considering the statistical distribution of dynamic fracture … · 2016-11-17 · e399 and e1820...
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Considering the Statistical Distribution of Dynamic Fracture Toughness Data and the Actual Loading Rate at Fracture Initiation when applying ASTM
E1921 at Elevated Loading Rates
Uwe MayerMaterials Testing Institute (MPA)
University of StuttgartGermany
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Outline
Introduction Loading rate definition in existing standards Proposal of a new definition of the loading rate Test equipment for fracture mechanic tests at high
loading rates Discussion of results obtained from tests at high
loading rate Analysis of local stress history Multi-Temperature results at 105 MPa√m s-1, 1T C(T) Conclusion
15th International ASTM/ESIS Symposium on Fatigue and Fracture Mechanics, May 20-22, 2015, Anaheim, CA
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Introduction
Commonly different parameters are used for characterizing the loading rate of linear-elastic and elastic-plastic fracture mechanics test. For linear-elastic tests dK/dt can be kept approximately constant during the test, for elastic-plastic tests dJ/dt is constant after an initial acceleration during the linear-elastic part of the test.
dK/dt is the loading rate parameter for linear-elastic tests. dJ/dt is the loading rate parameter for elastic-plastic tests.
For the use of a Master Curve evaluation according to ASTM E1921 in the transition range of fracture toughness, results from both types of tests are used: fracture toughness K for linear-elastic tests and formally calculated values KJ from J for elastic-plastic tests. The open question regards the relevant loading rate, especially if different test series are compared, e.g. one test series with unstable crack initiation during linear-elastic loading and the other one with similar KJ-values calculated formally from J-values, being elastic-plastic due to smaller dimensions.
15th International ASTM/ESIS Symposium on Fatigue and Fracture Mechanics, May 20-22, 2015, Anaheim, CA
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Introduction
Results of a research project investigating the correlation of dynamic crack initiation and crack arrest, Böhme. (2012), that was funded by the German government, show differences of up to 30 K in T0,X obtained from linear-elastic test series and T0,X obtained from elastic-plastic test series with comparable dK/dt.
Dynamic fracture mechanics testing is specified in annexes of the standards ASTM E399 and E1820 and also in BS7448-3. In these standards fracture mechanics values J and K are determined basically the same way as for quasi-static tests.
f(a/w)
and
15th International ASTM/ESIS Symposium on Fatigue and Fracture Mechanics, May 20-22, 2015, Anaheim, CA
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Loading rate definition in existing standards
ASTM E 399 A10 (special requirements for rapid force, plane-strain fracturetoughness KIC(t) testing)
dK/dt=KQ/t
BS 7448 part 3 (3 MPa√m/s < dK/dt < 3×103 MPa√m/s)In BS 7448-3 two definitions for the loading rate are given:dKI/dt during the initial elastic loading of the specimen and the rate of change of the plastic component of the J integral dJp/dt, determined using the time interval for plastic deformation of the test specimen.
In ASTM E 1820 Annex 14 (rapid-load J-integral fracture toughness testing), also two different loading rate quantities are defined:
(dJ/dt)I measured before JQ(t), and (dJ/dt)T measured after JQ(t), where JQ(t) is the provisional, rate dependent J Integral at the onset of stable crack extension. (dJ/dt)Iis defined by using a linear regression analysis between 0.5 JQ(t) and JQ(t), even if the increase is quadratic over time (Figure 1).
The second loading rate is defined as the slope of the J versus time data beyond maximum force.
15th International ASTM/ESIS Symposium on Fatigue and Fracture Mechanics, May 20-22, 2015, Anaheim, CA
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Loading rate definition in existing standards
15th International ASTM/ESIS Symposium on Fatigue and Fracture Mechanics, May 20-22, 2015, Anaheim, CA
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0 0.1 0.2 0.3 0.4 0.5
J [Nmm
‐1] resp. K
J[M
Pam
0.5 ]
Time t [ms]
KJJ0.5 ∙ JQJQ(dJ/dt)I (ASTM E1820)
tQ
ASTM E1820 (linear fit)(dJ/dt)I = 2.8 x 105 N mm‐1 s‐1dK/dt = 5.1 x 105 MPam0.5 s‐1
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Loading rate definition proposal
15th International ASTM/ESIS Symposium on Fatigue and Fracture Mechanics, May 20-22, 2015, Anaheim, CA
These different definitions for the different parts of a fracture mechanics test at elevated loading rate are both useful for characterizing the loading rates of the tests. Only if results from both, linear-elastic tests and elastic-plastic tests are assessed together to describe the influence of the loading rate on cleavage fracture toughness for a material a unified definition of the loading rate for both types of tests is needed. This applies especially to the Master Curve evaluation according to ASTM E1921.
Since the J-integral correlates quadratic with K, the question arises during application of ASTM E1921 at high loading rates, if for the elastic-plastic range a quadratic increase of the J-integral leads to a loading rate comparable to linear-elastic tests.
However, usual testing conditions with constant displacement rate result in a linear increase of the J-integral over time in the plastic regime after the initial acceleration during the linear-elastic part of the test.
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Loading rate definition proposal
15th International ASTM/ESIS Symposium on Fatigue and Fracture Mechanics, May 20-22, 2015, Anaheim, CA
We analyze the correlation of the change over time of K and the change over time of J in the case of a linear-elastic fracture mechanics test for constant dK/dt:
(1)
/ (2)
(3) terms with vanish because = constant
solving for dK/dt leads to:
(4)
K = stress intensity factor (time series) E = Youngs modulus J = J-Integral (time series) ν = Poisson’s ratio dK/dt = loading rate
Proposal: Transfer of this correlation also to the elastic-plastic regime.
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Servo-hydraulic Testing Device
Servo-hydraulic testing machine(VHS 100/20 Schenck/Instron)
Fmax= 100 kN, vmax= 20 m/s
This machine incorporates large hydraulic accumulators (2x 280 l), high flow rate servovalves (6400 l/min) and a special slack adapter such that almost constant displacement rates during a complete test could be achieved.
The slack adapter minimizes the mass to be accelerated and hence reduces oscillations.
The computer controlled valves (6400 l /min) allow the load time characteristics to be optimized for any particular test condition or material.
15th International ASTM/ESIS Symposium on Fatigue and Fracture Mechanics, May 20-22, 2015, Anaheim, CA
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Force measurement strain gauges
At high loading rates the only acceptable force measurement technique is the use of strain gauges on parts of the specimen, which remain elastic during the test.
In previous investigations positions on the upper (fixed) part and lower (moving) part of the specimen at which the strain behaves accordingly proportional to force were identified by means of numerical simulation.
15th International ASTM/ESIS Symposium on Fatigue and Fracture Mechanics, May 20-22, 2015, Anaheim, CA
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Onset of cleavage at 2x105 MPa√m s-1, 1T C(T)
At loading rates up to 2x105 MPa√m s-1, the time of the start of unstable crack propagation can be determined from the load drop measured using the force strain gauges. This instant of time correlates well with that indicated by the crack tip strain gauges.
15th International ASTM/ESIS Symposium on Fatigue and Fracture Mechanics, May 20-22, 2015, Anaheim, CA
‐0.15
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0.0092 0.0093 0.0094 0.0095 0.0096 0.0097 0.0098
Volta
ge [V
]
CTCM09 2x105 MPa m/s
Force [kN]
Time [s]
Force on moving side
Force on fixed side
Force averaged
Crack tip strain gauge 1
Crack tip strain gauge2
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Material from a Reactor Pressure VesselBiblis C ( 22 NiMoCr 3 7 equivalent to A 508 Cl.2)
15th International ASTM/ESIS Symposium on Fatigue and Fracture Mechanics, May 20-22, 2015, Anaheim, CA
The specimens were extractedfrom the middle sector of theRPV with crack tip between 2/3 and ¾ of the thickness
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Mastercurve evaluation according to ASTM E 1921
Force vs. Crack Opening Displacement and Mastercurve according to ASTM E1921 for the test series at -20°C, 2x105 MPa√m s-1
Material: 22 NiMoCr 3 7 (similar to A 508 Cl.2) Specimen type: 1T C(T) (Materials Testing Institute University of Stuttgart)Test device: High rate servo-hydraulicKJC_50%=30 + 70 exp [ 0.019 ( T - T0 )], T0,quasi-static=-68°C KJC,d_50%=30 + 70 exp [ 0.019 ( T - T0,5 )], T0,5=+15°C
15th International ASTM/ESIS Symposium on Fatigue and Fracture Mechanics, May 20-22, 2015, Anaheim, CA
0.0 0.2 0.4 0.6 0.8 1.00
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e [k
N]
COD [mm]
CM07 CM08 CM09 CM10 CM11 CM12 CM13 CM14
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Mastercurve evaluation according to ASTM E 1921
15th International ASTM/ESIS Symposium on Fatigue and Fracture Mechanics, May 20-22, 2015, Anaheim, CA
0.0 0.2 0.4 0.6 0.8 1.00
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e [k
N]
Displacement [mm]
TN1-SEB10-02 TN1-SEB10-07 TN1-SEB10-09 TN1-SEB10-12 TN1-SEB10-14 TN1-SEB10-17 TN1-SEB10-19 TN1-SEB10-21 TN1-SEB10-22 TN1-SEB10-24 TN1-SEB10-26 TN1-SEB10-29 TN1-SEB10-31 TN1-SEB10-32 TN1-SEB10-34 TN1-SEB10-36 TN1-SEB10-37 TN1-SEB10-39 TN1-SEB10-41 TN1-SEB10-42 TN1-SEB10-44 TN1-SEB10-46 TN1-SEB10-47 TN1-SEB10-51 TN1-SEB10-54 TN1-SEB10-55 TN1-SEB10-69 TN1-SEB10-79 TN1-SEB10-86 TN1-SEB10-90 TN1-SEB10-96 TN1-SEB10-100
Force vs. Displacement and Mastercurve according to ASTM E1921 for the test series at-20°C, 3x105 MPa√m s-1
T0,5=-7°C
Results from pendulum tests with SEB 10/10. Tests performed at Fraunhofer Institute for Mechanics of Materials, IWM, Freiburg.
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Analysis of a pendulum test with a SE(B) 10/10 specimen
15th International ASTM/ESIS Symposium on Fatigue and Fracture Mechanics, May 20-22, 2015, Anaheim, CA
Force-displacement curve of a pendulum test with a SE(B) 10/10 specimen at 1m/s, resulting in dK/dt = 3x105 MPa√m s-1
(Fraunhofer Institute for Mechanics of Materials, IWM, Freiburg)
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Time t [ms]
dKJ/dtdJ/dt(dJ/dt)I (ASTM E1820)dK/dt (ASTM E1820)
First derivative of J(t) and KJ(t) during test time and (dJ/dt)I according ASTM E1820, A14
Test performed at Fraunhofer Institute for Mechanics of Materials, IWM, Freiburg.
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Analysis of a pendulum test with a SE(B) 10/10 specimen
15th International ASTM/ESIS Symposium on Fatigue and Fracture Mechanics, May 20-22, 2015, Anaheim, CA
Above J=58 N/mm (KIJ = 116 MPa√m, KIJ(1T) = 96 MPa√m) dK/dt calculated with the proposed definition declines below 105 MPa√m s-1, while the rate of KIJ calculated after conversion from J is near to 3x105 MPa√m s-1 for the entire test.
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dK/dt calculated using d2J/dt^2
dKJ/dtcompared to
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Analysis of local stress history
15th International ASTM/ESIS Symposium on Fatigue and Fracture Mechanics, May 20-22, 2015, Anaheim, CA
For linear elastic tests the major principal stress in the region, where the unstable crack starts, shows a sharp increase with crack opening displacement (COD). If plastic deformation starts to be a significant part of the macroscopic specimen behavior, the incline of the major principal stress with COD becomes more and more gentle, especially if the maximum moves towards the ligament with increasing distance from the fatigue pre-crack.
Result of an analysis of the quasi-static loading of a 1T C(T) specimen.
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Analysis of local stress history
15th International ASTM/ESIS Symposium on Fatigue and Fracture Mechanics, May 20-22, 2015, Anaheim, CA
The time course of this major principal stress plays a tangential role for the behavior of the material as long as the test is quasi-static and there is no or only small sensitivity to the loading rate.
This changes significantly for higher loading rates. Dynamic fracture tests are generally performed using a constant displacement rate, thus the COD is proportional to time.
In case of dynamic tests we can transfer these observations of the increase of the stress normal to the fracture plane with COD to the stress rate relating to time. This view on the local stress rate near the unstable crack initiation supports the conception that the loading rate is decreasing, if the test ceases to be globally linear-elastic.
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Mastercurve evaluation according to ASTM E 1921
15th International ASTM/ESIS Symposium on Fatigue and Fracture Mechanics, May 20-22, 2015, Anaheim, CA
Following this proposal the result of tests should not be included in the determination of T0,5 if the loading rate is too low at cleavage initiation.
This is the case for 6 out of 32 tests of the test series with 1 m/s displacement rate using the pendulum machine and has a strong effect on the determined value for the reference temperature T0,5.This can be seen as a population of data above 100 MPa√m. If we censored the KJcd(1T)-values higher than 96 MPa√m, as it would be done if the values were higher than KJclimit, T0,5 would be evaluated to +2°C instead of -7°C, calculated according to the current edition of ASTM E1921.
Tests performed at Fraunhofer Institute for Mechanics of Materials, IWM, Freiburg.
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Multi-Temperature results at 105 MPa√m s-1, 1T C(T)
15th International ASTM/ESIS Symposium on Fatigue and Fracture Mechanics, May 20-22, 2015, Anaheim, CA
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Force vs. Crack Opening Displacement and Mastercurve according to ASTM E1921 for the first test series of the current project at 20°C, 7x105 MPa√m s-1
This test series seems to verify the T0,5=+15°C determined in the previous project at -20°C, 2x105 MPa√m s-1
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Multi-Temperature results at 105 MPa√m s-1, 1T C(T)
15th International ASTM/ESIS Symposium on Fatigue and Fracture Mechanics, May 20-22, 2015, Anaheim, CA
Mastercurve evaluation assuming Log-Normal distribution as it is done for crack arrest using ASTM E1221. The lower bound shows better agreement with the KIR-curve than the lower bound according to ASTM E1921.
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Multi-Temperature results at 105 MPa√m s-1, 1T C(T)
15th International ASTM/ESIS Symposium on Fatigue and Fracture Mechanics, May 20-22, 2015, Anaheim, CA
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Multi-Temperature results at 105 MPa√m s-1, 1T C(T)
15th International ASTM/ESIS Symposium on Fatigue and Fracture Mechanics, May 20-22, 2015, Anaheim, CA
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Multi-Temperature results at 105 MPa√m s-1, 1T C(T)
15th International ASTM/ESIS Symposium on Fatigue and Fracture Mechanics, May 20-22, 2015, Anaheim, CA
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Multi-Temperature results at 105 MPa√m s-1, 1T C(T)
15th International ASTM/ESIS Symposium on Fatigue and Fracture Mechanics, May 20-22, 2015, Anaheim, CA
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Multi-Temperature results at 105 MPa√m s-1, 1T C(T)
15th International ASTM/ESIS Symposium on Fatigue and Fracture Mechanics, May 20-22, 2015, Anaheim, CA
We got different results fordK/dt = 2x105 MPa√m s-1 (X= Log (dK/dt)= 5.3)and dK/dt =7x105 MPa√m s-1 (X= Log (dK/dt)= 5.8)Because of this significant difference we use two digits for X:T0,53 and T0,58
Mastercurve: KJC,d_50%=30 + 70 exp [ p(T - T0,X )]
Obviously the shape of the Mastercurve used for the evaluation of quasistatic testsaccording to ASTM E1921, is not appropriate for these dynamic test results.We try the proposal of Schindler:
Quasi-static Mastercurve: p= 0.019 KJc,d_50%=30 + 70 exp [ 0.019 (T - T0,X )]
Proposal Schindler: using a rate dependent, with a value for p up to 0.045We make a first attempt using p=0.03
KJc,d_50%=30 + 70 exp [ 0.03 (T - T0,X )]
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Multi-Temperature results at 105 MPa√m s-1, 1T C(T)
15th International ASTM/ESIS Symposium on Fatigue and Fracture Mechanics, May 20-22, 2015, Anaheim, CA
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Multi-Temperature results at 105 MPa√m s-1, 1T C(T)
15th International ASTM/ESIS Symposium on Fatigue and Fracture Mechanics, May 20-22, 2015, Anaheim, CA
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Multi-Temperature results at 105 MPa√m s-1, 1T C(T)
15th International ASTM/ESIS Symposium on Fatigue and Fracture Mechanics, May 20-22, 2015, Anaheim, CA
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30
Multi-Temperature results at 105 MPa√m s-1, 1T C(T)
15th International ASTM/ESIS Symposium on Fatigue and Fracture Mechanics, May 20-22, 2015, Anaheim, CA
For the test series at dK/dt = 2 x105 MPa√m s-1 the Mastercurve with p=0.03 seems to fit very well. For the test series at dK/dt =7 x105 MPa√m s-1 theMastercurve is too low at -20 °C
This shows, that the steeper Mastercurve with p=0.03 is not valid over thewhole transition range and a narrower validity range than +-50 K has to beused if this modification of the Mastercurve for high rate loading is applied.
With the currently limited number of tests at dK/dt = 2 x105 MPa√m s-1 and20° C the proposed censoring method is not applicable.
More tests have to be performed to enhance the statistical significance of theanalysis
If the test temperature is very near to T0,x (less than 10 K) the influence of theused exponential factor p of the Mastercurve has clearly no significantinfluence on the dermined T0,x .
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31
Conclusion
15th International ASTM/ESIS Symposium on Fatigue and Fracture Mechanics, May 20-22, 2015, Anaheim, CA
A new definition of the loading rate is proposed for the transition range of fracture toughness. This can be helpful for clarifying, why for different types of test series, evaluated according to the current version of ASTM E1921, differences of up to 30K for T0,X were determined (X is defined as the order of magnitude of dK/dt). Different loading rates may be one factor.
With the proposed definition the loading rate of each test can be checked to be within the scope. If not, in some cases censoring may be an option to determine a more accurate reference temperature.
Further experimental and numerical investigations are needed for the validation of this procedure.
The influence of other parameters, such as adiabatic heating in the plastic zone, constraint and small amounts of ductile crack growth will be investigated in the current project.
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32
Conclusion
15th International ASTM/ESIS Symposium on Fatigue and Fracture Mechanics, May 20-22, 2015, Anaheim, CA
Sensitivity to loading rate is too high to allow the mixing offracture toughness values determined over one total order of magnitudeProposal: use 2 digits of the logarithm of the loading rate (T0,53 resp. T0,58)
Even if only results with the same loading rate are used, the shape of themastercurve is different from the one used in ASTM E1921 for test seriesat elevated loading rates
First analyses show a good agreement using an exponent ofp=0.03 instead of p=0.019
But: p=0.03-shape seems not to be applicable in the lower shelf at temperatures30 K below T0
Range for the determination of T0,X has to be narrowed in comparison to theT0 +- 50K range used in ASTM E1921Proposal: T0,X +- 25K
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33
Acknowledgement
The research project
“Analysis and Validation of Fracture Mechanical Assessment Methods under Dynamic Loading”
is funded by the German Federal Ministry for Economic Affairs and Energy (Project No. 1501472B) on the basis of a decision by the German Bundestag. The project is a cooperation of FraunhoferInstitute for Mechanics of Materials, IWM, Freiburg and Materials Testing Institute University of Stuttgart, MPA, Germany.
15th International ASTM/ESIS Symposium on Fatigue and Fracture Mechanics, May 20-22, 2015, Anaheim, CA
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17.05.2015 ASTM-Workshop Anaheim1
Rate-sensitivity of the MC-shape and its effect on the uncertainty of T0
Hans-Jakob SchindlerMat-Tec AG, Winterthur, Switzerland
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17.05.2015 ASTM-Workshop Anaheim2
Contents
• Evidence of rate-dependence of Master Curve• Effects of loading rate on T0
• Possibilities to account for rate-dependence of MC in E1921
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17.05.2015 ASTM-Workshop Anaheim3
Actual shape:
KJc from tests at elevated loading rates
07030 TTpJc eK
Under elevated loading rates the median KJc(1T)-curve does not follow 0019.07030 TT
Jc eK
0
50
100
150
200
250
300
350
400
450
-40 -20 0 20 40 60
T-T0 [K]
KJc
[MPa
*m^0
.5]
medium ratequasistaticTrend medium rateMC-50% pfMC 95 % pfMC 5 % pf
window of validity
Material: RPV-steel 22NiMoCr3
quasistatic and medium rate (0.8T-SENB)
0
100
200
300
400
500
-40 -30 -20 -10 0 10 20 30 40 50 60
T - T0,x
KJd
(1T)
0.4T SEB- a/W=0.5 impact
0.4T SEB- a/W=0.3 impact
0.8T-SE(B) medium rate
0.4T-SEB medium rate
MC 5 % pf
MC 95 % pf
MC 50% pf
validity limit 0.4T
validity limit 0.8T
Medium and high loading rates (0.4T and 0.8T SENB)
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17.05.2015 ASTM-Workshop Anaheim4
Representative loading rateLoading rates of quasi-static tests
0
0.2
0.4
0.6
0.8
1
1.2
1.4
0 20 40 60 80 100 120 140
K_J
dK_J
/dt
1T- CT 3.2- T SE(B)1.6T SE(B) 0.8T SE(B)0.4T SEB 0.4T SE(B)- 0.3
30
5/ 25
1J
JrefJ dK
dtdKK
Representative loading rate:
mean dKJ/dt in range 5 MP·m0.5 < KJ < 30 MP·m0.5 :
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17.05.2015 ASTM-Workshop Anaheim5
Rate-dependence of Exponent p
0.010
0.015
0.020
0.025
0.030
0.035
0.040
0.045
-1 0 1 2 3 4 5 6
log(dK/dt) [MPam^.5/s]
p
valid tests only
all tests
quasi-static
0.010
0.015
0.020
0.025
0.030
0.035
0.040
0.045
0.1 0.3 0.5 0.7 0.9 1.1 1.3 1.5 1.7 1.9dK/dt [MPam^.5/s]
p
valid tests only
all tests
TpCK TmedJc ln)30ln( )1(/
Determination of p from:y = 0.018x + 5.5575
0
1
2
3
4
5
6
-130 -110 -90 -70 -50 -30 -10
Temperature [°C]
ln(K
Jc(1
T)-3
0)
1T-CT
100 Mpam .̂5
Linear (1T-CT)
T0
p1
Results:
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17.05.2015 ASTM-Workshop Anaheim6
Effect of test-temperature on T0 for p > 0.019(for single-temperature testing acc. E1921))
-30
-20
-10
0
10
20
30
-50 -30 -10 10 30 50
Ttest - T0 [°C]
Bias
in T
0 [°C
]
p= 0.02
p= 0.025
p= 0.03
019.01)( 1001000
pTTTT test
T
KJc
T100T0B T0
ATtestA Ttest
B
100
0
Test series A
Test series B p>0.019
MC(A)
MC(B)
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17.05.2015 ASTM-Workshop Anaheim7
T0 of multi-path welds
s
t t
sinner surface
(a) (b)
upper ring
lower ring
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17.05.2015 ASTM-Workshop Anaheim8
Experimental KJc-data of weld material
Master-Curve TL-OrientierungSE(B)-Probe
Master-Curve TS-OrientierungSE(B)-Probe
JK = 1.40 MPa·m0.5/sLoading rate:
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17.05.2015 ASTM-Workshop Anaheim9
Variability of T0 through the thickness
-120
-110
-100
-90
-80
-70
-60
0 20 40 60 80 100 120 140 160 180 200 220 240 260Distance from inner surface [mm]
Ref
eren
ce te
mpe
ratu
re [°
C]
-120
-110
-100
-90
-80
-70
-60
0 20 40 60 80 100 120 140 160 180 200 220 240 260Distance from inner surface [mm]
Ref
eren
ce te
mpe
ratu
re [°
C]
T-L-specimens (0.4T-SEB): T-S-specimens (0.4T-SEB): :
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17.05.2015 ASTM-Workshop Anaheim10
Bias with respect to test temperature
-20-15-10-505
10152025
-25 -15 -5 5 15mean test temperature - T0
T 0 -
T tre
nd
-10
-5
0
5
10
15
20
-25 -20 -15 -10 -5 0Mean test temperature - T0
T 0 -
T tre
nd
T-L-specimens (0.4T-SEB): T-S-specimens (0.4T-SEB):
Indication that p > 0.019 (p ≈ 0.035)
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17.05.2015 ASTM-Workshop Anaheim11
Shape of MC of Weld Material T-L crack orientation T-S crack orientat ion
Layer Posit ion (s ) T0 Ttest-T0 p T0 Ttest-T0 p [mm] [K] [K] (-) [K] [K] (-) B 15.9 -108.6 -6.9 0.032 -113.5 -4.5 0.021C 25.9 -82.8 -12.7 0.016 -97.8 -4.2 0.050D 36.2 -89.4 -6.4 0.035 -104.6 -2.4 0.035E 46.5 -81.5 -17.7 0.044 -89.8 -10 .2 0.076F 56.8 -86 -7.4 0.004 -87.8 -8.2 0.063G 67.1 -79.3 -9.6 0.033 -84.2 -4.9 0.055H 77.4 -70.7 -15.1 0.028 -90.3 -9.7 0.042I 87.7 -93.6 -11.7 0.030 -90.9 -0.5 0.032J 98 -76.5 -15.5 0.044 -88.4 -7.6 0.025K 108.3 -93.5 -4.5 0.007 -98.3 4.3 0.024L 118.6 -96.3 -21.1 0.032 -91 -6.9 0.065M 128.9 -75.2 -11.1 0.047 -97.9 -11 .1 0.052N 139.2 -80.7 -6.8 0.023 -93.8 2.8 0.037O 149.5 -70.8 -9.1 0.018 -84.4 -4.7 0.047P 159.8 -82.4 -8.7 0.039 -93 1.6 0.025Q 170.1 -69.7 -12.6 0.035 -86.7 -3.3 0.056R 180.4 -88.4 -14.7 0.031 -102.3 11.0 0.019S 190.7 -75.4 -16.2 0.021 -95.5 -13 .5 0.047T 201 -108.7 -11.9 0.038 -94.8 -12 .3 0.035U 211.3 -94.8 -20.8 0.067 -104.3 -4.7 0.025V 221.6 -86.9 -6.4 0.027 -95.9 -13 .1 0.040W 231.9 -95.4 -7.4 0.033 -98.5 -7.5 0.019X 242.2 -99.5 -10.2 0.055 -91.1 -14 .2 0.047Y 252.5 -89.2 -6.8 0.034 -100.6 -0.5 0.005
Average -86.5 -11.3 0.032 -94.8 -5.2 0.039
)(exp7030)( 0)( TTpTK medJc
0.010
0.015
0.020
0.025
0.030
0.035
0.040
0.0 0.2 0.4 0.6 0.8 1.0 1.2 1.4 1.6
dK/dt [MPam^.5/s]p
GrundmaterialSchweissgut
T-L
T-S
Fits in trend of base material
Indicates that p is not much influenced by yield stress
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17.05.2015 ASTM-Workshop Anaheim12
Reference temperature T100 by the OEF-method
-120
-110
-100
-90
-80
-70
-60
-50
0 20 40 60 80 100 120 140 160 180 200 220 240 260Distance from inner surface [mm]
Ref
eren
ce te
mpe
ratu
re [°
C]
ASTM E1921
OEF-method
ä
-120
-110
-100
-90
-80
-70
-60
-50
0 20 40 60 80 100 120 140 160 180 200 220 240 260Distance from inner surface [mm]
Ref
eren
ce te
mpe
ratu
re [°
C]
ASTM E1921
OEF-method
T-L-specimens (0.4T-SEB) T-S-specimens (0.4T-SEB)
30ln2485.411))(1()(
1100
iTJcitestav
N
i av
KTppN
T
with pav= 0.032 (T-L) and 0.039 (T-S), resp.
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17.05.2015 ASTM-Workshop Anaheim13
Dynamic T0- Data from Boehme et al. 2012
-80-70-60-50-40-30-20-10
0102030
0 1 2 3 4 5 6 7log(dKI/dt)
T0 [°
C]
T100Böhme et al./p=0.3eq. (13)eq. (2)
Böhme, W., Mayer, U., Reichert, T., et al. (2012),”, IWM-Freiburg, Project No. 150 1368, Report No. 665/2012,
-80
-70
-60
-50
-40
-30
-20
-10
0
10
20
30
0 1 2 3 4 5 6 7 8 9 10 11 12 13 14 15 16ln(dKI/dt)
T0 [°
C]
T100,x
Böhme et al./ E1921
theory
Data Boehme et al.
-30
-20
-10
0
10
20
30
-40 -30 -20 -10 0 10 20
Ttest-T0/predicted
T0-T
0/pr
edic
ted
p≈0.3
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17.05.2015 ASTM-Workshop Anaheim14
Dynamic T0- data from Joyce,Tregoning&Roe
-20
0
20
40
60
80
100
-200 -180 -160 -140 -120 -100 -80 -60 -40 -20 0
T0 - T_test
T0 -
T_pr
ed
-40
-20
0
20
40
60
80
100
120
140
-2 -1 0 1 2 3 4 5 6 7
log(dK/dt)
T0
eq (15)E1921To[C]
-40
-20
0
20
40
60
80
100
120
-2 -1 0 1 2 3 4 5 6 7
log(dK/dt)
T100
eq (15)E1921To[C]
-20
0
20
40
60
80
100
-120 -100 -80 -60 -40 -20 0 20
T_test-T100
T100
-T_p
red
p= 0.03p= 0.035T0-T0predLinear (T0-T0pred)
J. Testing and Evaluation, Vol. 34, 2006
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17.05.2015 ASTM-Workshop Anaheim15
Exponent p as a function of loading rate
0.010
0.015
0.020
0.025
0.030
0.035
0.040
0.045
-1 0 1 2 3 4 5 6
log(dK/dt) [MPam^.5/s]
p
valid tests only
all tests
"quasi-static"
0.010
0.015
0.020
0.025
0.030
0.035
0.040
0.0 0.2 0.4 0.6 0.8 1.0 1.2 1.4 1.6
dK/dt [MPam^.5/s]
p
Base MaterialWeld
Simplified trend:
25.1035.025.15.0021.0019.0
5.0019.0
J
JJ
J
KforKforK
Kforp
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17.05.2015 ASTM-Workshop Anaheim16
Detrimental effects of fixed p (=0.019)
• Deterministic influence of test temperature on T0
• Increased uncertainty prevents physical trends from being recognized in experimental data, such as, for examples:
•Increases uncertainty of T0
•Requires extra safety margin in a safety analysis
•Enables T0 to be manipulated by the choice of test temperature
•Effect of thickness on T0
•Variation of T0 through the thickness of welds
•Saturation of rate effects (lower and upper bound)
!!
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17.05.2015 ASTM-Workshop Anaheim17
Conclusions
• p is affected by loading rate for • For p > 0.019, self-consistency of E1921 is violated• Designability of T0 is not tolerable in a standard • The problem with p>0.019 should be addressed in E1921, at
least as a note or bias.• Preferably, improvements to reduce this effect should be made
JK > 0.6 MPa·m0.5/s
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17.05.2015 ASTM-Workshop Anaheim18
Possibilities for improvements in E1921
1. Providing p as a function of loading rate
2. Allowing p to be determined individually by linear regression in a logKJc-vs.-T - plot
3. Alternative methods to determine T0For example: - CF-method
- restriction to certain specimen types and sizes (to get rid of validity criteria)
25.1035.025.15.0021.0019.0
5.0019.0
J
JJ
J
KforKforK
Kforp
Tentatively:
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17.05.2015 ASTM-Workshop Anaheim19
Determination of T0 by exponential fit
y = 0.018x + 5.5575
0
1
2
3
4
5
6
-130 -110 -90 -70 -50 -30 -10
Temperature [°C]
ln(K
Jc(1
T)-3
0)
1T-CT
100 Mpam .̂5
Linear (1T-CT)
T0
p1
030 TTpJc eCK
0ln)30ln( TTpCK JCmed p
CT
)30100ln(0
Example: 1T-C(T)-tests:
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17.05.2015 ASTM-Workshop Anaheim20
CF-Method
0
50
100
150
200
250
300
350
400
450
500
-40 -20 0 20 40 60 80
T - T0
KJc(
1T) [
MPa
*m0.
5]
MC 98 % pofLower-bound 1T
Ts
Ttest -T0/L Ttest -T0/U
0
50
100
150
200
250
300
350
400
450
500
-80 -70 -60 -50 -40 -30 -20 -10 0 10
Temperature [C]
KJc
(1T)
[MP
am0.
5 ]
MC, pof = 98 %Lower Bound 1TMC, pf= 50% 1.6T-SEB -valid1.6T-SEB -invalid
window of validity
T0
Principle: Example 1.6T:
-90
-80
-70
-60
-500 20 40 60 80 100
Thickness B [mm]
T0 [°
C]
by E1921from 2 invalid data
Comparison of CF-results from the two most invalid tests with standard T0:
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17.05.2015 ASTM-Workshop Anaheim21
Further changes in Appendix to E1921
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Master Curve Analyses of a Dynamic Toughness Round-RobinIAEA CRP8, 2006-2009
E. Lucon - NIST, Boulder CO (USA)*formerly at SCK•CEN, Mol (Belgium)
Workshop on “Fracture Toughness Testing and Evaluation at Elevated Loading Ratesin the Ductile-to-Brittle Transition Region of Ferritic Steels”
Anaheim CA, 17th May 2015
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Round-Robin Exercise (RRE)
11 participants signed up (1 did not supply results)
For each participant: 10 precracked and side-grooved JRQ specimens to be impact tested in the ductile/brittle transition regime
Impact speed: 1.2 m/s (~105 MPam/s)
Minimum response frequency of acquisition system: 100 kHz
Minimum sampling rate: 2 μs
Pre-test dimensional measurements: B, BN, W
Post-test dimensional measurements: ao, af
Test procedure: latest ESIS TC5 draft (Dec 2005) and future ISO/ASTM standard E1921 & E1820 (Annex A17)
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Master Curve results suppliedby the participants
Lab# N r ni
To(°C)
To(°C)
dK/dt(MPam/s)
1 10 9 1.40 -2.3 6.0 3.51E+05
2 10 9 1.40 1.6 6.0 3.21E+05
3 10 7 1.12 -9.9 6.8 3.70E+05
4 8 8 1.18 10.0 6.6 4.14E+05
5 10 10 1.57 2.1 5.7 3.29E+05
6 10 9 1.32 4.6 6.0 3.44E+05
7 10 8 1.33 -20.4 6.4 2.69E+05
8 10 9 1.40 -1.1 6.0 3.36E+05
9 10 7 1.07 -2.5 6.8 4.25E+05
10 10 9 1.40 -3.8 6.0 5.02E+05
Average values 1.32 -2.2 6.2 3.66E+05
All participants providedvalid To measurements
Max difference betweenindividual To = 30.4 °C
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0
50
100
150
200
250
300
350
-50 -25 0 25 50
T-To,lab (°C)
KJC
,1T (
MPa
m)
#1 #2 #3 #4 #5 #6 #7 #8 #9 #10
MC
1%
99%
95%
5%
Normalized representationof RRE Master Curve results
RRE results effectivelyfollow the Master Curveand its tolerance bounds
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0
50
100
150
200
250
-50 -40 -30 -20 -10 0 10 20 30Temperature (°C)
KJc
,1T
(MPa
m)
#1 #2#3 #4#5 #6#7 #8#9 #10Overall MC
95%
5%LB
MC
Overall Master Curve forall available results
N r niTo
(°C)To(°C)
98 85 13.21 -4.2 2.0
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-40
-30
-20
-10
0
10
20
30
Ref
eren
ce te
mpe
ratu
re T
o (°C
)
#1 #2 #3 #4 #5 #6 #7 #8
ALLLABS
2
#9 #10
Comparison between individual and overall reference temperatures
Outlier lab: KJc too high To too low
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Effects of removing the outlier laboratory (#7)
N r niTo
(°C)To(°C)
dK/dt(MPam/s)
88 77 11.98 -0.8 2.1 3.77E+05
Maximum difference between individual To drops to 19.8 °C
None of the reported To isstatistically different at the95% (±2s) confidence level
0
50
100
150
200
250
-50 -40 -30 -20 -10 0 10 20 30Temperature (°C)
K Jc,
1T (M
Pa
m)
#1 #2#3 #4#5 #6#8 #9#10 Overall MC
95%
5%LB
MC
-40
-30
-20
-10
0
10
20
30
Ref
eren
ce te
mpe
ratu
re T
o (°C
)
#1 #2 #3 #4 #5 #6 #7 #8
ALLLABS
2
#9 #10
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Common reanalysis of RRE results by ForschungsZentrum Rossendorf
(individual KJc and To)
Lab#
To,or(°C)
To,recalc(°C)
To(°C)
KJc(%)
1 -2.3 3.5 -5.8 9.1
2 1.6 3.7 -2.1 4.2
3 -9.9 -5.2 -4.6 17.5
4 10.0 1.6 8.4 -3.3
5 2.1 1.7 0.4 -2.6
6 4.6 11.8 -7.2 18.0
7 -20.4 -22.3 1.9 0.7
8 -1.1 -1.3 0.2 -0.1
9 -2.5 11.3 -13.8 28.5
10 -3.8 N/A N/A N/A
Average -2.2 0.5 -2.5 8.0
Large differences due to:
• Elastic component: different values of E and anvil span S• Plastic component: different interpretation of specimen compliance
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Possible requirementon the time to fracture (tf)
ISO & ASTM drafts at the time required for a quasi-static evaluation: tf > 5 (i.e. fracture after 5 oscillations)
Previously (Ireland et al, EPRI – 70’s): tf > 3 With:
If the requirement is not fulfilled a quasi-static evaluation (i.e. E 1820-type) cannot be used, and dynamic methods are required
For RRE specimens, = 54.7 μs and therefore: 3 = 164 μs and 5 = 274 μs
0
3.36 ' N SW E B CS
speed of sound in metal
specimen compliance
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Re-analysis of the RRE resultsaccording to the requirement
48 out of 98 tests (49%) do not satisfy the more stringent criterion (tf > 5)
Only 8 out of 98 tests (8%) do not satisfy the less stringent criterion (tf > 3)
Effect on Master Curve analyses
Application of the more stringent requirement can yield significantly lower (i.e. non-conservative) To
Replacing KJc with the value at 3 (52.5 MPam) or at 5 (90 MPam)
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Conclusions drawn from theRound-Robin Exercise (1)
• Results supplied by the participants were very consistent and showed reasonable scatter.
• The Master Curve approach was proven to be fully applicable to impact fracture toughness measurements obtained in the ductile-to-brittle transition region.
• The quality of impact fracture toughness measurements strongly depends on the quality of instrumented force values. Hence, a reliable calibration of the instrumented striker is of primary importance.
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Conclusions drawn from theRound-Robin Exercise (2)
• The guidelines provided by ISO/ASTM draft procedures and followed by RRE participants for test execution and data analysis proved to be reliable and easy to implement.
• The radius of the instrumented striker (2 mm or 8 mm) had negligible influence on the measured To.
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Recommendations forfuture work
• Establish correlations between crack arrest toughness (KIa) and dynamic/impact fracture toughness (KId).
• Compare lower bound Master Curves (corresponding to low fracture probabilities) obtained from dynamic/impact toughness measurements with the ASME KIR lower bound curve.
• Determine an “equivalent” dynamic RTTo,dyn
(similar to ASME Code Cases N-629 and N-631) for indexing the ASME lower bound KIR curve.
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Full details in:
http://www-pub.iaea.org/books/IAEABooks/8162/Master-Curve-Approach-
to-Monitor-Fracture-Toughness-of-Reactor-
Pressure-Vessels-in-Nuclear-Power-Plants
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VTT TECHNICAL RESEARCH CENTRE OF FINLAND LTD
Estimation of the loading rateKim Wallin VTT
Workshop on Fracture Toughness Testing and Evaluation at Elevated Loading Rates in the Ductile-to-Brittle Transition Region of Ferritic Steels.
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25/06/2015 2
ASTM E1921
The ASTM E1921 testing standard contains loading rate estimates for the SE(B) and C(T) specimens. It must be emphasized that the estimates are only valid for a case of linear-elastic loading, or in the linear part of the load-displacement curve. The estimates are in the standard given in a tabulated form only, but they are based on the principle represented by Eqs. They perform a simple transformation of displacement into load via the compliance function and the transformation of load to stress intensity factor via the standard KI calibration functions.
I E1921
LL
E S / W f a / WK :SE(B)
W C a / W)
I E1921
LL
E f a / WK : C(T)
W C a / W)
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25/06/2015 3
Elastic plastic case
In the elastic regime, there is a linear dependency between specimen displacement rate and fracture mechanical loading rate, but this dependency is lost with the development of plasticity in the specimen. The linear-elastic equations overestimate the loading rate, when the specimens experience plasticity. Accounting for the effect of plasticity on the loading rate requires a relation between elastic-plastic crack driving force and total displacement.
f
140MPa1
SE(B) f(a / W 0.4) : J (W a) 1.4W
f
140MPa1
C(T) fa(a / W 0.5) : J (W a) 1.4 1.6 0.6W W
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25/06/2015 4
Post test estimate
Lucon and Scibetta concluded that the optimum post test loading rate estimate is simply obtained by dividing the facture toughness value with the time needed to reach the fracture toughness. This “average” loading rate corresponded very well to the mean value of dK/dt during the test. They did note, however, that the “average” loading rate cannot be estimated for tests containing e.g. partial unloadings.
A new analytical procedure is presented here. It can be used to estimate either the instantaneous or average loading rate allowing for unloadings.
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25/06/2015 5
New analytical procedure
f
f
ff
est 0.5 70MPa140MPa
f
70MPa1.4 b E ' 0.5W SE(B)
Ka / W 0.3...0.7
J1.4 b
f
f
ff
est 0.5 70MPa140MPa
f
a 70MPa1.4 b 1.6 0.6 E ' 0.5W W C(T)
Ka / W 0.4...0.7
Ja1.4 b 1.6 0.6W
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25/06/2015 6
Comparison of relation between elastic-plastic and linear-elastic loading rate estimates.
20 40 60 80 100 120 140 160 180 200 2200.3
0.4
0.5
0.6
0.7
0.8
0.9
1.0
1.1
d/dt = 0.2 mm/min d/dt = 150 mm/min d/dt 1.4 m/s
.
.
Kes
t / K
E192
1
KJC [MPam]
Lucon and Scibetta data
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25/06/2015 7
Comparison of elastic-plastic loading rate estimate with experimental “average” loading rate estimate
20 40 60 80 100 120 140 160 180 200 2200.4
0.6
0.8
1.0
1.2
1.4
1.6
1.8
2.0
d/dt = 0.2 mm/min d/dt = 150 mm/min d/dt 1.4 m/s
Kes
t / (K
Jc/t c)
KJC [MPam]
.
Lucon and Scibetta data
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25/06/2015 8
Comparison of mean elastic-plastic loading rate estimate with experimental “average” loading rate estimate
Lucon and Scibetta data
20 40 60 80 100 120 140 160 180 200 2200.4
0.6
0.8
1.0
1.2
1.4
1.6
1.8
2.0 d/dt = 0.2 mm/min d/dt = 150 mm/min d/dt 1.4 m/s
Kes
t-mea
n / (K
Jc/t c)
KJC [MPam]
.
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25/06/2015 9
Conclusions
It is debateable whether the mean loading rate or the instantaneous loading rate is the more appropriate parameter to describe loading rate. The difference between the two can, in the worst situation, be of the order of 50 %. This difference is still comparatively small when considering the effect of loading rate on fracture toughness.
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© Fraunhofer-Institut für Werkstoffmechanik IWM
ASTM E1921/Anaheim/May2015/Boe
Statistical Distribution of Dynamic Fracture Toughness Values, Shape of Dynamic Master Curves and Crack Tip Loading Rates
Implications for a High Rate Appendix of ASTM E1921
Wolfgang Böhme
Thomas Reichert
Johannes Tlatlik
Fraunhofer Institute for Mechanics of Materials IWM, Freiburg, Germany ([email protected])
Workshop on Fracture Toughness Testing and Evaluation at Elevated Loading Rates in the Ductile-to-Brittle Transition Region of Ferritic SteelsSponsored by E080706 Task Group on Ductile-Brittle TransitionAnaheim, May 17th, 2015
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© Fraunhofer-Institut für Werkstoffmechanik IWM
2 ASTM E1921/Anaheim/May2015/Boe
Experience obtained during two joint projects ofFraunhofer IWM (Freiburg) & MPA (Stuttgart)
„Dynamic Master-Curves (MC) for high loading rates“(Phase 1 in 2010-2013 and Phase 2 in 2014-2016)
Determination of Dynamic Fracture Toughness Values KJc,d(T, dK/dt) at elevated crack tip loading rates:
dK/dt = 3 x 103 MPa m0,5 s-1 ……. 5 x 106 MPa m0,5 s-1
according to ASTM E1820 and E1921
Results will be presented in more detail at the ASTM/ESIS-conference this week:
Mayer (MPA/Stuttgart) Thursday, May 21st, 1:30 PM
Böhme & Reichert (IWM/Freiburg) Thursday, May 21st, 2:20 PM
Background
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© Fraunhofer-Institut für Werkstoffmechanik IWM
3 ASTM E1921/Anaheim/May2015/Boe
Material and Specimens
Cracks in T-S-orientation
(2/3 T ≤ ao ≤ 3/4 T)
22 NiMoCr 3 7 (similar to A 508 Cl.2) T0,stat = -68 °C
RTNDT = -20 °C
Material is the same as in previous investigations on quasistatic Master Curves:[1] Hohe, J., Siegele, D. et al.: Kritische Überprüfung des Masterkurven-Ansatzes im Hinblick auf die Anwendung bei deutschen Kernkraftwerken,
Forschungsvorhaben BMWi-FKZ 1501239, Abschlussbericht IWM Freiburg, 2004.
[2] Roos, E., Eisele, U., et al.: Kritische Überprüfung des Masterkurven-Ansatzes im Hinblick auf die Anwendung bei deutschen Kernkraftwerken, Forschungsvorhaben BMWi-FKZ 1501240, Abschlussbericht MPA Stuttgart, Februar 2006.
Location for specimen sampling
originally provided for Biblis C and well qualified
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© Fraunhofer-Institut für Werkstoffmechanik IWM
4 ASTM E1921/Anaheim/May2015/Boe
High Rate Experiments and Measuring TechniquesCrack Mouth Opening Displacement CMOD
Digital Image Correlation (DIC: ARAMIS) to measure CMOD
Strain gauge
CMOD
Force (Striker)
with high-speed cameraand DIC-evaluation
IWMMPACT25-Probe
Grundplatte
Montagefläche
FaserbündelStrichgitter
Querschnitt durch dasFaserbündel:
Strichgitter bzw. Maßverkörperung
Glasfaserbündel inMetallferrule
Beleuchtung Beleuchtung
Messung
Strain gauges for local forcemeasurement and detection
of crack initiation (backside)
C(T)25 specimen
Mounting surface
Base plate
Cross section through fiber bundle
Lighting
Measurement
Lighting
Fiber glass bundle in metal-ferrule
SE(B) 40/20, v0 = 0.6 m/s, dK/dt = 2·105 MPa√m s-1, T = -20°C
Grating resp. measurement scale
Grating Fiber bundle
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© Fraunhofer-Institut für Werkstoffmechanik IWM
5 ASTM E1921/Anaheim/May2015/Boe
Dynamic Fracture Toughness KJc,dEvaluation at Elevated Loading Rates
Determination of KJc,d based on locally measured Force- and CMOD-signals
Evaluation of the Force-CMOD curve according to ASTM E1921
AeAp
Loca
lFor
ce (s
trai
nga
uge)
[kN
]
CMOD [mm]
P
CCMOD
1
SE(B)40/20v0 = 2.5 m/sdK/dt = 3·105 MPa√m s-1
Loca
l for
ce (s
trai
n ga
uge)
[kN
]
Global force (striker) [kN]
quasi-dynamic calibration at intermediate loading rates KJc,d (Ap, P)
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© Fraunhofer-Institut für Werkstoffmechanik IWM
6 ASTM E1921/Anaheim/May2015/Boe
Force-Time Curves SE(B)10/10, a/W = 0.3, T = -20 °C
0.10
ASTM E1820 requirement tf > tW violated at dK/dt = 3·106 MPa√m s-1
v0 = 1 m/sdK/dt = 3·105 MPa√m s-1
v0 = 0.6 m/sdK/dt = 2·105 MPa√m s-1
v0 = 6 m/sdK/dt = 3·106 MPa√m s-1
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© Fraunhofer-Institut für Werkstoffmechanik IWM
7 ASTM E1921/Anaheim/May2015/Boe
Force vs. Displacement (LLD) or CMOD SE(B)10/10, a/W = 0.3, T = -20 °C
CLLD1
CCMOD
1 CCMOD
1
v0 = 1 m/sdK/dt = 3·105 MPa√m s-1
v0 = 0.6 m/sdK/dt = 2·105 MPa√m s-1
v0 = 6 m/sdK/dt = 3·106 MPa√m s-1
Even at dK/dt = 3·106 MPa√m s-1, the local measurements result in F(CMOD)-curves which can be evaluated according to ASTM E1921
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8 ASTM E1921/Anaheim/May2015/Boe
High Rate Fracture Toughness KJc,d5% Lower Bound Curves vs. Temperature
KJc,d(1T)-data and corresponding 5%-MC’s of all dynamic tests at various crack tip loading rates dK/dt Quasistatic KJc,5%
Rate-dependent KJc,d,5%
KIR lower bound curve
some 5%-fractile curves are below the KIR(RTNDT)-curve
dK/dt in MPa√m s-1
All fracture toughness data meet the validity requirements of ASTM E1921 All fracture toughness values KJc,d(1T) are above the KIR(RTNDT) curve
IWM/Freiburg: SE(B)10/10 SE(B)40/20
MPA/Stuttgart: 1T-C(T)25
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9 ASTM E1921/Anaheim/May2015/Boe
High Rate Reference TemperaturesT0,Xvs. dK/dt Dynamic Master Curve reference temperature T0,X vs. loading rate T0,X: Rate dependent
reference temperature evaluated based on Weibull distribution (according to ASTM E1921)
T0,KIR: KIR-corresponding Master Curve reference temperature,
ASTM E1921 estimate:
15,273ln
15,273.,0,0
X
TT statest
x
09,166,1.,0
72219015,273
exp9,9,0 statT
YSstatT with
ASTM E1921 estimate is reasonable for some but not for all series of tests!
Are there two distinct collectives: a brittle and a more ductile one???
SE(B)-Results: IWM/Freiburg
C(T)-Results: MPA/Stuttgart
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10 ASTM E1921/Anaheim/May2015/Boe
Correction to T0,est.
15,273
ln15,273,0
,0
XT
T statX
est
09.166,1,0
72219015,273
exp9,9,0 statT
ysstatT
Ref: Wallin, K., „Effect of Strain Rate on the Fracture Toughness Reference Temperature T0 for Ferritic Steels“, in Recent Advances on Fracture, R.K. Mahidhara, A.B. Geltmacher and K. Sadananda, eds., The Mineral, Metals & Materials Society, 1997
)(,0 XT dyn ASTM E 1921-14a eq. (3)
ASTM E 1921-14a eq. (4)
X = dK/dt in MPa√ms-1
with
and
Estimated value of T0,X
correction:YS(RT)
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11 ASTM E1921/Anaheim/May2015/Boe
Correction to T0,est.Re
ference tempe
rature T
0,AS
TMin °C
Loading rate dK/dt in MPa√m s‐1
ASTM E1921‐11a estimate(with T0,stat. = ‐68°C, YS(T0,stat.))
ASTM E1921‐11a estimate(with T0,stat. = ‐68°C, YS(RT))
Corrected:
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12 ASTM E1921/Anaheim/May2015/Boe
High Rate Fracture Toughness Datavs. T-T0
Fracture toughness values KJc,d(1T) of all dynamic tests normalized to T0
and 5%-, 50%- and 95%-fractile Master Curves
All fracture toughness data meet the validity requirements of ASTM E1921
SE(B)-Results: IWM/Freiburg
C(T)-Results:MPA/Stuttgart
dK/dt in MPa√m s-1
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13 ASTM E1921/Anaheim/May2015/Boe
Deviation of High Rate Reference Temperaturefrom ASTM-Estimate: T0,X –T0,est
two collectives?
bimodal fracture?
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14 ASTM E1921/Anaheim/May2015/Boe
Statistical Analysis
Statistical distribution of fracture toughness KJc,d(1T) values data set with 32 dynamic SE(B)10/10-tests at dK/dt ≈ 3·105 MPa√m s-1
The lognormal-distribution is in better agreement with the experimental data set compared to the Weibull-distribution of ASTM E1921 (b = 4, Kmin = 20 MPa√m)
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15 ASTM E1921/Anaheim/May2015/Boe
Alternative T0,X-EvaluationLognormal-Distribution Alternative Master Curve evaluation assuming a lognormal-distribution
(with σ = 0.21, determined from the statistical analysis)
Some of the 5%-curves are still below the KIR(RTNDT) curve at higher temperatures
dK/dt in MPa√m s-1
SE(B)-Results: IWM/Freiburg
C(T)-Results: MPA/Stuttgart
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16 ASTM E1921/Anaheim/May2015/Boe
Alternative Master Curve evaluation with rate-dependent shape factor p Adjustment of value p is based on a multi-
temperature Master Curve evaluationof a large data set of test results [3] with
different SE(B) specimen widths: 0.4T, 0.8T, 1.6T and 3.2T
crack loading rates up to ≈ 105 MPa√m s-1
Alternative T0,X-EvaluationShape of High Rate Master Curves
Schindler, H. J. and Kalkhof, D. (2012). “Effect of loading rate on shape of the ductile-to-brittle transition curve”, presented at ASTM Committee E08 Meeting, Nov. 2012, Tampa, Florida, USA.
030,TTp
medJc eCTK
A value of p = 0.030 was used below for alternative dynamic Master Curve evaluations
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17 ASTM E1921/Anaheim/May2015/Boe
Alternative T0,X-EvaluationShape of High Rate Master Curves
Comparison of MC-evaluation according to ASTM 1921 with alternative MC-evaluation with p = 0.030 Two SE(B) 40/20 test series at two different test temperatures and
comparable crack loading rate dK/dt = 3·106 MPa√m s-1 and 5·106 MPa√m s-1
improved description for both series of testswith p = 0.030
MC according to ASTM E1921p = 0.019
MC with p = 0.030
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18 ASTM E1921/Anaheim/May2015/Boe
DiscussionAlternative T0,X-Evaluation, MC-shape
Alternative Master Curve evaluation with p = 0.030
5% Master Curves are now above the KIR(RTNDT) curve and closer to the data
dK/dt in MPa√m s-1
SE(B)-Results: IWM/Freiburg
C(T)-Results: MPA/Stuttgart
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19 ASTM E1921/Anaheim/May2015/Boe
High Rate Fracture Toughness KJc,d5% Lower Bound Curves vs. Temperature
dK/dt in MPa√m s-1
Best approach so far: Weibull und p = 0.030
IWM/Freiburg: SE(B)10/10 SE(B)40/20
MPA/Stuttgart: 1T-C(T)25
Weibull Lognormal Weibull und p = 0.030
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20 ASTM E1921/Anaheim/May2015/Boe
Proposals on the Evaluation of High Rate Tests
Our results lead to the following
Suggestions on a High Rate Appendix of ASTM E1921:
In addition to the “quasistatic evaluation” based on the Weibull distribution it should be opened to other statistical evaluations:
e.g.: lognormal, as in ASTM E1221 (Crack Arrest),
and/or
it should be opened to a rate dependent shape factor “p” :
e.g.: as proposed by Schindler/Kalkhofin order to take into account adiabatic heating at the crack tip
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21 ASTM E1921/Anaheim/May2015/Boe
Crack Tip Loading Rate dK/dt or dJ/dtDefinitions According to Various Standards
t
FA
0.5FA
FBS 7448-3 (2005)
dJP/dt with tP and plasticwork Up
Fc
tp
dKI/dt = slope K(0.5FA) till K(FA)
t
ASTM E1820 (2013)ASTM E1921 (2014)
J
t
JQ
linear fit
tQ
(dJ/dt)I = slope 0.5JQ till JQdK/dt = KJc,d/tf
KJ
t
KJc,d
tf
FFc
t
FFQ
0.5JQ
onset of stable crack extension
(dJ/dt)T = slope JQ till JQ+0.5(Jmax-JQ)
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22 ASTM E1921/Anaheim/May2015/Boe
Idea: Definition of crack tip loading rate similarily toISO 26203-2 (2011)
The various definitions of strain rates such as
the time-dependent strain rate (3), the characteristic strain rate (2), and the limits for a high rate test at a sufficient
constant strain rate (dashed box) are adopted from:Böhme, W.: FAT-Richtlinie „Dynamische Werkstoffkennwerte für die Crashsimulation“, MP Materials Testing, Carl Hanser Verlag, München, Vol. 50 (4), S. 199 – 205 (2008)
Idea: Development of similar definitions for the crack tip loading rate for the high rate appendix of ASTM E1921
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23 ASTM E1921/Anaheim/May2015/Boe
Evaluation of Crack Tip Loading Ratesbased on KJ(t)
Type: SE(B) 10x10Machine: PendulumTemp.: 0 °Cv0: 1.2 m/sKJd: 140.7 MPam0.5
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24 ASTM E1921/Anaheim/May2015/Boe
Evaluation of Crack Tip Loading Ratesbased on J(t)
Type: SE(B) 10x10Machine: PendulumTemp.: 0 °Cv0: 1.2 m/sKJd: 140.7 MPam0.5
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25 ASTM E1921/Anaheim/May2015/Boe
Proposal on the Crack Tip Loading Rate
Calculation of a nominal value: dK/dt|nom (based on vo and specimen size) Evaluation of the actual dKJ/dt(t)-curve: dKJ/dt(t)|actual
Determination of a characteristic value, e.g.: dKJ/dt|char = mean {dKJ/dt (t = t0.5FA … tFA)} Validity-Requirement: |dKJ/dt(t)|actual - dKJ/dt|char | < 0.40 x dKJ/dt|char
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26 ASTM E1921/Anaheim/May2015/Boe
SummaryProposals for ASTM E1921 Annex “High Rate”
Our results lead to the following suggestions: In addition to the “quasistatic evaluation” based on the Weibull distribution,
the high rate appendix should be opened to other statistical evaluations:
E.g.: lognormal, as in ASTM E1221 (Crack Arrest)
Rate dependent shape factor “p”, as proposed by Schindler/Kalkhofin order to take into account adiabatic heating at the crack tip
The definition of the crack loading rate dK/dt should be extended:
Calculation of a nominal value: dK/dt|nom
Evaluation of the actual dKJ/dt(t)-curve: dKJ/dt(t)|actual
Determination of a characteristic value, e.g.: dKJ/dt|char = mean {dKJ/dt (t = t0.5FA … tFA)} Validity-Requirement: |dKJ/dt(t)|actual - dKJ/dt|char | < 0.40 x dKJ/dt|char
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27 ASTM E1921/Anaheim/May2015/Boe
Acknowledgement
The research project
“Analysis and Validation of Fracture Mechanical Assessment Methods under Dynamic Loading”
is funded by the German Federal Ministry of Economic Affairs and Energy (Project No. 1501472A) on basis of a decision by the German Bundestag.
The project is a cooperation of Fraunhofer Institute for Mechanics of Materials, IWM, Freiburg and Materials Testing Institute University of Stuttgart, MPA, Germany
Thank you for your attention!