EP3147379B1 - Plaque d'acier épaisse - Google Patents

Plaque d'acier épaisse Download PDF

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Publication number
EP3147379B1
EP3147379B1 EP15795946.1A EP15795946A EP3147379B1 EP 3147379 B1 EP3147379 B1 EP 3147379B1 EP 15795946 A EP15795946 A EP 15795946A EP 3147379 B1 EP3147379 B1 EP 3147379B1
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Prior art keywords
mass percent
content
steel plate
microstructure
percent
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EP15795946.1A
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German (de)
English (en)
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EP3147379A1 (fr
EP3147379A4 (fr
Inventor
Yusuke SANDAIJI
Masao Kinefuchi
Haruya KAWANO
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Kobe Steel Ltd
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Kobe Steel Ltd
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Priority to EP19220022.8A priority Critical patent/EP3656886A1/fr
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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
    • C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
    • 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
    • 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
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • 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
    • C22C38/38—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
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • 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

Definitions

  • the present invention relates to steel plates. Specifically, the present invention relates to a steel plate that is mainly used as materials for structures such as ships buildings, bridges, and construction machinery, has a tensile strength of 490 MPa to less than 650 MPa, and offers excellent fatigue properties.
  • portions of large structures susceptible to fatigue damage have been protected from fatigue fracture by schemes such as designing of the portions to have such a shape as to less cause stress concentration, and use of high-strength steel plates.
  • schemes such as designing of the portions to have such a shape as to less cause stress concentration, and use of high-strength steel plates.
  • the resulting structures obtained according to the schemes cause higher production cost due to a higher number of steps or due to the use of more expensive steel plates. Accordingly, demands are made to provide a technique for allowing a steel plate itself to have better fatigue properties.
  • fatigue strength in particular fatigue limit
  • a steel plate having a high fatigue limit to tensile strength ratio is considered as a steel plate having excellent fatigue properties, where the fatigue limit to tensile strength ratio is calculated by dividing the fatigue limit by the tensile strength.
  • Nonpatent Literature (NPL) 1 presents how various influencing factors affect fatigue strength.
  • the fatigue fracture process can be divided into a process (1) and a process (2). In the process (1), a load is repeatedly applied, and, finally, cracks are generated. In the process (2), the generated cracks grow and lead to rupture (breakage).
  • solid-solution strengthening, precipitation strengthening, and grain refinement are considered to be effective in the process (1), because restrainment of accumulation of dislocations is effective in this process.
  • grain refinement and second phase strengthening are considered to be effective in the process (2), because elimination or minimization of crack propagation is effective in this process.
  • Patent Literature (PTL) 1 proposes a technique in which the steel is controlled to have a two-phase microstructure including fine ferrite and hard martensite, and the difference in hardness between the two phases is specified to be 150 or more in terms of Vickers hardness. The technique is intended to lower the crack propagation rate and to contribute to a longer fatigue life after crack initiation.
  • PTL 2 proposes a technique for lowering the crack propagation rate by allowing the steel to have a mixed microstructure including fine ferrite and bainite. This technique is expected to offer longer fatigue life after crack initiation also in fatigue fracture. However, the technique lacks consideration of fatigue properties before crack initiation at all.
  • PTL 3 proposes a technique of allowing carbides to precipitate in ferrite phase so as to offer higher fatigue strength.
  • This literature lacks description about fatigue properties after crack initiation.
  • the technique in PTL 3 targets thin steel sheets and gives no consideration to toughness and other properties necessary for large structures at all.
  • JP 2012 172256 A discloses a low yield ratio high strength hot rolled steel sheet which shall have a low temperature toughness, as well as a method for manufacturing the same.
  • the present invention has been made under these circumstances and has a main object to provide a steel plate having excellent fatigue properties.
  • the present invention has achieved the objects and provides a steel plate as follows.
  • the steel plate contains C in a content of 0.02 to 0.10 mass percent, Mn in a content of 1.0 to 2.0 mass percent, Nb in a content of greater than 0 mass percent to 0.05 mass percent, Ti in a content of greater than 0 mass percent to 0.05 mass percent, Al in a content of 0.01 to 0.06 mass percent, Cu in a content of 0.1 to 0.6 mass percent, and Ni in a content of greater than 0 mass percent to 0.6 mass percent, where a ratio [Ni]/[Cu] of the Ni content [Ni] to the Cu content [Cu] is 0.5 to less than 1.2, optionally comprising Si in a content of 0.1 to 0.6 mass percent, where the total content of Si and Cu is 0.3 mass percent or more, optionally comprising, in chemical composition, at least one selected from the group consisting of
  • average equivalent circle diameter refers to an average of “equivalent circle diameters” of grains of a phase in question, where the “equivalent circle diameter” refers to the diameter of a grain of the phase in terms of a circle having an equivalent area to the grain.
  • the steel plate according to the present invention preferably further contains at least one selected from the group consisting of (b) and (c) below.
  • the steel plate may have further improved property or properties depending on the type of an element to be contained.
  • the steel plate preferably further contains at least one selected from the group consisting of
  • the present invention can practically provide steel plates that have excellent fatigue properties.
  • the inventors of the present invention made investigations of the total life of steel plates leading up to fatigue fracture and particularly of proportions of the prior-stage life leading to crack initiation and of the subsequent-stage life from crack initiation leading up to rupture. As a result, the inventors found that the prior-stage life leading to crack initiation occupies about one half of the total life leading up to fatigue fracture; and that the prior-stage life leading to crack initiation occupies a larger proportion with a decreasing stress level and a resulting increasing total life. The results indicate that increase of the total life leading up to fatigue fracture requires not only better fatigue properties after crack initiation, but also better fatigue properties leading to crack initiation. In particular, at around the fatigue limit, increase in prior-stage life is considered to be effective because the prior-stage life leading to crack initiation tends to occupy a larger proportion of the total life.
  • the inventors made various investigations on conditions for a longer prior-stage life. As a result, the inventors found that a steel plate as follows can have a longer prior-stage life, and consequently have a longer total life leading up to fatigue fracture.
  • This steel plate is appropriately controlled in the chemical composition, and conditions typically on the fraction(s) of principal phase(s), the effective grain size of grains of the phase(s), the average equivalent circle diameter of the remainder microstructure excluding the principal phase(s), and the dislocation density ⁇ as determined by X-ray diffractometry.
  • the present invention has been made based on these findings.
  • the present invention will be illustrated below.
  • the inventors made investigations on various steel plates about how elements to be added affect the fatigue strength. Consequently, the inventors found that the addition of Si and/or Cu significantly improves the fatigue strength. In general, moving dislocations, which move by repeated stress, move irreversibly due typically to cross slip, and this causes fatigue cracking. It is known that the dislocations form a cell structure in this process. The inventors found that the addition of Si and/or Cu in a total amount of 0.3 mass percent or more restrains the cell structure formation.
  • the inventors also found that other elements to be added, such as Mn and Cr, do not noticeably offer the effect of restraining dislocations from forming a cell structure, but rather lower the transformation temperature to cause the formation of lower bainite, which has a high dislocation density; and that such other elements to be added do not so much improve fatigue strength as compared with static strength.
  • the inventors prepared various steel plates under different rolling conditions and made investigations on how the rolling conditions affect the mechanical properties and fatigue strength of the resulting steel plates.
  • steel plates when caused to have a higher dislocation density typically by rapidly cooling the steel plates down to a low temperature, or by applying compression reduction (performing rolling) at a temperature equal to or lower than the Ar 3 transformation temperature, have higher static strength such as yield stress and tensile strength, but have not so higher fatigue strength as compared with the static strength, and have a lower fatigue limit to tensile strength ratio.
  • a steel plate having a dislocation density ⁇ of greater than 2.5 ⁇ 10 15 m -1 as determined by X-ray diffractometry (XRD) undergoes significant improvement in static strength due to dislocation hardening and tends to have a lower fatigue limit to tensile strength ratio.
  • the dislocation density ⁇ is preferably 2.0 ⁇ 10 15 m -1 or less, and more preferably 1.5 ⁇ 10 15 m -1 or less.
  • the dislocation density ⁇ is 5.0 ⁇ 10 13 m -1 or more in terms of lower limit.
  • Fig. 1 depicts schematic explanatory views of a steel plate according to the present invention.
  • Figs. 1(a) and 1(b) are a schematic perspective view and a schematic side view, respectively, of the steel plate according to the present invention.
  • Figs. 1(a) and 1(b) illustrates a rolling direction L, a transverse direction (width direction) W, a thickness direction D, a steel plate surface S1, and a section S2 in the thickness direction D in parallel with the rolling direction L.
  • a steel plate is allowed to have excellent fatigue properties by controlling the microstructure of a longitudinal section (namely, the section S2 in Figs. 1(a) and 1(b) ) as follows, where the longitudinal section is in parallel with the rolling direction, and where the microstructure is in a surface layer at a position adjacent to the steel plate surface S1, for example, in a surface layer at a position about 1 to about 3 mm deep from the steel plate surface S1 in the thickness direction.
  • the surface layer herein is defined to be at a portion about 1 to about 3 mm deep from the steel plate surface, in order to evaluate a surface layer of the steel plate itself excluding a scale layer, because the steel plate surface immediately after production may include the scale layer of about 0.1 to about 2 mm depth (thickness) when produced under some production conditions.
  • the ferrite and upper bainite are phases that are relatively resistant to introduction of moving dislocations upon formation of the phases, as compared with other phases. This restrains the fatigue limit to tensile strength ratio from decreasing and contributes to longer life leading to crack initiation.
  • the microstructure in the surface layer is controlled to include at least one of ferrite and upper bainite in a total fraction of 80 area percent or more.
  • the fraction of the at least one of ferrite and upper bainite is preferably 85 area percent or more, and more preferably 90 area percent or more.
  • the fraction of the at least one of ferrite and upper bainite is 100 area percent, but is typically about 98 area percent or less.
  • the effective grain size of grains is specified to be 10.0 ⁇ m or less, where the grains herein are each defined as a region surrounded by high-angle grain boundaries with a misorientation of 15° or more between adjacent grains of ferrite or upper bainite.
  • the term "effective grain size" refers to an average length of the grains in the thickness direction.
  • the effective grain size of the grains of at least one of ferrite and upper bainite is preferably 6 pm or less, and more preferably 5 pm or less.
  • the lower limit of the effective grain size of the grains of at least one of ferrite and upper bainite is typically greater than about 2 pm.
  • the upper bainite phase can have a smaller size as compared with the ferrite phase, but is attended with shear deformation upon transformation, to which moving dislocations are readily introduced
  • bainitic transformation when allowed to occur at a low temperature, often gives a lower bainite phase containing a large amount of moving dislocations.
  • the bainite transformation start temperature Bs is preferably controlled appropriately. From this viewpoint, the bainite transformation start temperature Bs calculated according to Expression (1) is preferably 640°C or higher, and more preferably 660°C or higher.
  • the remainder microstructure excluding the ferrite and the upper bainite in the surface layer is controlled to have an average equivalent circle diameter of 3.0 ⁇ m or less.
  • the remainder microstructure is controlled to have an average equivalent circle diameter of 3.0 pm or less, because the remainder microstructure, if having an average equivalent circle diameter greater than 3.0 pm, may cause toughness and other properties to significantly deteriorate.
  • the average equivalent circle diameter of the remainder microstructure is preferably 2.5 ⁇ m or less, and more preferably 2.0 pm or less in terms of upper limit; and is 0.5 pm or more in terms of lower limit.
  • the remainder microstructure excluding the ferrite and the upper bainite in the surface layer basically includes martensite, martensite-austenite constituent (MA), pearlite, and pseudo-pearlite.
  • the martensite-austenite constituent which is formed typically in cooling process after rolling, undergoes expansive transformation in its formation process, introduces moving dislocations into the matrix, and causes the steel plate to have a shorter life leading to crack initiation.
  • the proportion of the martensite-austenite constituent in the remainder microstructure in the surface layer is controlled to be an area percent of 5% or less.
  • the area percent of the martensite-austenite constituent is preferably minimized, and is more preferably 3% or less, furthermore preferably 1% or less, and most preferably 0%.
  • the steel plate according to the present invention as being incorporated with C, Mn, Nb, and other alloy elements as appropriate, is allowed to surely have a fine ferrite phase and/or an upper bainite phase.
  • the steel plate as being: controlled in elements to be added such as Si and Cu as appropriate, restrains dislocations from forming a cell structure, which causes fatigue crack initiation.
  • the steel plate can have excellent fatigue properties. From these viewpoints, the elements are controlled in the following manner.
  • Carbon (C) is important to allow the steel plate to have strength at certain level.
  • the carbon content is specified to be 0.02 mass percent or more.
  • the carbon content is preferably 0.03 mass percent or more, and more preferably 0.04 mass percent or more.
  • the steel plate if containing carbon in an excessively high content, may have excessively high strength to fail to have desired tensile strength.
  • this steel plate when undergoing accelerated cooling, may have excessive hardenability, have a large dislocation density p, and offer lower fatigue properties.
  • the carbon content is controlled to be 0.10 mass percent or less, and is preferably 0.08 mass percent or less, and more preferably 0.06 mass percent or less.
  • Manganese (Mn) has a significance to ensure hardenability so as to give a fine microstructure.
  • the Mn content is specified to be 1.0 mass percent or more.
  • the Mn content is preferably 1.2 mass percent or more, and more preferably 1.4 mass percent or more.
  • the steel plate if containing Mn in an excessively high content, may have excessive hardenability, have a higher dislocation density p, and fail to have sufficient fatigue properties.
  • the Mn content is controlled to be 2.0 mass percent or less, and is preferably 1.8 mass percent or less, and more preferably 1.6 mass percent or less.
  • Nb greater than 0 mass percent to 0.05 mass percent
  • Niobium (Nb) is effective for better hardenability and for a finer microstructure.
  • the Nb content is preferably controlled to be 0.01 mass percent or more, and more preferably 0.02 mass percent or more.
  • the steel plate if containing Nb in an excessively high content, may have excessive hardenability and fail to have desired fatigue properties.
  • the Nb content is controlled to be 0.05 mass percent or less, and is preferably 0.04 mass percent or less, and more preferably 0.03 mass percent or less.
  • Titanium (Ti) effectively contributes to better hardenability and, simultaneously, forms TiN to allow the heat-affected zone upon welding to have a finer microstructure and to restrain reduction in toughness.
  • the Ti content is preferably 0.01 mass percent or more, and more preferably 0.02 mass percent or more.
  • Ti if contained in an excessively high content, may form coarse TiN particles and may cause the steel plate to have properties such as toughness at lower levels.
  • the Ti content is controlled to be 0.05 mass percent or less, and is preferably 0.04 mass percent or less, and more preferably 0.03 mass percent or less.
  • Aluminum (Al) is useful for deoxidation and, if contained in a content less than 0.01 mass percent, may fail to offer effective deoxidation.
  • the Al content is preferably 0.02 mass percent or more, and more preferably 0.03 mass percent or more.
  • the steel plate, if containing Al in an excessively high content may have excessive hardenability, have a higher dislocation density p, and fail to offer desired fatigue properties.
  • the Al content is controlled to be 0.06 mass percent or less, and is preferably 0.05 mass percent or less, and more preferably 0.04 mass percent or less.
  • Silicon (Si) contributes to solid-solution strengthening to a large extent and is necessary for ensuring the strength of the base metal Simultaneously, this element restrains the movements of dislocations and restrains the cell structure formation.
  • the Si content is specified to be 0.1 mass percent or more.
  • the Si content is preferably 0.2 mass percent or more, and more preferably 0.3 mass percent or more.
  • the steel plate, if containing Si in an excessively high content may include the remainder microstructure formed in excess and coarsely and may suffer from reduction in other properties such as toughness.
  • the Si content is controlled to be 0.6 mass percent or less, and is preferably 0.55 mass percent or less, and more preferably 0.5 mass percent or less.
  • Copper (Cu) restrains the cross slip of dislocations and effectively restrains the cell structure formation.
  • the Cu content is specified to be 0.1 mass percent or more.
  • the Cu content is preferably 0.2 mass percent or more, and more preferably 0.3 mass percent or more.
  • the steel plate, if containing Cu in an excessively high content may not only have excessive hardenability, but also become susceptible typically to cracking upon hot working.
  • the Cu content is controlled to be 0.6 mass percent or less, and is preferably 0.55 mass percent or less, and more preferably 0.5 mass percent or less.
  • Si and Cu can offer the common activity of restraining cell structure formation of dislocations.
  • the steel plate may contain these elements in combination.
  • the effect of restraining cell structure formation of dislocations by Si and Cu is effectively offered when the total content of Si and Cu ([Si] + [Cu]) is 0.3 mass percent or more.
  • the total content is preferably 0.4 mass percent or more.
  • a preferred upper limit of the total content ([Si] + [Cu]) is the total of the preferred upper limits of the two elements.
  • Ni greater than 0 mass percent to 0.6 mass percent
  • Nickel (Ni) effectively contributes to better hardenability and contributes to a finer microstructure. Simultaneously, this element effectively restrains cracking upon hot working, where the cracking may more readily occur by the addition of Cu.
  • Ni is preferably contained in a content of 0.1 mass percent or more, and more preferably 0.2 mass percent or more.
  • the steel plate if containing Ni in an excessively high content, may have excessive hardenability, have an excessively high dislocation density p, and thereby fail to have desired fatigue properties.
  • the Ni content is controlled to be 0.6 mass percent or less, more preferably 0.5 mass percent or less, and furthermore preferably 0.4 mass percent or less.
  • the steel plate if having an excessively high Ni content [Ni] with respect to the Cu content [Cu], may hardly enjoy the effect of restraining cell structure formation of dislocations by Cu.
  • the ratio ([Ni]/[Cu]) of the Ni content [Ni] to the Cu content [Cu] is controlled to be less than 1.2, and more preferably 1.1 or less.
  • the ratio ([Ni]/[Cu]) is 0.5 or more in terms of lower limit.
  • the steel plate according to the present invention includes the elements as mentioned above as a basic composition, with the remainder consisting of approximately iron. However, it is naturally accepted that inevitable impurities such as P, S, and N are contained in the steel The inevitable impurities are brought into the steel in circumstances of raw materials, facility materials, and production equipment. It is also effective that the steel plate according to the present invention positively contains one or more of elements below.
  • the steel plate can have a still better property or properties according to the type(s) of elements) to be contained.
  • Vanadium (V), chromium (Cr), and molybdenum (Mo) effectively allow the steel plate to have better hardenability and to have a finer microstructure.
  • the steel plate preferably contains each of V in a content of 0.01 mass percent or more, Cr in a content of 0.1 mass percent or more, and Mo in a content of 0.01 mass percent or more alone or in combination.
  • the steel plate if containing at least one of these elements in an excessively high content, may have excessive hardenability, have an excessively high dislocation density p, and fail to have desired fatigue properties.
  • V, Cr, and Mo are preferably controlled to be respectively 0.5 mass percent or less, 1.0 mass percent or less, and 0.5 mass percent or less.
  • the contents of V, Cr, and Mo are more preferably controlled to be respectively 0.4 mass percent or less, 0.8 mass percent or less, and 0.4 mass percent or less.
  • Boron (B) contributes to better hardenability and, in particular, restrains a coarse ferrite phase from forming, and thereby allows a fine upper bainite phase to form more readily.
  • the boron content is preferably controlled to be 0.0005 mass percent or more, and more preferably 0.001 mass percent or more.
  • the steel plate if containing boron in an excessively high content, may have excessive hardenability, have an excessively high dislocation density p, and fail to have desired fatigue properties.
  • the boron content is preferably controlled to be 0.005 mass percent or less, and more preferably 0.004 mass percent or less.
  • the thickness of the steel plate according to the present invention is not limited, but having an excessively small thickness, may less offer longer crack propagation life. From this viewpoint, the steel plate has a thickness of preferably 6 mm or more, and more preferably 10 mm or more.
  • the steel plate according to the present invention meets the conditions (requirements) and is not limited in production method. However, it is preferred to control production conditions as mentioned below, so as to give the microstructure morphology for better fatigue properties.
  • the production conditions are conditions in a series of production process for the steel plate using a slab, such as a slab, having a chemical composition within the ranges.
  • a steel is made via ingot making and casting, and is subjected to hot rolling.
  • the production conditions include the heating temperature before hot rolling; the cumulative compression reduction in the entire hot rolling process; the finish-rolling temperature; the average cooling rate from the finish-rolling temperature or 800°C, whichever is lower, down to 600°C; and the cooling stop temperature.
  • the slab is preferably heated up to a temperature range of 1000°C to 1200°C, and more preferably up to 1050°C or higher.
  • the heating is preferably performed up to a temperature range of 1000°C or higher so as to eliminate or minimize coarsening of grains and to still ensure a cumulative compression reduction in hot rolling of 70% or more, as mentioned below.
  • the heating if performed up to an excessively high temperature of higher than 1200°C, may fail to contribute to refinement (size reduction) of the microstructure even when sufficient compression reduction is applied.
  • the heating temperature is preferably controlled to be 1200°C or lower, and more preferably 1150°C or lower.
  • the cumulative compression reduction in the entire hot rolling process is preferably 70% or more, and more preferably 75% or more.
  • sufficient compression reduction is to be applied in the non-recrystallization temperature range.
  • the finish-rolling temperature is preferably controlled within the range of the Ar 3 transformation temperature to the (Ar 3 transformation temperature + 150°C) so as to ensure desired fine microstructure and to still restrain excessive dislocations from being introduced into the microstructure after rolling (as-rolled microstructure).
  • the finish-rolling temperature is more preferably controlled within the range of (the Ar 3 transformation temperature + 20°C) to (the Ar 3 transformation temperature + 100°C).
  • Ar 3 transformation temperature 910 ⁇ 230 C + 25 Si ⁇ 74 Mn ⁇ 56 Cu ⁇ 16 Ni ⁇ 9 Cr ⁇ 5 Mo ⁇ 1620 Nb
  • [C], [Si], [Mn], [Cu], [Ni], [Cr], [Mo], and [Nb] represent contents (in mass percent) respectively of C, Si, Mn, Cu, Ni, Cr, Mo, and Nb.
  • cooling is preferably performed at an average cooling rate of 15°C/second or less from the finish-rolling temperature or 800°C, whichever is lower, down to 600°C or lower.
  • the cooling if performed at an average cooling rate greater than 15°C/second, may cause the microstructure transformation to complete at an approximately low temperature unless a process such as isothermal holding is performed. This causes excessive introduction of dislocations and fails to give desired fatigue properties.
  • the average cooling rate is more preferably 10°C/second or less.
  • the cooling at the average cooling rate may be stopped at a temperature (namely, cooling stop temperature) of 500°C or higher. This restrains coarse ferrite phase formation and ensures a fine ferrite or upper bainite phase.
  • the cooling if stopped at a temperature lower than 500°C, may cause the transformation to complete at a low temperature, cause excessive dislocations to be introduced, and fail to give desired fatigue properties.
  • the temperature range within which cooling is performed at the average cooling rate is from 800°C down to 600°C when the finish-rolling temperature is higher than 800°C; and is from the finish-rolling temperature down to 600°C when the finish-rolling temperature is lower than 800°C.
  • the average cooling rate in terms of lower limit is preferably 3.0°C/second or more, from the viewpoint of microstructure control in the steel plate.
  • Ingots of steels having chemical compositions corresponding to Steels A to W as given in Table 1 were made via melting and casting according to a common ingot-making technique, subjected to hot rolling under conditions of rolling condition types "a" to "l” given in Table 2, and yielded steel plates having a thickness of 20 mm.
  • Table 1 an element indicated with “-” was not added; and the symbol “[Si]+[Cu] "refers to the total content of Si and Cu.
  • the Ar 3 transformation temperatures given in Table 1 are values determined according to Expression (5).
  • the term “entire hot rolling process cumulative compression reduction” refers to the cumulative compression reduction in the entire hot rolling process.
  • the steel plates were each subjected to measurements of the microstructure and effective grain size of the steel plate, the size of the remainder microstructure as a second phase, the tensile strength, the fatigue properties, and the dislocation density p, according to procedures as follows. Test specimens in all the measurements were sampled so that the measurement position be a position 3 mm deep from the steel plate surface.
  • a sample was cut out at a position 3 mm deep from the steel plate surface so as to expose a plane in parallel with the rolling direction of the steel plate and in perpendicular to the steel plate surface. This was polished using wet emery papers of #150 to #1000 and was then polished to a mirror-smooth state using a diamond abrasive as an abrasive.
  • the mirror-smooth test specimen was etched with 2% nitric acid-ethanol solution, i.e., Nital solution, the etched test specimen was observed in three view fields in an observation area of 3.71 ⁇ 10 -2 mm 2 at 400-fold magnification, images of which were taken and analyzed using an image analyzing software Image Pro Plus ver.
  • the effective grain size of ferrite and/or upper bainite was analyzed at a position 3 mm deep from the steel plate surface in a longitudinal section in parallel with the rolling direction of the steel plate.
  • the measurement was performed by scanning electron microscope (SEM)-electron backscatter pattern analysis (EBSP). Specifically, a grain size was measured, where the "grain” is defined as a region surrounded by a high-angle grain boundary having a misorientation between adjacent grains of 15° or more.
  • the measurement was performed using an EBSP system (trade name OIM) supplied by TEX SEM Laboratories in combination with a SEM, in a measurement area of 200 ⁇ m by 200 pm at a measurement step (interval) of 0.5 pm.
  • a measurement point having a confidence index of less than 0.1 was excluded from the analysis object, where the confidence index indicates the reliability of a measurement orientation.
  • the cut lengths of the grain boundaries thus determined were measured at 100 points in the thickness direction, and an average of the cut lengths was defined as the effective grain size.
  • a measurement with an effective grain size of 2.0 ⁇ m or less was determined as a measurement noise and excluded.
  • the observation area was determined as a region around the position 3 mm deep from the steel plate surface with a spread of 100 pm on both sides in the thickness direction.
  • the size of the remainder microstructure excluding the ferrite and the upper bainite was determined in the following manner.
  • a sample was cut out at a position 3 mm deep from the steel plate surface so as to expose a plane in parallel with the rolling direction of the steel plate and in perpendicular to the steel plate surface. This was polished using wet emery papers of #150 to #1000 and was then polished to a mirror-smooth state using a diamond abrasive as an abrasive.
  • the mirror-smooth test specimen was etched with 2% nitric acid-ethanol solution, i.e., Nital solution, the etched test specimen was observed in an observation area of 3.71 ⁇ 10 -2 mm 2 at 400-fold magnification.
  • the observation area was determined as a region around the position 3 mm deep from the steel plate surface with a spread of 100 pm on both sides in the thickness direction. Images of the observed test specimen were taken and analyzed using the image analyzing software, an area per one grain of the remainder microstructure was calculated, and the equivalent circle diameter of grains of the remainder microstructure was determined from the calculated area. In this experimental example, measurements in three view fields were averaged, and the average was defined as the equivalent circle diameter.
  • the area percentage of MA was determined in the following manner.
  • the mirror-smooth test specimen after polishing to a mirror-smooth state was etched with a LePera etchant and observed in an observation area of 3.71 ⁇ 10 -2 mm 2 at 400-fold magnification.
  • a phase corroded to white was defined as the MA, images of which were taken and analyzed using the image analyzing software to fractionate phases. Measurements in five view fields were averaged, and the average was defined as the area percentage of MA.
  • the LePera etchant was a 5:6:1 mixture of a solution A, a solution B, and ethanol
  • the solution A was a solution of 3 g of picric acid in 100 ml of ethanol.
  • the solution B was a solution of 1 g of sodium disulfite in 100 ml of distilled water.
  • the tensile strength TS was measured by sampling a tensile test specimen having a thickness of 4 mm and a gauge length of 35 mm from each steel plate at a position 2 to 6 mm deep from the steel plate surface, and subjecting the test specimen to a tensile test according to JIS Z 2241:2011.
  • the fatigue properties were determined in the following manner.
  • a steel plate sample having a thickness of 4 mm was cut out from each steel plate at a position 2 to 6 mm deep from the steel plate surface, from which a test specimen as illustrated in Fig. 2 was prepared.
  • the test specimen surface was polished with emery papers up to #1200 to eliminate or minimize influence of surface conditions.
  • the resulting test specimen was subjected to a fatigue test using a servo-electric hydraulic fatigue tester supplied by INSTRON Co., Ltd. under conditions as follows.
  • the fatigue properties are affected by the tensile strength TS.
  • a 5000000-cycle fatigue limit to tensile strength ratio was determined, and a sample, when having a 5000000-cycle fatigue limit to tensile strength ratio of greater than 0.51, was accepted herein.
  • the 5000000-cycle fatigue limit to tensile strength ratio is a value determined by dividing a 5000000-cycle fatigue limit by the tensile strength TS.
  • the 5000000-cycle fatigue limit was determined in the following manner.
  • test specimen was subjected to a fatigue test at such a stress amplitude as to give a stress amplitude ⁇ a to tensile strength TS ratio ( ⁇ a/TS) of 0.51, and whether the test specimen underwent rupture upon the 5000000th cycles was examined.
  • the dislocation density ⁇ was determined by subjecting each sample to X-ray diffractometry to determine a half peak width (full-width at half maximum) of ⁇ -Fe, and calculating the dislocation density from the half peak width.
  • An analyzer used herein was an X-ray diffractometer RAD-RU300 (trade name, supplied by Rigaku Corporation), with a cobalt tube as a target.
  • the true half peak width ⁇ was calculated from ⁇ m and ⁇ s according to Expression (8), and this was substituted into Expression (7), based on which ⁇ oos ⁇ / ⁇ - sin ⁇ / ⁇ was plotted. Three points, i.e., (110), (211), and (220) points were fitted by the method of least squares.
  • the strain ⁇ was calculated from the slope (2 ⁇ ) of the fitting line and was substituted into Expression (6) to calculate the dislocation density ⁇ .
  • Table 3 presents, of each steel plate, the microstructure, the effective grain size, the remainder microstructure size, the tensile strength TS, the fatigue properties, and the dislocation density ⁇ .
  • Test number ' Steel Rolling condition type Tensile strength TS (MPa) Microstructure* of steel plate surface layer Total of ferrite and upper bainite in steel plate surface layer (area percent) Effective grain size ( ⁇ m) Remainder microstructure size ( ⁇ m) MA fraction in steel plate surface layer (area percent) ⁇ [ ⁇ 10 13 m -1 ]
  • Fatigue properties 1 A a 581 F+B 95 5.5 1.1 1.1 1.2 no rupture 3 C a 529 F+B 94 4.9 0.8 0.7 1.3 no rupture 4
  • D a 630 F+B 93 4.6 0.9 0.1 1.7 no rupture 5
  • E a 559 F+B 92 6.2 1.0 0.5 0.9 no rupture 7 G a 536 F+B 94 5.7 1.4 0.7 0.8 no rupture 8 H a 610 F+
  • Test Nos.1 to 17 were produced under appropriately controlled conditions using steels having appropriately controlled chemical compositions, met the conditions in the surface layer specified in the present invention, and offered excellent fatigue properties.
  • Test Nos.18 to 34 were samples failing to meet at least one of the conditions specified in the present invention, and each had poor fatigue properties.
  • Test No. 18 employed a steel plate derived from Steel K having a low carbon content and failed to have a tensile strength TS at the predetermined level. Accordingly, other properties than the microstructure were not evaluated in this sample.
  • Test No. 19 employed a steel plate derived from Steel L having an excessively high carbon content and had an excessively high tensile strength TS. Accordingly, other properties than the microstructure were not evaluated in this sample.
  • Test No. 20 employed a steel plate derived from Steel M not meeting the condition that "the total content of Si and Cu is 0.3% or more", failed to restrain cell structure formation of dislocations, and had inferior fatigue properties.
  • Test No. 21 employed a steel plate derived from Steel N having an excessively high Si content, had an excessively large size of the remainder microstructure, and had inferior fatigue properties.
  • Test No. 22 employed a steel plate derived from Steel O having an excessively high Mn content, had a high tensile strength TS and a high dislocation density p, and offered inferior fatigue properties.
  • Test No. 23 employed a steel plate derived from Steel P having an excessively low Mn content, failed to have a tensile strength TS at the predetermined level, had an excessively large effective grain size, and offered inferior fatigue properties.
  • Test No. 24 employed a steel plate derived from Steel Q having an excessively high Cu content, had an excessively high dislocation density p, and offered inferior fatigue properties.
  • Test No. 25 employed a steel plate derived from Steel R having an excessively high Ni content and not meeting the condition: [Ni]/[Cu] ⁇ 1.2. This sample had an excessively high dislocation density p, and offered inferior fatigue properties.
  • Test No. 26 employed a steel plate derived from Steel S having an excessively high Cr content, had an excessively high dislocation density p, and offered inferior fatigue properties.
  • Test No. 27 employed a steel plate derived from Steel T having an excessively high Mo content, had an excessively high dislocation density p, and offered inferior fatigue properties.
  • Test No. 28 employed a steel plate derived from Steel U having an excessively high V content, had an excessively high dislocation density p, and offered inferior fatigue properties.
  • Test No. 29 employed a steel plate derived from Steel V having a bainite transformation start temperature Bs lower than 640°C, had an excessively high dislocation density p, and offered inferior fatigue properties.
  • Test No. 30 was a sample produced via rolling under conditions of the type g with an excessively high heating temperature in hot rolling, had an excessively large effective grain size, and offered inferior fatigue properties.
  • Test No. 31 was a sample produced via rolling under conditions of the type h with an excessively low cumulative compression reduction in hot rolling, had an excessively large effective grain size, and offered inferior fatigue properties.
  • Test No. 32 was a sample produced via rolling under conditions of the type i with an excessively low finish-rolling temperature, had an excessively high dislocation density p, and offered inferior fatigue properties.
  • Test No. 33 was a sample produced via rolling under conditions of the type j with an excessively high average cooling rate down to 600°C, had an excessively high dislocation density p, and offered inferior fatigue properties.
  • Test No. 34 was a sample produced via rolling under conditions of the type k with an excessively low cooling stop temperature, had an excessively high dislocation density p, and offered inferior fatigue properties.

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Claims (2)

  1. Plaque d'acier comprenant :
    C en une teneur de 0,02 à 0,10 % en masse ;
    Mn en une teneur de 1,0 à 2,0 % en masse ;
    Nb en une teneur supérieure à 0 % en masse jusqu'à 0,05 % en masse ;
    Ti en une teneur supérieure à 0 % en masse jusqu'à 0,05 % en masse ;
    Al en une teneur de 0,01 à 0,06 % en masse ;
    Cu en une teneur de 0,1 à 0,6 % en masse ; et
    Ni en une teneur supérieure à 0 % en masse à 0,6 % en masse, où le rapport [Ni]/[Cu] de la teneur en Ni [Ni] à la teneur en Cu [Cu] est compris entre 0,5 et moins de 1,2 ;
    comprenant éventuellement du Si en une teneur de 0,1 à 0,6 % en masse ;
    où la teneur totale en Si et Cu est de 0,3 % en masse ou plus,
    comprenant éventuellement, en composition chimique, au moins un élément choisi dans le groupe constitué de :
    (b) au moins un élément choisi dans le groupe constitué de :
    V en une teneur supérieure à 0 % en masse à 0,5 % en masse ;
    Cr en une teneur supérieure à 0 % en masse jusqu'à 1,0 % en masse ou moins ; et
    Mo en une teneur supérieure à 0 % en masse à 0,5 % en masse ; et
    (c) B en une teneur supérieure à 0 % en masse à 0,005 % en masse,
    le reste étant constitué de fer et d'impuretés inévitables,
    dans laquelle une microstructure d'une couche superficielle de la plaque d'acier comprend au moins un élément parmi la ferrite et la bainite supérieure dans une fraction totale de 80 % de surface à 100 % de surface, telle que déterminée par le procédé de mesure définie dans la description sous le titre « Steel Plate Surface Layer Microstructure » (« Microstructure de couche superficielle de plaque d'acier »),
    dans laquelle, parmi la microstructure de la couche superficielle, la microstructure restante, à l'exclusion de la ferrite et de la bainite supérieure, présente éventuellement une fraction de martensite-austénite de 0 % de surface à 5 % de surface, telle que déterminée par le procédé de mesure définie dans la description sous le titre « Remainder Microstructure Size » (« Taille de microstructure restante »),
    dans laquelle les grains dudit au moins un élément parmi la ferrite et la bainite supérieure présentent une taille de grain effective de 2 µm à 10,0 µm, où la taille de grain effective se réfère à une longueur moyenne des grains dans le sens de l'épaisseur, telle que déterminée par le procédé de mesure définie dans la description sous le titre « Ferrite and Upper Bainite Effective Grain Sizes in Surface Layer » (« Taille effective de grains de ferrite et de bainite supérieure dans une couche superficielle »),
    dans laquelle, parmi la microstructure de la couche superficielle, des grains d'une microstructure restante excluant la ferrite et la bainite supérieure ont un diamètre de cercle équivalent moyen de 0,5 µm à 3,0 µm, tel que déterminé par le procédé de mesure définie dans la description sous le titre « Remainder Microstructure Size » (« Taille de microstructure restante »), et
    dans laquelle la plaque d'acier présente une densité de dislocation ρ de 5,0 x 1013 m-1 à 2,5 x 1015 m-1, déterminée par diffractométrie aux rayons X avec le procédé de mesure définie dans la description sous le titre « Dislocation Density ρ »(« Densité de dislocation ρ »).
  2. Plaque d'acier selon la revendication 1,
    dans laquelle la plaque d'acier a une température de début de transformation de bainite Bs de 640 °C ou plus, où la température de début de transformation de bainite est calculée à partir de la composition chimique selon l'Expression (1) : Bs ° C = 830 − 270 C − 90 Mn − 37 Ni − 70 Cr − 83 Mo
    Figure imgb0009
     où [C], [Mn], [Ni], [Cr] et [Mo] représentent les teneurs (en % en masse) respectivement de C, Mn, Ni, Cr, et Mo.
EP15795946.1A 2014-05-22 2015-05-15 Plaque d'acier épaisse Active EP3147379B1 (fr)

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WO2018034071A1 (fr) * 2016-08-19 2018-02-22 株式会社神戸製鋼所 Tôle d'acier épaisse et son procédé de production
CN109023048B (zh) * 2018-08-06 2020-08-25 首钢集团有限公司 一种460MPa级高强抗震耐火耐候钢热轧卷板及其生产方法
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JP2007197823A (ja) * 2005-12-28 2007-08-09 Jfe Steel Kk 低降伏比５５０ＭＰａ級高張力厚鋼板およびその製造方法
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EP3147379A1 (fr) 2017-03-29
JP2016000855A (ja) 2016-01-07
CN106460114A (zh) 2017-02-22
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JP6472315B2 (ja) 2019-02-20
EP3656886A1 (fr) 2020-05-27

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