ITI-TRD PROGRESS REPORT TO MATERIALS LABORATORY3, 'WRIGHT AIR DEVELOPMENT CENTER DEPARTMENT OF THE AIR FORCE ON FOUR LOW-ALLOY STEELS FOR ROTOR DISKS OF GAS TURBINES IN JET ENGINES By A. Zonder Jo W. Freeman PROJECT NUMBER: 14903 AIR FORCE CONTRACT NUMBER: AF33(038)-13496 EXPENDITURE ORDER NUMBER: 605-227 SR-7 September 30, 1951

THIRD PROGRESS REPORT ON FOUR LOW-ALLOY STEELS FOR ROTOR DISKS OF GAS TURBINES IN JET ENGINES SUMMARY This report is the Third Progress Report on an investigation being carried out for the Materials Laboratory, Wright Air Development Center, Department of the Air Force. The time period covered is from 1 July 1951 to 30 September 1951. Air Force Contract Number: AF33(038)-13496 (Expenditure Order Number: 605-227 SR-7) authorizes the investigation. The investigation is to study the high-temperature properties of four lowalloy steels, 4340) 17-22A(S), H40, and C-422, in the form of forged J-33 jet engine disks. A concurrent investigation of the high-temperature properties of the products of isothermal transformation of each steel is being carried out utilizing bar stock. The results of the structural studies are to be correlated with the results to be obtained from the disks. The jet-engine disks were received from Canton Drop Forge and Manufacturing Company on 27 July 1951. Four of the disks (the oil-quenched and interruptedquenched disks of 4340 and 17-22A(S)) have been split and the center slabs cut out. Hard spots in the C-422 alloy disks were encountered. The slabs have'been magnafluxed and macroetched and found to be sound. Also, a hardness survey has been made on each center slab. The results obtained to date from creep-rupture tests in the investigation of the properties of the products of isothermal transformation are as follows:

2 Test Stress to Cause 1% Total Temp. Deformation in 1000 Hrs. Steel Heat Treatment BHN (eF) (psi) 3h40 N.1750~F+ To 1 Hr. at 1100~F 292/311 1100 4,250 N.1750OF+ To 1 Hro at 1100~F 301/303 1000 13,300 17-22A(S) N.1750~F+ T. 10 Hrs at 1200~F 291/317 1100 19,000 H-40 N.1950~F+ To 18 Hrs at 1200~F 312/320 1100 27,800 C-422 N1ol900~F+ T. 24 Hrs at 1200~F 299/306 1100 28,700 For 4340O steel, the upper-bainite structure was the only structure which showed a significantly higher creep strength than the normalized structure. This was true at both 1000~ and 1100~ Fo The oil-quenched, upper-pearlite, lowerpear-lite, and lower-bainite structures possessed creep strengths which were either approximately equal to or lower than that of the normalized structure. For 17-22A(S) steel, the oil-quenched, upper-pearlite, lower-pearlite, and lower-bainite structures all had lower creep strengths than the normalized structure. To date, the upper-bainite structure has not been tested. For H-40 steel, results to date show the normalized structure to be stronger than the oil quenched structure. For C-422 steel, results to date show the normalized structure and oilquenched structure to have similar creep strengthso Additional tempering data for 17-22A(S), H-40, and C-422 have been obtained. The time-temperature-transformation curve for H-40 has been outlined, and work is in progress on the time-temperature-transformation curve for C-422. INTRODUCTION This report covers the progress made between 1 July 1951 and 30 September 1951 on an investigation of the high-temperature properties of four ferritic alloys in the form of forged rotor disks for gas turbines in jet engines.

3 The purpose of this investigation is twofold, namely: A. To determine the effect of heat treatment upon the high-temperature properties of four low-alloy steels in the form of contour forged J-33 jet engine disks. The steels to be investigated are 4340, 17-22A(S), H-40, and C-h2 2 As a further clarification of the effect of heat treatment upon the high-temperature properties of these steels, a concurrent study of the creep-rupture properties of the products of isothermal transformation of each of these steels is being carried out, utilizing bar stock. B. To establish design curves out to 1000 hours, for each steel, showing stress vs. time for (1) rupture, (2) start of third-stage creep, and (3) total deformations of lo0, 0.5, 0.2, and 0.1ol percent. These design curves are to be established at 1100~ F and two other temperatures for the heat treatment which gives the best practical properties. PROCEDURE AND PROPOSED TESTING CONDITIONS The procedure and proposed testing conditions to be used in this investigation were outlined on pages 3, and 6 - 9 of the first Progress Report. A plan for sectioning the disks and a detailed outline of the proposed testing to be carried out was submitted by the University to Wright Field shortly after the disks were received. Wright Field approved these proposals as they are presented belowo The plan for sectioning the disks is shown in figures 1 and 2. The detailed outline of the testing to be carried out on the disks is as follows: A. The stub shaft and boss will be cut off of each disk, B. A slab (1, 2, alnd 3) will be cut from the center of each disk and used for: 1. A Brinell hardness surveys

4 2. Macroetching and magnaflux examination. 3. Room temperature tensile tests on specimens 1W, 1X, 2W, 2X, 2Y, and 2Zo C. Conduct sufficient tests on specimens 4W, hX, 4Y, 4z, 6W, 6X, 6Y, and 6Z from each disk to establish the stress-rupture time curve and the stress for 1% total deformation in 1000 hours at 1100~ F. Do Send quarter section to WO Brown, Lewis Flight Propulsion Laboratory of the NACA. E. Review data from (B) and (C) and recommend the heat treated disk of the most practical interest for each alloy. On agreement as to the muou practical heat treatment, the disk will be used for complete testing, and the following additional tests will be made: 1. Short-time tensile tests at 1100~ F and two other temperatures to be agreed upon using specimens 1Y, lZ, 3W, 3X, 3Y, 3Z, 14X, 14Y, and 14Z. 2. Creep and rupture tests using specimens from 7, 8, 9, 10, 11 12, and 13 as necessary to determine the design curves for the material at the rim. Checks will be made to see if there is a difference between surface and center specimens. 3. Single check creep-rupture tests on tangential specimens using stresses selected to produce fracture in 1000 hours at each test temperature. 4o All specimens used will be 0.505-inch diameter with a 2-inch gage length. Check rupture tests will be run on 0,250-inch diameter specimens taken radially and as near the rim as possible in one case and the center in the other to determine the variation in properties.

5 TEST MATERIALS The chemical analyses reported for the disks are as follows: C Mn Si P S Cr Ni Va Mo W Cu Steel (%) (%) (%) (%) (%) (%) (%) (%) (%) (%) (%) Heat No. 14340 040 0.76 0.29 0.o01 0.015 0.74 lil - 0.50 - - 656601 17-22A(S) 0.30 0.57 0.60 OoO1.0 0.019 1.22 0o23 0o24 0.49 - 0,13 38516 H-4 0 0o29 0.48 0.26 0.012 0o018 3,05 0.49 0.85 0o49 0.55 K-2509 3-422 0,23 0,81 0.16 Oo011 0o012 13,9 0.65 0,25 1.03 0.84 - W-3561 The Canton Drop Forge and Manufacturing Company reported that the disks were given the following heat treatments with resulting surface hardness values as shown: Surface Brinell Hardness Rim Hub Treatment 4340 STEEL 285 285 #1 First treatment ^ No 1750'F + 2 Hrs at 1200~F Second treatment No 1750oF 255 255 #2 As forged 302 285 #3 First treatment OoQo from 1750~F + 8 Hrs at 1200~F Second treatment - OoQo from 1550~F + tempered at 1050'F 302 293 #4 Water quench from 1750~F until black, then withdrawn until glow returned. This was repeated until the glow did not return upon withdrawal, Transferred to furnace at 700~F for 8 Hrs + 2 Hrs at 1200"F NOTE: Second treatments were used because the first treatments produced hardness values lower than a hardness specification of 280 to 320 Brinell. 17-22A(S) STEEL 302 285 #1 No 1750~F + 2 Hrs at 1200~F 293 277 #2 As forged 302 302 #3 OoQ. from 1750~F + 8 Hrs at 1200~F 341 331 #4 First treatment - interrupted quench from 1750~F (same treatment as 4340, #4) Second treatment - 2 Hrs at 1200~Fo This second treatment was required because the initial hardness of 399 Brinell was too high.

6 Surface Brinell Hardness Rim -Hub Treatment H-4O STEEL 341 341 #1 First treatment - No 1950~F + 2 Hrs at 1200~F Second treatment - Retempered at 1200~F 363 363 #2 As forged 341 352 #3 First treatment -C.Qo from 1950F + 8 Hrs at 1200~F Second treatment -Retempered at 1200~F 341 331 #4 First treatment - Interrupted quench from 1950~F (same treatment as 4340, #4) Second treatment - Retempered at 1200~F NOTE: The additional tempering of the second treatments was required because the first treatments resulted in too high hardness values (#1 - 429/444 BHN, #3 - 415 BHN, #h - 363/389 BHN)o C-422 STEEL 321 331 #1 No 1900~F + 2 Hrs at 1200~F 321 388 #2 As forged 285 321 #3 As forged 285 285 #h 0. Qe from 1900~F + 8 Hrs at 1200~F Disks numbered 1, 3, and 4 of each steel were shipped to the University. RESULTS The results obtained to date are presented separately for each steel under (1) disk investigation, and (2) investigation of the properties of the products of isothermal transformation. lo Disk Investigation 4340 STEEL The center slab has been cut from the oil-quenched disk and the interruptedquenched disk. Both slabs were magnafluxed and macroetched and found to be soundo Brinell hardness surveys have been taken on both slabs, and these are shown in figures 3 and 4. The oil-quenched disk had a Brinell hardness range of 260 to

7 320, The principal hardness ranges were 260 to 280 near the center and 280 to 310 towards the edges. The interrupted-quenched disk had a Brinell hardness range of 272 to 342, although most of the hardness values were from 280 to 300, 17-22A(S) STEEL The center slab has been cut from the oil-quenched disk and the interruptedquenched disk, Both slabs were magnafluxed and macroetched and found to be sound. Brinell hardness surveys were taken on both slabs, and these are shown in figures 5 and 60 The oil-quenched disk had a Brinell hardness range of 285 to 343, although most of the hardness values were between 300 to 325. The interruptedquenched disk had a Brinell hardness range of 302 to 350. H-40 AND C-422 STEELS To date, no work has been done on these disks, except that hard spots in the interior of the C-422 disks stopped the sectioning for preparation of samples9 2, Investigation of the Properties of the Products of Isothermal Transformation 4340 STEEL The first criterion used in evaluating the high temperature properties of the different microstructures for each steel was the stress to cause one percent total deformation in 1000 hours at 1100~Fo Because of the poor strength of h340 at 1100~F, testing at 1000~F was initiated. The results obtained to date are as follows: Test Stress to Cause 1% Total Tempo Deformation in 1000 Hours Structure BHN (~F) (psi) Norm. + To 1 Hr at 1100OF 292/311 1100 4,250 Normo + To 1 Hr at 1100~F 301/303 1000 13,300 O Q. + T. 10 Hrs at 100'F1100 309 1100 less than 250

8 Structure OoQ* + To 10 Hrs at 11OO00F Lower Pearlite Lower Pearlite Upper Bainite Upper Bainite Lower Bainite + To 1-1/4 Hrs; at 1100~ F Lower Bainite + To 1-1/4 Hrs at 1100~ F Upper Pearlite BHN 306 275 270 319 322 301 294 219 Test Temp. (*F) 1000 1100 1000 1100 1000 1100 1000 1000 Stress to Cause 1% Total Deformation in 1000 Hours (psi) less than 13,300 it i 4,250 " <~ 13,300 greater than 4,250 O 13,300 less than 4,250 about 13,300 about 13,300 Because of the low strengths of the various structures of 4340, creep testing was limited to only one test for each structure other than the normalized structure and the upper bainitic structure. The upper bainitic structure was the only structure showing a significantly higher creep strength as compared to the normalized structure. The upper pearlitic structure was not tested at 1100~ F because of its low hardness. Table I shows the creep data obtained to date from creep tests run on various microstructures of 4340. Figure 7 shows a plot of stress vso time for specified total deformations for the normalized structure tempered to an approximate hardness of 300 Brinell and creep tested at 1000~ F. 17-22A(S) STEEL The hardness values obtained for various heat treatments are as followsTreatment Brinell Hardness As normalized 1 hour at 1750~F 361 As oil quenched from 1750~F 52h

9 Treatment Brinell Hardness Austenitize 1 hour at 1750~F + 1-1/2 hours at 1350~F 315 (Upper Pearlite) Austenitize 1 hour at 1750'F + 10 hours at 1150*F 375 (Lower Pearlite) Austenitize 1 hour at 1750~F + 2 hours at 900~F 466 (Upper Bainite) Austenitize 1 hour at 1750~F + 5 minutes at 700~F 365 (Lower Bainite) The hardness values obtained for the bainitic structures are being investigated in order to determine why the upper bainite is harder than the lower bainite o The tempering behaviors of the normalized and oil-quenched structures have been reported previouslyo Figures 8 to 11 show the tempering behaviors of the lower-bainite, upper-pearlite, lower-pearlite, and upper-bainite structures. The results obtained to date from creep-rupture tests at 1100~F are as follows: Stress to Cause 1% Total Deformation in 1000 Hours Structure BHN (psi) Norm. + To 10 Hrs at 1200~F 291/317 19,000 OoQo + To 1 Hr at 1300~F 302/306 15,000 Upper Pearlite 309/313 less than 19,000 Lower Pearlite + T. 12 Hrs at 1200~F 291/313 t M 19,000 Lower Bainite + To 12 Hrs at 1200~F 302/303 " V 19,000 The creep data obtained to date from tests run on various microstructures of 17-22A(S) are included in table IIo Figure 12 shows a plot of stress vso time for specified total deformations for the normalized structure tempered to an approximate hardness of 300 Brinell and creep tested at 1100~Fo

10 H-40 STEEL The time-temperature-transformation curve for H-h0 has been outlined and is shown in figure 13. Results obtained in determining this curve indicate that the only microstructures which can be developed by isothermal treatment are upper and lower bainiteo Holding for time periods out to 24 hours at temperatures above 900*F results in the appearance of a very small amount of a dark-etching material in the grain boundaries of the matrix material. This dark-etching material could not be identified, even after examining it at a magnification of 2000 diameters. Other than this, there were no signs of any transformation of the austeniteo The hardness values obtained for various heat treatments are as follows: Treatment Brinell Hardness Normalize 1 hour at 1950~F 435 Oil quench from 1950OF 522 Austenitize 1 hour at 1950F + 10 hours at 750'F 481 (Upper Bainite) Austenitize 1 hour at 1950~F + 1/2 hour at 600~F 417 (Lower Bainite) The hardness values obtained for the bainitic structures are being investigated in order to determine why the upper bainite is harder than the lower bainiteo The tempering behaviors of the normalized and oil-quenched structures have been reported previously. Figures 14 and 15 show the tempering behavior of the two bainite structures. The following results have been obtained from creep tests run at 1100~F: Stress to Cause 1 Percent Total Deformation in 1000 Hours Structure BHN (psi) Norm. + To 18 hours at 1200~F 312/320 27,800 OoQ. + To 12 hours at 1200~F 321/323 23..300 Creep data obtained to date are included in table IIIo Figure 16 shows a plot of stress vso time for specified total deformations

11 for the normalized structure, tempered to a hardness of approximately 300 Brinello C-422 STEEL The hardness values obtained after normalizing and oil quenching C422 Steel were as follows: Treatment Brinell Hardness Normalize 1 hour at 1900~F 484 Oil Quench from 1900~F 494 The tempering behaviors of these structures are shown in figures 17 and 18. The stress to cause one percent total deformation in 1000 hours at 1100'F is 28,700 psi for the normalized structure tempered to a Brinell hardness of 299/306. Creep data obtained to date are included in table IV, This data indicates that the oil quenched and normalized structures, when tempered to a hardness of about 300 Brinell, have similar creep properties. Figure 19 is a plot of stress vs. time for specified total deformation for the normalized structure tempered to a Brinell hardness of 300o Work is now in progress on the determination of the time-temperaturetransformation curve for C-422. FUTURE WORK Creep-rupture testing, for determination of the heat-treated disk with the most practical properties, will be initiated as soon as test units are availableo The program on the bar stock is to be continued to define the relationship between microstructure and creep-rupture propertieso

TABLE I, OF 4340 3TEEL AT 1000~ F CREEP PROPERTIES AND 11 00 F Heat Treatment N*1750*F+T, 1 Hr, at 1100~F ft n t T ff nnT~ y~n BHN 292 511 299 509 275 519 Test Temp. (~OF 1100, 1100 1100 1100 1100 1100 0.Q* + T* 10 Hrs, at 1100~F Aust. 1750~F + 111 Hrs. at 1050~F - (Lower Pearlite) Aust. 1750~F + 28 Hirs. at 350~F - (Upper Bainite) A4ust., 1750~1F + 1li Hrs. at 650~1F +T. 12 Hrs. at 110OOF (Lower Bainite) N.1750~F + T. 1 Hr. at 110OOF OQ* + T. 10 Hrs. at 1100~F Aust. 1750~F + 10 Hrs. at 1240~F (Upper Peal..rlite) Aust. 1750~F + 111 Hrs. at 1050~F (Lower Pearlite) Aust. 1750~F + 28 Hrs. at 850~F (Upper Bainite) Aust. 1750~F -+ 1-1 Hrs, ~-at 650~1F + T. I — -Hrs. at 1100~F (Lower "Bainite) *Completed Creep Test. bExtrap~olated Value. Stress (PS i) 2,000 4,9000 6, 000 4,500 4,250 4,500 4,500 12 9,000 15,f000 13,000 13,000 15,000 TLmime in Progress (rs) 1056* 1056* 1050 * 1050 * 470,1012* 1012* 1000*:11534* 1026* 1105* Minimum Creep Rate 0.22 0.52 2.4 3.16 0.-a48 1.72 0.57 1.45 1.15 0.57 0.2 0.57 1.04 1.14 11.57 0.*28 0.76 0.51 0.63 0.54 0.355 0.27 0.051 1.57 1.71 0.47 1.12 0.59 00.9 0.81 0.48 0.5 8 0.78 3.07,2.96 0.72 2.0 0.58 1.085 1.74 0.77 86 18 8 5 9 17 50V^2 9 5 2 6,22, 2 1 78 484 101 1104 90 552 1416 286 2158 217 15851b 456z C 2150 b 556 628 1400 b Percent Total Defornation at Indicated Time Periods 300. Hrs 500 Hrs,1000 Hrs.Time 0.1^ in Hours for Specified Total Deformaitions 0.2^ 0.5^.0 301 1100 19 156 301 303 306 219 1000 1QOO 1000 1000 12 2 3 6 114 25 27 63 802 19 6 248 528 270 1000 350 2.0 2 6 46 141 322 1000 15,000 1 C1274 4 * 0.24 0.27 0.33 0.47 5 294 1000 13, 0 0 810 0.5 0.64 2 32 500 - - --- - — - -I --- I I — ---. -` — — -.1 — .. -— --- — - --- -— ` --- --- ---- - -- -- -- --- I

TABLE II GRE'. —4P P-ROP"ER"TIE` OF 17-22A(1SN STE-7L AT 1100 Heat Treatment N.1750Q~F + T. 12. Hrs. at 1200~F 0.q. + T. 1 Hr. at 130OOF?T ~ ~? ~tT( r~t A11ust. 1750~F + 10 Hrs. at 1150~F +T 2Hs (Upper00 (eaLower )e,!-ri IT it n ft Vt Irv ft r Aust. 170F+ 5 M,,in. at 700~F + T. 12 Hrs. at 121001F (Lower Bainite) ti I *T *It tf ff*~~ BffuHN 502 291 517 5311 506 502 509 515 515 291 502 Stress, -(PS1 ) 10, 000 14, 000 17,000 20, 000 20,p000 15, 000 19,p000 15,9000 19,000 15, 000 19,000o 14,000 Timde'- In Pro gr-e s s..-(HITS) 105 6* 1150* 105A6* 140 14~0 1 0 40, * Minimum. Creep Rate [%/,z10QO Hrs 0.16 0.5 0.4.5 0.86 1.66 0.85 2.04 Percent Total1 Deformation at Indicated Time Periods 500 H-rs 500 Hrs. 10,OO Hrs 0.26 0.51 Q.38 0.22 0.28 0.44 0.25 0.54 0.58 0.43 0-6 7 0.84 1.49 0.5%9 0.52 0. 99 0.o88 2.04 Time in Hours for -S')pecifi'ed Total Deformations 0.1 0.2LI 0.5-5 1.20,I 48 230 1204b 14 177 857 10-70b 146 375 656 115 139 545 % 2 48 470 1006 117 159 35-6 14 1 12C9 10 54 14 79 194 24 A 101 C 268) 1.46 1.09 1.41 I C4i 820 0.45 22 67 621 Com —leted Creep Test. bExtrapolated Value. AReached 0.1 - Deformation on Loading. — ~ll~llnnrrWsrrYIIILI~rrr~*~111315~C ~ —...-.

TABLE II I CREEP PRO-PERTIESE. OF H-40 STEEL AT 1100~F Heat TreAtlTent N. -1950 ~F + T. 18 Hrs. at 12000F nT? *I T? B-HN 316 520 512 521 525 Stress (Psi4) 27,50 0 31,1000 34, 000 50,~000 24,000 Tpim~e i n Pro gres s -.-(Hrs)~ 1132* 720O~ 127 2' 8 6 5 880 -Minimaum Creep Rate {%/1000 Hrs) 0.64 1.05 1.48 2.57 0.85 Percent Tota~l Deformjtion art Indicated Time Pe iods 5300 Hrs 500 Hrs 3. -I-000 Hrs 0.42 0.55 0.94 0.55 0.765 Time in Hours for Sp7,eci~fied Total Deformations 0.1% 0.2% ' 0.5 -.'IC 3 7 429 105 —4 A 7 274 677 A 5 161 A. 2 94 279 A 25 500~ 862 it t? ftt 0.%, + T. 12 Hrs. at 1200~F *t T? r T~ It 1.06 0.,,5 1.85 0.o6 6 TABLE IV CREEP PROPERTIES OF C-422 STEEL AT 1100~OcF N, 1900~F + T. 24 Hrs. at 1200~F Tl Tt n n lo,0 6 299 305 307 30,000 355,000 59,000 50,000 19 20 8190 566~ 570 0.88 2.24 6.28 0.67 1.35 5.o0 0.64 0.82 1.96 A A A A 35 112 D 16 D 9 1 155 690 157 46 ft r) t~ 0.Q, + T* 4 Hrs. at 1200~F *Completed Creep Test.~Broke at This Time. Iece.^Dfrmto nLaig ARearched 0.21o Deformation on Loading. --- -- -.1-lr — -. --- —. — ---- --- --

Figure 1. - Proposed Method for Sectioning Disks to be Investigated under Project M903.

Figure 2. - Cross-Section View of Center of Disk.

....* * * o * * * O0 o. o oo -- - ---- D 0 (D CD 0 D)0 (D () 0 (D0 ( < D (D L__-_ — D _____ 0 0D **0 o o o o 0 0000 00 o.00 0 = 260-220 Brinel- Hairdness * = 281i-300 It = 301-320 t Heat Tr.eat.on..: First trea'tmont - 0.... from 1i?0F; + Hrs. at 1200~F. Second treatiJ -.. fron 15jO t. Lem ered at 105v Fo iI i I I I I I Fiure 3. - Brirel hardne.ss su urvve on cen er section (1-2-3) o' isk #3 of Llio steel.

e e 0 0 * 0 0 * 0 0 * 0 o 0 0 0 0 0 0 0 0 0 0 e *O 0 0 00 0 0 0 0 00 0 0 C 0 0 0 0 0 i I I i I I i I i / 0 0 0 o 0 0 0 0 0 0 \ o 0 \ i I 0 0 0 (O 0 O00 0 - 00' r- 0 0 0 0 0 O0., 0 0 0 0 0 0 0 00 0 o o o ~ 0 0 * 0 e 0 e e * O 00 0 0 0C ) Ti 4)3 4J 4-3 143 0 0 0 0 0 0 0 0 0 0 0 0 0 4,3 e-.4 -:7 0 0 C: 0 00 0 / 0 ( 0 *0 * e) rt' C.

e e * e o 0 0 0 0 0 * e * *O o 0 *.T 0 0 - 0 0 0 0 * 0 0e 0 0 G e e e 0o 0o 0o 0o 0 o 0 0 0 0 0 0 0 e e e ~ e \ ~ \ 6 0 e ' e i * I I 0 01.I 0 0 0 0 0 e 0 0 0 0 0 0 0 e e 0 e 0 e 0 0 0 0 0 0 0 0 0 0 0 0 0 0 0 0 0 0 0 0 0 0 0 0 0 0 e e r-A (A) INJ 0. 0 o I 0 0 (\J cU x) Q 0 F '-4 424 N N "-4 0 '.4 (4 L 1 42D 4..) "I I -, 1 -il t,I,, I C7-1

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20.. 20oc....i -6,COOO...? hI.... O. '-...........................10 iure..vs. Time or Indic..ted Tota........ at ~ * + 1 Hour - 1100' F........... O i':: J — '.: 7EsI.t1 e d't 1surat........................ ^ i:':;1:.-'~ ~ ~~. *: -..;:.:.::: ^. '..:..........:.r ~ ' ' +.... Qm........t'.:.... ~: Q Q...-...;..::: -.:.'..:Z.:...........;'.....; ' i 1.. - -..., -. -......................,..., i ".......................................... i.:.~......................, ";............ ' ':1 "o — _ - -- -- 100... 1000 Time, Hours L Deformations at 1000., F for 4340 Steel Normal sed 'inell Hardness 301 to 303., Hour I -

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