Astm stp 1189 1993

STP 1189 Fracture Mechanics: Twenty-Third Symposium Ravinder Chona, editor ASTM Publication Code Number (PCN) 04-011890-30 AsT 1916 Race Street Philadelphia, PA 19103 Copyright by ASTM Int'l (all rights reserved); Wed Dec 23 19:12:57 EST 2015 Downloaded/printed by University of Washington (University of Washington) pursuant to License Agreement No further reproductions authorized ASTM Publication Code Number (PCN) 04-011890-30 ISBN: 0-8031-1867-8 ISSN: 1040-3094 Copyright 1993 AMERICAN SOCIETY FOR TESTING AND MATERIALS, Philadelphia, PA All rights reserved This material may not be reproduced or copied, in whole or in part, in any printed, mechanical, electronic, film, or other distribution and storage media, without the written consent of the publisher Photocopy Rights Authorization to photocopy items for internal or personal use, or the internal or personal use of specific clients, is granted by the AMERICAN SOCIETY FOR TESTING AND MATERIALS for users registered with the Copyright Clearance Center (CCC) Transactional Reporting Service, provided that the base fee of $2.50 per copy, plus $0.50 per page is paid directly to CCC, 27 Congress St., Salem, MA 01970; (508) 744-3350 For those organizations that have been granted a photocopy license by CCC, a separate system of payment has been arranged The fee code for users of the Transactional Reporting Service is 0-8031-1867-8/93 $2.50 + 50 Peer Review Policy Each paper published in this volume was evaluated by three peer reviewers The authors addressed all of the reviewers' comments to the satisfaction of both the technical editor(s) and the ASTM Committee on Publications The quality of the papers in this publication reflects not only the obvious efforts of the authors and the technical editor(s), but also the work of these peer reviewers The ASTM Committee on Publications acknowledges with appreciation their dedication and contribution to time and effort on behalf of ASTM Printedin Baltimore,MD September1993 Copyright by ASTM Int'l (all rights reserved); Wed Dec 23 19:12:57 EST 2015 Downloaded/printed by University of Washington (University of Washington) pursuant to License Agreement No further reproductions authorized Foreword The Twenty-Third National Symposium on Fracture Mechanics was held on 18-20 June 1991 in College Station, Texas ASTM Committee E24 on Fracture Testing was the sponsor Ravinder Chona, Texas A&M University, presided as symposium chairman and is the editor of this publication Copyright by ASTM Int'l (all rights reserved); Wed Dec 23 19:12:57 EST 2015 Downloaded/printed by University of Washington (University of Washington) pursuant to License Agreement No further reproductions au Contents Overview JERRY L SWEDLOW MEMORIAL LECTURE Structural Problems in Search of Fracture Mechanics Solutions J M BARSOM ELASTIC-PLASTIC FRACTURE M E C H A N I C S - - A N A L Y S E S AND CONSTRAINT ISSUES Crack Initiation Under Generalized Plane-Strain Conditions D g M SHUM AND J G MERKLE 37 Experimental Relationship Between Equivalent Plastic Strain and Constraint for Crack Initiation w G REUTER, W R LLOYD, R L WILLIAMSON, J A SMITH, AND J S EPSTEIN 55 A Comparison of Weibull and ~/1~Analyses of Transition Range D a t a - D E McCABE 80 Near-Crack-Tip Transverse Strain Effects Estimated with a Large Strain Hollow Cylinder Analogy J G MERKLE 95 The Conditions at Ductile Fracture in Tension T e s t s - - g J DEXTER AND S ROY 115 Developing J-R Curves Without Displacement Measurement Using Normalization g LEE AND J D LANDES 133 Evaluation of Dynamic Fracture Toughness Using the Normalization M e t h o d - R HERRERA, G CARCAGNO, AND L A DE VEDIA 168 Asymptotic Analysis of Steady-State Crack Extension of Combined Modes I and III in Elastic-Plastic Materials with Linear Hardening H YUAN AND A CORNEC An Asymptotic Analysis of Static and Dynamic Crack Extension Along a Ductile Bimaterial Interface/Anti-Plane Case H YUAN AND K.-H SCHWALSE 185 208 Copyright by ASTM Int'l (all rights reserved); Wed Dec 23 19:12:57 EST 2015 Downloaded/printed by University of Washington (University of Washington) pursuant to License Agreement No further reproductions authorized ELASTIC-PLASTIC FRACTURE M E C H A N I C S - - A P P L I C A T I O N S An Application Methodology for Ductile Fracture Mechanics J D LANDES, Z ZHOU, AND K H BROWN 229 Growth of Surface Cracks During Large Elastic-Plastic Loading Cycles-R C McCLUNG, S J HUDAK, JR., M L BARTLETT, AND J H FITZGERALD 265 Level-3 Crack-Tip Opening Displacement (CTOD) Assessment of Welded Wide Plates in Bending Effect of Overmarching Weld metal s BERGE, O I EIDE, AND M FUJIKUBO 284 Limit Pressure Analysis of a Cylindrical Vessel with Longitudinal Crack-X CHEN, P ALBRECHT, AND J JOYCE 310 A Deep Part-Through All-Around Circumferential Crack in a Cylindrical Vessel Subject to Combined Thermal and Pressure Load L CHEN, P C PARIS, AND H TADA 330 Study of a Crack-Tip Region Under Small-Scale Yielding Conditions-C A SCIAMMARELLA, A ALBERTAZZI, JR., AND J' MOURIKES Fracture Properties of Specially Heat-Treated ASTM A508 Class Pressure Vessel Steei D J ALEXANDER AND R D CHEVERTON 344 365 LINEAR-ELASTIC FRACTURE M E C H A N I C S - - A N A L Y S E S Cracked Strip Problem Subjected to a Nonsymmetric Transverse Loading by a Stamp o s YAH~jl AND Y DEMIR 383 Stress Intensity Factor Solutions for Partial Elliptical Surface Cracks in Cylindrical Shafts K.-L CHEN, A.-Y KUO, AND S SHVARTS 396 Analysis of Circumferential Cracks in Circular Cylinders Using the WeightFunction Method s R METTU AND R G FORMAN 417 LINEAR-ELASTIC FRACTURE M E C H A N I C S - - A P P L I C A T I O N S Environmentally Controlled Fracture of an Overstrained A723 Steel Thick-Wall C y l i n d e r - - J H UNDERWOOD, V J OLMSTEAD, J C ASKEW, A A KAPUSTA, AND G A YOUNG 443 Fatigue Lifetimes for Pressurized, Eroded, Cracked, Autofrettaged Thick Cylinders A P PARKER, R C A PLANT, AND A A BECKER 461 An Evaluation of Fracture Mechanics Properties of Various Aerospace Materials J A HENKENER, V B LAWRENCE, AND R G FORMAN 474 Copyright by ASTM Int'l (all rights reserved); Wed Dec 23 19:12:57 EST 2015 Downloaded/printed by University of Washington (University of Washington) pursuant to License Agreement No further reproductions autho Leak-Before-Break and Fatigue Crack Growth Analysis of All-Steel On-Board Natural Gas Cylinders G s BHUYAN FATIGUE AND NONDESTRUCTIVE 498 EVALUATION Intergranular Delamination and the Role of Artificial Aging Conditions on the Fracture of an Unreerystallized Aluminum-Lithium-Zirconium (AI-Li-Zr) Alloy P c M c K E I G H A N , B M H I L L B E R R Y , A N D T H S A N D E R S , JR 515 Development of Fatigue Life Prediction Program for Multiple Surface Cracks-536 Y - J K I M , Y.-S C H O Y , A N D J - H L E E Fatigue Crack Growth Behavior of Titanium Aluminide Ti-25AI-25Nb-551 S J B A L S O N E , D C M A X W E L L , A N D T F B R O D E R I C K Fatigue Crack Growth Rate Measurements in Aluminum Alloy Forgings: Effects of Residual Stress and Grain Flow R w B U S H , R J BUCCI, P E M A G N U S E N , 568 A N D G W K U H L M A N Fatigue Crack Growth Analysis of Structures Exposed to Fluids with Oscillating Temperature Distributions s CHATTOPADHYAY 590 Development of a Fatigue Crack Growth Rate Specimen Suitable for a Multiple Specimen Test Configeration F g D E S H A Y E S A N D W H H A R T T 598 Ultrasonic Characterization of Fatigue Crack Closure R B THOMPSON,O BUCK, 619 A N D D K R E H B E I N COMPOSITES AND NONMETALS Dehonding Force of a Single Fiber from a Composite Body s.-s LEO AND 635 J L H I L L A Finite-Element Analysis of Nonlinear Behavior of the End-Loaded Split Laminate Specimen c R C O R L E T O A N D H A H O G A N 649 Investigating the Near-Tip Fracture Behavior and Damage Characteristics in a Particulate Composite Material c.-T LIU 668 Modeling the Progressive Failure of Laminated Composites with Continuum Damage Mechanics o c LO, D H ALLEN,AND C E HARRIS 680 Effect of Fiber-Matrix Debonding on Notched Strength of Titanium Metal-Matrix Composites c A B I G E L O W A N D W S J O H N S O N 696 Evolution of Notch-Tip Damage in Metal-Matrix Composites During Static Loading J G B A K U C K A S , J R , J A W E R B U C H , T - M T A N , A N D A C W 713 LAU Copyright by ASTM Int'l (all rights reserved); Wed Dec 23 19:12:57 EST 2015 Downloaded/printed by University of Washington (University of Washington) pursuant to License Agreement No further reproductions authorized Experimental Verification of a New Two-Parameter Fracture M o d e l - D E RICHARDSON AND J G GOREE 738 Translaminate Fracture of Notched Graphite/Epoxy L a m i n a t e s - - c E HARRIS 751 A N D D H M O R R I S Near-Tip Behavior of Particulate Composite Material Containing Cracks at Ambient and Elevated T e m p e r a t u r e s - - c w SMITH, L WANG, H MOUILLE, 775 A N D C - T LIU Static Fatigue in Dilatant-Zone-Toughened Ceramics K DUAN, B COTTERELL, 788 A N D Y - W MAI Fracture Energy Dissipation Mechanism of Concrete z GUO, J.-H YON, N M H A W K I N S , A N D A S K O B A Y A S H I 797 P R O B A B I L I S T I C A N D D Y N A M I C ISSUES Probabilistic Fracture Mechanics Evaluation of Local Brittle Zones in HSLA-80 Steel Weldments L ~ EISELSTEIN, D O H A R R I S , T M S C O O N O V E R , A N D C A R A U 809 Rapid Crack Propagation in Polyethylene Pipes: The Role of Charpy and Dynamic Fracture Testing P s L E E V E R S , P Y A Y L A , A N D M A W H E E L 826 Effects of Sample Size and Loading Rate on the Transition Behavior of a Ductile Iron (DI) Alloy R S A L Z B R E N N E R A N D T B C R E N S H A W 840 Author Index 859 Subject Index 861 Copyright by ASTM Int'l (all rights reserved); Wed Dec 23 19:12:57 EST 2015 Downloaded/printed by University of Washington (University of Washington) pursuant to License Agreement No further reproductions authorized STP1189-EB/Sep 1993 Overview The National Symposium on Fracture Mechanics has evolved, since its beginnings in 1965, into an annual forum for the exchange of ideas related to the fracture of engineering materials The Twenty-Third National Symposium carried on this tradition and was held in College Station,Texas, on 18-20 June 1991 The symposium was sponsored by ASTM Committee E24 on Fracture Testing, with the cooperation and support of the Department of Mechanical Engineering at Texas A & M University The diversity of interests and the wide range of problem areas in which fracture mechanics can play a role in ensuring structural integrity was reflected in the topic areas that were addressed in the 63 papers that were presented at the symposium The symposium drew I l0 attendees from 18 countries around the world, highlighting the strong international flavor that the National Symposium and ASTM's fracture-related activities have acquired over the years The efforts of the authors of the manuscripts submitted for publication and the diligence of the persons entrusted with the task of peer-reviewing these submittals have resulted in the compilation of papers that appear in this volume These papers represent a broad overview of the current state of the art in fracture mechanics research and should serve as a timely recording of advances in basic understanding, as a compilation of the latest test procedures and results, as the basis of new insights and approaches that would be of value to designers and practitioners, and as a stimulus to future research The volume opens with the paper by Dr John M Barsom, who delivered the Second Annual Jerry L Swedlow Memorial Lecture at this symposium Barsom's presentation addressed the need for a better understanding of the basic issues involved in several different structural applications of fracture mechanics technology As such, it serves as a road map for future directions and is a highly appropriate tribute to the memory of the individual who played a very important role in shaping the National Symposium into the forum that it is today Following the Swedlow Lecture are forty-five papers that have been broadly grouped into seven topical areas, based on the main theme of each paper These groupings are, however, only intended as an aid to the reader, since no classification can ever be absolute Topics of interest to a particular reader will therefore be found throughout this volume, and the reader is encouraged to consult the Index for the location of topics of specific interest The groupings that have been adopted are detailed next and are similar to the broad categories that were used to divide the presentations into coherent topical sessions at the symposium itself The first group of nine papers addresses analytical and constraint-related issues in elastic-plastic fracture mechanics, with much of the emphasis being on topics related to transition range behavior The next section of seven papers also deals with elastic-plastic fracture, but emphasizes applications Following this are two sections that both address linear-elastic fracture mechanics, with a group of three papers emphasizing analytical aspects, and a group of four papers that are more applications oriented Subcritical crack growth and nondestructive evaluation methods are the joint themes of the next group of eight papers Following this are eleven papers addressing the fracture of composites and nonmetals, a topic area that is receiving increasing attention from the fracture community and which had significant repre- Copyright*by1993 by ASTM International www.astm.org Copyright ASTM Int'l (all rights reserved); Wed Dec 23 19:12:57 EST 2015 Downloaded/printed by University of Washington (University of Washington) pursuant to License Agreement No further reproductions authorize FRACTURE MECHANICS: TWENTY-THIRD SYMPOSIUM sentation at a National Symposium for the first time Finally, a grouping of three papers dealing with probabilistic and dynamic issues closes out this volume In addition to the technical program, a highlight of the symposium was the presentation by Dr George R Irwin of the 1991 medal named in his honor to Dr Hugo A Ernst of the Georgia Institute of Technology, and the presentation by Dr C Michael Hudson, Chairman of Committee E24, of the 1991 Award of Merit and designation of Fellow of ASTM to Dr Richard P Gangloff of the University of Virginia The Symposium Organizing Committee consisting of Prof T L Anderson, Prof R Chona, Dr J P Gudas, Dr W S Johnson, Jr., Prof V, K Kinra, Prof J D Landes, Mr J G Merkle, Prof R J Sanford, and Mr E T Wessel are pleased to have been a part of this very significant technical activity The committee and the symposium chairman in particular would like to express their appreciation of the support received from the authors of the various papers presented at the symposium; of the thoroughness of the peer-reviewers who have played a major role in ensuring the technical quality and archival nature of the contents of this publication, of the efforts by various ASTM staffto help make the symposium and this volume a success, particularly Mr P J Barr, Ms L Hanson, Ms H M Hoersch, Ms M T Pravitz, Ms D Savini, and Ms N Sharkey; and of the support, encouragement, and assistance extended by Prof W L Bradley, Head of the Department of Mechanical Engineering at Texas A&M University Finally, the symposium chairman would like to especially thank Ms Katherine A Bedford, Staff Assistant at Texas A&M University, for all her contributions during the planning of the symposium and the preparation of this volume Ravinder Chona Department of Mechanical Engineering,Texas A&M University,CollegeStation, Texas; symposium chairman and editor Copyright by ASTM Int'l (all rights reserved); Wed Dec 23 19:12:57 EST 2015 Downloaded/printed by University of Washington (University of Washington) pursuant to License Agreement No further reproductions authorized 852 FRACTUREMECHANICS:TWENTY-THIRD SYMPOSIUM FIG Montage ofJhacture surface ofB = cm specimen tested at elevated rate at - 29"C Fracture initiated in cleavage then changed to ductile tearing from sample to sample in a multiple-specimen test) These are preliminary results based on detailed measurements of selected specimens These measurements must be extended to all of the specimens tested at - 29~ to determine whether this difference (that is, different amount of cleavage at initiation) is always present Discussion The experiments reported in the previous section demonstrate a clear effect of temperature and loading rate on the initiation fracture toughness In addition, there seems to be an effect of size on the fracture toughness behavior in the vicinity of the transition region The effects of temperature and loading rate are clearly shown in Fig Considering first only a single loading rate (and constant specimen size), there is a narrow temperature range through which the initiation fracture toughness undergoes a significant decrease with decreasing temperature This decrease in toughness is accompanied by a change in fracture mechanism from ductile tearing to (brittle) cleavage For the slow loading rate tests, the transition between high and low toughness takes place in the - to - 120"C range (Fig 3) For the high rate testing, the change occurs over the range of > to - 40~ (Fig 3) Comparing curves for static loading rates with the high loading rate curves indicates that the major effect of increased loading rate is to cause the ductile-brittle transition range to occur at higher temperatures The increase in loading rate may also broaden the temperature range between fully ductile and fully brittle behavior The effect of loading rate on the level of fracture toughness on either the upper- or lower-"shelf" regimes seems to be minimal There was no measurable effect on the toughness level o f the lower shelf, while there may be a slight enhancement in the upper-shelf toughness (for the high loading rate) once fully ductile tearing is attained (see for example, the data for the 1-cm-thick specimen at + 25~ The small increase in toughness with increased loading rate may be expected because of an increase in yield strength as the loading rate is raised The Copyright by ASTM Int'l (all rights reserved); Wed Dec 23 19:12:57 EST 2015 Downloaded/printed by University of Washington (University of Washington) pursuant to License Agreement No further reproductions authorize SALZBRENNER AND CRENSHAW ON FRACTURE TOUGHNESS OF DUCTILE IRONS 853 effects o f temperature and loading rate on the fracture toughness of this ferritic DI alloy are similar to those that have been commonly observed in other iron-based alloys [ 11] The observations associated with sample size that are reported in this paper are not as straight forward to describe as the rate and temperature effects In static rate testing, the B = and cm specimens show that transition behavior takes place in the - 90 to - 120~ range There is no evidence of cleavage instability (from the load displacement record) at - 80"C However, as the specimen thickness is increased to cm (at - " C ) , the sample exhibited considerable plastic deformation, but failed by cleavage This significant change in behavior took place despite only a minimal decrease in initiation fracture toughness At a somewhat lower temperature ( 90~ the 1- and 2-cm-thick specimen showed plasticity and (semi-)stable crack extension that was accompanied by some instability (that is, small "pop-ins" that were arrested) in the P-LLD record After a limited amount o f crack extension, these specimens ultimately became unstable and failed by cleavage at the end of the test The fracture surface showed that ductile tearing preceded cleavage failure In contrast, at a specimen thickness o f cm, just a minor amount o f plastic deformation was seen at - " C (in the P-LLD record) before unstable crack initiation Only cleavage was noted on the fracture surface of the B cm specimen at - 90~ Although the number of measurements is small, the effect of size does not seem to be caused by the "statistical effect" reported elsewhere [12,13] If statistically occurring weak links dominate the fracture toughness behavior, small specimens should show a large variatiQn in toughness from sample-to-sample Large specimens on the other hand would be more likely to exhibit a lower toughness since "weak links" are more likely to be present However, in the current experiments, smaller specimens (B = and cm) did not display the scatter in toughness behavior that would be expected if the statistical appearance of microstructural weak links was a dominant factor Further, the presence of some cleavage (for example, pop-in instabilities) indicates that there were sufficient initiation sites or "weak links," but insufficient constraint to propagate a cleavage failure [14] The data are thus consistent with the contention that the apparent size effect is caused by an increased constraint that in turn increases the stored energy that can extend the crack once it has initiated Additional experiments will need to be performed to determine whether or not "constraint" can be proven conclusively as the cause of the size effects observed during toughness testing of DI in the transition region At elevated loading rates, there is an effect of size between the B - and cm specimens at - and +25~ The B = cm specimens exhibit a higher initiation toughness as well as higher overall J-&a curves At 29"C both the B = and cm specimens initiate in cleavage, but then shift into stable ductile tearing The reason for the shift into ductile tearing is not presently understood The displacement versus time records not show any decrease (until the displacement limiter is contacted) that might be associated with a decrease in the loading rate caused either by the capacity o f the load frame or some aspect of the experimental setup Additional experimental work is required to determine if any aspects of experimental technique (for example, specifics of the precracking procedure) may cause the specimen to initiate in cleavage, while retaining the capability to revert to ductile tearing (after, for example, the crack has extended beyond a "zone" damaged during precracking) The samples tested at - 29~ seemed to show a slightly different amount of cleavage, which might explain the lower initiation toughness for the B = cm specimen compared to the B = cm specimen An additional set of detailed measurements will be required to determine whether a statistically meaningful difference in the amount of cleavage between the two specimens is, in fact, present For the specimens tested at room temperature, there was a minor amount of cleavage noted in the B = specimen, while none was found in the B = cm specimen Again, additional testing will be required to determine if the small difference in cleavage can consistently be observed between the two different-sized specimens Copyright by ASTM Int'l (all rights reserved); Wed Dec 23 19:12:57 EST 2015 Downloaded/printed by University of Washington (University of Washington) pursuant to License Agreement No further reproductions 854 FRACTUREMECHANICS: TWENTY-THIRD SYMPOSIUM The J-Aa curves (for the B = and cm specimens) were each the result of measuring several specimens at - 29"C Each individual specimen behaved in a consistent manner, and thus the data (taken as a whole) strongly suggest that the differences shown in Fig (for high rate tests of different specimen thicknesses) are not due to experimental error, but are reproducible changes in the way each type of specimen behaves A recently published paper by Anderson and Dodds [15] describes suggested size criteria for size independent results for specimens in the transition region where the specimen fails by cleavage, but also exhibits enough plasticity to make measurement by linear elastic techniques essentially impractical The size criteria that they developed (using finite-element modeling) is B, b, a > 200(Jc/ay) (2) where B, b, and a are specimen-specific dimensions reflecting the specimen thickness, the length of the remaining ligament, and the (initial) crack length, respectively The flow strength, a r, of the alloy is equal to ~ (yield strength plus ultimate strength) The value of J at unstable crack extension (cleavage), Jc, is calculated as described previously The 200 multiplier used in Eq compares to a value of 25 required to meet the criteria set in ASTM E 813-87 for testing fully plastic alloys For linear elastic testing, the relevant equation is B, b, a > 2.5(Kxdar,) (3) where K~c is the linear elastic fracture toughness and ~rysis the yield strength of the alloy For the current alloy, the different size criteria (at room temperature, quasi-static loading, rates, and using the highest values of J~c measured for the B = and cm specimens) are: (1) for a direct measure of the linear elastic fracture toughness (that is, if large-specimen dimensions alone could cause the material to behave in a linear elastic manner), B, b, a > 51 cm; (2) for a specimen size independent measure ofJc (Eq 2), B, b, a > 4.7 cm; and (3) for a fully elasticplastic alloy, B, b, a > 0.59 cm (the specimen size requirements in (1), (2), and (3) are calculated for descriptive purposes o n l y - - m o r e exact values should be calculated using the toughness values (Kl~, Jc, or Jic) and the ays or ay measured at the appropriate temperature and loading rate) Using the criteria of Eq and noting that the specimen failed by cleavage, the B = cm specimen meets the validity requirement for Jc measurements at - 80"C (and lower temperatures) If the arguments promulgated in Ref 15 are applicable to the ferritic DI alloy tested here, the B cm specimen should be sufficient to measure the size independent fracture toughness at temperatures that cover a large portion of the transition region Increasing the specimen dimensions will not appreciably lower the initiation fracture toughness, nor will there be any further change in the fracture mechanism (since the specimens failed by cleavage) The results for the B = cm specimens that were tested at - and +25"C also met the requirements of Eq 2, even though these specimens did not exhibit any cleavage crack growth An extension of the arguments presented by Anderson and Dodds [ 15] suggest that testing even larger specimens is not likely to induce a cleavage-type failure Equation can also be applied to the high rate measurements The B = cm specimen should provide a valid Jc for values of ~ 19.5 kJ/m and below, while the B = cm specimen can be used to measure directly Jc values up to ~ kJ/m (these values were calculated using the actual values for Bnet (Table 4) and strength values measured from high rate tension tests (Table 2)) The results from the B = cm specimens at - * C a n d below shouldthus provide valid Jc, while the larger specimen (B - cm) should allow the valid Jc measurement at - 29"C Experiments should be conducted, however, to verify that increased size will not cause Copyright by ASTM Int'l (all rights reserved); Wed Dec 23 19:12:57 EST 2015 Downloaded/printed by University of Washington (University of Washington) pursuant to License Agreement No further reproductions autho SALZBRENNER AND CRENSHAW ON FRACTURE TOUGHNESS OF DUCTILE IRONS 855 the toughness to be lowered further even though the size criteria of Eq were met Results from the B = cm specimen at 29~ and the B = l and cm specimens at + 25~ not meet the validity requirements of Eq Using the results from the B = cm specimen at + 25~ Eq suggests that a specimen of B = 3.0 cm should be tested to determine whether cleavage failure (at + 25~ can be induced in this alloy by the effects of increased constraint Using the validity guidelines presented by Eq 2, the data presented in Fig can be used to begin to provide a rational basis for selecting an appropriate value of fracture toughness for fracture mechanics assessments of very heavy-walled DI nuclear transportation casks The lowest temperature that must be considered for accident conditions is - 20~ ( 29~ which is very conservative considering the heat loading provided by contents such as spent nuclear fuel The loading rate applied during the high-rate fracture toughness tests surpassed that measured during actual drop tests conducted without impact limiters [16,17] For example, the time to peak load in the high-rate laboratory tests was ~0.75 ms, while the time to peak load during an actual drop test [16] was ~ 1.4 ms The effects of loading rate on the increase in the ductile-to-brittle transition behavior should be captured conservatively by the laboratory measurements (assuming verification of the lack of further size effects as discussed previously) The high rate toughness at - 29~ (with suitable error bars that should be provided by additional testing) can thus be used as a conservative estimate for the minimum toughness to assess cask safety from a fracture mechanics perspective The initiation J-value at - ~ from Fig is 35.2 kJ/m and compares well to previous high rate measurements [9] for similar samples from other ferritic DI alloys (at - ~ that range from 32.9 to 34.5 kJ/m (in every case, the specimen dimensions exceeded those required by Eq 2) It is also important to note that each reported initiation fracture toughness value was determined from a multiple-specimen technique, and that of the total of 18 specimens that have been tested (at - 29~ none have failed at an unexpectedly low toughness value (thus, specimen dimensions seem to be adequate to ensure that the lowest fracture toughness behavior will be measured) In comparing the values of high-rate fracture toughness of DI as determined by others, it is important to note the broad range of techniques used The precracked Charpy techniques generally provide a loading rate that is comparable to the loading rate used in this study (that is, /~ ~ 105 MPa ml/E/s) The upper-shelf dynamic fracture toughness values determined from such studies [18,19,20] are generally lower (that is, they range from 12 to 25 kJ/m 2) than the values determined by the technique used for this work Other high rate methods that use precracked specimens that are larger than the standard Charpy [ 19,20,21] have produced estimates of fracture toughness that range from 37 to 53 kJ/m This level of toughness is in general agreement with the measurements reported in this paper It is emphasized, however, that these other methods generally not directly control or measure the crack extension Conclusions The effects of temperature and loading rate on the fracture toughness of ductile iron are generally consistent with the behavior observed in many ferritic steels Namely, as the temperature is lowered, the alloy can undergo a transition from (high toughness) ductile tearing to (low toughness) cleavage failure Increasing the loading rate causes the ductile-to-brittle transition temperature range to be shifted to higher temperatures Even though all specimens that were tested exceeded the specimen size requirements with respect to elastic-plastic testing, there appears to be an effect of specimen size (that is, thickness) near the transition temperature range for a specific loading rate Static rate testing demonstrated that increasing the specimen dimensions caused the fracture mechanism to change The change in fracture mechanism could be accompanied by either a minimal change in iniCopyright by ASTM Int'l (all rights reserved); Wed Dec 23 19:12:57 EST 2015 Downloaded/printed by University of Washington (University of Washington) pursuant to License Agreement No further reproductions authoriz 856 FRACTURE MECHANICS: TWENTY-THIRD SYMPOSIUM tiation toughness (at - ~ or a quite significant decrease (at 90"C) For specimens that were tested at high loading rate, an increase in size caused a decrease in initiation toughness This occurred without a dramatic change in the fracture appearance The results o f all tests were examined with respect to size criteria suggested by Anderson and Dodds [14] The results from the largest specimens tested at static loading rate should be sufficient to establish the size-independent fracture toughness of the material Similarly, the largest specimen tested - ~ for the high loading rate, should be large enough to provide a valid toughness value (that is, an increase in specimen dimensions should not cause a change in fracture mechanism, nor a dramatic decrease in the level of toughness) If the fracture toughness measured at high loading rate at - ~ is, in fact, size independent (as suggested by the Anderson and Dodds criteria), this value can be used in the fracture mechanics based evaluation o f the fracture resistance o f heavy-walled nuclear transport casks The high loading rate tests were performed at a rate that exceeds that applied during regulatory (9 m) drop tests and in that respect can be considered conservative Additional testing is required to verify the size independence Acknowledgments This work was performed at Sandia National Laboratories, Albuquerque, New Mexico, supported by the U.S Department o f Energy under Contract Number DE-AC04-76DP00789 References [1] Salzbrenner, R., Sorenson, K B., and Wellman, G W., "Application of LEFM Design to Nuclear Material Transport Casks," International Journal of Radioactive Materials Transport, Vol l, 1990, pp 33-4O [2] Code of Federal Regulations Title l O, Part 71, "Packaging forTransportationofRadioactiveMaterial," Aug 1983 [3] Salzbrenner, R., Van Den Avyle, J A., Lutz, T J., and Bradley, W L "Fracture Toughness Testing of Ductile Cast Irons," Fracture Mechanics: Sixteenth Symposium, ASTM STP 868, M F Kanninen and A T Hopper, Eds., American Society for Testing and Materials, Philadelphia, 1985, pp 328-344 [4] Salzbrenner, R., "Fracture Toughness Behavior of Ferritic Ductile Cast Iron," Journal of Materials Science, Vol 22, 1987, pp 2135-2147 [5] Salzbrenner, R andCrenshaw, T B.,"MultipleSpecimenJ-integralTestingatIntermediate Rates," Experimental Mechanics, Sept 1990, pp l 7-223 [6] Kanninen, M F and Popelar, C F., Advanced Fracture Mechanics, Oxford University Press, New York, 1985, pp 281-391 [7] Joyce, J A and Hackett, E M., "Transition Range Drop Tower J-R Curve Testing of Al06 Steel," Experimental Mechanics, Sept 1989, pp 274-278 [8] Salzbrenner, R and Sorenson, K B., "Dynamic Fracture Toughness Measurements of Ferritic Ductile Cast Iron," Proceedings, PATRAM '89, The 9th International Symposium on the Packaging and Transportation of Radioactive Materials, ] l - l June 1989, Washington, DC, Oak Ridge National Laboratory, Oak Ridge, TN, 1989, pp 728-735 [9] Salzbrenncr, R and Crenshaw, T B., "'Mechanical Property Mapping of the Ductile Cast Iron MOSAIK Cask," Sandia Report SAND90-0776, UC-512, Sandia National Laboratories, Albuquerque, NM, Aug 1990 [10] Nakamura, T., Shih, C F., and Freund, L B., "'Three Dimensional Simulation of a Dynamically Loaded Three-Point-Bend Ductile Fracture Specimen," Proceedings, Third International Conference on Nonlinear Fracture Mechanics, American Society for Testing and Materials, Knoxville,TN, 6-8 Oct 1986 [ 11 ] Barsom, J M and Rolfe, S T., Fracture & Fatigue Control in Structures: Applications of Fracture Mechanics, Second Edition, Prentice-Hall, Inc., Engiewood Cliffs, NJ, 1987, pp 109-158 [12] Landes, J D and Shaffer, D H., "Statistical Characterization of Fracture in the Transition Region,'" Fracture Mechanics (12th Conference), ASTM STP 700, American Society for Testing and Materials, Philadelphia, 1980, pp 368-382 Copyright by ASTM Int'l (all rights reserved); Wed Dec 23 19:12:57 EST 2015 Downloaded/printed by University of Washington (University of Washington) pursuant to License Agreement No further reproductions authorized SALZBRENNER AND CRENSHAW ON FRACTURE TOUGHNESS OF DUCTILE IRONS 857 [13] Bates, R C., "Micromechanical Modeling for Prediction of Lower Shelf, Transition Region, and Upper Shelf Fracture Properties," Fracture Mechanics: Microstructure and Micromechanisms S V Nair, J K Tien, R C Bates, and O Buck, Eds., American Society for Metals International, Metals Park, OH, 1989, pp 131-168 [14] Anderson, T L and Williams, S., "Assessing the Dominant Mechanism for Size Effects on CTOD Values in the Ductile-to-Brittle Region," Fracture Mechanics: Seventeenth Volume, ASTM STP 905, J H Underwood, R Chait, C W Smith, D P Wilhem, W A Andrews, and J C Newman, Eds., American Society for Testing and Materials, Philadelphia, 1986, pp 715-740 [15] Anderson, T L and Dodds, R H., Jr., "Specimen Size Requirements for Fracture Toughness Testing in the Ductile-Brittle Transition Region," Journal of Testing and Evaluation, Vol 19, 1991, pp 123-134 [16] Sorenson, K B., Salzbrenner, R., Wellman, G., Uncapher, W., and Bobbe, J., "Results of the First Thirty Foot Drop Test of the MOSAIK KfK Cask," presented at Waste Management '91, American Society of Mechanical Engineers, New York, Tucson, AZ, 24-28 Feb 1991 [17] Gunther, B and Frenz, H., "Ductile Cast Iron (DCI) Progress on Research Activities on Fracture Mechanics," Proceedings, PATRAM '89, The Ninth International Symposium on the Packaging and Transportation of Radioactive Materials, 11-16 June 1989, Washington, DC, Oak Ridge National Laboratory, Oak Ridge, TN, 1989, pp 736-742 [18] Kobayashi, T., Yamamoto, H., and Matsuo, K., "Evaluation of Dynamic Fracture Toughness on Heavy Wall Ductile Cast Iron for Container," Engineering Fracture Mechanics, Vol 30, No 3, 1988, pp 397-407 [19] McConnell, P and Sheckherd, B., "High Loading Rate Fracture Toughness of Nodular Ductile Cast Iron," FCC 84-12-3R, Fracture Control Corporation, Goleta, CA, 1984 [20] Tanner, G M and Bradley, W L., "Evaluation of the Fracture Toughness of Ductile Iron Using Fatigue Precracked Charpy, Dynamic Tear, and Compact Tension Specimens," Fracture Mechanics: Eighteenth Symposium, ASTM STP 945, D T Read and R P Reed, Eds., American Society for Testing and Materials, Philadelphia, 1988, pp 405-418 [21] Krasowsky, A J., Kramarenko, I V., and Kalaida, V V., "Fracture Toughness of Nodular Graphite Cast Irons Under Static, Impact, and Cyclic Loading," Fatigue and Fracture of Engineering Materials and Structures, Vol 10, No 3, 1987, pp 223-237 Copyright by ASTM Int'l (all rights reserved); Wed Dec 23 19:12:57 EST 2015 Downloaded/printed by University of Washington (University of Washington) pursuant to License Agreement No further reproductions authorized STP1189-EB/Sep 1993 Author Index A Albertazzi, A., Jr., 344 Albrecht, P., 310 Alexander, D J., 365 Allen, D H., 680 Askew, J C., 443 Awerbuch, J., 713 Dexter, R J., 115 Duan, K., 788 E Eide, O I., 284 Eiselstein, L E., 809 Epstein, J S., 55 B Bakuckas, J G., Jr., 713 Balsone, S J., 551 Barsom, J M., Jerry R Swedlow memorial lecture, Bartlett, M L., 265 Becker, A A., 461 Berge, S., 284 Bhuyan, G S., 498 Bigelow, C A., 696 Broderick, T F., 551 Brown, K H., 229 Bucci, R J., 568 Buck, O., 619 Bush, R W., 568 C Carcagno, G., 168 Chattopadhyay, S., 590 Chen, K.-L, 396 Chen, L., 330 Chen, X., 310 Cheverton, R D., 365 Choy, Y.-S., 536 Corleto, C R., 649 Comec, A., 185 Cotterell, B., 788 Crenshaw, T B., 840 D de Vedia, L A., 168 Demir, Y., 383 Deshayes, F R., 598 FitzGerald, J H., 265 Forman, R G., 417, 474 Fujikubo, M., 284 G Goree, J G., 738 Guo, Z., 797 H Harris, C E., 680, 751 Harris, D O., 809 Hartt, W H., 598 Hawkins, M., 797 Henkener, J A., 474 Herrera, R., 168 Hill, J L., 635 Hillberry, B M., 515 Hogan, H A., 649 Hudak, S J., Jr., 265 Johnson, W S., 696 Joyce, J., 310 K Kapusta, A A., 443 Kim, Y.-J., 536 Kobayashi, A S., 797 Kuhlman, G W., 568 Kuo, A.-Y., 396 859 Copyright* 1993Int'l by ASTM www.astm.org Copyright by ASTM (all rightslntcrnational reserved); Wed Dec 23 19:12:57 EST 2015 Downloaded/printed by University of Washington (University of Washington) pursuant to License Agreement No further reproductions authorized 860 FRACTUREMECHANICS:TWENTY-THIRD SYMPOSIUM L Landes, J D., 133, 229 Lau, A C W., 713 Lawrence, V B., 474 Lee, J.-H., 536 Lee, K., 133 Leevers, P S., 826 Leu, S.-S., 635 Liu, C.-T., 668, 775 Lloyd, W R., 55 Lo, D C., 680 S Salzbrenner, R., 840 Sanders, T H., Jr., 515 Schwalbe, K.-H., 208 Sciammarella, C A., 344 Scoonover, T M., 809 Shvarts, S., 396 Shum, D K M., 37 Smith, C W., 775 Smith, J A., 55 Swedlow memorial lecture, 2nd, M T McCabe, D E., 80 McClung, R C., 265 McKeighan, P C., 515 Magnusen, P E., 568 Mai, Y.-W., 788 Maxwell, D C., 551 Merkle, J G., 37, 95 Mettu, S R., 417 Morris, D H., 751 Mouille, H., 775 Mourikes, J., 344 Tada, H., 330 Tan, T.-M., 713 Thompson, R B., 619 U Underwood, J H., 443 V Vedia, de-, L A., 168 O Olm~ead, V J., 443 P Paris, P C.,330 Parke~ A P.,461 Plant, R C A.,461 W Wang, L., 775 Wheel, M A., 826 Williamson, R L., 55 Y R Rau, C A., 809 Rehbein, D K., 619 Reuter, W G., 55 Richardson, D E., 738 Roy, S., 115 Yahsi, O.S.,383 Yayla, P.,826 Yon, J.-H.,797 Young, G A.,443 Yuan, H.,185,208 Z Zhou, Z.,229 Copyright by ASTM Int'l (all rights reserved); Wed Dec 23 19:12:57 EST 2015 Downloaded/printed by University of Washington (University of Washington) pursuant to License Agreement No further reproductions authorized STP1189-EB/Sep 1993 Subject Index Bulge tests, 809 Butt-welded wide plates, 284 A Acoustic emission, 713 Adherent, 635 Adhesive bonds, 635 Adhesive failure, 635 Aerospace materials, 474, 515, 568 Aging conditions, aluminum-lithiumzirconium alloys, 515 Airframe components, fatigue crack growth rate, 568 Allowable flaw size, 498 Alloys, aluminum-lithium-zirconium, 515 Aluminum alloys, 568, 619 Aluminum-lithium alloys, 515-517, 521 Alternating technique, stress intensity solutions, 396 Autofrettaged thick cylinders, 461 Anti-plane Mode III loading conditions, 185, 194, 199, 208 Application methodology ductile fracture mechanics, 229 Asperities 619 ASTM standards A 710, 810 D 1002-72, 635 D 1876-72, 635 D 2094-69, 635 E 399-83, 740 E 647-88a, 568 E 813-87, 840 Asymptotic analysis, 185,208 Axisymmetric loading, 417 C Calibrations, 229 Casks for nuclear transportation, 840 Ceramics, 788 Charpy test, 168, 365, 826 Circumferential cracks, 37, 417 Cleavage fracture transition range data, 80 Compact crack arrest specimen, 365 Composite materials, 649, 751,775 Compressed natural gas, 498 Concrete fracture, 797 Constraint fracture toughness material, 55 transition range data, 80 transverse strain effects, 95 Contact stresses, 383, 619 Continuum damage mechanics, 680 Crack arrest, 365, 826 Crack closure, 536, 619 Crack extension, I 15, 219-220 Crack initiation and growth aluminum alloy forgings, 568 autofrettaged thick cylinders, 461 behavior of titanium aluminide, 551 closure, 265 constraint, 55 ductile bimaterial interface, 208 equivalent plastic strain, 55 fatigue, 498 fracture behavior, 668 high performance ceramics, 788 measurements in aluminum alloy forgings, 558 near tip behavior, 775 reactor pressure vessel, 37 shape, 265 small-scale yielding conditions, 344 steel on-board gas cylinders, 498 surface cracks during loading, 265 B Bending, welded wide plates, 284 Biaxial loading, 738 Biaxial particulate composites, 775 Bimaterial interface, 208 Boundary element method stress intensity factor, 461 Brittle fracture, I 15, 809, 826 861 Copyright by ASTM Int'l (all rights reserved); Wed Dec 23 19:12:57 EST 2015 Downloaded/printed by University of Washington (University of Washington) pursuant to License Agreement No further reproductions authorized 862 FRACTUREMECHANICS:TWENTY-THIRD SYMPOSIUM Crack initiation and growth continued titanium aluminide, behavior, 551 toughness, 37 transverse strain effects, 95 Crack length measurement, 133 Crack opening, 668, 775, 797 Crack propogation, 474, 826 Crack shape development, 498 Crack tip blunting, 95 Crack tip field, 185 Crack tip opening displacement (CTOD), 37, 284 Cracked strip, 383 Cracks, limit pressure analysis, 310 CTOD (see Crack tip opening displacement) Cylinder tests, 503 Cylinders, pressurized, 461 D Damage, 649, 668 Damage initiation, 713 Damage prediction, 713 Damage progression, 713 Damage tolerance aluminum alloy forgings, 568 laminated composite structures, 751 Debonding angle, 635 Debonding force, 635, 696 Defect assessment, 284 Deformation characteristics, 185, 713 Delamination toughness, 515, 649 Displacement, 133 Dominant eigenvalue, 775 Double cantilever beam, 635 Doubly bonded zone, 635 Ductile fracture crack growth, 265 tension tests, 115 mechanics, 229 tearing, 265 Ductile to brittle transition, 365, 840 Dynamic crack growth, 208 Dynamic crack opening displacement, 619 Dynamic crack resistance, 826 Dynamic fracture testing, 168, 826 E Elastic adhesives, physical constants, 641 Elastic plastic fracture mechanics brittle zones in steel weldments, 809 cylindrical vessel, 330 ductile iron (DI) alloy, 840 dynamic fracture toughness, 168 loading cycles, 265 welded wide plates, 284 Elastic plastic materials, 185 Electron beam welding, 365 Elliptical cracks, 396 Empirical formula J-R curves, 133 Energy dissipation rate, 797 Energy release rate, 797 Environmental cracking, 443 Environmental effects, titanium aluminide, Ti-25Al-25Nb, 551 Epoxy laminates, 75 l Equivalent plastic strain, 55 Equivalent remote biaxial stresses (ERBS), 738 ERBS (see Equivalent remote biaxial stresses) Erosion, 461 Error sources and management-microphotography, 77 Eta factor, 168 Explosive bulge tests, 809, 823 F Failure conditions, 635, 680, 713, 738 Failure probability, brittle zones in steel weldments, 809, 823 Failure process zone, 668, 713 Fatigue crack closure, 619 Fatigue crack growth, 474, 498, 536, 568 analysis, 590 test summary, 479 Fatigue (materials) aluminum alloy forgings, 568 Aluminum-lithium-zirconium (Al-Li-Zr) alloy, 515 A710 steel, 809 A723 steel, 443 autofrettaged thick cylinders, 46 l brittle failure, l 15 composite material, 668 circular cylinders, 417 crack closure, 619 crack initiation and growth, 5, 37, 265, 46 I, 474 cracked strip problem, 383 cylindrical vessel, 310, 330 damage prediction, 713 developing J-R curves, 133 ductile fracture mechanics, 229 ductile iron (DI) alloy, 840 dynamic fracture toughness, 168 Copyright by ASTM Int'l (all rights reserved); Wed Dec 23 19:12:57 EST 2015 Downloaded/printed by University of Washington (University of Washington) pursuant to License Agreement No further reproductions authorized INDEXES elastic plastic materials, crack growth during loading cycles, 185, 265 elliptical surface cracks, 396 failure criterion, 738 fatigue crack growth behavior, 551 fracture model, 738 graphite/epoxy laminates, 751 life prediction, 536 magnesia stabilized zirconia, 788 metal matrix composites during static loading, 713 normalization, 168 oscillating temperature distributions, 590 particulate composite material, 668, 775 polyethylene pipes, 826 small-scale yielding conditions, 344 space shuttle main engine (SSME), 265 steel on-board gas cylinders, 498 structural problems, thick wall cylinder A723 steel, 443 titanium aluminide, Ti-25AI-25Nb, 551 titanium metal matrix composites, 696 transition range, data, 80 transverse strain effects, 95 zirconia toughened alumina, 788 welded wide plates, 284 Feedlines, steam generator, nuclear pressure vessels, 590 Ferritic steels nuclear transportation casks, 840 transition temperature, 80, 840 Fiber reinforced composite materials, 648 Fiber stress, 696 Finite element analysis circumferential cracks in circular cylinders, 417 ductile fracture in tension tests, 115 fiber-matrix debonding, 696 intergranular delamination, 515 nonlinear behavior, 649 progressive failure of laminated composites, 680 titanium metal-matrix composites, 696 Flat rolled plate, 568 Flaw size, 498 Fractography, 551 Fracture behavior, 515, 668 Fracture (materials) A710 steel, 809 autofrettaged thick cylinders, 461 aerospace materials, 474 aluminum-lithium-zirconium, 515 cylinder vessel, limit pressure analysis 310 ductile iron (DI) alloy, 840 863 fracture model, 738 graphite/epoxy laminates, 751 magnesia/zirconia toughened alumina, 788 Fracture mechanics aerospace materials, 474 aluminum alloy forgings, 568 A710 steel, 809 A723 steel, 443 autofrettaged thick cylinders, 46 l behavior of particulate composite material, 775 brittle failure, 115 circular cylinder, 417 composite material, 668 crack extension analysis, 185, 208 crack initiation and growth, 55, 265 cracked strip problem, 383 cylindrical vessel, I0, 330 dissipation mechanism of concrete, 797 ductile bimaterial interface, 208 ductile fracture, 115, 229, 840 dynamic fracture toughness using normalization, 168 elastic plastic materials, 185, 265 elliptical surface cracks, 396 fatigue crack closure, 619 fatigue crack growth, 498, 551 fatigue life prediction, 536 fiber matrix debonding, 696 fracture model, 738 graphite/epoxy laminates, 751 high performance ceramics, 788 J-R curves using normalization, 133 metal matrix composites during static loading, 713 methods, 498 nonlinear behavior, 649 oscillating temperature distributions, 590 particulate composite material, 668 polyethylene pipes, 826 pressure vessel steel, 365 small scale yielding conditions, 344 static fatigue in high performance ceramics, 788 structural problems, 229, 265,443 tests, 443, 474 titanium aluminide, Ti-25AI-25Nb, 551 titanium metal matrix composites, 696 toughness, 515, 738 transition range data, 80 transverse strain effects, 95 welded wide plates, 284 Fracture mechanics solutions, Fracture model, 738 Copyright by ASTM Int'l (all rights reserved); Wed Dec 23 19:12:57 EST 2015 Downloaded/printed by University of Washington (University of Washington) pursuant to License Agreement No further reproductions authorized 864 FRACTUREMECHANICS:TWENTY-THIRD SYMPOSIUM Fracture process zone, 797 Fracture resistance of ferritic ductile iron alloys for nuclear transportation casks, 840 Fracture surface examinations, 713 Fracture testing, 168 Fracture toughness aerospace materials, 474 delamination, 515 displacement measurement, 133 ductile fracture mechanics, 229, 840 fracture model, 738 graphite/epoxy laminates, 751 plane-strain conditions, 37 pressure vessel steel, 365 small-scale yielding conditions, 344 steel on-board natural gas cylinders, 498 transverse strain effects, 95 Fracture toughness specimens, 55, 229 Frequency, 551 G Grain flow, aluminum alloy forgings, 568 Grain morphology, 515 H Heat affected zones, 809 High-strength low alloy steel, 809 Hold time, 551 Hollow cylinder, 417 HRR (Hutchinson, Rice, and Rosengren) stress field, 344 Hydrogen stress cracking, 443 Inelasticity, 649 Instrumental Charpy test, 168 Integral transform techniques, 383 Interaction effect, 536 Intermetallic materials, 551 Irradiated nuclear reactor pressure vessels, safety analysis, 330 J-integral, 649, 840 J-R curves, 133, 168, 265, 344 K K analysis, 443 L Laminated composites, 680, 751 Large deformation analysis, 115 Large strains, 95 Leak before break failure, 498, 505 LEFM (see Linear elastic fracture mechanics) Life prediction, 536 Limit pressure, 310 Linear elastic fracture mechanics (LEFM), 738, 840 Linear fracture mechanics, 344 Lithium, aluminum-lithium-zirconium alloys, 515 Load displacement, 168, 229 Load shielding, 619 Loading conditions axisymmetric, 417 circular cylinders, 417 cracked strip problem, 265 ductile fracture mechanics, 229, 383, 840 ductile iron alloy for nuclear transportation casks, 840 elastic plastic materials, 185 Loads, 133, 396 Local brittle zones, 809 M Magnesia-stabilized zirconia, 788 Materials AI-2.6Li-0.09Zr alloy, 515 A533-B steel, tensile strength tests, 83 7050-T74, residual stress screening, 580 metal matrix composites, 713 titanium aluminide, Ti-25A1-25Nb, 551 titanium metal matrix composites, 696, 699 Matrix damage, 680 Maximum failure stress, 635 Metal matrix composites, 713 Methodologies ductile fracture mechanics, 229 pressurized thermal shock, 310, 330 Micrographs, 696 Micromechanics, 37, 69 Microphotography error sources and management, 77 Mixed mode fracture, 396 Mixed mode loading conditions, 185 Mode II delamination, 649 Moir6 interferometry, 797 Copyright by ASTM Int'l (all rights reserved); Wed Dec 23 19:12:57 EST 2015 Downloaded/printed by University of Washington (University of Washington) pursuant to License Agreement No further reproductions authorized INDEXES N NASA/FLAGRO computer program aerospace materials testing, 474, 480 NDE (see Nondestructive evaluation) Near tip fields, 775 Necking ductile fracture in tension tests, 115 Nonlinear fracture mechanics, 185 Nondestructive evaluation (NDE), 265 Nonlinear finite element analysis, 649 Normalization, 133, 168 Notched laminates, 751 Nuclear reactor pressure vessels, safety analysis, 330 Nuclear transportation casks, 840 865 Pressure vessel steel, 365 Pressurized plastic pipelines, 826 Pressurized thermal shock, 330 Pressurized water reactors oscillating temperature distributions, 590 plane-strain fracture toughness, 37 Probabilistic fracture mechanics, 809 Progressive failure analysis methodology, 680 Pump shaft cracking, 396 Q Quasi-static crack growth, 208, 215 R O Oscillating temperature, 590 Overloads, 619 P p-version finite element, 417 Partical elliptical cracks, 396 Part-through flaw, pressure vessel, 330 Particulate composites, 668, 775 Perturbation analysis, 185 Pipeline steel, chemical composition, 118 Pipelines, 826 Pipes, 417 Plane strain, 37, 474 Plane strain, Mode I, 185, 202, 204 Plane strain, test conditions, 443 Plane stress fracture, 515 Plane stress, Mode I, 185 Plastic deformation, 344 Plastic linear hardening materials, 208 Plastic radius, 344 Plastic strain, 55 Plastic zone, 344 PMMA (see Polymethyl methacrylate) Polyethylene pipes, 826 Polymethyl methacrylate (PMMA), 738 Power law, 133 Predictions, 229 Pressure vessels autofrettaged thick cylinders, 461 cracks in circular cylinders, 417 limit pressure analysis, 310, 323-324 thermal shock, 330 Random loading, 536 Range marking, 265 Rapid crack propagation, 826 Reactor pressure vessel, 37 Residual stress, 443, 46 l, 568 Resistance to crack initiation, 37, 265 Ring-forged pressure vessels circumferential flaws, 37 Ring-forged vessels, 37 S Safety analysis, nuclear reactor pressure vessels, 330 Scanning electron microscopy, 443 Shaft residual life, 396 Shear stresses, 185, 649 Singly bonded zone, 635 Size effects of specimens, 80, 87, 91 Size requirements of specimens, 80 Slip-line, 37, l0 Small-scale yielding, 344 Space shuttle main engine (SSME), 265 Space system hardware, 474 Specimen size, 840 SSME (see Space shuttle main engine) Static fatigue, 788 Steady-state crack extension, 185 Steam generator feedlines, 590 Steel aerospace materials, 474 AISI 4130 grade 31 HRC compressed natural gas cylinders, 498 A508 class pressure vessel steel, 365 charpy impact properties, 368 Copyright by ASTM Int'l (all rights reserved); Wed Dec 23 19:12:57 EST 2015 Downloaded/printed by University of Washington (University of Washington) pursuant to License Agreement No further reproductions authorized 866 FRACTUREMECHANICS:TWENTY-THIRD SYMPOSIUM Steel continued chemical composition, 366 fracture toughness results, 374, 377 tensile properties, 370 A533 grade B, transition range data, test conditions, l A710 grade A class 3, brittle zones in weldments, 809 A7 l0 tension tests, 66-67 A723 fracture, 443,445,449 HSLA-80, brittle zones in weldments, 809 low-alloy pipe steel, chemical composition, and mechanical properties, 170-17 l natural gas cylinders, 498 on-board cylinders, 498 storage fuel tanks for vehicles, 498 tremethylcyclopentanone (TMPC) line pipe steel, I 15 Storage fuel tanks for vehicles, 498 Strain, 95, 115 Strength of materials, 344 Stress crack initiation, 55 cracked strip problem, 383, 392-393 deformation behavior, 696 ductile bimaterial interface, 208 elastic plastic materials, 185 energy release rate, 635 fiber-matrix debonding, 696 laminated composites, 680 near crack tip effects, 95 thick wall cylinder, 443 welded wide plates, 284 Stress-intensity factor solutions, 396, 417, 424-425, 435,461, 635 Structural analysis, 284 Structural components, 229 Structural failure/integrity, 55,443 Structural problems, fracture mechanics, Subcritical crack growth, 788 Surface cracks, 265, 536 Swedlow memorial lecture, 2nd, T T-stress, 738 Temperature, 551 Temperature oscillations, 590 Tensile stress, 310 Tension tests, 55 crack initiation, 66-67 ductile fracture, 115 transition range data, 83 Test methods, 265, 284, 443, 474 Thermal shock, pressure vessels, 310, 330 Thermal streaming, 37 Thermal stresses, 590 Thermal tensile stress, 310 Thermal transients in metal structures, 590 Thick laminates, 751 Thick wall cylinder, 443 Thickness effect, 515 Titanium aluminide, Ti-25AI-25Nb, 551 Titanium metal matrix composites, 696 Three dimensional crack analysis, 396 Through transmission, 619 Toughness, 5, 37, 229, 474 Transformation-toughened ceramics, 788 Transition temperature, 80, 840 Translaminate fracture, 751 Transverse strain, 95 U,V, W Ultrasonic scattering, 619 Variable amplitude loading, 619 Weight function, 417 Weibull analysis, 80, 85, 87 Weld defect distribution, 809 Welding, electron beam, 365 Weldments, 284, 417, 809 Wide plate tests, 284 Z Zirconia toughened alumina, 788 Zirconium, aluminum-lithium-zirconium alloys, 515 Copyright by ASTM Int'l (all rights reserved); Wed Dec 23 19:12:57 EST 2015 Downloaded/printed by University of Washington (University of Washington) pursuant to License Agreement No further reproductions authorized