Argyrakis, C

Leevers, PS

Özbek, P

Polymer Testing

English

Instrumented three-point bend impact fracture tests are widely used to evaluate pipe grade polymers. Often specimens cut from small-diameter pipe are used, and these are necessarily arc-shaped. Because the orientation and thermal history may differ between extruded pipe and compression moulded plaque material, this additional difference in geometry must be properly accounted for, or it may mask any effects on material properties. This paper modifies a previously published solution for the geometry-dependent energy correction factor for arc-shaped specimens, and extends it to a wider range of standard pipe geometries. When the results are properly corrected, the effects of processing on a commercial PE100 appear to be minor.Accepted versio

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Fracture mechanics analysis of arc shapedspecimens for pipe grade polymersPemra Özbek, Christos Argyrakis and Patrick LeeversDepartment of Mechanical Engineering, Imperial College London, LondonSW7 2AZ, UKAbstractInstrumented three-point bend impact fracture tests are widely used to evaluatepipe grade polymers. Often specimens cut from small-diameter pipe are used,and these are necessarily arc-shaped. Because the orientation and thermal his-tory may differ between extruded pipe and compression moulded plaque ma-terial, this additional difference in geometry must be properly accounted for,or it may mask any effects on material properties. This paper modifies a previ-ously published solution for the geometry-dependent energy correction factorfor arc-shaped specimens, and extends it to a wider range of standard pipe ge-ometries. When the results are properly corrected, the effects of processing ona commercial PE100 appear to be minor.Key words: Polymer Pipe, Arc shaped specimen, Fracture, Impact, Single edgenotch bend, Geometry factor, Energy correction factor, Compliance1 IntroductionExtruded pipe is one of the most firmly established high-volume appli-cations for a number of thermoplastics. Because even the toughest unre-inforced thermoplastics are susceptible to fracture under conditions ofhigh constraint and high strain rate, one of the most widely used criteriafor evaluating them is their resistance to impact fracture. Even if impactis not the most likely of threats in service, it is regarded as imposing themost critical and decisive conditions on the material.In Europe the most commonly used impact test method is the Charpythree-point bend impact test, using a notched straight bar specimen. Formaterials which fracture (rather than bending or tearing), the ISO 17281Instrumented Charpy Test method allows the energy dissipated by thePreprint submitted to Elsevier 11 July 2009various failure modes involved to be much more finely distinguished andquantified by geometry-independent parameters, providing a better toolfor resin development. With advances in recording equipment and in theuse of fracture mechanics, the data obtained are becoming more reliable,and the analysis easier. However, intrinsic mechanical filtering normallylimits the impact speed to 1 m/s, which is lower than that of a pendulumCharpy test.According to linear elastic fracture mechanics (LEFM) the impact fractureresistance (or critical strain energy release rate), Gc is given byGc UBWa=W(1)where U is the stored energy at crack initiation, B the specimen thickness(assumed to be uniform), W is the width of the specimen in the crackgrowth direction and  a geometry factor, related to the compliance by  CdC=da=W(2)Clearly, the reliability of Gc depends on the accuracy of a=W. Forstraight SEN(B) specimens, a=W evaluations for various geometriesare well established [1] and are tabulated in ISO 17281.The extrusion and cooling process history during pipe production mayrender the properties of pipe-grade polyethylene substantially differentfrom those of the compression or injection moulded plaques from whichSEN(B) specimens are cut [2,3]. It is therefore much more relevant to testspecimens cut from pipe, and for small-diameter pipe these must be arc-shaped (Fig. 1). For specimens of this shape,  values are less securelyestablished.Niglia [4] derived an expression for the geometry factor  by combiningthe fracture mechanics calibration functions tabulated in ASTM 399-90with compliance results from finite element (FE) analysis. Similar meth-ods have since been used by Nezbedová et al. [5,6] to analyse sandwich-structured specimens made from multilayer pipe. However, using Niglia’sresults, we determined Gc values for pipe-grade polyethylenes which dif-fered from those using ‘straight’ specimens to an apparently inexplicabledegree. The objective of the present study was to investigate whether theFE analysis and the boundary conditions could be made more realistic.It also seemed desirable to obtain calibrations for a wider range of pipediameter and thickness dimensions relative to the specimen span and2depth. The dimensions of plastic pipe are defined by the outside diame-ter D and the Standard Dimension Ratio of D to minimum thickness.2 AnalysisIn LEFM, the influence of specimen geometry on fracture is treated ineither of two conventional frameworks. The Irwin stress intensity factor,K  Ypa (3)for a crack of length a depends on the applied load P and, through adimensionless parameter Y , on the specimen geometry. For a given two-dimensional specimen shape of constant thickness B the applied loadis expressed as an applied stress   P=BX where X is a suitable in-plane dimension: often the length W at which the crack would meet theopposite free surface. The strain energy release rate or crack driving forceparameter is given by the Irwin-Kies relationshipG  12P2dCdA(4)where the specimen geometry determines the functional dependence Caof load point compliance on crack length. The K and G parameters are in-terrelated via Young’s modulus E byK2  E0G (5)where E0  E under plane stress and E0  E=1   2 under plane strainconditions,  being Poisson’s ratio. Relating Eqs. 3 and 5 givesEP22BdCda Y 2 2a (6)For the SEN(B) specimen, it is conventional to express Y in terms of thenominal surface bending stress [1] so that:  32SWPBW(7)where S is the span and W is the width of the specimen. RearrangingEq. 6 allows the Y factor to be determined from a compliance calibration3Ca=WY 2aW BE02 S=W2dCda=W(8)where E0BCa=W depends only on the 2D shape of the body. Alterna-tively, Eq. 2 can be used to determine  from Y , having evaluated thecompliance by integrating Eq. 8 to giveC  2BE0SW2 ZY 2aWdaW C0: (9)Here, C0 is the integration constant, representing the uncracked compli-ance and can be found through finite element analysis (Table 1) or exper-imental measurements.For an arc-shaped, single edge notched bend geometry, ASTM E 399-90gives the stress intensity factor (K) in terms of two geometric functions,(ha=W and fa=W), which are defined for two different span to widthratios (S=W  3 and 4). Using these relations K can be determined byK  PSBW 3=21 1  rhaWfaW; (10)where r is the ratio of the inner to outer diameter of the pipe. From Eqs.5 and 10, one can define Y byY  23aW 1=2 1 1  rhaWfaW(11)which is used to determine compliance by Eq. 9 and hence  via Eq. 2.3 CalculationsThe arc-shaped SEN(B) specimen geometry studied here was based onASTM E 399-90 (Fig. 1). To evaluate the compliance of this specimen, theintegral part of Eq. 9 was determined symbolically using the MATLAB 7package. By definition, the integral constant, C0, is the compliance of anunnotched specimen, and to determine it FE analysis was used [5,6].Modelling of the problem included the design and evaluation of differentexperimental geometries. Having a variety of 8-node finite elements (shell,4aWr2r10.1WSFig. 1. Arc shaped geometry dimensions according to ASTM E 399-90quad, plane stress) that could be applied to the current problem, it iscrucial to choose a mesh which can reflect the real situation as preciselyas possible. The mesh chosen was mapped, in order to have more degreesof freedom around the areas that had very small curvature. The numberof elements used was 2,000 for 8-node plane stress (quad elements) and4,000 using triangular elements. The differences between results fromthese two forms was very smalland by varying the number of elements(h-method) the overall compliance value changed by less than 3%. Due tosymmetry, only half of the domain needed to be modelled. In the modelused by Niglia [4], lateral displacements were assumed to be zero notonly on the plane of symmetry (the crack plane) but also at the supports.However, polymer specimens are very compliant, and the assumption thatthey do not slip laterally on the support points was not supported byexperimental observation. With the aim of improving the accuracy of theFE model, displacements on the support points were constrained onlyvertically.Table 1Integral Constant values, C0EB, a=W  0S=W=3 S=W=4 S=W=6C0E0B 12.8 22.6 69.6The un-cracked compliance values are then used in Eq. 9 together with theintegration function to determine  according to Eq. 2. It is also possibleto determine  by fitting a polynomial equation to each set of FE resultsshown in Fig. 2. This polynomial can then be used to calculate the overallcompliance value in Eq. 2 in order to determine the energy correctionfactor. As seen in Fig. 3, the two approaches agree well, giving confidence52502001501005000 0.2 0.4 0.6 0.8S/W = 3S/W = 4S/W = 6Dimensionless load point compliance, E′BCDimensionless crack length, a/WFig. 2. Dimensionless compliance values computed for various S/W ratios by FEanalysisin the use of FE results for further analysis.0.2 0.4 0.6 0.8Dimensionless crack length, a/W0.70.60.50.40.30.20.10Energy correction factor, φS/W = 4S/W = 3ASTM 399-90Finite element analysisFig. 3. Comparison between FE approach and tabulated functionsSince the equations are defined in the standard only for two geometries(S=W  3 and 4), two approaches were used to calcualte results for S=W 6 . The first approach was simply to linearly interpolate the coefficients ofthe fitting polynomial, as Williams [1] did for the original straight SEN(B)geometry. In order to check the validity of this linear exprapolation, was calculated using Eq. 2 from the overall compliance (C) of S=W  6 byfitting a polynomial equation to the FE results shown in Fig. 2. Fitting thethird-order polynomial  A0 A1aWA2aW2A3aW3(12)6to these curves gives, for SDR 11, the constants An shown in Table 2.Table 2Polynomial coefficients for Eq. 12, linearly extrapolated for S=W  6S=W  3 S=W  4 S=W  6A0 0:99 1:09 1:29A1  2:89  3:15  3:66A2 3:80 4:02 4:44A3  2:00  2:05  2:16As Figure 4 shows, the  values obtained by those two approaches agreereasonably well.0.60.40.200.810 0.2 0.4 0.6 0.8Dimensionless crack length, a/WEnergy correction factor, φArc-shaped (extrapolated)Arc-shaped (FE analysis)StraightFig. 4. Energy correction factor for straight and arc-shaped SEN(B) specimenswith S=W  6Also shown on Fig. 4 is the Williams [1] energy correction factor forstraight SEN(B) specimens. This emphasises that for shallow notch depthsthe arc shaped specimen is much more compliant than the straight spec-imen, due to the shallow cross section above the supports (Fig. 1), givingit greater capacity to store energy for a given Gc. As a result, we mightexpect the the arc-shaped specimen to show a higher transition temper-ature for a given material, since more ductile energy absorption will beneeded to stop an unstable crack before it breaks the free surface.Calculations were repeated for radius ratios r corresponding to standardSDR values 17.6, 13.6 and 9. The results are given in Table 3 in the di-mensionless form C0EB. The geometry factor () was then determined as7a function of a=W for each r at S=W ratios of 3 and 4 and the resultswere extrapolated to S=W  6, which are shown in Fig. 5.Table 3Uncracked compliance of arc-shaped specimens from pipes of various geome-tries, C0EBSDR S=W  3 S=W  49 9.10 18.613.6 15.1 26.917.6 18.1 35.1SDR 17.6, r = 0.885SDR 13.6, r = 0.853SDR 11, r = 0.818SDR 9, r = 0.77610.80.60.40.20.2 0.4 0.6 0.80Dimensionless crack length, a/WEnergy correction factor, φ(a)SDR 17.6, r = 0.885SDR 13.6, r = 0.853SDR 11, r = 0.818SDR 9, r = 0.77610.80.60.40.20.2 0.4 0.6 0.80Dimensionless crack length, a/WEnergy correction factor, φSDR 17.6, r = 0.885SDR 13.6, r = 0.853SDR 11, r = 0.818SDR 9, r = 0.77610.80.60.40.20.2 0.4 0.6 0.80Dimensionless crack length, a/WEnergy correction factor, φ(b) (c)Fig. 5. Energy corrections for arc-shaped specimens of span/depth ratio (a) 3(b) 4 and (c) 6, for diameter ratios r corresponding to pipe of various standarddimension ratios (SDR).Figure 6 illustrates that the energy calibration factor  values finallycalculated here are much higher than those derived by Niglia [4], espe-cially for small a=W ratios (short notches). This is due to the differencein boundary conditions. Releasing the spurious lateral constraints previ-ously applied at the support points substantially increases the uncrackedload-point compliance. If the support points were in fact to be laterallypinned, the lateral stress would substantially reduce the crack drivingforce at all notch depths: only by removing the lateral constraint is it8possible to assume that the Y factor is identical to that for a straightspecimen.0.2 0.4 0.6 0.8Dimensionless crack length, a/W0.70.60.50.40.30.20.10Energy correction factor, φS/W = 4 (Niglia et al.)S/W = 4 (this analysis)Fig. 6. Comparison of the present energy correction factor with that of Niglia [4]4 ExperimentalUsing these results, the impact fracture resistance (Gc) of the same ma-terial was compared for three different SEN(B) specimen geometries: anarc-shaped one cut from commercial pipe, a compression moulded arc-shaped one and a compression moulded straight one. The objective wasto distinguish the effect of processing conditions from that of specimengeometry.A pipe-grade polyethylene of strength class PE 100, provided in gran-ular form, was compression moulded using a hydraulically driven hotpress with electrically heated platens. The material was an unpigmentedmodified high density (949 kg m 3) grade of weight-average molecularweight 257 kg mol 1. The granules were left to melt at 160C for 25 minunder low pressure, and then a pressure of 10 MPa was applied for 5minutes in order to release trapped air and excess material. To let thecrystalline phase approach its equilibrium structure, the mould was thenleft to cool in the machine under 10 MPa pressure until the temperaturereached 60C.For the straight SEN(B) specimens, 12 mm thick plate was obtained bycompression moulding according to ASTM standard D-1928-96. A flashtype picture frame type mould of length 200 mm, width 200 mm andthickness 12 mm, with thick walls to minimise excess edge heat loss dur-9ing cooling, was used. From these plaques, impact bend test specimenswere prepared with dimensions B  6, W  12 and l  70 mm. For thepipe specimens, samples were directly cut from the cross section, giv-ing an arc-shaped geometry with the dimensions of B  5, W  10 andl  70 mm, and with the initial notch extending radially from the in-side surface. To obtain arc-shaped specimens with compression-mouldedmaterial properties, a special compression mould for segment-shapedplaques was constructed, so that cooling conditions in the crack planewere essentially ‘radial only’.From these plaques, the specimens were machined to achieve an arc-shaped geometry matching the nominal dimensions of those from pipe.All specimens were notched to 25% of their thickness with a fresh ra-zor blade, according to ISO 17281, paying attention to minimise plasticdeformation near the notch. Specimens were tested according to the stan-dard across a wide range of temperature, using a conditioning chamberfor temperature control and a digital oscilloscope for data recording. Foreach test Gc was determined from the energy up to peak load, Up, usingEq 1.The results are compared in Fig. 7. The arc-shaped specimen results ob-tained using the original (i.e. uncorrected)  calibration are not plotted;however, the amplitude of the correction now made can be inferred from6. Results from all geometries are now broadly consistent, those fromarc-shaped specimens obtained by compression moulding and from ex-trusion being virtually indistinguishable.121086420-30 -20 -10 0 10 20Impact fracture resistance, Gc (kJ/m2 )Temperature (°C)Arc-shaped (compression moulded)Arc shaped (extruded pipe)Straight (compression moulded)Fig. 7. Impact fracture toughness of the same PE100 material measured usingthree different specimen types105 ConclusionThe determination of impact fracture resistance using instrumented im-pact fracture toughness testing of arc-shaped specimens according to ISO17281 has been reviewed. New evaluations of the ISO 17281 geometryfactor  have been made using existing tabulated functions and new FEresults for the uncracked specimen compliance, based on more realisticboundary conditions. A pipe grade polyethylene, tested using ISO 17281and analysed using the new calibrations, showed considerably better con-sistency in Gc between different geometries.References[1] J. Williams. Fracture Mechanics of Polymers. Ellis Horwood, Chichester UK,1987.[2] P. Davis. Process/property interactions in the new polyethylenes. PhD thesis,University of London, 1999.[3] R. K. Krishnaswamy, P. S. Leevers, M. J. Lamborn, A. M. Sukhadia, D. F.Register, and P. L. Maeger. Rapid crack propagation (RCP) failures in HDPEpipes: structure-property investigations. Polymer Engineering and Science,46:1358–1362, 2006.[4] J. Niglia, A. Cisilino, R. Seltzer, and P. Frontini. Determination ofimpact fracture toughness of polyethylene using arc-shaped specimens.Engineering Fracture Mechanics, 69:1391–1399, 2002.[5] E. Nezbedová, Z. Knesl, and B. Vlach. Determination of impact fracturetoughness of polyethylene using arc-shaped specimens. Plastics, Rubberand Composites, 36(5):207–212, 2007.[6] J. Niglia, A. Cisilino, R. Seltzer, and P. Frontini. Determination of impactfracture toughness of polyethylene using arc-shaped specimens. Strengthof Materials, 40(1):134–137, 2008.11

Fracture mechanics analysis of arc shaped specimens for pipe grade polymers

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Fracture mechanics analysis of arc shaped specimens for pipe grade polymers

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