ML19329E018

App 4A,App A,Of Rancho Seco PSAR, Properties & Microstructure of Spray-Quenched Thick-Section Steels. Reprinted from Welding Research Council Bulletin 120,Feb 1967

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i.

I Docket 50-312 Amendment No. 1 February 2, 1968 l

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APPENDIX A

'l l

l THE PROPERTIES AND MICROSTRUCTURE OF I

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SPRAY-QUENCHED THICK-SECTION STEELS f

j by T

S. S. Strunck, A. W. Pense and R. D. Stout i

[

Reprinted from i

Welding Research Council Bulletin No. 120 I

February 1967 J

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Welding Research Council f

New York, N. Y.

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1 CLIMAX MOLYEDENUM COMPANY An AMAX Division 1270 Avenue of the Americas, New York, N. Y. 10020 Printed in U.S.A.

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The 3roper:ies and Micros':ruc~:ure o" Spray-Quenchec a

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ee s by S. S. Strunck, A. W. Pense and R. D. Stout A DSTRACT, With the increasing use of thick-action demands with the conventional materials at hand.

quenched and t,empered steels for nuclear and chemical With this increase in wall thickness, both strength reactors, there is a definite need for information on the properties of some of the newer low-alloy high-strength and toughness are decreased and fabr. cation costs steels when given such thick-section heat treatment. Of are increased. It is to be expected, then, that panicular interest are yield and tensile strengths attainable, both new materials and heat treatments should be the notch toughness to be expected, the plastic fatigue strengths,vailable and the kinds of microstructure that developed for such heavy-walled vessel apph.ea-appear to be characteristic of these thicknesses.

tions. In practice, these two developments are In the program reported here, four quenched and tem-pered heavy-section steels-A212 Grade B, A533 Grade B, complementary. The new materials available A542 and AS43-were studied in the simulated 6-in. thick for these vessels are of significantly greater harden-and 12-in. thick quenched, tempered and stress-relieved con-ability than those previously used. This makes dition. Specimens taken from these simulated heavy sec-tions were evaluated to provide a characterization of the 9uenchin8 and temperin& treatments more de-properties and structure of heavy-section, heat-treated, sirable than with conventional steels because in low-alloy steels.

heavy sections where accelerated cooling can do The 6 to 12 m,results show that increasing the,section size from little to improve, for example, a carbon steel, the

. produced no important changes m strength, notch toughness or fatigue resistance in these steels in the higher alloy steels respond to produce microstruc-(o) quenched, tempered and stress-relieved condition. When tures representing improved strength and tough-

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c mparing 1-in. thick plate with the heavy sections, strength decreased only modestly while notch toughness decreased ness. The use of such steels has alreadY been substantially. Because of their initial good toughness, shown to be of advantage in section sizes up to 4 however, the alley steels etill exhibited transition tempera-in, both from the standpoint of strength and notch tures be, low -10' F. The fatigue and elevated temperature h

touE ness '-8 In section sizes over 4 in.' some properties of the steels were simtlar to those found in thmner sections of equivalent tensile strength. The results of the industrial experience has already been obtained.

microstructure study confirmed the mechanical property However, a program. surveying some of the newer betw enI' II and E2 [n.Io*d[t$*truoure was and more promising materials in a systematic beerved 6

s manner had not been done. Therefore, the pro-gram described in this paper was undertaken to introduction provide such a survey of four of the newer heavy-In view of the recent trend to larger pressure walled pressure-vessel materials.

vessels for the higher operating pressures and In this program, four steels-A212 Grade B (in temperatures of the nuclear power and chemical the quenched and tempered condition), A533 industries, considerable effort has been expended Grade B, A542 and A543-all of which are of in the development of new materials and heat potential use in heavy-walled vessels, were com-treatment procedures for large heavy-walled re-pared in heavy-section sizes. It was believed actor vessels. In the past, these vessels have that four properties are of interest in a study of U f

been of carbon or low-alloy steels and the heat the response of low-alloy steels to acceleratect treatment most commonly used has been cooling in heavy sections.

The first of these normalizing and stress relieving. Current in-is yield and tensile strength at room and dustrial practice is moving away from these more elevated temperatures. The advantage of the established materials and procedures because of steels must be realized by practical increasas in both economics and safety. As the size and re-both yield and tensile strength in the center thick-quirements of the newer vessels have increased, nesses of heavy-section plates if they are to be fsv) so has the wall thickness required to meet these attractive. The extent to which such increases

's can be maintained as section size increases be-l S. S. Strunck is Research Assistant. A. W. Pense.a Associate Profemmor,and Comes an important question.

R. D. Stout is Dean of the Graduate Srbool, Ish;gh University. Bethlehern.

l Pa.

A second area of importance, indeed a critical l

a3re'N.**No"itt '"I "e'"w5fn' Te"."e.Ta7.'un*,i?""" *""

one from the safety standpoint, is the kind of h

nn-me Thick Section Steels 0$00 uUoc t

toughness properties that ccn be cxpected as e Because of the thickness of these pl:tes, it was result cf quenching cnd tempering cf a he:vy-possibl2 to perform duplicita mechtnic:1 prop-section 1:w-Clloy steel pt:te. It has been sh;wn erty tests on both center-r.nd qu rter-thickness that a favorable balance of both strength and positions to reveal any differences in the behavior toughness can be maintained in thinne -section of materials from these locations. Therefore, 1:w alloy plates; to what extent can this Le main-there were essentially eight sources of material 3

tained as section sizes increase? Because of the for testing, i.e., center-and quarter-thickness 1.

importance of this area, the notch toughness tests locations in four different steels. The as-received conducted in this program were supplemented by properties of the plates are listed in Table 2.

plcne-strain fracture toughness evaluations on A533B, A542, and A543 by Westinghouse, and Heat Treatment notch tensile tests were conducted on the A212B cnd A5338 by Syracuse University. Heat-treated In order to produce data usefulin evaluating the m:terial from this program was furnished to them suitability of the four quenched and tempered for this purpose. The results of these tests are steels to heavy-section service, it was necessary to reported separately in his Bulletin.

heat treat the plates to reproduce heavy-section A third area of interest in this study is the quenched and tempered microstructures. It can fatigue resistance of the steels in the 1000 to be seen from Table 1 that the plates as-received 100,000 cycle failure range. While few failures in were from 6% to 8 in. in thickness. Since this pressure vessels have been directly attributed to initial thickness insured that the plates were fatigue, the role of fatigue in initiating cracks that representative of heavy sections in chemistry and 1:ad to failures cannot be ignored in vessel design.

rolling practice it was decided to cut %-in. thick The fourth area of interest in the study of the test plates from the center thickness and quarter steels is the influence of the cooling treatments on thickness positions of the original plates and to th3 microstructures that are produced by the heat treat these test plates in such a manner as to qu:nching and tempering of heavy sections.

match the cooling rate from austenitizing that Microstructure may appear to be of second-w uld be characteristic of two typical plate thick-ary interest when mechanical property data nesses--6 in. and 12 in. In order to select cooling are known. Since properties of alloy plates are rates appropriate for these thicknesses, a large strongly influenced by microstructure, the evalua-body of both calculated and experimental data on c ling rates during the quenching of heavy-tion of microstructures produced by the heat

-]s section plates was obtained and studied."

treatment of heavy-section plate can give valuable clues to the combinations of steels and treatments These data are summarized in Fig. 1.

Since that are required in orde: to produce useful relatively few of the experimental cooling rate data properties as section size is increased.

available were obtained on large-size heavy-section The study reported in this paper must be con-plates, and dip as well as spray quenching may be sidered limited in scope in that it includes data from single heats of only four typical steels. How-sv:r, the specimens were cut from both the quarter 9

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point and center thickness locations of com-wme,,,

m rcially-produced heavy pt s and thus the

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investigation provides cooromated data on the characteristics of commercially-produced low-4't

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alloy high-strength steels when heat treated for j'"

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h:avy-section service. It should therefore serve

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g, a) a useful guide for the further development of j*

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Materials as*s E

Four steels with actual or potential use in heavy-

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walled pressure vessels were included in the experi-j x

• "'h m:ntal study..These were A212 Grade B, A533 Grade B, A542, and AS43. The chemical com-u ss' positions of these steels are listed in Table 1.

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Tin four steels were obtained as heavy thickness production plates, as indicated. Both quarter-

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these production plates and are listed in Table 1.

Fig.1-cooling rates in plates quenched from austenitizing 0167 J

2 Thich Section Steels puuO]

Table 1-Compositions and Heat. Treatment Temper;tures f r the Heavy.Section Steels As received thickness,

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Steel C

Mn P

S Si Ni Cr Mo Cu Al in.

Tnatment temperatures Q

A212B Ladle

.25

.70.012.037.23

.15

.07

.16

.037 6%

Austenitizing 1650' F 1 hr Quarter

.27

.72.007.025

.24

.12

.08

<.01

.15

.020 Tempering 1200* F 8 hr Center

.28

.73

.007.025

.24

.13

.08

<.01

.16

.019 Stress relief 1100* F 24 hr A533B Ladle

.20 1.28.019.030

.21

.53

.15

.52

.27

.031 7%

Austenitizing 1650' F 1 hr Quarter

.19 1.26.024.028.25

.52

.13

.52

.30

.022 Tempering 1200' F 8 hr Center

.18 1.25.024.025

.24

.52

.13

.51

.29

.025 Stress relief 1100* F 24 hr A543 Ladle

.17

.32.013.017

.28 3.65 1.86

.48 8

Austenitizing 1575' F 1 hr Quarter

.16

.34

.014.020

.27 3.60 1.89

.53

.07

.004 Tempering 1200* F 8 hr Center

.15

.32

.013.020.28 3.55 1.85

.50

.06

<.004 Stress relief 1100' F 24 hr A542 Ladle

.14

.46

.010.020.28

.25 2.35

.99

.19

.024 7%

Austen;tizing 1750' F 1 hr Quarter

.15

.46

.013.024

.31

.21 2.32 1.14

.23

.006 Tempering 1200* F 8 hr Center

.15

.46

.013.027

.30

.22 2.34 1.11

.22

.006 Stress relief 1100* F 24 hr Table 2-As-Received Mechanical Properties

• of the Heavy-Section Steels Yield Tensile

% El.

% R of Charpy V-notch Material Heat treatment str.ksi str. kai (2 in.)

A energy, (t-lb A212B Aust.1650' F, water quench. tempered 1225* F, 6 41.7 74.2 33 at 10' F-41, 40, 40 hr, stress relieved 1125' F,20 hr, furnace cool A5333 Aust. 1575' F, water quench, tempered 1225' F, 69.4 89.9 27 66.2 at 10' F-37,35,38 4 hr, stress relieved 1125' F,30 hr, furnace cool AS42 Aust.1700' F, water quench, tempered 1175' F,7 94.7 111.4 19 60.5 at 10' F-23. 30,24 hr, air cool A543 Double quenched and tempered 96.1 119.1 16.8 44.5 at 10' F-40. 60, 70, 74 at -120' F-35, 36, 38, 34

!' Q)

' Longitudinal properties, quarter thickness.

employed for accelerated cooling of heavy plates, X 16 in. x 24 in with internal baffles adjusted to it was thought wise to select generally conservative obtain the desired cooling rate. The cooling values for cooling rates attainable from quenching.

rates were obtained for the larger plates by using The cooling rates selected to represent the 6-in.

aluminum foil baffles set at experimentally deter-and 12-in. thicknesses were 0.85* F/sec and 0.25' mined distances from a free hanging plate. Therm-F/see, respectively, and are indicated on Fig.1.

ocouples were attached to the plates before These two cooling rates were then reproduced in austenitizing to monitor the cooling rates during the 2/.-in. thick test plates by simulated cooling the " quenching" cycle. Since some variation in treatments.

cooling rates did occur, only plates with cooling The material received for the program was in the rates within 0.05* F/see of that selected were form of plates approximately 10'/,in. wide by 24 used in the experimental study. To reduce edge in. long by the plate thickness (6-8 in.). These effects, approximately l'/s in. was removed from were cut into two sections approximately 10'/,in, the test plate edges before specimens were ma-by 18 in by the thickness and 10'/, in. by 6 in. by chined.

the thickness. The plates were then sectioned The tempering treatment given to the plates

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along the thickness dimension and 8/.-in. thick (Table 1) was designed to simulate the typical slices were removed at both quarter-thickness treatment given to a heavy-section plate. Since positions and two 8/.-in. thick slices were removed heavy-section plates often receive one or more on either side of the center-thickness position.

long stress-relief treatments during fabrication These plates were then heat treated as indicated operations, it was also felt desirable to include a in Table 1.

A system of aluminum foil baffles heavy-section stress-relief treatment, followed by was used to retard the cooling of the plates from a cooling rate from stress-relief as specified by the O

austenitizing to the degree necessary to produce ASME Boiler and Pressure Vessel Code for a 12-

, (.)

the desired cooling rates. This system varied in, thick plate. The test plates were accordingly somewhat with the size of the test plate, but stress-relieved for 24 hr at 1100* F followed by basically consisted of cooling the smaller plates cooling at a rate of approximately 40* F per hr in an aluminum foil lined box of dimensions 12 in.

to 600* F.

In order to determine if this slow 0168 "* "* ' ' *'

Thick Section Steels 3

cooling treatment from stress-relief was diterious Results and Discussion to toughness, some pl;tes w;re cooled at a rate cf With reg:rd to ths dita obtained in this study, 240' F per hour (approximating the air cooling of it is important to keep in mind that the program is c heavy-section plate) to study the effect of this made up of single-heat data only for the four steels coolm, g treatment.

involved and provides no statistical information.

3 On the other hand, the heats used in the study are

)

Testing Schedule e mmercially-produced heavy-section steels and therefore do represent material taken from heats The schedule of tests for each of the four steels of acceptable commercial quality. Moreover, the et quarter-and center-thickness and at two cooling real value of the program lies not so much in the r tes (6-in. and 12-in. thickness simulations) specific levels of strength and toughness obtained, included room-and elevated-temperature tension as in the comparative behavior of the various tests, Charpy V-notch and drop weight tests, steels and in the general response of the steels to cnd cantilever bending fatigue tests. In addition heat treatment in heavy sections.

to these mechanical property tests, photomicro-I'"*"'*P'

gr:phs were prepared of each of the four steels in ths simulated 6-in. and 12-in. conditions at various The results of the room-and elevated-tempera-st:ges in their heat treatment.

ture tension tests for the four steels may 1 e found The tension tests were performed in air on in Table 3 and in Figs. 2 to 9.

For three of the four longitudinal 0.252-in. diam tension test specimens steels tested the difference in cooling rate between with 1.0 in. gage length. Tests were performed the 0.85* F/sec (6-in.) condition and the 0.25* F/

ct room temperature and at elevated temperatures sec (12-in.) condition did not produce any ap-up to 1100* F.

A strain rate of 0.05 in./ minute preciable difference in mechanical properties.

was used for all tests. Center-and quarter-thick-For A212B, A542 and A543, the largest difference ness specimens of all four steels at bcth cooling in either yield or tensile strength observed between rates were tested at room temperature and 200* F.

the two cooling rates for a given position was Center-thickness specimens of both cooling rates about 3% increase in strength for the 6-in. material w:re tested at 400* F,800* F, and 1000* F, while while for a majority of the cases this dif-quarter-thickness specimens of both cooling rates ference was even smaller. For A533 Grade B, w:re tested at 600 F,900* F and 1100* F.

The however, there was a difference of about 10% in t:mperature during the elevated temperature yield strength and 5% in tensile strength between tests was controlled to within

• 5* F.

At least the two conditions, the 6-in. material once again j

two specimens were tested for each condition at being the stronger.

cach temperature and the results averaged.

In terms of general strength level, the A212 The impact tests were standard Charpy V-Grade B is by far the weakest of the four steels, notch and standard specimen type P-2 drop-with a yield strength less than half that of A542 weight tests.'

The Charpy test data were or A543, and a tensile strength about 65% that of evaluated for the 15 ft-lb energy transition tempera.

A542 or A543. The A533 Grade B lies approxi-ture, the 15 mil expansion transition temperature, mately in the mid-range between these two values.

the 50% shear fracture appearance transition It should be noted that when given either the 6-in.

temperature and the upper shelf energy value, or 12-in. treatment, the A533 Grade B, A542 The drop-weight test was evaluated for the nil and A543 all meet Class 1 specifications for these ductility temperature. All Charpy impact speci-grades while the A212 Grade B would be below m:ns were parallel to the plate rolling direction minimum specifications in the quarter-thickness and were notched transverse to the plate sur-material for either thickness.

face. Each Charpy series consisted of from 15-30 In general, there was but little difference in specimens.

strength properties between the two plate posi-The low-cycle fatigue tests consisted of con-tions, reflecting the general uniformity of composi-st nt deflection bending tests (R

- 1) on tions shown in the chenical analysis of Table 1.

standard Lehigh cantilever-bend fatigue speci-For two steels, AU u Gnide B and A542, the mid-m:ns. This specimen is 18 in. long by 25/2 in.

thickness sp V ueri v~re somewhat stronger, wide by ', in. in thickness in the test section, while for fl, s w t.vo,.A212 Grade B and A543, The range of testing included total strain ranges the qua m Q -

t a specimens were stronger.

producing failures between 1000 and 200,000 These difwrences %e no more than about 5% in cycles. Both the total strain ranges for the first yield strength and 3% in tensile strength for any visible cracking of the specimen and for complete of the steels. The only apparent segregation of separation of the specimen were recorded. Be-alloy elements or carbon evident in Table 1 T,

cause of the size of these specimens, it was neces-occurred in A543 where the quarter-section V

sary to run transverse rather than longitudinal chemistry is richer in nickel, chrordum and specimens in the fatigue portion of the study.

molybdenum. b.N 4

Thick Section Steels

Table 3-Itoom-and Elevated-Temperature Tensile Properties of the Heavy Section Steels 0.2 %

Ultimate 0.2%

Ultimate ofset tensile elonga. reduc.

ofset tensile elonga-reduc.

, f))

yield strength. tion in tion of yield strength. tion in tion of Steel and condition point.ksi ksi 1 in.

area Steel and condition point.ksi kai 1 in, area (V

Roor Temperature Room Temperature A212B A542 (Class I) 6 in. Quarter

• 39.6 6'F. 6 40.5 64.9 6 in. Quarter 94.2 111.4 20.0 68.6 6 in. Center 42.2 70.8 36.0 62.9 6 in. Center 94.2 112.2 21.0 70.4 12 in. Quarter

• 40.1 68.3 38,0 64.1 12 in. Quarter 92.9 110.5 21.0 72.4 12 in. Center 42.6 71.6 35.5 60.7 12 in. Center 93.7 111.4 16.0 63.2 200* F 200* F 6 in. Quarter 42.4 70.0 30.0 65.1 6 in. Quarter 101.5 113.4 20.0 72.1 6 in. Center 43.7 71.8 29.0 64.7 6 in. Center 100.1 112.0 19 0 71.7 12 in. Quarter 40.7 69.2 28.0 66.9 12 in. Quarter 98.8 112.3 15.0 td.o 12 in. Center 41.7 70.7 29.0 64.8 12 in. Center 98.3 111.6 15.0 66.9 400* F 400* F 6 in. Center 30.9 64.1 29.5 63.6 6 in. Center 95.2 111.5 13.0 62.5 12 in. Center 30.5 60.9 33.0 64.5 12 in. Center 91.2 111.1 14.0 61.6 600* F 600* F 6 in. Quarter 23.3 63.6 33.5 61.0 6 in. Quarter 79.4 98.3 14.0 60.0 12 in. Quarter 24.4 66.6 24.0 62.5 12 in. Quarter 74.3 92.3 14.0 62.6 800* F 800* F 6 in. Center 23.4 53.5 35.5 71.6 6 in. Center 82.7 96.2 16.0 64.8 12 in. Center 21.7 49.0 45.0 78.2 12 in. Center 83.1 88.6 15.0 62.8 900* F 900* F 6 in. Quarter 20.5 39.5 41.0 83.2 6 in. Quarter 75.0 82.4 17.0 64.5 12 in. Quarter 21.0 40.8 38.0 79.9 12 in. Quarter 71.1 79.4 16.5 64.6 1000* F 1000* F 6 in. Center 18.6 31.7 39.0 80.9 6 in. Center 70.0 74.7 22.0 77.3 12 in. Center 18.6 30.8 43.0 85.0 12 in. Center 70.5 75.1 65.4 1100' F 1100* F fs

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6 in. Quarter 16.4 25.1 36.0 84.5 6 in. Quarter 58.7 63.3 21.0 75.1 12 in. Quarter 16.3 25.9 37.0 82.5 12 in. Quarter 58.4 60.7 19.0 75.8 Room Temperature Room Temperature A533B (Class I)

A543 (Class I) 6 in. Quarter 70.0 88.7 28.0 69.5 6 in. Quarter 86.5 106.4 25.0 71.0 6 in. Center 68.2 85.9 27 0 71.2 6 in. Center 86.3 103.4 28.0 68.9 12 in. Quarter 64.1 84.6 29.0 68.8 12 in. Quarter 86.3 103.2 25.0 72.6 12 in. Center 59.0 80.6 34.0 70.1 12 in. Center 84.0 101.2 27.0 69.5 200* F 200* F 6 in. Quarter 64.8 82.5 25.0 69.3 6 in. Quarter 83.0 99.5 21.5 71.1 6 in. Center 63.4 79.8 21.0 69.7 6 in. Center 85.0 101.5 23.0 70.8 12 in. Quarter 56.7 77.5 28.0 68.0 12 in. Quarter 75.4 91.0 21.0 71.8 12 in. Center 49.9 70.0 29.0 70.6 400' F 400* F 6 in. Center 75.9 93.5 21.0 73.3 6 in. Center 60.4 80.7 22.5 12 in. Center 71.6 87.4 19.5 68.7 12 in. Center 45.8 68.4 23.5 66.4 600* F 600* F 6 in. Quarter 72.3 89.5 20.0 67.5 6 in. Quarter 58.1 83.6 21.0 60.0 12 in. Quarter 72.5 92.0 20.0 66.8 12 in. Quarter 48.5 78.9 23.0 58.0 ggg. p 800' F 6 in. Center 68.1 92.3 20.0 68.8 6 in. Center 56.7 78.0 20.0 68.9 12 in. Center 70.4 83.5 20.0 68.4 12 in. Center 40.4 71.1 26.5 66.3 gogo p 900* F 6 in. Quarter 62.6 72.2 25.0 77.3 6 in. Quarter 51.7 64.6 22.0 73.8 12 in. Quarter 64.1 72.7 24.0 78.7 12 in. Quarter 41.4 58.4 28.0 74.9 1000' F 1000* F 6 in. Center 57.0 62.0 32.5 84.2 6 in. Center 47.5 54.8 80.1 12 in. Center 57.3 60.7 21.0 83.8 12 in. Center 34.4 47.7 79.4 1100* F ON 1100* F 6 in. Quarter 48.2 52.8 27.0 87.6 k)

6 in. Quarter 44.2 45.5 26.0 81.4 12 in. Quarter 47.0 49.5 87.7 12 in. Quarter 36.1 39.8 38.0 82.6

• Cooling rate 0.85* F/sec, quarter thickness.

0170

• Cooling rate 0.25' F/sec, quarter thickness.

Thick Section Sleets 000?S L

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200 4CD ECD 800 KID 12CD 0

200 4CD 600 000 100C 1200 Testina Temperature -Y Testeg Temperature-Y Fig. 2-The influence of temperature on the yield and tensile Fig. 4--The influence of temperature on the yield and tensile strength of quenched and tempered A2128 strength *oflA5338 m

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200 4CD 6CD 800 ICID 1200 Testeg Temperature *F Testing Temperature

• F Fig,3-The influence of temperature on the elongation and re-Fig. 5-The influence of temperature on the elongation and re-duction of area of quenched and tempered A2128 duction of area of A5338 The room-temperature tensile ductilities of the compared to room temperature. The loss in four steels reflect, inversely, the tensile properties yield strength at this temperature is about 40?o of the steels. Those materials and conditions for the A212 Grade B and about 20?o for A533 with the lowest strength generally had the highest Grade B.

For A542 and A543, the tensile strength tensile ductility. The variations in ductility in loss at 600* F is somewhat greater, about 15Fo, th2 same steel with different conditions of treat-but the initial room temperature strength of these m;nt were small compared to those between steels is high enough to more than offset the in-steels. The dutility of the A212 Grade B was creased loss. The loss in yield strength of A542 almost twice that of the A542 while A533 Grade and A543 at 600 F is also about 157c. Above B and AS43 were intermedisle.

800* F the yield and tensile strengths of all of the The elevated-temperature tensile properties of steels appear to decrease sharply to values at thuteels, found in Figs. 2 to 9, show that all of the 1100* F that are approximately 507o of the room steels tend to have aging reactions between room temperature values. These eight figures (Figs.

temperature and 800* F that cause their tensile 2-9) include data from both center-and quarter-

]

i strength curves to remain relatively high up to thickness specimens (as may be seen from Table 3) 800* F.

For two materials, A212 and A533, the and both cooling rates. No apparent trends due loss in tensile strength is only about 57o at 600* F to section position appeared in the curves and the G

Thick Section Steels b

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200 400 600 800 4000 8200 Testeig Tempasture

• F Testing Temperature *F Fig. 6-This influence of temperature on the yield and tensile Fig. 8--The in'luence of temperature on the yield and tensile strength of AM2 strength of AM3 KD 100 i

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e

• 6 9o-EWm 90 Elongotion,,,, o e

,,2 te 80- Reduction of Areo 80-P a piate 7o.

o

. 8 % g-

/

8 e

g,-g 60-o 60 g

e

{ 50-

{ 50-40-4o U

30-30- %

s8 "*

~

Ae 20-

• N e -

'8 20 10-10-O o

o 2CD 4CD 600 800 1000 I200 0

200 400 6CD 8CD HKD 1200 Testing Tenperature *F Testing Ternperature

• F Fig. 7-The influence of temperature on the elongation and re.

Fig. 9-The influence of temperature on the elengation and duction of area of AM2 reduction of area of AM3 points are plotted without differentiating them.

Impact Properties Some differences due to cooling rate are apparent.

The summarized Charpy impact test results and For A533 Grade B, and to a lesser extent A542, the the drop-weight test results for the four steels are differences in strengths observed for the two found in Tables 4 and 5 and Figs.10 and 11. The cooling rates are more pronounced at elevated Charpy impact test curves are found in Figs.

temperatures. In these two cases the faster Al to A20.

The Charpy impact tests results cooled (6-in. thick) plate holds some strength generally confirm the tension test results with advantage. For the A543 and to a lesser extent respect to the influence of section location.

A212, the aging characteristics of the two different There was little or no effect in A212 Grade B or cooling conditions are somewhat different but A533 Grade B, while for A542 and A543 a decrease neither condition holds a distinct advantage.

of about 10* F in Charpy V-notch 15 ft-lb or 15 mil The elevated-temperature ductilities continue to transition temperature for the quarter-section reflect inversely the trends observed in the strength location was noted. For A212 Grade B and A533

/O curves. The ductilities generally continue to Grade B there was also little influence of cooling

( (,)

remain ranked in the same order as at room rate on toughness. For A542 and A543 a measur-temperature, while aging peaks in the strength able improvement in 15 ft-lb or 15 mil transition curves are mirrored by ductility minima in the temperature exists in the 6-in. plate as compared same temperature range.

to the 12-in. plate. In A542 this amounts to 0172 f

00 -

Thick Section Steels 7

Table 4--Charpy V-Notch Impact Test Data Table 5-Drop-Weight Test Data NDT NDT (*F)

-Trans. temp. *F--.

fiz Shelf Energy

-6 in. Plates-~ -12 in. Plates-Chemistry and 15 15 50 % energy energy requind Center Quarter Center Quarter cooling rate ft.lb mils shear (t-lb ft-lb Steel (ft-lb) chem.

chem.

chem.

chem.

A212 Grade B A212 Grade B 285 0

0

+ 10

+ 10

).

6 in. Plate centera

+ 28 0

+ 90 9

61 A533 Grade B 333

- 20

- 10

- 10

- 10 6 in. Plate RC A542 380

- 30

- 40

- 20

- 30 cenkt

+ 22

- 10

+ 90...

A543 380

- 110

- 110

- 110

- 110 6 in. Plate quarter * + 28

-2

+108 9

77 6 in. Plate RC quarter

+ 24

- 10

+ 90...

12 in. Plate center

+32

-4

+ 90 10 61 12 in. Plate RC jy$y $$$$ $$$Y $kiY iTiY ikik center

+ 28

+2

+94 Tjo...k..,.... h h..b ; h. [ "". ;?"..

"a" 12 in. Plate quarter + 32

-2

+ 105 10 74 12 in. Plate RC Syyygjj

2j

_ """ b j g

hjg %

jg jg quarter

+ 16

- 14

+ 84

5

=

1E' E,333 33 s A533 Grade B Ej 6 in. Plate center

- 28

- 56

+ 34 17 88

@ -so Zi,,,,,

s '

6 in. Plate RC 5,

c-c a

!

Ess" center

- 28

- 60

+ 54...

i -co-

'["[,,T. =,*,,*,,,,a,a,o,w,,,,=,,,,

3M s s s~

6 in. Plate quarter - 28

- 46

+ 38 15 80

)

6 in. Plate RC t.co-

'-',***C.*o*y*"',,*,*"

~

E quarter

- 24

- 48

+56

[

j 12 in. Plate center

- 20

- 48

+ 60 18 79 o -zoo-azize Ame as42 As43 12 in. Plate RC cenkr

- 24

- 56

+ 54...

12 in. Plate quarter - 16

- 40

+ 68 16 75 Fig.10-The Charpy V-notch impact test results for the four heavy 12 in. Plate RC section steels quarter

- 26

- 54

+ 60 A542 6 in. Plate center

- 66

- 72

+ 90 20 70 6 in. Plate RC

+ 20

• I,?

center

- 44

- 48 +110 YYYY '??D,?

??

_ !%c' - Y ~U-5~$~5--

6 in. Plate quarter - 70

- 78

+72 20 86 o

$5I 00 6 in. Plate RC 44YY h5 SI 0 '

quarter

- 50

- 54

+ 90..

It-12 in. Plate center

- 26

- 38 + 102 16 53

-20 g

g ;g 12 in. Plate RC 0

~ ~,

center

- 44

- 50

+62 1-40 I '

12 in. Plate quarter - 36

- 48

+ 80 16 93 Ch55 12 in. Plate RC ho a'D $",,!

I

-g, quarter

- 50

- 52

+ 44 g

...n.

?h,$

A543-d

~

Ec"J."s D A% 5L*!Od*'

-j 6 in. Plate center - 120 - 134

- 50 17 77 i

6 in. Plate RC W

center

- 150 - 160

- 70

-100

%30 6 in. Plate quarter - 130 - 136

- 38 20 71 M

6 in. Plate RC

-tzo Aztts Ams AS42 AS43 -

quarter

- 180 - 192

- 86...

12 in. Plate center 112

- 46 12 69 Fig.11-The drop weight test tes ts for the four heavy section ce te

- 164 - 172

- 58 12 in. Plate quarter -110 -120

- 50 15 70 12 in. Plate RC quarter

- 176 - 184

- 96 observed, with the largest improvements occur-a Center thickness position.

ring in the 12-in. plate specimens. The re-

• Quarter thickness position.

sponse of A542 to the rapid cooling treatment from RC - Cooled at 240' F/hr from stress relief-all others stress relief was mixed while for the other steels a cooled at 40' F/hr.; 12 m. plate cooled at 0.25' F/see from cust;nitizing,6 in. plate cooled at 0.85* F/sec from austeni.

Very slight improvement was noted.

tizing.

In general, the A543 has markedly superior notch toughness to any of the other steels in the about 35* F, while for A543 it amounts to about program and A212 Grade B had the poorest tough-20' F.

ness of the four steels. A difference in transition The use of a rapid cooling treatment from stress-temperature of over 100 F separates these two teli:f is seen to substantially improve the impact extremes while A533 Grade B and A542 are in the resistance of only one steel-A543. For this steel, intermediate range. Both of these latter steels decreases in the 15 ft-lb or 15 mil transition have transition temperatures more than 40* F

{)) - t;mperature of between 6' F to 70* F were lower than the A212 Grade B. 8 Thick Section Steels

The drop-w ight test d ta, presented in Tabis 5 consists predominantly of a mixture of upper and cad Fig.11, sh::w no response to section location lowsr bainite, with littla apparent difference or cooling rate from austenitizing for A533 Grade between the microstructures of the specimens B and A543 steels. Only A542 steel shows much cooled at the 6-in. and 12-in. cooling rates. The influence of cooling rate or location, as the 6-in. microstructure of the A543 steel (Fig.15) appears ((f thickness materialis superior to the 12-in. and the to consist predominantly of lower bainite, with quarter section is superior to the center section. some upper bainite, although the amount of trans-The results of the drop-weight tests confirm the formation to upper bainite is significantly less over-all results of the Charpy impact tests as the than occurred in the A542 steel. The occurrence steels show the same relative behavior in both tests. of substantial spheroidization during tempering The NDT temperatures are slightly higher than and stress relieving is apparent from the micro-the Charpy 15 ft-lb transition temperature for structures of the three alloy steels, but differences A533 Grade B, A542 and A543, as indicated by the in microstructure between the specimens slowly higher NDT "fix" energy listed in Table 4, while cooled and rapidly cooled from stress relieving for A212 Grade B the NDT temperature is lower are not revealed by the light microscope, even than that for the 15 ft-lb criterion in the Charpy though a substantial difference in Charpy impact test. behavior exists for these two conditions. Fatigue Tests Comparison of Light and Heavy-Section Behavior The fatigue test data obtained for the four steels It may be helpful to compare the properties of are found in Table 6 and Figs. A21 to A24. The the four steels m the heavy-section sizes studied response of the four steels to fatigue conditions '".the program with the properties which were ob-follows the pattern normally expected of low-alloy tamed in previous programs for these steel grades high-strength steels. The higher-stmngth steels treated to represent quenched and tempered, and have superior fatigue resistance in the 100,000 n rmalized and tempered, plates of relatively light section. Figures 16 and 17 summarize the tensile cycle failure region, while the lower-strength but more ductile steels are superior in the low-cycle and Charpy test properties representative of plates region. The levels of fatigue life attained in' ranging from less than 1-m. to 15-m. thickness on these tests are comparable to those found in equal-the basis of coohng rate from austenitizmg. For strength lighter-section plate. the most part the tensile properties show a gradual loss of strength as thickness is mcreased. The Microstructures notch toughness uniformly decreases with greater thickness; but A212 and A543 show a progressive The microstructures of the four project steels loss, while A533 and A542 sustain most of the loss are seen in Figs.12 to 15. The A212 Grade B steel of toughness as sections are increased to about 4 (Fig.12) consists of fairly coarse aggregates of in., above which relatively little change is incurred. e ferrite and pearlite, with the difference in cooling 3 rate from austenitization resulting in no significant Summan difference in microstructure. Tempering and stress relieving resulted in some spheroidization of The results of the study of the four heavy-the pearlitic carbides. The microstructure of the section steels can be summarized as follows: A533 steel (Fig.13) consists largely of ferrite and

1. There were no important changes in strength, low-temperature transformation products, re-notch toughness, or fatigue resistance produced by flecting the microsegregation occurring during the reduction of cooling rate during quenching cooling, with the enriched austenite remaining when the section size is increased from 6 in. to 12 after the ferrite precipitates, finally transforming to in. in A212 Grade B, A533 Grade B, A542, or areas of high-carbon high-alloy martensite or A543 steels tested in the quenched, tempered and bainite. The ferrite precipitation and resulting stress-relieved condition.

microsegregation is markedly more pronounced at

2. The property most affected by increase of the the 12-in cooling rate than at the 6-in. cooling rate.

section thickness from 1-in. to the 6 to 12 in. range The microstructure of the A542 steel (Fig.14) is notch toughness. Rises of 50 to 100* F in transi-Table 6-Plastic Fatigue Resistance of the Heavy-Section Steels Total strain range-% s/n in. Crack Failur: l$ Steel Condition 5000 cyc 10,000 cyc 50,000 cyc 5000 cyc 10,000 cye 100,000 cyc A212B 12 in. Center and quarter chem. 0.75 0.60 0.36 1.20 0.92 0.39 v A533B 6 in, and 12 in. center and quarter chem. 0.71 0.59 0.37 0.82 0.68 0.40 ' A542 12 in. Ce,..er and quarter chem. 0.80 0.69 0.50 0.95 0.79 0.49 A543~ 12 in. Ceter and quarter chem. 0.79 0.65 0.50 0.96 0.78 0.48 0174 () O n n n .' i ' Thich Section Steels y _-~v, l

) e t=n,ta. (o.as ri.m.: azirs t2 t== pt.c. (o.as*ri 6 t=m paa. (o.as rt =.) s.ssa 12 t=m et.c. (o.n'r/=.) O'" u'y d,r' O*Wmm

^ a a' n ds.9y

-.- g J L4 1i ^ *..,,*d,.W' n 3,. m l ' ef .} W l uh.:.% k $ &u f,,;,}< l h .b % 9 -t % nw b6 q j k JA' a a' e {;) I U[aD:j q 4.,'l Nh*h,.h M 4I T d. i . E A .:.=h.4 ,g

'.a

?hiv;@g.s i k<3 g ~; g.5 M 1

u. m

.g 'N l'.k,!.'Mbb b.I ,[ {g j J Y, **$ ( -M, serYa$.a 7 . IY/ k'*t4)A'. 'g ",ll "*,""" g. d h.5 ( j o=achd .'J(% I 4 {p \\' % [gy j ,' N.t W 'f. e$ w.yf f.. k: ~ ~ FNXj V: g M i .se r.u...,.,.... f.. T si ' c g. p y l 4- - ?b 5 (h;,, ~ 'Y A.

f fh,

$)Nt -:il,v f..J.f } .y.J x v: s (_2 .. '. - c s. a. I Fig.14-The microstructure of AS42 (Nital etch, X 500) i Fig.12-The microstructure of A2128 (Nital etch, X 500) I a t=m et.e. (o.ss ri. .) a543 in t a,1.i. (o.as ri. .) e =m,ta. co es rt....) a332n 12 i.ch,i.. (o.25 rt.... J Z %t*C SY.9; -.. q w ; 1 4 g 4. %.=hu F=Y, y-h '5';f. %mhd ~ )+ ~' rs: rs: E=E lE4! 'N'. ,( , h 'r

• r p;

y'i f,'{ cy { i,,*,' sir. ,a U** *** ' ) u.n mt) ppf k b O 2*d b f $:r a Fig.13-The microstructure of A5338 (Nital etch, X 500) Fig.15-The microstructure,of A543 (Nital etch, X 500) e 017d 10 Thick Section Steels NUUIl -

W ... i s i i i i i. . i i 3 A m Tome Sereniph"' N Oo ,e .ne,

• d

' /*'"'* 8" TIE!L. Io. /] 4o. o 0 20-20-A543 AS42 ~ 0 o i k so- ._-e,,- -So ,,, e e it E o ? g.-oo. /e -So- [g .. Tempered at12OO'F ~' a aTemperedat1350*F- $ oo- -e A212 Grode B / eo odeA a a a Gr.adeB. N _2 o 2 4 6 e o 12 14 o 2 4 6 8 o r2 14 16 4 6 8 c 12 14 o 2 4 6 8 C 12 I4 is Quenched andTempered Platelheness-m Quenched and Tempered PiareThickness-in Fig.16-The strength and toughness of A2128 and A533 as in. Fig.17-The strength and toughness of A542 and A543 as in. fluenced by simulated plate thickness. fluenced by simulated plate thickness tion temperature were observed in these steels. Acknowledgment Fortunately, the alloy steels display transition The authors are grateful to the members of the temperatures below -10* F even in heavy sec-Materials Division of the Pressure Vessel Research tions. The notch toughness of the A543 steel Committee for their advice and guidance, and to was markedly superior to that of the other steels PVRC for support of the investigation. They treated at coohng rates corresponding to the thick-wish also to express their appreciation to the Foster-nesses of either 6 or 12 m. Wheeler Corp. which contributed extensive ser-

3. The fatigue properties of the steels matched vices in the preparation of the test plates.

those of steels with similar tensile properties developed in lighter sections. The allowable g strain range for a fatigue life of 100,000 cycles (j correlated well with tensile strength, while the strain range for 5000 cycles appeared to be related principally to the ductility of the steel (as observed in previous work). References

4. The elevated temperature tension tests indi-

1. cro. J. H.. ana stout. R. D.. "rhe Performance of High Strength cated about the same characteristics in these steels s"""J,"773*"co' M, !",S.'"'

8'**"' " ""' " " '3' "*"*'*h as those observed in thin-gage steels, including the

2. om. J. H., ana stout. R. D.. -eropertie. and Weldability of High.

Strength Preneure.Vennel Steels in Heavy Sections," Ibid.,38 (3) Research stra.in-agmg phenomena m. the 400-800* F tempera-Suppi.. tS7.e to 167.e.19s7.

3. Gross, J. H., Kotteamp, E. H., and stout. H. D.. "Effect of Heat ture range. For A533 Grade B and A542, the rre.t ent on th. uiero.tructure.nd eropertiee of er ore.ve e Steet "

6-in. thick plate material 'vas superior to the 12-in. 16i4 37 (4), Reemarch Suppl.160.e to 168.e.1958.

4. Lorentz. R. E Jr.. " Utilization of Quenching and Tempering for plate material at elevated temperatures to 1000* F.

Imp =v-nent in Properties of Low Ailoy Steels in Heavy Thicknesses for Welded Construction."16sd 41 (10). Research Suppl. 433.s to 447.e,1962.

5. Metallographic examination generally sub-

5. Kottcamp. E. H Canonico, D. A., and Stout. R. D., " Prediction of the P

" * '" h stantiated the small differences in properties ob- . Dred 'N",'O "h suq. 3 ' ?s't 6." served between specimens cooled at the rate to be

6. stout. R. D "Higherotrength Steels for Weided-Structures." Ibid.,

Se (7), Remoarch Suppl.,273.s to 283.a.1960. expected m. a 6-m.. section and those cooled to

7. rua k. P. e.. ana retiini. w. s.. " Standard usthoa for NRL Drop Weight Test." NRL Report 5831, 1962, United States Naval Research match a 12.m. section.

tahor,to,y wa.hington. D. c. Of76 UU U 7 (- ~ y( Thick Section Steels tt

u. = l p _ N Jw 2# s s _ f :[. e 1 , j./* 3 ~ :j /e e / hf i .M /,/ i h ~~ , :,3 i olN l~ _ge l" _py' "' 36 =

• w.

.u. .u. u. .= .u. .u. .= = = u. = w.-,- m % w. m Fig. Al--Charpy V-notch impact data for code-stress-relieved Fig. A4-Charpy V-notch impact data for code-stress-relieved A2128,6 in. plate, quarter location A212B,12 in. plate, center location u. u. i -[ l ~ ~ f a--. /

1. "M j

~_. j t'/I 3 w e i,, / n i,, 1 fr i 3 9/ g . n i 1 d' ,,t/ s I i f7~ j" ,,2 Y j" 5.f'h m. i g, u. .u. u. -.-.--m m Fig. A2---Charpy V notch impact data for code-stress-relieved Fig. AS-Charpy V notch impact data for code-stress-relieved A2128,6 in. plate, center location A5338,6 in. plate, quarter location j I 1 u. u. u. I -/ / ~t / 2 y / c, g,. a ) / / / /'s M j n/ .?= -7 3 1. 3 h,, _ _ _ g //6 j,, kk i I' i M A., M f 4 l 4-4 #o .y SM*

• .y j

..pg- .a ( i j .= -o. u. u. .= .u. = u. u. .m .,- m F3 Al--Charpy V-notch impact data for code stress relieved Fig. A6-Charpy V-notch impact data for code-stress-relieved A2128,12 in. plate, quarter location A5338,6 in. plate, center I ~ ,.,, n 7 _ 12 Thich Section Steels GUviJ

_. m Y / \\\\ ./ s _s l ( (u..;') / / J y-- j = = a., tr/ i ,/ dk N = = } } M i .r% i _ ' ff 'i. L _. ..W,, .= = a5.. f f l .Vg A.g ta J .-. - p y - y-w . ~ _ _. g . c., ._.-.c., Fig. A7-Charpy V. notch impact data for code-stress. relieved Fig. A10-Charpy V-notch impact data for code stress relieved A5338.12 in. plate, quarter location A542,6 in. plate, center location = = i }. I ,/, ~ ~ e. e. ___d*[ __I_ /J' ] t j / f,. I/ j., f ^ !fi. j ^ lV, y ( s )i d '. i __. :..I /e I i . L. i r g

f...___

e AV e A a,, B I -.-g_pK.. I ' J f L4 .. 3/ -s en ~ ~ _ en Fig. A8-Charpy V-notch impact data for code-stress-relieved Fig. All--Charpy V notch impact data for code stress-relieved A5338.12 in. plate, center location A542.12 in. plate, quarter location I i ~ {. ~ ~ ~ / f ../VT a /Y a' l l i i i F i., i 1 j. I g/. I T } - ---p,,-- A i i _.-$- /$ i .-. -l.Y.<.0 A / _I e I" _to, tge../ I s e m O, I" .g4-.-... =, / p i: ) m., .-._.c., ._.c, Fig. A9-Charpy V notch impact data for code-stress relieved Fig. A12-Charpy V notch impact data for code stress-relieved AS42. 6 in. plate. quarter location AS42.12 in. plate, center location 4' 0178 Jm u 4 v i 't ~ 13 Thich Section Steels vv

. l _ / I a-a- / l 7 e j } j / f j,, / fe I ~ 2,, I ./.e[-. , /_ / I 8 s N.e ' }., .Y / I f-p/ I A,- .-.)i l 2

a a

j) I A,, Ed 8 3 j U.._. j e # y -_.._ i ._popar ..__; g. .= u. .= s. = u. = .-- m w -. w m Fig. A13-Charpy V notch impact data for code. stress relieved Fig. A16-Charpy V. notch impact data for code-stress-relieved A543,6 in, plate, quarter location A543,12 in. plate, center location 3---. y s,. s-f a-g j .. -.L i / / \\ i i / i- = I l / y-s s - y -- i i n A W j gr g __g 4 -. Wj j" . si

- o pp-j.

..g -3. m.. m __m Fig. A14--Charpy V. notch impact data for code stress reiieved Fig. A17--Charpy V. notch impact data for stress relieved and air AS43,6 in. plate, center locatlon cooled AS43 6 in. plate, quarter location u. u. ~ a-a- / l ./ j i., - / /* i., . / -/.. .--. _ e.!g .c j a f-.. / p w j ..gg,=- ) _g g a i u. w -m -.-- m Fig. A15--Charpy V. notch impact data fnr code-stress-relieved Fig. A18-Charpy V. notch impact data for stress relieved and A543,12 in. plate, quarter location air cooled A543 6 in. plate, center location 14 Thich Section Steels

= i o o i 6i j I Z / ..dw, I o a I

a. =

1.,:-

.. ~ / ,V ( e,-m., 1 J.- ww. i J n 3 V f y j[ "*Efn _a e/e 2 i rt s i.- J td 4M l,, ,s.sf,A , ;,4 i o -= p ,.., s , i i, u- .. i, s, e v = = u. .u.... c,, 6.

4.,r.

oir. ._6,r. Fig. A19-Charpy V notch impact data for stress relieved and air cooled A54312 in. plate, quarter location Fig. A22-Plastic fatigue data for heavy section A533B = n i i i im i i n n i ! 1 1I k' h fl /

8. "

/-

• '.o c;

o c n j

• r

.I *- -- il Dd :_ I 'I C' I 4 f, M /j_ l," t T s Xo ____41__. 4 ad a-((/q) i / r v a ( .g.p - v a 8' W l l -t J _-yy i c .m___ s ,y 's u. .'"= - m ~,o..., l~g. A20-Charpy V. notch impact data for stress relieved and air

• " "*'~""

cooled AS4312 in, plate, center location Fig. A23-P;astic fatigue data for heavy section AS42

'i i

r I i--y-in ~ g g 1 3 N A h l I s h i i i ,N. N at il I I l t- ,.i. s c__c4c i x x, ,I. ' a". ~m J,.. - o I

• w i

o q s i .4 i Ns. o j[ j ~ N I.. i o I I i .c y e 's.' I lf [m') i ,i i,. 2 ,..,.s . a -..,c s.,ys.,; ^U.1 .c,,.... o,., y. ,i, w.. .,.o. ..e ...o.. .m. .,~ --. Fig. A21-Plastic fatigue data for heavy section A212B Fig. A24-Plastic fatigue data for heavy section AS43 i Thick Section Steels OOOQ4 15 l m f}}