The University of Michigan * Office of Research Administration Ann Arbor, Michigan BORON AND TITANIUM ADDITIONS TO "17-22-A"V STEEL by R, Jackowski J, W. Fre-erma Project 04603-63-T February 5, 1965 Report No, 248 The Timken Roller Bearing Company Steel and Tube Division Canton, Ohio

BORON AND TITANIUM ADDITIONS TO "17-22-A"V STEEL A previous investigation (Report 243) had suggested that titanium and boron when added separately to "17-22-A1V steel could improve creep-rupture properties at temperatures of up to 1100~F to a remarkable extent. In the investigation being reported both elements were added simultaneously to heats with carbon contents ranging from 0. 10 to 0. 26 percent. The manganese contents were in the range of 0, 52 to 0. 65 percent. "A" induction heats and "0" arc furnace heats were made, rolled to barstock or forged to discs, heat treated and machined to specimens by The Timken Roller Bearing Company. A range of heat treatments were used. Evaluations were primarily based on rupture tests at 1100~F, Three materials were tested at 1200F as well. CONCLUSIONS Rupture test properties at 1100~F were considerably improved over those of "17-22-A"V steel by the addition of boron and titanium. Both strength and ductility were improved. Two of three arc furnace heats gave test results as either barstock or forgings which agreed well with the properties of induction heats. They were, in fact, considerably bette r One of the arc furnace heats, however, had comparatively poor properties as barstock. Forgings from the heat compared quite well with the other heats. Evidently unidentified factors in chemical composition or prior history of working had a considerable effect on properties, Limited data indicated that the nitrogen content of the arc heat with the lowest properties was similar to that of the induction heats with the high comparative properties. The properties of the arc furnace heats were as good as or better than the properties of the induction heats, unlike the results obtained 1

from heats with only boron added (Report 243). This suggested that the titanium protected the boron in the arc furnace heats. Isothermal transformation did not improve properties of the arc heat with the lower properties, Oil quenching forgings improved ductility but not strength for the one heat investigated. In all cases strength increased and ductility decreased with increasing temperature of heat treatment. This seemed to be associated with solution of TiC particles in the microstructureso The properties of radial and tangential specimens were not excessively different, Very low carbon (0. 10 percent) resulted in soft material with low rupture strength for 100 hours. Only single survey tests did not indicate whether or not properties would compare better at prolonged time periods. The heat also had high boron and titanium. TEST MATERIAL Tensile specimens 0, 505 inches in diameter were supplied by The Timken Roller Bearing Company from six heats of modified "17-22-A"V steel having the following reported chemical compositions: Heat No. C Mn P S Si Cr Ni Mo V B Ti N (%) (%) (%) (%) (%) (%) (%) (%) (%) (%) (%) (%) A134.20 57.015.033.79 1.84,24.49.77.0036 o33.012 A135.25.52.015.031.79 1.70.16.51.77.0092.43.010 A73. 10 54.017,026.75 1 30 -.53.28.042.67 02392.26.61 018.017. 58 1.49.29.48.71.0028,35.011 02629.21.63.010.012.64 1.49.33.53.70.0026.32 02630.24.65,012.014 63 1 47.27,49.71.0022.37 The "A" heats were 300 pound induction heats and the "0" heats 2, 000 pound arc furnace heats, The specimens supplied from the induction heats were machined from heat treated 1 inch barstock, Specimens from the electric arc furnace heats were machined from both 1 inch diameter heat treated barstock and heat treated upset pancake forgings* 2

Parts of each of the arc furnace heats were forged at 21000F to 7 inch square billets. The billet from Heat 02392 was then upset forged into 15 inch diameter by four inch thick pancakes and Heats 02629 and 02630 to 15/2 inch diameter by three inch thick pancakes. The pancake forgings were sectioned and sampled as indicated in Figure 1 for Heat 02392 and in Figure 2 for Heats 02629 and 02630. The heat treatments used together with the reported hardness values are presented in Table l. The room temperature mechanical properties as reported by The Timken Roller Bearing Company are presented in Table 2. For rupture tests where the stress exceeded 40, 000 psi the diameter of the gage section of the specimens were reduced to bring the load requirements within the capacity of the rupture units. RESULTS AND DISCUSSION The preliminary portions of this investigation were conducted on specimens made from barstock from induction furnace heats. The composition of the most promising heats was then duplicated in larger arc melted "O" furnace heats. Both barstock and forgings were made from these latter heats, The stress-rupture data obtained from the differest materials in their various conditions are shown in Table 3, The stress-rupture time curves derived from these data are presented in Figures 3, 4 and 5. The indicated rupture strengths for 100 and 1000 hours at 1100~F for the heats are shown in Table 4 together with the indicated ductilities in these time periods. Induction Furnace Heats Examination of the data from induction furnace heats (Figure 3 and Table 4) indicated the following effects from adding boron plus titanium to "17-22-A"V steel on rupture properties at 11000F: 3

1. The heats with carbon contents of 0. 20 and 0. 25 (A134 and A135) had higher indicated strengths than "17-22-A"V steel. 2. Heat A73 with 0. 10 percent carbon was much weaker. The carbon was too low to develop the hardness associated with the high strengths of Heats A134 and A135 or regular "17-22-A"V steel. Only single tests were conducted so that there was no way of estimating what the comparative long time strengths might be, 3. Increasing the temperature of heat treatment raised rupture strength but reduced ductility. The ductility was similar to "17-22-A"V steel for Heats A134 and A135 when heat treated at 1950'F, with substantially high rupture strengths. When heat treated at 18000F the ductility was higher but the strengths were only on the high side of the range for "17-22-A"V steel. 4. Heat A73 had substantially higher rupture strength when the temperature of heat treatment was raised to 2100~F from 1950~F. Ductility was reduced but was still high compared to the harder materials from the higher carbon heats. 5. Boron plus titanium did not raise the rupture strength in comparison with Heat A127 made only with boron. Ductility may have been higher. Comparative data (Report 243) for adding only titanium to'17-22-Al"V steel are not available. When added to "17-22-A"S steel it increased strength and ductility to a remarkable extent. To obtain the high strength it was, however, necessary to heat treat at 19500-20500F. Evidently when titanium was added it was necessary to use higher temperatures of heat treatment to dissolve TiC. The solution of TiC was required before the necessary hardness could be obtained. The solution of TiC apparently also led to increased rupture strengths as well (see Report 243). The increased strength from the high temperature heat treatments of the heats with boron and titanium presumably was therefore due to the solution of TiC, The microstructure of the boron plus titanium heats (Plates 1, 2 and 3) indicated that titanium prevented coarsening of the grain size and bain4

itic structure resulting from heat treatment at 1950~F. The microstructure of the 0, 10 percent carbon Heat A73 appeared to be made up of ferrite plus titanium carbonitrides when heat treated at 19500F. Raising the temperature of heat treatment to 2100~F induced some bainite toform for the test conditions evaluated, Both the low carbon content and the presence of titanium apparently restricted hardening and thereby restricted strength. Maintaining the V/C ratio of the 0. 10 percent carbon heat (A73) at 2, 8 did not cause high strengths to be devloped at 100 hours. A proper ratio, however, could still be very effective for prolonged service although tests were not run to determine if this did occur. The boron content was also comparatively very high at 0. 042 percent. The titanium level was also high at 0.67 percent. Arc Furnace Heats Data were obtained from rupture tests at 1100~F on samples from three heats (Heats 02392, 02629 and 02630). All three heats had very similar chemical compositions (page 2). The results for tests at 1100~F (Figures 4 and 5 and Table 4) are summarized in Figure 6. Pertinent points in the data are: 1. The rupture strengths of the arc furnace heats were high in comparison to "17-22-A"V steel. The differential increased markedly with the temperature of heat treatment of the boron plus titanium heats. 2, The barstock from the arc furnace heats had substantially higher strengths than the barstock from the induction furnace heats (Figure 6), except for Heat 02392. The strengths were similar to those for the boron-containing induction Heat A127. The heats did not undergo the reduction in strength observed for arc furnace heats with only boron added (Report 243). 3, The forgings had strengths similar to the barstock from the same heat for 100 hours. At 1000 hours the forgings tended to be lower in strength. 5

4. Isothermal transformation of barstock did not seem effective in raising the strength of Heat 02392 barstock. The same was true for oil quenching forgings and it may have reduced strength. Both may have improved ductility, 5. The forgings exhibited better ductility than the barstock in Heat 02392. This was also true for the other two heats. 6. In all cases raising the temperature of heat treatment raised the rupture strength and reduced the elongation (Figure 6 and Table 4). 7. In general radial specimens from the forgings had higher strength than those taken tangentially. 8, Microstructures (Plates 4 through 11): (a) All of the Heat 02392 barstock tended to have a distinct " grain" structure. This was exaggerated in the isothermally transformed barstock (Plates 4 and 5). Presumably this type of structure was responsible for the comparatively low strength and especially ductility. Plate 5, showing the microstructure of the isothermally transformed materials, emphasizes the wide differences in structure with similar hardness values which can exist in the alloy. (b) The forgings from Heat 02392 had the bainitic structures (Plates 6 and 7) associated with high strength in this alloy. The forging normalized from 1850~F had a very coarse grain structure (Plate 7). This presumably caused low ductility (c) The oil quenched forgings had a tempered bainitic type structure (Plate 8) which has been associated with good strength and ductility in this alloy. The ductility was good. Rupture strengths were, however, somewhat low, suggesting that tempered martensite was present in the microstructure. (d) Heats 02629 and 02630 had the tempered bainitic structures (Plates 9, 10 and 11) associated with high strength and ductility in the alloy. The exception was the barstock from Heat 02630 normalized from 1850 F (Plate 10). It had the distinct "grain structure" associated with low ductility in the alloy. The forgings had finer tempered bainitic structures than the barstock. 6

9. The reason for the comparatively low properties of Heat 02392 in relation to the other two arc furnace heats is not known. The limited information available suggests that there exists a considerable difference in transformation characteristics among the heats. The reason for this difference is uncertain. The data also suggest that variables in the conditions of working were involved since barstock was so much poorer than forgings for Heat 02392, Heat 02392 had a nitrogen content similar to that of the induction heats (see page 2), This suggests that some other factor was involved, These data furthermore do not indicate the reasons why the properties of the arc heats compared so favorably with those of the induction heats while they were so inferior where only boron was added (see Report 243), Possibly the titanium "protected" the boron in some way. RUPTURE TESTS AT 1200~F Very limited testing at 12000F indicates that boron plus titanium can increase strength at 1200~F (Table 4). Specimens from induction Heat A134 had substantially higher strength than "17-22-A"V steel. The specimens from barstock from arc furnace Heat 02392 were no stronger than "17-22-A"V steel. This barstock, however, seemed unduly weak at 1100~F in comparison to other arc furnace heats or to forgings from the same heat. It is therefore possible that boron plus titanium can be beneficial. The data suggest that boron plus titanium also improve ductility at longer times in the rupture tests. In accordance with most data for quenched Cr-Mo-V steel, the oil quenched forging from Heat 02392 (Figure 4) was. low in rupture strength. 7

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TABLE 3 Rupture Data at 1100~ and 1200~F for Boron and Titanium Modified "117-22-A"V Steel Heat Treatment Specimen Temp. Stress Rupture Time Elong. Red. of (a) Direction (~F) (psi) (hours) (%oin2ins) Area (%) Heat A134 - Barstock N1800+T1200 - 1100 50,000 137 13.5 68.5 N1800+T1200 - 1100 40,000 1070 21.0 68.5 N1950+T1250 - 1100 60,000 86 10.0 43.0 N1950+T1250 - 1100 50,000 803 4.5 9.5 N1950+T1250 - 1100 40,000 3472 3.5 7.5 N1950+T1250 - 1200 30,000 228 6,0 (a) N1950+T1250 - 1200 25,000 454 11.0 31.0 Heat A135 - Barstock N1800+T1200 - 1100 45,000 260 24.0 61.5 N1800+T1200 - 1100 40,000 499 25.0 61.5 N1950+T1250 - 1100 55,000 236 12.0 48.0 N1950+T1250 - 1100 40,000 2177 9.5 36.0 Heat A73 - Barstock N1950+T1200 - 1100 25,000 36 34.0 86.0 N2100+T1100 - 1100 35,000 209 18.0 81.0 Heat 02392 - Barstock N1800+T1200 - 1100 55,000 67 1. 5 3.5 N1800+T1200 - 1100 49,000 140 1.5 4.0 N1800+T1200 - 1100 40,000 597 3.0 4.5 N1800+T1200 - 1200 30,000 86 8.5 13.5 N1800+T1200 - 1200 20,000 268 14.5 34.0 N1950+T1250 - 1100 55,000 130 3.0 3 5 N1950+T1250 - 1100 43,000 597(b) 3.0 5.5 N1950+T1250 - 1200 30,000 146 4.5 11.0 N1950+T1250 - 1200 20,000 723 7. 5 12.0 continued...

TABLE 3 continued Heat Treatment Specimen Temp. Stress Rupture Time Elong. Red. of (a) Direction (~F) (psi) (hours) (%in2ins) Area (%) Aus1850-Isol225 1100 52,000 41,5 8.5 17.5 Ausl850-Iso1225 1100 40,000 408 8 0 10.5 Aus 1850-Iso225 1200 30,000 81 22.5 43.0 Aus1950-Iso1225 1100 50,000 140 2.0 6.5 Aus1950-Iso1225 1200 20,000 466 16.0 23.0 Heat 02392 - Pancake Forging N1800+T1200 R 1100 55,000 61 9.0 34.0 N1800+T1200 R 1100 45,000 268 11.5 27.0 N1800+T1200 Ta 1100 40,000 395 6.0 14.5 N1850+T1200 R 1100 55,000 34 5.0 23.5 N1850+T1200 Ta 1100 50,000 292 2.5 4.5 N1850+T1200 R 1100 45,000 448 7.0 11.5 N1850+T1200 Ta 1100 44,000 740 1.5 7.0 OQ1800+T1200 R 1100 55,000 52 12.0 39.0 OQ1800+T1200 Ta 1100 55,000 45 17.5 52.5 OQ1800+T1200 R 1100 45,000 296 11.0 23.5 OQ1800+T1200 R 1100 40,000 515 8.5 27.0 OQ1800+T1200 Ta 1100 40,000 229 13.0 28.5 OQ1800+T1200 R 1200 20,000 169 17.0 38.0 OQ1800+T1200 Ta 1200 20,000 153 14 5 30.0 Heat 02629 - Barstock N1750+T1200 1100 55,000 64.3 16.5 55.0 N1750+T1200 1100 45,000 239 19.5 68.5 N1750+T1200 1100 35,000 1198 20.5 65.5 N1850+T1200 1100 55,000 238 6.0 27.0 N1850+T1200 1100 50,000 488 4.5 24.0 N1850+T1200 1100 46,000 943 6.5 17.0 Heat 02629 - Forging N1850+T1200 R 1100 60,000 90.3 19.5 69.0 N1850+T1200 R 1100 55,000 175 17.0 69.0 N1850+T1200 R 1100 52,000 754 15.5 66.0 N1850+T1200 Ta 1100 52,000 119 13.0 59.5 N1850+T1200 Ta 1100 46,000 330 22.0 69.0 c ontinued...

TABLE 3 concluded Heat Treatment Specimen Temp. Stress Rupture Time Elong. Red. of (a) Direction ( ~F) (psi) (hours) (%in 2 ins) Area(%) Heat 02630 - Barstock N1750+T1200 - 1100 55,000 47.7 25.0 69.5 N1750+T1200 1100 45,000 268 19 0 60.0 N1750+T1200 - 1100 38,000 540 19.5 62.0 N1750+T1200 - 1100 35,000 761 24.0 65.0 N1850+T1200 - 1100 55,000 189 3 0 8 0 N1850+T1200 - 1100 50,000 471 4,0 8.0 N1850+T1200 - 1100 46,000 967 5,5 8 0 Heat 02630 - Pancake Forging N1850+T1200 R 1100 60,000 108 17.0 64.5 N1850+T1200 R 1100 52,000 348 13.5 63.0 N1850+T1200 Ta 1100 51,900 217 15.0 67.0 N1850+T1200 Ta 1100 50,000 244 17.5 69.0 N1850+T1200 R 1100 44,000 671 16.0 79.0 N1850+T1200 R 1100 38,000 1412 22.0 73. 5 N1850+T1200 Ta 1100 38,000 867 20.0 74.0 (a) - All temperatures in ~F (b) - Broke in gage mark R - Radial specimen Ta - Tangential specimen Aus - Austenitize Iso - Isothermally transform N - Normalize OQ - Oil quench T - Temper

TABLE IV Rupture Strengths at 1100~ and 1200~F for Boron and Titanium Modified "17,22-A"V Steel Heat Treatment Rupture Strength Rupture Test Additions made to Heat Austenitized Tempered (psi) Elongation (o) "17-22-A"V No. Material (~F) (~F) BHN 100 hrhr. 1000 hr. 100 hr. Rupture Properties at 1100~F "17-22-A"V + Ti + B Induction Heats 36 ppm B -.33% Ti A134 Barstock 1800 1200 311/321 52,000 40,000 14 21 36 ppm B -.33% Ti A134 Barstock 1950 1250 302/311 59,000 49,000 10 4 92 ppm B -.43% Ti A135 Barstock 1800 1200 311/321 (52,000) 35,000 25 92 ppm B -.43% Ti A135 Barstock 1950 1250 293/311 (62,000) 45,000 - 10 420 ppm B -.67% Ti - A73 Barstock 1950 1200 128 (21, 000) - 30. 10%C - 28% V A73 Barstock 2100 1100 217/228 (39,000) - 20 "17-22-A"V + Ti + B "O" Arc Furnace Heats 28 ppm B -. 35% Ti 02392 Barstock 1800 1200 352/363 52,000 37,000 1.5 3 28 ppm B -. 35% Ti 02392 Barstock 1950 1250 331/341 57, 000 40, 000 3 3 28 ppm B -. 35% Ti 02392 Barstock 1850 Iso 1225 321/331 47, 000 (36, 000) 8 8 28 ppm B -. 35% Ti 02392 Barstock 1950 Iso 1225 341 52, 000 - 2 28 ppm B -. 35% Ti 02392 Forging (R) 1800 1200 311/321 51, 000 (37, 000) 9 12 28 ppm B -. 35% Ti 02392 Forging (T) 1800 1200 311/321 - (35,000) - 6 28 ppm B -.35% Ti 02392 Forging (R) 1850 1200 277/311 50,000 42,000 5 7 28 ppm B -. 35% Ti 02392 Forging (T) 1850 1200 277/311 - 42,000 - 1.5 28 ppm B -. 35% Ti 02392 Forging (R) (OQ) 1800 1200 293/311 51,000 35, 000 12 8.5 28 ppm B -. 35% Ti 02392 Forging (T) (OQ) 1800 1200 293/311 47,000 (30, 500) 17 26 ppm B -.32% Ti 02629 Barstock 1750 1200 321 51,000 36,000 16 20 26 ppm B -.32% Ti 02629 Barstock 1850 1200 321 (62, 000) 46, 000 - 6. 5 26 ppm B -.32% Ti 02629 Forging (R) 1850 1200 302/321 59,000 50,000 20 15 26 ppm B -.32% Ti 02629 Forging (T) 1850 1200 302/321 53,000 (40,000 ) 13 22 ppm B -. 37% Ti 02630 Barstock 1750 1200 341 50, 000 32, 500 (25) 24 22 ppm B -.37% Ti 02630 Barstock 1850 1200 331/341 (59,000) 46,000 (3) 6 22 ppm B -.37% Ti 02630 Forging (R) 1850 1200 311/331 62,000 40,000 17 (16/22) 22 ppm B -.37% Ti 02630 Forging (T) 1850 1200 311/331 (60,000) 37,000 15 (20) Typical Values for "17-22-A"V Steel Experimental induction heat Barstock 45'0052, 000 30, /36,000 8 5 Production heats Barstock C and Mn high for hardenability 40, 000/50, 000 24, 000/33, 000 5 4 Rupture Properties at 1200~F "17-22-A"V + Ti + B Induction Heat 36 ppm B -.33% Ti A134 Barstock 1950 1250 302/311 (37,000) (21,000) (6) (11) "17-22-A"V + Ti + B "O" Arc Furnace Heat 28 ppm B -. 35% Ti 02392 Barstock 1800 1200 352/363 28, 000 (13, 000) 8 28 ppm B -. 35% Ti 02392 Barstock 1950 1250 331/341 33, 000 18, 500 4 (7) 28 ppm B -. 35% Ti 02392 Barstock 1850 Iso 1225 321/331 - - 22 - 28 ppm B -.35% Ti 02392 Barstock 1950 Iso 1225 341 16, 000 16, 000 - 15 28 ppm B -. 35% Ti 02392 Forging (R) (OQ) 1800 1200 293/311 22, 000 - 17 28 ppm B -. 35% Ti 02392 Forging (T) (Q0) 1800 1200 293/311 22, 000 - 15 Typical Values for "17-22-A"V Steel Production heats Barstock C and Mn high for hardenability 25, 000/30, 000 13, 000/15, 000 10 3.5 (a) - Data from Report 243 Iso - Isothermally transformed (R) - Radial specimen (T) - Tangential specimen (00) - Oil quenched ppm - Parts per million

Radial' Tests Radial Tests Sample 1 Sample 5 Sample 2' Sample 6 Sample 3 Sample 7 Sample 4 Sample 8 Figure 1. Sketch to show Location of Test Specimens in 15-inch Diameter by 4-inch thick Forgings from Heat 02392.

Brinell, Etch and Radial Test Slice Radial Tests Sample I__ _ _ 4 Figure 2. Sketch to show Location of Test Specimens in 15 z-inch Diameter by 3-inch thick Forgings from Heats 02629 and 02630.

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2'' ~,t' ~:'' ^ S -^^. <: ^ ^"^.- ", ^ *..'~....~'.~'~,,4,~.' ~'~'.' J,.,',~..' /4 ~ q_'4' ~... ~..'" ~~~~~~~~ ~~3~s-r^^ *... -.,.-:-;:r`~~~~~~~~~~~~~~~~~~~~~~~~~~~~~:4'~.?.~!i~, ~'~t'.? L~>~'~:'>o,,-~ "':"!:, ~'~ ~? ~'k,,. Ni~i,, lb -, - ( * 2 "^ ^V Y 4c V *C034 "f'',l.~.'y'~.~'a.;~..-,' a,~"'':<l',4'~^ >.'". "'' u<' & "^y "''^.'A ~^ - ".?' A l.~ "' < *''^' -'t *< - ^Y ^ i ^ V * - ^y^,- ~ -'^^^^.^^^s-.^;^^^' ~(ii-\- *' r*\,... w^ ~ ~.~._-..~ I:...~ ~-:i"^^ r:*c..... ).'. e',^-..'*. ~. -......,.....-'.....,.,..,-.~......,,,*..i:,~.....^^ ~,,~.. u.......-~. ~,~.', u:.-..:'- /-~,.i... -.'V',: —':~x " ~~!'. ~.".;.~:,j?: ~ ~,!..'x:. *^!~:.v.,-.' T' ~',,+'.:., ~ ~: -.:' -— * * "k,~ ~ ~ ~';?:v^....'.,*..4. ~ ~....~..',":~.... ~.?^'-':~:,~...*' r-:*.....,-:,..,-.- -" */ti':>*'V'... "^ S*' -'^,. ~ ^- 1'',~....., *..!:.- -':.-'.**' * ~~'-4.....? 4.s,' ^ ^ * ^4 ^.';X:'c' ~'.'.~ * -'* ^,r. ", ~r'.'. ~" t' ", AA,:~....... ~~....:5^0:-C~i.,,~,:..... ~.;.-*..;\r.~ av ii.~-~~~~~~~~~~~~~~~~~~~1 Vi k h~~~~~~~tC tj^r ~c..:..:1-'-?^^.-...25 -,?.. ^ a -' -^ M ^^"^^ ^^ ~' ^ ^,.'"*, -, I',>\l' ~.^^.^ f.~ -..... —.-,..^...%.,;,.i^7'~... ~......'........,""..~-' —-:}.'^ --, -..t..:.. <..;. - -.,.,*;.., ". i ~~~~~~~ A ^^'~~~'~r4"::;*:lt^<%' -* *r " \^ ^?:;, r^ - Y7..~. {~,.s: -w+,~ Plate No. 1. O-i mc. of 0.2 p ~..,0.,..0036 percent..oro, 0.33 peren T. Steel, Ha:t. ~','A134.. ~r heat t e a'. b'~ 3'1`~~~~~~~~~~~~~~~~~~~~~.,~:,~:~.:.,+.. ~...':::~''~:~:-:' ~:.~,t.k,: — j",?~.~~.::r:.it"'>'.~'"~~;L'''.~."~".,..E:".'~:~'! Fi~'P:: 3>""~:.~.,. ~ _..'.'~'/,:'-'~'',~'2 -', "-":.,~?'~';:::~'~:~.::;:,:,~.,,3~..:.~.? It'.-~~~~~~~~~.!ri~,Y i~.~.~ *"'~./_.~-.: f ~,~,~. ~ ~~ P~ r b: Y~t; i3,,~ ~5:.C~-::.i ~~~~i~~~~~~~~~~~:','",~ ~ (..~,'. ~~~~~~~~~~~~~~~~~~~~~~~~_~~~~~~~~~~~.~:;F. > x.'.;".,'.~p I'~'-"',L.:,. ~%.~','.~'~,'~'.,i::..,'~''~~.'....':g.~. %...s~~~~p;; rt ~: C~~~~~~~~~~~''"; r:~~~ ~~~~~~;, p~~~~~~~~~~~-(' —....':;.. _, P~~~~~~~~~ ~~~~~~~~. ~' ~ ~",, cl'~~~~~~~~~~~~~~~~~~~~~...'~ ~.'~ --,,X,rP' ~ /L _T~C;1;p:;' ~ ~~~~~~~ ~ ~ ~ ~ ~~...~..,.:, /~ —,~ ~,. ~....~ ~ —~~-;I ~ ~ ~ ~ ~ ~~~.v'~'.' -:_ w'3 >-'~,~,~~~~~~~~~~~,.~.' cX',-,' ~,.~'..,, I'J~-~~~~~~'';~~~.I~,,.,...~ r~..,~..-;~:.... R~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~. *~~~~~~~.,.~ -;,~:,.-, <:\

. Normalized 195000~F, tempered for 6 hours at 1250F to 293/311 BHN. A135A Barstock heat treated as indicated A135. Barstock heat treated as indicated. 05~~~~~~~~~~~~~~~~

A' Normalized 1950F, tempered for 6 hours at 1200F to 128 BHN S —-^O! i.''I X..,, A,'...."::.),A./ ll BC. ~..-,.:;.'.4 - ". ~ ~ 4i Ple N. 3. /i mcotuur of 0. 10 pc Carbon.0 / 4..^^^:.' 0 / +:3 0.. 4 c B'. ~f.'<'/,_._.~F".-.' 9', 3. T.'' "..,,. -..., PlteN.3. Oin.m r of 0. 10 percent.Cro 7 + 0. 042 percent Boron + 0. 67 percentTitaniumSteel, Heat A73. Barstock heat treated as indicated.

X1OOD X1 000D BA Normalized 19500F, tempered for 6 hours at 1250~F to 331/341 BHN. + 0. 0028 percent Boron + O. 35 percent Titanium Steel, Heat X00XlOOOD X0D.q. ~',,, - ~ - ~ -.~.~4'4 ~,,~~~~~~

X 1 00D XS 1 0 0 0 D Ax Austenitized 1850 ~F, cooled to and held for 6 hours at 1225~F to X100D X1000D A. Austenitized 1850~F, cooled to and held for 6 hours at 1225~F to 341 BHN, Plate Now 5. Original mic rostructure of 0. 26 perc ent Carbon " 17 22 -A"V 02392. Barstock heat treated as indicated. ~'~:;,.. \

Plate No. 6 Original microstructure of 0.26 percent Carbon ~',-" ~-A-V 11 hours at 1200~F to 311/321 BHN..? Po,.;.~;..,..' ~..'I,r..'' b~~ XlO Xl-O''O.OD,~~.' ~-., B~~~~~~~~~~~~~~~~~~~~~~. Tangntia spcie..'/~ -'"-'-'..".~r'1., Plate'No 6.;'Originalr.'-'. mirotrctr of 0.;'26 - - percent~ Carbon.'1-'' AV +~~~~~~~~~/ 0. 0028- percent- Boro +..~ 0...~ 35. pecn.iaiu teHa 02392~~~~~~~~~r.' Forin normalize from 1.0. and'- tempe-~red~ fo 11 hours at 12000F to 311/321 BHN~~~~~~~~~~~~~~~~~~~~..'~

...-,:.'. ~ "-... ~ r. ~ f ~ ~'"*'I it ~~~~~~~~~~~~~~~~~~~~~~~~~T~~~~~~~~~~~~~ 5iT~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~ 3~~~~~t t~~i~~s' "~' D:'/:': 4~//~:,.r. T'~.,....~' "~''~"~' ~..,, g~'s~:S,~'~.;..o~~.f'V,~100D X1000D A. Radial specimen.: ~2.-"~ ".:,-'-"':' - "'"'.. ih~:?~~~~ ~ ~ "2"""""""""' I.!~ ~ ~~~~~~~~~~~~~~~~~ IJ::: ~ ~ ~ ~ ~ ~ ~ ~ 4.{.t~- *,,e,-' "-'7'.':".., 6'.~..``......`..~.;~`..:.~;.~`.d..:~.....~.`..':.'.,':..;'~~.. "''', V' < F; 1~f~~~~~~~~~~~~~h~~~-.-il ~/ic~~~~~~~~~~~~~~~~~':$i o.~~~~~~~~~~*.;~.1 ~'~1;.-;_'.:,''..'. j~~~~~,:; ~.' Z.,.::i/'....~~~. s 6:..;P. ~...>', ~ ~i _'AI *~'~ 1r i~~~(.,....'. life ~ ~ ~ ~ ~ f B. T..a spec.imen. Plate~~~~~~~~~~~~"~' No~'., 7-'.i Origina micrstrutur of' 0'.26 peren Carbon "17"'-A"V to~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~l 27/31 HN.,.,.-.....~~c........."-*,-~. ~.,..., -.,".-.'"-.'"":'."';.."'~.';~;.'~..~~.. l~:. " —..."..;*.'~., ~..-.:y...:.~'."..,..,.,,.:':,~~,I,..:...:...-x",.'.......':'k'... ~.. ~ ~!..<..?.C..~,...'~,.-,~.''....,...........~'/'::',: ~f",'Y""..."''"'.."" """' M~~~' ~ ",. id. ~ -d~.';."-'....'.,'L -*';I~K,..r:~ ~.?~~~~ ~ ~ ~~~~~~~~~~~ o ~;."'-~ %-': "~..,~.,. ~~/c,l,?:- I,......) r r., -..;,:,......,.,. ~,......:'.~T:'?..,.,.',~~~~~~~~~~~~~~~~~~4'~....'.~;., ~ ~'_ "'- -."i;~N.\.~-'..;-,' - ~....-..',.'.~ -'. ~. ".'.',-..1.;.~.:. -,~~~..,'.'..'?~',:- -.. " ~, -.,x,',' %i. ~;.~lipr~ -"~~,";,'':2"_.,~~~'",,~',,~..''-.' -,-,....'..... - L~: ~' ~:.'~,,~":',,~:,~.~ -~ 4/',:'"'..'.',"-. ~.'~~~~ ~~~~~~~,.i ~...,...:,.,,.. J..'...'~~~~~ ~' ~~ "',' ~"....' ~~~~~~~~~~~~~~~~~~~~ +..02 eret B ro 03 prcn TiaimSteHa ignraiefro. 1 5~, tepre o 6 vI hrs at 100f: to~~~~~~ 277/311 BHN

~-. %~ ~ ~ ~ ~'"~,~' ~'r'', 1~';S:!"'A.-~.' "p I'l ~~~~~~~ ~, ~,-*.* -,',.'",:" 47-~~~~~.~./.,' ~ 4,;, ia.,,,,.~. X~~~~~~~ I,~YC, r e. ji~ t~hr ~',,' -'-x ~n' ~-.~.-~...~.~r:~ ~:...~ ~~. -,","Z'~.'..~, \,,,'-...,~i!,i~ ~~` ~ XlOOD XlOOOD B. Tangential specimen.:: + ~ 0. 0028' pecn Boo...1-;, 0,.. 35: percent Tianu Stel Hea ing0 oi unhe rm180F emee or6hus t100 to 293/311BH"N. ~.,.-........~~~i,:,....,d~., ~~t~..,,~~~~c.....,.:..;~,~ I,,~ _,,:. "~ ~ ~,''.~!i), ~.~..~..-..,..~:.~....:~ If.;~.~r~.~ -,i' ~~~~~~~~~~~~~ ~:'i':..:.,~-.~...~... iI ~. "':~+'";.~~~.~. i ~ ~ ~ ~ ~ ~ ~'t "' Cf.... a tp: I- J,~~~" 7'~~~~~~~~~~.. -,.,...~J.. "-:~~,'" ~':~'... 4 ~~~~~~~: f~ b.~' ".~i ".. -.C':.'C; ~.,:"-~- / 2,~-;i~~~~~~~;74.~~~~~~'? i...J-.....~ ~':t.~'.,..1;..~.-f. ~.'C ~:'~ ~ ~ i~''~ It'.~~...L Bo Tagnl spcmn B.~~~ 0o008 erentia Boo..5percient,a~m.teII~ 02 392. o15 inch diameter by 4.inch thick upset pancake forging o~_l quenched from 1800~F, tempered /or 6 heurs-at 1200~F to 293/311 BHN.

.51~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~.'A ~~~~~~~'~~4 C~ *x -,,. -.. ":;,~.~.~,,',,- -~'a __ \..~~~~~~~~~~~~,. ~- ~~~: ~ c~~~:~;~:l up -...:~,;.,, v,.'.~' ~, ~,.~'.~,..~~,,..., ~:..... V,~.~, ~.,,-~,,~,:;,~ ~....?.~,:.,~'~ ~. ~;~ "~~. ~ ~,r. J,.~~~~~~~~~~~~';~, ~r'~ ~ ~ ~ ~ ~ ~ ~ ~ ~ ~~~~~~~~~ 1~~~~~~- 1 ~. "..... %.,IL". ~.A c' ~;II~ ~ ~ ~ ~ ~ ~ ~ ~ ~ ~ ~ ~ ~ ~ ~ ~ ~ ~~~~~~~~~~~~~~/ — ~~b~ ".,,.,.'. ~:-;,,~ ~';.... 4 X100D X1000D A. Normalized 1750OF, tempered for 6 hours at 1200~F to 321 BHN. ~' Spiis: -,.. * * 0 t-~ \ - M7,,,, J -~~~~~~~~~~...,,,r *2.. X100D XlOOOD~~~~~~~~~~~10 C ~ ~ ~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~' ~~ ~~ ~' ~r~~.0r ~ ~ ~ ~::I:~t -L ~~~~'' rM~~~~~~~~~~~~~~~~~.: ~ + 0.~: 002 pecn Boo + 0. 3 pretTanuSelHa..~~022, Basokettrae"a'nictd i' ~ ~j~ l~j~ I~ li J~~: i i h::. ~ rr,. - ~ ~ ~ ~~~~~~~~~~~~~~~~~~~~~~~~~~~~~I r-:st. ~~~~~~~~~::~,::; ~~'.,' i C!/..~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~~ -~~~~~~~~~~~~~~~~~~~~~~~,, ~. L''. 0~6Z 9 Bartoc heagt t reae sidctd

"17-22"V ~ X100D c' o itn <'t Hea ~.' n.o ~' -* f F 8 ~ and9 -.te..pre.''A' o 3' / " Plate.... - *O'riginal' o 2 pe n "17.22"A.*V o. 0 pre Bor. ~'.''perm ali zedf ro m' a %- \ te ~' e' at'/': t o

X1 00D X1 000D ~"?~'~-~#,, ~.'- ~Q. ~~~~~~Be,~~~~~~ Radial specimen from Heat 02630 311/"331 BHN.:'! A. Radial specimen from Heat 02629 302 321 BHN. I!~I.:,.,,: / <vx,:.-''