EP3279361B1 - Barre laminée à chaud ou fil machine laminé à chaud, composant et procédé de fabrication d'une barre laminée à chaud ou fil machine laminé à chaud - Google Patents

Barre laminée à chaud ou fil machine laminé à chaud, composant et procédé de fabrication d'une barre laminée à chaud ou fil machine laminé à chaud Download PDF

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EP3279361B1
EP3279361B1 EP16773271.8A EP16773271A EP3279361B1 EP 3279361 B1 EP3279361 B1 EP 3279361B1 EP 16773271 A EP16773271 A EP 16773271A EP 3279361 B1 EP3279361 B1 EP 3279361B1
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hot rolled
steel
content
less
wire rod
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EP3279361A1 (fr
EP3279361A4 (fr
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Akira Shiga
Manabu Kubota
Hajime Hasegawa
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Nippon Steel Corp
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Nippon Steel Corp
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    • 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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/52—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length
    • C21D9/525—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length for wire, for rods
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
    • B21B1/16—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling wire rods, bars, merchant bars, rounds wire or material of like small cross-section
    • 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
    • C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
    • 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
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/06—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires
    • 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
    • C21D8/06—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires
    • C21D8/065—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires 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
    • 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
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • 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
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • 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
    • C22C38/20—Ferrous alloys, e.g. steel alloys containing chromium with copper
    • 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
    • C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
    • 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
    • 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
    • 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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/005—Ferrite
    • 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
    • C21D2211/009—Pearlite

Definitions

  • Patent Document 1 discloses steel for a gear including Si: 0.1% or less, and P: 0.01% or less.
  • the steel for a gear disclosed in Patent Document 1 has high strength and high reliability with toughness, by decreasing the Si content and P content.
  • the surface fatigue strength and bending fatigue strength of the case hardening steel disclosed in Patent Document 4 has not been investigated, and these may be low.
  • the steel bar for hot forging disclosed in Patent Document 5 satisfies high bending fatigue strength, surface fatigue strength, and machinability, by regulating the total amount of Cr and Mo contents.
  • machinability may be insufficient, in a case of mass production.
  • the case hardening steel disclosed in Patent Document 6 only the improvement of low cycle fatigue strength is shown, and bending fatigue strength, surface fatigue strength, wear resistance, and machinability thereof have not been investigated.
  • Electron Probe Micro Analyzer In the measurement for distribution of the Mn contents, Electron Probe Micro Analyzer (EPMA) is used. A beam diameter at the time of the measurement using the EPMA is set as 1 ⁇ m, and linear analysis is performed within a range of 50 mm in parallel with a surface at a position separated by 15 mm from a slab surface.
  • a value of Expression (2) is defined as a value obtained by dividing the Mn content in the space between dendrites measured by the linear analysis by an average Mn content in the slab measured in advance.
  • this case indicates an ideal state in which there is no difference between Mn contents in a core and the space between the primary arm of the dendrite in the slab and no segregation of Mn is generated.
  • a percentage of the Mn segregation is high, a difference between Mn contents in the core and in the space between primary arms of the dendrite in the slab is large, a lot of hard bainite structures are generated, and machinability is deteriorated.
  • the hot rolled bar or hot rolled wire rod of the present invention was completed based on the aforementioned findings.
  • the hot rolled bar or hot rolled wire rod according to the present invention will be described in detail.
  • “%" of the amounts of elements configuring a chemical composition means “mass%”.
  • a hot rolled bar or hot rolled wire rod according to the present invention is defined in claims 1 to 3, and a manufacturing method thereof in claim 5.
  • Claim 4 refers to a component obtained by machining the hot rolled bar or hot rolled wire rod.
  • S Sulfur
  • MnS increases machinability of steel. Meanwhile, when S is excessively included, coarse MnS is formed. The coarse MnS decreases bending fatigue strength and surface fatigue strength of steel. Therefore, S content is 0.008 to less than 0.040%.
  • a preferable lower limit of the S content exceeds 0.008%, and the lower limit thereof is more preferably 0.009% or more and even more preferably 0.010% or more.
  • a preferable upper limit of the S content is 0.030% or less, and the upper limit thereof is more preferably less than 0.030% and even more preferably less than 0.020%.
  • Cr increases hardenability of steel and resistance to temper softening of steel. Accordingly, Cr increases bending fatigue strength, surface fatigue strength, and wear resistance of steel. Meanwhile, when Cr is excessively included, generation of a bainite is promoted in steel after hot rolling, after hot forging, or after normalizing. Accordingly, machinability of steel is deteriorated. Therefore, Cr content is 1.60 to 2.00%. A preferable lower limit of the Cr content exceeds 1.60%, and the lower limit thereof is more preferably 1.70% or more and even more preferably 1.80% or more. A preferable upper limit of the Cr content is less than 2.00%, and the upper limit thereof is more preferably 1.95% or less and even more preferably 1.90% or less.
  • Molybdenum (Mo) may be included or may not be included. Mo increases hardenability of steel and resistance to temper softening. Accordingly, Mo increases bending fatigue strength, surface fatigue strength, and wear resistance of steel. Meanwhile, when Mo is excessively included, generation of a bainite is promoted in steel after hot rolling, after hot forging, or after normalizing. Accordingly, machinability of steel is deteriorated. Therefore, Mo content is 0 to 0.10%. A preferable lower limit of the Mo content is 0.02% or more. A preferable upper limit of the Mo content is less than 0.10%, and the upper limit thereof is more preferably 0.08% or less and even more preferably 0.05% or less.
  • Al deoxidizes steel. Al is also combined with N to form AlN.
  • the AlN prevents coarsening of austenite grains due to carburizing and heating. Meanwhile, when Al is excessively included, coarse Al oxides are formed. The coarse Al oxides decrease bending fatigue strength of steel. Therefore, Al content is 0.025 to 0.05%.
  • a preferable lower limit of the Al content exceeds 0.025%, and the lower limit thereof is more preferably 0.027% or more and even more preferably 0.030% or more.
  • a preferable upper limit of the Al content is less than 0.05%, and the upper limit thereof is more preferably 0.045% or less and even more preferably 0.04% or less.
  • N Nitrogen
  • Al or NbN prevents coarsening of austenite grains due to heating for carburizing. Meanwhile, when N is excessively included, it is difficult to stably manufacture steel in steel making process. Therefore, N content is 0.010 to 0.025%.
  • a preferable lower limit of the N content exceeds 0.010%, and the lower limit thereof is more preferably 0.012% or more and even more preferably 0.013% or more.
  • a preferable upper limit of the N content is less than 0.025%, and the upper limit thereof is more preferably 0.020% or less and even more preferably 0.018% or less.
  • Bi is an important element in the present invention.
  • a small amount of Bi becomes an inoculant nucleus of solidification, decreases a dendrite arm spacing during solidification, and refines a solidifated structure.
  • the segregation amount of an element which is easily segregated, such as Mn is decreased, generation of a bainite structure due to microsegregation is prevented, and machinability is improved.
  • the Bi content is set to be 0.0001% or more.
  • the Bi content is 0.0001% or more and less than 0.0050%.
  • the Bi content is preferably 0.0010% or more.
  • Oxygen (O) is combined with Al to form an oxide inclusion.
  • the oxide inclusion decreases bending fatigue strength of steel. Therefore, it is preferable that an O content is as small as possible.
  • the O content is 0.002% or less.
  • the preferable O content is less than 0.002% and the O content is more preferably 0.001% or less. It is more desirable that the O content is as small as possible, within a range not causing an increase in cost in steel making process.
  • the chemical composition of the hot rolled bar or hot rolled wire rod according to the embodiment may include Nb, instead of a part of Fe.
  • Niobium (Nb) is a selective element. Nb is combined with C and N to form Nb carbide, Nb nitride, or Nb carbonitride.
  • the Nb carbide, Nb nitride, and the Nb carbonitride prevent coarsening of austenite grains during carburizing and heating, in the same manner as the Al nitride. If a small amount of Nb is included, the effect described above is obtained. Meanwhile, when Nb is excessively included, the Nb carbide, the Nb nitride, and the Nb carbonitride are coarsened. Accordingly, the coarsening of austenite grains during carburizing and heating cannot be prevented. Therefore, Nb content is 0.08% or less. A preferable lower limit of the Nb content is 0.01% or more. A preferable upper limit of the Nb content is less than 0.08%, and the upper limit thereof is more preferably 0.05% or less.
  • the remainder of the chemical composition of the hot rolled bar or hot rolled wire rod according to the embodiment is Fe and impurities.
  • the impurities in the embodiment are elements mixed from ores or scraps used as a raw material for steel, or are elements mixed in an environment of manufacturing process.
  • the impurities are, for example, copper (Cu) or nickel (Ni).
  • the Cu and Ni contents which are the impurities are approximately the same as the Cu and Ni contents in SCr steel and SCM steel regulated as JIS G4053 alloy steel for machine structural use, the Cu content is 0.40% or less and the Ni content is 0.80% or less.
  • Nickel (Ni) has an effect of increasing hardenability and is an element effective for further increasing fatigue strength. Thus, nickel may be included, if necessary. However, when the Ni content is excessively included, not only the effect for increasing fatigue strength along with the improvement of hardenability is saturated, but also a bainite structure is easily generated in steel after hot rolling, after hot forging, or after a normalizing treatment. Therefore, the amount of Ni in a case of including Ni is set as 0.80% or less. The amount of Ni in a case of including Ni is preferably 0.60% or less. In addition, in order to stably obtain the effect for increasing fatigue strength along with the improvement of hardenability, the amount of Ni in a case of including Ni is preferably 0.10% or more.
  • Copper (Cu) has an effect for increasing hardenability and is an element effective for further increasing fatigue strength. Thus, copper may be included, if necessary. However, when the Cu content is excessively included, deterioration in hot ductility and hot workability becomes significant. Therefore, the amount of Cu in a case of including Cu is set as 0.40% or less. In addition, the amount of Cu in a case of including Cu is preferably 0.30 or less. A preferable lower limit of the Cu content is 0.1% or more.
  • F1 defined in Expression (1) is 1.70 to 2.10.
  • F 1 Cr + 2 ⁇ Mo
  • a symbol for an element in Expression F1 represents the amount of the corresponding element (mass%).
  • F1 is less than 1.70, at least one of bending fatigue strength, surface fatigue strength, and wear resistance of steel is decreased.
  • F1 exceeds 2.10 the generation of a bainite is promoted in steel after hot rolling, after hot forging, or after normalizing. Therefore, machinability of steel is deteriorated.
  • F1 is 1.70 to 2.10, it is possible to increase bending fatigue strength, surface fatigue strength, and wear resistance of steel, while preventing deterioration in machinability of steel.
  • a preferable lower limit of F1 is 1.80 or more.
  • a preferable upper limit of F1 is less than 2.00.
  • Mn is microsegregated in steel slab used when manufacturing the hot rolled bar or hot rolled wire rod of the present invention by hot rolling
  • the generation of a hard bainite structure is promoted in the microstructure of steel after hot rolling and machinability is deteriorated. Therefore, it is preferable that microsegregation of Mn is prevented in the steel slab. Even when Expression (1) is satisfied, when microsegregation of Mn is large, the amount of the hard bainite structure is increased and machinability is deteriorated.
  • a manufacturing method of a hot rolled bar or hot rolled wire rod according to an embodiment of the present invention will be described.
  • a slab which satisfies the chemical composition described above and in which a ratio of the Mn contents (Mn max /Mn) satisfies Expression (2) is manufactured.
  • Mn max represents Mn content in space between primary arms of a dendrite and Mn represents Mn content in steel.
  • a slab may be obtained by continuous casting steel including the chemical composition or a steel ingot may be obtained by ingot casting steel including the chemical composition.
  • a mold having a size of 220 mm ⁇ 220 mm is used, a superheat temperature of molten steel in a tundish is set as 10°C to 50°C, and a casting speed is set as 1.0 m/min to 1.5 m/min.
  • an average cooling rate in a temperature range from a liquidus temperature to a solidus temperature at a position of depth of 15 mm from a slab surface is set to 100 °C/min or faster and 500 °C/min or lower, when casting the molten steel including the chemical composition described above.
  • a cross section of the obtained slab can be etched with picric acid, a space ⁇ ( ⁇ m) between primary arms of a dendrite at a position of depth of 15 mm from the slab surface can be measured, and an average cooling rate A (°C/min) within a temperature range from a liquidus temperature to a solidus temperature can be calculated using the space between primary arms of a dendrite based on the following expression.
  • ⁇ 710 ⁇ A ⁇ 0.39
  • the temperature range from a liquidus temperature to a solidus temperature is a temperature range from the start of solidification to the end of solidification. Accordingly, the average cooling temperature in this temperature range means the average solidification rate of the slab.
  • the average cooling rate described above can be achieved, for example, by a method of controlling a size of a cross section of a mold or a casting speed to a proper value or increasing the amount of cooling water used for water cooling, immediately after casting. Both of continuous casting and ingot casting can be applied.
  • the manufactured slab is inserted into a heating furnace, heated at a heating temperature of 1250°C to 1300°C for 10 hours or longer, and subjected to blooming, to manufacture a billet.
  • the heating temperature described above means an average temperature in the furnace and the heating time means an in-furnace time.
  • cooling may be performed to reach room temperature, under the conditions in which the cooling rate becomes equal to or lower than a cooling rate in naturally cooling, but, in order to increase productivity, it is preferable to perform the cooling by suitable methods such as air cooling, mist cooling, and water cooling at a point when the temperature has reached 600°C.
  • the heating temperature means an average temperature in the furnace and the heating time means the in-furnace time.
  • the finish temperature of the hot rolling means a surface temperature of a bar or hot rolled wire rod at an exit of final stand in a roller including a plurality of stands.
  • the cooling rate after finish rolling indicates a cooling rate at the surface of the bar or hot rolled wire rod.
  • a reduction of area (RD) represented by Expression (3) is preferably 87.5% or greater.
  • RD 1 ⁇ cross section area of steel bar or hot rolled wire rod / cross section area of billet ⁇ 100
  • the cross section area means an area of a cross section perpendicular to a longitudinal direction, that is, an area of a transverse section.
  • a change of an average cooling rate in a temperature range from a liquidus temperature to a solidus temperature at a position of a depth of 15 mm from a surface of the slab was performed by changing the amount of cooling water of the mold.
  • the slab of each mark was heated at 1250°C for 2 hours.
  • the heated slab was hot rolled to manufacture a plurality of round bars having a diameter of 35 mm. After the hot rolling, the round bars were naturally cooled in the atmosphere. In this manner, various hot rolled bars or hot rolled wire rods were manufactured.
  • the Mn max was acquired by the following method.
  • a test piece having a width of 50 mm ⁇ a length of 50 mm ⁇ a thickness of 8 mm in a thickness direction was collected from a surface layer of the manufactured slab, and a surface having a width of 50 mm ⁇ a length of 50 mm was set as a "test surface". After performing resin embedding of the test piece, the test surface was mirror polished.
  • EPMA was used in the measurement for distribution of the Mn contents.
  • a beam diameter at the time of the measurement using EPMA was set as 1 ⁇ m, and linear analysis was performed within a range of 50 mm in parallel with a surface at a position separated by 15 mm from a slab surface.
  • the distribution of the Mn contents between the primary arms of the dendrite was measured by linear analysis using EPMA, and a maximum value of the measured Mn contents was set as the Mn content (Mn max ) in the space between dendrites.
  • Mn max Mn content
  • a value obtained by dividing the Mn content in the space between dendrites measured by linear analysis by an average Mn content in the slab was set as the value of F2.
  • the machining of the round bar of each steel number having a diameter of 35 mm was performed to manufacture a roller pitching small roller test piece (hereinafter, simply referred to as a small roller test piece) shown in FIG. 1 and Ono-type rotating bending fatigue test piece with notches shown in FIG. 2 (in both FIG. 1 and FIG. 2 , the unit for the dimensions in the drawings is mm).
  • the small roller test piece shown in FIG. 1 includes a test portion (columnar portion having a diameter of 26 mm and a width of 28 mm) at the center.
  • Each test piece manufactured was subjected to carburizing hardening under the conditions shown in FIG. 3 using a gas carburizing furnace. After hardening, tempering was performed at 150°C for 1.5 hours. Finish machining of grip sections was performed with respect to the small roller test piece and the Ono-type rotating bending fatigue test piece with notches, in order to remove a strain due to heat treatment.
  • the large roller shown in FIG. 4 is formed of a steel satisfying the standards in JIS standard SCM420 (steel number 17) and was manufactured by typical manufacturing processes, that is, processes of normalizing, test piece processing, eutectoid carburizing using a gas carburizing furnace, low temperature tempering, and polishing.
  • a lubricant commercially available oil for automatic transmission
  • a contact portion surface of a test portion between the large roller and the small roller test piece in a direction opposite to a rotation direction, under the condition of an oil temperature of 90°C.
  • the roller pitching test was performed and the surface fatigue strength was evaluated.
  • the number of roller pitching tests was set as 6. After the test, an S-N diagram, in which a vertical axis indicates surface pressure and a horizontal axis indicates the number of cycles until the pitching is occurred, was drawn. Among the steels in which the pitching did not occur until the number of cycles became 2.0 ⁇ 10 7 times, the highest surface pressure was defined as surface fatigue strength of the corresponding steel number. Among the damaged portions on the surface of the small roller test piece, a case where the maximum area thereof is 1 mm 2 or greater was defined as the pitching is occurred.
  • Table 3 shows surface fatigue strength obtained by the test.
  • surface fatigue strength of the steel number 16 which is obtained by carburizing of the steel 16 satisfying the standards of JIS standard SCr420H which is typical steel as general-purpose steel, was set as a reference value (100%).
  • the surface fatigue strength of each test number is shown as a percentage (%) with respect to the reference value. When the surface fatigue strength is 120% or greater, it is determined that excellent surface fatigue strength is obtained.
  • the wear amount of a test portion of the small roller test piece when the number of cycles was 1.0 ⁇ 10 6 times was measured. Specifically, the maximum height roughness (Rz) was acquired based on JIS B0601 (2001). A small Rz value indicates high wear resistance. In the measurement of the wear amount, a roughness meter was used. Table 3 shows the wear amounts. In the wear amounts in Table 3, the wear amount of the steel number 16 was set as a reference value (100%). The wear amount of each steel number was shown as a percentage (%) with respect to the reference value. When the wear amount is 80% or smaller, it is determined that excellent wear resistance is obtained.
  • the bending fatigue strength was acquired by an Ono-type rotary bending fatigue test.
  • the number of tests in the Ono-type rotary bending fatigue test was set as 8 for each steel number.
  • the test was performed by setting a rotation speed at the time of the test as 3000 rpm and other conditions as those of a normal method.
  • the highest stress was defined as middle cycle rotary bending fatigue strength.
  • the highest stress was defined as high cycle rotary bending fatigue strength.
  • Chip property of substrate is P20 type grade of cemented carbide, no coating, Conditions: circumferential speed of 200 m/min, sending of 0.30 mm/rev, cutting of 1.5 mm, watersoluble cutting oil is used Measurement item: wear amount of main cutting edge for flank after cutting time of 10 minutes
  • Table 3 shows the average cooling rate, the F2 value, whether or not cracks occurs during casting, the microstructure, the middle cycle bending fatigue strength, the high cycle bending fatigue strength, the surface fatigue strength, the wear amount, and the wear amount of main cutting edge.
  • underlines in Table 3 mean that conditions of Expression (2) and the object of the present invention are not satisfied.
  • the chemical composition of the steels 1 to 15 were in the range of the chemical composition of the rolled steel bar or a bar or hot rolled wire rod for hot forging according to the embodiment, and Expression (1) and Expression (2) were satisfied. As a result, the steels 1 to 15 had excellent bending fatigue strength, surface fatigue strength, wear resistance, and machinability.
  • the Mn content and the Mo content exceeded the upper limits of the Mn content and the Mo content of the hot rolled bar or hot rolled wire rod according to the embodiment. Since the Mo content was large, the bending fatigue strength and the surface fatigue strength were equal to or higher than the regulation. However, since the value of F1 exceeded the upper limit of Expression (1) and Mn was excessively included, a lot of hard bainite was generated and machinability was deteriorated.
  • the Mo content exceeded the upper limit of the Mo content of the hot rolled bar or hot rolled wire rod according to the embodiment and the Al content was equal to or less than the lower limit of the Al content thereof.
  • the Al content was small and austenite grains were coarsened, but the Mo content was excessive, and a decrease in the bending fatigue strength was avoided.
  • F1 exceeded the upper limit of Expression (1), machinability was deteriorated.
  • the chemical composition of the steel 22 were in the range of the chemical composition of the hot rolled bar or hot rolled wire rod according to the embodiment. However, the value of F1 of the steel 22 was lower than the lower limit of Expression (1), and fatigue strength was decreased.
  • the Cr content was equal to or less than the lower limit of the Cr content of the hot rolled bar or hot rolled wire rod according to the embodiment and the Mn content and the Mo content exceeded the upper limits of the Mn content and the Mo content thereof.
  • the Mo content was excessively included, the Cr content was equal to or less than the lower limit of the Cr content and the value of F1 was lower than the lower limit of Expression (1). Accordingly, as a result, the bending fatigue strength and the surface fatigue strength were decreased.
  • the Si content was equal to or lower than the lower limit of the Si content of the hot rolled bar or hot rolled wire rod according to the embodiment and the Mn content exceeded the upper limit of the Mn content thereof.
  • the surface fatigue strength was decreased and the machinability was deteriorated.
  • the Si content and the Mn content exceeded the upper limits of the Si content and the Mn content of the hot rolled bar or hot rolled wire rod according to the embodiment. As a result, in the steel 25, the machinability was deteriorated.
  • the Si content, the Mo content, and the Mn content exceeded the upper limits of the Si content, the Mo content, and the Mn content of the hot rolled bar or hot rolled wire rod according to the embodiment and the Al content was equal to or lower than the lower limit of the Al content thereof.
  • the Al content was small and austenite grains were coarsened, but the Mo content was excessive, and a decrease in the bending fatigue strength was avoided.
  • F1 exceeded the upper limit of Expression (1), machinability was deteriorated.
  • the steel 27 and the steel 28 did not include Bi.
  • the chemical composition thereof were in the range of the chemical composition of the hot rolled bar or hot rolled wire rod according to the embodiment, except for the Bi content, and Expression (1) was satisfied. However, the value exceeded the upper limit of Expression (2). As a result, the machinability was low. Specifically, it was assumed that, since Bi was not included, the microsegregation of Mn was large, hard bainite was generated, and machinability was deteriorated.
  • the Mn content was equal to or less than the lower limit of the Mn content of the hot rolled bar or hot rolled wire rod according to the embodiment. As a result, the bending fatigue strength and the surface fatigue strength were decreased. It was considered that, since Mn content was small, core strength was insufficient and the bending fatigue strength and the surface fatigue strength were decreased.
  • the steel 31 is an example in which the Bi content is more than the range regulated in the present invention. Accordingly, hot workability was deteriorated and cracks occurred during casting.
  • the chemical composition of the steel 33 was in the range of the chemical composition of the hot rolled bar or hot rolled wire rod according to the embodiment. However, since the average cooling rate is equal to or faster than the desired upper limit value thereof, the solidificated structure becomes uneven and cracks due to the uneven structure may occur. Accordingly, hot workability was deteriorated and cracks occurred.
  • the chemical composition of the steel 34 was in the range of the chemical composition of the hot rolled bar or hot rolled wire rod according to the embodiment.
  • the average cooling rate was less than the lower limit thereof, and solidification was excessively slow. Accordingly, the space between dendrites was widened, and Mn was segregated. As a result, the value of F2 exceeded the upper limit of Expression (2) and the machinability was deteriorated.
  • the Al content exceeded the upper limit of the Al content of the hot rolled bar or hot rolled wire rod according to the embodiment. As a result, coarse Al oxides were generated and the bending fatigue strength was decreased.

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Claims (5)

  1. Barre laminée à chaud ou fil machine laminé à chaud comprenant une composition chimique contenant, en % de masse,
    C : 0,05 à 0,30 %,
    Si : 0,30 à 0,60 %,
    Mn : 0,40 à 1,0 %,
    S : 0,008 à moins de 0,040 %,
    Cr : 1,60 à 2,00 %,
    Mo : 0 à 0,1 % ou moins,
    Al : 0,025 à 0,05 %,
    N : 0,010 à 0,025 %,
    Ti : 0 à 0,003 %,
    Bi : 0,0001 à 0,0050 %, comprenant éventuellement en outre
    Nb : 0,08 % ou moins et/ou
    un ou plusieurs éléments choisis parmi
    Cu : 0,40 % ou moins et
    Ni : 0,80 % ou moins,
    et le reste contenant du Fe et des impuretés,
    dans lequel les quantités de P et O dans les impuretés sont respectivement
    P : 0,025 % ou moins, et
    O : 0,002 % ou moins ;
    dans lequel la microstructure est de ferrite-perlite ou ferrite-perlite-bainite, et l'expression (1) est satisfaite, 1,70 ≤ Cr + 2 × Mo ≤ 2,10
    Figure imgb0014
     où un symbole d'élément dans l'expression (1) représente la quantité d'un élément correspondant en % de masse.
  2. Barre laminée à chaud ou fil machine laminé à chaud selon la revendication 1, comprenant, à la place d'une partie du Fe, en % de masse,
    Nb : 0,08 % ou moins.
  3. Barre laminée à chaud ou fil machine laminé à chaud selon la revendication 1 ou 2, comprenant, à la place d'une partie du Fe,
    un ou plusieurs éléments choisis parmi Cu : 0,40 % ou moins et Ni : 0,80 % ou moins.
  4. Composant obtenu par usinage de la barre laminée à chaud ou du fil machine laminé à chaud selon l'une quelconque des revendications 1 à 3.
  5. Méthode de fabrication d'une barre laminée à chaud ou d'un fil machine laminé à chaud selon l'une quelconque des revendications 1 à 3, comprenant :
    la fabrication d'une brame comprenant une composition chimique selon l'une quelconque des revendications 1 à 3 par coulée en continu ou coulée en lingotière, dans laquelle la vitesse de refroidissement moyenne dans la plage de température allant d'une température de liquidus à une température de solidus en une position de profondeur de 15 mm à partir de la surface de la brame est établie à 100°C/min ou plus et 500°C/min ou moins,
    dans laquelle le rapport des teneurs en Mn (Mnmax/Mn) satisfait à l'expression (2) : 1,0 < Mn max / Mn < 2,4
    Figure imgb0015
     où, dans l'expression (2), Mnmax représente la teneur en Mn d'un espace entre les bras primaires d'une dendrite et Mn représente la teneur en Mn d'un acier en % de masse, dans laquelle la mesure pour la distribution des teneurs en Mn utilise une EPMA, dans laquelle le diamètre du faisceau au moment de la mesure utilisant une EPMA est établi à 1 µm, et une analyse linéaire est effectuée dans la plage de 50 mm parallèlement à la surface en une position séparée de 15 mm par rapport à la surface de la brame, l'insertion de la brame manufacturée dans un four de chauffage, chauffé à une température de chauffage de 1250°C à 1300°C pendant 10 heures ou plus, et la soumission de celle-ci à un dégrossissage, pour fabriquer une billette, et l'insertion de la billette dans un four de chauffage, chauffé à une température de chauffage de 1250°C à 1300°C pendant 1,5 heures ou plus, et laminage à chaud de celle-ci par établissement de la température de finition à 900°C à 1100°C, après le laminage de finition, le refroidissement de celle-ci dans l'atmosphère dans des conditions dans lesquelles la vitesse de refroidissement devient égale ou inférieure à la vitesse de refroidissement lors d'un refroidissement naturel.
EP16773271.8A 2015-03-31 2016-03-31 Barre laminée à chaud ou fil machine laminé à chaud, composant et procédé de fabrication d'une barre laminée à chaud ou fil machine laminé à chaud Active EP3279361B1 (fr)

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CN107429359B (zh) 2020-05-19
JP6465206B2 (ja) 2019-02-06
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EP3279361A4 (fr) 2018-10-24
US20180355455A1 (en) 2018-12-13
KR20170121267A (ko) 2017-11-01

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