Effect of Case Carburizing on Mechanical Properties And Fatigue Endurance Limits of P/M Steels. *Hoeganaes Corporation Cinnaminson, NJ 08077

Size: px
Start display at page:

Download "Effect of Case Carburizing on Mechanical Properties And Fatigue Endurance Limits of P/M Steels. *Hoeganaes Corporation Cinnaminson, NJ 08077"

Transcription

1 Effect of Case Carburizing on Mechanical Properties And Fatigue Endurance Limits of P/M Steels George Fillari*, Thomas Murphy*, Igor Gabrielov** *Hoeganaes Corporation Cinnaminson, NJ **Borg Warner Automotive Livonia, MI ABSTRACT Case carburizing has long been a basic technique for the improvement of the wear and fatigue resistance and of PM steel components. The key to the successful improvement in carburizing, however, is understanding, and interpreting the microstructure of the carburized case. The main area for growth in the PM industry is in the high performance gearing applications. The success of penetrating this area depends upon the ability to understand the key components that effect the fatigue endurance limits of PM materials. This paper will examine and illustrate how tensile properties and the fatigue endurance limits of a P/M hybrid alloy are affected by alloying additions and carburizing. INTRODUCTION Carburizing is the addition of carbon to the surface of low-carbon steels at temperatures generally between 850 C and 950 C (1560 F and 1740 F), at which austenite, with its high solubility for carbon, is the stable crystal structure. Hardening is accomplished when the high-carbon surface layer is quenched to form martensite so that a high-carbon martensitic case with good wear and fatigue resistance is superimposed on a tough, low-carbon steel core. [1] Case depth of carburized steel is a function of carburizing time and the available carbon potential at the surface. [2] When prolonged carburizing times are used for deep case depths, a high carbon potential produces a high surface-carbon content, which may thus result in excessive retained austenite or free carbides. These two microstructural elements both have adverse effects on the distribution of residual stress in the casehardened part. Consequently, a high carbon potential may be suitable for short carburizing times but not for prolonged carburizing. In regards to fatigue properties, Low retained austenite content and fine austenitic grain sizes, which create a microstructure of finely dispersed retained austenite and tempered martensite, prevent nucleation of fatigue cracks, or retard fatigue crack initiation until very high stress levels are reached. In contrast, low-stress applications that fracture at low cycles is related to high retained austenite levels and coarse austenite grain sizes. [1]

2 TEST PROGRAM The test program was intended to investigate the performance levels achievable on tensile properties and rotating bend fatigue response of a hybrid PM steel by using a secondary heattreatments such as case carburizing. This program was divided into three parts. 1. Investigate alloying elements such as graphite and nickel on mechanical properties. 2. To investigate the effect of carburizing times on properties. 3. To estimate the percentage of retained austenite in the carburized case. EXPERIMENTAL PROCEDURE The compositions of the test materials that were evaluated in this study are listed in Table I. The base powder was water atomized and pre-alloyed with 0.85 w/o molybdenum. The 85HP was premixed with nickel and graphite. The nickel used was INCO 123 and the graphite was Asbury 3203H. Each premix contained 0.75 w/o Lonza Acrawax C as the lubricant system. Table I. Premix Compositions Premix Base Powder Nickel Graphite Acrawax C ID Bal. w/o w/o w/o A Ancorsteel 85HP B Ancorsteel 85HP C Ancorsteel 85HP D Ancorsteel 85HP TEST SPECIMEN / COMPACTION AND SINTERING Tensile dog-bone, impact, and fatigue samples were compacted to a density of 7.20 g/cm 3. Green density, sintered density, and transverse rupture strength was determined from the average of five compacted transverse rupture (TRS) specimens (ASTM B-528). Tensile strength, yield strength, and maximum elongation were obtained from the average of five dog-bone tensile samples (ASTM E-8). Apparent hardness measurements were performed on the surface of the dog-bone tensile samples using a Rockwell hardness tester. All measurements were conducted using the HRA scale for ease of comparison. All test pieces were sintered under production conditions in an Abbott continuous belt high temperature furnace at the Hoeganaes R&D facility, in Cinnaminson, NJ. The sintering condition used for the test specimen is listed below.

3 SINTERING CYCLE Sintering Temperature: 1150 C (2100 F) (1260 C (2 F) for premix 3) Atmosphere: 90 v/o N 2-10 v/o H 2 Time in Hot Zone: 20 minutes For the samples that were carburized, the parameters are listed below. CARBURIZING CYCLE 1 Temperature: Time at Temperature Quench: CARBURIZING CYCLE 2 Temperature: Time at Temperature Quench: 925 C (1700 F) vacuum furnace 180 minutes, Pressure / Nitrogen 925 C (1700 F) 240 minutes, Pressure / Nitrogen All samples were tempered at 204 C (400 F) in air for 1hr. prior to testing. Tensile testing were performed on a 267,000 N (60,000 lb.) Tinius Olsen universal testing machine with a cross-head speed of mm/min (0.025 in/min). Elongation values were determined by utilizing an extensometer with a range of 0-20%. The extensometer was attached to the samples up to failure. Rotating bending fatigue samples were pressed to a density of 7.20 g/cm 3, and machined from blanks that were sintered at 1150 C (2100 F) under an atmosphere of 90 v/o N 2-10 v/o H 2. The heat treated fatigue samples were rough machined following sintering then heat treated, finished ground, and polished to size. The dimensions of the specimen used for this analysis, along with allowable dimensional tolerances, are shown in Figure 1. Fatigue testing was performed on six randomly selected Fatigue Dynamics RBF-200 machines at a rotational speed of 8000 rpm. These rotating bending machines are of the mechanical and nonresonant type and are an efficient means of inducing fatigue in a specimen of round cross section. [3]. A staircase method was used utilizing 30 samples and a run-out limit of 10 7 cycles. The staircase method of testing was regulated so that there were both failures and run-outs at a minimum of two stress levels. [4] The percentage of failures for each stress level was calculated and plotted on a log-normal graph. From these plots, the fatigue endurance limit (FEL) at 50% and 90% was determined by linear extrapolation. The 50% FEL represents the stress level where 50% of the specimens will break and 50% will run-out. The 90% FEL represents the stress level where 90% of the specimens will run-out and 10% will break.

4 Figure 1. Dimensions of Rotating Bending Fatigue Specimen RESULTS AND DISCUSSION The mechanical properties of the alloys evaluated are summarized in Tables II trough Table VI. Shown in Figure 2 and 3 are the effects of alloy content and carburizing times on ultimate tensile and yield strengths for the alloys tested. In the as sintered condition, the tensile strengths for the alloys at a sintered density of 7.20 g/cm 3 are 490 MPa (71*10 3 psi), 559 MPa (81*10 3 psi), 621 MPa (90*10 3 psi) and 738 MPa (107*10 3 psi) for alloys A, B, C and D. Elongations are in the range of %. For the samples that were carburized in the first cycle, the tensile strengths were increases between % to 835 MPa (121*10 3 psi), 850 MPa (123*10 3 psi), 850 MPa (123*10 3 psi) and 910 MPa (131*10 3 psi), when compared to the as sintered condition. Samples that were subjected to the second carburizing cycle resulted in increases in tensile strengths between 5 20 % to 1000MPa (145*10 3 psi), 891 MPa (129*10 3 psi), 987 MPa (143*10 3 psi) and 959 MPa (139*10 3 psi) when compared to the first cycle. Increases in yield strengths also follow the same trend. High temperature sintering for alloy 3 resulted in an increase in tensile strength from 3 13 %. Table II. As Sintered Properties for The Alloys Tested at 1150 C (2100 F). Sintered Condition Material Density HRA UTS OFFSET Elong ID (g/cm³) (MPa/10 3 psi) (MPa/10 3 psi) % /71 352/ As Sintered /81 386/ /90 407/ / /76 3.1

5 Table III. Tensile Properties for Samples Subjected to Both Carburizing Cycles. The Alloys Tested. Sintered at 1150 C (2100 F) Sintered Apparent 0.20% Condition Material Density Hardness UTS Offset Elong Cycle C (400 F) Cycle C (400 F) ID (g/cm 3 ) HRA (MPa/10 3 psi) (MPa/10 3 psi) % A / / B / / C / / D / / A / / B / / C / / D / / Table IV. Alloy C Tensile Properties for Samples Subjected to Both Carburizing Cycles. Sintered at 1260 C (2 F) Carburizing Sintered Apparent 0.20% Condition & Density Hardness UTS Offset Elong Tempering Temp (g/cm 3 ) HRA (MPa/10 3 psi) (MPa/10 3 psi) % Cycle 205 C / / Cycle 205 C / / AS SINT CYCLE 1 CYCLE X X 800 UTS (MPa) Alloy A Alloy B Alloy C Alloy D Figure 2. Ultimate tensile strength as a function of alloy content and carburizing cycle. Samples sintered at 1150 C (2100 F) - X indicates the strength of alloy sintered at 1260 C (2 F)

6 1000 AS SINT CYCLE 1 CYCLE Yield Strength (MPa) X X Alloy A Alloy B Alloy C Alloy D Figure 3. Yield strength as a function of alloy content and carburizing cycles. Samples sintered at 1150 C (2100 F) - X indicates the strength of alloy sintered at 1260 C (2 F) Rotating bending fatigue data were collected on samples compacted to a density of 7.20 g/cm3. The fatigue endurance limits determined for the materials, along with sintered densities are shown in Table V. Figure 4, illustrates the fatigue performance for the alloys tested along with the fatigue ratios for 90%. What is interesting to note is that the carburized samples resulted in fatigue endurance limits equivalent to or greater than samples that were machined from AISI 8620 wrought. The wrought samples were machined in the principal working direction (longitudinal) and perpendicular to the principal working direction (transverse). [6] Table V. Rotating Bending Fatigue Results sintered at 1150 C (2100 F) Tempered at 205 C (400 F) Carburizing Sintered Condition Material Density Survival Limits Fatigue Ratio ID (g/cm 3 ) 50% 90% 90% Survival A /67 449/ B /68 455/ Cycle 1 C /72 483/ D /73 490/ C* /73 497/ A /60 393/ B /66 462/ Cycle 2 C /70 469/ D /63 414/ C* /71 476/ (* Alloy C Sintered at 1260 C (2 F)

7 600 Fatigue Endurance Limit (MPa) 550 C-1 (.58 UTS) D-1 (.53 UTS) 1260 C (.51 UTS) 1260 C (.46 UTS) C-2 (.47 UTS) B-2 (.52 UTS) A-1 (.53 UTS) D-2 (.43 UTS) 400 B-1 (.55 UTS) A-2 (.52 UTS) 350 Wrought Long..35 UTS) Wrought Trans..26 UTS) Tensile Strength (MPa) Figure 4. The relationship of fatigue endurance limits and tensile strength of the alloys tested, along with the fatigue ratios for 90% compared to AISI 8620 wrought. The etched microstructure in the as-sintered condition are illustrated in Figure 5(a-d). Figure 5a. consist mostly of divorced pearlite, ferrite with some martensitic regions. Figure 5b is similar with nickel rich regions and bainite and martensite. Figure 5c is similar to Figure a and b. The microstructure of Figure 5d consist of divorced pearlite, areas of martensite, and some bainite. Figures 6 through 10 compares the microstructure of the samples subjected to both carburizing cycles. These microstructures are taken from the center of the fatigue samples at the reduced sections. From Figures 6 10 (a-b) you can clearly see the carburized case that resulted from the first cycle. These samples resulted in a case depth of about 1100 µm (Alloy A), (Alloy B), 1000 µm (Alloy C), 1100 µm (Alloy D), and 1000 µm (Alloy C sintered at 1260 C (2 F), respectively. When compared to the samples subjected to the second carburizing cycle (Figures 6 10 (e-f), these samples were through hardened with no evidence of a definitive carburized case. The etched structure for the alloys carburized in the first cycle are similar. In the reduced section (Figure 6 10 c,) consist of acicular martensite, retained austenite with some nickel rich regions. The etched structure of the softer core of alloy A (Figure 6d), consist of lathe martensite, bainite and nickel rich regions. The core of alloy B and C (Figure 7d and 8d) consist of divorced pearlite and nickel rich regions. The core of alloy D (Figure 9d) consist of mostly lathe marensite, nickel rich regions, bainite, and unresolved pearlite. The core of alloy C sintered at 1260 C (2 F), (Figure 10d) consist of lathe martensite, nickel rich regions and divorced pearlite. The microstructures for the alloys that were through hardened in the second cycle are also similar. In the reduced sections (Figure 6-10, g-h) consist mostly of acicular martensite, retained austenite with nickel rich regions.

8 Figure 11 illustrates the Vickers Hardness HV of the alloys tested. Hardness readings were taken from the surface of the case to the core in increments of in. As a result of the through hardening, the samples subjected to the second cycle resulted in a higher hardness (HV) though out the sample. The samples from the first cycle initially were harder at the surface and gradually decreased in hardness as the distance increased from the surface to the core. In terms of the effect of the nickel and graphite. In the as-sintered condition, ultimate tensile strength increased with nickel content. For the alloys that contained 0.15 w/o graphite, as the nickel content increase from 2.0 to 4.0 w/o the UTS increase more than 25 % to 621 MPa (90*10 3 psi). For the alloys that contained 0.30 w/o graphite, as the nickel content was increased to 4.0 w/o the UTS increased more than 30 % to 738 MPa (107*10 3 psi). The same trends also resulted for the yield strength. For the alloys at 0.15 w/o graphite, the yield increased more than 15 % to 407 MPa (59*10 3 psi). At 0.30 w/o graphite, yield strength increased more than 35 % to 524 MPa (76*10 3 psi). For the samples that were carburized (cycle 1) the increases were minimal. For the alloys that contained 0.15 w/o graphite, as the nickel content increase from 2.0 to 4.0 w/o the UTS increase were about 2 % to 850 MPa (123*10 3 psi). For the alloys that contained 0.30 w/o graphite, as the nickel content was increased to 4.0 w/o the UTS increased about 5 % to 910 MPa (131*10 3 psi). The yield strength on the other hand decreased as the nickel content was increased to 4.0 w/o. For the alloys at 0.15 w/o graphite, the yield strength decreased more than 15 % to 607 MPa (88*10 3 psi). At the 0.30 w/o graphite contents, yield strength decreased more than 25 % to 607 MPa (88*10 3 psi). For the samples that were through hardened (cycle 2), at the 0.15 w/o graphite, as the nickel content increase to 4.0 w/o the UTS decreased to 987 MPa (143*10 3 psi), but was negligible. At 0.30 w/o graphite, as the nickel content was increased to 4.0 w/o the UTS resulted in a slight increase to 959 MPa (139*10 3 psi). The same trends also resulted for the yield strength as in the first cycle. For the alloys at 0.15 w/o graphite, the yield decreased more than 20 % to 718 MPa (104*10 3 psi). At the 0.30 w/o graphite contents, yield strength decreased 10 % to 676 MPa (98*10 3 psi). For the high temperature sintering of alloy C for the first carburizing cycle, the UTS increases were about 15% to 966 MPa (140*10 3 psi), changes in yield were negligible. For the second carburizing cycle, a slight increase in UTS to 1021 MPa (148*10 3 psi), changes in yield were negligible.

9 (a) (b) (c) (d) Figure 5. Microstructure of the as sintered samples: (a)alloy A, (b) Alloy B, (c) Alloy C, (d) Alloy D. Sintered at 1120 C (2050 F)

10 (a) (e) (b) (f) (c) (g) (d) (h) Figure 6. Microstructures of alloy A: (a-c (case) d (core) subjected to carburizing cycle-1) (e-g (case) h (core) subjected to carburizing cycle-2) Sintered at 1150 C (2100 F)

11 (a) (e) (b) (f) (c) (g) (d) (h) Figure 7. Microstructures of alloy B: (a-c (case) d (core) subjected to carburizing cycle-1) (e-g (case) h (core) subjected to carburizing cycle-2) Sintered at 1150 C (2100 F)

12 (a) (e) (b) (f) (c) (g) (d) (h) Figure 8. Microstructures of alloy C: (a-c (case) d (core) subjected to carburizing cycle-1) (e-g (case) h (core) subjected to carburizing cycle-2) Sintered at 1150 C (2100 F)

13 (a) (e) (b) (f) (c) (g) (d) (h) Figure 9. Microstructures of alloy D: (a-c (case) d (core) subjected to carburizing cycle-1) (e-g (case) h (core) subjected to carburizing cycle-2) Sintered at 1150 C (2100 F)

14 (a) (e) (b) (f) (c) (g) (d) (h) Figure 10. Microstructures of alloy C: (a-c (case) d (core) subjected to carburizing cycle-1) (e-g (case) h (core) subjected to carburizing cycle-2) Sintered at 1260 C (2 F)

15 (a) (b) Vickers Hardness Vickers Hardness Cycle 1 Cycle Distance from Surface (in.) Cycle 1 Cycle Distance from Surface (in.) Cycle 1 Cycle 2 Cycle 1260 C Cycle 1260 C Vickers Hardness Vickers Hardness (c) Distance from Surface (in.) Cycle 1 Cycle 2 (d) Distance from Surface (in.) Figure 11. Vickers Hardness (HV) of the samples evaluated. Sintered at 1150 C (2100 F) a) Alloy A, b) Alloy B, c) Alloy C 1260 C (2 F) d) Alloy D ESTIMATE OF RETAINED AUSTENITE CONTENT IN CARBURIZED SAMPLES A study was conducted to evaluate the effect of surface carburization of test bars for the alloys tested. The metallographic test pieces used in this exercise were cross-sections cut from sintered and carburized impact bars. Cross-sections from the carburized impact bars from the first cycle were cut, mounted, ground and polished using well-established metallographic practices. The prepared surfaces were then etched using a combination of 2 v/o nital and 4 v/o picral. Preliminary visual examination confirmed the presence of the carburized case where the microstructure consisted of martensite and retained austenite, nickel rich regions, and a few small areas of bainite. The etched surfaces were further prepared by stain etching with an aqueous solution of 25 w/o sodium bisulphite. A contrast was created in the microstructure between the martensite, which was colored by the stain etch, and the featureless white retained austenite/ni-rich regions. An automated image analysis system was used to measure the amount of the unstained white areas (retained austenite). During the analysis, the features coinciding with a near white detection setting were separated into large and small feature groups. The small features were < 30 µm 2 and appear as small, angular needles located between the martensite needles. The large features, > 30 µm 2 and appear to be a combination of Ni-rich regions and areas containing diffused Ni with the elevated carbon content from the carburization process.

16 Area measurements were made in strips of fields along the edge of each cross-section. Each strip was a single field in height and 30 fields across. The first strip was positioned beneath the sample edge at a distance of 150 µm from the edge. The second strip was extended 150 µm µm into the sample. Each strip was approximately 6 mm long. In making the measurements, the total volume of the compact was considered, including porosity. It was not subtracted from the calculations. Table 6 list the volume percent measurements of the two white feature sizes (retained austenite) and the averages at specific distances within the part along with the average minus the volume of the Ni-regions. Table VI. Area Percent Measurements Retained Aust + Ni-rich Depth Average w/o Sample-Strip Feature Size Average (v/o) micron Ret. Aust < 30 micron < 30 micron < 30 micron > 30 micron > 30 micron > 30 micron < 30 micron < 30 micron < 30 micron < 30 micron < 30 micron > 30 micron > 30 micron > 30 micron > 30 micron > 30 micron The averages of the small fractions remain consistent throughout the examination, staying between 2 and 4 v/o for all samples. The major difference appeared in the measurement of the large features, especially in the 4 w/o Ni premixes. An interpretation problem was seen in these tests where the separation of the retained austenite from the areas containing very high Ni contents could not be made because of any clear distinction between chemical and/or microstructural composition was apparent. The increased alloy content from the diffused Ni coupled with the increase in carbon content from the carburization treatment probably caused the Ms temperature in some regions to be lowered sufficiently to prevent transformation to martensite. Further tests were preformed to determine the amount of Ni-rich regions present in the premixes with both Ni contents and in the areas unaffected by the carburization treatment. Core microstructures for premixes 1 (2w/o Ni) and 3 (4w/o Ni) were used as non-carburized examples. It was thought the possibility of comparing and subtracting the amount of core Ni-rich phases from the total may help quantify the higher alloyed retained austenite in the carburized case. To accomplish this, the samples were prepared and re-etched with the nital/picral combination. The etch/stain procedure described previously to develop the microstructural contrast was ineffective on the core microstructures because the constituents within the cores were obviously different from the carburized cases. The cores consist of ferrite, divorced pearlite, bainite, some martensite, Ni-rich regions, and probably retained austenite surrounding the Ni-rich regions.

17 150 µm µm Figure 12. A85HP Ni C case/core transition. 25X Manual point counts were performed to determine the amount of Ni-rich phase. Results of point counts were 5.1 v/o for premix 1 and 11.1% for premix 3. These values were then subtracted from the average values given in Table 6. An example of how the areas and fields on the impact sample is given in Figure 12. From Table 6 it is clear that nickel plays an important role in the formation of retained austenite. The samples that contained 4.0 w/o Ni resulted in an increase in retained austenite for more than 70 % to for the samples that contained 0.15 w/o Gr and more than 50 % for the sample that contained 0.15 w/o Gr (in the range of µm). At this level of retained austenite, between 5 % 15 %, any differences in mechanical properties appear to be negligible. CONCLUSION 1. At a nominal density of 7.20 g/cm3, as expected in the as sintered condition the ultimate and yield strength increased as the carbon and nickel contents increased. Alloy A (2.0 w/o Ni, 0.15 w/o Gr.) resulted in the highest tensile properties, in the carburized (cycle-1) condition, and the through hardened (cycle-2) condition. The second carburizing cycle resulted in parts that were through hardened, resulted in a higher martensitic structure from the surface to the core. The increase in martensite resulted in higher ultimate and yield properties when compare to the case carburized samples. 2. The 90 % fatigue survival limits remained fairly constant for the 1 st carburizing cycle. The limits varied between 53 to 58%. High temperature sintering reduced the 90% fatigue limits to 51%. With respect to tensile properties, high temperature sintering for the 1 st carburizing cycle resulted in an increase of 15% to 966 MPa (140*10 3 psi), changes in yield were negligible.

18 3. The 90 % fatigue survival limits decreased for the 2 nd carburizing cycle. The limits varied between 39 to 52%. High temperature sintering reduced the 90% fatigue limits to 46%. With respect to tensile properties, high temperature sintering for the 2 nd carburizing cycle resulted in a negligible increase in ultimate and yield strength. 4. For both carburizing cycles, increasing the nickel content from 2.0 w/o to 4.0 w/o resulted in minimal if any increases in tensile and fatigue properties. 5. The carburized samples resulted in fatigue endurance limits equivalent to or greater than samples that were machined from AISI 8620 wrought. 6. Nickel plays an important role in the formation of retained austenite. The samples that contained 4.0 w/o Ni resulted in an increase in retained austenite for more than 70 % to for the samples that contained 0.15 w/o Gr and more than 50 % for the sample that contained 0.15 w/o Gr (in the range of µm). At this level of retained austenite, between 5 15 %, any differences in mechanical properties appear to be negligible. ACKNOWLEGEMENTS The authors wish to acknowledge the contributions of Gerald Golin and Thomas Murphy to this paper and their timely preparation of the metallographic samples is much appreciated.

19 REFERENCES 1. Krauss, G., Principles of Heat Treatment of Steels, American Society for Metals, Vol. 1, pp Case Hardening of Steel, ASM International, Vol. 1, pp. 4, Manual on Fatigue Testing, University Microfilms, Inc., Baltimore, MD, Rice, R.C., Fatigue Data Analysis, ASM International, Metals Handbook, Vol. 8, 9 th Edition, pp , W. Jandeska, R. Slattery, H. Fran, A. Rawlings, P. King, Rolling Contact Fatigue Evaluation of Powder Forged FLN2-4405, To be presented 2005 International Conference on Powdered Metallurgy and Particulate Materials, Montreal, Canada.

EFFECT OF MOLYBDENUM CONTENT IN PM STEELS

EFFECT OF MOLYBDENUM CONTENT IN PM STEELS EFFECT OF MOLYBDENUM CONTENT IN PM STEELS Bruce Lindsley and Howard Rutz Hoeganaes Corporation Cinnaminson, NJ 08077, USA ABSTRACT Molybdenum (Mo) is a highly effective alloying element in ferrous powder

More information

A SUPERIOR SINTER-HARDENABLE MATERIAL. M.C. Baran, A.H. Graham, A.B. Davala, R.J. Causton, and C. Schade Hoeganaes Corporation Cinnaminson, NJ 08077

A SUPERIOR SINTER-HARDENABLE MATERIAL. M.C. Baran, A.H. Graham, A.B. Davala, R.J. Causton, and C. Schade Hoeganaes Corporation Cinnaminson, NJ 08077 A SUPERIOR SINTER-HARDENABLE MATERIAL M.C. Baran, A.H. Graham, A.B. Davala, R.J. Causton, and C. Schade Hoeganaes Corporation Cinnaminson, NJ 08077 Presented at PM 2 TEC 99 International Conference on

More information

Methods to Improve the Fatigue Life of Sinter-Hardened Components

Methods to Improve the Fatigue Life of Sinter-Hardened Components Methods to Improve the Fatigue Life of Sinter-Hardened Components Alan Taylor GKN Sintered Metals Salem, Indiana Francis Hanejko Hoeganaes Corporation Cinnaminson, NJ Abstract: Previous experimental work

More information

EFFECT OF POST SINTERING THERMAL TREATMENTS ON DIMENSIONAL PRECISION AND MECHANICAL PROPERTIES IN SINTER-HARDENING PM STEELS

EFFECT OF POST SINTERING THERMAL TREATMENTS ON DIMENSIONAL PRECISION AND MECHANICAL PROPERTIES IN SINTER-HARDENING PM STEELS EFFECT OF POST SINTERING THERMAL TREATMENTS ON DIMENSIONAL PRECISION AND MECHANICAL PROPERTIES IN SINTER-HARDENING PM STEELS Bruce Lindsley and Thomas Murphy Hoeganaes Corporation Cinnaminson, NJ 08077

More information

SURFACE-HARDENABLE HEAT TREATED P/M STEELS

SURFACE-HARDENABLE HEAT TREATED P/M STEELS ABSTRACT SURFACE-HARDENABLE HEAT TREATED P/M STEELS W. Brian James and Robert J. Causton Hoeganaes Corporation Riverton, NJ 08077 USA Presented at the Powder Metallurgy World Congress, San Francisco, CA,

More information

Atomized Low Apparent Density (AD) Iron Powder For Advanced PM Applications

Atomized Low Apparent Density (AD) Iron Powder For Advanced PM Applications Atomized Low Apparent Density (AD) Iron Powder For Advanced PM Applications Peter Sokolowski and Francis Hanejko Hoeganaes Corporation Cinnaminson, NJ 08077 ABSTRACT A low apparent density atomized iron

More information

VACUUM SINTERING AND SINTER-HARDENING OF Mo AND Ni LOW ALLOYED STEEL

VACUUM SINTERING AND SINTER-HARDENING OF Mo AND Ni LOW ALLOYED STEEL Powder Metallurgy Progress, Vol.4 (2004), No 2 79 VACUUM SINTERING AND SINTER-HARDENING OF Mo AND Ni LOW ALLOYED STEEL V. Stoyanova, A. Molinari Abstract The main purpose of this work is to investigate

More information

MICROSTRUCTURE AND MECHANICAL PROPERTIES OF A BAINITIC PM STEEL

MICROSTRUCTURE AND MECHANICAL PROPERTIES OF A BAINITIC PM STEEL MICROSTRUCTURE AND MECHANICAL PROPERTIES OF A BAINITIC PM STEEL Chris Schade & Tom Murphy Hoeganaes Corporation Cinnaminson, NJ 08077 Alan Lawley & Roger Doherty Drexel University Philadelphia, PA 19104

More information

Effect of Molybdenum Content on Mechanical Properties of Sintered PM Steels. Candido Ruas, Sylvain St-Laurent Quebec Metal Powders Limited

Effect of Molybdenum Content on Mechanical Properties of Sintered PM Steels. Candido Ruas, Sylvain St-Laurent Quebec Metal Powders Limited Effect of Molybdenum Content on Mechanical Properties of Sintered PM Steels Candido Ruas, Sylvain St-Laurent Quebec Metal Powders Limited Keywords: Molybdenum Steel Powder, Binder Treatment, Diffusion

More information

25 s/50g. The Effect of Compaction Pressure on Ancorsteel 85 HP with 0.5 w/o Zinc Stearate Green Density. Green Strength (MPa)

25 s/50g. The Effect of Compaction Pressure on Ancorsteel 85 HP with 0.5 w/o Zinc Stearate Green Density. Green Strength (MPa) 71-AS8HP-D-2 Pg 1 of 7 Ancorsteel 8 HP Typical Analysis and Properties Composition (weight %) (w/o) Ancorsteel 8 HP is a water atomized, prealloyed low-alloy steel powder for high performance applications.

More information

ABSTRACT INTRODUCTION

ABSTRACT INTRODUCTION EFFECT OF CARBON CONTENT AND POST-SINTERING COOLING RATE ON MECHANICAL PROPERTIES OF HIGH DENSITY SINTERED MATERIALS MADE FROM DIFFUSION-BONDED POWDERS L. Tremblay and F. Chagnon Quebec Metal Powders Limited

More information

Lean Hybrid Low-Alloy PM Molybdenum Steels

Lean Hybrid Low-Alloy PM Molybdenum Steels Lean Hybrid Low-Alloy PM Molybdenum Steels W. Brian James, Bruce Lindsley, Howard G. Rutz, and K.S. Narasimhan Hoeganaes Corporation, Cinnaminson, NJ, USA Abstract The volatility in the price of alloy

More information

DESIGNING LOW ALLOY STEEL POWDERS FOR SINTERHARDENING APPLICATIONS

DESIGNING LOW ALLOY STEEL POWDERS FOR SINTERHARDENING APPLICATIONS DESIGNING LOW ALLOY STEEL POWDERS FOR SINTERHARDENING APPLICATIONS F. Chagnon and Y. Trudel Quebec Metal Powders Limited Paper presented at the 1996 World Congress on Powder Metallurgy & Particulate Materials

More information

A Metallographic Investigation Into the Effect of Sintering on an FC-0205 Premix. Thomas F. Murphy, George B. Fillari, Gerard J.

A Metallographic Investigation Into the Effect of Sintering on an FC-0205 Premix. Thomas F. Murphy, George B. Fillari, Gerard J. A Metallographic Investigation Into the Effect of Sintering on an FC-0205 Premix Thomas F. Murphy, George B. Fillari, Gerard J. Golin Hoeganaes Corporation 1001 Taylors Lane Cinnaminson, NJ 08077 Abstract

More information

The Influence of Silicon on the Mechanical Properties and Hardenability of PM Steels

The Influence of Silicon on the Mechanical Properties and Hardenability of PM Steels The Influence of Silicon on the Mechanical Properties and Hardenability of PM Steels Chris Schade & Tom Murphy Hoeganaes Corporation Cinnaminson, NJ 08077 Alan Lawley & Roger Doherty Drexel University

More information

P/M High Strength Magnetic Alloys

P/M High Strength Magnetic Alloys P/M High Strength Magnetic Alloys Igor Gabrielov, Christopher Wilson, Timothy Weilbaker, & Arthur Barrows Borg Warner Corporation Livonia, Michigan Francis Hanejko & George Ellis Hoeganaes Corporation

More information

Heat treatment and effects of Cr and Ni in low alloy steel

Heat treatment and effects of Cr and Ni in low alloy steel Bull. Mater. Sci., Vol. 34, No. 7, December 2011, pp. 1439 1445. Indian Academy of Sciences. Heat treatment and effects of Cr and Ni in low alloy steel MOHAMMAD ABDUR RAZZAK Materials and Metallurgical

More information

Challenges in Processing of P/M Chromium Manganese Low-Alloy Steels

Challenges in Processing of P/M Chromium Manganese Low-Alloy Steels Challenges in Processing of P/M Chromium Manganese Low-Alloy Steels Robert J. Causton 1 and Bruce A. Lindsley 2 1 Hoeganaes Corporation, Buzau, Romania 2 Hoeganaes Corporation, Cinnaminson, NJ 08077, USA

More information

PROPERTIES OF DIFFUSION BONDED ALLOYS PROCESSED TO HIGH DENSITIES. F. G. Hanejko and H. G. Rutz Hoeganaes Corporation Riverton, NJ 08077

PROPERTIES OF DIFFUSION BONDED ALLOYS PROCESSED TO HIGH DENSITIES. F. G. Hanejko and H. G. Rutz Hoeganaes Corporation Riverton, NJ 08077 PROPERTIES OF DIFFUSION BONDED ALLOYS PROCESSED TO HIGH DENSITIES F. G. Hanejko and H. G. Rutz Hoeganaes Corporation Riverton, NJ 08077 U. Engström and B. Johansson Höganäs AB Höganäs, Sweden Presented

More information

Development of a Lubricant System for Improved Performance of Premixes

Development of a Lubricant System for Improved Performance of Premixes Development of a Lubricant System for Improved Performance of Premixes Kylan McQuaig, Chris Schade, Peter Sokolowski Hoeganaes Corporation Cinnaminson, NJ 08077 Abstract Particulate lubricants are commonly

More information

ADVANCED PROPERTIES OF HIGH DENSITY FERROUS POWDER METALLURGY MATERIALS

ADVANCED PROPERTIES OF HIGH DENSITY FERROUS POWDER METALLURGY MATERIALS ADVANCED PROPERTIES OF HIGH DENSITY FERROUS POWDER METALLURGY MATERIALS H. G. Rutz, A. J. Rawlings and T. M. Cimino HOEGANAES CORPORATION RIVERTON, NJ 08077 Presented at PM 2 TEC '95 May 14-17, 1995 -

More information

Heat Treatment of Steel Lab Report. Justin Lance 11/16/2011 Engineering 45 Lab Section 3 Troy Topping

Heat Treatment of Steel Lab Report. Justin Lance 11/16/2011 Engineering 45 Lab Section 3 Troy Topping Heat Treatment of Steel Lab Report Justin Lance justalance@gmail.com 11/16/2011 Engineering 45 Lab Section 3 Troy Topping troytopping@gmail.com ABSTRACT We observed how the properties of 4140 steel vary

More information

Machinability Enhancement of PM Stainless Steels Using Easy-Machinable Stainless Steel Powder. Bo Hu, Roland T. Warzel III, Sydney Luk

Machinability Enhancement of PM Stainless Steels Using Easy-Machinable Stainless Steel Powder. Bo Hu, Roland T. Warzel III, Sydney Luk Machinability Enhancement of PM Stainless Steels Using Easy-Machinable Stainless Steel Powder Bo Hu, Roland T. Warzel III, Sydney Luk North American Höganäs, Hollsopple, PA 15935 USA ABSTRACT PM stainless

More information

Electron Beam Melted (EBM) Co-Cr-Mo Alloy for Orthopaedic Implant Applications Abstract Introduction The Electron Beam Melting Process

Electron Beam Melted (EBM) Co-Cr-Mo Alloy for Orthopaedic Implant Applications Abstract Introduction The Electron Beam Melting Process Electron Beam Melted (EBM) Co-Cr-Mo Alloy for Orthopaedic Implant Applications R.S. Kircher, A.M. Christensen, K.W. Wurth Medical Modeling, Inc., Golden, CO 80401 Abstract The Electron Beam Melting (EBM)

More information

Processing of Ferro-Phosphorus-Containing Mixes in Low Hydrogen Atmospheres

Processing of Ferro-Phosphorus-Containing Mixes in Low Hydrogen Atmospheres Processing of Ferro-Phosphorus-Containing Mixes in Low Hydrogen Atmospheres K.S. Narasimhan, D.J. Kasputis & G. Fillari Hoeganaes Corporation & J. C. Lynn DaimlerChrysler Corporation Presented at PM 2

More information

Heat Treating Basics-Steels

Heat Treating Basics-Steels Heat Treating Basics-Steels Semih Genculu, P.E. Steel is the most important engineering material as it combines strength, ease of fabrication, and a wide range of properties along with relatively low cost.

More information

ALUMINUM POWDER METALLURGY

ALUMINUM POWDER METALLURGY ALUMINUM POWDER METALLURGY Increased demand for light weight components, primarily driven by the need to reduce energy consumption in a variety of societal and structural components, has led to increased

More information

FATIGUE LIFE OF FORGED, HARDENED AND TEMPERED CARBON STEEL WITH AND WITOUT NORMALIZING

FATIGUE LIFE OF FORGED, HARDENED AND TEMPERED CARBON STEEL WITH AND WITOUT NORMALIZING FATIGUE LIFE OF FORGED, HARDENED AND TEMPERED CARBON STEEL WITH AND WITOUT NORMALIZING A. Zabett 1*, R. Irankhah 1, M. Miri Disfani 1, I. Zohur Karimi 1, M. Hashemi 2 1- Ferdowsi University of Mashad,

More information

Engineering Materials

Engineering Materials Engineering Materials Heat Treatments of Ferrous Alloys Annealing Processes The term annealing refers to a heat treatment in which a material is exposed to an elevated temperature for an extended time

More information

Surface treatment evaluation of induction hardened and tempered 1045 steel

Surface treatment evaluation of induction hardened and tempered 1045 steel University of Wollongong Research Online Faculty of Engineering and Information Sciences - Papers: Part A Faculty of Engineering and Information Sciences 2014 Surface treatment evaluation of induction

More information

This article appeared in a journal published by Elsevier. The attached copy is furnished to the author for internal non-commercial research and

This article appeared in a journal published by Elsevier. The attached copy is furnished to the author for internal non-commercial research and This article appeared in a journal published by Elsevier. The attached copy is furnished to the author for internal non-commercial research and education use, including for instruction at the authors institution

More information

Experiment E: Martensitic Transformations

Experiment E: Martensitic Transformations Experiment E: Martensitic Transformations Introduction: The purpose of this experiment is to introduce students to a family of phase transformations which occur by shear rather than diffusion. In metals,

More information

Phase Transformations in Metals Tuesday, December 24, 2013 Dr. Mohammad Suliman Abuhaiba, PE 1

Phase Transformations in Metals Tuesday, December 24, 2013 Dr. Mohammad Suliman Abuhaiba, PE 1 Ferrite - BCC Martensite - BCT Fe 3 C (cementite)- orthorhombic Austenite - FCC Chapter 10 Phase Transformations in Metals Tuesday, December 24, 2013 Dr. Mohammad Suliman Abuhaiba, PE 1 Why do we study

More information

EXPERIMENT 6 HEAT TREATMENT OF STEEL

EXPERIMENT 6 HEAT TREATMENT OF STEEL EXPERIMENT 6 HEAT TREATMENT OF STEEL Purpose The purposes of this experiment are to: Investigate the processes of heat treating of steel Study hardness testing and its limits Examine microstructures of

More information

Precipitation Hardening. Outline. Precipitation Hardening. Precipitation Hardening

Precipitation Hardening. Outline. Precipitation Hardening. Precipitation Hardening Outline Dispersion Strengthening Mechanical Properties of Steel Effect of Pearlite Particles impede dislocations. Things that slow down/hinder/impede dislocation movement will increase, y and TS And also

More information

Optimized Carburized Steel Fatigue Performance as Assessed with Gear and Modified Brugger Fatigue Tests

Optimized Carburized Steel Fatigue Performance as Assessed with Gear and Modified Brugger Fatigue Tests 22-1-13 Optimized Carburized Steel Fatigue Performance as Assessed with Gear and Modified Brugger Fatigue Tests Copyright 22 Society of Automotive Engineers, Inc. Jason J. Spice and David K. Matlock Colorado

More information

DEVELOPMENT OF STAINLESS STEEL AND HIGH ALLOY POWDERS. Christopher T. Schade Hoeganaes Corporation, Cinnaminson, NJ

DEVELOPMENT OF STAINLESS STEEL AND HIGH ALLOY POWDERS. Christopher T. Schade Hoeganaes Corporation, Cinnaminson, NJ DEVELOPMENT OF STAINLESS STEEL AND HIGH ALLOY POWDERS ABSTRACT Christopher T. Schade Hoeganaes Corporation, Cinnaminson, NJ John Schaberl ANCOR Specialties, Ridgway, PA Advanced melting technology is now

More information

Maximizing the Value and Performance of Chromium, Manganese, and Silicon Containing PM Steels

Maximizing the Value and Performance of Chromium, Manganese, and Silicon Containing PM Steels Maximizing the Value and Performance of Chromium, Manganese, and Silicon Containing PM Steels Michael L. Marucci & Bruce Lindsley - Hoeganaes Corporation USA 31. Hagern Symposium Outline Introduction &

More information

The Effect of Heat Treatment Atmosphere on Hardening of Surface Region of H13 Tool Steel

The Effect of Heat Treatment Atmosphere on Hardening of Surface Region of H13 Tool Steel Journal of Materials Science and Chemical Engineering, 2013, 1, 20-29 Published Online November 2013 (http://www.scirp.org/journal/msce) http://dx.doi.org/10.4236/msce.2013.16004 The Effect of Heat Treatment

More information

Alloys SUPER SQUARE

Alloys SUPER SQUARE Alloys ETD 150...8-2 ETD 150 Rounds...8-2 AISI 4140/41L40 - Annealed...8-3 AISI 4140 - Annealed Flats And Squares... 8-4 thru 8-5 AISI 4140 - Annealed Rounds... 8-5 thru 8-6 AISI 4140 Rounds HR Q&T...8-7

More information

Hot Forging Behaviour of Sintered AISI 8720 P/M Steels

Hot Forging Behaviour of Sintered AISI 8720 P/M Steels Hot Forging Behaviour of Sintered AISI 8720 P/M Steels 1 L. Arulmani, 2 K.S. Pandey 1 Dept. of Mechanical Engineering, R.R. Institute of Technology, Bangalore, India. 2 Department of Metallurgical and

More information

Resource Guide. Section 3: Ductile Iron

Resource Guide. Section 3: Ductile Iron Resource Guide Section 3: Ductile Iron Section 3 Ductile Iron Description of Grades... 3-3 65-45-12 Ferritic... 3-4 80-55-06 Partially Pearlitic... 3-6 100-70-02 Pearlitic... 3-8 4512 HRDS Heat Resistant...

More information

Progress in Friction Stir Welding High Temperature Materials

Progress in Friction Stir Welding High Temperature Materials Progress in Friction Stir Welding High Temperature Materials Carl D. Sorensen Brigham Young University BRIGHAM YOUNG UNIVERSITY Agenda History Tool Materials Weld Metal Properties Materials Welded With

More information

Effect of Precipitation Hardening on Microstructural Characteristics of 15-5 Ph Steel

Effect of Precipitation Hardening on Microstructural Characteristics of 15-5 Ph Steel International Journal of Engineering Research and Development e-issn: 2278-067X, p-issn: 2278-800X, www.ijerd.com Volume 9, Issue 1 (November 2013), PP. 22-26 Effect of Precipitation Hardening on Microstructural

More information

AISI A2 Cold work tool steel

AISI A2 Cold work tool steel T OOL STEEL FACTS AISI A2 Cold work tool steel Great Tooling Starts Here! General AISI A2 is an air- or oil hardening chromiummolybdenum-vanadium alloyed tool steel characterized by: Good machinability

More information

SINTERABILITY OF HIGH-SPEED STEELS M2, M3/2 AND T15

SINTERABILITY OF HIGH-SPEED STEELS M2, M3/2 AND T15 SINTERABILITY OF HIGH-SPEED STEELS, M3/2 AND Romário Mauricio Urbanetto Nogueira CEFET/PR UNED/MD romarioun@ig.com.br César Edil da Costa DEM-CCT/UDESC edil@joinville.udesc.br Keywords high speed steels,

More information

POLITECNICO DI TORINO Repository ISTITUZIONALE

POLITECNICO DI TORINO Repository ISTITUZIONALE POLITECNICO DI TORINO Repository ISTITUZIONALE Relationships between tensile and fracture mechanics properties and fatigue properties of large plastic mold steel Original Relationships between tensile

More information

Validation of VrHeatTreat Software for Heat Treatment and Carburization

Validation of VrHeatTreat Software for Heat Treatment and Carburization Validation of VrHeatTreat Software for Heat Treatment and Carburization John Goldak a, Jianguo Zhou a, Stanislav Tchernov a, Dan Downey a, a Goldak Technologies Inc, Ottawa, Canada December 12, 2007 1

More information

An Assessment of Mechanical Properties of Medium Carbon Steel under Different Quenching Media

An Assessment of Mechanical Properties of Medium Carbon Steel under Different Quenching Media An Assessment of Mechanical Properties of Medium Carbon Steel under Different Quenching Media M. B. Ndaliman Department of Mechanical Engineering, Federal University of Technology Minna, Nigeria Abstract

More information

MSE-226 Engineering Materials

MSE-226 Engineering Materials MSE-226 Engineering Materials Lecture-7 ALLOY STEELS Tool Steels TYPES of FERROUS ALLOYS FERROUS ALLOYS Plain Carbon Steels Alloy Steels Cast Irons - Low carbon Steel - Medium carbon steel - High carbon

More information

Lecture 31-36: Questions:

Lecture 31-36: Questions: Lecture 31-36: Heat treatment of steel: T-T-T diagram, Pearlitic, Martensitic & Bainitic transformation, effect of alloy elements on phase diagram & TTT diagram, CCT diagram, Annealing, normalizing, hardening

More information

Effect of Heat Treatment on Microstructure and Mechanical Properties of Medium Carbon Steel

Effect of Heat Treatment on Microstructure and Mechanical Properties of Medium Carbon Steel International Journal of Engineering Research and Development ISSN: 2278-067X, Volume 2, Issue 1 (July 2012), PP. 07-13 www.ijerd.com Effect of Heat Treatment on Microstructure and Mechanical Properties

More information

Injection Moulding and Heat Treatment of Ni-Cr-Si-B Alloy Powder

Injection Moulding and Heat Treatment of Ni-Cr-Si-B Alloy Powder Injection Moulding and Heat Treatment of Ni-Cr-Si-B Alloy Powder M. Y. Anwar 1, M. Ajmal 1, M. T. Z. Butt 2 and M. Zubair 1 1. Department of Met. & Materials Engineering, UET Lahore. 2. Faculty of Engineering

More information

Processing and Properties of MIM AISI 4605 via Master Alloy Routes

Processing and Properties of MIM AISI 4605 via Master Alloy Routes Processing and Properties of MIM AISI 4605 via Master Alloy Routes Andrew J Coleman, Keith Murray, Martin Kearns, Toby A. Tingskog*, Bob Sanford** & Erainy Gonzalez** Sandvik Osprey Ltd., Red Jacket Works,

More information

ME 216 Engineering Materials II

ME 216 Engineering Materials II ME 216 Engineering Materials II Chapter 12 Heat Treatment (Part II) Mechanical Engineering University of Gaziantep Dr. A. Tolga Bozdana Assistant Professor Hardenability It is the ability of steel to harden

More information

ISO INTERNATIONAL STANDARD

ISO INTERNATIONAL STANDARD INTERNATIONAL STANDARD ISO 898-5 Second edition 1998-08-01 Mechanical properties of fasteners made of carbon steel and alloy steel Part 5: Set screws and similar threaded fasteners not under tensile stresses

More information

Heat Treatment of Steels : Metallurgical Principle

Heat Treatment of Steels : Metallurgical Principle Heat Treatment of Steels : Metallurgical Principle Outlines: Fe ad Fe-Fe 3 C system Phases and Microstructure Fe-Fe 3 C Phase Diaram General Physical and Mechanical Properties of each Microstructure Usanee

More information

Evaluation of Mechanical Properties of Medium Carbon Low Alloy Forged Steels by Polymer Quenching

Evaluation of Mechanical Properties of Medium Carbon Low Alloy Forged Steels by Polymer Quenching IOP Conference Series: Materials Science and Engineering PAPER OPEN ACCESS Evaluation of Mechanical Properties of Medium Carbon Low Alloy Forged Steels by Polymer Quenching To cite this article: B R Chandan

More information

Special Steels for Precise Die and Mold

Special Steels for Precise Die and Mold DURO for Cold Work Special Steels for Precise Die and Mold R For Cold Work High Toughness Grades High Wear Resistance Grade DURO-Created by NACHI s original technology Steels with superior balance of toughness

More information

Mat E 272 Lecture 19: Cast Irons

Mat E 272 Lecture 19: Cast Irons Mat E 272 Lecture 19: Cast Irons November 8, 2001 Introduction: One reason steels and cast iron alloys find such wide-ranging applications and dominate industrial metal production is because of how they

More information

Torsional Fatigue Performance of Induction Hardened 1045 and 10V45 Steels

Torsional Fatigue Performance of Induction Hardened 1045 and 10V45 Steels Proceedings of the 28th ASM Heat Treating Society Conference October 20 22, 2015, Detroit, Michigan, USA Copyright 2015 ASM International All rights reserved asminternational.org Torsional Fatigue Performance

More information

PRELIMINARY INVESTIGATIONS OF LOW-NICKEL STAINLESS STEELS FOR STRUCTURAL APPLICATIONS

PRELIMINARY INVESTIGATIONS OF LOW-NICKEL STAINLESS STEELS FOR STRUCTURAL APPLICATIONS PRELIMINARY INVESTIGATIONS OF LOW-NICKEL STAINLESS STEELS FOR STRUCTURAL APPLICATIONS J. Kerr and R. Paton Mintek, Private Bag X3015, Randburg. 2125. South Africa. E-mail: jonathank@mintek.co.za ABSTRACT

More information

QRO 90 SUPREME Hot work tool steel

QRO 90 SUPREME Hot work tool steel T O O L S T E E L F A C T S QRO 90 Hot work tool steel Great Tooling Starts Here! Cover photo: Bo Dahlgren This information is based on our present state of knowledge and is intended to provide general

More information

Microstructures of Mild Steel Spring after Heat Treatment.

Microstructures of Mild Steel Spring after Heat Treatment. Microstructures of Mild Steel Spring after Heat Treatment. O.R. Adetunji, Ph.D.*; S.I. Kuye, Ph.D.; and M.J. Alao, B.Eng. Mechanical Engineering Department, College of Engineering, Federal University of

More information

PROPERTIES AND MICROSTRUCTURES OF SINTERED STAINLESS STEEL PREPARED FROM 304L AND 410L POWDERS

PROPERTIES AND MICROSTRUCTURES OF SINTERED STAINLESS STEEL PREPARED FROM 304L AND 410L POWDERS PROPERTIES AND MICROSTRUCTURES OF SINTERED STAINLESS STEEL PREPARED FROM 304L AND 410L POWDERS B. Vetayanugul, N. Tosangthum, R. Krataitong, M. Morakotjinda, A. Daraphan, T. Yotkaew, O. Coovattanachai

More information

Uddeholm Formvar. FORMVAR is a trade mark registered in the European Union

Uddeholm Formvar. FORMVAR is a trade mark registered in the European Union Uddeholm Formvar FORMVAR is a trade mark registered in the European Union UDDEHOLMS AB No part of this publication may be reproduced or transmitted for commercial purposes without permission of the copyright

More information

Resource Guide. Section 2: Gray Iron

Resource Guide. Section 2: Gray Iron Resource Guide Section 2: Gray Iron Section 2 Gray Iron Description of Grades... 2-3 G1 Partially Ferritic... 2-4 G1A Ferritic... 2-6 G2 Highly Pearlitic... 2-8 G2A Highly Perlitic High-Strength... 2-10

More information

The ATI 17-4 precipitation hardening stainless steel (S17400) is covered by the following wrought product specifications.

The ATI 17-4 precipitation hardening stainless steel (S17400) is covered by the following wrought product specifications. ATI 17-4 Precipitation Hardening Stainless Steel (UNS S17400) INTRODUCTION ATI 17-4 precipitation hardening stainless steel (S17400), Type 630, is a chromium-nickel-copper precipitation hardening stainless

More information

PROPERTIES OF HEAT TREATED P/M ALLOY STEELS. Robert J. Causton, Jack A. Hamill, Jr. Hoeganaes Corporation, Riverton, NJ 08077

PROPERTIES OF HEAT TREATED P/M ALLOY STEELS. Robert J. Causton, Jack A. Hamill, Jr. Hoeganaes Corporation, Riverton, NJ 08077 PROPERTIES OF HEAT TREATED P/M ALLOY STEELS Robert J. Causton, Jack A. Hamill, Jr. Hoeganaes Corporation, Riverton, NJ 08077 ABSTRACT Suresh O. Shah Remington Powder Metal Products, Hazen, AR 72064 Further

More information

It is our intent to always maintain the highest level of quality metals obtainable from our mill sources.

It is our intent to always maintain the highest level of quality metals obtainable from our mill sources. This stock catalog contains the sizes, weights and descriptions of all standard Steel, Brass, Bronze and Dura-Bar Cast Iron items that are available from stock for immediate delivery. However, new items

More information

LAB IV. Effects of Heat Treatment on Steel, Aluminum and Brass Alloys - Microstructure and Properties

LAB IV. Effects of Heat Treatment on Steel, Aluminum and Brass Alloys - Microstructure and Properties LAB IV Effects of Heat Treatment on Steel, Aluminum and Brass Alloys - Microstructure and Properties PRE LAB PREPARATION (required!) 1. Using the ASM metal handbooks or other resources find and print/copy

More information

Predicting Distortion and Residual Stress in a Vacuum Carburized and Gas Quenched Steel Coupon

Predicting Distortion and Residual Stress in a Vacuum Carburized and Gas Quenched Steel Coupon Predicting Distortion and Residual Stress in a Vacuum Carburized and Gas Quenched Steel Coupon A. Freborg, B. Ferguson and Z. Li Deformation Control Technology, Cleveland, Ohio USA Keywords: Heat Treatment

More information

Impact 7 Steel. A Durable, Dependable Steel Solution For Harsh Environments. Technical Data. Alloy Description. Alloy Type. Typical Applications

Impact 7 Steel. A Durable, Dependable Steel Solution For Harsh Environments. Technical Data. Alloy Description. Alloy Type. Typical Applications Impact 7 Steel Technical Data A Durable, Dependable Steel Solution For Harsh Environments Alloy Description As a world leader in steel manufacturing, TimkenSteel specializes in providing custom steel solutions

More information

Resource Guide. Section 4: Ni-Resist

Resource Guide. Section 4: Ni-Resist Resource Guide Section 4: Ni-Resist Section 4 Ni-Resist Description of Grades... 4-3 201 (Type 1) Ni-Resist... 4-4 202 (Type 2) Ni-Resist... 4-6 Stock Listings... 4-8 4-2 Ni-Resist Description of Grades

More information

Mechanical Properties of Electron Beam Welded Spheroidal Graphite Cast Iron and Mild Steel Welded Joints*

Mechanical Properties of Electron Beam Welded Spheroidal Graphite Cast Iron and Mild Steel Welded Joints* Materials Transactions, Vol. 52, No. 10 (2011) pp. 1920 to 1925 #2011 Japan Foundary Engineering Society Mechanical Properties of Electron Beam Welded Spheroidal Graphite Cast Iron and Mild Steel Welded

More information

Institutional repository of Jönköping University

Institutional repository of Jönköping University Institutional repository of Jönköping University http://www.publ.hj.se/diva This is an author produced version of a paper published in Metallurgical and Materials Transactions A. This paper has been peer-reviewed

More information

With Dura-Bar you will be able to:

With Dura-Bar you will be able to: Dura-Bar Stock List Dura-Bar is an engineered iron designed to meet our customers most critical requirements. It is manufactured to strict process controls that provide world-class quality and uncompromising

More information

QRO 90 SUPREME. Hot work tool steel

QRO 90 SUPREME. Hot work tool steel QRO 90 SUPREME Hot work tool steel This information is based on our present state of knowledge and is intended to provide general notes on our products and their uses. It should not therefore be construed

More information

Cast steel: Group of ASTM standards for steel castings and forgings

Cast steel: Group of ASTM standards for steel castings and forgings Cast steel: Group of ASTM standards for steel castings and forgings Abstract: This group of ASTM specifications covers standard properties of steel and iron castings and forgings for valves, flanges, fittings,

More information

Investigation of Stress Relief Heat treatment on Carbon Steel AISI 1045 Weld

Investigation of Stress Relief Heat treatment on Carbon Steel AISI 1045 Weld Proceedings of the 5th IIAE International Conference on Industrial Application Engineering 27 Investigation of Stress Relief Heat treatment on Carbon Steel AISI 5 Weld Prachya Peasura a,* a,* Department

More information

Evaluation of Khaya Seed Oil (Mahogany Oil) as Quenchant in the Hardening Process of Plain Carbon Steel.

Evaluation of Khaya Seed Oil (Mahogany Oil) as Quenchant in the Hardening Process of Plain Carbon Steel. Evaluation of Khaya Seed Oil (Mahogany Oil) as Quenchant in the Hardening Process of Plain Carbon Steel. Prof. S.B. Hassan 1 and V.S. Aigbodion, Ph.D. 2 * 1 Department of Metallurgical and Materials engineering,

More information

CLASSIFICATION OF STEELS

CLASSIFICATION OF STEELS 7 Alloy Steels CLASSIFICATION OF STEELS low carbon

More information

AEROSPACE MATERIAL SPECIFICATION

AEROSPACE MATERIAL SPECIFICATION AEROSPACE MATERIAL SPECIFICATION AMS 6414K Issued JAN 1964 Revised FEB 2007 Superseding AMS 6414J Steel, Bars, Forgings, and Tubing 0.80Cr - 1.8Ni - 0.25Mo (0.38-0.43C) (SAE 4340) Vacuum Consumable Electrode

More information

11.3 The alloying elements in tool steels (e.g., Cr, V, W, and Mo) combine with the carbon to form very hard and wear-resistant carbide compounds.

11.3 The alloying elements in tool steels (e.g., Cr, V, W, and Mo) combine with the carbon to form very hard and wear-resistant carbide compounds. 11-2 11.2 (a) Ferrous alloys are used extensively because: (1) Iron ores exist in abundant quantities. (2) Economical extraction, refining, and fabrication techniques are available. (3) The alloys may

More information

How to tackle fatigue failures

How to tackle fatigue failures How to tackle fatigue failures The number of cycles that a metal can endure before it breaks is a complex function of the static and cyclic stress values, the alloy, heat-treatment and surface condition

More information

Effect of Alloying Elements and Processing Parameters on Mechanical Properties of Austempered Ductile Iron

Effect of Alloying Elements and Processing Parameters on Mechanical Properties of Austempered Ductile Iron Journal of Materials and Metallurgical Engineering Effect of Alloying Elements and Processing Parameters on Mechanical Properties of Austempered Ductile Iron Amar Kumar Das 1, Jyoti Prakash Dhal 2 *, Ranjit

More information

INTRODUCTION. Think HSS

INTRODUCTION. Think HSS INTRODUCTION Think HSS SUMMARY METALLURGY 2 Excellent strength 3 A super sharp edge 4 Safe and reliable tools Alloy elements 6 The influence of alloy elements 7 Standard compositions of HSS 8 The HSS-PM

More information

Characterization of Titanium Alloy Friction Stir Butt-Welds TIMET 54M, ATI 425 and BOATI Standard Grain

Characterization of Titanium Alloy Friction Stir Butt-Welds TIMET 54M, ATI 425 and BOATI Standard Grain Characterization of Titanium Alloy Friction Stir Butt-Welds TIMET 54M, ATI 425 and BOATI Standard Grain A. Cantrell, K. Gangwar, and M. Ramulu University of Washington Dan Sanders The Boeing Company 7th

More information

Grade Etch color C Si Mn Cr Mo P S Ni. 416 Dark 0,22 <1 <1,25 13 <0,6 <0,06 0, Bright 0,23 <1 < <0,04 0,03 3

Grade Etch color C Si Mn Cr Mo P S Ni. 416 Dark 0,22 <1 <1,25 13 <0,6 <0,06 0, Bright 0,23 <1 < <0,04 0,03 3 Stainless damascus barrel steel for rifles Damasteel s stainless Barrel steel is a RSP (Rapid Solidification Powder) based steel with AISI 416/431 as the constituent alloys. The steel is developed and

More information

ATI Datalloy HP TM Alloy

ATI Datalloy HP TM Alloy ATI Datalloy HP TM Alloy UNS N08830 INTRODUCTION ATI Datalloy HP TM alloy is a Ni-Cr-Mo-Fe non-magnetic high strength alloy with exceptional pitting and crevice corrosion resistance, while maintaining

More information

MICROMECHANISMS OF CLEAVAGE FRACTURE IN THE HAZ OF C-MN COMMERCIAL STEEL WELD

MICROMECHANISMS OF CLEAVAGE FRACTURE IN THE HAZ OF C-MN COMMERCIAL STEEL WELD MICROMECHANISMS OF CLEAVAGE FRACTURE IN THE HAZ OF C-MN COMMERCIAL STEEL WELD C. Moya-Gutiérrez, A. Martín-Meizoso, I. Ocaña-Arizcorreta CEIT, Centro de Estudios e Investigaciones Técnicas de Guipúzcoa

More information

Phase Investigation of Austempered Ductile Iron

Phase Investigation of Austempered Ductile Iron Orissa Journal of Physics ISSN 0974-8202 Orissa Physical Society Vol. 19, No.1 February 2012 pp. 73-80 Phase Investigation of Austempered Ductile Iron S K SWAIN 1, R K PANDA 2, J P DHAL 3, S C MISHRA 4

More information

E-BRITE E-BRITE. Technical Data Sheet. Stainless Steel: Superferritic GENERAL PROPERTIES PLANAR SOLID OXIDE FUEL CELLS CHEMICAL COMPOSITION

E-BRITE E-BRITE. Technical Data Sheet. Stainless Steel: Superferritic GENERAL PROPERTIES PLANAR SOLID OXIDE FUEL CELLS CHEMICAL COMPOSITION E-BRITE Stainless Steel: Superferritic (UNS 44627, ASTM Type XM-27) GENERAL PROPERTIES E-BRITE alloy is a high purity ferritic stainless steel which combines excellent resistance to corrosion and oxidation

More information

VDM Alloy 80 A Nicrofer 7520 Ti

VDM Alloy 80 A Nicrofer 7520 Ti VDM Alloy 80 A Nicrofer 7520 Ti Material Data Sheet No. 4048 February 2017 February 2017 VDM Alloy 80 A 2 VDM Alloy 80 A Nicrofer 7520 Ti VDM Alloy 80 A is a nickel-chromium alloy that can be age-hardened.

More information

Ferrous Alloys. Steels

Ferrous Alloys. Steels Ferrous Alloys Ferrous alloys those of which iron is the prime constituent are produced in larger quantities than any other metal type. They are especially important as engineering construction materials.

More information

HAYNES 244 alloy a new 760 C capable low thermal expansion alloy

HAYNES 244 alloy a new 760 C capable low thermal expansion alloy MATEC Web of Conferences 14, 17004 (2014) DOI: 10.1051/matecconf/20141417004 c Owned by the authors, published by EDP Sciences, 2014 HAYNES 244 alloy a new 760 C capable low thermal expansion alloy Michael

More information

Correlation of Hardness Values to Tensile Strength

Correlation of Hardness Values to Tensile Strength Correlation of Hardness Values to Tensile Strength Semih Genculu, P.E. Various procedures and approaches are utilized to determine if a given material is suitable for a certain application. The material

More information

ATI ATI 2205 Alloy (UNS S31803 and S32205) Duplex Stainless Steel. Technical Data Sheet

ATI ATI 2205 Alloy (UNS S31803 and S32205) Duplex Stainless Steel. Technical Data Sheet Alloy (UNS S31803 and S32205) Duplex Stainless Steel GENERAL PROPERTIES alloy (UNS S31803 and/or S32205) is a nitrogenenhanced duplex stainless steel alloy. The nitrogen serves to significantly improve

More information

Grain Size of Commercial High Speed Steel

Grain Size of Commercial High Speed Steel Grain Size of Commercial High Speed Steel Rejane A. Nogueira, Oscar O. Araújo Filho, Leonardo F. M. Souza, João F. Liberati, Lucio Salgado, Francisco Ambrozio Filho (*) (*) Instituto de Pesquisas Energéticas

More information

Mechanical behavior of crystalline materials - Stress Types and Tensile Behaviour

Mechanical behavior of crystalline materials - Stress Types and Tensile Behaviour Mechanical behavior of crystalline materials - Stress Types and Tensile Behaviour 3.1 Introduction Engineering materials are often found to posses good mechanical properties so then they are suitable for

More information