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Commission of the European Communit ies
nuclear science
andtechnology
High cyc le fa t igue
o f
austeni t ic s ta in less stee ls
Repor t
EUR 13084
N
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Commiss ion o f the European Communi t ies
nuclear science
and technology
High cycle fat igue
of
austenit ic stainless steels
J.P. Gauthier , D. Lehmann
Commissar iat l nerg ie atomique
Centre d'tudes nuclaires de Saclay
F-91191 Gif-sur-Yvette
In cooperation with
Dr Picker
AEA
Technology
Risley
Dr Meurer
I n t e ra t om
Bergisch Gladbach
CONTRACT No RA1-009 1 -F
Fina l repor t
This work was performed under the
Commission of the European Communities
for the: wo rking group 'Codes and standards'
activity group 3: 'Materials'
wit hin the Fast Reactor Coordinating Comm ittee
Directorate-General
Science, Research and Development
199 0 EUR 130 84
EN
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Published by the
C O M M I S S I O N O F T H E E U R O PE A N C O M M U N I T I E
S
Di rec t o ra t e - Genera l
Telecommunicat ions, In format ion Indust r ies and Innovat
ion
L 2920 Luxembourg
LEGAL NOTICE
Neither the Commission of the European Communities nor any
person acting on
behalf of the Commission is responsible for the use which might
be made of the
fol lowing information
Cataloguing data can be found at the end of this publication
Luxembourg: Office for Official Publications of the European
Communities, 1990
ISBN 92-8 26-1 904 -4 Catalogue number: CD -NA -130 84-E N-C
ECSC-EEC-EAEC, Brussels Luxe mb ourg, 1990
Printed in Belgium
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FOREWORD AND EXECUTIVE SUMMARY
The Commission of the European Communities is assisted in its
actions
regarding fast breeder reactors by the Fast Reactor
Coordinating
Committee which has set up the Safety Working Group and the
Working
Group Codes and Standards (WGCS).The letter's mandate is to
harmonize
the codes, standards and regulations used in the EC member
countries for
the design, material selection, construction and inspection of
LMFBR
components.
The present report is the revised final report of CEC Study
Contract
N RA1-0091-F performed under WGCS/Activity Group 3 : Materials.
As most
AG3 work, this study concerned the evaluation of material data
to be
used in LMFBR design codes. The main contractor was CEA (France)
with
UKAEA (UK) and INTERATOM (FRG) as participants.
The report concerns the evaluation of high cycle fatigue
properties of
three austenitic stainless steels : type AISI 316 (UKAEA tests),
type
AISI 316L (CEA tests) and type AISI 304 (INTERATOM
tests).
The data on
these steels comprised some 550 data points from 14 casts. This
data set
covered a wide range of testing parameters : temperature from 20
to
625C,
frequency from 1 to 20,000 Hz, constant amplitude and random
fatigue loading, with and without mean stress etc. However, the
testing
conditions chosen by the three partners differed considerably
because
they had been fixed independently and not harmonised prior to
the tests.
This created considerable difficulties when the results were
pooled for
the evaluations to be performed in the present study.
Experimental procedures and statistical treatments used for the
three
sub-sets of data are first described and discussed. Results
are
presented in tables and graphs. Although it is often difficult
to single
out the influence of each parameter due to the different
testing
conditions,
several interesting conclusions can be drawn :
- The HCF properties of the three steels are consistent with the
0.2
proof stress, the fatigue limit being larger than, the latter
at
temperatures above 550C. The type 304 steel has lower
tensile
properties than, the two other steels and hence also lower
HCF
properties.
- Parameters which clearly have a significant effect on HCF
behaviour
are mean stress or R-ratio (less in the non endurance region
than in
the enduranceregion),temperature, cast or product.
- Other parameters have probably a weak or no effect but it is
difficult
to conclude due to insufficient data : environment, specimen
orientation, frequency, specimen geometry.
Recommendations for future work conclude the report. One of
these is
that partners of collaborative actions should agree on a common
test
matrix and experimental procedures prior to any testing.
L.H. Larsson
III
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CONTENTS
Page
1-INTRODUCTION 1
2
-
SUPPLY
OF
AVAILABLE DATA
and
EXPERIMENTAL METHODS 2
2.1 -Supplyofavailable data 2
2.2 -High cycle fatigue experimental methods 4
3
-
PRESENTATIONOF THEDATA COLLECTION
6
3.1 -
Establishment
of the
data bank
6
3.2 -Presentationof thedata 7
3.3 - Use of thedata bank 8
4-EVALUATION
OF THE
HIGH CYCLE BEHAVIOUR
OF THE
304-316-316L
AUSTENITIC STAINLESS STEELS 8
4.1 -Methodology 8
4.2 -Comparisonof thebehaviourof thedifferent types
of materials 9
4.2.1 -Type304 and 316steels 9
4.2.2 -Type304 and 316Lsteels 10
4.2.3 -Type316 and 316Lsteels 10
4.2.4- Conclusion
11
4.3 -Effectofother experimental parameters 11
4.3.1 -
Effect
of a
mean stress
11
4.3.2 -Effectof Rratio 12
4.3.3 -Effectoftemperature 12
4.3.3.1 -Type316steel 12
4.3.3.2 -Type304stell 12
4.3.3.3 -Type316Lsteel 12
4.3.4 -Effectofenvironment 13
4.3.5 -Effectof theorientationof thespecimens 13
4.3.6 -Effectofcasttocast(orproducttoproduct)
variability 13
4.3.6.1 -Type304steel 13
4.3.6.2
-
Type
316L
steel
14
4.3.7 -
Effect
of the
frequency
15
4.3.8 -Effectof thespecimen geometry 15
5-GENERAL DISCUSSION 16
5.1 -Data base 16
5.2 -Experimental methods 16
5.3 -
General data
18
5.4 -
Comparison between materials
18
5.5 -
Effect
of
different parameters
19
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5.5.1 - Parameters having a significant and
sometimes strong effect 19
5.5.1.1- Material 19
5.5.1.2- Mean stress-and R ratio 20
5.5.1.3- Test temperature 20
5.5.1.4- Cast or product 20
5.5.2 - Parameters having probably a weak effect or no
effect but for which it is difficult to conclude
due to lack of data 21
5.5.2.1
- Environment 21
5.5.2.2
- Specimen orientation 21
5.5.2.3- Frequency 21
5.5.2.4- Specimen geometry 21
6-RECOMMENDATIONS AND PERSPECTIVES 22
7 - CONCLUSIONS 23
REFERENCES 26
APPENDICES 29
Appendix 1
Appendix 2
Appendix 3
Appendix 4
Appendix 5
Data to be provided 31
UKAEA data 33
INTERATOM data 34
(4-1,
4-2, 4-3) : CEA data 35
Truncation of peaks in narrow band random
amplitude high cycle fatigue testing using
a resonant machine 38
TABLES 41
FIGURES 73
VI
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1 - INTRODUCTION
For major LMFBR components high cycle fatigue (HCF) has not
yet
been considered as an essential cause of damage. However, it
appears that
in some situations this factor has to be considered. These
situations are
essentially related to thermal oscillations (thermal striping)
or vibra
tions.
Up to now, essentially data on low cycle fatigue (LCF) are
avail
able and very often, for high cycle fatigue evaluation, these
low cycle
fatigue data are extrapolated for higher cycles to rupture. Some
results
and the collection of low cycle fatigue data made in a previous
study
contract (RAP-027-F) indicate that these extrapolations are
generally over-
conservative.
As the available data, in terms of endurance limit, are
relatively
scarce in each country, it appeared to be very profitable to put
all the
data together and to derive some recommendations for high cycle
fatigue
evaluation. The purpose of this study is:
1. to collect information on methods for HCF evaluation in
different
countries
2.to collect the available data in terms of :
. individual results
. determination of the endurance limit using statistical methods
(stair
case)
This data collection would be restricted to load controlled
tests
but would include push pull tests, rotating bending tests
etc...
3. To analyse the data examining the connection between LCF
tests (strain
controlled) and HCF tests (load controlled) as well as the
influence of
specimen geometry and surface roughness.
The contract was placed with CEA, who has subcontracted with
UKAEA
(Risley) and Interatom
(Bensberg).
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This report details HCF data supplied by CEA(France),UKAEA
(Great
Britain) and INTERATOM (Germany), and derived from a data bank
especially
built by CEA in the frame of this CEC contract.
These data are discussed and analysed. The main work concerns
the
effect of different experimental parameters on the S-N curves,
which are
derived from the tables 10 to 58 of the data bank. A particular
emphasis is
made on the relative behaviour of the different types of
stainless steels:
304,316 and 316 L.
2-SUPPLY OF THE AVAILABLE DATA and EXPERIMENTAL METHODS
2. 1 -Supply of available data
Appendices2,
3 and 4 give respectively the UKAEA, INTERATOM and CEA da
ta according to a format previously agreed by the participants
(Appendix 1) .
The stainless steels tested are :
- type AISI 316 for UKAEA
- type AISI 304 for INTERATOM (DIN 1.4948/X6CrNil8-ll)
- type AISI 316L for CEA (AFNOR Z2CND17-12)
UKAEA data include the effects of :
- cast to cast variation
- form of product
- type of cycling (sine or NBR : narrow band random,
corresponding to an
irregularity factor of I = 9 9 )
For the NBR loading, the effects of:
- temperature (400C to 625C)
- mean stress (0 to 103 MPa)
are taken into account.
* - number of mean level crossings with a positive slope
number of peaks (or troughs)
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INTERATOM data include the effects of:
- cast to cast variation (many casts)
- temperature (400C to 600C)
- mean stress (R = -1 to 0.33)
- type of cycling (constant amplitude orrandom).
CEA data include the effects of :
- cast to cast variation
- type of specimens
- type of machines
- specimen orientation
- temperature (10 to 550C)
- frequency (10 to 20 000 Hz)
- type of cycling (constant or random
amplitude).
Because the effects of some parameters have been studied by
UKAEA using only random fatigue tests, the other participants
have completed
their data with results coming from their own random fatigue
tests.
To perform random fatigue tests, UKAEA uses a modified
Amsler
vibrophore machine while INTERATOM and CEA use servo hydraulic
machines. In
the three cases gaussian random processes are generated.
INTERATOM and CEA
use the same generation method, based on Markov matrix
utilisation.
Remarks :
1 - In addition, complementary results concerning INTERATOM HCF
tests,
particularly correlation between fatigue data and
metallurgical
properties have been provided by INTERATOM.
2 - Details of UKAEA random fatigue tests can be found in two
publications
provided by UKAEA:
refs.
[1] and [2].
Details of the random fatigue method used by INTERATOM and CEA
are
given in ref. [3].
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Details of random fatigue tests results obtained at CEA are
presented in ref. [4].
2.2 - High cycle fatigue experimental methods
. All the data provided by the three countries are derived
only
from push pull tests.
The types of machines used are as follows:
At UKAEA: resonance test machine
At INTERATOM: servohydraulic test machine
At CEA: servohydraulic, resonance and ultrasonic test
machines.
Calibration procedures are needed to perform fatigue tests
according to the standards. INTERATOM and CEA gave some details
on these
calibration procedures.
. The specimens used by UKAEA and INTERATOM have a parallel
gauge
length whereas all the specimens used by CEA are of hourglass
type. The
UKAEA specimens have a diameter of 5.05 mm whereas those tested
by
Interatom have a 8 mm diameter. Most of the CEA tests have been
performed
with specimens having a diameter of 8 or 6 mm whereas for tests
in pressu
rised water and ultrasonic tests they had a smaller diameter (3
mm) . The
dimensions of the different specimens are given on figs.l to
6.
The importance of the surface machining on the fatigue life
evalua
tion is well known. For this reason the major number of the CEA
specimens
are longitudinally ground (the surface machining is not known
for some of
them).
For specimens having a parallel gauge length, the common
practice is
to use a fine turned machining as shown by INTERATOM
Indications.
. At UKAEA, specimens have been taken with their axis parallel
to
the bar axis or to the rolling direction of the product, whereas
at
INTERATOM specimen axis are perpendicular to these directions.
At CEA,
specimen axis are either parallel or perpendicular to the
rolling direction
of the product, but a small number of CEA fatigue tests have
been performed
with specimens having a short transverse orientation.
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. All the INTERATOM tests have been performed in air. UKAEA
tests
have been performed in air or He. Most of the CEA tests have
been performed
in air, but some were done in pressurised water environment. For
CEA tests
performed on ultrasonic machines a water cooling system has been
used.
. From an experimental point of view, one must notice that it
is
necessary to carefully perform HCF tests: when the test is
starting, in the
beginning of the cycling, the temperature of the specimen may
significantly
increase (up to 100C in some cases) depending on the frequency
and on the
stress level. The three countries have mentioned this fact and
perform their
tests so as to limit the Increase of the specimen temperature.
For example,
CEA uses steps before reaching the nominal stress level, in
order to have an
increase of the specimen temperature less than about 20C (as an
example see
table 51), or even modifies the frequency for tests performed in
the non
endurance domain. This effect is particularly important for
austenitic
stainless steels because the fatigue limit is generally high as
compared to
the 0.2 % proof stress.
. The methods used in the three countries to perform the tests
and
to analyse the results are different: UKAEA and INTERATOM employ
a regres
sion analysis on the whole experimental S-N couples of values in
the S-N
experimental field, whereas CEA uses statistical methods to
perform tests:
- The stair-case method [5] in the endurance zone to determine
the
fatigue limit (average stress level corresponding to a given
number of
cycles to failure) (Fatigue limits are presented in Tables 1 and
2 ) ;
- the "Henry's straight line" method [6] in the non endurance
zone:
determination of the average number of cycles to failure
corresponding to 3
or 4 different stress levels.
Then a regression analysis is made on these mean stress
values.
Most of the CEA tests were performed in the endurance region.
Some
attention has been paied to the statistical aspects of the high
cycle
fatigue in the frame of this contract, but it raises the
question wether the
same statistical parameters are obtained by the two approaches.
It would be
of interest to perform some work in this field and to do a
literature survey
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(17],
[8] . . . ) . A comparison of the two approaches is not so easy
because
the CEA method needs a higher number of tests to establish the
S-N curves;
that obviously improves the accuracy of the results.
The advantages of the CEA (French) method might be:
- The experimental programme is clear and easier to conduct.
- It allows a direct determination of the fatigue limit (stair
case
method),often enough for design.
- It allows a quantitative analysis of the effect of different
parameters
on the fatigue life in the non endurance and endurance
regions.
3 - PRESENTATION OF THE DATA COLLECTION
3.1 - Establishment of the data bank
The details of the work are given in a report [9]. The data
bank
has been built on a micro computer withD.BASEIII
+
software. It takes into
account a total of 553 tests. The tests are gathered by groups
correspon
ding to the same test conditions, as described hereunder.
1
Country ' Number of campaigns ' Number of tests '
' UKAEA 1 14 1 88 '
1
INTERATOM ' 19 ' 240 '
1
CEA 1 18 1 225 (279-54*) '
1
TOTAL 1 51 1 553 '
* numbers of cycles unknown for groups n 2 and 8 (the results of
stair case
method are only considered)
Details on groups are given in Tables 7 to 9. The file
structure
is given in Tables 1 to 6 of ref. [9], The relation between the
files Is
given p. 9 of ref. [9]. The dictionary code is given In appendix
1 of ref.
[9].
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3.2 - Presentation of the data
It is shown through the following tables :
. Product identification : Table 3,
. Heat treatment : Table 4,
. Chemical composition : Table 5,
. Tensile properties : Table 6
. Group features : Tables 7 to 9
. Test results : Tables 10 to 58.
The following comments can be made:
. The fatigue tests concern several different casts of the
3 steels: 3 at UKAEA, 4 at CEA and 7 at Interatom. The tested
products are
plates at INTERATOM and CEA, and plates and bar at UKAEA. Their
thickness
lies generally between 13 mm and 45 mm excepted for two CEA
products which
are thicker (80 mm and 130mm). The final heat treatments of the
three
types of steel are comparable: 1020C to 1100C annealed, and
water
quenched.
. The chemical compositions of the steels are respectively
in
accordance with the corresponding standards.
. The products exhibit comparable grain sizes typically between
4
and 5 ASTM; however, one of the UKAEA products (plate) has a
very low grain
size (10
ASTM),
whereas the CEA product N 12690 has a heterogeneous grain
size (3 to 5ASTM). In this last case, specimens were taken in
the half
thickness (where the grain size is equal to 5
ASTM).
. The ferrite content is known only for one CEA product. It
is
very low (0 to 0.4 ) .
. A few hardness results are available. The average hardness
of
type 316 steel (UKAEA) and 316 L steel (CEA) are close together
(= 153 HV) .
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. It can be seen in Table 6 of the report that the tensile
proper
ties of type 304 steel are lower than those of type 316 and 316L
steels.
When looking at the CEA tensile test results, no clear effect of
the speci
men orientation on the tensile properties appears.
3.3 - Use of the data bank
The report [9] gives a general presentation of the data bank.
It
is not a guide for use of this data bank. In a first step, a
guide will be
available (in english) with a corresponding floppy disc, further
to some
corrections in the data base, to make it coherent. In a second
step, a
software able to analyse the data of the data bank could be
added. It will
be possible to purchase the guide and floppy disc under an order
to CEC.
A-EVALUATION OF THE HIGH CYCLE FATIGUE BEHAVIOUR OF THE 304 -
316 - 316L
AUSTENITIC STAINLESS STEELS
4.1- Methodology
Data issued from the data bank as shown In Appendix 1 were used
for
the
evaluation. To better understand the effect of different
parameters,
these are studied through the comparison of S-N curves. The -Nf
couples of
values have been classified by groups in the data bank; for a
given group,
they correspond to the same experimental parameters (cast, mean
stress
comean'temperature and so on).
Tables 7 to 9 list these groups for the three countries giving
all
the corresponding parameters. Tables 10 to 58 give the test
results rela
tive to each group.
As mentioned earlier, the fatigue test results under stress
control (which are only considered here) include random fatigue
test
results,partially due to the fact that most of the UKAEA fatigue
tests were
performed under random loading.
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The different S-N curves given in the figures 7 to 30
(correspond
ing to different cases of
comparison),
have been established using a micro
computer associated with a CEA software.
On each graph the campaign number is indicated, together with
the
main parameters of tests.
Remark :
Comparison of results can be made taking into account S-N curves
as
mentioned before but also taking into account fatigue limits
when statisti
cal treatments have been made (CEA
results).
The fatigue limits of type
316L steels are presented in Tables 1 and 2.
4.2 - Comparison of the behaviour of the different types of
materials
4.2.1 - Type 304 and 316 steels
The comparison can only be made on fig. 7 (case n
c
1).
In this case, the average stress o
mean
is equal to 69 MPa for the
316 steel and between 50 MPa and 110 MPa for type 304 steel
which is not too
much different (R =0.33)).The test temperature is 625C for type
316 steel
and 550C for type 304 steel.
One can make a realistic hypothesis that there is a slight
effect
of the temperature between 550C and 625C for type 304 steel
(see
results on fig. 17 case n 11 obtained, however, with zero
meanstress).
The orientations of the tested specimens are different; the
effect
of orientation is unknown for type 316 and type 304 steels; but
we can
notice that there is no effect of orientation for type 316L
steel in the
endurance region, and we can suppose that it is also the case
for type 304
and 316 steels.
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In these conditions, the S-N curve relative to the type 304
steel
seems slightly lower than the one corresponding to the type 316
steel. Let
us notice that type 304 steel results correspond to the product
referenced
402 which exhibits a higher fatigue resistance than the other
304 steel
products.
4.2.2 - Type 304 and 316L steels
The comparison can be shown on 3 figures:
. Figure 8 (case n 36 ), in which tests conditions of the
different pro-
ducts considered are the same.
. Figure 9 (case n 3) , in which the test temperatures are
slightly dif-
ferent (400C for type 304 steel, 300C for type 316 L steel).
CEA
fatigue tests have shown that the HCF results performed in the
endurance
region at 300C are close to those made at 550C for the same
product,
all other parameters being equal (see case 13).
. Figure 10 (case n 4 ) , in which the test conditions are the
same under
random loading (with an irregularity factor I = 70 % ) .
When considering all these 3 cases, we can see that type 304
steels
exhibit significantly lower fatigue resistances than those of
type 316L
steel,except the 304 steel product n 402 for which the fatigue
resistance
is only slightly lower than that of type 316L steel.
4.2.3 - Type 316 and 316L steels
This comparison shown in fig. 11 (case n 5) can be made only
for
NBR tests (I 99 % for CEA tests). The test temperatures are 400C
for
type 316 steel and 300C for type 316L steel but the effect of
temperature
in this range seems very small for type 316L steel. The
orientations of
specimens are different (parallel to the rolling direction for
type 316
steel and perpendicular to the rolling direction for type
316Lsteel). But
the CEA fatigue test results show no significant effect of the
orientation
of the specimens on the fatigue resistance, this being at 300C
In the
endurance region for tests performed under constant amplitude of
loading;
however, this effect is not known in the case of random fatigue
tests.
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Figure 11 (case n 5) shows a great difference between type
316
steel results and those on type 316L steel. But, although the
probability
density functions of peak amplitude are the same the maximum
values of the
applied stress do not exceed 4 (where is the mean square root)
for type
316 steel [1], [2] as compared to 5.26 for type 316L steel [3],
[4] (for
type 304 steel tested at INTERATOM, they used the same kind of
machine and
software as CEA). In addition, for UKAEA random fatigue tests
performed on
a resonance machine, they introduce a truncation of the peak
effect as
described in Appendix 5. So one can consider that the loading
spectrum
applied to type 316 steel gives less damage than the one applied
to type
316L steel (and to type 304
steel).
It results from this discussion that we cannot positively
conclude
on any difference existing between the behaviours of these two
kinds of
steels (316 and 316L), only on the base of the results given in
fig. 11
(case n5) . A lot of work is necessary to compare the UKAEA
experimental
method with the CEA and INTERATOM experimental method, in
particular with
the aim to compare the fatigue damages calculated by these two
methods.
4.2.4 - Conclusion
Concerning the effect of material, the comparison is not so
easy
because of the lack of data available in the same test
conditions. However,
it can be pointed out that the HCF resistance of the type 304
steel is
generally lower than the type 316L and 316 steel one. So one
must consider
that 304 product n 402 exhibits a particularly good behaviour in
comparison
with that of the other 304 products.
It seems that the HCF resistance of type 316 and 316L steels
are
close together but it is difficult to discriminate them due to
the lack of
data obtained in the same test conditions.
4.3 - Effect of other experimental parameters
4.3.1 - Effect of a mean stress
This effect has been only examined by UKAEA for random
fatigue
tests. Fig. 12 and fig. 13 (cases n 6 and 7) show the strong
effect of a
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mean stresson the S-N curves(as expected, fatigue resistance
decreases
whenthe mean stress
increases).
This effectisgreaterin theendurance
zone thanin the nonendurance zone. One cannotice thatafatigue
limit
does
not
seem
to
exist
for
this type
of
test
or may be
exists
in the
regime
of very high numberofcycles.
4.3.2 -Effectof Rratio
Thishasonly been examinedbyINTERATOMfig. 14(casen37).As
expectedthetendencyis todecrease the fatigue limit whenthe
Rratio
increases.
In the nonendurance regionitseemsto be thereverse. Thisis
partially
due to the
scatter (induced
by the
lack
of
data)
and
also because
the effectof Rratioisprobably smallerinthis regionas it
hasalready
been found
by
UKAEA
in
random fatigue tests.
4.3.3 -Effectoftemperature
This parameterhasbeen examined separatelyon thethree steels.
4.3.3.1 -Type316steel(NBRtests)
A significant effect
has
been found
for
tests without mean stress
as shownin fig. 15 (case
n9).
As expected fatigue resistance decreases
whenthetest temperature increases. Theeffectishigherin
theendurance
region thanin the nonendurance region, between 400Cand625C. But
the
scatterishigh. Theeffectissmallerfortests withamean stress
equal
to
69 MPa as
shown
on fig. 16
(casen10).
4.3.3.2 -Type304steel
Figure
17
(case nll) shows
a
moderate effect
of the
test tempera
tureon the S-N curves (results obtainedon theproductN
325),between
400Cand600C.
4.3.3.3 -Type316Lsteel
Figure 18 (case n 13) shows that the S-N curve obtained for
testat 300Cis very closeto the one (results obtained
castnT1231)
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corresponding to tests performed at 550C. Figure 19 (case n 14)
shows a
large effect of the test temperature between 20C and 550C (tests
concer
ning the cast nT7793).
4.3.4 - Effect of environment
The effect of environment has been examined on type 316 and
316L
steels.
It has been shown that helium does not improve fatigue
resistance of
type 316 steel (figs. 20 and 21 (cases 18 and 19)) and that
pressurised
water environment has no effect on the fatigue resistance of
type 316L steel
(fig.
22 (case n 20)). But these results must be carefully
considered,
because there are too few data in the experimental field, and
also because
the fatigue lives are too short to show any significant effect (
t
m a x
< one
week for most of the
tests).
4.3.5 - Effect of the orientation of the speci
mens
This effect has been only examined on type 316L steel. No
diffe
rence on fatigue resistance at 300C has been observed when
taking the
specimens in the longitudinal or transverse orientations of the
cast n
T1231 (figure 23 (casen21)).
On the contrary, a strong difference In fatigue resistance
between
short transverse and transverse orientations at 10C has been
observed, but
on a very thick product and also the cast for which details are
unfortuna
tely unknown, as shown fig. 24 (case n 22) .
4.3.6 - Effect of cast to cast (or product to product)
variability
This has been particularly examined on type 304 steel for
which
there is a lot of data.
4.3.6.1- Type 304 steel
Figure 25 (case n 27) shows a moderate effect of cast to
cast
variation on the S-N curves at 400C (cast 294771 (product n 402)
is not
considered because there are no experimental results at this
temperature).
On the other hand, fig. 26 (case n 38) seems to show a slightly
higher
effect at 550C. But, looking at the case n 38 with sufficient
attention,
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one can see that the effect of cast to cast must be considered
as very
important if the cast n 294771 (product n 402) is taken into
account.
The S-N curve corresponding to this cast is in particular
significantly
above the S-N curves relative to the other casts. This
phenomenon has
already been mentioned previously.
The relative situations of the S-N curves cannot be related to
the
corresponding tensile properties (in particular the 0.2 proof
stress).
But they can clearly be correlated to the grain size of the
products, parti
cularly at 550C (see Table 59) indicating a strong dependence of
the high
cycle fatigue properties on the grain size of the products made
of type 304
steel at this temperature. No sufficient information is
available to extend
this result to the other steels.
It is however interesting to compare high cycle fatigue
results
obtained on type 316 steel on cast N R7406 (product number 33)
with those
obtained on cast N 13899 (product number 40) because the
respective grain
sizes are very different (5 ASTM and 10 ASTM respectively),this
comparison
being possible only for fatigue tests performed under random
loading.
Figure 15 (case N 9) indicates that there is no effect of
grain
size although the grain sizes are very different. This suggests
to be very
careful in the application of effects observed on fatigue tests
performed
under constant amplitude loading to tests performed under random
loading, as
also from one material to another.
Moreover we can deduce from INTERATOM fatigue test results
that
the grain size is an important parameter to consider when one
wants to
compare the behaviour of different austenitic stainless
steels.
4 3 6 2
- Type 316L steel
A comparison can be made through figure 8 (case n 36) at
550C
between the S-N curves obtained respectively for the casts n
7793
(product n 31776) and n 1231 (product n12690): That relative to
the
latter cast is lower than the other one. In particular, we
cannot consider
that it is an effect of cast to cast variation, but rather an
effect of the
final product. The cast n 7793 (product 31776) corresponds to a
plate
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which had been slightly cold worked by bending prior to taking
the specimens
for tests. Its tensile properties are higher than those of the
cast nT
1231 (see Table 6 ) . Therefore figure 8 (case n 36) indicates
that there
may exists a correlation between the fatigue limit and 0.2 %
P.S. of the
same product.
Another significant cast to cast effect could be seen
through
figure 27 (case n 30). But unfortunately little is known about
the cast
(N E6083) and the tested product (grain size, and so on).
Moreover, the
diameter of the specimens taken in this cast is 6 mm, whereas it
is 8 mm for
those taken in the cast n T1231 (product 12690) (see
chapter5.5.2.4the
discussion on the geometry of the
specimens).
4.3.7 - Effect of the frequency
A significant effect of the frequency on the HCF resistance of
the
type 316L steel at room temperature does not appear clearly
through figure
28 (case n 31) . But this result has to be carefully considered
because
many test parameters are different:
- casts,
- thickness of the products,
- specimen geometries,
- cooling systems.
This could have been better established when considering fig.
29
(case n 32) on which all the parameters of tests are similar
except the
frequency, but unfortunately the variation of the frequency is
too small as
compared to the previous case N31.
4.3.8 - Effect of the specimen geometry
There is a lack of data to allow an accurate study of this
effect:
In fig. 30 (case n 33) a comparison between fatigue results
obtained on cy
lindrical and hourglass specimens taken from type 304 steel
product may be
tried. If the grain size of the tested material (5.5 ASTM for
cylindrical
specimens and 4.5 ASTM for hourglass specimens) is taken into
account, one
can reasonably think that there is probably no effect. A more
quantitative
study would be necessary to conclude on the effect of this
parameter.
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5 - GENERAL DISCUSSION
5.1 - Data base
Concerning the working out of the data base some comments can
be
made:
a - creating and asking
It is not easy to build a data base when all experiments are
fi
nished. It is more interesting to create a dynamic data base at
the begin
ning of a group of tests; this method allows the partners to
choose common
values for the parameters and to continue the experiments in a
better way.
b - Structure
It is Important to devise a common structure of the data base
at
the start of the work to make easier the exchange of results and
the loading
in the data base.
c - Communication
The local and extended network is a good tool to make most
of
Informatics data treatments directly from the laboratories.
5.2 - Experimental methods
Two aspects are to be considered. First the geometries of
the
specimens used by the three countries are different and depend
of the type
of machine used. There are not enough available data to clearly
appreciate
the effect of the geometry of the specimens. Only one case of
possible
comparison exists based on INTERATOM data (see paragraph
4.3.8)
between
hourglass and cylindrical specimens; no (or a slight) effect is
shown.
Several types of specimens are used by CEA but quantitative
comparisons
between these different geometries are not possible because they
were used
on very different machines specifically built for working in
different
frequency ranges. Moreover, the cooling systems are different as
other
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experimental details. However, we can notice that there is no
evident
effect of the specimen geometry linked with frequency,
environment (andpro
duct ) on the HCF properties of the type 316L steel.
Secondly, the increase in the temperature of the specimen at
the
very beginning of the test has been particularly mentioned. This
effect
seems to be important for stainless steels because the fatigue
limit is
close to the 0.2% P.S. Tests were performed carefully by the
three coun
tries to limit this phenomenon. Only CEA gives some details on
the test
procedure (see paragraph 2.2) but no result exists to quantify
the conse
quences of this effect on the high cycle fatigue properties.
The methods used by the three countries to perform the tests and
to
analyse the results are different. As mentioned before, UKAEA
and INTERATOM
employ a regression analysis on the whole experimental S-N
couples of expe
rimental values in the experimental field. CEA uses statistical
methods to
perform tests:
- stair case method in the endurance zone,
- Henry's straight line method in the non endurance zone ( 3 or
4 stress
levels),
- then regression analysis on the mean values (see paragraph
2.2) .
Most of the CEA fatigue test results were obtained In the
endurance region excepted at 300C on one cast. But the S-N curve
for
stainless steels being flat even down to about 10 000 cycles at
high
temperature and due to the scattering CEA produced a certain
amount of
results in the non endurance region. UKAEA and INTERATOM also
gave a few
results under 10 000 cycles. So, if we can consider that the
three coun
tries produced data in about the same experimental field, they
do not
exhibit enough fatigue results at high stress levels showing a
lack of data
In these experimental conditions. These data are needed in
particular in
view of performing damage calculations linked to high peaks of
spectrum.
However, fatigue under load control in this region necessitates
a decrease
of the frequency. Because some problems may appear when
performing fatigue
tests under load control In this region, the problem of
connection between
LCF and HCF tests is put. Attention has been paid to statistical
aspects in
paragraph 2.2. The interest of the CEA method has been
presented.
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But a lot of work seems necessary to be performed. The amount
of
work necessary to discuss the fitting of the experimental data
was too
important to do this work in the frame of this contract. Many
questions
remain,
such as :
- May the two approaches give the same statistical parameters,
what are
the respective accuracies ?
- How many tests are necessary to get a good estimation of the
mean S-N
curve (50% probability of failure) and of the scatter ?
- Which mathematical equations give the best fit to the results
?
Some connection with design people seems necessary in this
field.
5.3 - General data
There is very often a lack of information in each country,
concern
ing:
- identification of the cast and products,
- grain sizes,
- ferrite contents,
- hardnesses,
- heat treatments,
- tensile properties: uniform elongations, orientation of the
specimens.
This makes the analysis more difficult. Some of this
information
might be probably collected but it would be necessary to spend a
lot of time
and to perform some complementary measurements.
5.4 - Comparison between materials
The HCF properties of the three steels are consistent with the
0.2%
Proof Stress. In particular the fatigue limit is clearly higher
than the
0.2% PS at 550C (625C for UKAEA) for the three steels. CEA
fatigue test
results allow to establish a relation between fatigue limit
o
Q
and 0.2% PS
for type 316L steel depending on the temperature.
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In Table 60, we can see that the ratio o
D
/0.2 PS increases when
the temperature increases.
which Is lower than 0.2 PS at 20C becomes
higher at 550C. The lower HCF resistance of type 304 steel as
compared to
that of type 316 and 316L can be linked with the corresponding
0.2 PS. How
ever,INTERATOM results show that the grain size of the tested
product must
also be taken into account to explain the fatigue behaviour of
the stainless
steels.
The effect is discussed hereafter.
5.5 - Effect of different parameters
The effects of different parameters on the HCF properties of
the
three steels have been examined. Unfortunately these effects are
very dif
ficult to evaluate precisely because very often several
parameters are not
constant at the same time. In several cases, It is not possible
to separate
the effect of each parameter. The details of the analysis of the
role of
each parameter are given in paragraph 4 (4.3.1 to4.3.8). We can
classify
these parameters into two groups.
5.5.1 - Parameters having a significant and sometimes strong
effect
5 5
- Material
As mentioned before the type 304 steel exhibits a fatigue
resist
ance lower than that of type 316 and 316L steels, an exception
is thepro
duct n 402 giving an S-N curve close to that of type 316L steel
in the same
test conditions. It seems that the difference in the grain size
is suffi
cient to explain the lower positions of S-N curves of type 304
steels (see
paragraph4.3.6).
The grain size would seem to have a great effect when looking
at
the INTERATOM results. This is surprising because it does not
vary very
much.
Any way it is difficult to conclude whether it is only a grain
size
effect because the different grain sizes correspond to different
casts. In
particular the grain size is not well correlated with 0.2 PS
(see Table 59) .
Comparisons between type 316 steel and the other steels are
diffi
cult because most of the UKAEA fatigue results are obtained
under random
loading, and the method used by UKAEA to generate random
processes Is dif-
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ferent from that used by INTERATOM and CEA. Although a
comparison between
the two methods used to generate random loading was not an
objective of the
contract, some information has been exchanged in particular with
the aim to
analyse fatigue damages produced by the two methods.
A grain size effect has not been observed by UKAEA on type
316
steel for fatigue tests under random loading. One conclusion
might be that
the application of some effects on fatigue from tests performed
under
cons
tant amplitude loading to tests performed under random loading
and from a
material to another one must be made with some precautions.
5.5.1.2- Mean stress and R ratio
Mean stress and R ratio have a significant effect on the HCF
beha
viour,
which is already well known. Only UKAEA and INTERATOM have
studied
these effects. They have found that the mean stress effect would
be less in
the non endurance region than in the endurance region, as
mentioned in para
graph 4.3.2.
5.5.1.3- Test temperature
Test temperature has a great effect on the HCF behaviour of
stain
less steels when considering a large range of temperatures (10C
to625C).
But the evolution of the fatigue behaviour with temperature is
complex. For
example CEA fatigue tests give no difference in the results
obtained at
300C or 550C.
5.5.1.4- Cast or product
In each country specimens are taken in products each of them
cor
responding to a different cast. There can be either a product
effect or a
cast to cast effect, or a combination of the two as mentioned
previously.
If no cast effect is considered the product effect could be
linked to the
grain size, this aspect has been developed In paragraph
4.3.6.
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5.5.2 - Parameters having probably a weak effect or no effect
but
for which It is difficult to conclude due to lack of data
5.5.2.1- Environment
No effect has been found (He, air, PWR environment) but the
durations of the fatigue tests are too short to show any
eventual effect.
5.5.2.2- Specimen orientation
CEA fatigue results on type 316L steel give no effect of the
specimen orientation at 300C in the endurance region. But there
is a great
lack of data at other high temperatures, in the non endurance
region, and
for the other steels. Elsewhere CEA results show that there is a
strong
difference In the fatigue resistance of the type 316L steel at
room tempera
ture between short transverse and transverse orientations (on
the product
having a large
thickness).
5.5.2.3- Frequency
Quantitative and accurate comparisons are not possible for a
large
range of frequencies because many parameters are not always the
same :
specimen geometry, environment, products, and so
on....
But all the CEA
results show that the frequency seems to have a weak effect or
no effect.
5.5.2.4- Specimen geometry
An INTERATOM case gives no effect (or weak effect) of the
specimen
geometry, but it is difficult to be more affirmative because the
concerned
casts are not the same. CEA uses different specimen geometries
but they are
linked to different frequencies, environments and products.
However, the
effect seems to be weak or non existent.
Remark -
It has not been possible to discuss all the objectives
proposed
in the frame of this contract due to the extensive amount of
work for a
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complete study. In particular two Important problems have not
been investi
gated :
- the connection between LCF,tests (strain controlled) and HCF
tests (load
controlled).
This is a very important problem In connection with damage
calculations,
- surface roughness,
which could be examined in a second phase of work.
6-RECOMMENDATIONS AND PERSPECTIVES
Some recommendations and perspectives can be deduced from the
gene
ral discussion.
The evaluation of the effect of different parameters on HCF
of
stainless steel should be based on tests using products very
well known and
characterized from a metallurgical point of view. In addition to
informa
tions asked In the frame of this contract, it has been shown
that the know
ledge of the grain size is very important. Toughness
measurements, and
metallurgical structures should also be of interest.
The test procedures are very important when looking at the
scatter
of the results. In particular, some work should be done to
define a good
test procedure, allowing In particular a "moderate" Increase of
the specimen
temperature at the beginning of the test, for this type of
steel.
Some directions for future work can be proposed:
I
o
) Work that needs no supplementary fatigue tests:
. study of statistical methods to perform tests and analyse the
results
(bibliography )
. connection between LCFand HCF test results
. study of methods to provide random loading (bibliography,...)
for damage
calculation developments
. connection with design problems.
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2) Work that needs supplementary fatigue tests:
. test procedures (method to limit the increase of specimen
temperature at
the beginning of cycling)
. accurate study of the effect of:
- specimen geometry
- roughness of the gauge length of specimens
- frequency particularly in the non endurance region.
- thickness of the product
- orientation of the specimens
- mean stress
- grain size
- thermal ageing
. fatigue tests at high levels of stress (in connection with
damage
calculations)
. random fatigue tests
. comparison of the effect of some parameters on the HCF
resistance under
constant amplitude loading and random loading
. comparison of the HCF resistance under stress control and
under strain
control.
7 - CONCLUSIONS
. Most of data and all the fatigue test results on type 316
steel
(UKAEA),
304
(INTERATOM),
316L (CEA) have been included in a data bank built by
CEA with DBASE III+ software. Building such a data base takes a
lot of
time when all experiments are finished. It is more interesting
to create
a dynamic data base at the beginning of a serie of tests.
. From the experimental point of view, some attention must be
paid to
experimental procedures to perform HCF tests on austenitic
stainless
steels dealing with the increase of specimen temperature at
the
beginning of the cycling. It seems that there is a need to
establish
accurate procedures avoiding the specimen temperature to
increase too
much.
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CEA does not use a direct fit approach to treat fatigue results
as UKAEA
and INTERATOM but performs fatigue tests using statistical
methods
(stair case method and Henry's straight line method) and
fitting. Time
has not been found in the frame of the contract to completely
compare
the two approaches and to determine what is the need to
establish S-N
curves with a good accuracy.
Some difficulties have been met to understand the fatigue
behaviour of
the three steels because of a lack of data in each country (like
better
knowledge of the
structure).
The fatigue behaviour of austenitic stainless steels is good
particu
larly at high temperature where the fatigue limit becomes higher
than
the 0.2% PS.
A relation between fatigue limit and 0.2 % PS seems well
established. It
explains probably why fatigue resistance of type 304 steel is
lower than
that of the two other steels excepted for one cast of 304 steel
the
results of which are close to those of 316L steel for example
(in the
same test
conditions).
The grain size seems to be an Important parameter to understand
fatigue
behaviour of austenitic stainless steels as shown through
INTERATOM
results. However, the apparent strong relation of fatigue
resistance of
type 304 steel with grain size (it increases when the grain size
de
creases) must be considered with care because each grain size
value
corresponds to a different cast. The effect has not been found
under
random loading (UKAEA
results).
The effect of different parameters has been examined on each
steel.
Some of them have a significant or strong effect like:
- mean stress and R ratio
- temperature
- product
as expected. Several examples are presented but the comparison
is not
often easy because the respective experimental conditions of
considered
fatigue programmes are not always the same. It appears that
these
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effects would not be exactly the same in the non endurance
region and
between HCF under constant amplitude and HCF under random
loading, but
the scatter does not allow to quantify these effects or would
need
statistical studies using of lot of tests.
Others have probably a weak effect or no effect but it is
difficult
to conclude due to lack of data, as :
- environment (corresponding to the test conditions used)
- specimen orientation
- frequency
- specimen geometry.
A lot of work remains to be performed in the HCF field of
austeni
tic stainless steels and may constitute objectives of a further
contract. This
would Include the performance of new tests to improve the
knowledge of the
fatigue behaviour of the three steels.
One can list some of the open questions (cf. paragraph 6) :
- study of statistical methods to perform tests and treat
results,
- connection between LCF and HCF test results
- study of methods to provide random loading (stress control,
strain
control) with damage calculations, which require the performance
of
tests at high stress levels
- connection with design problems
- experimental procedures
- better knowledge of the effect of specimen roughness, specimen
geometry,
- frequency, specimen orientation, mean stress, grain size,
thermal ageing.
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REFERENCES
[1] D.J. WHITE and J. LEWSZUK
Narrow band random fatigue testing with Amsler vibrophore
machines
Journal Mech. Eng. Science, Vol. 11, n 6, 1969.
[2] D.J. WHITE
Effect of truncation of peaks in fatigue testing using narrow
band
random loading
Int.
Journal Mech. Sci, 1969, Vol. 11, pp. 667-675.
[3] E. HAIBACH, R. FISHER, W. SCHUTZ, M. HUCK
Standard random load sequence of gaussian type recommended for
gene
ral application in fatigue testing; its mathematical background
and
digital generation.
Intern.
Conf. on "Fatigue Testing and Design" - London - 4/1976.
[4] J.P. GAUTHIER, P. PETREQUIN
High cycle fatigue of austenitic stainless steels under
random
loading.
Post-SMIRT Seminary (Sixth International Seminar of Inelastic
Ana
lysis and Life Prediction in High Temperature
Environment),
Paris,
August
24-25,
1987.
[5] G.E. DIETER
Mechanical metallurgy.
Mc.Graw - Hill books company, Inc. New-York, Toronto, London
1961,
[6] Recueil de normes franaises statistiques, tome 1, 1985
Editi par l'AFNOR.
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REFERENCES (cont.)
[7] A guide for fatigue testing and the statistical analysis of
fatigue
data,
prepared by committee E-9 on fatigue.
ASTM special technical publication N. 91-A (second edition)
1963.
[8] Statistical analysis of fatigue data.
A symposium sponsored by ASTM Committee E-9 on Fatigue
Pittsburgh, Pa., 30-31 Oct. 1979
ASTM STP 744.
[9] D. LEHMANN
Crationd unebase de donnies sur les rsultats d'essais de
fatigue
grand nombre de cycles sur les aciers inoxydables
austnitiques.
N.E.
CEA SRMA 88-1077. Fivrier 1988.
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P P E N D I C E S
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APPENDIX 1
HIGH CYCLE FATIGUE PROPERTIES OF AUSTENITIC STAINLESS STEELS
(Load controlled only)
Data to be provided
TABLE
1 :
High cycle fatigue experimental methods
- National standards
- Type of tests (pushpull,rotating bending...)
- Type of machine, calibration
- Specimens: shape, dimensions (mm), surface roughness
- Orientation
- Environment
- Statistical analysis methods
TABLE 2: General data
- Material grade
- Steel designation
- Cast N
- Supplier
- Product form
- Product number
- Product dimensions (mm)
- Chemical analysis (wt ) , cast, product
- Final heat treatment
- Microstructure, ASTM grain size, ferrite content
- Hardness
- Tensile properties at room and high temperatures
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TABLE 3: High cycle fatigue data
- Steel designation, cast N
- Temperature (C)
- Environment
- Frequency
- Mean stress
- Stress range
- Number of cycles to failure
- Endurance limit
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APPENDIX 2
UKAEA DATA FOLLOWING TABLE 1 OF APPENDIX 1 (Attachment 1)
HIGH CYCLE FATIGUE EXPERIMENTAL METHODS
National standards
BS 3518: Part 1
BS 3518: Part 2
BS 3518: Part 3
BS 3518: Part 4
BS 3518: Part 5
1962 General principles
1962 Rotating bending fatigue tests
1963 Direct stress fatigue tests
1963 Torsional stress fatigue tests
1966 Guide to the application of statistics
The status of these documents was re-affirmed by the British
Stan
dards Institution in 1984.
Type of Test: Push Pull
Type of Machine: Amsler Vibrophore
Specimen: Standard Amsler Type: 5.05 mm dia, 20 mm
Parallel gauge length, tapering out
with 22 mm radius to Mil threaded head.
Orientation :
Products 2 and 33 (Round bar) : Axis of specimens parallel to
bar axis
Products 40 (Plate) : Axis of specimens parallel to rolling
direction
Environment :
Air or He as listed
Statistical analysis methods :
Regression analysis
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APPENDIX 3
INTERATOM DATA FOLLOWING TABLE 1 OF Appendix 1
HIGH CYCLE FATIGUE EXPERIMENTAL METHODS
National standards : DIN 50100
Type of Test :
Type of Machine
Push pull
MTS,
Servohydraulic 50 kN
Calibration :
MPA Dortmund to better than 1 % each range: 5, 10,
20,
50 kN calibration service of MPA
Dortmund is approved by PTB
Specimens
Round, surface roughness: fine turned
Orientation :
Perpendicular to the rolling direction
Environment :
Air
Statistical Analysis
Method : Regression analysis
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APPENDIX 4.1
CEA DATA FOLLOWING TABLE 1 of Appendix 1
HIGH CYCLE FATIGUE EXPERIMENTAL METHODS
National standards
The French AFNOR standards are:
NF A 03-400 (aot 1983)
Essais de fatigue : principes gnraux
(Fatigue tests : general principles)
NF A 03-401 (aot 1983)
Essais de fatigue par charge axiale
(Fatigue tests using axial loading)
NF A 03-402 (aot 1983)
Essais de fatigue par flexion rotative (aot 1983)
(Fatigue tests using rotating bending)
NF A 03-509 (aot 1983)
Etalonnage des machines d'essai de fatigue
(Calibration of fatigue test machines)
Type of test
Axial loading
35
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APPENDIX 4.2
Type of machine, calibration
- MTS servohydraulic 100 KN
- LOSENHAUSEN HU S 100 KN servohydraulic
- AMSLER vibrophore (3) 50 KN ? - Bruyres-le-Chtel (2) -
CENS/DEMT
(1)
- INSTRON resonance test machine 100 KN type 1603
- ULTRASONIC type (CENG/LAMA)
- Calibration :
TheS R M A machines are first aligned so that the upper and
the
lower grips have the same
axis.
The different ranges (10, 20, 50, 100 KN) are calibrated with
a
dynamometric ring using a mechanical measurement. This ring is
calibrated
by the LNE (National Test
Laboratory).
This calibration is controlled by VERITAS Office which gives
a
certificate.
Specimens shape, dimensions (mm), surface roughness,
orientation
- For the specimens shapes, see fig. 3 to 6.
- Surface roughness:
It is not available for all the specimens. For the specimen
of
fig.
3: (probably for specimen of fig. 4
also):
End step to 8.05 or 6.05 with depth 1/10 mm, moving 2 to
3/100 mm.
Then longitudinal grinding with a grind: fine grains 38 to 42
-
rate 1000 r/mn - moving 3 to 4/100 mm to obtain the final
diameter of 8 mm
(or 6).
The specimen orientations are TL (perpendicular to the
rolling
direction),
LT and TS.
36
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APPENDIX 4 . 3
E n v i r o n m e n t
- Air
- Some tests in pressurised water environment. For tests
performed on
resonance or ultrasonic machines, it is necessary to use a
cooling
system: compressed air or water cooling.
Temperature : 10, 20, 300, 320C and 550C.
Frequency
- Servohydraulic machines : 40 Hz
- AMSLER resonance machine : 150, 163-166, 350 Hz
- INSTRON resonance machine : 140
- ULTRASONIC testing machine : 19 600, 20 000 Hz
Statistical analysis methods
Endurance zone: stair - case method.
Non-endurance zone : Henry's straight line method.
A regression analysis is employed on experimental data
correspon-
ding to a probability of failure of 50%.
French laboratories often use BASTENAIRE equations.
CEA use a power law
= C
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APPENDIX 5
TRUNKATION OF PEAKS IN NARROW BAND RANDOM AMPLITUDE HIGH CYCLE
FATIGUE
TESTING USING A RESONANT MACHINE
C. Picker
Narrow band random loading tests on Type 316 steel were
performed by
UKAEA using an Amsler Vibrophore machine as described in Ref 1,
measuring
the load as a RMS value directly from a meter.
The narrow band random process is, in effect, a waveform of
frequency
f but with a slowly varying random amplitude and phase. There
are as many
crossings of zero amplitude as peaks, and the probability of a
given
amplitude falling within a certain range is statistically
predictable. The
expected number of crossings
slope in unit time is given by
expected number of crossings (f ) of stress level (s) with a
positive
f
s
f
o
ex
P ( )
(1)
where is the root mean-square value.
The expected number of peaks occurring in the interval between s
and
s+ds will be : -
'..*. -1-
*. i, ( t j i ) *
and the probability density function of a peak of amplitude s
occurring is
therefore represented by the Rayleigh probability density
function : -
P(s) = K exp ^ 1
v;
0
., (3)
( )
'
e x
P I 27 ' J (Fig. 1)
The wide band generator used in the tests produced a
Gaussian
instantaneous voltage distribution up to 4. The response of the
system
plus specimen, however, may show deviations compared with the
input and
there is a possibility of a cut-off or truncation of peaks at
some stress
level (s ). Peaks which would otherwise have exceeded the level
s are
truncated at that level (see Fig. 2 ) .
Examination of the truncation of peaks in narrow band random
amplitude
loading tests on Type 316 steel has been made in only three
cases, these
were tests on Product No 2 at 625C using a mean stress of 69
MPa. The
results are show in Fig. 3 where the square of the ratio of
stress
amplitude to RMS stress ((s/o
2
)) is plotted against the number of peaks
exceeding t
he level s/ in 10
5
cycles. The results indicate that, at a RMS stress
level of 49.7 MPa, there was little truncation of peaks up to 4
times the
RMS value. However, truncation of peaks occurred for higher
stresses, the
degree of truncation increasing with the RMS stress. There
are,
unfortunately, insufficient data from these tests to enable the
amount of
truncation to be estimated for tests in other conditions (ie for
different
temperatures, materials or mean stress levels).The true waveform
applied
to the specimen is therefore not known precisely in the majority
of cases.
Reference
1. WHITE D.J. and LEWZUK J. - Narrow band random fatigue testing
with
Amsler Vibrophore machines. Jnl of Mechanical Engineering
Science,
Vol.
11, 1969, pp. 598-604.
38-
-
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6>(3)
.o
0.2
\
0 1 2 3 4
s G
Fig 1. Probability density function for the
Rayleigh distribution
0.5s
a
v 1
Time
Fig 2a. Response of a strain gauged specimen in an Amsler
Vibrophore excited by a sine random generator
Fig 2b. Response in random loading with truncation level at
s
39
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10 10* 10* 10 '
No OF CYCLES EXCEEDING LEVEL S/0 IN 100000 CTCLES
TRUNCATION OF PEfiKS IN NARROW BAND RANDOM LOADING TESTS
ON TYPE 3 1 6 STEEL AT 625C MEAN STRESS = 69MPa
R
- 4 0 -
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T B L E S
41
-
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-
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s f
P
-
Material
316L sm
316
L
SP
3I.LSPH
3iL SPH
316L
316 L
316 L Ch
induct
CL platt
5200 3loox/t5mir
Cast T??93
CL plate
520X 3200x45mm
Cast T7?93
CL plaire
26.5mm tiickness.
CailrT1231
CL plate
26.5 mm Sicknes s
Casi- TM231
Cat E O B 3
CL
CLplatt
&D mm Jnickness
Cabt E 5106
B loc k
300 130*1(10 mm
Spec imen
CEA
23 .
89
fi&. 3
Resonance
type
fifi.
4
CEA 23- f l
fi&. 3
CEA 23-ff)
R & . 3
Resanan r_e
fiA.e .S
Ultrasonic
type
a . 6
(J l i ro on ic
type
TL
TL
TL
LT
LT
LT
TL
rs
Testing mattimi
MTS
E le ct ro h y d r a u l i c
10
Amsler resonance
besting m ad i rne
typt IO HFP-44?8
Ams le r r t&onanc t
besh'ng machine
type 10HFP.4-22
I n s l r o n 1603
Resonance.
tes t ing machine
I n s t r u n 1603
Resonance
test ing machine
Amsler resonance
testing madiine
Hpetial resonance
testina machine
Ultrasonic ,
best ing
m a c h i n e .
Ultrasonic
besting,
machine
Test concUkanA.
_Air
-Compress, air
-Cooling
_Air
-Compress, air
.Cooling
_ Air
_ Air
.Air
( a t m . press')
-Pressurised water
. 450 ba n
_Air
- W a t e r t o o l i n g
-Air
-\Naier cooling
Temperat.
l isi.
20
20
550
3
550
300
32
10
&raa.4fl:C
/xj
ID
nJ10
( r e f l u e n t /
( H i )
40
150
1 6 3 .
166
140
142
350
20 000
19 600
y
T.C
T.C
T.C
T.C
T.C
TX
T.C
Cycles for
stair-case
2x10
e
IO
7
1
e
10*
10
e
5x
-
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-F*
C P
r -
i
e n
C
c
Material
316LSPH
3I6L5PM
3)6 L PH
316L SPH
34tL
5PH
Jtoducb
CL plate
26.5 mm mickness
Cast
T1231
CL plate
26.5mmttiickness
Cast
T1231
CL plate
26.mm mickness
Cas t
CL plate
200
M 0x46 mm
Cast T?7
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COUNTRY
UKAEA
UKAEA
UKAEA
INTERATOM
INTERATOM
INTERATOM
INTERATOM
INTERATOM
INTERATOM
INTERATOM
CEA
CEA
CEA
CEA
CEA
MATERIAL
GRADE
AISI
316
AISI
316
AISI
316
AISI
304
AISI
304
AISI
304
AISI
304
AISI
304
AISI
304
AISI
304
AISI
316L
AISI
316L
AISI
316L
AISI
316L
AISI
316L
CAST
NUMBER
S3475
R7406
13899
219629
231861
273711
227766
VK256
LK3206
294771
E6083
T1231
T7793
E5106
SUPPLIER
1
2
3
3
3
4
5
5
3
6
6
6
6
PRODUCT
FORM
PLATE
BAR
PLATE
PLATE
PLATE
PLATE
PLATE
PLATE
PLATE
PLATE
PLATE
PLATE
PLATE
PLATE
PRODUCT
OR
CODE
NUMBER
2
33
40
173
206
207
325
326
327
402
12690
31776
35528P
PRODUCT
DIM(MM)
13.00
38.00
32.00
20.00
20.00
20.00
40.00
20.00
45.00
20.00
130.0
26.50
45.00
80.00
HEAT
TREAT.
HRSD
1020-1070
SA-OQ/WQ
HRSD
UNKNOWN
UNKNOWN
UNKNOWN
1060
SA-WQ
1050
SA-WQ
1050
SA-WQ
1020
SA-WQ
UNKNOWN
UNKNOWN
1100
SA-WQ
1070
SA-WQ
UNKNOWN
ASTM
GRAIN
SIZE
5
,.062mm
10
,.032nm
4
4.5
4.0
3.5
4.5
4.0
5.5
3to4,5 S,1/2T
FERRITE
CONTENT
0,0.4
S.1/2T
and 1/4T
HARDNESS
156 HB
152 HB
156 HV
150 HV
PRODUCT IDENTIFICATION
OQ/WQ
: OIL OR
WATER QUENCH TABLE
3
COUNTRY
UKAEA
UKAEA
UKAEA
INTERATOM
INTERATOM
INTERATOM
INTERATOM
CEA
CEA
HEAT
TREAT.
IDENT.
1
4
1
3
3
3
3
3
3
HRSD
SA-OQ/WQ
HRSD
SA-WQ
SA-WQ
SA-WQ
SA-WQ
SA-WQ
SA-WQ
TEMP.
ANNEALED
C O
1020-1070
1060
1050
1050
1020
1100
1070
TIME
ANNEALED
(MM)
20
45
21
COOLING
DOWN
OIL or
WATER
WATER
WATER
WATER
WATER
WATER
WATER
PROOUCT
NUMBER
2
33
40
325
326
327
402
12690
31776
CAST
NUMBER
S3475
R7406
13899
227766
VK256
LK3206
294771
T1231
T7793
HEAT TREATMENT
TABLE
4
- 4 5 -
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e n
COUN
TRY
UKAEA
UKAEA
UKAEA
INTER
INTER
INTER
INTER
INTER
INTER
INTER
CEA
CEA
CEA
CEA
CEA
MATER.
GRAD.
316
316
316
304
304
304
304
304
304
304
316L
316L
316L
316L
316L
CAST
NUMBER
S3475
R7406
13899
219629
231861
273711
227766
VK256
LK3206
294771
T1231
1231
T7793
793
PRODUCT
NUMBER
2
33
40
173
206
207
325
326
327
402
12690
12690
31776
31776
CAST
C)
PROD
P)
C
C
C
.0400
.0440
.0300
.0510
.0549
.0419
.0506
.0411
.0368
.0600
.0320
.0200
.0200
.0220
.0230
Ni
12.04
12.80
10.45
11.28
11.15
11.08
10.89
10.14
10.29
10.72
11.92
12.35
12.31
12.50
12.50
Cr
17.05
17.60
17.00
17.38
17.78
18.01
18.55
18.94
18.99
17.82
17.00
17.91
17.54
17.31
17.21
1.70
1.57
1.59
1.79
1.82
1.62
1.37
1.78
1.59
1.67
1.69
1.74
1.74
1.71
1.63
Cu
.040
.030
.040
.047
.050
.370
.370
.170
.180
Si
.34
.48
.46
.38
.44
.70
.37
.44
.30
.46
.46
.48
.49
.28
.32
Mo
2.81
1)
2.57
2.32
0.09
0.04
0.08
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COUNTRY
UKAEA
UKAEA
UKAEA
UKAEA
UKAEA
UKAEA
UKAEA
UKAEA
INTERATOM
INTERATOM
INTERATOM
INTERATOM
INTERATOM
INTERATOM
INTERATOM
INTERATOM
INTERATOM
INTERATOM
INTERATOM
INTERATOM
INTERATOM
INTERATOM
CEA
CEA
CEA
CEA
CEA
CEA
CEA
CEA
CEA
CEA
CEA
CEA
CEA
CEA
MATERIAL
GRADE
316
316
316
316.
316
316
316
316
304
304
304
304
304
304
304
304
304
304
304
304
304
304
316L
316L
316L
316L
316L
316L
316L
316L
316L
316L
316L
316L
316L
316L
CAST
NUMBER
S3475
R7406
R7406
R7406
13899
13899
13899
13899
219629
219629
231861
231861
273711
273711
227766
227766
VK256
VK256
LK3206
LK3206
294771
294771
E6083
E6083
E6083
T1231
1231
T1231
T1231
T1231
T1231
T1231
T7793
T7793
T7793
T7793
PRODUCT
NUHBER
2
33
33
33
40
40
40
40
173
173
206
206
207
207
325
325
326
326
327
327
402
402
12690
12690
12690
12690
12690
12690
12690
31776
31776
31776
31776
TEMP
CC)
20
20
450
625
20
400
600
650
20
550
20
550
20
550
20
550
20
550
20
550
20
550
20
20
320
20
20
20
300
300
550
550
20
20
550
550
ORIENTATION
//
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//
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//
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//
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rol.dir.
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-
1
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.dir.
-L
rol.dir.
J-
rol.dir.
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-
1
-
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J-
rol.dir.
-
1
-
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r.
1
rol.dir.
J-
rol.dir.
-
1
-
rol.dir.
1
rol.dir.
-
1
-
rol.dir.
//
rol.dir.
-L
rol.dir.
//
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J-
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1
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J- rol.dir .
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-L rol .dir.
0 2XPS
MPa)
310
290
217
153
256
160
146
135
240
129
218
120
220
126
273
155
246
126
255
117
258
132
266
310
146
293
293
274
179
174
145
146
285
295
160
154
1 0XPS
MPa)
279
170
258
150
279
157
313
189
309
163
296
150
304
172
329
329
311
206
203
174
174
UTS
MPa)
614
589
476
400
574
457
404
377
561
381
556
374
566
371
575
385
603
391
597
406
604
406
580
580
493
599
599
587
465
462
437
429
567
580
405
413
UNIFORM
ELONGATION
)
51.0
51.0
52.0
36.0
37.0
35.0
38.0
49.0.
50.0
34.0
34.0
TOTAL
ELONGATION
)
51.0
61.0
39.0
31.0
51.0
41.0
42.0
47.0
61.2
36.6
64.4
39.6
64.5
38.1
62.9
37.2
61.4
39.3
70.9
39.3
70.0
41.1
76.0
56.0
40.0
62.0
62.0
64.0
46.0
48.0
45.0
47.0
66.0
64.0
46.0
45.0
R OF A
X)
73.0
58.0
61.0
60.0
53.0
55.0
52.0
73.0
65.0
74.0
64.0
73.0
68.0
71.0
66.0
77.0
72.0
74.0
68.0
79.0
72.0
79.0
79.0
84.0
76.0
76.0
74.0
74.0
80.0
79.0
69.0
60.0
TABLEOFTENSILE PROPERTIES
TABLE6
47
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1^
CO
CAMP.
NUM.
01
02
03
04
05
06
07
08
09
10
11
12
13
14
COUNTRY
UKAEA
UKAEA
UKAEA
UKAEA
UKAEA
UKAEA
UKAEA
UKAEA
UKAEA
UKAEA
UKAEA
UKAEA
UKAEA
UKAEA
MATERIAL
GRADE
AISI 316
AISI 316
AISI 316
AISI
316
AISI316
AISI316
AISI316
AISI316
AISI316
AISI316
AISI316
AISI
316
AISI316
AISI316
CAST
NUMBER
R7406
R7406
13899
R7406
R7406
R7406
m
R7406
S3475
R7406
S3475
m
13899
13899
PRODUCT
NUMBER
33
33
40
33
33
33
33
+
33
2
33
2
4=0*
40
40
HEAT
TREAT.
1020-1070
SA-OQ/WQ
1020-1070
SA-OQ/WQ
HRSD
1020-1070
SA-OQ/WQ
1020-1070
SA-OQ/WQ
1020-1070
SA-OQ/WQ
1020-1070
SA-OQ/WQ
1020-1070
SA-OQ/WQ
HRSD
1020-1070
SA-OQ/WQ
HRSD
HRSD
HRSD
HRSD
TYPEOF
TEST
CONST.
AMPL.
CONST.
AMPL.
CONST.
AMPL.
RAND.
FAT.
RAND.
FAT.
RAND.
FAT.
RAND.
FAT.
W W
m
RAND.
FAT.
RAND.
FAT.
RAND.
FAT.
RAND.
FAT.
RAND.
FAT.
TEST.
MACH.
SPECIMEN
TYPE
AMSLER
AMSLER
AMSLER
AMSLER
AMSLER
AMSLER
AMSLER
AMSLER
AMSLER
AMSLER
AMSLER
AMSLER
AMSLER
AMSLER
NUM.
TESTS
11
8
1
14
13
6
4
2
6
5
6
2
1
9
OR. ENVIRON.
HE
AIR
AIR
AIR
AIR
AIR
HE
HE
AIR
AIR
AIR
AIR
AIR
AIR
TEST
TEMP.
625
625
625
625
625
400
625
625
625
625
400
400
400
625
FREQ.
(HZ)
ffi'
fio
100
i s -
i -
la
w
-
f
97
95
SIGN.
FORM.
SIN
SIN
SIN
MEAN
STRESS
(MPA)
69
69
69
0
103
0
69
69
69
69
69
69
69
0
R
-1.00
-1.00
-1.00
IRR.
FAC.
0.99
0.99
0.99
0.99
0.99
0.99
0.99
0.99
0.99
0.99
0.99
GROUP LIST
NOTE
:
VALUE
OF
IRREGULARITY FACTOR PROPOSED
FOR
UKAEA
NBR
TEST
IS .99
TABLE
7
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CD
CAMP.
NUM.
01
02
03
04
05
06
07
08
09
10
11
12
13
14
15
16
17
18
19
COUNTRY
INTER
INTER
INTER
INTER
INTER
INTER
INTER
INTER
INTER
INTER
INTER
INTER
INTER
INTER
INTER
INTER
INTER
INTER
INTER
MATERIAL
GRADE
AISI
304
AISI304
AISI304
AISI
304
AISI304
AISI
304
AISI304
AISI
304
AISI304
AISI
304
AISI304
AISI
304
AISI304
AISI
304
AISI
304
AISI
304
AISI
304
AISI304
AISI304
CAST
NUMBER
227766
227766
227766
227766
227766
219629
219629
273711
273711
VK256
VK256
LK3206
LK3206
294771
231861
294771
294771
294771
294771
PRODUCT
NUMBER
325
325
325
325
325
173
173
207
207
326
326
327
327
402
206
402
402
402
402
HEAT
TREAT.
1060
SA-WQ
1060
SA-WQ
1060
SA-WQ
1060
SA-WQ
1060
SA-WQ
UNKNOWN
UNKNOWN
UNKNOWN
UNKNOWN
1050
SA-WQ
1050
SA-WQ
1050
SA-WQ
1050
SA-WQ
1020
SA-WQ
UNKNOWN
1020
SA-WQ
1020
SA-WQ
1020
SA-WQ
1020
SA-WQ
TYPEOF
TEST
CONST.
AMPL.
CONST.
AMPL.
CONST.
AMPL.
CONST.
AMPL.
CONST.
AMPL.
CONST.
AMPL.
CONST.
AMPL.
CONST.
AMPL.
CONST.
AMPL.
CONST.
AMPL.
CONST.
AMPL.
CONST.
AMPL.
CONST.
AMPL.
CONST.
AMPL.
CONST.
AMPL.
CONST.
AMPL.
CONST.
AMPL.
RAND.
FAT.
RAND.
FAT.
TEST.
MACH.
2
2
2
2
2
2
2
2
2
2
2
2
2
2
2
2
2
2
2
SPECIMEN
TYPE
ROUND
ROUND
ROUND
ROUND
ROUND
ROUND
ROUND
ROUND
ROUND
ROUND
ROUND
ROUND
ROUND
ROUND
HOUR.
ROUND
ROUND
ROUND
ROUND
NUM.
TESTS
18
16
17
15
20
12
12
11
12
11
12
12
12
8
14
10
12
9
7
OR. ENVIRON.
AIR
AIR
AIR
AIR
AIR
AIR
AIR
AIR
AIR
AIR
AIR
AIR
AIR
AIR
AIR
AIR
AIR
AIR
AIR
TEST
TEMP.
400
450
500
550
600
400
550
400
550
400
550
400
550
550
550
550
550
550
550
FREQ.
(HZ)
5 8
50
50
50
50
40
40
40
40
40
40
40
40
30
k
-
7/26/2019 CDNA13084ENC_001
58/104
CTI
o
CAMP.
NUM.
01
02
03
04
05
06
07
08
09
10
11
13
14
15
16
17
18
19
COUNTRY
CEA
CEA
CEA
CEA
CEA
CEA
CEA
CEA
CEA
CEA
CEA
CEA
CEA
CEA
CEA
CEA
CEA
CEA
MATERIAL
GRADE
AISI316L
AISI316L
AISI
316L
AISI316L
AISI
316L
AISI316L
AISI316L
AISI
316L
AISI316L
AISI
316L
AISI316L
AISI316L
AISI
316L
AISI
316L
AISI
316L
AISI316L
AISI316L
AISI316L
CAST
NUMBER
7793
7793
7793
1231
1231
6083
6083
5106
1231
1231
1231
1231
7793
7793
1231
1231
PRODUCT
NUMBER
31776
31776
31776
12690
12690
35528
12690
12690
12690
12690
31776
31776
12690
12690
HEAT
TREAT.
1070
SA-WQ
1070
SA-WQ
1070
SA-WQ
1100
SA-WQ
1100
SA-WQ
UNKNOWN
UNKNOWN
UNKNOWN
UNKNOWN
UNKNOWN
1100
SA-WQ
1100
SA-WQ
1100
SA-WQ
1100
SA-WQ
1070
SA-WQ
1070
SA-WQ
1100
SA-WQ
1100
SA-WQ
TYPEOF
TEST
CONST.
AMPL.
CONST.
AMPL.
CONST.
AMPL.
CONST.
AMPL.
CONST.
AMPL.
CONST.
AMPL.
CONST.
AMPL.
CONST.
AMPL.
W U T
CONST.
AMPL.
CONST.
AMP
