Development of an Improved HPS-100W Steel for Bridge ApplicationsA. D. Wilson, Bethlehem Steel, J. H. Gross, Lehigh University, R. D. Stout, Lehigh University,

R. L. Asfahani, United States Steel and S. J. Manganello, Consultant

Abstract

After extensive laboratory studies, a Cu-Ni alloy steel withsignificantly improved properties for 690 MPa (100 ksi) yield-strength weathering steel infrastructure applications, such asbridges, was recommended. To confirm these results, a 150 MT(165-ton) full-scale heat of the recommended composition wasproduced. Plate and tubular products were evaluated for 690MPa (100 ksi) applications by quenching and temper-aging. Theinvestigation indicated that the products replicated quitefaithfully the excellent strength, toughness, and weldabilityobserved in plates from laboratory heats. Additional refinementof the chemistry took place with another laboratory heat withhigher manganese content. The results indicated that thehardenability and the yield and tensile strength after aging wereincreased sufficiently to ensure meeting a minimum yieldstrength of 690 MPa (100 ksi) through 64 mm (2-1/2-inch)plates. Based on the Alternative ASTM Standard G 101(Predictive Method Using the Data of Townsend)1, the steelshows an excellent calculated atmospheric weathering corrosionindex of 7.5.

On the basis of these studies, the following composition isproposed for an HPS-100W* Cu-Ni age-hardening ASTM A709Grade in weight percent: 0.06 C, 1.25 Mn, 1.00 Cu, 0.75 Ni,0.50 Mo, 0.50 Cr, 0.02 Cb and 0.06 V.

Additional large-scale programs are currently underway todocument improved mechanical properties and weldability andto test prototype HPS-100W girders for strength, ductility,fatigue, and fracture performance.

Introduction

The specification for a 690W (100W) (690 MPa {100 ksi})minimum-yield-strength, weathering grade) bridge steel iscontained in ASTM A709, “Standard Specification forStructural Steel for Bridges”1, and the specified compositionsare based on ASTM A514, “Standard Specification for High-Yield-Strength, Quenched and Tempered Alloy Steel Plate,Suitable for Welding” 1. Although the various A709 690W(100W) grades have performed satisfactorily in numerous bridgeapplications,

they have only moderate fracture toughness and require preheatfor welding, which is a costly fabrication operation. Whilebridges have not commonly utilized 690 MPa (100 ksi) yieldstrength steel, a steel with better fracture toughness andcorrosion resistance, that can be welded with limited preheatwould significantly increase its use in bridges with concomitantcost savings. To respond to this need, the Lehigh UniversityCenter for Advanced Technology for Large Structural Systems(ATLSS) began a program to develop an improved 690W(100W) steel as part of the American Iron and Steel Institute(AISI), Federal Highway Administration (FHWA) and U.S.Navy High-Performance Steel (HPS) Steering Committeeprogram. Specific assistance was provided from U. S. Steel inthe melting of laboratory heats, the production by BethlehemSteel Corporation of a commercial heat of the optimumcomposition and the production of plates and tubes by both steelcompanies.

The ATLSS program, conducted over a ten-year period,involved four phases: (1) selection of a metallurgical alloysystem2, (2) optimization of the selected Cu-Ni age-hardeningcomposition3, (3) the production and evaluation of a 150 MT(165-ton) commercial heat4, and (4) the proposal of aspecification for an HPS-100W ASTM A709 Cu-Ni Grade5.Additional large-scale test programs on the HPS-100W Cu-NiGrade are currently underway to document its improvedweldability and to test prototype girders for strength, ductility,fatigue and fracture performance. Additionally, extensiveCharpy V-notch (CVN) and compact-tension fracture-toughnesstests are being conducted by the Turner-Fairbanks Laboratory,FHWA. The results of the ATLSS development program aresummarized in the present report.

Experimental Results

Selection of a Metallurgical Alloy System - The selectionof a metallurgical alloy system involved the melting of 227 kg(500-pound) laboratory heats of the compositions listed in TableI. Steels 1 and 2 are low-carbon boron-free quenched andtempered steels. Boron was omitted because of its embrittlingeffect, which was reported by ATLSS and subsequently by otherinvestigators6. Steels 3-5 are Cu-Ni precipitation-strengthenedsteels with increasing copper contents and correspondingincreases in nickel to offset any hot-shortness related to copper.The use of the Cu-Ni system allows lower carbon contents.Other alloy additions allow higher strength levels and thicker

* Throughout this paper, HPS-100W will be used to refer toan improved grade of weathering steel with 690 MPa (100ksi) minimum yield strength

products.7 Typical tensile and CVN properties for 1-inch-thickplate of the four laboratory steels are listed in Table II. Theresults indicated that the mechanical properties of the Cu-Niage-hardening steels (Steels 3, 4 and 5) were significantly betterthan those for Steels 1 and 2. The strength of the steels wasrelated to their respective Jominy-test8 characteristics as inFigure 1, which shows that increasing the hardenabilityincreased the strength at all plate thicknesses. Steel 3 is marginalfor a 690W (100W) specification.

These data led to the conclusion that the Cu-Ni age-hardening system would readily meet a minimum yield strengthof 690 MPa (100 ksi) in plates well over 25 mm (1-inch) and atcarbon contents of 0.06 to 0.07 percent, far below the typicalcarbon content of 0.15 percent for structural steels such as theASTM A514 grades. This low carbon would ensure excellenttoughness and weldability. The next step, therefore was tooptimize the composition of the Cu-Ni age-hardening steel.

Optimization of the Cu-Ni System - The optimization ofthe Cu-Ni system involved 136 kg (300-pound) laboratory heatsthat were cast into 45 kg (100-pound) ingots. The compositions,Steels A, B, E. and F, Table III, comprise a factorial programbased on three carbon contents (0.04, 0.06, and 0.08%), twomanganese contents (1.00 and 1.50%), and two molybdenumcontents (0.25 and 0.50%). The base composition of 1.00 Cuand 0.75 Ni was found to be as low as practical to achieve thestraightening of the precipitation hardening reaction.

The as-quenched Jominy curves for the four steels areshown in Figure 2, 3, and 4 for carbon contents of 0.04, 0.06 and0.08 percent, respectively. Also shown in Figure 5 are theJominy curves for Steel B6 as-quenched and after aging at 510,565, 620, and 675C (950, 1050, 1150, and 1250F). SimilarJominy curves were obtained for the other steels, but are notshown because evaluation of the Jominy curves and theirmechanical properties resulted in the selection of Steel B6 as theoptimum composition for an HPS-100W bridge steel.

The mechanical properties for Steels B4, B6, and B8 arelisted in Table IV. The results indicate that the yield strengths at0.04 percent carbon would be too low over the temperingtemperatures of interest, particularly in heavy sections, that theyield strengths at 0.08 percent carbon were higher than required,and that the yield strengths at 0.06 percent carbon were the bestcompromise from the standpoint of strength and toughness. Notethat the CVN energy values for Steel B6 at –40C (-40F) are 122-244J (90-180 ft-lbs.) compared with the ASTM A709specification of 47.5 J (35 foot-pounds) at –23C (–30F).

The results of weldability implant tests on the four steels arecompared with each other and with A852 and A514 type steelsin Table V. In nearly all cases, the threshold failure stresses ofthe Cu-Ni steels were at or above their typical yield strengths. Adiscernible lowering of their threshold stress occurred with anincrease in the carbon content, but only the 0.08%C Steel F withthe highest carbon equivalent showed a threshold stresssignificantly below its yield strengths. The same effect of carbonon threshold stress was observed for the A852 and A514 steels.The results of the implant tests of the Cu-Ni steels indicate thatthey are sufficiently resistant to heat-affected-zone cracking tobe welded by low-hydrogen processes without preheating,

provided that the carbon content is maintained at or below 0.08percent. Additional larger-scale tests are underway to confirmthe implant-test results.

Production and Evaluation of a 150MT (165-Ton)Commercial Heat - To confirm the suitability of Steel B6 asthe optimum composition for an improved 690W (100W) bridgesteel, a 150 MT (165-ton) heat was electric-furnace melted at theCoatesville plant of Bethlehem Lukens Plate to the aimcomposition shown in Table VI. Also shown are the heatanalysis and product analyses.

Melting and Rolling - The ladle of steel was vacuum-degassed and calcium treated. It was teemed (bottom-poured)into ingot molds, stripped, slabbed, and shipped for furtherprocessing as shown in Table VI along with the final materialsproduced.

Jominy-Test Results – The Jominy curves for the as-quenched and for the quenched and aged Jominy specimens areshown in Figure 6. The curves are very similar to those for SteelB6 shown in Figure 5, as expected.

Mechanical Properties – The product forms, heat treatmentsand associated mechanical properties are listed in Table VII.These data demonstrate that the composition selected is mostsuitable for plates through 25 mm (1-inch) thick. Above 25 mm(1 inch), some adjustment in steel composition would beappropriate. To avoid the possible need to re-heat treat heavy-gauge product to obtain the 690 MPa (100 ksi) minimum yieldstrength, a study 5 was conducted on a laboratory heat thatindicated that an increase in the manganese content from 1.00 to1.25 percent would ensure meeting the minimum yield strengththrough 64 mm (2-1/2 in.). The composition and mechanicalproperties of this steel are listed in Table VIII. To illustrate theexcellent CVN toughness of the production heat, full Charpycurves for 25 mm and 51 mm (1- and 2-inch) plates for theproduction heat and for the higher manganese laboratory heatafter aging at 620 C (1150F) are shown in Figure 7. A summaryof all tensile and CVN data on all plates is shown in Figures 8and 9.

Some interest was expressed in the effect of interrupted-accelerated cooling (IAC)9 and of controlled rolling on themechanical properties of the production plates. Previous workhas shown the Cu-Ni system to respond well to theseprocesses10. The results of limited trials for such practices arelisted in Table IX. The results for the IAC indicate that yieldstrengths of 690 MPa (100 ksi) may be possible, but additionaltests would be required to confirm the results. The results forcontrolled-rolling suggest that an aging treatment would berequired to meet a minimum yield strength of 482 MPa (70 ksi).

Implant-Test Results – Figure 8 illustrates the limited dataobtained from implant tests of production material. The resultsindicate that the threshold stress for cracking was at or above690 MPa (100 ksi). This suggests that welding using low-hydrogen processes can be undertaken without the need topreheat. Larger-scale tests are currently underway to confirmthis observation.

Metallography – The microstructures at various distancesfrom the quenched-end of the Jominy specimen are illustrated inFigure 9. The microconstituents range from essentially all

martensite at the 3.2 mm (2/16-inch) location to decreasingamounts of MA constituent (martensite/austenite) and increasingamounts of ferrite at increasing distances from the quenched-end. The microstructures that would be expected at the mid-thicknesses of various plate thicknesses correspond to thefollowing distances from the quenched-end, as shown in Figure9 (25 mm = 6/16”, 51 mm – 11/16”, 76 mm = 14/16”, 102 mm =12/16”).

Weathering Characteristics – The following table comparesthe calculated corrosion-resistance index for the production heatcompared with typical 50W, HPS-70W, and 100W.

A709 Grade Alternative ASTM G1 Index50W 6.2 HPS 70W 6.7100W 6.5HPS-100W (Cu-Ni) 7.5

Proposed Specification for an Improved HPS-100WBridge Steel - On the basis of the various ATLSS studies andreview by the Steel Advisory Group of the AISI HighPerformance Steel Committee, the following composition4 isproposed for an HPS-100W Cu-Ni age-hardening ASTM A709Grade:

C Mn P S Si Cu Ni0.08 0.95 0.015 0.006* 0.15 0.90 0.65Max. 1.50 Max. Max. 0.35 1.20 0.90

Cr Mo V Cb Al N0.40 0.40 0.04 0.01 0.020 0.0150.65 0.65 0.08 0.03 0.050 Max.

* steels should be calcium-treated for sulfide shape control

Conclusions

After extensive laboratory studies, a Cu-Ni steel withsignificantly improved properties for 690W (100W)infrastructure applications, such as bridges, was recommended.To confirm these results, a 150 MT (165-ton) full-scale heat ofthe recommended composition was produced. The plate andtubular products were evaluated for 690W (100W) applicationsby quenching and temper-aging. The investigation indicated thatthe production plates replicated quite faithfully the excellentstrength, toughness, and weldability observed in plates fromthe 45 kg (100-pound) laboratory heats. A further laboratoryheat was evaluated with increased manganese content. Theresults indicated that the hardenability and the yield and tensilestrength after aging were increased sufficiently to ensuremeeting a minimum yield strength of 690 MPa (100 ksi) through64 mm (2-1/2-inch) plates. On the basis of the AlternativeASTM G101 Standard, the steel shows an excellent calculatedcorrosion indexof 7.5.

Acknowledgements

The guidance of the Steel Advisory Group ofAISI/FHWA/U.S. Navy High Performance Steel SteeringCommittee and the support of the Federal HighwayAdministration and the Pennsylvania Infrastructure TechnologyAlliance are gratefully acknowledged. The assistance of theproduction (Bethlehem – Burns Harbor, Coatesville andConshohocken; U.S. Steel – Gary and Fairfield) and research(Bethlehem Homer Research Laboratories; U. S. Steel TechnicalCenter) locations are also appreciatively acknowledged. Theauthors would like to thank Mrs. Rose Terriman for herassistance in developing this paper.

References

1. ASTM Annual Book of Standards, Vol. 01.04 and Vol.03.02, 2002.

2. Gross, J. H. and Stout, R. D., “ATLSS Studies on ChemicalComposition and Processing of High Performance Steels”,ATLSS Report No. 95-04, March 1995.

3. Gross, J.H., Stout, R. D., and Dawson, H.M., “Copper-Nickel High Performance 70W/100W Bridge Steels - PartII”, ATLSS Report No. 98-02, May 1998.

4. Gross, J.H. and Stout, R. D., "Evaluation of a ProductionHeat of an Improved Cu-Ni 70W/100W Steel", ATLSSReport No. 01-10, June 2001.

5. Gross, J.H. and Stout, R. D., "Proposed Specification for anHPS-100W Cu-Ni Age-Hardening ASTM A709 GradeBridge Steel", ATLSS Report No. 01-15, Nov. 2001.

6. Tanaka, A.,"Information on the New Steel HT780 WithLow-Cracking Sensitivity", Nippon Steel Corporation, June1995 and Private Communication

7. A. D. Wilson, E. G. Hamburg, D. J. Colvin, S. W.Thompson, G. Krauss, “Properties and Microstructures ofCopper Precipitation Aged Plate Steels”, ConferenceProceedings, Microalloyed HSLA Steels, ASMInternational, 1988.

8. USS Carilloy Steels, Carnegie-Illinois Steel Corporation,Pittsburgh, PA, 1948.

9. R. L. Bodnar, Y. Shen, D. W. Elwood, F. C. Feher, G. J.Roe, “Accelerated Cooling on Burns Harbor’s 160” PlateMill”, Accelerated Cooling/Direct Quenching of Steels, ed.R. Asfahani, ASM International, 1997.

10. S. J. Manganello and A. D. Wilson, “Direct Quenching andIts Effects on High Strength Armor Plate”, Low-CarbonSteels for the 90’s, ed. R. Asfahani and G. Tither, TMS,1993.

Table 1 – Chemical Composition of Series A

C Mn P S Si Cu Ni Cr Mo V Al N Cb CE*1 0.074 1.000 0.009 0.003 0.250 0.007 0.750 0.500 0.490 0.071 0.021 0.006 0.030 0.542 0.110 0.990 0.011 0.003 0.250 NA 0.800 0.500 0.490 0.069 0.030 0.006 0.031 0.583 0.068 1.520 0.009 0.004 0.260 0.730 0.750 0.500 0.250 NA 0.035 0.006 0.030 0.614 0.066 1.000 0.008 0.004 0.270 1.080 0.900 0.740 0.490 NA 0.027 0.005 0.032 0.665 0.067 1.250 0.008 0.004 0.280 1.230 1.250 0.740 0.490 0.070 0.029 0.005 0.032 0.76

NA – none added – no boron added to any heat

* CE = C + Mn/6 + Si/6 + (Cu + Ni) /15+ (Cr + Mo + V)/5

Table II – Mechanical Properties of Series A Steels

Tensile PropertiesCharpy V-Notch

Energy Absorbed, J (ft-lb.)

Processing Condition Temperature, oC, (oF)Y.S.MPa

Y.S.ksi

T.S.MPa

T.S.ksi

Y.S.T.S. -180C 00F -400C -40 o F

Steel 1 – A*Tempered 649C, (1200F)Tempered 677C, (1250F)

676676

9898

738738

107107

0.920.92

108191

80141

5465

4048

Steel 2 – A* Tempered 621C, (1150F)Tempered 677C, (1250F)

800807

116117

889855

129124

0.900.94

3443

2532

2023

1517

Steel 3 – A*Tempered 566C, (1050F)Tempered 593C, (1100F)

690669

10097

752738

109107

0.920.91

146283

108209

122258

90190

Steel 4 – A*Tempered 607C, (1125F)Tempered 635 C, (1175F)

779745

113108

827793

120115

0.940.94

157165

117122

117160

86118

Steel 5 – A*Tempered 649C, (1200F)Tempered 691C, (1275F)

869724

126105

896765

130111

0.970.95

115167

85123

102156

75115

*A – austenitized at 899C, (1650F)

Table III – Chemical Composition of Series B Steels

A4 A6 A8 B4 B6 B8 E4 E6 E8 F4 F6 F8C 0.045 0.064 0.082 0.043 0.061 0.080 0.042 0.060 0.076 0.040 0.059 0.081Mn 1.000 1.010 1.000 1.010 1.020 1.010 1.520 1.520 1.500 1.510 1.500 1.490P 0.012 0.013 0.013 0.010 0.011 0.010 0.011 0.011 0.012 0.010 0.011 0.011S 0.003 0.003 0.003 0.003 0.003 0.003 0.003 0.003 0.003 0.003 0.003 0.003Si 0.230 0.230 0.240 0.260 0.270 0.260 0.250 0.260 0.270 0.250 0.250 0.250Cu 1.020 1.020 1.020 1.000 1.010 1.000 1.000 1.020 1.020 0.990 0.990 0.990Ni 0.750 0.740 0.750 0.750 0.770 0.760 0.770 0.800 0.810 0.780 0.780 0.770Cr 0.500 0.500 0.500 0.510 0.510 0.510 0.510 0.510 0.520 0.500 0.500 0.500Mo 0.240 0.240 0.240 0.500 0.500 0.500 0.250 0.260 0.260 0.510 0.500 0.500V 0.057 0.056 0.056 0.054 0.054 0.054 0.059 0.057 0.056 0.059 0.059 0.059Cb 0.015 0.015 0.015 0.018 0.017 0.018 0.016 0.016 0.016 0.017 0.017 0.016Al (total) 0.022 0.020 0.019 0.024 0.015 0.012 0.025 0.021 0.019 0.022 0.026 0.025

Table IV – Longitudinal Mechanical Properties of B Steels After Various Heat Treatments

Tensile Properties Hard. CVN Transition Temperatures CVN Energy

Processing Condition Temperature Y.S.MPa

Y.S.

ksi

T.S.MPa

T.S.

ksi

Y.S.T.S. HRC

47 J oC

(35 ft. lb.)oF

50%FATT

oC oFJ@

-40oCFt.-lbs.@

-40oF

B4 Steel SQ25Tempered 566C, (1050F)Tempered 621C, (1150F)Tempered 677 C, (1250F)

745731676

10810698

827786717

120114104

0.910.920.94

2523.5

17

-122-122-183

-90-90

-135

-34 -30-34 -30-46 -50

136150190

100110140

B4 Steel SQ102Tempered 566C, (1050F)Tempered 621C, (1150F)Tempered 677 C, (1250F)

655648627

959491

772745696

112108101

0.850.810.90

2120

15.5

-136-115-129

-100-85-95

4.4 40-29 -20-51 -60

136176230

100130170

B6 Steel SQ25Tempered 566C, (1050F)Tempered 621C, (1150F)Tempered 677 C, (1250F)

800807738

116117107

883862772

128125112

0.900.930.95

28.52721

-149-190-230

-110-140-170

-51 -60-48 -55-62 -80

122163217

90120160

B6 Steel SQ102Tempered 566C, (1050F)Tempered 621C, (1150F)Tempered 677 C, (1250F)

724676648

1059894

820793717

119115104

0.880.850.90

2322.5

19

-102-149-149

-75-110-110

4.4 40-54 -65-51 -60

136190244

100140180

B8 Steel SQ25Tempered 566C, (1050F)Tempered 621C, (1150F)Tempered 677 C, (1250F)

889869772

129126112

958917807

139133117

0.920.950.96

30.529.5

23

-136-176

<-237

-100-130

<-175

-29 -20-43 -45-84 -120

115142210

85105155

B8 Steel SQ102Tempered 566C, (1050F)Tempered 621C, (1150F)Tempered 677 C, (1250F)

724703669

10510297

848820745

123119108

0.850.860.89

25.523.520.5

-136-108-197

-100-80

-145

10 50-20 -5-23 10

108129190

8095

140

SQ25 – simulated quench of 25 mm (1 in.) plate 28oC (50oF/sec.)SQ102 – simulated quench of 102 mm (4 in.) plate 5oC (9oF)/sec.

Table V – Implant Welding Test Results

Typical Yield Strength MPa (ksi)

Threshold to FailureStress MPa (ksi)

Cu-Ni Steels MPa ksi MPa ksiSteel A – 0.04% C 621 90 772 112Steel A – 0.06% C 655 95 731 106Steel A – 0.08% C 690 100 648 94Steel B – 0.04% C 655 95 820 119Steel B – 0.06% C 690 100 731 106Steel B – 0.08% C 724 105 690 100Steel E – 0.04% C 655 95 820 119Steel E – 0.06% C 690 100 690 100Steel E – 0.08% C 724 105 690 100Steel F – 0.04% C 690 100 772 112Steel F – 0.06% C 724 105 690 100Steel F – 0.08% C 793 115 648 94A852 – 0.06% C 448 65 621 90A852 – 0.10% C 517 75 517 75A852 – 0.15% C 552 80 496 72A514F Type Steels – 0.06% C 724 105 690 100A514F Type Steels – 0.11% C 758 110 531 77

Table VI – Melting and Rolling of Production Heat R8660

1. Chemical Composition - 150t (165 ton) heat, bottom poured ingots

C Mn P S Si Ni Cu Cr Mo V Cb AlAim 0.060 1.00 LAP LAP 0.25 0.75 1.00 0.50 0.50 0.060 0.020 0.030Ladle 0.060 0.99 0.005 0.002 0.27 0.75 0.98 0.51 0.50 0.059 0.020 0.035Ing. 3* 0.057 1.00 0.005 0.003 0.27 0.74 1.00 0.51 0.49 0.059 0.022 0.033Ing. 3* 0.056 1.00 0.006 0.003 0.27 0.75 1.00 0.51 0.49 0.059 0.022 0.032Ing. 6* 0.059 0.99 0.005 0.003 0.27 0.73 1.00 0.52 0.48 0.058 0.022 0.032

* 25mm (1”) and 51mm (2”) plate from Ingot 3 and 38mm (1-1/2”) plate from Ingot 6 were analyzedThe steel in the ladle was vacuum degassed and calcium treated (0.0012%)

2. Product Production

Facility *HeatTreatment Product Sizes (mm) Product Sizes (in.) # of Pcs.

A HRL IAC & Aged Various Plate 4B BH IAC Q&T 25 mm x 2.4 m x 16.8 m

51 mm x 2.4 m x 12.2 m1” x 96” x 660”2” x 96” x 480” Plate

22

C Gary CR, Q&T 25 mm x 2.4 m x 6.1 m51 mm x 2.4 m x 6.1 m

1” x 96” x 240”2” x 96” x 240” Plate

11

D CV/CN Q&T 6.4 mm x 2.0 m x 15.2 m9.5 mm x 2.4 m x 15.2 m19 mm x 2.1m x 11.0 m19 mm x 2.1 m x 6.4 m38 mm x 2.1 m x 15.2 m64 mm x 2.0 m x 5.1 m

1/4” x 80” x 600” 3/8” x 96” x 600”3/4” x 81” x 433”3/4” x 81” x 252”1-1/2” x 84” x 600”2-1/2” x 80” x 200”

Plate 541111

E Fairfield Q&T 251 mm dia. x 7.62 mm x14.3 m

9-7/8” dia. x 0.30” thick x 564” **

SeamlessTube

6

* Bethlehem Steel (HRL – Homer Research, BH – Burns Harbor, CV/CN – Coatesville or Conshohocken) U.S. Steel (Gary Works, Fairfield Works)

Table VII – Mechanical Properties of Production Heat Quenched and Tempered Plates and Tubes

Plate Thick.(mm)

PlateThick. (in.)

Heat Treatment*Temper/Aging

Yield Str.MPa

Yield Str.ksi

TensileMPa

Tensileksi

Charpy V-NotchTough. J@-34oC

CharpyV-NotchTough (ft-lb.)@–30F

6.4 1/4” Mill 621 C, (1150F) 827 120 862 125 100 (1) 74 (1)9.5 3/8” Mill 621 C, (1150F) 800 116 841 122 182 (2) 134 (2)9.5 3/8” Mill 593 C, (1100F) 772 112 827 120 202 (2) 149 (2)9.5 3/8” Lab 621 C, (1150F) 793 115 827 120 225 (2) 166 (2)9.5 3/8” Lab 649 C, (1200F) 738 107 772 112 233 (2) 172 (2)19 3/4” Mill 621 C, (1150F) 772 112 827 120 228 16819 3/4” Lab 621 C, (1150F) 731 106 786 114 197 14525 1” Mill 621 C, (1150F) 752 109 820 119 209 15425 1” Lab 566 C, (1050F) 786 114 869 126 168 12425 1” Lab 621 C, (1150F) 786 114 841 122 196 14225 1” Lab 677 C, (1250F) 710 103 752 109 263 19425 1” Lab 621 C, (1150F) 765 111 841 122 163 12038 1-1/2” Mill 621 C, (1150F) 703 102 793 115 199 14738 1-1/2” Mill 621 C, (1150F) 717 104 793 115 203 15051 2” Mill 593 C, (1100F) 710 103 793 115 172 12751 2” Lab 566C, (1050F) 690 100 800 116 152 11251 2” Lab 621 C, (1150F) 724 105 793 115 179 13251 2” Lab 677C, (1250F) 662 96 710 103 203 15051 2” Lab 593 C, (1100F) 703 102 786 114 136 10064 2-1/2” Mill 621 C, (1150F)

head703 102 800 116 165 122

64 2-1/2” Mill 621 C, (1150F) tail 696 101 800 116 160 118Tubes Tubes Mill 621 C, (1150F) 793 115 855 124 77 (3) 58 (3)

* All products austenitized at 899C (1650F) (1) 1/2 size; (2) 3/4 size; (3) 2/3 size converted where applicable

Table VIII – Composition and Mechanical Properties of Laboratory Heat with 1.25% Mn

Tensile Properties Hard. CVN Transition Temperatures CVN Energy

Processing Condition, Temperature Y.S.MPa

Y.S.

ksi

T.S.MPa

T.S.

ksi

Y.S.T.S. HRC

47 J oC

(35 ft. lb.) oF

50%FATT

oC oFJ@

-40oCFt.-lbs.@

-40oF

25 mm (1”) Thick Plate, WaterQuenched, Quarter-ThicknessA* WQ + Aged 566C, (1050F)A* WQ + Aged 621C, (1150F)A* WQ + Aged 677C, (1250F)

820814738

119118107

889862772

129125112

0.920.940.96

29.227.622.3

-84<-84<-84

-120<-120<-120

-15 5-60 -75-84 -120

136176237

100130175

25 mm (1”) Thick Plate, PolymerQuenched, Quarter-ThicknessA* PQ + Aged 566C, (1050F)A* PQ + Aged 621C, (1150F)A* PQ + Aged 677C, (1250F)

696710655

10110395

848814731

123118106

0.820.870.90

23.823.720.0

-79<-84<-84

-110<-120<-120

>-1 30-43 -45-51 -60

115156203

85115150

51 mm (2”) Thick Plate, WaterQuenched, Quarter ThicknessA* WQ + Aged 566C, (1050F)A* WQ + Aged 621C, (1150F)A* WQ + Aged 677C, (1250F)

690765627

10011191

814834703

118121102

0.830.920.89

24.524.018.0

-60-73-76

-75-100-105

21 704 40

-34 -30

119149197

88110145

C Mn P S Si Cu Ni Cr Mo V Cb AlProduction Heat 0.060 0.99 0.005 0.002 0.27 0.98 0.75 0.51 0.50 0.059 0.020 0.035Lab Melt 0.060 1.26 0.010 0.002 0.25 1.03 0.73 0.50 0.50 0.060 0.021 0.029Lab Plate 0.058 1.27 0.010 0.004 0.25 0.99 0.71 0.51 0.50 0.060 0.022 0.031

*A – austenitized at 899C, (1650F)

Table IX – Mechanical Properties of Interrupted-Accelerated Cooled and Control-Rolled Plates

Charpy V-NotchToughness

Heat TreatmentY.S.MPa

Y.S.ksi

T.S.MPa

T.S.ksi

J@ -400C

Ft-lbs.@-40 o F

25 mm (1”) Thick PlateMill IAC 798 C (1468 F) to 513 C (955 F)Age 566 C (1050 F)Age 621C (1150 F)Age 677C (1250F)

621676703690

9098

102100

731848834786

106123121114

149149190190

110110140140

51 mm (2”) Thick PlateMill IAC 877 C (1610 F) to 513 C (955 F)Age 566 C (1050 F)Age 621C (1150 F)Age 677C (1250F)

717696710669

10410110397

793869834758

115126121110

1364288

152

1003165

11225 mm (1”) Thick PlateControl RolledControl Rolled + Age 621 C (1150 F)Control Rolled + Norm. 899 C (1650 F)Control Rolled + Norm. + Age.

427607421558

62886181

690731696703

100106101102

12916961

203

9512545

15051 mm (2”) Thick PlateControl Rolled + Age 621 C (1150 F)Control Rolled + Norm. 899 C (1650 F)Control Rolled + Norm. + Age.

455600359496

66875272

703745648655

1021089495

68176

741

50130

530

IAC – Interrupted Accelerated Cooling

Figure 1 - Jominy Test Results for Steels 3, 5, 7, 9 - As-Quenched (1/16” = 1.6 mm) Figure 2 - Jominy Test Results for Steels A, B, E, F

Figure 3- Jominy Test Results for Steels A, B, E, F at 0.06% C - As-Quenched (1/16” = 1.6 mm) Figure 4 - Jominy Test Results for Steels A, B, E, F

at 0.04% C - As-Quenched (1/16” = 1.6 mm)

at 0.08% C - As-Quenched (1/16” = 1.6 mm)

Figure 6 - Jominy Test Results for Production Heat (1/16” = 1.6 mm)

Figure 7 - Energy Transition Curves for Lab Heat B6 and Production Heat Figure 8 - Implant Test Re

Figure 5 - Jominy Test Results for Laboratory Heat B6 (1/16” = 1.6 mm)

sults for Production Heat

Figure 9 - Jominy Test Microstructures of Production Heat - As-Quenched

Tensile Properties

90

100

110

120

130YS UTS

YS 690 (100) min.

UTS 760 (110) min.

.25 .375 .75 1.0 1.5 2.0 2.5

896

827

758

690

621

MPa ksi

6.3 9.5 19 25 38 51 64mmInches

Plate Thickness

Figure 10 - Summary of Tensile Properties for Production Plates of HPS-100W

CVN Energy @

0

50

100

150

200

.25 .375 .75 1.0

271

203

136

68

J Ft-lbs.

mmInches

6.3 9.5 19 25

Figure 11 - Summary of Charpy-V-Notch Impact

-34oC (-30oF)

1.5 2.0 2.5

47 J (35 ft. lb) min.

38 51 64 Plate Thickness

Results for Production Plates of HPS-100W