WO2013084265A1 - Acier pour structures mécaniques et son procédé de fabrication - Google Patents

Acier pour structures mécaniques et son procédé de fabrication Download PDF

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Publication number
WO2013084265A1
WO2013084265A1 PCT/JP2011/006857 JP2011006857W WO2013084265A1 WO 2013084265 A1 WO2013084265 A1 WO 2013084265A1 JP 2011006857 W JP2011006857 W JP 2011006857W WO 2013084265 A1 WO2013084265 A1 WO 2013084265A1
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Prior art keywords
mass
less
steel
ferrite
addition
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PCT/JP2011/006857
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English (en)
Japanese (ja)
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稔 本庄
長谷　和邦
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Ｊｆｅスチール株式会社
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Priority to PCT/JP2011/006857 priority Critical patent/WO2013084265A1/fr
Priority to IN1143KON2014 priority patent/IN2014KN01143A/en
Publication of WO2013084265A1 publication Critical patent/WO2013084265A1/fr

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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
    • 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
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • 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
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
    • 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
    • C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
    • 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
    • C22C38/16—Ferrous alloys, e.g. steel alloys containing 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
    • 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
    • C21D2211/005—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

  • the present invention relates to a machine structural steel suitable for automobile parts, machine structural parts, etc., in particular, a machine structural steel that does not require tempering treatment by quenching and tempering, and a method for producing the same.
  • parts that require high strength and high toughness include carbon steel materials for machine structures represented by S45C, and low mechanical structures containing Cr and Mo. Alloy steel quenching and tempering treatment materials have been used. However, in recent years, from the viewpoint of cost reduction or CO 2 emission reduction, development of non-tempered steel that can omit the quenching and tempering treatment has been actively promoted.
  • Non-Patent Document 1 As a typical non-heat treated steel, there is a ferrite / pearlite type non-heat treated steel (for example, see Non-Patent Document 1). This is because, in the cooling process after rolling, the ferrite and pearlite transformation precipitates almost at the same time, strengthening the ferrite with V carbide and obtaining the same strength as the quenched and tempered material, but the toughness is lower than the quenched and tempered material There was a problem.
  • Patent Document 1 discloses rolling (first rolling) in which coarse austenite crystal grains before rolling are recrystallized in the austenite recrystallization region, and austenite in the austenite non-recrystallized region. It is described that strain is imparted (second rolling) and the generation of pro-eutectoid ferrite in the crystal grains is promoted by the strain, thereby obtaining a fine ferrite-pearlite structure to improve low-temperature toughness.
  • Patent Document 2 states that the surface reduction rate of rough rolling in the temperature range below T1 ° C. is 25% or less, and then the surface reduction is performed in the temperature range from (T2-200) to T2 ° C. according to the following T2. After finishing rolling with a rate of 25% or more, toughness is improved by cooling to 650 ° C. at a cooling rate of 5 ° C./s or more.
  • T1 (° C.) ⁇ 5440 / (log [V] [C] ⁇ 3.314) ⁇ 173
  • T2 (° C.) 910 ⁇ 203 [C] +44.7 [Si] ⁇ 30 [Mn] ⁇ 20 [Cu] ⁇ 15.2 [Ni] -11 [Cr] +31.5 [Mo] +104 [V] +400 [Ti] +460 [Al] +700 [P]
  • an object of the present invention is to provide a high-strength and high-toughness steel for machine structures with a non-tempered and low alloy composition.
  • the inventors manufactured steels in which the addition amount of C, Si, Mn, P, S, Al, and O was changed and the fraction of processed ferrite was changed, and the strength and toughness. Investigated earnestly. As a result, it has been found that the strength and toughness of the material are improved by optimizing the addition amount of C, Si, Mn, P, S, Al and O, and controlling the fraction of processed ferrite within an appropriate range.
  • the present invention has been completed.
  • the gist configuration of the present invention is as follows. (1) C: 0.35 to 0.60 mass%, Si: 0.1 to 1.0 mass%, Mn: 0.1-1.5% by mass, P: 0.025 mass% or less, S: 0.025 mass% or less, Al: 0.01 to 0.10% by mass and O: 0.0015% by mass or less, having a component composition consisting of the balance inevitable impurities and Fe, and comprising a ferrite and pearlite structure containing 10 to 50% processed ferrite Machine structural steel.
  • Nb 0.1% by mass or less
  • B 0.0002 to 0.005 mass%
  • Rolling with a reduction rate of 10% or more per pass in a temperature range of 3 points or less of Ar is performed at least in one pass, and the finishing temperature is (Ar 3 ⁇ 10 ° C.) to (Ar 3 ⁇ 150 ° C.)
  • a method for producing steel for machine structural use characterized in that hot rolling is performed and then left to cool.
  • Nb 0.1% by mass or less
  • C 0.35-0.60 mass%
  • C is an essential element for ensuring the necessary strength. If it is less than 0.35% by mass, the strength of the steel decreases, so 0.35% by mass or more is added. On the other hand, if it exceeds 0.60% by mass, the toughness of the steel is reduced. From the above, the C content is set to 0.35 to 0.60 mass%.
  • Si 0.1-1.0 mass% Si is an effective element for adjusting the deoxidizer and strength in the steelmaking process. To obtain these effects, 0.1% by mass or more is necessary. On the other hand, if it exceeds 1.0% by mass, the toughness is impaired, so the range is 0.1 to 1.0% by mass.
  • Mn 0.1-1.5% by mass Mn is an important element for adjusting the strength, but in order to obtain the effect, 0.1% by mass or more is necessary. On the other hand, if it exceeds 1.5% by mass, the toughness is impaired, so 0.1 to 1.5% by mass The range.
  • P and S are elements that deteriorate toughness, and it is preferable to reduce them as much as possible, but 0.025% by mass is allowed.
  • Al 0.01-0.10 mass% Al is an element added as a deoxidizer, and its effect is poor when it is less than 0.01% by mass. On the other hand, if it exceeds 0.10% by mass, the toughness is adversely affected, so Al is in the range of 0.01 to 0.10% by mass. To do.
  • O 0.0015% by mass or less
  • O is preferably as low as possible because it combines with Si and Al to form hard oxide-based nonmetallic inclusions, resulting in a decrease in toughness.
  • the O content is 0.0015% by mass or less.
  • Cr 1.0 mass% or less
  • Cu 1.0 mass% or less
  • Mo 1.0 mass% or less
  • W 1.0 mass% or less
  • Ni 1.0 mass% or less Cr
  • Cu, Mo, W and Ni solid solution strengthening elements. It is an effective element for strength adjustment. Therefore, as needed, it is possible to add any one or two or more of the above five types, preferably 0.05% by mass or more.
  • any element exceeds 1.0% by mass, the toughness decreases, and therefore, it is preferably 1.0% by mass or less.
  • Nb 0.1% by mass or less
  • Ti 0.2% by mass or less
  • V 0.15% by mass or less
  • Nb has an effect of preventing coarsening of crystal grains by forming carbonitrides and forms precipitates with C. Although it is an element useful for obtaining strength, if added over 0.1 mass%, the toughness decreases, so it was made 0.1 mass% or less.
  • Ti has an effect of fixing N in steel as TiN and preventing coarsening of crystal grains, and also forms a precipitate with C in the same manner as Nb, and thus is an element useful for obtaining strength.
  • the toughness decreases, so the content was made 0.2% by mass or less.
  • V is an element that contributes to the improvement of strength by forming precipitates with C like Nb and Ti. The effect is saturated even if added over 0.15% by mass. Further, since precipitates increase and toughness decreases on the contrary, the content is preferably 0.15% by mass or less.
  • B 0.0002 to 0.005 mass%
  • B is an element that increases the strength of the steel after tempering by increasing the hardenability, and can be contained as necessary. In order to acquire the said effect, adding at 0.0002 mass% or more is preferable. However, if added over 0.005 mass%, the toughness deteriorates. Therefore, B is preferably 0.0002 to 0.005 mass%.
  • Pb 0.01 to 0.40 mass%
  • Bi 0.01 to 0.40 mass%
  • Ca 0.0005 to 0.0100 mass%
  • Pb 0.01-0.40 mass%
  • Pb is an element that improves machinability.
  • Pb is preferably added in an amount of 0.01% by mass or more.
  • the toughness is lowered, so 0.010 to 0.40 mass% is preferable.
  • Bi 0.01-0.40 mass% Bi is an element that improves machinability. In order to acquire the effect, it is preferable to add at 0.01 mass% or more. On the other hand, if added over 0.40% by mass, the toughness is remarkably lowered, so 0.01 to 0.40% by mass is preferable.
  • Ca 0.0005 to 0.0100 mass% Ca is an element that improves machinability. In order to acquire the effect, adding at 0.0005 mass% or more is preferable. On the other hand, even if added over 0.0100% by mass, the effect is saturated, so 0.0005 to 0.0100% by mass is preferable.
  • the structure of the steel for machine structure of the present invention will be described.
  • a low-temperature transformation structure such as martensite, bainite or a mixed structure other than ferrite and pearlite as a base structure
  • steel for machine structure represented by a large diameter steel bar having a diameter of 100 mm ⁇ or more
  • the base structure is not a low-temperature transformation structure but a ferrite and pearlite structure.
  • Means for achieving high strength in the ferrite and pearlite structures include a method of increasing the pearlite fraction of the second phase, a method of further reducing the ferrite structure, and a method of hardening the ferrite by solid solution strengthening and precipitation strengthening.
  • a method of rolling in a two-phase region (austenite + ferrite) to increase a part of ferrite to a high dislocation density, etc. can be considered.
  • the method of refining ferrite is advantageous for increasing the yield stress (hereinafter referred to as YP), but the increase in tensile strength (hereinafter referred to as TS) is small.
  • YP yield stress
  • TS tensile strength
  • the method for increasing the pearlite fraction requires addition of a large amount of C.
  • excessive addition of C is not preferable because it causes a decrease in toughness as described above.
  • the method of strengthening ferrite by adding a solid solution strengthening element or a precipitation strengthening element requires a large amount of alloy elements to be added, resulting in an increase in alloy costs and a decrease in toughness.
  • the use of processed ferrite can suppress the addition of C and alloy elements to the minimum, and can increase YP and TS.
  • the method using the processed ferrite can increase the strength without controlled cooling (accelerated cooling) after hot rolling, so the thermal stress generated during cooling and the transformation stress generated along with the transformation It is possible to increase the strength while suppressing the occurrence of internal cracks due to the effect of.
  • the microstructure of the steel is a ferrite and pearlite structure containing processed ferrite in an area ratio of 10 to 50%.
  • the reason why the processed ferrite fraction is in the range of 10 to 50% of the entire steel structure in terms of the area ratio is as follows. That is, if the fraction of the processed ferrite is less than 10%, the steel cannot be sufficiently strengthened. On the other hand, if it exceeds 50%, the strength increases but the toughness decreases and the two phases (austenite + ferrite). This is because the risk of roll breakage accompanying an increase in load during zone rolling increases.
  • the processed ferrite is a ferrite introduced with work strain formed by hot rolling in a two-phase region (austenite + ferrite) below the Ar 3 transformation point. Usually, the ferrite is traced, If the length of the minor axis and the major axis is determined, and the ratio of the major axis to the minor axis (aspect ratio) is defined as ferrite having a ratio of 2 or more, the area occupied in the microstructure can be quantified. The rate can be measured.
  • the steel having the above-described component composition is melted by a usual method using a converter, an electric furnace or the like, and a usual method such as a continuous casting method or an ingot casting method is used.
  • a steel material such as slab, billet or bloom.
  • treatment such as ladle refining or vacuum degassing may be added.
  • the steel material is charged into a heating furnace, reheated, and then hot-rolled to obtain, for example, a non-tempered steel bar having desired dimensions, structure, and characteristics.
  • the reheating temperature of the steel material needs to be in the range of 900 to 1250 ° C.
  • the heating temperature is less than 900 ° C.
  • the deformation resistance during rolling becomes large, so that hot rolling becomes difficult.
  • heating above 1250 ° C may cause surface marks, increase scale loss and fuel consumption.
  • it is in the range of 900 to 1200 ° C.
  • the cumulative area reduction rate at a temperature of 3 points or less of Ar exceeds 80%, the rolling load increases and rolling becomes difficult, or the number of rolling passes increases, leading to a decrease in productivity. Furthermore, the amount of processed ferrite exceeds 50%, and the strength of the steel increases too much, leading to a decrease in toughness. Therefore, the cumulative area reduction rate at 3 points or less of Ar is 80% or less.
  • the cooling following the hot rolling It is preferable to cool the cooling following the hot rolling. This is because when accelerated cooling is performed after hot rolling, the structure becomes a low-temperature transformation structure such as martensite, bainite, or a mixed structure other than ferrite + pearlite, and it is difficult to make the structure in the cross section uniform. In addition, internal cracking is likely to occur due to the thermal stress generated during cooling and the transformation stress generated with the transformation. Therefore, it is preferable to cool the cooling following hot rolling. Specifically, the cooling may be performed at 0.5 ° C./s or less.
  • a steel bar will be specifically described as an example of steel for machine structural use.
  • Steel having the component composition shown in Table 1 is melted in a vacuum melting furnace or converter to form a bloom, and this bloom is charged into a heating furnace and heated, and then hot rolled in accordance with the conditions shown in Table 2. Hot rolled into a round bar.
  • a JIS No. 4 tensile test piece and a JIS No. 3 Charpy impact test piece were cut out from a 1/4 depth portion from the surface of the obtained rolled steel bar, and the mechanical properties were evaluated.
  • the rolling temperature was measured by installing a radiation thermometer on the entry side and the exit side of the mill. Further, the finish rolling temperature in Table 2 refers to the temperature on the exit side during final rolling. Yield strength, tensile strength, and toughness (impact value) were judged to have improved characteristics when improved by 10% or more compared to conventional S45C (reference steel).
  • Table 3 shows the processed ferrite fraction, yield strength, tensile strength, impact value, and structure evaluation results.
  • the results of Table 3 are summarized in FIGS. 1 to 3.
  • Steels B-4 to 8 satisfying the component composition, structure and production conditions of the present invention show yield values, tensile strengths and impact values that are 10% or more better than standard steels, It can be seen that while having high strength, it has high toughness.
  • the steels B-2, 3, 9 and 10 which do not have the microstructure of the present invention have yield strength, tensile strength and impact value. It can be seen that the toughness is reduced due to the standard steel level or higher strength.
  • Table 6 shows the processed ferrite fraction, yield strength, tensile strength, impact value, and structure evaluation results.
  • Steels C-1 to C-11 satisfying the component composition, structure and production condition of the present invention have yield values, tensile strengths, and impact values that are 10% or more better than those of standard steels. It can be seen that it is strong but has high toughness.

Abstract

La présente invention concerne un acier à haute résistance et haute ténacité destiné à des structures mécaniques, qui est obtenu sans trempe et avec un faible alliage. Ledit acier comprend une composition de ferrite et de perlite et présente une composition de composants qui comporte de 0,35 % à 0,60 % en masse de C, de 0,1 % à 1,0 % en masse de Si, de 0,1 % à 1,5 % en masse de Mn, au maximum 0,025 % en masse de P, au maximum 0,025 % en masse de S, de 0,01 % à 0,10 % en masse d'Al et au maximum 0,0015 % en masse de O, le reste comprenant des impuretés inévitables et du Fe, en incluant de 10 % à 50 % de ferrite traitée.
PCT/JP2011/006857 2011-12-07 2011-12-07 Acier pour structures mécaniques et son procédé de fabrication WO2013084265A1 (fr)

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PCT/JP2011/006857 WO2013084265A1 (fr) 2011-12-07 2011-12-07 Acier pour structures mécaniques et son procédé de fabrication
IN1143KON2014 IN2014KN01143A (fr) 2011-12-07 2011-12-07

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Application Number Priority Date Filing Date Title
PCT/JP2011/006857 WO2013084265A1 (fr) 2011-12-07 2011-12-07 Acier pour structures mécaniques et son procédé de fabrication

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Cited By (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN107245653A (zh) * 2017-05-27 2017-10-13 江苏金基特钢有限公司 一种用于天然气传输的钢管
CN107245654A (zh) * 2017-05-27 2017-10-13 江苏金基特钢有限公司 一种轴承钢及其制备方法
CN112063929A (zh) * 2020-09-21 2020-12-11 江阴方圆环锻法兰有限公司 新型盾构机用轴承锻件及其锻造方法

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Publication number Priority date Publication date Assignee Title
JPS62199750A (ja) * 1986-02-27 1987-09-03 Nippon Steel Corp 靭性の優れた非調質棒鋼およびその製造方法
JP2004346415A (ja) * 2003-05-26 2004-12-09 Nippon Steel Corp 超高温熱間鍛造非調質部品とその製造方法
JP2009263684A (ja) * 2008-04-22 2009-11-12 Nissan Motor Co Ltd 鋼製部品の製造方法
JP2010229475A (ja) * 2009-03-26 2010-10-14 Jfe Steel Corp 高強度高靱性熱間鍛造品の製造方法
JP2011241465A (ja) * 2010-05-21 2011-12-01 Sumitomo Metal Ind Ltd 高周波焼入れ用圧延鋼材およびその製造方法
JP2011246769A (ja) * 2010-05-27 2011-12-08 Jfe Steel Corp 機械構造用鋼およびその製造方法

Patent Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS62199750A (ja) * 1986-02-27 1987-09-03 Nippon Steel Corp 靭性の優れた非調質棒鋼およびその製造方法
JP2004346415A (ja) * 2003-05-26 2004-12-09 Nippon Steel Corp 超高温熱間鍛造非調質部品とその製造方法
JP2009263684A (ja) * 2008-04-22 2009-11-12 Nissan Motor Co Ltd 鋼製部品の製造方法
JP2010229475A (ja) * 2009-03-26 2010-10-14 Jfe Steel Corp 高強度高靱性熱間鍛造品の製造方法
JP2011241465A (ja) * 2010-05-21 2011-12-01 Sumitomo Metal Ind Ltd 高周波焼入れ用圧延鋼材およびその製造方法
JP2011246769A (ja) * 2010-05-27 2011-12-08 Jfe Steel Corp 機械構造用鋼およびその製造方法

Cited By (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN107245653A (zh) * 2017-05-27 2017-10-13 江苏金基特钢有限公司 一种用于天然气传输的钢管
CN107245654A (zh) * 2017-05-27 2017-10-13 江苏金基特钢有限公司 一种轴承钢及其制备方法
CN112063929A (zh) * 2020-09-21 2020-12-11 江阴方圆环锻法兰有限公司 新型盾构机用轴承锻件及其锻造方法

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