EP2976437A1 - Air-hardenable bainitic steel with enhanced material characteristics - Google Patents
Air-hardenable bainitic steel with enhanced material characteristicsInfo
- Publication number
- EP2976437A1 EP2976437A1 EP14771156.8A EP14771156A EP2976437A1 EP 2976437 A1 EP2976437 A1 EP 2976437A1 EP 14771156 A EP14771156 A EP 14771156A EP 2976437 A1 EP2976437 A1 EP 2976437A1
- Authority
- EP
- European Patent Office
- Prior art keywords
- steel part
- air cooling
- controlled air
- steel
- hardness
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Granted
Links
- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 102
- 239000010959 steel Substances 0.000 title claims abstract description 102
- 239000000463 material Substances 0.000 title description 10
- 238000001816 cooling Methods 0.000 claims abstract description 61
- 238000000034 method Methods 0.000 claims abstract description 38
- 238000010438 heat treatment Methods 0.000 claims abstract description 33
- 238000005242 forging Methods 0.000 claims abstract description 29
- 239000000203 mixture Substances 0.000 claims abstract description 27
- 230000006698 induction Effects 0.000 claims abstract description 14
- 239000012535 impurity Substances 0.000 claims abstract description 7
- 238000009863 impact test Methods 0.000 claims description 2
- 238000010791 quenching Methods 0.000 abstract description 23
- 230000000171 quenching effect Effects 0.000 abstract description 21
- 238000005496 tempering Methods 0.000 abstract description 16
- 238000003754 machining Methods 0.000 abstract description 10
- 229910052799 carbon Inorganic materials 0.000 abstract description 8
- 229910052719 titanium Inorganic materials 0.000 abstract description 6
- 229910052804 chromium Inorganic materials 0.000 abstract description 4
- 229910052748 manganese Inorganic materials 0.000 abstract description 4
- 229910052757 nitrogen Inorganic materials 0.000 abstract description 4
- 229910052750 molybdenum Inorganic materials 0.000 abstract description 3
- 229910052796 boron Inorganic materials 0.000 abstract description 2
- 229910052710 silicon Inorganic materials 0.000 abstract description 2
- 229910001563 bainite Inorganic materials 0.000 description 26
- 230000008569 process Effects 0.000 description 20
- 238000003303 reheating Methods 0.000 description 12
- 229910000742 Microalloyed steel Inorganic materials 0.000 description 11
- 229910000859 α-Fe Inorganic materials 0.000 description 11
- 229910000734 martensite Inorganic materials 0.000 description 10
- 229910001562 pearlite Inorganic materials 0.000 description 9
- 239000010936 titanium Substances 0.000 description 9
- 238000010586 diagram Methods 0.000 description 8
- 239000011572 manganese Substances 0.000 description 8
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 7
- 229910001566 austenite Inorganic materials 0.000 description 7
- 239000011651 chromium Substances 0.000 description 7
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 7
- 230000009466 transformation Effects 0.000 description 7
- 229910000851 Alloy steel Inorganic materials 0.000 description 6
- 238000005275 alloying Methods 0.000 description 6
- 230000015572 biosynthetic process Effects 0.000 description 6
- 238000005096 rolling process Methods 0.000 description 6
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 4
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 4
- 239000000047 product Substances 0.000 description 4
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 description 3
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 3
- 229910001567 cementite Inorganic materials 0.000 description 3
- 238000004519 manufacturing process Methods 0.000 description 3
- 150000001247 metal acetylides Chemical class 0.000 description 3
- 238000012545 processing Methods 0.000 description 3
- 230000000717 retained effect Effects 0.000 description 3
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 description 2
- 229910045601 alloy Inorganic materials 0.000 description 2
- 239000000956 alloy Substances 0.000 description 2
- 238000005336 cracking Methods 0.000 description 2
- 229910052742 iron Inorganic materials 0.000 description 2
- KSOKAHYVTMZFBJ-UHFFFAOYSA-N iron;methane Chemical compound C.[Fe].[Fe].[Fe] KSOKAHYVTMZFBJ-UHFFFAOYSA-N 0.000 description 2
- 238000012423 maintenance Methods 0.000 description 2
- 239000011733 molybdenum Substances 0.000 description 2
- 239000003921 oil Substances 0.000 description 2
- 239000002244 precipitate Substances 0.000 description 2
- 239000000126 substance Substances 0.000 description 2
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 2
- ZOXJGFHDIHLPTG-UHFFFAOYSA-N Boron Chemical compound [B] ZOXJGFHDIHLPTG-UHFFFAOYSA-N 0.000 description 1
- OAICVXFJPJFONN-UHFFFAOYSA-N Phosphorus Chemical compound [P] OAICVXFJPJFONN-UHFFFAOYSA-N 0.000 description 1
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 description 1
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 description 1
- 239000005864 Sulphur Substances 0.000 description 1
- 238000005452 bending Methods 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 230000008859 change Effects 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 238000000354 decomposition reaction Methods 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- 239000012530 fluid Substances 0.000 description 1
- 239000004615 ingredient Substances 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 229910052698 phosphorus Inorganic materials 0.000 description 1
- 239000011574 phosphorus Substances 0.000 description 1
- 238000004881 precipitation hardening Methods 0.000 description 1
- 238000005204 segregation Methods 0.000 description 1
- 239000010703 silicon Substances 0.000 description 1
- 239000007921 spray Substances 0.000 description 1
- 238000009628 steelmaking Methods 0.000 description 1
- LEONUFNNVUYDNQ-UHFFFAOYSA-N vanadium atom Chemical compound [V] LEONUFNNVUYDNQ-UHFFFAOYSA-N 0.000 description 1
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/18—Hardening; Quenching with or without subsequent tempering
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/18—Hardening; Quenching with or without subsequent tempering
- C21D1/19—Hardening; Quenching with or without subsequent tempering by interrupted quenching
- C21D1/20—Isothermal quenching, e.g. bainitic hardening
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/002—Heat treatment of ferrous alloys containing Cr
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/005—Heat treatment of ferrous alloys containing Mn
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/008—Heat treatment of ferrous alloys containing Si
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D7/00—Modifying the physical properties of iron or steel by deformation
- C21D7/13—Modifying the physical properties of iron or steel by deformation by hot working
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/005—Modifying the physical properties by deformation combined with, or followed by, heat treatment of ferrous alloys
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/34—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of silicon
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/002—Bainite
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2261/00—Machining or cutting being involved
Definitions
- the present disclosure relates generally to an air-hardenable bainitic steel and, more particularly, to an air-hardenable bainitic steel with enhanced material characteristics.
- Structural components for machinery such as track links used on the undercarriage of track-type earth moving machines, are required to have material characteristics that include good yield strength, good wear resistance, good toughness, and good rolling contact fatigue resistance.
- Track links used on the tracks of a track-type machine such as a bulldozer or other earth moving equipment are well known in the industry.
- a track link typically has a lower portion, or the body of the link, and an upper portion, or the rail portion of the link. It is important that the rail portion of the track link have high surface hardness, whereas the body portion of the track link can have lower surface hardness for increased machinability. A high surface hardness in the rail portion is necessary because the rail portion is subjected to severe wear and spallation from continuous contact with track rollers.
- a lower surface hardness in the body portion of the track link allows holes for bushings to be more easily machined into the body portion.
- the lower surface hardness of the body portion of the track link also allows for a press fit between a bushing and the hole in the track link body without creating excessive residual stresses.
- the manufacturing processes for obtaining the desired material characteristics in a track link or other structural component have typically included hot forging the component from a steel billet, followed by cooling, reheating to austenization temperatures, quenching, and tempering. These heat treatment processes may then be followed by additional heating of at least select portions of the component, quenching again, and tempering again before the final machining.
- Processing of a track link includes first heating a steel part to approximately 1150 - 1350 degrees C to bring the material to an austenite phase field, and then hot forging the part. The part is then slowly cooled to room temperature, followed by two heat treatment processes. In the first heat treatment process the track link is reheated to austenization temperature, quenched to room temperature, and then tempered to a hardness of
- the alloy steel disclosed in the '474 patent may provide improved wear and rolling contact fatigue resistance, still further improvements in manufacturing costs and material characteristics may be possible.
- the '474 patent describes the use of significant quantities of expensive alloying elements such as Chromium (Cr) and Molybdenum (Mo) to achieve improved levels of rolling contact fatigue strength, ductility, bending fatigue life and fracture toughness, coupled with rolling contact wear resistance similar to or better than those of the current heat treated pearlitic rails.
- the bainitic microalloyed steel produced in accordance with the chemistry and processes of the present disclosure solves one or more of the problems set forth above and/or other problems in the art. Summary
- the present disclosure is directed to a method of producing a forged steel part, including providing steel billet having a composition including, on a weight basis:
- V 0.00 - 0.15 wt. %
- the present disclosure is directed to an air- hardenable bainitic steel part having a composition including, on a weight basis
- V 0.00 - 0.15 wt. %
- the present disclosure is directed to a forged steel part manufactured to have a chemical composition including, on a weight basis:
- V 0.00 - 0.15 wt. %
- a balance of Fe and incidental impurities a microstructure that is greater than 50% by volume bainitic microstructure throughout the entire steel part, and the forged steel part being manufactured by hot forging, controlled air cooling after the hot forging to produce a bainitic microstructure of greater than 50% bainite throughout the forged steel part, and final machining.
- Fig. 1 is a schematic diagram of an exemplary disclosed process eliminating typical heat treating steps
- Fig. 2 is a continuous cooling transformation (CCT) diagram for producing the microstructure of an exemplary embodiment of the disclosure.
- Fig. 3 is a flowchart depicting an exemplary disclosed method that may be used to produce an exemplary microalloyed bainitic steel with enhanced characteristics.
- a microalloyed, air-hardenable, predominantly bainitic steel with enhanced strength, wear, and toughness characteristics is disclosed.
- the microalloyed, bainitic steel may be economically produced without requiring many of the heat treatment processes previously thought necessary to achieve desired strength, wear, and toughness characteristics.
- the typical heat treatment processes following hot forging of a steel part may include cooling, reheating to austenization temperature, quenching, and tempering. These heat treatment processes may then be followed by reheating select portions of the steel part a second time using induction, quenching a second time, and tempering a second time before the final machining.
- At least the first sequence of heat treatment steps involving reheating, quenching, and tempering may be required with conventional hot forging processes in order to obtain desired strength and toughness characteristics, while at the same time ending up with a part that is not too hard for machining.
- Significant cost savings may be achieved if at least some of these intermediate heat treatment processes can be eliminated.
- Capital investments for heat treatment capacity, and maintenance costs on the furnaces and other equipment may be reduced.
- the microalloyed, bainitic steel may be provided with the necessary composition and cooling after hot forging to arrive at a hardness of approximately 50 - 55 Rockwell C hardness (HRC) without even requiring the induction reheating, quenching, and tempering before final machining.
- HRC Rockwell C hardness
- a predominantly bainitic microstructure is a microstructure that consists of at least 50% by volume of a bainitic microstructure. Certain embodiments may have at least 70% by volume of a bainitic microstructure. Other embodiments may have at least 85% by volume of a bainitic microstructure.
- Bainite is a microstructure that forms in steels at temperatures of approximately 250-550 °C (depending on alloy content). Bainite is one of the decomposition products that may form when austenite (the face centered cubic crystal structure of iron) is cooled past a critical temperature of 727 °C (1340 °F) depending on alloy content.
- a bainitic microstructure may be similar in appearance and hardness characteristics to tempered martensite.
- bainite commonly consists of cementite and dislocation-rich ferrite.
- the high concentration of dislocations in the ferrite present in bainite makes this ferrite harder than it normally would be.
- CCT continuous cooling transformation
- the temperature range for transformation to bainite 250-550 °C is between those for pearlite and martensite.
- the cooling rate to form bainite is more rapid than that required to form pearlite, but less rapid than that required to form martensite (in steels of the same composition).
- a microalloyed steel having the chemistry discussed in more detail below may be initially heated to austenization temperatures of approximately 1150 - 1350 °C or greater.
- the steel may then be hot forged into the desired shape, and control cooled from the forging temperature to achieve a bainitic microstructure.
- atmospheric cooling or forced air cooling using a blower may be conducted.
- the steel may be cooled rapidly down to about the eutectoid transformation temperature, and then cooled slowly over a range from about 900 to 500 °C.
- the steel may be cooled quickly to about 500 to 300 °C after hot forging, and may be kept at an equilibrium temperature somewhere in the range from about 500 to 300 °C to promote bainite transformation.
- the cooling rate may be determined by reference to a CCT diagram, to know the range for cooling rates passing through the bainite transformation region and, thereby, controlling to the determined cooling rate range.
- the CCT diagram may have been previously prepared, stored in a database, or otherwise made available for control of the cooling process.
- the forged product may be air cooled using fans or other means of circulating the cooling air to achieve a cooling rate that falls approximately within the range from 0.5 to 5 °C per second, or 30 to 300 °C per minute, when cooling between approximately 900 °C and 500 °C. Most alloying elements will lower the temperature required for the maximum rate of formation of bainite, though carbon is the most effective in doing so.
- Bainite generally has a hardness that is greater than the typical hardness of pearlite and less than the hardness of martensite. Pearlite in the microstructure may contribute to reduced toughness.
- the composition and processing of the microalloyed steel according to various embodiments of this disclosure are selected to avoid or at least minimize the amount of pearlite present. In commercial practice a small amount of pearlite, such as less than 2 percent by volume, may unavoidably be present, particularly in the center of large sections, but care is taken to minimize its presence and effects.
- the bainite microstructure essentially has a two-phase microstructure composed of ferrite and iron carbide or cementite.
- upper bainite can be described as aggregates of ferrite laths that usually are found in parallel groups to form plate-shaped regions.
- the carbide phase associated with upper bainite is precipitated at the interlath regions, and depending on the carbon content, these carbides can form nearly complete carbide films between the lath boundaries.
- Lower bainite also consists of an aggregate of ferrite and carbides. The carbides precipitate inside of the ferrite plates.
- the carbide precipitates are on a very fine scale and in general have the shape of rods or blades. For this reason, the bainitic microstructure becomes useful in that no additional heat treatments are required after initial cooling to achieve a hardness value between that of pearlitic and martensitic steels.
- the material characteristics of the microalloyed and forged steel can vary over a large range depending on the particular types and quantities of alloying elements included in the composition.
- steel contains sufficient amounts of Si and/or Al
- the carbide formation can be significantly retarded such that carbide does not have enough time to form during the continuous cooling process, resulting in a mixed microstructure of bainitic ferrite and retained austenite.
- This type of bainitic microstructure may be referred to as "carbide free" bainite.
- bainite may provide superior toughness to conventional types of bainite.
- the composition of alloying elements included in accordance with various embodiments of this disclosure results in a steel part having the strength, hardness, and toughness characteristics previously only achieved by including the intermediate heat treatment steps following hot forging of reheating to austenization temperature, quenching, and tempering.
- a part that is 70% by volume bainitic microstructure may exhibit greater strength, hardness, and toughness characteristics than a part that is 50% by volume bainitic microstructure balanced with ferrite and/or pearlite type of microstructure. Additionally, a part that is 85% or greater by volume bainitic microstructure may exhibit even further enhanced characteristics of strength, hardness, and toughness than the part that is 70% by volume bainitic microstructure balanced with ferrite and/or pearlite type of microstructure. As shown in Fig.
- intermediate heat treatment steps of reheating to austenization temperature, quenching, and tempering may be eliminated before the final machining of a forged product in accordance with various implementations of this disclosure.
- Induction reheating of select portions of the steel part such as the rail portion of a track link used in contact with the tracks on earth moving machinery, may be included to achieve enhanced hardness and strength characteristics for certain parts or portions of parts. The increased hardness can also improve the wear resistance of the selected portions of the steel part.
- the alloying elements that are added to the composition in accordance with various embodiments of this disclosure may also be selected to obtain the desired volume percentages of bainitic microstructure throughout the part, regardless of the different cooling rates that may be experienced in different sections or portions of the part having different thicknesses.
- the bainitic microstructure obtained after controlled air-cooling may also exhibit the same or similar hardness and strength characteristics as were previously achieved by following hot forging with quenching, reheating, quenching again, and tempering.
- a microalloyed steel may exhibit a martensitic microstructure after rapid cooling from hot forging temperatures through quenching in oil or water.
- the martensitic microstructure may have a Rockwell C hardness (HRC) of 50 after quenching depending on the carbon content of the steel.
- Typical methods of processing this martensitic microstructure steel may then include reheating back up to austenitic temperatures of approximately 800 °C - 950 °C, quenching again, and then tempering by reheating again to approximately 500 °C - 590 °C in order to soften the steel to approximately HRC 30.
- the controlled air cooling process for producing a predominantly bainitic microstructure according to various implementations of this disclosure may result in the same hardness of HRC 30 without all of the quenching, reheating, quenching and tempering steps previously required.
- the predominantly bainitic microstructure may contain greater than 50% by volume of bainitic microstructure.
- the hardness after air cooling in accordance with this disclosure may fall within the range from approximately 35 - 45 HRC.
- the types and quantities of microalloying elements included in the composition of the air-hardenable, bainitic steel in accordance with various embodiments may also enable achievement of hardness levels after air cooling that fall
- microalloyed steel may have a chemical composition, by weight, as listed in Table 1 :
- Carbon (C) contributes to the attainable hardness level as well as the depth of hardening.
- the carbon content is at least 0.25% by weight to maintain adequate core hardness after tempering and is no more than about 0.40% by weight to assure resistance to quench cracking and steel toughness. It has been found that if the carbon content is more than about 0.40% by weight, water quenching may cause cracking or distortion in complex-shaped articles and, in such cases, a less drastic quench medium such as oil may be required. Therefore an advantageous range of C is from approximately 0.25 - 0.40 wt.%.
- the microalloyed, bainitic steel according to various implementations of this disclosure may be air cooled in accordance with select cooling curves on the CCT diagram of Fig. 2.
- Manganese (Mn) is a low cost allow and contributes to the deep hardenability and is therefore present in most hardenable alloy steel grades.
- the disclosed alloy steel contains manganese in an amount of at least 1.50% by weight to assure adequate core hardness and contains no more than about 3.00% to prevent manganese segregation and the formation of blocky retained austenite.
- the Si may also help deoxidation of the molten steel, as well as contributing to the formation of a carbide-free bainite with improved toughness when sufficient Si is added into the steel.
- Chromium contributes to the hardenability of the present steel alloy and may be added in small amounts not exceeding 1.00% by weight in order to allow for adjustment of the CCT curve to form a predominantly bainitic microstructure after air cooling. More Chromium increases steel cost.
- Mo Molybdenum
- B Boron
- the forged steel may have large prior austenite grain sizes, resulting in poor toughness.
- the remainder of the alloy steel composition is essentially iron, except for nonessential or residual amounts of elements which may be present in small amounts.
- Titanium (Ti) may also be provided in amounts approximately between 0.02 - 0.06% to form titanium carbonitrides to prevent grain coarsening before and after forging.
- Sulphur (S) which in small amounts may be beneficial in that it promotes machining, may also be provided in small enough amounts so as to not contribute to any loss of ductility and toughness.
- Phosphorus (P) in an amount over 0.05% may cause embrittlement, and preferably the upper limit should not exceed 0.035%.
- Other elements generally regarded as incidental impurities may be present within commercially recognized allowable amounts.
- Manufactured articles such as track links, having the above stated composition, may be advantageously initially formed to a desired shape by hot forging after heating up the microalloyed steel to austenization temperatures of approximately 1 150 - 1350 °C. The formed articles are then controlled cooled as described above to produce a predominantly bainitic microstructure. Select portions of the hot forged articles, such as the rail portions of a track link, may then receive additional heat treatment by induction heating the select portions, quenching, and tempering before final machining to a desired final dimension.
- Fig. 3 illustrates an exemplary method that may be used to produce a predominantly bainitic microalloyed steel part in accordance with various implementations of this disclosure. Fig. 3 will be discussed in more detail in the following section to further illustrate the disclosed concepts.
- the steel and method of making the steel in accordance with various implementations of the present disclosure may reduce costs by eliminating heat treatment steps typically performed after hot forging.
- the disclosed microalloyed, forged, air-hardenable bainitic steel may provide similar hardness, strength, and toughness characteristics to previously hot forged and heat treated steel parts, but without requiring all of the heat treatment processes.
- the microalloying elements in combination with the controlled air cooling may produce a predominantly bainitic microstructure after air cooling from hot forging temperatures.
- Select portions of the steel parts produced in accordance with the composition and processes of this disclosure may be further hardened if desired using localized induction heating followed by quenching and tempering.
- the composition of the bainitic steel in accordance with this disclosure may be adjusted within the disclosed ranges, and air cooled in order to achieve a hardness after air cooling falling in the range from approximately 50 - 55 HRC with no further heat treatment.
- the steel part produced in accordance with various advantageous implementations of this disclosure exhibits material characteristics that may include a body hardness of 35 - 45 HRC after air cooling for good machinability with no heat treatment, a body yield strength that is greater than 1000 mega- pascals (MPa) after the air cooling, a hardness at the portions that have been additionally hardened through selective induction heating of greater than approximately 50 HRC, and a body toughness of approximately 20 Joules or greater in the Charpy impact test at room temperature.
- material characteristics may include a body hardness of 35 - 45 HRC after air cooling for good machinability with no heat treatment, a body yield strength that is greater than 1000 mega- pascals (MPa) after the air cooling, a hardness at the portions that have been additionally hardened through selective induction heating of greater than approximately 50 HRC, and a body toughness of approximately 20 Joules or greater in the Charpy impact test at room temperature.
- a microalloyed steel having the composition shown above in Table 1 may be heated to austenization temperatures of approximately 1 150 degrees C to 1350 degrees C.
- the types of parts being manufactured in accordance with various implementations of this disclosure may include parts that require good machinability in at least one portion, high yield strength, good wear characteristics, and good toughness.
- One exemplary application of the disclosed compositions and processes is for track links used in the tracks of a track-type machine such as a bulldozer or other earth moving equipment.
- the size of the parts determines the size of a steel billet that is initially heated to austenization temperatures in accordance with step 320.
- the heated billet may be hot forged to a desired configuration.
- step 324 may include air cooling the hot forged product at a cooling rate that results in the formation of a predominantly bainitic microstructure throughout the hot forged part.
- the cooling rate may be chosen to avoid the formation of a large amount of martensitic microstructure or a predominantly ferrite and pearlite microstructure.
- the hot forged steel may be cooled at a rate that falls approximately in the range from 0.5 to 5 degrees C per second as the steel cools from approximately 900 degrees C to approximately 500 degrees C.
- the weight percentages of the alloying elements in the composition of the steel may be varied in order to change the phase transformation curves on the CCT diagram, and achieve the desired predominantly bainitic microstructure at cooling rates achieved by transporting the hot forged steel parts along a conveyor at ambient temperatures.
- the microalloyed steel may also be advantageously provided with a composition that achieves the desired bainitic microstructure and hardness levels throughout the part even at the different cooling rates that may be experienced by different sections of the part having different thicknesses.
- the predominantly bainitic microstructure may be a microstructure with greater than 50% bainite, or more advantageously greater than 70% bainite, or still more advantageously greater than 85% bainite throughout the hot forged steel part.
- the hardness levels throughout the entire forged steel part after air cooling may fall within the range from approximately 35 - 45 HRC. In other advantageous embodiments, the hardness levels throughout the forged steel part may fall within the range from approximately 40 - 55 HRC after air cooling with no further heat treatment.
- select portions of the steel part may be induction heated in order to achieve higher hardness levels.
- select portions of the steel part may be induction heated in order to achieve higher hardness levels.
- a high surface hardness may be desired for the rail portion because the rail portion may be subjected to severe wear from continuous contact with track rollers.
- a lower surface hardness in the body portion of the track link allows holes for bushings, pins, and bolts to be more easily machined into the body portion.
- the lower surface hardness of the body portion of the track link also allows for a press fit between a bushing and the hole in the track link body without creating excessive residual stresses.
- the hardness of the induction heated portions of the steel part may fall within the range from approximately 50 - 57 HRC.
- At step 328 after select portions of the steel part have been induction heated, at least these heated portions of the steel part may be quenched, using techniques such as directed sprays of quenching fluids onto the induction heated areas of the part. Following quenching, at step 330, the steel part may be reheated to tempering temperatures in order to improve its toughness. Final machining may then occur at step 332.
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- Chemical & Material Sciences (AREA)
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- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Crystallography & Structural Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
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Abstract
Description
Claims
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
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US13/848,829 US20140283960A1 (en) | 2013-03-22 | 2013-03-22 | Air-hardenable bainitic steel with enhanced material characteristics |
PCT/US2014/031201 WO2014153398A1 (en) | 2013-03-22 | 2014-03-19 | Air-hardenable bainitic steel with enhanced material characteristics |
Publications (3)
Publication Number | Publication Date |
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EP2976437A1 true EP2976437A1 (en) | 2016-01-27 |
EP2976437A4 EP2976437A4 (en) | 2016-12-14 |
EP2976437B1 EP2976437B1 (en) | 2019-05-15 |
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EP14771156.8A Active EP2976437B1 (en) | 2013-03-22 | 2014-03-19 | Air-hardenable bainitic steel with enhanced material characteristics |
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US (2) | US20140283960A1 (en) |
EP (1) | EP2976437B1 (en) |
JP (1) | JP6382937B2 (en) |
KR (1) | KR20150132320A (en) |
CN (1) | CN105143474A (en) |
AU (1) | AU2014235986B2 (en) |
RU (1) | RU2015143271A (en) |
WO (1) | WO2014153398A1 (en) |
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US9440693B2 (en) * | 2014-03-20 | 2016-09-13 | Caterpillar Inc. | Air-hardenable bainitic steel part |
JP6782060B2 (en) * | 2015-01-22 | 2020-11-11 | 臼井国際産業株式会社 | How to manufacture fuel rails |
JP6789611B2 (en) * | 2015-01-22 | 2020-11-25 | 臼井国際産業株式会社 | Manufacturing method of fuel rail for gasoline direct injection |
CN106048149A (en) * | 2016-07-16 | 2016-10-26 | 柳州科尔特锻造机械有限公司 | Heat treatment process of low-alloy steel |
US10882574B2 (en) * | 2016-07-26 | 2021-01-05 | Caterpillar Inc. | Method of track link manufacture |
MX2016013350A (en) * | 2016-10-06 | 2018-04-05 | Aboytes Trejo Juan | Process and system for thermal treatment of low- and medium-carbon alloyed steel parts for the production of a desired crystalline structure. |
WO2018215813A1 (en) * | 2017-05-22 | 2018-11-29 | Arcelormittal | Method for producing a steel part and corresponding steel part |
CN107385156B (en) * | 2017-06-29 | 2019-01-15 | 江南工业集团有限公司 | The Strengthening and Toughening composite heat treating method of 30CrMnSiA steel |
WO2021009543A1 (en) * | 2019-07-16 | 2021-01-21 | Arcelormittal | Method for producing a steel part and steel part |
CN112008031B (en) * | 2020-08-25 | 2023-06-16 | 无锡继平新材料科技有限公司 | Forging and heat treatment process of valve body for shale gas exploitation |
CN114850365A (en) * | 2022-04-19 | 2022-08-05 | 中国恩菲工程技术有限公司 | Bainite-based grinding medium and preparation method and application thereof |
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2013
- 2013-03-22 US US13/848,829 patent/US20140283960A1/en not_active Abandoned
-
2014
- 2014-03-19 KR KR1020157028786A patent/KR20150132320A/en not_active Application Discontinuation
- 2014-03-19 RU RU2015143271A patent/RU2015143271A/en not_active Application Discontinuation
- 2014-03-19 WO PCT/US2014/031201 patent/WO2014153398A1/en active Application Filing
- 2014-03-19 EP EP14771156.8A patent/EP2976437B1/en active Active
- 2014-03-19 JP JP2016504346A patent/JP6382937B2/en active Active
- 2014-03-19 AU AU2014235986A patent/AU2014235986B2/en active Active
- 2014-03-19 CN CN201480016289.4A patent/CN105143474A/en active Pending
-
2015
- 2015-09-04 US US14/845,699 patent/US20150376750A1/en not_active Abandoned
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AU2014235986B2 (en) | 2017-11-16 |
AU2014235986A1 (en) | 2015-11-05 |
US20140283960A1 (en) | 2014-09-25 |
US20150376750A1 (en) | 2015-12-31 |
EP2976437A4 (en) | 2016-12-14 |
WO2014153398A1 (en) | 2014-09-25 |
KR20150132320A (en) | 2015-11-25 |
EP2976437B1 (en) | 2019-05-15 |
CN105143474A (en) | 2015-12-09 |
JP6382937B2 (en) | 2018-08-29 |
RU2015143271A (en) | 2017-04-27 |
JP2016518521A (en) | 2016-06-23 |
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