresses. For instance, when a planar load is applied to the composite, the current Mises true stress is given by

σ¯eml=σ¯11ml2+σ¯22ml2σ¯11mlσ¯22ml+3σ¯12ml2,E29
σ¯11ml=σ¯11ml1+dσ11m,E30.1
σ¯22ml=σ¯22ml1+K22eqdσ22m,E30.2
σ¯12ml=σ¯12ml1+K12dσ12m,E30.3
K22eq={K22t,ifdσ22m>0and(σ¯em)l1<σ̂emK̂22t,ifdσ22m>0and(σ¯em)l1σ̂emK22c,ifdσ22m<0.E31

The homogeneous stress increments, {dσ11m, dσ22m, dσ12m}, are calculated from Eqs. (8.2) and (8.4) in which {σ110, σ220, σ120} are replaced by {dσ110, dσ220, dσ120}.

Using the data of Tables B.1 and B.2, the transverse tensile SCFs of the nine UD composites after the interface crack together with the crack (half) angles are calculated from Eqs. (22) and (23). The critical transverse and Mises stresses are also obtained from Eqs. (26) and (28), respectively. They are summarized in Table 5. It is seen that the half crack angles of the carbon and glass fiber matrix interfaces under a transverse tension are close to 70°, consistent with the measured result shown in Figure 4b. Comparing the resulting σ̂220with the corresponding measured transverse tensile strengths, one can see that four composites, i.e., AS4/3501-6, IM7/8551-7, S2-Glass/Epoxy, and G40-800/5260 systems, have or nearly have a perfect interface bonding up to failure. The remaining five composites will undergo an interface debonding early before failure. There are two composite systems, S2-Glass/Epoxy and G40-800/5260, having a more than enough interface bonding strength, implying that more than enough efforts might have been paid.

E-glass
LY556
E-glass
MY750
AS4
3501–6
T300
BSL914C
IM7
8551–7
T300
PR319
AS
epoxy
S2-glass
epoxy
G40–800
5260
K̂22t7.697.224.955.045.416.975.437.345.68
ψ71.8°71.9°73.9°73.9°73.4°72°73.3°71.8°72.8°
σ̂220(MPa)20.328.244.44.772.533.51974.393.2
σ̂em(MPa)28.639.853.95.7690.646.324105.1119.4

Table 5.

Transverse tensile SCFs and other relevant parameter of the nine composites after interface debonding.

8.3 Off-axial strength prediction

A composite strength is assumed if either a fiber or a matrix failure is attained. A matrix failure is detected through, e.g., Tsai-Wu’s criterion (as isotropic materials are a subset of anisotropic composites), whereas a fiber failure is assessed by the generalized maximum normal stress failure criteria [16], through the following expressions:

F1σ¯11ml2+σ¯22ml2σ¯11mlσ¯22ml+F2σ¯12ml2+F3σ¯11ml+σ¯22ml1,E32.1
F1=1/σu,tmσu,cm,F2=1/σu,sm2,F3=1/σu,tm1/σu,cm.E32.2
σeq,tflσu,tforσeq,cflσu,cf,E33.1
σeq,tfl=σf1l,ifσf3l<0,σf1l3+σf2l313,ifσf3l=0,E33.2
σeq,cfl=σf3l,ifσf1l>0,σf3lσf1lifσf1l0.E33.3

σf1l, σf2l, and σf3l(σf1σf2σf1) are the three principal stresses of the fiber calculated from

σ11fl=σ11fl1+dσ11f,E34.1
σ22fl=σ22fl1+dσ22f,E34.2
σ12fl=σ12fl1+dσ12f.E34.3

σu,tfand σu,cfare longitudinal tensile and compressive strengths of the fiber, respectively.

Two UD composites, Kevlar-49/epoxy and E-glass/8804 epoxy systems, were subjected to off-axial tensile load up to failure. Constituent properties and transverse tensile strengths of the two composites as well as fiber volume fractions were provided in Ref. [51, 52] and cited in Table 6. From them, the SCFs of the matrices and the critical Mises stresses can be calculated and are also shown in the table. The predicted off-axial strengths of the Kevlar-49/epoxy and E-glass/8804 composites are plotted in Figures 5 and 6, respectively. The SCFs in the Kevlar fiber system with a perfect interface bonding are close to 1, because the transverse modulus of the Kevlar fiber is comparable to that of the matrix. Nevertheless, the transverse tensile SCF of the matrix in the Kevlar fiber system after the interface crack is still significantly higher than that with the perfect interface bonding. Both of the critical transverse loads of the composites, σ̂220= 1.2 MPa for the Kevlar and σ̂220= 42.4 MPa for the glass composites, are smaller than the corresponding transverse tensile strengths, 27.7 and 45.3 MPa, respectively, and the two composites will undergo an interface crack. However, the Kevlar fiber system will crack much earlier than the E-glass fiber system does when subjected to a transverse tensile load.

E11f(GPa)E22f(GPa)G12f(GPa)ν12fν23fσu,tf(GPa)Em (GPa)νmσu,tm(MPa)σu,cm(MPa)σu,sm(MPa)VfK22tK22cK̂22tK12σ̂em(MPa)
Kevlar-49/
epoxy
124.14.12.90.350.352.063.450.3569120500.551.081.072.741.171.1
E-glass/
8804
717128.20.260.261.53.10.297086390.512.972.025.61.3859.6

Table 6.

Constituent properties and resulting matrix parameters of two UD composites [51, 52]

Figure 5.

Comparison of different schemes’ predictions with experiments [53] for off-axial tensile strengths of a Kevlar-49/epoxy UD composite.

Figure 6.

Comparison of different schemes’ predictions with experiments [53] for off-axial tensile strengths of an E-glass/8804 UD composite.

Given an off-axial tensile load increment, dσθ, where θ is the off-axial angle, the stress increments {dσ110, dσ220, dσ120} are obtained through a coordinate transformation, and the interface cracking load, σ̂θ0, can be determined through Eq. (27). Consider the Kevlar fiber composite, for instance, and take θ = 30°. The homogenized stresses of the matrix are obtained from Eqs. (8.2), (8.4), and (8.6) as σ11m=0.115σθ, σ22m=0.234σθ, and σ12m=0.32σθ, whereas the true stresses before the interface crack are σ¯11m= 0.115σθ, σ¯22m=0.253σθ, and σ¯12m=0.374σθ. Hence, the interface cracking load σ̂3000= 1.11/0.684 = 1.623 MPa.

After the interface crack, only the transverse tensile stress increment of the matrix will be amplified with a different SCF. The true stresses of the matrix in the Kevlar fiber composite with θ = 30° and after the interface crack are given by σ¯11m= 0.115σθ, σ¯22m= 0.41 + 0.641(σθ − 1.623), and σ¯12m=0.374σθ. As the matrix failure occurs first, the predicted ultimate off-axial tensile strength from Eq. (32) is σ300u,t= 80.5 MPa, very close to the measured one, 83.4 MPa [53].

The measured data for the Kevlar and the glass composites taken from Pindera et al. [53] and Mayes et al. [52] are also shown on Figures 5 and 6, respectively. In order to display the predicted results at most off-axial angles more clearly, the predictions at angles smaller than 10° are not included in the figures. Three kinds of predictions have been made. One is with a perfect interface bonding assumption, another without any SCF of the matrix considered, and the third is incorporated with an interface crack. As expected, the predictions without any SCF are far away from the experiments at most off-axial angles, whereas those with the interface crack incorporated agree the best with the measured data. The perfect bonding assumption for both of the composites results in the predictions lied in between the other two kinds of predictions. Whereas the perfect bonding assumption up to a composite failure for the E-glass fiber system is good enough (Figure 6), the same assumption for the Kevlar fiber system generates significant prediction errors in general (Figure 5). This is because the E-glass fiber system under consideration has a critical transverse load (42.4 MPa) quite close to the transverse tensile strength, 45.3 MPa. On the other hand, the Kevlar fiber system can only sustain a transverse tensile load up to 1.2 MPa before an interface crack, which is very small compared to the transverse tensile strength, 27.7 MPa. This is consistent with a common observation that a Kevlar fiber-reinforced polymer matrix composite generally undergoes a much earlier interface debonding before an ultimate failure.

It is noticed that the three kinds of predictions arrive at the same longitudinal strength for each composite, i.e., 1137 MPa for the Kevlar fiber and 852 MPa for the E-glass fiber composites. Both of them correlate well with the experimental data, i.e., 1142 MPa for the Kevlar composite [53] and 817.5 MPa for the glass composite [52]. However, both of them have already undergone an interface crack (σ̂000= 22.3 MPa for the Kevlar and 725.4 MPa for the glass composites) before the longitudinal strength is attained. Both of the examples confirm that only a transverse tensile load carrying capacity is influenced by an interface crack.

9. Conclusion

Micromechanical failure and strength prediction of a UD composite is systematically described in this chapter. The internal stresses in the fiber and matrix must be calculated at first. Although various methods are available for this purpose, a thorough compassion study has shown that Bridging Model is the most potential owing to its simplicity with closed-form formulae, high accuracy, and the unique feature of consistency in the internal stress calculation. These stresses are homogenized quantities. They must be converted into true values before being used for a failure assessment against the original strength data of the fiber and matrix. Otherwise, a predicted strength of the composite may be far away from the experiment. The difference in the overall prediction accuracies between use of the homogenized and the true stresses can be as large as more than five times. As the homogenized and the true stresses in the fiber are the same, the true stress determination for the matrix becomes essential. It has been demonstrated in the chapter that the true stresses of the matrix under any load condition are obtained by multiplying its homogenized counterparts with SCFs of the matrix in the composites. Such an SCF cannot be determined following a classical way. Instead, it must be defined as a line-averaged stress divided by a volume-averaged quantity. All of the SCFs subjected to various kinds of loading and with a perfect interface bonding have been presented in the chapter. It is known that an interface debonding only has a significant influence on the transverse tensile load carrying ability, and the transverse tensile SCF of the matrix after the interface debonding has also been obtained. The theory is equally well applicable to the failure and strength prediction of any other continuous fiber-reinforced composite, once it is subdivided into a combination of UD composites.

Acknowledgments

Partial financial supports from the National Natural Science Foundation of China with grant numbers of 11832014 and 11472192 are greatly acknowledged.

A.1 Eshelby’s method

The stiffness tensor of the composite by this method is given by [15]

Kij=Sij1=Kijm+VfKijfKijmI+LijSijmKijfKijm1,EA.1

Kijfand Kijmare the stiffness tensors of the fiber and matrix, respectively, and [Lij] is the Eshelby’s tensor reading [16]

Lij=000000L2211L2222L2233000L3311L3322L33330000002L23230000002L13130000002L1212,EA.2
L2211=L3311=νm21νm,L2222=L3333=121νm34+12νm2,L1212=L1313=1/4,
L2233=L3322=121νm1412νm2,L2323=121νm14+12νm2.EA.3

νm is Poisson’s ratio of the matrix.

A.2 Mori-Tanaka method

Non-zero bridging tensor elements of Mori-Tanaka method are given below [54]:

A11=EmE11f1+νmνmν12f1+νm1νm,EA.4
A12=EmE22fνm1ν23f21+νm1νmEmE11fν12f1+νm1νm+νm21νm=A13,EA.5
A21=EmE11fνmν12f21+νm1νm=A31,EA.6
A22=EmE22fv23f38vm1vm+1+EmE11fv12fvm2vm1vm+1+vm+14vm58vm1vm+1=A33,EA.7
A32=EmE22f3v23f18vm1vm+1+EmE11fv12fvm2vm1vm+1+vm+114vm8vm1vm+1=A23,EA.8
A44=GmG23f141vm+34vm41vm,EA.9
A55=Gm+G12f2G12f=A66.EA.10

G23fis the fiber transverse shear modulus.

A.3 Rule of mixture model

By this model, five elastic moduli of the composite are obtained as [19]

E11=VfE11f+VmEm,EA.11
ν12=Vfν12f+Vmνm,EA.12
E22=Em1Vf1Em/E22f,EA.13
G12=G13=Gm1Vf1Gm/G12f,EA.14
G23=Gm1Vf1Gm/G23f.EA.15

A.4 Chamis model

By simply replacing Vf in Eqs. (A.13)(A.15) with Vf, respectively, one obtains the Chamis model’s formulae [20].

A.5 Modified rule of mixture model

Formulae for E11 and ν12 are the same as Eqs. (A.11) and (A.12). The modified formulae for the other three moduli are [19]

E22=4η22G23η22+mG23,m=1+4η22ν122E11,1η22=1Vf+ηkVmVfΛ22f+VmηkΛm,EA.16
1G12=1Vf+η12VmVfG12f+Vmη12Gm,η12=121+GmG12f,EA.17
1G23=1Vf+η23VmVfG23f+Vmη23Gm,η23=141νm34νm+GmG23f,EA.18
ηk=121νm1+ΛmΛ22f,EA.19
Λ22f=0.5K22f+K23f,Λm=0.5K22m+K23m. EA.20

Kijfand Kijmare the stiffness elements of the fiber and matrix.

A.6 Halpin-Tsai formulae

E22=4ΛLG23ΛL+mG23,m=1+4ΛLν122E11,ΛLΛm=1+12νmηVf1ηVf,EA.21
1G12=1Vf+η12VmVfG12f+Vmη12Gm,η12=121+GmG12f,EA.22
1G23=1Vf+η23VmVfG23f+Vmη23Gm,η23=141νm34νm+GmG23f,EA.23
η=Λ22f/Λm1Λ22f/Λm+12νm.EA.24

It is noted that the formulae for E11 and ν12 are the same as Eqs. (A.11) and (A.12), respectively [21].

A.7 Hill-Hashin-Christensen-Lo model

E11=VfE11f+VmEm+4ν12fνm2Vf1VfVfΛm+1VfΛ22f+1Gm,EA.25
ν12=Vfν12f+Vmνm+ν12fνmVf1VfVfΛm+1VfΛ22f+1Gm1Λm1Λ22f,EA.26
E22=20.5/KT+0.5/G23+2ν122/E11,EA.27
G12=GmG12f+Gm+VfG12fGmG12f+GmVfG12fGm,EA.28
KT=Km+Vf1Λ22fΛm+1VfΛm+Gm,EA.29
A1G23Gm2+2BG23Gm+C1=0,EA.30
A1=3VfVm2(GfGm1)(GfGm+ηf)+[GfGmηm+ηfηm(GfGmηmηf)Vf3][Vfηm(GfGm1)(GfGmηm+1)],EA.31
B1=3VfVm2(GfGm1)(GfGm+ηf)+12[GfGmηm+(GfGm1)Vf+1][(ηm1)(GfGm+ηf)2(GfGmηmηf)Vf3]+Vf2(ηm+1)(GfGm1)[GfGm+ηf+(GfGmηmηf)Vf3],EA.32
C1=3VfVm2GfGm1GfGm+ηf+GfGmηm+VfGfGm1+1GfGm+ηf+GfGmηmηfVf3,EA.33
ηf=34ν23f,ηm=34νm.EA.34

Eq. (A.30) is applicable only to composites with an isotropic fiber reinforcement [22].

A.8 Self-consistent model

The self-consistent formulae are represented as follows [15]:

Kij=Kijm+VfKijfKijmMijfEA.35
Mijf=I+L˜ijSijKijfKij1EA.36
L˜ij=SijA˜ijKijfIKijfKij1KijEA.37

where A˜ijis the bridging tensor correlating the homogenized stresses of the composite with those of the fiber in a concentric cylinder assemblage (CCA) model, i.e., a two-phase CCA model, through σi=A˜ijσjf, whose non-zero elements are given by [54]

A˜11=E11E11E22ν12fν12E11fE11E22ν122,EA.38
A˜12=A˜13=E11E11fE221ν23fν12+E22f2E11ν12f+E11fν121+ν232E11fE22fE11E22ν122,EA.39
A˜21=A˜31=E11E22ν12ν12f2E11fE11E22ν122,EA.40
A˜22=A˜33=E11E22f5+ν23+E223ν23f8E22fE11E22ν122E22ν12E11ν12f+E11fν122E11fE11E22ν122,EA.41
A˜23=A˜32=E11E2213ν23f+E22f3ν2318E22fE11E22ν122+E22ν12E11fν12E11ν12f2E11fE11E22ν122,EA.42
A˜44=1+ν23f8E22G23fν122+E11E22+2G23f3ν234E22fE11E22ν122,EA.43
A˜55=A˜66=G12f+G122G12f.EA.44

The self-consistent model is implicit, and an iteration has to be carried out to determine the five effective elastic moduli, E11, E22, G12, ν12, and ν23, of the composite.

A.9 Generalized self-consistent model

Basic equations of the generalized self-consistent model are the same as Eqs. (A.35)(A.37), except that the bridging tensor in Eq. (A.37), A˜ij, correlating the stresses of the composite with those of the fiber is no longer obtained on a two-phase CCA model but on a three-phase CCA one shown in Figure A.1. In the latter case, however, generally non-explicit expressions exist for the bridging tensor elements A˜ij. Solution for the resulting linear algebraic equations is necessary [54].

Figure A.1.

(a) Schematic for generalized self-consistent method. (b) A three-phase CCA model (b→∞) for the generalized self-consistent method.

As pointed out in Ref. [54], a three-phase CCA model (Figure A.1) can be sufficiently well approximated with two step two-phase CCA ones. In the first step, the fiber and matrix phase constitutes a UD composite, whose effective elastic moduli, E11eq, E22eq, ν12eq, G12eq, and ν23eq, can be obtained from Eq. (6) in which the bridging tensor [Aij] is defined by Eqs. (A.4)(A.10). Then, this UD composite is regarded as an equivalent fiber to embed into the composite. The resulting bridging tensor Aijeqcorrelating the stresses of the composite with those of the equivalent fiber is given by Eqs. (A.38)(A.44), providing that E11f, E22f, ν12f, G12f, and ν23finvolved are replaced by E11eq, E22eq, ν12eq, G12eq, and ν23eq, respectively.

From σi=Aijeqσjeqand σif=VfI+VmAij1σjeq, it is obtained that

A˜ijAijeqVfI+VmAij.EA.45

A.10 Double inclusion method (DIM)

This method [4] has been incorporated into a commercial software, Digimat [40], for composites. As any prediction by this method is performed with Digimat, the formulae of the method are omitted.

E-glass
LY556
E-glass
MY750
AS4
3501–6
T300
BSL914C
IM7
8511–7
T300
PR319
AS
epoxy
S2-glass
epoxy
G400–800
5260
E11f(GPa)807422523027623023187290
E22f(GPa)807415151915158719
ν12f0.20.20.20.20.20.20.20.20.2
G12f(GPa)33.3330.8151527151536.327
ν23f0.20.20.070.070.360.070.070.20.357
σu,tf(MPa)215021503350250051802500350028505860
σu,cf(MPa)145014502500200032002000300024503200
Em (GPa)3.353.354.244.080.953.23.23.45
νm0.350.350.340.350.380.350.350.350.35
σu,tm(MPa)808069759970857370
σu,cm(MPa)120120250150130130120120130
σu,sm(MPa)545450705741505257
Vf0.620.60.60.60.60.60.60.60.6

Table B.1.

Mechanical properties of the fibers and matrices of the nine UD composites used in WWFEs [25, 26, 27]

E-glass
LY556
E-glass
MY750
AS4
3501–6
T300
BSL914C
IM7
8511–7
T300
PR319
AS
epoxy
S2-glass
epoxy
G400–800
5260
E11 (GPa)53.545.612613816512914052173
E22 (GPa)17.716.211118.45.6101910
ν120.2780.2780.280.280.340.3180.30.30.33
G12 (GPa)5.835.836.65.55.61.3366.76.94
G23 (GPa)6.325.793.933.932.81.863.356.73.56
σ11u,t(MPa)114012801950150025601378199017002750
σ11u,c(MPa)57080014809001590950150011501700
σ22u,t(MPa)354048277340386375
σ22u,c(MPa)114145200200185125150180210
σ12u(MPa)727379809097707290
σ23u(MPa)505055_5745504057

Table B.2.

Mechanical properties of the nine UD composites used in WWFEs [25, 26, 27]

E-glass
LY556
E-glass
MY750
AS4
3501–6
T300
BSL914C
IM7
8511–7
T300
PR319
AS
epoxy
S2-glass
epoxy
G400–800
5260
By Eshelby’s method
E11 (GPa)50.8145.68136.61139.51167.07138.36139.8153.42175.31
E22 (GPa)7.157.017.307.087.731.985.916.766.52
ν120.280.280.270.270.290.280.270.280.28
G12 (GPa)2.672.613.092.943.070.762.402.522.68
G23 (GPa)2.422.372.602.492.500.672.052.282.19
By Bridging Model
E11 (GPa)50.945.7136.7139.6167.2138.4139.953.5175.4
E22 (GPa)18.116.89.79.611.24.418.716.910.2
ν120.2570.260.2560.260.2720.260.260.260.26
G12 (GPa)6.285.845.545.356.461.824.645.815.8
G23 (GPa)6.245.83.763.663.761.553.295.773.51
By Mori-Tanaka’s method
E11 (GPa)50.945.76136.7139.6167.3138.4139.953.5175.4
E22 (GPa)11.711.028.7578.5739.6653.027.48110.788.473
ν120.2490.2520.260.2570.2670.2520.2560.2520.254
G12 (GPa)4.604.324.534.354.921.303.674.234.36
G23 (GPa)4.063.833.323.213.231.062.773.722.92
By rule of mixture method
E11 (GPa)50.8745.74136.7139.6167.2138.38139.8853.5175.4
E22 (GPa)8.2527.847.3947.147.7152.1696.0617.58176.779
ν120.2570.260.2560.260.2720.260.260.260.26
G12 (GPa)3.082.923.393.233.420.852.652.822.99
G23 (GPa)3.082.922.932.812.810.822.362.822.51
By Chamis method
E11 (GPa)50.8745.74136.7139.6167.2138.38139.8853.5175.4
E22 (GPa)13.6412.869.4969.2610.4153.4618.19212.6049.425
ν120.2570.260.2560.260.2720.2720.260.260.26
G12 (GPa)5.134.835.124.915.521.454.144.734.88
G23 (GPa)5.134.833.933.813.801.333.334.733.49
By modified rule of mixture method
E11 (GPa)50.8745.74136.7139.6167.2138.38139.8853.5175.4
E22 (GPa)11.6110.938.658.469.532.987.3710.718.35
ν120.2570.260.2560.260.2720.2720.260.260.26
G12 (GPa)4.604.324.544.354.921.293.674.234.35
G23 (GPa)4.063.823.323.213.231.062.773.732.91
By Halpin-Tsai formulae
E11 (GPa)50.8745.74136.7139.6167.2138.38139.8853.5175.4
E22 (GPa)11.6911.08.768.579.663.027.4810.778.47
ν120.2570.260.2560.260.2720.2720.260.260.26
G12 (GPa)4.604.324.544.354.921.293.674.234.35
G23 (GPa)4.063.823.323.213.231.062.773.732.91
By Hill-Hashin-Christensen-Lo method
E11 (GPa)50.945.8136.7139.6167.3138.4139.953.5175.4
E22 (GPa)12.912.011.85
ν120.2490.2520.2530.2570.2670.2520.2560.250.25
G12 (GPa)4.64.324.544.354.921.293.674.234.35
G23 (GPa)4.654.334.25
By self-consistent method
E11 (GPa)50.9445.81136.72139.65167.31138.40139.9253.55175.43
E22 (GPa)18.9116.809.148.9910.374.198.0617.399.33
ν120.2310.2350.2500.2540.2620.2380.2510.2330.247
G12 (GPa)11.349.806.376.259.364.185.8210.948.98
G23 (GPa)6.966.153.533.433.521.553.066.363.25
By generalized self-consistent method
E11 (GPa)50.945.8136.7139.6167.3138.4139.953.5175.4
E22 (GPa)12.8712.038.938.7710.13.277.7211.88.85
ν120.2490.2520.2530.2570.270.250.2560.250.254
G12 (GPa)4.64.324.544.34.91.23.64.24.35
G23 (GPa)4.654.333.423.323.421.192.94.253.09
By double-inclusion method (Digimat [40])
E11 (GPa)50.947.2141.1144.2172.8143144.555.2181.2
E22 (GPa)16.215.99.359.210.54.118.2616.19.48
ν120.2340.2340.2480.2520.2570.2380.2490.2340.244
G12 (GPa)6.736.5855.85.637.122.1356.656.46
G23 (GPa)5.785.673.643.543.551.513.165.73.28
By FE-square fiber array
E11 (GPa)50.945.8136.7139.6167.3138.4139.953.5175.4
E22 (GPa)16.2614.99.549.4210.883.988.4514.869.63
ν120.2460.250.2520.2560.2660.250.2550.2490.252
G12 (GPa)4.964.584.684.55.151.383.824.54.57
G23 (GPa)6.495.893.793.713.791.583.325.893.47
By FE-hexagonal fiber array
E11 (GPa)50.8945.77136.70139.56167.26138.38139.9053.50175.37
E22 (GPa)12.6011.728.898.729.893.197.6611.518.68
ν120.2490.2510.2530.2550.2670.2590.2560.2510.252
G12 (GPa)4.624.324.544.354.911.303.674.224.35
G23 (GPa)3.034.183.403.293.321.142.864.073.01
By FE-square diagonal fiber array
E11 (GPa)50.8945.77136.71139.56167.30138.42139.8853.51175.43
E22 (GPa)10.409.858.308.099.032.717.129.607.92
ν120.2480.2500.2510.2550.2640.2510.2600.2500.255
G12(GPa)4.874.564.684.505.161.383.824.484.58
G23 (GPa)2.593.253.062.942.950.902.503.152.65
By FE-random fiber array
E11 (GPa)50.9045.77136.71139.37167.27138.37139.9053.51175.41
E22 (GPa)13.7612.798.928.769.973.437.7312.778.84
ν120.2410.2450.2480.2550.2630.2410.2520.2430.250
G12 (GPa)4.584.294.424.334.691.293.604.214.29
G23 (GPa)5.084.743.483.533.431.282.974.693.12

Table B.3.

Predicted elastic moduli of the nine UD composites by different models.

E-glass
LY556
E-glass
MY750
AS4
3501–6
T300
BSL914C
IM7
8511–7
T300
PR319
AS
epoxy
S2-glass
epoxy
G400–800
5260
Eshelby’s method
λ11.5771.6231.6481.6501.6541.6631.6531.6311.655
λ21.3701.3221.2041.2051.2471.3081.2341.3241.270
λ31.3011.2571.2201.2181.2011.2551.2281.2591.225
λ41.1691.1311.1231.1241.1301.1331.1261.1321.130
Bridging Model
λ11.5731.6181.6461.6481.6501.6621.6511.6271.654
λ20.4420.4530.6210.6120.5770.4670.5760.4460.554
λ30.4420.4530.6210.6120.5770.4670.5760.4460.554
λ40.4380.4490.4980.4940.4600.4360.4790.4430.454
Mori-Tanaka’s method
λ11.5711.6161.6471.6471.6501.6621.6511.6251.653
λ20.7930.8010.8680.8670.8550.8070.8520.7970.841
λ30.7340.7390.8000.7930.7820.7430.7800.7380.782
λ40.6350.6440.6740.6700.6500.6360.6610.6400.647
Rule of mixture method
λ11.5731.6181.6461.6481.6501.6621.6511.6271.654
λ21.3041.3031.6611.7551.7251.3521.5761.3041.418
λ31.0011.0021.0001.0011.0000.9991.0001.0000.998
λ41.0001.0011.0001.0001.0001.0001.0001.0001.000
Chamis method
λ11.5731.6181.6461.6481.6501.6621.6511.6271.654
λ20.7200.7240.9250.9770.9640.7610.8820.7260.796
λ30.5600.5640.5640.5640.5640.5630.5640.5640.562
λ40.5600.5640.5630.5630.5640.5640.5630.5640.564
Modified rule of mixture method
λ11.5731.6181.6461.6481.6501.6621.6511.6271.654
λ20.8080.8130.9570.9660.9340.8400.9330.8110.890
λ30.7340.7410.8000.7930.7800.7420.7790.7370.785
λ40.6350.6430.6720.6710.6500.6380.6620.6400.648
Halpin-Tsai formulae
λ11.5731.6181.6461.6481.6501.6621.6511.6271.654
λ20.7940.8000.8670.8700.8600.8090.8560.8000.839
λ30.7340.7410.8000.7930.7800.7420.7790.7370.785
λ40.6350.6430.6720.6710.6500.6380.6620.6400.648
Hill-Hashin-Christensen-Lo method
λ11.5711.6161.625
λ20.7270.7550.745
λ30.6360.6420.636
λ40.6350.6430.640
Self-consistent method
λ11.5671.6121.6451.6461.6491.6621.6501.6221.653
λ20.4590.4960.8060.7950.7640.5490.7550.4710.713
λ30.3850.4200.7100.6990.6610.4650.6570.3960.644
λ40.1970.2240.3950.3820.2720.1550.3380.1950.250
Generalized self-consistent method
λ11.5711.6161.6461.6471.6501.6621.6511.6251.653
λ20.7920.7990.8700.8670.8540.8090.8570.7980.839
λ30.7340.7400.8000.7930.7800.7420.7790.7380.785
λ40.6350.6430.6730.6710.6500.6380.6620.6400.648
Double inclusion method (Digimat)
λ11.5681.6171.6471.6481.6501.6621.6521.6261.654
λ20.5430.5170.7660.7580.7290.5590.7210.5020.679
λ30.4850.4650.6660.6570.6490.4810.6200.4530.633
λ40.4020.3860.4630.4560.4040.3630.4290.3760.396
FE-square fiber array
λ11.5701.6161.6451.6471.6491.6621.6511.6251.653
λ20.6160.6350.7730.7690.7440.6500.7350.6300.721
λ30.4210.4440.6120.5960.5660.4540.5650.4360.568
λ40.5820.6000.6430.6390.6140.5930.6280.5960.611
FE-hexagonal fiber array
λ11.5711.6161.6461.6461.6501.6621.6511.6251.653
λ20.2950.7660.8530.8500.8250.7750.8280.7600.815
λ31.0190.6690.7650.7560.7410.6770.7370.6670.742
λ40.6330.6430.6730.6710.6510.6360.6620.6410.647
FE- FE-square diagonal fiber array
λ11.5711.6161.6451.6461.6491.6621.6511.6251.653
λ20.4540.8560.9320.9280.9210.8640.8090.8560.898
λ31.2100.8900.9280.9260.9190.8930.9180.8870.916
λ40.5940.6040.6430.6400.6130.5930.6280.5990.609
FE-random fiber array
λ11.5701.6151.6451.6471.6491.6621.6511.6251.653
λ20.6600.6760.8300.8260.8020.6940.7980.6620.777
λ30.5660.5780.7310.6620.6950.5920.6920.5690.693
λ40.6110.6210.6060.6010.6340.6090.6500.6150.629

Table B.4.

The coefficients λi’s for the nine composites by different models.

Download

chapter PDF

© 2018 The Author(s). Licensee IntechOpen. This chapter is distributed under the terms of the Creative Commons Attribution 3.0 License, which permits unrestricted use, distribution, and reproduction in any medium, provided the original work is properly cited.

How to cite and reference

Link to this chapter Copy to clipboard

Cite this chapter Copy to clipboard

Zheng-Ming Huang (November 5th 2018). Micromechanical Failure Analysis of Unidirectional Composites [Online First], IntechOpen, DOI: 10.5772/intechopen.80807. Available from:

chapter statistics

201total chapter downloads

More statistics for editors and authors

Login to your personal dashboard for more detailed statistics on your publications.

Access personal reporting

We are IntechOpen, the world's leading publisher of Open Access books. Built by scientists, for scientists. Our readership spans scientists, professors, researchers, librarians, and students, as well as business professionals. We share our knowledge and peer-reveiwed research papers with libraries, scientific and engineering societies, and also work with corporate R&D departments and government entities.

More about us