EP2003221A1 - Sehr dünnes hartstahlblech und verfahren zu seiner herstellung - Google Patents

Sehr dünnes hartstahlblech und verfahren zu seiner herstellung Download PDF

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EP2003221A1
EP2003221A1 EP07741011A EP07741011A EP2003221A1 EP 2003221 A1 EP2003221 A1 EP 2003221A1 EP 07741011 A EP07741011 A EP 07741011A EP 07741011 A EP07741011 A EP 07741011A EP 2003221 A1 EP2003221 A1 EP 2003221A1
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Prior art keywords
steel sheet
phase
average
major axis
thin steel
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French (fr)
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EP2003221B1 (de
EP2003221A4 (de
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Hidekuni Murakami
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Nippon Steel Corp
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Nippon Steel Corp
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    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/06—Surface hardening
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • 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
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0421—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the working steps
    • C21D8/0426—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
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0447—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment
    • C21D8/0457—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment with diffusion of elements, e.g. decarburising, nitriding
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • C21D9/48—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals deep-drawing sheets
    • 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
    • C22C38/004—Very low carbon steels, i.e. having a carbon content of less than 0,01%
    • 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
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—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
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
    • B21B1/40—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling foils which present special problems, e.g. because of thinness
    • 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
    • C21D2201/00—Treatment for obtaining particular effects
    • C21D2201/05—Grain orientation
    • 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
    • C21D2211/004—Dispersions; Precipitations
    • 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
    • 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
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0421—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the working steps
    • C21D8/0436—Cold 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
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0421—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the working steps
    • C21D8/0442—Flattening; Dressing; Flexing

Definitions

  • the present invention relates to a thin steel sheet having a sheet thickness of 0.400 mm or less which also includes a surface treated steel sheet used for electric equipments, electronic parts, building materials and metallic containers, and to a method of manufacturing the same.
  • the present application claims the benefit of priority to Japanese Patent Application No. 2006-102766 , the content of which is incorporated herein by reference.
  • a thin steel sheet having a sheet thickness of 0.400 mm or less has been used for various purposes such as for electric equipments, electronic parts, building materials and metallic containers, and a process of making a steel sheet more thin has been carried out to lower the cost of raw material.
  • a member employing such material accordingly causes decrease in its strength, and thus hardening of material is also generally required at the time of thinning the material.
  • One of obvious problem occurring in such an extra thin and hard material is deterioration in formability.
  • a thin material immediately causes breakage when constriction is occurred, and thus it is extremely important to give a uniform deformation.
  • a tensile test which is generally applied for evaluating characteristics of a steel sheet, it means that a sheet has to be hardened without turning down a uniform elongation.
  • a steel sheet for containers for which a heavy working such as drawing, ironing or tensile elongation is performed methods disclosed in Patent Documents 1 to 3 or the like have been proposed to assure the formability.
  • An object of the present invention is to prevent breakage or constriction caused by lack of uniform deformation, which is a problem occurring upon using an extra thin, hard material.
  • an object is to, for deterioration in elongation due to a hardening of material, consider the deterioration of local elongation on a priority basis so as to assure a uniform elongation and to prevent a local deformation (constriction) up to a high strained region even for the same total elongation.
  • another object of the present invention is to make clear a material condition, and to provide a steel sheet employing such the condition and a manufacturing method thereof.
  • the present inventors have carried out a research on dispersing various second phases in a steel sheet for hardening the steel sheet.
  • it belongs to a category of precipitation hardening and transformation hardening, and a material can be hardened by dispersing a second phase, according to which, of course, the formability deteriorates.
  • the inventors found out that when a second phase having a specific morphology is dispersed in a steel sheet, hardening is achieved while preventing deterioration in uniform elongation.
  • the inventors have in detail investigated morphology, amount and kind of second phase and also scopes of steel sheet materials for obtaining preferable properties, and thus completed the present invention. Key points of the present invention are as shown below.
  • the present invention relates to a thin steel sheet having a sheet thickness of 0.400 mm or less and a manufacturing method thereof.
  • a hot rolling condition is limited thereby controlling the morphology of oxide.
  • rolling and elongation of oxide in the present invention completely differs from those provided with a limit of hot rolling condition for an enameling steel sheet. More specifically, it had been very difficult to get an idea to put a rolled and elongated oxide into practical use for a thin steel sheet aimed by the present invention, according to an extension technique provided with a limit of hot rolling condition for an enameling steel sheet.
  • oxide in a thin steel sheet as for the present invention is controlled because it is an extremely unfavorable substance. This is because deformation concentrated around the oxide gives highly sensitive effect in breaking a base material as the base material itself is thin. A good example can be shown by flange formability in a process of manufacturing cans. In regard to a steel material used for such purpose, an oxide amount is strictly controlled and its production is given at a very low level.
  • a technical difference in regard to a manufacturing method of enameling steel sheet and the present invention are mentioned as follows. First, in a production of enameling steel sheet, an oxide is temporarily rolled and elongated at a hot rolling step but the oxide cracks in the following cold rolling step thereby forming many voids around the cracked oxide. All oxides in an end product are finely cracked and are in an isotropic form.
  • the oxide has to be a rolled and elongated oxide at a final stage, and thus a hot rolling step is employed as a way for this.
  • a hot rolling step is employed as a way for this.
  • an oxide rolled and elongated under hot rolling is still kept as a rolled and elongated oxide even after the cold rolling and annealing, and an anisotropic form is necessarily maintained to an end product.
  • this difference may be fundamentally exhibited by difference in the composition of oxides.
  • a compounded form of relatively soft Mn-containing oxide with hard Nb-, B-containing oxide works preferably in accelerating cracking.
  • oxide be provided as a homogeneous substance and not as a compounded product including oxides of different composition, so as to give a uniform deformation at the time of cold rolling and avoid cracking.
  • the steel of the present invention is invented on the basis of new findings such as when an oxide is rolled and elongated to a specific form and maintained as it is, a work hardening behavior thereof dramatically changes, and when a local deformation is strongly controlled, it well acts on a practical elongation capacity even in the case of a thin steel sheet.
  • a hard, extra thin material exhibiting more uniform elongation capacity up to a high strained region while preventing a local deformation (constriction) from occurring, even if the same strength and the same total elongation are employed, can be obtained.
  • a thin material is used, such as breakage due to a lack of uniform deformation and a generation of constriction.
  • the C amount is set to 0.800% or less to avoid deterioration in formability.
  • the amount is preferably 0.100% or less, more preferably 0.060% or less.
  • the amount is preferably from 0.0050 to 0.040%, more preferably from 0.0080 to 0.030%.
  • the content of C to be needed from the viewpoint of assuring the strength or the like may be low.
  • the required strength can still be achieved at the C content of 0.0050% or less.
  • the content of 0.0030% or less, as well as 0.0015% or less can also be employed. From the point of maintaining high drawability by improving an r value, it is preferable for the C amount to be small.
  • the N amount is also set to 0.800% or less to avoid deterioration in formability.
  • the amount is preferably 0.100% or less, more preferably 0.060% or less.
  • the amount is preferably from 0.0050 to 0.040%, more preferably from 0.0080 to 0.030%.
  • the content of N to be needed from the viewpoint of assuring the strength or the like may be low.
  • the required strength can still be achieved at the N content of 0.0050% or less.
  • the content of 0.0030% or less, as well as 0.0015% or less can also be employed. From the point of maintaining high drawability by improving an r value, it is preferable for the N amount to be small.
  • Si is set to 2.0% or less because at a too high content, formability or surface treatment property deteriorates.
  • oxide when oxide is used as the second phase, remaining of oxygen in the steel may become difficult or a rolled and elongated oxide which being the preferred characteristic for the present invention may be hardly obtained, as described later.
  • the Si content when carburization or nitriding is carried out for forming the second phase, there may be a case where C or N entered in the steel forms coarse Si carbide or Si nitride in a crystalline grain boundary and thus causing brittle cracks.
  • the Si content may have to be 1.5% or less, further 1.0% or less.
  • the Si amount it is preferable for the Si amount to be small.
  • the formability can be improved by setting the content to be 0.5% or less, further 0.1% or less, or even further 0.07% or less.
  • Mn is set to 2.0% or less because at a too high content, formability or surface treatment property deteriorates. Meanwhile, in the steel of the present invention, when oxide is used as the second phase, as described later, a rolled and elongated oxide which is preferable for the present invention is readily obtained. In addition, when sulfide is used for forming the second phase, a rolled and elongated sulfide can be readily obtained, and thus this element is useful. Consequently, a preferred range of Mn is from 0.05 to 1.0%, preferably from 0.15 to 0.8%, and even more preferably from 0.25 to 0.7%.
  • P is set to 0.10% or less because at a too high content, not only the formability deteriorates, but also when carburization or nitriding are performed for forming the second phase, the carburization property or nitriding property of the steel sheet is obstructed. From the point of maintaining high formability, it is preferable for the P amount to be small.
  • the formability can be improved by setting the content to be 0.05% or less, further 0.01% or less.
  • S is set to 0.100% or less or otherwise deteriorates heat-rolling ductility and becomes the cause of obstructing the casting or hot rolling.
  • Mn, Cu, TI, REM or the like when a large amount of Mn, Cu, TI, REM or the like is added and a sulfide thereof is used as the second phase that is needed for the present invention, deterioration in hot-rolling ductility is small and thus this element is useful. Consequently, a preferred range of S is from 0.015 to 0.080%, preferably from 0.025 to 0.070%, and even more preferably from 0.035 to 0.060%.
  • Al is set to 3.0% or less because at a high content, there may be a problem such as casting becomes difficult or defects on the surface increase.
  • the Al content may sometimes have to be 0.010% or less, further 0.005% or less, even further 0.002% or less, or particularly further 0.001% or less.
  • Al may serve as an element of forming an intermetallic compound such as Ni 3 Al, and exhibits a preferable effect on the dispersion of the second phase needed for the present invention.
  • the content may vary depending on the kind or amount of metallic element forming a compound together with Al, but in this case, the Al content is preferably 1.0% or more, further 1.5% or more, even further 2.0% or more.
  • O is preferably set to 0.010% or less when an oxide is not used as the second phase that provides the characteristic of the present invention because deoxidation via Al, Si, Ti or the like occurs. It is set so because when oxide in the steel becomes an isotropic form (spherical) which gives no effect for exhibiting advantages of the present invention, this element readily becomes the cause of cracking. Even in the case where an oxide is used as a useful second phase, excessive oxide may readily become the cause of cracking, and thus the O content has to be set to 0.200% or less, preferably 0.010 to 0.100%, more preferably 0.020 to 0.080%, even more preferably 0.030 to 0.050%.
  • Ti causes the increase of recrystallization temperature of the steel sheet, and significantly deteriorates passability of extra thin steel sheet subjected in the present invention in annealing. Therefore, the Ti content is set to be 4.00% or less.
  • the content may be 0.04% or less, more preferably 0.01% or less.
  • oxides, sulfides, carbides, nitrides and intermetallic compounds, of Ti can be used as the second phase that provides the characteristic of the present invention.
  • the content may vary depending on the kind or amount of an element forming the compound, but a sufficient effect can be exhibited at a content of 0.06% or more. More preferred is 0.100% or more.
  • Nb has the same effect as Ti that it causes the increase of recrystallization temperature, and significantly deteriorates passability of extra thin steel sheet subjected in the present invention in annealing. Therefore, the Nb content is set to be 4.00% or less.
  • the content may be 0.04% or less, more preferably 0.01% or less.
  • oxides, sulfides, carbides, nitrides and intermetallic compounds, of Nb can be used as the second phase that provides the characteristic of the present invention.
  • the content may vary depending on the kind or amount of an element forming the compound, but a sufficient effect can be exhibited at a content of 0.06% or more. More preferred is 0.100% or more.
  • REM also has the same effect as Ti and Nb, and as it is an expensive element, the content is set to be 4.00% or less.
  • the content may be 0.04% or less, more preferably 0.01 % or less.
  • oxides, sulfides, carbides, nitrides and intermetallic compounds, of REM can be used as the second phase that provides the characteristic of the present invention.
  • the content may vary depending on the kind or amount of an element forming the compound, but a sufficient effect can be exhibited at a content of 0.06% or more. More preferred is 0.100% or more.
  • B also has the same effect as Ti and Nb. However, its ability to form carbonitride is less than that of Ti or Nb although it may vary depending on the added amount.
  • B is added simultaneously with those elements for the purpose of forming carbide or nitride as the second phase, it causes the increase of recrystallization temperature of the steel sheet, and significantly deteriorates passability of extra thin steel sheet subjected in the present invention in annealing. Therefore, B is useful in the case where Ti or Nb content is small.
  • the upper limit is set to 0.0300% because an excessive amount results in notable cracks in a steel slab upon casting.
  • the content may be 0.0020% or less, more preferably 0.0010% or less.
  • oxides, sulfides, carbides, nitrides and intermetallic compounds, of B can be used as the second phase that provides the characteristic of the present invention.
  • the content may vary depending on the kind or amount of an element forming the compound, but a sufficient effect can be exhibited at a content of 0.0040% or more. More preferred is 0.0100% or more.
  • Cu is set to 8.00% or less because at a too high content, not only the recrystallization temperature significantly increases, but also defects in surface quality are occurred and formability or surface treatment property deteriorates.
  • a metallic Cu phase, an intermetallic compound phase or the like can also be used as the second phase.
  • a sulfide is used for forming the second phase, a rolled and elongated sulfide is readily obtained and thus this is element is useful. Consequently, a preferred range of Cu is from 0.10 to 4.00%, more preferably from 0.20 to 3.00%, even more preferably from 0.30 to 2.50%.
  • Ca is a useful element for the steel of the present invention as when a sulfide is used as the second phase, a rolled and elongated sulfide can be readily obtained.
  • Ca is usually hardly contained in a large amount in the steel due to high reactivity, and thus the amount is set to 1.00% or less.
  • a preferred range is from 0.01 to 0.50%, more preferably from 0.05 to 0.30%.
  • Ni is an expensive element, and its amount is set to 8.00% or less.
  • Ni serves as an element of forming an intermetallic compound such as Ni 3 Al, and it exhibits a favorable effect for the dispersion of the second phase needed for the present invention.
  • the amount may vary depending on the kind or amount of metallic element forming a compound together with Ni, but is preferably 1.0% or more, further 1.5% or more, even further 2.0% or more.
  • Cr is also an expensive element, and its amount is set to 20.00% or less. When a Cr compound is not used as the second phase that provides the characteristic of the present invention, there is no need of adding Cr, and the amount may be 0.06% or less, more preferably 0.02% or less.
  • oxides, sulfides, carbides, nitrides and intermetallic compounds, of Cr can be used as the second phase that provides the characteristic of the present invention.
  • the amount may vary depending on the kind or amount of an element forming the compound, but a sufficient effect can be exhibited at a content of 0.10% or more. More preferred is 0.50% or more, even more preferred is 1.5% or more, and further more preferred is 2.50% or more.
  • the content of elements other than those mentioned above is not particularly limited, but Sn, Sb, Mo, Ta, V and W are added each by an amount of 0.10% or less which in total giving a sum of amounts of 0.50% or less, so as to impart properties not provided by the present invention. With this amount, the effect of the present invention is not interfered in any way. However, it is necessary to give an attention as there may be a case where those elements form a coarse compound having an isotropic form and thus deteriorating the formability.
  • the amount of each element is preferably set to 0.010% or less and a sum of amounts of 0.050% or less, more preferably set to 0.0020% or less and a sum of amounts of 0.0050% or less, and even more preferably set to 0.0010% or less and a sum of amounts of 0.0030% or less.
  • the observation method of the second phase is not particularly limited to those defined in the present invention.
  • the morphology can be observed directly by a physical measuring equipment such as an electron microscope which allows the observation of micro regions.
  • an observation can be made by a high-power optical microscope.
  • an optical microscope or a scanning electron microscope (SEM) steel sheets a cross section of which is polished and further subjected to etching can be observed, and with a transmission electron microscope (TEM), a thin film as well as an extracted replica obtained by a SPEED method, or the like can be observed.
  • SEM scanning electron microscope
  • a residue in which a matrix is dissolved by an electrolysis extraction may also be observed.
  • the observed second phase can be identified by EDX or electron beam diffraction patterns, but the technique is not limited to these and any analytical instrument currently providing a significantly improved performance may also be used. The point is that it is fine as long as a form, size and number density, or if necessary a kind, of the second phase can be determined according to an appropriate method. It is thought that there may be a case where a full identification is difficult in some kinds that provide a composition of various phases. However, since the effect of the present invention is achieved regardless of the kind by dispersing a second phase in a specific morphology, those difficult to be identified can also be included in the present invention.
  • volume fraction and the number density when more fine nitrides are considered using more advanced analytical instrument, these values may be increased. However, the effect of the present invention still can be distinguished when a size of 0.02 ⁇ m or greater is used as an object with the use of a physical instrument of normal level.
  • the present invention has a feature of containing 0.05% or more of the second phase observed as above, having an average major axis of 0.10 ⁇ m or greater and an average minor axis of 0.05 ⁇ m or greater and satisfying average major axis/average minor axis ⁇ 2.0.
  • the size of average major axis is preferably 0.20 ⁇ m or greater, more preferably 0.50 ⁇ m or greater, even more preferably 1.00 ⁇ m or greater, even more preferably 2.00 ⁇ m or greater, even more preferably 5.00 ⁇ m or greater.
  • a too large second phase it becomes the cause of breakage in an early stage of work thereby significantly deteriorating the ductility.
  • the size is set preferably to 30 ⁇ m or less, more preferably to 20 ⁇ m or less.
  • the average major axis/average minor axis is preferably 3.0 or more, more preferably 5.0 or more, even more preferably 8.0 or more.
  • the volume fraction is preferably 0.1 % or more, more preferably 0.3% or more, even more preferably 1.0% or more, even further preferably 2.0% or more.
  • the fraction is set preferably to 20% or less, more preferably to 10% or less.
  • the number density of the second phase 0.01 pieces/ ⁇ m 2 or more when a cross section of the steel sheet is observed and 0.001 pieces/ ⁇ m 2 or more when a spatial dispersion is measured such as when a thin film is observed with extraction replica or transmission electron microscope, will exhibit a remarkable effects of the present invention.
  • the number density is preferably 0.03 pieces/ ⁇ m 2 or more, more preferably 0.1 pieces/ ⁇ m 2 or more, even more preferably 0.3 pieces/ ⁇ m 2 or more.
  • the number density is preferably 0.003 pieces/ ⁇ m 2 or more, more preferably 0.01 pieces/ ⁇ m 2 or more, even more preferably 0.03 pieces/ ⁇ m 2 or more.
  • the number density correlates with the above-mentioned size and volume fraction, and it is necessary to be careful not to extremely increase or decrease the density within the scope of not deteriorating the formability as in the size and volume fraction.
  • the second phase in the present invention is harder than an Fe phase provided as a matrix, and thus a deformation of matrix occurs on a priority basis upon a deformation of steel sheet.
  • the deformation of matrix is restricted by the second phase, work-hardening of the matrix becomes significant. Consequently, it is believed that the strain transmissibility improves and the deformation continues while being covered in a larger area thereby giving a higher uniform elongation.
  • an anisotropic second phase is dispersed, it is believed that a restriction degree in the matrix becomes greater than that in a general isotropic second phase.
  • the deformation of matrix that is a main phase making the most of the sheet by volume is definitely the reason for a uniform deformation in the steel of the present invention and not the second phase.
  • the main phase is Fe
  • a main phase in the present invention is supposed as a ferrite phase of Fe.
  • Its volume fraction is preferably 80% or more.
  • a pearlite, bainite or martensite is known as the phase mainly composed of Fe, but in the present invention, as strengthening the sheet is achieved by a dispersion of second phase, the main phase is preferably a soft and uniform phase from the viewpoint of formability.
  • the volume fraction is preferably 85% or more, more preferably 90% or more, so as to avoid deterioration in elongation capacity due to a formation of second phase in excess.
  • an orientation relationship of the second phase and the main phase is also an important matter. As already mentioned in the mechanism above, the effect of the present invention is believed to correlate with a binding state of Fe phase and the second phase.
  • an average major axis of the second phase is preferably in a ⁇ 100> orientation or a ⁇ 110> orientation of the Fe phase that is in contact with the second phase. This orientation relationship can be determined by usual electron beam diffraction or the like.
  • a kind of second phase is described next.
  • the second phase is a simple substance of or a composite compound of oxide, sulfide, carbide, nitride or an intermetallic compound
  • a remarkable effect can be obtained.
  • oxides including one or two of Fe, Mn, Si, Al, Cr, REM, Ti and Nb can be employed.
  • sulfide sulfides including one or two of Ti, Mn, Cu, Ca and REM can be employed.
  • carbide carbides including one or two of Fe, Ti, Nb, Si and Cr can be employed.
  • nitride nitrides including one or two of Fe, Ti, Nb, Al, B and Cr can be employed.
  • intermetallic compound intermetallic compounds including one or two of Fe, Ti, Nb, Al, Si and Mn can be employed.
  • carbide a pearlite composition that is normally observed for steel, in specific, a layer composition including cementite and a ferrite phase generated due to a transformation of austenite at high temperature is excluded for the present invention as it cannot provide an effect of the present invention at all.
  • metamorphic intermetallic compound there are NiAl, Ni 3 Al, Ni 3 (Al, Ti), N 2 TiAl, Ni 3 Ti, Ni 3 Mo, Ni 4 Mo, Ni 3 Nb, Co 3 W, Fe 2 Mo, Fe 2 Ti, Fe 2 (Ni, Co) and the like.
  • oxides, sulfides, carbides, nitrides and intermetallic compounds are a compound usually seen in a steel material, and a special compound is not necessarily employed. However, a special compound can still be formed to a morphology lying within the scope of the present invention.
  • the kind of the phase is not limited to those mentioned above as only the representative elements are mentioned in the above.
  • the second phase that exists in steel is not limited to one kind and a case where two or more kinds are combined is also included in the present invention. These may exist independently or may together form a composite compound. Moreover, a phase that is not included in the present invention from a morphological view can also be existed simultaneously.
  • the important matter is the morphological feature of the second phase.
  • This difference is thought to be affected by kind or amount of the second phase that can be formed in a steel sheet; a morphology difference that can be controlled by manufacture conditions as described later; and kind of the second phase itself that also correlates with a binding state with the matrix.
  • classification of preferred kind of the second phase and the element forming the second phase can be made as shown below.
  • the kind can be ranked as follows: intermetallic compound>carbide ⁇ nitride>oxide>sulfide.
  • this order is made only by estimating the effect assuming that the morphology and the amount are the same, and there may be a case where assuring the amount or controlling the morphology is difficult depending on the manufacturing method or the kind of the second phase. Thus, this order is only for a rough indication.
  • the effect of elements the following points can be mentioned.
  • oxide preferred are those including Fe, Mn and REM; while Si, Al, Cr, Ti and Nb provide a small effect.
  • sulfide preferred are Mn, Ca and REM; while Ti and Cu provide a small effect.
  • carbide preferred are Cr, Ti and Si; while Fe and Nb provide a small effect.
  • nitride preferred are Fe, Ti, B and Cr; while Nb and Al provide a small effect.
  • an intermetallic compound preferred are Fe, Al, Si and Mn; while Ti and Nb provide a small effect.
  • a region in a thickness direction of the steel sheet employed in this specification will be described with reference to FIG. 1 .
  • the terms '1/8 sheet thickness surface layer' and '1/4 sheet thickness center layer' indicate corresponding regions shown in FIG.1 .
  • a region corresponding to '1/8 sheet thickness surface layer' is present on both surfaces of the steel sheet, but those having only one '1/8 sheet thickness surface layer' on any side can also be included in the scope of the present invention.
  • the second phase which is the characteristic of the present invention is not necessarily uniformly dispersed in a whole area when distribution in a direction of the steel sheet is taken into consideration, and it may be unevenly distributed in the sheet thickness direction. It is rather better to form a multilayer constitution including a layer with many second phases and a layer with less second phases in a thickness direction, from the viewpoint of effect of the present invention. A mechanism for this is not clear, but it is believed that a layer with many second phases and a layer with less second phases restrict the deformation of one another thereby increasing the measure of work hardening, and thus a local deformation is controlled. This can be thought alternatively that an effect similar to a restricting relationship between the second phase and the matrix is occurring in macro-spaces.
  • the volume fraction of the second phase (a volume fraction of 1/8 sheet thickness surface layer)/(a volume fraction of 1/4 sheet thickness center layer) ⁇ 10 is preferable, or regarding the number density of the second phase, (a volume fraction of 1/8 sheet thickness surface layer)/(a volume fraction of 1/4 sheet thickness center layer) ⁇ 10 is preferable.
  • the ratios are preferably 20 or more, more preferably 50 or more, even more preferably 100 or more, even further preferably 200 or more.
  • it is necessary to be careful not to form too many second phases in the surface layer part because it may cause a surface defect or may cause the sheet to break readily.
  • the present invention applies only to a steel sheet having a sheet thickness of 0.400 mm or less. This is because there is no point of applying a technique limited to a uniform elongation to a steel sheet having a greater thickness as in the present invention because upon working, molding still takes place to a certain degree after the formation of constriction due to a local ductility.
  • the technique can be used usefully to an extra thin steel sheet having a thickness of preferably 0.250 mm or less, more preferably 0.200 mm or less, even more preferably 0.150 mm or less.
  • a preferred applicable material is a steel sheet satisfying a maximum strength ⁇ 350 MPa and HR30T Rockwell hardness ⁇ 54, according to a tensile test (specifically, a tensile test carried out with the use of a tensile test specimen having a parallel part of 25 mm wide and 60 mm long under conditions of a distance between marks of 50 mm and a deformation rate of 5 mm/min) carried out with the use of a JIS5 tensile test specimen. More preferred is a steel sheet satisfying a maximum strength 400 ⁇ MPa and HR30T Rockwell hardness ⁇ 57, and even more preferred is a steel sheet satisfying a maximum strength ⁇ 450 MPa and HR30T Rockwell hardness ⁇ 61.
  • the steel sheet of the present invention provides the characteristic in satisfying (uniform elongation)/(local elongation) ⁇ 1.0, according to a tensile test carried out with the use of a JIS5 tensile test specimen.
  • the ratio is preferably 1.5 or more, more preferably 2.0 or more, even more preferably 3.5 or more, even further preferably 5.0 or more.
  • the steel satisfies yield stress/maximum strength ⁇ 0.9, more preferably 0.8 or less, even more preferably 0.7 or less, even further preferably 0.6 or less, according to a tensile test carried out with the use of a JIS5 tensile test specimen.
  • a preferred embodiment includes rolling and elongating an oxide by rolling in a hot-rolling step to be modified into a preferable form. In order to do this, a certain degree of work amount is required, and a thickness of a steel slab subjected to casting is set to preferably 50 mm or more, more preferably 150 mm or more. In order for the rolled and elongated oxide to have an appropriate size, a size of the oxide before subjected to rolling and elongation is preferably between 10 ⁇ m and 25 ⁇ m.
  • the oxide is rolled and elongated by rolling and accordingly an acicular oxide which is preferable for the present invention is obtained.
  • the oxide is hardly rolled and elongated at a temperature lower than 1000°C, such as at about 900°C or below, it partly cracks, and oxides having a reasonable acicular morphology disperse at an appropriate interval in the steel sheet.
  • a temperature control upon hot-rolling a strain amount for each temperature region and also a control of strain rate so as to control softening of work-hardened ferrite, also become important.
  • a preferable effect as in the case of oxide can be obtained.
  • a case where a carbide is used as the characteristic second phase will be illustrated.
  • a carbide having a more preferable configuration from C and additive elements which are previously contained in a steel by heat treatment or the like in manufacturing processes.
  • a method of using carburization will be illustrated as the more preferable configuration.
  • the condition includes after cold rolling, performing a carburization treatment at a temperature ranging between 600 and 700°C under a condition of giving ⁇ (carburization time (sec)) * (carburization temperature (°C)) ⁇ / ⁇ (carburizing gas concentration (%)) * (cooling rate in carburization treatment (°C/sec)) ⁇ ⁇ 20, simultaneously with or after a recrystallization annealing, thereby increasing a C amount by 0.0002% or more. If the temperature is out of above range, carburization efficiency decreases at a low temperature side, and on the contrary if the temperature is too high, the configuration of the carbide may be easily isotropic.
  • the preferable configuration of the second phase can be achieved. Basically, since the carbide can be sufficiently grown with a gradual cooling treatment at a high temperature for a long time while suppressing the growth of the deposition nucleus of the carbide in a low C concentration, the development of the anisotropic second phase is remarkable.
  • the carburization condition it is preferable to control the value of the above formula such that only surface part is carburized.
  • This value may also depend on the plate thickness, and is preferably 500 or less, more preferably 200 or less.
  • the condition of atmosphere including the type of carburizing gas may be the generally known condition.
  • the carburizing method is not limited to the gas carburization illustrated herein, and the generally known carburizing method can be applied.
  • 0.0002 % or more which is the increased amount of C may seem to be very small as the increased amount, but this amount is sufficient for exhibiting the effect of the present invention in consideration of the increased amount at a surface layer of the steel plate in an extra thin material.
  • the condition includes after cold rolling, performing a nitriding treatment at a temperature ranging between 600 and 700°C under a condition of giving ⁇ (nitriding time (sec)) * (nitriding temperature (°C)) ⁇ / ⁇ (nitriding gas concentration (%))* (cooling rate in nitriding treatment (°C/sec)) ⁇ ⁇ 20, simultaneously with or after a recrystallization annealing, thereby increasing an N amount by 0.0002% or more.
  • the condition of atmosphere including the type of nitriding gas may be the generally known condition.
  • the nitriding method is not limited to the gas nitration illustrated herein, and the generally known nitriding method can be applied similar to the case of carburization.
  • the intermetallic compound is used as the second phase
  • the cooling speed is too rapid, the nucleus generation frequency of the intermetallic compound becomes high and the anisotropic growth is not occurred so that the isotropic intermetallic compound is formed with high density.
  • the manufacturing methods of various second phases illustrated herein are different depending on elements forming the objective second phase and amounts thereof and not limited to the above described ranges. If the kind of elements forming the second phase, the type and amount of the second phase to be formed, and the directionality of the configuration to be controlled are known, suitable conditions can be sought within in a general metallurgical category and it is not difficult for a person skilled in the art to identify the conditions through several trial.
  • a re-cold rolling may be performed after a recrystallization annealing for the hardness adjustment or plate thickness adjustment.
  • the rolling reduction ranging from about several % near the skin-pass which is performed for the shape adjustment up to 50% or more similar to a cold rolling is practically used.
  • the effect of the present invention is not damaged.
  • the rolling reduction is too high, an absolute value of uniform elongation becomes small.
  • a work-hardened amount in a uniform elongation region becomes small so that it is not a preferable method considering the application of the effect of the present invention.
  • the rolling reduction is preferably 30% or less, more preferably 20% or less, further preferably 10% or less, and most preferably 3% or less.
  • the effect of the present invention does not depend on the heat history and manufacturing history, after component adjustment and before annealing. Since a slab in case of performing a hot rolling is not limited to a manufacturing method such as a continuous casting process and does not depend on the heat history until reaching a hot rolling, the effect of the present invention can be achieved even with a slab reheating method, CC-DR method directly heat rolling the cast slab without reheating, and a thin slab casting omitting the rough rolling or the like. Furthermore, the effect of the present invention can be obtained even with a dual phase region rolling having a finishing temperature of ⁇ + y phases and a continuous hot rolling which rolls by connecting a rough bar, without depending on a hot rolling condition.
  • the steel of the present invention is particularly preferable when it is used for a member having a welded portion, because a uniform deformation property in a heat-affected portion is improved and the occurrence of a constricted part is suppressed.
  • the steel plate of the present invention can be used with any surface treatment. In the scope of the present invention, the steel plate is not damaged by applying the surface treatment.
  • the surface treatment includes applying tin, chrome (tin-free), Ni, zinc, aluminum or the like which is generally performed for a metal plating.
  • the effect of the present invention can be obtained with respect to a primitive plate for a laminate steel plate coated with an organic film which is used recently.
  • the steel plate of the present invention can be generally used for electric apparatuses, electronic components, architectural materials or metal containers, and also can be used in other applications if the use thereof includes the task similar to the above-described matter.
  • a hard extra-thin material exhibiting more uniform elongation capacity while preventing a local deformation (constriction) from occurring up to a high strained region, even if the same strength and the same total elongation are employed, can be obtained.

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* Cited by examiner, † Cited by third party
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US20120067469A1 (en) * 2009-05-18 2012-03-22 Hidekuni Murakami Very thin steel sheet and production method thereof
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Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US20040244885A1 (en) * 2001-10-29 2004-12-09 Hidekuni Murakami Steel sheet for vitreous enameling and method for producing the same
EP1514949A1 (de) * 2002-06-17 2005-03-16 JFE Steel Corporation PLATTE AUS FERRITISCHEM NICHTROSTENDEM STAHL MIT Ti UND HERSTELLUNGSVERFAHREN DAFÜR
WO2006027854A1 (ja) * 2004-09-09 2006-03-16 Nippon Steel Corporation 極薄容器用の鋼板およびその製造方法
EP1865085A1 (de) * 2005-03-31 2007-12-12 Kabushiki Kaisha Kobe Seiko Sho Hochfestes kaltgewalztes stahlblech mit hervorragender beschichtungshaftung, verarbeitbarkeit und wasserstofffversprödungsfestigkeit sowie stahlkomponente für ein fahrzeug
EP1950317A1 (de) * 2005-11-09 2008-07-30 Nippon Steel Corporation Stahlblech stranggussemaillierung mit hoch hervorragender unempfindlichkeit gegenüber fischschuppenbildung und herstellungsverfahren dafür

Family Cites Families (9)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH02118026A (ja) 1988-10-28 1990-05-02 Kawasaki Steel Corp 缶用鋼板の製造方法
JPH086143B2 (ja) 1990-03-06 1996-01-24 新日本製鐵株式会社 板取り性が優れた極薄溶接缶用鋼板の製造法
JP3726371B2 (ja) 1996-08-30 2005-12-14 Ｊｆｅスチール株式会社 時効硬化性が大きく、材質安定性に優れる缶用鋼板およびその製造方法
JP4213833B2 (ja) * 1999-10-21 2009-01-21 新日本製鐵株式会社 溶接部靱性に優れた高靱性高張力鋼とその製造方法
JP2002003987A (ja) 2000-06-26 2002-01-09 Nippon Steel Corp 溶接性と低温靭性に優れた低降伏比高張力鋼およびその製造方法
CN1276987C (zh) * 2001-10-19 2006-09-27 住友金属工业株式会社 具有优异的可加工性和成型精度的薄钢板及其制造方法
JP3817216B2 (ja) 2002-11-15 2006-09-06 新日本製鐵株式会社 溶接熱影響部の靭性に優れた鋼材および鋼溶接部材
JP4315844B2 (ja) * 2004-03-05 2009-08-19 株式会社神戸製鋼所 塗膜密着性に優れた高強度冷延鋼板
JP4245540B2 (ja) 2004-10-04 2009-03-25 新光機器株式会社 ハンディ式キャップチップ取外し装置

Patent Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US20040244885A1 (en) * 2001-10-29 2004-12-09 Hidekuni Murakami Steel sheet for vitreous enameling and method for producing the same
EP1514949A1 (de) * 2002-06-17 2005-03-16 JFE Steel Corporation PLATTE AUS FERRITISCHEM NICHTROSTENDEM STAHL MIT Ti UND HERSTELLUNGSVERFAHREN DAFÜR
WO2006027854A1 (ja) * 2004-09-09 2006-03-16 Nippon Steel Corporation 極薄容器用の鋼板およびその製造方法
EP1865085A1 (de) * 2005-03-31 2007-12-12 Kabushiki Kaisha Kobe Seiko Sho Hochfestes kaltgewalztes stahlblech mit hervorragender beschichtungshaftung, verarbeitbarkeit und wasserstofffversprödungsfestigkeit sowie stahlkomponente für ein fahrzeug
EP1950317A1 (de) * 2005-11-09 2008-07-30 Nippon Steel Corporation Stahlblech stranggussemaillierung mit hoch hervorragender unempfindlichkeit gegenüber fischschuppenbildung und herstellungsverfahren dafür

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
See also references of WO2007116913A1 *

Cited By (17)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US20120067469A1 (en) * 2009-05-18 2012-03-22 Hidekuni Murakami Very thin steel sheet and production method thereof
US9689052B2 (en) * 2009-05-18 2017-06-27 Nippon Steel & Sumitomo Metal Corporation Very thin steel sheet and production method thereof
EP2341156A1 (de) 2010-01-04 2011-07-06 Benteler Automobiltechnik GmbH Verwendung einer Stahllegierung in einem Warmform- und Presshärteprozess
DE102010003997A1 (de) * 2010-01-04 2011-07-07 Benteler Automobiltechnik GmbH, 33102 Verwendung einer Stahllegierung
US9163303B2 (en) 2010-04-07 2015-10-20 Toyota Jidosha Kabushiki Kaisha Austenitic heat-resistant cast steel
CN102443743A (zh) * 2010-10-09 2012-05-09 王振民 多元合金耐磨钢固定锲
US10006111B2 (en) 2011-09-07 2018-06-26 Hitachi Powdered Metals Co., Ltd. Sintered alloy and manufacturing method thereof
DE102012016645B4 (de) * 2011-09-07 2019-12-05 Hitachi Powdered Metals Co., Ltd. Sinterlegierung und Herstellungsverfahren hierfür
US9765678B2 (en) 2012-05-10 2017-09-19 Hitachi Metals, Ltd. Heat-resistant, austenitic cast steel having excellent machinability and exhaust member made thereof
US20190300993A1 (en) * 2016-07-19 2019-10-03 Nippon Steel & Sumitomo Metal Corporation Steel for Induction Hardening
US20190241997A1 (en) * 2016-07-19 2019-08-08 Nippon Steel & Sumitomo Metal Corporation Steel for Induction Hardening
US20190300992A1 (en) * 2016-07-19 2019-10-03 Nippon Steel & Sumitomo Metal Corporation Steel for Induction Hardening
US20190153574A1 (en) * 2016-07-19 2019-05-23 Nippon Steel & Sumitomo Metal Corporation Steel for Induction Hardening
US20190300994A1 (en) * 2016-07-19 2019-10-03 Nippon Steel & Sumitomo Metal Corporation Steel for Induction Hardening
US10801091B2 (en) * 2016-07-19 2020-10-13 Nippon Steel Corporation Steel for induction hardening
US10808304B2 (en) * 2016-07-19 2020-10-20 Nippon Steel Corporation Steel for induction hardening
CN108374126A (zh) * 2018-04-17 2018-08-07 东北大学 一种高强度细晶粒钢筋及其制备方法

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CN101415851B (zh) 2011-06-08
JPWO2007116913A1 (ja) 2009-08-20
CN101415851A (zh) 2009-04-22
ES2575997T3 (es) 2016-07-04
KR101065545B1 (ko) 2011-09-19
KR20080106330A (ko) 2008-12-04
WO2007116913A1 (ja) 2007-10-18
EP2003221A4 (de) 2014-12-03
JP5058978B2 (ja) 2012-10-24

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