IN
DEGREE PROJECT MECHANICAL ENGINEERING, SECOND CYCLE, 30 CREDITS
STOCKHOLM SWEDEN 2020 ,
Fatigue Testing of a Unidirectional Carbon Fiber Reinforced Polymer
Investigation of damage development using Digital Image Correlation
LARS JOHAN WENNER BERG
KTH ROYAL INSTITUTE OF TECHNOLOGY
SCHOOL OF ENGINEERING SCIENCES
Utmattningstest av en enkelriktad
kolfiberförstärkt polymer
LARS BERG
Aerospace Engineering Date: December 14, 2020 Supervisor: Per Wennhage Examiner: Zuheir Barsoum
School of Industrial Engineering and Management Host company: Scania CV AB
Swedish title: Utmatting av komposit
iii
Abstract
Carbon Fibre Reinforced Plastic (CFRP) is a material with high specific proper- ties and good fatigue and vibration dampening characteristics, and can potentially be used instead of steel and aluminium in heavy duty vehicles. This work fo- cuses on testing methodology and the fatigue properties of a unidirectional (UD) material in the 0° and 90°orientation, reproducing and validating the method de- veloped by Wanner[1]. While conducting a fatigue test of a CFRP composite in tension-tension fatigue, in-situ strain measurements were performed to examine the gradual elongation of the specimen (as this relates to stiffness loss, i.e. fatigue damage). An imaging methodology capturing the specimen at peak loading has been developed, including a trigger mechanism that activates the camera at the de- sired time and cycle count, as well as a method of extracting the photograph of the specimen at maximum displacement, allowing for peak-to-peak comparison.
A method improving specimen production output and consistency has been de- veloped. SN-curves have been produced for both 0° and 90° fibre orientations.
Micrography of sectioned specimen has been conducted. The study finds the fa-
tigue limit of the 0° specimen to be as high as 80 % of the material tensile fail-
ure strength, while results from the 90° study indicate a lower but inconclusive
value. An attempt at qualitatively determining the factors causing the material be-
haviour has been made and is deliberated upon.
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Sammanfattning
Kolfiberförstärkt plast (CFRP) är ett material med höga specifika mekaniska egen-
skaper och goda utmattnings- och vibrationsdämpande egenskaper, och kan poten-
tiellt ersätta stål och aluminium i fordonsstrukturer. Detta arbete fokuserar på test-
metodik och utmattningsegenskaperna för ett enkelriktat material (UD) i 0° och
90° orientering, reproduktion, validering och utveckling av metoden utvecklad av
Wanner [1]. Under genomförande av utmattningsprovning av en CFRP-komposit i
drag belastning utfördes töjningsmätningar på plats för att undersöka den gradvisa
töjningen av provet (eftersom detta avser styvhetsförlust, dvs utmattningsskada). En
avbildningsmetodik som fångar provet vid toppbelastning har utvecklats, inklusive
en utlösningsmekanism som aktiverar kameran vid önskad tid och cykelantal, samt
en metod för att extrahera fotografiet av provet vid maximal förskjutning, vilket
möjliggör jämförelse vid olika cykelantal. En metod som förbättrar provstavspro-
duktion och kvalitet har utvecklats. S-N kurvor har skapats för både 0° och 90° fiber-
orientering. Mikrografi av snittprov har utförts. Studien indikerar at utmattnings-
gränsen för provet i 0° kan vara så hög som 80 % av materialets dragfasthållfasthet,
medan resultaten från 90° studie indikerar ett lägre men tvetydigt värde. Ett försök
att kvalitativt bestämma de faktorer som orsakar det materiella beteendet har gjorts.
v
Acknowledgements
I wish to express deep gratitude to Sara Eliasson for her invaluable cooperation, patience and tutelage during this project, as well as to Associate Prof. Per Wennhage and Prof. Zuheir Barzoum for their insight and leadership.
I wish to thank Scania CV AB and KTH for providing me the opportunity to conduct this study and for helping in its realisation.
Lastly I wish to to thank Anders Beckman and Monica Norrby for their
assistance and solutions in the LWS lab, and Johan Nygren, Johan Larsson
as well as the entire Weld and Composite Mechanics Group for their
inclusion and input on this challenging topic.
Contents
1 Introduction 1
1.1 Purpose of study . . . . 1
1.2 Fatigue . . . . 2
2 Literature review 3 2.1 Reference litterature . . . . 3
2.2 Digital image correlation . . . . 7
3 Methodology 10 3.1 Introduction . . . . 10
3.2 Test material . . . . 11
3.3 Specimen manufacturing . . . . 12
3.4 Static testing . . . . 15
3.5 Fatigue testing . . . . 17
3.5.1 Out-of-plane twist . . . . 17
3.5.2 Clamping grips . . . . 18
3.5.3 Ramp testing . . . . 18
3.5.4 Fatigue process . . . . 19
3.6 DIC capture . . . . 19
3.6.1 Photography . . . . 21
3.6.2 Verification . . . . 22
3.6.3 Failure types . . . . 23
3.7 Micrography . . . . 23
4 Results 25 4.1 Overview . . . . 25
4.1.1 Camera trigger mechanism . . . . 25
4.2 DIC post processing . . . . 30
4.2.1 Peak determination . . . . 30
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CONTENTS vii
4.3 Fatigue test results . . . . 32
4.4 Fatigue S-N Curves . . . . 34
4.5 0
◦DIC fatigue measurements . . . . 35
4.6 90
◦DIC fatigue measurement . . . . 36
4.7 1-FA-6 displacement and strain . . . . 36
4.8 Migrographs . . . . 37
5 Discussion 38 5.1 Overview . . . . 38
5.1.1 Fatigue results . . . . 38
5.1.2 DIC . . . . 39
5.1.3 Micrography . . . . 41
5.1.4 Sources of error and uncertainty . . . . 41
6 Conclusion 43 6.1 Overall impressions . . . . 43
6.1.1 On the viability of 2D-DIC . . . . 43
6.2 Suggested improvements . . . . 44
Bibliography 47 A Test manual 50 A.1 Notes on 2D-DIC testing . . . . 50
A.1.1 Procedure . . . . 50
A.1.2 Camera placement and RBM verification . . . . 52
A.1.3 Camera Trigger . . . . 54
A.1.4 Camera control software . . . . 56
A.1.5 Specimen preparation and speckle pattern . . . . 56
A.1.6 Illumination . . . . 57
B Arduino Setup 59
C Arduino Code 60
Nomenclature
AOI Area of Interest AWJ Abrasive Water Jet
CFRP Carbon Fibre Reinforced Plastic FLD Fatigue Life Diagram
GFRP Glass Fibre Reinforced Plastic HDV Heavy Duty Vehicle
LVDT Linear Variable Differential Transformer RBM Rigid Body Motion
UD Unidirectional (Fibre Orientation) UI User Interface
USB Universal Serial Bus UTS Ultimate Tensile Stress
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Introduction
1.1 Purpose of study
CFRP is a lightweight yet strong, stiff and durable material that has a growing application in the automotive industry. Lower vehicle mass equates to lowered energy requirements and fuel consumption, increased payload, and better perfor- mance. In addition to its high specific strength and stiffness[2], it can also exhibit a higher fatigue resistance than current alternatives in certain configurations[3].
High tensile strength steels typically have a fatigue limit in the range of 30 to 60 % of the Ultimate Tensile Strength (UTS)[4]. Unidirectional (UD) Carbon Fibre Reinforced Plastics (CFRP) regularly perform significantly better than this, and given that a modern truck is designed to a great extent against fatigue failure, its potential implementation in a Heavy Duty Vehicle (HDV) is of interest to Scania.
Whereas our understanding and modelling of the fatigue behaviour of metals has reached a mature level, modelling this behaviour for CFRP is still challenging, and more physical testing is required in order to develop and validate fatigue models. Other challenges also remain to be solved before widespread adoption of CFRP can occur in HDVs. This pertains to several phases in the life cycle of such a vehicle, from design and production, to maintenance and recycling. This work however, focuses on measuring and validating numerical fatigue models and the fatigue performance of a certain CFRP material already used in an automotive application, incorporating 2D Digital Image Correlation (2D-DIC) to measure strain in the sample over the course of testing, and investigating the damage that occurs.
validate numerical fatigue models
1
2 CHAPTER 1. INTRODUCTION
1.2 Fatigue
Fatigue is the process by which mechanical properties of a material degrade due to repeated loading. The magnitude of this cyclic loading and resulting stress may be much lower than that which would induce plastic changes or failure for a single loading. For instance, a truck axle routinely experiencing stresses half its failure stress, may experience fatigue failure after a certain amount of cycles. For an isotropic material such as a metal, this can occur due to imperfections present in the material, which either lowers the local material strength, or creates a stress concentration such that it is exceeded. These preconditions are necessary for what is known as crack growth to occur, and when it does, a physical discontinuity or crack, initiates. If conditions allow, this crack will propagate, the stress will be redistributed (and increase), ensuring further crack growth, typically in a direction perpendicular to the main tensile axis[4]. There are more or less two views on this phenomenon; one microscopic, focused on modelling of the crack geometry and conditions in an attempt to predict the rate of crack growth, as well as a macroscopic view - one in which statistical data is produced based on serial tests of standard geometries. This thesis work is conducting the latter.
Whereas fatigue damage to an isotropic material may be largely characterised by
a single parameter (crack growth), a composite exhibits a multitude of damage
mechanisms due to its inhomogenous nature. For a CFRP the material stiffness
and strength properties of each constituent typically differ by an order of magni-
tude in favour of the fibre, and the failure strain of the matrix is usually significantly
higher. The prevailing damage mechanisms differ in each constituent and at their
boundaries. A local failure in one constituent (for instance a single fibre break-
age) and the resulting redistribution of load may lead to a wholly different mode of
failure occurring elsewhere in the composite[5]. On the contrary, the redistributed
load may lead to a load scenario where damage growth is restrained, an example of
this would be the scenario where a progressing matrix crack is restrained (or pre-
vented from coalescing) by intersecting fibres[5]. This behaviour is dependent on
a multitude of factors that are difficult to control from a modelling and production
perspective, although its complexity is reduced somewhat in UD laminates.
Literature review
2.1 Reference litterature
Figure 2.1: Fatigue-life diagram according to Talreja et al[6]
Talreja and Singh[6] characterise the prevailing damage mechanism(s) and life as a function of strain level (or load level) in a fatigue life diagram (FLD). This diagram has three distinct regions, as shown in fig. 2.1
The first region is at high load, near the failure strain of the fibres (but still far below the failure strain of a typical matrix) low cycle fatigue range, where some fibres fail outright.
Each fibre failure redistributes load on
the remaining fibres, potentially causing more fibres to fail . If enough fibres fail, the stress in the remaining fibres will exceed the tensile capacity and fail. The rate at which this process occurs varies greatly, as is evident in large horizontal spread in the diagram. Testing in this region is characterised by "sudden death"
(unstable successive fibre failure) and by being non-progressive (i.e. apparent lack of material degradation).
3
4 CHAPTER 2. LITERATURE REVIEW
Figure 2.2: Types of fatigue damage, a ) fibre breakage, b ) fibre bridged matrix cracking, c ) matrix cracking without crack coalescence [6], reproduced.
In the case where the gradual process of individual fibre failure halts, the process might not resume again until the matrix has degraded sufficiently to redistribute load sufficiently to continue the process. This second region is a sloped area in the middle to high cycle fatigue range that is characterised by matrix fatigue cracking, with a crack forming at a point of local fibre failure or traversing the fibre after debonding with it (see fig. 2.2). The resulting load redistribution may cause an arresting fibre to fail, or further accelerate matrix damage. The horizontal spread in this region is less than in the first region, but still significant.
The third region is the high-cycle, fatigue limit region, where either the stresses in the matrix are insufficient to cause significant crack formation, or that growth of cracks traversing the fibre is effectively arrested. Any load redistribution occurring is insufficient to cause fibre failure within a predefined number of cycles. This number is referred to as the composite fatigue limit, in this study initially set to 2 ∗ 10
5cycles (later increased to 5 ∗ 10
5cycles).
The location of region one and three (and subsequently the span of region two), is governed by the material properties of the constituent materials. The region one scatter band is centred on the failure strain of the fibres, whereas region three is at the fatigue limit of the matrix. This indicates that the fatigue performance of a composite with a matrix fatigue limit close to the failure strain of the fibres, may produce fatigue test data in a very narrow region in terms of loading (region one spread, with a very narrow region two, and run-outs below this).
One may casually observe that the expected spread of fatigue life results in the
SN-curve for a composite is the opposite of that of a metal (which has a low
spread at high load levels, but increased spread with lowered load and increased
life). The spread in fibre failure (which dominates region one) is subject to many
CHAPTER 2. LITERATURE REVIEW 5
factors, particularly material surface imperfections. Due to the high anisotropy of the composite, even small deviations in fibre orientation or load alignment has a large impact on the fatigue performance[7], apart from increased material strength in off-axis directions, misalignment may introduce undesired shear loads and damage effects as a result. Talreja and Singh[6] refer to the matrix fatigue limit as a constituent property, however Brunbauer and Pinter[8] has compared specimen with different fibre volume fraction (V
f) in 90° (where fatigue performance is as- sumed to be matrix dominated) as well as homogeneous matrix material specimen and found that the composite specimen had a significantly poorer performance, illustrating that the fatigue limit of the matrix also has dependencies. Further- more, void content in the matrix also plays a large role in its fatigue performance[9].
Figure 2.3: Nominal stress amplitude vs life of 0° UD specimen of V
f= 55% and 30%, reproduced[10].
Brunnbauer and Pinter[10] tested UD CFRP fatigue performance with regards to V
f, load ratio and nominal stress amplitude (analogous to load level in this case). Two SN curves of UD CFRP 0° are reproduced in fig. 2.3. Here, results (particularly for the V
f= 30% specimen) are distributed in a fairly small range, but with large horizontal spread at the load level corresponding to region one, as well as a slope corresponding to region two.
Gamstedt and Talreja[11] are able to observe and document the aforementioned
damage types (fibre bridged cracking and debonding) at the microscopic level, and
also correlate them to the proposed damage regions in the FLD.
6 CHAPTER 2. LITERATURE REVIEW
Figure 2.4: Load level vs life for six 0° UD specimen, by Wanner[1], reproduced.
Wanner’s[1] work with the same CFRP material that is used in this study, aimed to develop a testing methodology w.r.t. specimen adhesive, tab configuration, tab material, and clamping force and its conclusions formed a framework for this study. Wanner was also able to produce a preliminary SN curve containing six data points(fig. 2.4). These results fall in the region proposed by Talreja [6], and have low spread in the high-load, low-cycle fatigue region, but the results are too few to determine a fatigue limit conclusively. Wanner’s work formed the outset for this thesis, which continues the work using much of its methodology
Figure 2.5: Overview of test setup used by Sanjay et al[12]
Sanjay et al[12] focused on in-situ full field strain development in a notched specimen, and also conducted micrography of sections of tests that were stopped pre-failure. The specimen was photographed at peak load and DIC analysis performed.
The study inspired this study in its methodology, but was performed under different circumstances.
The specimen, being notched, sustained localised damage at a predictable location, allowing for ideal
placement of the high-speed camera. This again allows for better resolution and
CHAPTER 2. LITERATURE REVIEW 7
opportunities to capture local events at higher detail. The article features DIC colour-plots of the strain for the notched region, as opposed to average strains, see fig. 2.5.
2.2 Digital image correlation
Digital Image correlation (DIC), is an image processing method of tracking surface displacements. It is commonly used in static testing of materials, and has the benefit of being non-contacting, full field (i.e. it can capture the entire surface of the specimen, unlike a strain gauge or linear variable differential transformer (LVDT) extensometer, which produce an "average" by default), and time efficient once the method is established.
Figure 2.6: Principle of operation of 2D-DIC in a tension test, from digitalimagecorrelation.org [13]
(CC-BY-4.0).
DIC is used in this project to track the developing fatigue induced deformation between cycles at constant load. In this application the so called 2D-DIC method is used, which relies on capture from a single camera. The method is subject to one important condition: It assumes in-plane displacement. This poses challenges for the testing as it requires the camera axis to be perfectly normal to the specimen surface, which in turn must be completely flat [14].
The testing machine used in this experiment has a rotational degree of freedom which is problematic due to low torsional rigidity of the specimen,
to counter this an aluminium bracket was installed on the piston, which effectively limits the out of plane rotation tendency to near zero (one side of the bracket is in constant contact with the support column of the test machine). fig. 2.8 illustrates the magnitude of error that can result from out-of-plane translation.
Other sources of error include lens distortion, an optical aberration that can
produce a fish-eye effect in the images. This problem can be dealt with in software
by introducing a lens correction factor which would have to be measured for this
specific setup. Due to time constraints and reasonable results in preliminary tests
8 CHAPTER 2. LITERATURE REVIEW
using an aluminium specimen, this has been neglected in this study.
The DIC algorithm used works in the following manner: a sequence of images are compared with a reference (initial image). Each image contains the Area of Interest (AOI) that is selected in advance (a speckle pattern fills this area completely). Within this area the algorithm selects a number of subsets which it attempts to match to the corresponding subsets in each image in the sequence. If a match is made, the centre-to-centre distance can be measured from the reference image to the current image.
Figure 2.7: Subset matching and displacement
The consistency of the algorithms ability to match subsets and yield results is dependent on numerous factors; speckle pattern, camera resolution, specimen illumination (strength and homogeneity). The speckle pattern should consist of speckles with roughly the same size, and the area coverage should be roughly 50 %. Each speckle should be between 10 to 20 pixels in size, and the "grey tone area"
(gamma gradient) between completely white and completely black should ideally not be more than 3-4 pixels [13]. Uneven illumination of the specimen makes matching less likely as it affects the thresh-
olding process used by the algorithm to differentiate between white and black areas
CHAPTER 2. LITERATURE REVIEW 9
Figure 2.8: Example of pseudo-strain caused by out-of-plane displacement of 1 mm, at an imaging distance of 61 cm
psuedo=
g
0g
0− ∆g − 1
=
610 610 − 1 − 1
= 0.1652% (2.1)
Methodology
3.1 Introduction
By comparing the sample at a constant load at different times (cycle counts, or
"specimen life"), the gradual degradation in the specimen can be investigated, as done previously by Sanjay et al[12]. This study aims to combine the rigorous testing scheme developed by Wanner[1], while additionally comparing peak to peak displacement using DIC.
All tests have been conducted in tension-tension, meaning that the sample is sub- jected to loading causing stress to vary sinusoidally between a low and high state, as in shown fig. 3.1 a. The applied load at both levels is constant, i.e. load controlled.
Fatigue damage coincides with elongation of the specimen, as shown in subfigure c.
.
Figure 3.1: a) Sinusoidal load, b) constant maximum load level resulting in increasing maximum strain over the course of the test (c).
σ = F
appliedA
specimenR = σ
minσ
maxS = σ
maxσ
f ailure(3.1) The ratio of minimum to maximum stress is known as the load ratio R
10
CHAPTER 3. METHODOLOGY 11
(eq. (3.1)). Positive ratios means non-alternating stress, i.e. tension-tension or compression-compression; subsequently negative R-ratios indicate stresses alternating between tension and compression. The load ratio has been demonstrated to impact fatigue performance[7], and it was originally an ambition of this work to perform testing at three load ratios R = (0.1, 0.5, 0.8) and compare. However this goal was abandoned due to time constraints.
Figure 3.2: Stress-time curve for a specimen under different load ratios.
The ratio of maximum stress to UTS is known as load level S. The relationship between load level and cycles to failure for a given sample and material type can be plotted in a Wöhler diagram, or S-N curve. Here, the abscissa constitutes number of cycles endured prior to failure on a logarithmic scale, and the load level is plotted on the ordinate, examples of which are shown in fig. 2.3 and fig. 2.4.
3.2 Test material
The CFRP material tested is a stitch-bonded UD non-crimp, epoxy-carbon composite produced with a resin transfer moulding (RTM) technique. The constituent properties of the material are given in table 3.1.
Property Zoltec UD Dow Epoxy Composite
Tensile strength 4137 MPa 68 MPa 1290 MPa*
Young’s modulus 242 GPa 2.8 GPa 118 GPa*
Elongation at
break 1.7 % 7 % 1.18 %*
Density 1810 kg m
−31160 kg m
−31400 kg m
−3V
fna na 48.6 %
Table 3.1: Material properties, * measured
12 CHAPTER 3. METHODOLOGY
The material was received as 300 mm by 650 mm plates, which were subsequently cut. All the available plates exhibited a slight tendency of fibre waviness near the edges of the plate, and care was taken to use material farther from the edges where this effect was less pronounced. As a result of the closed-mould manufac- turing method, both front and back surfaces of the plate feature a glossy, even finish.
3.3 Specimen manufacturing
The 0° and 90° specimen were manufactured in accordance with ASTM- D3039/D3039M[15], with 5 mm wider tabs to compensate for any potential lack of coverage due to tab misalignment during gluing, as recommended by Wanner[1].
Figure 3.3: 0° Specimen dimensions, all measurements in mm
The CFRP Material was cut into strips using a diamond bladed band-saw, whereas the aluminium tabs were cut with either an abrasive water jet (AWJ) or a hydraulic precision metal shear to the dimension as per fig. 3.3 and fig. 3.4 for the 0° and 90° specimen respectively.
In order to develop the DIC-methodology, and with the test material being in lim-
ited supply, around two dozen additional specimen were manufactured using left-
over scrap material made earlier by Wanner for this purpose. These had been
manufactured in-house using the vacuum-assisted resin infusion (VARTM) tech-
nique, resulting in a carbon-vinyl-ester composite that was cut to similar dimen-
sions as the Audi specimen, except with a thickness of 2.4 mm, and with an infe-
rior surface quality on one side (a so called "B-side"[5], as a result of the manu-
facturing technique). These tests were only occasionally carried out uninterrupted,
and data collection on the samples was done for the purpose of developing the
test, consequently they are not treated here.
CHAPTER 3. METHODOLOGY 13
Figure 3.4: 90° Specimen dimensions, all measurements in mm
Each individual specimen was measured at three locations to determine width and thickness, these values where then averaged and used to calculate a nominal cross sectional area. This area in turn determined the appropriate loads (σ
minand σ
max) for the desired load level S (eq. (3.1).
Figure 3.5: Specimen alignment and gluing jig
To ensure specimen consistency and efficient production, a gluing template tool was manufactured out of a 20 mm aluminium plate, using an abrasive water jet cutter. The purpose of this tool is to ensure proper alignment of tab and test material, and can be seen in figure fig. 3.5. This jig consists of a lower slab embedding 4 mm round steel pins to constrain any movement of the specimen material and end tabs during gluing. A top slab with cuts allowing the steel pins to pass through
is placed on top to apply even pressure to the six specimen inside. The jig is then placed in an oven for post curing of the glue, and the semi-fixed steel pins allows adequate tolerance for thermal expansion during the curing process and easy removal afterwards.
Initially an AWJ process was considered for cutting the specimen themselves,
but this was later decided against (in favour of a diamond blade saw), as the
material is susceptible to delamination with this method[16, 17]. The change to
using a saw for cutting precluded the option to cut specimen post-gluing, as the
constituent materials require different saw blades. The specimen glue area (50
x 15 mm) and was subjected to a light grind with 400 and 800 grit sandpaper,
14 CHAPTER 3. METHODOLOGY
washed with dishing soap and rinsed, wiped and left to dry for a minimum of one hour. The tab area (50 x 20 mm) was machine ground with 400 grit sandpaper and cleaned with pressurised air, and rinsed with acetone prior to gluing.
To ensure consistent glue thickness, simple, serrated glue spreading pads were 3D
printed, reducing material waste while providing a controlled glue thickness. The
adhesive used is the two component epoxy DP420M, determined by Wanner[1] to
be well suited for this use. Immediately after adhesive application, the assembled
jig is placed in an oven and allowed to cure at 50
◦C for one hour, as per the
DP420M product specification[18], which lists a lap shear strength of 24 MPa
bond to aluminium, and 35 MPa to CFRP. Metal weights were distributed atop
the jig prior to the glue hardening and left there during curing process to ensure
adequate contact and consolidation of glued surfaces.
CHAPTER 3. METHODOLOGY 15
3.4 Static testing
Figure 3.6: Static tension specimen immediately prior to failure, note that tilted appearance is due to the view being from a single (in this case the left) camera.
To verify the static UTS obtained by Wanner[1] for the test material, two static
tests were conducted. The specimen were made with spare pre-cut material
16 CHAPTER 3. METHODOLOGY
and featured 15 mm wide glass fibre reinforced plastic (GFRP) tabs but were otherwise similar to the fatigue specimen as given infig. 3.4. The move to GFRP tabs for static testing is done to lower the chance of slippage and pullout, as they exhibit greater resistance to pull-out compared to aluminium tabs, at the cost of having lower thermal conductivity (which is a considerable problem in fatigue testing, see section 3.5). As thermal issues were of no concern in static testing consisting of one slow cycle, GFRP tabs were successfully used.
Equipment Item
Tension machine Instron 4505
Grips Mechanical
Camera and lens 50 mm Aramis 5M LT 3D system
Software GOM ARAMIS PRO
Table 3.2: Equipment used in static testing
An Instron 4505 100 kN machine was for used for the static tests, and each specimen was loaded under displacement control at a rate of 2 mm min
−1, as per ASTM D3039/D3039M[5]. The displacement and strain capture and computation was conducted with a Aramis 3D-DIC setup, producing a strain-time dataset.
The test machine logged displacement and load over the same duration, and the
combination of this data yielded the stress-strain curve given in fig. 3.7. The two
test results fell within the range found by Wanner[1], who tested five specimen,
yielding an average UTS of 1295 MPa, with a S.D. (standard deviation) of
108 MPa.
CHAPTER 3. METHODOLOGY 17
Figure 3.7: 3D-DIC Stress vs
yymeasurement on the first of two static tension tests.
3.5 Fatigue testing
Fatigue testing has been conducted at the Lightweight Structures Laboratory at KTH Stockholm
1, on a test setup as shown in fig. 3.9 and listed in table 3.3. The machine has a degree of freedom about its operating axis (the lower actuator piston is free to rotate), which, for a stiffer metal specimen is uncontroversial. A step-by-step instruction on how to correctly initiate a test is provided in appendix A
3.5.1 Out-of-plane twist
Due to the low torsional stiffness of the CFRP specimen considered here, the specimen twisted, causing out of plane motion (see section 2.2), so an aluminium guide bracket (fig. 3.8) was installed on the piston to mitigate this phenomenon by
1