US20160201175A1 - Age-hardenable steel - Google Patents

Age-hardenable steel Download PDF

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US20160201175A1
US20160201175A1 US14/765,029 US201414765029A US2016201175A1 US 20160201175 A1 US20160201175 A1 US 20160201175A1 US 201414765029 A US201414765029 A US 201414765029A US 2016201175 A1 US2016201175 A1 US 2016201175A1
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steel
aging treatment
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Masato Yuya
Masashi Higashida
Hitoshi Matsumoto
Tatsuya Hasegawa
Yutaka Neishi
Taizo Makino
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Nippon Steel Corp
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Nippon Steel and Sumitomo Metal Corp
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    • 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
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
    • C—CHEMISTRY; METALLURGY
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    • C21D1/06—Surface hardening
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    • C21D1/18—Hardening; Quenching with or without subsequent tempering
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    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
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    • 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
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    • 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
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    • 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
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    • 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
    • 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
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel 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
    • C22C38/40—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
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
    • 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
    • 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

Definitions

  • the present invention relates to an age-hardenable steel. More specifically, the present invention relates to a steel which is processed into a desired shape by hot forging and cutting process, and is thereafter subjected to age-hardening treatment (hereafter, simply referred to as “aging treatment”) to ensure desired strength and toughness by the aging treatment, and which is quite suitably used as a starting material for producing mechanical parts such as for automobiles, industrial machinery, construction machinery, and the like.
  • age-hardening treatment hereafter, simply referred to as “aging treatment”
  • Patent Document 1 discloses the following age-hardening steel.
  • an “age-hardening steel” containing: by mass %, C: 0.11 to 0.60%, Si: 0.03 to 3.0%, Mn: 0.01 to 2.5%, Mo: 0.3 to 4.0%, V: 0.05 to 0.5%, and Cr: 0.1 to 3.0%, and further containing, as needed, one or more kinds of Al: 0.001 to 0.3%, N: 0.005 to 0.025%, Nb: 0.5% or less, Ti: 0.5% or less, Zr: 0.5% or less, Cu: 1.0% or less, Ni: 1.0% or less, S: 0.01 to 0.20%, Ca: 0.003 to 0.010%, Pb: 0.3% or less and Bi: 0.3% or less, with the balance being Fe and inevitable impurities, wherein the following relationships are established among each component:
  • the steel is cooled at an average cooling velocity of 0.05 to 10° C./sec in a temperature range of 800° C. to 300° C. so that before the aging treatment, an area fraction of bainite structure is not less than 50%, hardness thereof is not more than 40 HRC, and the hardness becomes 7 HRC or more higher than that before the aging treatment, due to the aging treatment.
  • Patent Document 2 discloses the following bainite steel.
  • Patent Documents 3 and 4 disclose age-hardenable steels having a predetermined chemical composition or micro structure
  • Patent Documents 5 and 6 disclose, as a method for obtaining steel parts for mechanical structures, a method of performing aging treatment, in which steel material is cooled at a predetermined cooling velocity after hot forging, and thereafter is subjected to aging treatment in a predetermined temperature range.
  • Patent Document 1 JP2006-37177A
  • Patent Document 2 JP2011-236452A
  • Patent Document 3 WO2010/090238
  • Patent Document 4 WO2011/145612
  • Patent Document 5 WO2012/161321
  • Patent Document 6 WO2012/161323
  • a steel whose toughness has deteriorated has an increased notch susceptibility. With a higher notch susceptibility, the fatigue strength of steel becomes more likely to be affected by fine surface flaws.
  • Patent Document 1 Since the steel disclosed in Patent Document 1 is permitted to have a hardness before aging treatment of up to 40 HRC and thus a very high hardness, it is difficult to ensure machinability, specifically, cutting resistance is high so that tool life is decreased, thereby increasing cutting cost. While steels disclosed as a specific example include those whose hardness before aging treatment is less than 40 BRE, they contain not less than 1.4% of Mo, and in addition to that, their toughness is not taken into consideration at all.
  • the contents of alloying elements are adjusted so as to satisfy a particular parametric formula so that while the content of Mo is kept to be relatively low, the hardness before aging treatment (after hot forging) is not more than 300 ITV, and the hardness after aging treatment is not less than 300 HV.
  • sufficient efforts have not been made to increase toughness after aging treatment.
  • Hardness after hot forging which relates to cutting resistance and tool life is sufficiently low. Note that in the following description, the hardness after hot forging is referred to as “hardness before aging treatment”.
  • an age-hardenable steel which has a chemical composition containing not more than 1.0 mass % of Mo and in which hardness before aging treatment is not more than 290 HV, hardness increases by 25 in HV by aging treatment, and the below-described fatigue strength is not less than 350 MPa, as well as absorbed energy at 20° C. after aging treatment is not less than 16 J when evaluated by a Charpy impact test performed by using a standard specimen with a U-notch having a notch depth of 2 mm and a notch bottom radius of 1 mm according to JIS Z 2242.
  • V exhibits a precipitation peak of carbide at about 750 to 700° C. when cooled from a high temperature.
  • V since once resolved into the matrix, V will not precipitate until around 850° C., suppressing precipitation during hot forging is relatively easy.
  • V carbide is likely to precipitate at phase boundaries when austenite transforms into ferrite. Therefore, when a large amount of pro-eutectoid ferrite is generated during cooling after hot forging, since V carbide precipitates at phase boundaries thereby reducing the amount of dissolved V, it becomes not possible to secure an amount of dissolved V necessary for precipitating and hardening during aging treatment.
  • the present inventors have investigated conditions for stably obtaining a high area-fraction of bainite in the micro-structure, by varying the chemical composition of steel for a steel containing not less than 0.25 mass % of V. Further, they also investigated the age hardenability of those steels when they are subjected to aging treatment. As a result of that, the following findings (d) to (f) have been obtained.
  • the micro-structure after hot forging has close correlation with the contents of C, Mn, Cr and Mo. That is, if the contents of the above described elements are controlled such that the value represented by Formula (1), which is to be described below and shows an index of hardenability, falls within a specific range, precipitation of a large amount of pro-eutectoid ferrite, which is harmful for ensuring dissolved V, is suppressed. For this reason, a micro-structure containing bainite as a main phase, that is, a micro-structure containing not less than 70% in area fraction of bainite is obtained with ease so that it is possible to secure a sufficient amount of dissolved V.
  • Formula (1) which is to be described below and shows an index of hardenability
  • the present inventors investigated conditions to obtain absorbed energy of not less than 16 J at 20° C. after aging treatment evaluated by a Charpy impact test performed by using a standard specimen with a U-notch having a notch depth of 2 mm and a notch bottom radius of 1 mm, by preparing steels containing not less than 0.25 mass % of V, in, which contents of C, Si, Mn, Cr, Mo, and V satisfy both conditions as described in above (d) and (f), and which is subjected to hot forging and thereafter to aging treatment.
  • the following findings (g) to (i) have been obtained.
  • Elements that deteriorate toughness after aging treatment are C, V, Mo, and Ti. Among those, Ti combines with N and/or C to form TiN and/or TiC.
  • Precipitation of TiN and/or TiC may increase fatigue strength, but it significantly deteriorates toughness.
  • the intensity of action of Ti to deteriorate toughness is very high compared with V and Mo which are similar precipitation strengthening elements. For that reason, the content of Ti must be restricted as much as possible.
  • C forms cementite in steel, and may act as a starting point of cleavage fracture. Even when a steel which contains excess amounts of V and Mo with respect to C is subjected to aging treatment, some part of cementite remains V and Mo cause carbide to precipitate in the same crystal plane of matrix as a result of aging treatment, thereby accelerating the progress of cleavage fracture and deteriorating toughness. Therefore, to improve toughness, it is necessary to decrease the contents of C, V, and Mo.
  • bainite structure can be achieved by decreasing the transformation temperature from austenite to bainite. Decreasing of the transformation temperature of bainite can be achieved by increasing the contents of Mn and Cr which decrease the start temperature of bainite transformation.
  • the present invention has been made based on the above described findings, and its gist is an age-hardenable steel described below.
  • An age-hardenable steel having a chemical composition consisting of: by mass %, C: 0.05 to 0.20%, Si: 0.01 to 0.50%, Mn: 1.5 to 2.5%, S: 0.005 to 0.08%, Cr: 0.03 to 0.50%, Al: 0.005 to 0.05%, V: 0.25 to 0.50%, Mo: 0 to 1.0%, Cu: 0 to 0.3%, Ni: 0 to 0.3%, Ca: 0 to 0.005%, and Bi: 0 to 0.4%, with the balance being Fe and impurities, wherein P, Ti, and N included in the impurities are: P: 0.03% or less, Ti: less than 0.005%, and N: less than 0.0080%, and further wherein
  • F1 represented by the following Formula (1) is not less than 0.68
  • F2 represented by the following Formula (2) is not more than 0.85
  • F3 represented by the following Formula (3) is not less than 0.00
  • each symbol of element in the Formulas (1) to (3) means the content of the element in mass %.
  • the age-hardenable steel of the present invention has hardness before aging treatment of not more than 290 HV. Furthermore, using the age-hardenable steel of the present invention causes the hardness to increase by not less than 25 in HV through aging treatment performed after cutting process, and can ensure a fatigue strength of not less than 350 MPa, and an excellent toughness, that is, absorbed energy at 20° C. after aging treatment of not less than 16 J when evaluated by a Charpy impact test performed by using a standard specimen with a U-notch having a notch depth of 2 mm and a notch bottom radius of 1 mm. Therefore, the age-hardenable steel of the present invention can be quite suitably used as a starting material for mechanical parts such as for automobiles, industrial machinery, construction machinery, and the like.
  • FIG. 1 shows the shape of a uniaxial tension-compression type fatigue test specimen used in Examples. Numerical values in the FIGURE represent dimensions (unit: mm).
  • C is a crucial element in the present invention.
  • C combines with V and forms a carbide, thereby strengthening the steel.
  • C content is less than 0.05%, the carbide of V becomes not likely to precipitate, and therefore desired strengthening effect cannot be achieved.
  • C content is excessively large, the amount of C which does not combine with V and Mo, but combines with Fe to form carbide (cementite) increases, thereby deteriorating the toughness of steel. Therefore, C content is specified to be 0.05 to 0.20%.
  • the C content is preferably not less than 0.08%, and more preferably not less than 0.10%.
  • the C content is preferably not more than 0.18%, and more preferably not more than 0.16%.
  • Si is useful as a deoxidizing element during steel making, and also has an effect of dissolving into matrix and thereby increasing the strength of steel. To achieve such effects satisfactorily, Si content of not less than 0.01% is required. However, when the Si content is excessive, hot workability of steel is deteriorated and its hardness before aging treatment increases. Therefore, Si content is specified to be 0.01 to 0.50%. The Si content is preferably not less than 0.06%. Moreover, the Si content is preferably not more than 0.45%, and more preferably less than 0.35%.
  • Mn has effects of improving hardenability, and causing the micro-structure to contain bainite as a main phase. Further, Mn also has an effect of decreasing the bainite transformation temperature, thereby refining the bainite structure and improving toughness of the matrix. Further, Mn has an effect of forming MnS in steel, thereby improving chip treatability during cutting. To achieve such effects satisfactorily, Mn content needs to be at least 1.5%. However, since Mn is an element which is likely to segregate during solidification of steel, when its content is excessive, it is inevitable that variation of hardness increases within a steel part after hot forging. Therefore, Mn content is specified to be 1.5 to 2.5%. The Mn content is preferably not less than 1.6%, and more preferably not less than 1.7%. Moreover, the Mn content is preferably not more than 2.3%, and more preferably not more than 2.1%.
  • S content needs to be not less than 0.005%.
  • S content is specified to be 0.005 to 0.08%.
  • the S content is preferably not less than 0.01%.
  • the S content is preferably not more than 0.05%, and more preferably not more than 0.03%.
  • Cr has effects of improving hardenability, and causing the micro-structure to contain bainite as a main phase. Further, Cr also has an effect of decreasing the bainite transformation temperature, thereby refining the bainite structure and improving toughness of matrix.
  • Cr content is specified to be 0.03 to 0.50%.
  • the Cr content is preferably not less than 0.05%, and more preferably not less than 0.15%.
  • Al is an element having a deoxidizing effect, and to achieve such an effect, Al content needs to be not less than 0.005%. However, when Al content is excessive, coarse oxides are likely to be produced, thereby deteriorating toughness. Therefore, the Al content is specified to be 0.005 to 0.05%.
  • the Al content is preferably not more than 0.04%.
  • V 0.25 to 0.50%
  • V is the most crucial element in the steel of the present invention.
  • V has an effect of combining with C to form fine carbides during aging treatment, thereby increasing fatigue strength.
  • Mo when Mo is contained in steel, V has an effect of being compounded with Mo and precipitated by aging treatment, further increasing age hardenability.
  • V content needs to be not less than 0.25%.
  • V content is specified to be 0.25 to 0.50%.
  • the V content is preferably less than 0.45%, and more preferably not more than 0.40%.
  • the V content is preferably not less than 0.27%.
  • Mo has a relatively low precipitation temperature of carbide, and is an element which can be readily utilized for age-hardening. Mo has effects of improving hardenability, causing the micro-structure after hot forging to contain bainite as a main phase, and increasing its area fraction. Mo is compounded with V to form a carbide, thereby increasing age-hardenability. For that purpose, Mo may be contained as needed. However, since Mo is a very expensive element, an increase in its content will cause an increase in steel manufacturing cost, and also deterioration of toughness. Therefore, when Mo is contained, its content is specified to be not more than 1.0%. The content of Mo is preferably not more than 0.50%, more preferably not more than 0.40%, and further preferably less than 0.30%.
  • its content is preferably not less than 0.05%, and more preferably not less than 0.10%.
  • Each of Cu and Ni has an effect of increasing fatigue strength. Therefore, when higher fatigue strength is desired, these elements may be contained in the following range.
  • Cu has an effect of increasing fatigue strength. Therefore, Cu may be contained as needed. However, when Cu content increases, hot workability deteriorates. Therefore, when Cu is contained, its content is specified to be not more than 0.3%.
  • the Cu content is preferably not more than 0.25%.
  • its content is preferably not less than 0.1%.
  • Ni has an effect of increasing fatigue strength. Moreover, Ni also has an effect of suppressing the deterioration of hot workability due to Cu. Therefore, Ni may be contained as needed. However, increase of Ni content causes saturation of the above described effect in addition to increase of cost. Therefore, when Ni is contained, its content is specified to be not more than 0.3%. The Ni content is preferably not more than 0.25%.
  • its content is desirably not less than 0.1%.
  • the above described Cu and Ni only one of them, or two of them in combination may be contained.
  • the total content of the above described elements, when they are contained, may be 0.6% at which each of Cu and Ni contents has its upper limit value.
  • Each of Ca and Bi has an effect of prolonging tool life during cutting. Therefore, when further prolonged tool life is desired, these elements may be contained within the following range.
  • Ca has an effect of prolonging tool life. Therefore, Ca may be contained as needed. However, when Ca content increases, coarse oxides are formed, thereby deteriorating toughness. Therefore, when Ca is contained, its content is specified to be not more than 0.005%.
  • the Ca content is preferably not more than 0.0035%.
  • the Ca content is desirably not less than 0.0005%.
  • Bi has an effect of reducing cutting resistance and thereby prolonging tool life. Therefore, Bi may be contained as needed. However, when Bi content increases, hot workability deteriorates. Therefore, when Bi is contained, its content is specified to be not more than 0.4%. The Bi content is preferably not more than 0.3%.
  • the Bi content is preferably not less than 0.03%.
  • Ca and Bi only one of them, or two of them in combination may be contained.
  • the total content of these elements, when they are contained, may be 0.405% at which each of Ca and Bi contents has its upper limit value, but is preferably not more than 0.3%.
  • the age-hardenable steel of the present invention is a steel having a chemical composition consisting of the above described elements, with the balance being Fe and impurities, wherein P, Ti, and N included in the impurities are: P: 0.03% or less, Ti: less than 0.005%, and N: less than 0.0080%, and further wherein, F1 represented by the above described Formula (1) is not less than 0.68, F2 represented by the above described Formula (2) is not more than 0.85, and F3 represented by the above described Formula (3) is not less than 0.00.
  • impurities refer to those which are mixed from ores as the raw material, scrap, or manufacturing environments when steel material is industrially manufactured.
  • P is contained as an impurity and is an undesirable element in the present invention. That is, P segregates at grain boundaries, and thereby deteriorates toughness. Therefore, the P content is specified to be not more than 0.03%. The P content is preferably not more than 0.025%.
  • Ti is contained as an impurity and is a particularly undesirable element in the present invention. That is, Ti combines with N and/or C to form TiN and/or TiC, thereby causing deterioration of toughness, and particularly when its content is not less than 0.005%, toughness is significantly deteriorated. Therefore, Ti content is specified to be less than 0.005%. To ensure excellent toughness, the Ti content is preferably not more than 0.0035%.
  • N is contained as an impurity, and is an undesirable element which immobilizes V as a nitride in the present invention. That is, since V which has precipitated as a nitride will not contribute to age hardening, the N content needs to be kept low to suppress precipitation of nitride. For that purpose, the N content needs to be less than 0.0080%.
  • the N content is preferably not more than 0.0070%, and more preferably less than 0.0060%.
  • the age-hardenable steel of the present invention must satisfy the condition that F1 represented by the following Formula (1) is not less than 0.68:
  • each symbol of element in the Formula (1) means the content of that element in mass %.
  • F1 is an index for hardenability. Provided that the amount of each alloying element contained in steel is within the range described above, if F1 satisfies the above described condition, the micro-structure after hot forging will contain bainite as a main phase.
  • F1 is preferably not less than 0.70, and more preferably not less than 0.72. Moreover, F1 is preferably not more than 1.0, and more preferably not more than 0.98.
  • the age-hardenable steel of the present invention must satisfy the condition that F2 represented by the following Formula (2) is not more than 0.85:
  • each symbol of element in the Formula (2) means the content of that element in mass %.
  • F2 is an index showing hardness before aging treatment.
  • the age-hardenable steel of the present invention only satisfies the above described condition of F1
  • the hardness before aging treatment becomes excessively high and the cutting resistance during cutting process increases, thereby shortening tool life.
  • F2 is preferably not more than 0.82, and more preferably not more than 0.80. Moreover, F2 is preferably not less than 0.55, and more preferably not less than 0.60.
  • F3 not less than 0.00
  • the age-hardenable steel of the present invention must satisfy the condition that F3 represented by the following Formula (3) is not less than 0.00:
  • each symbol of element in the Formula (3) means the content of that element in mass %.
  • F3 is an index showing toughness after aging treatment. That is, only satisfying the conditions of F1 and F2 may result in deterioration of toughness after aging treatment, making it impossible to ensure targeted toughness.
  • F3 is preferably not less than 0.01.
  • the age-hardenable steel of the present invention preferably has an average block size of bainite of 15 to 60 ⁇ m.
  • block of bainite as used in the present invention refers to a region surrounded by boundaries with an orientation difference of not less than 15° when orientation analysis of the micro-structure is performed by an EBSD (Electron BackScatter Diffraction) method.
  • EBSD Electro BackScatter Diffraction
  • the average block size of bainite increases, the hardness before aging decreases, and therefore good machinability is obtained.
  • the average block size is excessively large, toughness will deteriorate.
  • the average block size is more preferably not less than 20 ⁇ m.
  • the average block size is more preferably not more than 45 ⁇ m, and further preferably not more than 30 ⁇ m.
  • the manufacturing method of the age-hardenable steel of the present invention will not be particularly limited, and it may be melted by a general method to adjust the chemical composition.
  • material to be subjected to hot forging hereafter, referred to as “material for hot forging”.
  • the above described material for hot forging may be of any kind such as a billet obtained by blooming an ingot, a billet obtained by blooming a continuous casting material, or a steel bar obtained by hot rolling or hot forging those billets.
  • the above described material for hot forging is subjected to hot forging and further to cutting process to be finished into a predetermined part shape.
  • the material for hot forging is heated at 1100 to 1350° C. for 0.1 to 300 minutes and thereafter forged such that the surface temperature after finish forging is not less than 900° C., thereafter being cooled to the room temperature with an average cooling velocity in a temperature range of 800 to 400° C. being 10 to 90° C./min (0.2 to 1.5° C./sec). After being cooled in this way, the material is further subjected to cutting process to be finished into a predetermined part shape.
  • the lower limit of this average cooling velocity is preferably 20° C./min, and the upper limit is preferably 80° C./min
  • the material is subjected to aging treatment to obtain a mechanical part such as for automobiles, industrial machinery, construction machinery, and the like, which have desired properties.
  • the above described aging treatment is performed, for example, in a temperature range of 540 to 700° C., and preferably in a temperature range of 560 to 680° C.
  • the retention time of this aging treatment is appropriately adjusted to be, for example, 30 to 1000 minutes depending on the size (mass) of the mechanical part.
  • Steels A to W in Tables 1 and 2 are steels whose chemical compositions are within the range defined in the present invention.
  • Steels X to AG in Table 2 are steels whose chemical compositions are out of the conditions defined in the present invention.
  • each steel bar was heated at 1250° C. and thereafter hot forged into a steel bar having a diameter of 60 mm.
  • Each of the hot-forged steel bars was temporarily allowed to cool to room temperature in the atmosphere. Thereafter, the steel bar was further heated at 1250° C. for 30 minutes and hot forged into a steel bar having a diameter of 35 mm with the surface temperature of the forged material at the time of finishing being kept at 950 to 1100° C. supposing that it is forged into a part shape. After hot forging, each steel bar was allowed to cool to room temperature in the atmosphere.
  • the cooling velocity during cooling in the atmosphere was measured by embedding a thermocouple at a depth of around R/2 (“R” indicates a radius of steel bar) in a steel bar, and reheating the steel bar, which had been hot-forged at the above described condition, up to around the finishing temperature for hot forging and thereafter allowing it to be cooled in the atmosphere.
  • R/2 indicates a radius of steel bar
  • measured average cooling velocity in a temperature range of 800 to 400° C. after forging was about 40° C./min (0.7° C./sec).
  • the hardness measurement was conducted in the following way. First, a specimen was prepared by transecting a steel bar, embedding it in a resin such that the cut plane became the surface to be inspected, and thereafter mirror-polishing it. Next, hardness measurement was conducted with the testing force being 9.8 N at 10 points around R/2 portion (“R” represents radius) in the surface to be inspected conforming to the “Vickers hardness test—testing method” in JIS Z 2244 (2009). Vickers hardness was determined by arithmetically averaging the values of the 10 points. It was judged that the hardness before the aging treatment was sufficiently low when the hardness was not more than 290 HV, and this was set as a target. It was also judged that the quantity of hardening was sufficiently large, when the difference of hardness in HV (hereafter, referred to as “ ⁇ HV”) between before and after the aging treatment became not less than 25, and this was set as a target.
  • ⁇ HV difference of hardness in HV
  • the measurement of area fraction of bainite in the micro-structure was conducted in the following way.
  • the specimen which was embedded in resin and mirror-polished for hardness measurement was etched with NITAL.
  • Micro-structure of the specimen after etching was photographed at a magnification of 200 by using an optical microscope.
  • the area fraction of bainite was measured by image analysis from a photographed picture. It was judged that the micro-structure became fully bainitic when the area fraction of bainite was not less than 70%, and this was set as a target.
  • the fatigue strength was investigated by sampling a uniaxial tension-compression type fatigue test specimen. That is, a smooth fatigue test specimen of a shape whose parallel portion, as shown in FIG. 1 , has a diameter of 3.4 mm and a length of 12.7 mm was taken in parallel with the forging direction (in the longitudinal direction of steel bar) from a R/2 portion of the steel bar, and was subjected to a fatigue test under conditions of room temperature, the atmosphere, a stress ratio of 0.05, and a test speed of 10 Hz.
  • the fatigue strength was determined as the maximum stress applied to the specimens which have not ruptured up to a number of stress repetition of 10 7 under the conditions described above. It was judged that the fatigue strength was sufficiently high when the fatigue strength was not less than 350 MPa, and this was set as a target.
  • the hardness before the aging treatment was not more than 290 HV, and the hardness increased by not less than 25 in HV, the fatigue strength increased to not less than 350 MPa, and further the absorbed energy in the Charpy impact test increased to not less than 16 J as the result of aging treatment, thus respectively achieving the targets so that strength and toughness after the aging treatment were successfully achieved at the same time. Further, the fact that the hardness before the aging treatment was low revealed that reduction of cutting resistance and prolongation of tool life can be expected.
  • the cut out steel bar was further heated at 1250° C. for 30 minutes and was hot forged into a steel bar having a diameter of 35 mm with the surface temperature of the forged material at the time of finishing being kept at 950 to 1100° C. supposing that it is forged into a part shape.
  • the steel bar was allowed to cool in the atmosphere, or by using a blower and mist to a temperature not more than 400° C. at various cooling velocities.
  • the hardness before aging treatment was measured by using some of the steel bars which, after being finished into a diameter of 35 mm by hot forging, was cooled to a temperature not more than 400° C. by using a blower and mist and further cooled to room temperature.
  • Example 1 The investigations of the hardnesses before and after the aging treatment, the absorbed energy in the Charpy impact test, and the fatigue strength were conducted under the same conditions as in Example 1. Moreover, target values of these were the same as in Example 1.
  • An interface between blocks has a complicated shape with unevenness. For that reason, when an observation surface of micro-structure is created in such a way to cut off the vicinity of an uneven end part of a block, it may be observed as if a block enclosed in another block was present. In such a case, measurement accuracy of the area of block will deteriorate. To eliminate such effects, when a certain block was fully enclosed in another block in a cross-sectional image, they were regarded as one block, and the area was determined from a larger block alone, neglecting the enclosed smaller block.
  • the size of block was defined as the diameter of a circle which has the same area. From the size of each block in region of 30000 ⁇ m 2 analyzed by the EBSD method, an average block size was calculated.
  • the size of each block was weighted according to the area of the block. That is, for n blocks 1 to n in an analysis region, supposing that the sizes of each block are D1, D2, Dn ( ⁇ m), and the areas thereof are S1, S2, . . . Sn ( ⁇ m 2 ), the average block size was determined as (D1 ⁇ S1+D2 ⁇ S2+ . . . +Dn ⁇ Sn)/30000.
  • the target of average block size was set to be 15 to 60 ⁇ m.
  • Table 4 shows results of each investigations described above.
  • Test No. C1 corresponds to Test No. A16 of Table 3.
  • the cooling velocity shown in Table 4 is an average cooling velocity in a temperature range of 800 to 400° C. during cooling after hot forging the steel bar having a diameter of 35 mm.
  • the measurement method of the average cooling velocity was the same as that in Example 1.
  • the average cooling velocity satisfied the average cooling velocity (10 to 90° C./min, that is, 0.2 to 1.5° C./sec) shown as one example of the method for manufacturing an age-hardenable steel of the present invention described above.
  • the average cooling velocity was faster than the aforementioned example of average cooling velocity. Comparing Test Nos. C1 to C6 to each other, it is seen that the slower the average cooling velocity, the larger the average block size of bainite becomes. Moreover, it is seen that the larger the average block size of bainite, the lower the hardness before the aging treatment becomes, and thus better machinability can be expected.
  • the age-hardenable steel of the present invention has hardness before aging treatment of not more than 290 HV, and therefore can be expected to have reduced cutting resistance and a prolonged tool life. Furthermore, using the age-hardenable steel of the present invention causes the hardness to increase by not less than 25 in HV through aging treatment performed after cutting process, and can ensure a fatigue strength of not less than 350 MPa, and an excellent toughness, that is, absorbed energy at 20° C.
  • the age-hardenable steel of the present invention can be quite suitably used as a starting material for producing mechanical parts such as for automobiles, industrial machinery, construction machinery, and so on.

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