CN109715842A - H profile steel and its manufacturing method - Google Patents

H profile steel and its manufacturing method Download PDF

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Publication number
CN109715842A
CN109715842A CN201780057895.4A CN201780057895A CN109715842A CN 109715842 A CN109715842 A CN 109715842A CN 201780057895 A CN201780057895 A CN 201780057895A CN 109715842 A CN109715842 A CN 109715842A
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steel
flange
content
profile steel
profile
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CN109715842B (en
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沟口昌毅
市川和利
杉山博一
清家彻哉
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Nippon Steel Corp
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Nippon Steel Corp
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
    • C—CHEMISTRY; METALLURGY
    • 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
    • C21D8/005—Modifying the physical properties by deformation combined with, or followed by, heat treatment of ferrous alloys
    • 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
    • B21B1/08—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 structural sections, i.e. work of special cross-section, e.g. angle steel
    • B21B1/088—H- or I-sections
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/48—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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/001—Austenite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/005—Ferrite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/008—Martensite

Abstract

A kind of H profile steel, as its chemical component, contain C, Si, Mn, Nb, V, Ti, N, as its metal structure, ferrite comprising 60% more than and less than 100 area %, the ferritic average grain diameter be 1~30 μm, flange with a thickness of 20~140mm, stretching yield stress is 385~530MPa, and the Charpy impact absorption at -20 DEG C can be 100J or more.

Description

H profile steel and its manufacturing method
Technical field
The present invention relates to intensity and the thick H profile steels and its manufacturing method of excellent in low temperature toughness.The application is based on On December 21st, 2016 claims priority at patent application 2016-248181 of Japanese publication, here cites its content.
Background technique
In recent years, enlarged, the high stratification of the buildings such as high building is promoting, as intensity required in structure Thick steel are utilized in component.But generally, for steel material, the thickness of product more increases, and intensity ensures to get over Difficulty, moreover, toughness ensures also to be more difficult to.
For such a problem, it proposes in patent document 1 a kind of for being utilized by Ca-Al system oxide strip The micronized effect to original austenite grains come ensures the steel of high intensity using cooling is accelerated to ensure toughness The technology of material.
In addition, proposing in patent document 2 a kind of for being utilized by Mg-S system field trash bring to original Austria The micronized effect of family name's body crystal grain ensures the technology of the steel of high intensity using cooling is accelerated to ensure toughness.
But in the thick steel plate of manufacture, if application accelerates cooling after hot rolling, in the inside of steel plate, with surface phase Than, cooling velocity is slack-off, and the temperature history in surface and internal cooling generates big difference, according to the position of steel, intensity, These mechanical properties of ductility, toughness create a difference.
In addition, for large-scale building, it is desirable to use thick H profile steel, but the shape of the H profile steel is special.It will If steel billet is configured to H shape, universal rolling etc. need to be applied, but for universal rolling, rolling condition (temperature, reduction ratio) It is restricted.Therefore, in the case where manufacturing H profile steel, especially in manufacture flange (edge of a wing: flange) with a thickness of 20mm or more Thick H profile steel in the case where, compared with the steel plate (thick steel plate) of general thickness, control mechanical property and be not easy.
For such a problem, a kind of will reduce is proposed in patent document 3 and patent document 4 C amount and is added to B's Natural cooling after hot rolling of steel billet, come ensure homogeneous mechanical property method.
In addition, disclosed in patent document 5~8 a kind of thick H profile steel by for the purpose ofs high intensity, high tenacity etc. or The manufacturing method of H profile steel.
Citation
Patent document
Patent document 1: No. 5655984 bulletin of Japan's patent
Patent document 2: No. 5867651 bulletin of Japan's patent
Patent document 3: Japanese Laid-Open 2003-328070 bulletin
Patent document 4: Japanese Laid-Open 2011-106006 bulletin
Patent document 5: the flat 11-158543 bulletin of Japanese Laid-Open
Patent document 6: the flat 11-335735 bulletin of Japanese Laid-Open
Patent document 7: Japanese Laid-Open 2016-84524 bulletin
Patent document 8: the flat 10-68016 bulletin of Japanese Laid-Open
Summary of the invention
In the past, the thick H profile steel with a thickness of 20mm or more of flange, it is not easy to mechanical property is controlled, therefore, in this way Thick H profile steel, only require satisfaction in the room temperature or at most toughness at 0 DEG C.But in recent years, it is contemplated that on cold ground The use in area etc., for thick H profile steel, it is desirable that excellent tenacity at lower temperatures.Moreover, it is contemplated that as the every of structural material The intensity of Unit Weight also requires yield stress (specifically, yield strength or σ thick H profile steel0.2(offset yield is strong Degree: the stress value of 0.2% residual deformation is generated) it is 385MPa or more.
The present invention is in view of such actual situation to complete, and the purpose is to provide intensity and excellent in low temperature toughness Thick H profile steel and its manufacturing method.
The gist of the invention is as follows.
(1) H profile steel that a technical solution of the invention is related to contains C in terms of quality % as the chemical component of steel: 0.05~0.160%, Si:0.01~0.60%, Mn:0.80~1.70%, Nb:0.005~0.050%, V:0.05~ 0.120%, Ti:0.001~0.025%, N:0.0001~0.0120%, Cr:0~0.30%, Mo:0~0.20%, Ni:0~ 0.50%, Cu:0~0.35%, W:0~0.50%, Ca:0~0.0050%, Zr:0~0.0050%, also, it is limited to Al: 0.10% or less, B:0.0003% is hereinafter, surplus includes Fe and impurity, in Ceq=C+Mn/6+ (Cr+Mo+V)/5+ (Ni+ When Cu)/15, C, Mn, Cr, Mo, V, Ni, Cu in above-mentioned chemical component meet 0.30≤Ceq≤0.48, the gold as above-mentioned steel Belong to tissue, in terms of Line Integral rate, ferrite comprising 60% more than and less than 100%, by the mixing group of martensite and austenite It knits MA and is limited to 3.0% hereinafter, the tissue other than above-mentioned ferrite and above-mentioned MA is limited to 37% hereinafter, above-mentioned iron is plain The average grain diameter of body is 1~30 μm, and when observing above-mentioned steel with the section orthogonal with rolling direction, shape is H-shaped, flange With a thickness of 20~140mm, when the width direction length of above-mentioned flange is denoted as F, at the width direction end away from above-mentioned flange The position of face (1/6) F, stretching yield stress are 385~530MPa, and stretchings maximum intensity is 490~690MPa, will be above-mentioned convex The thickness of edge is denoted as t2When, on the outside of width direction end face (1/6) F away from above-mentioned flange and the thickness direction away from above-mentioned flange Face (1/4) t2Position, the absorption of the Charpy-type test at -20 DEG C can be 100J or more.
(2) in the H profile steel described in above-mentioned (1), as the above-mentioned chemical component of above-mentioned steel, in terms of quality %, Ke Yihan There is Nb: greater than 0.02% and is 0.050% or less.
(3) in the H profile steel described in above-mentioned (1) or (2), the above-mentioned chemical component as above-mentioned steel can in terms of quality % Containing N: greater than 0.005% and for 0.0120% or less.
(4) in described in any item H profile steels of above-mentioned (1)~(3), as the above-mentioned chemical component of above-mentioned steel, with matter % meter is measured, Cu: less than 0.03% can be limited to.
(5) in described in any item H profile steels of above-mentioned (1)~(4), as the above-mentioned chemical component of above-mentioned steel, with matter % meter is measured, Al: less than 0.003% can be limited to.
(6) in described in any item H profile steels of above-mentioned (1)~(5), the above-mentioned thickness of above-mentioned flange can for 25~ 140mm。
(7) manufacturing method for the H profile steel that a technical solution of the invention is related to is any one for manufacturing above-mentioned (1)~(6) The method of the H profile steel, has:
Obtain the steel making working procedure of the molten steel for the chemical component recorded in any one with above-mentioned (1)~(5)；
Above-mentioned molten steel after above-mentioned steel making working procedure is cast, the casting process of steel billet is obtained；
By the heating process of the above-mentioned heating steel billet to 1100~1350 DEG C after above-mentioned casting process；
For the above-mentioned steel billet after above-mentioned heating process, so that shape when with the section observation orthogonal with rolling direction Shape becomes the hot-rolled process that the mode of H-shaped is rolled under the following conditions, and the condition is: being greater than 900 DEG C and is being 1100 DEG C temperature region below, the accumulation reduction ratio in the position of width direction end face (1/6) F away from flange are 20% or more, 730~900 DEG C of temperature region, above-mentioned position accumulation reduction ratio be 15% or more, 730 DEG C or more at a temperature of terminate Rolling；With
By the cooling process of the hot-finished material natural cooling after above-mentioned hot-rolled process.
Above-mentioned technical proposal according to the present invention, be capable of providing intensity and excellent in low temperature toughness thick H profile steel and its Manufacturing method.
Detailed description of the invention
Fig. 1 is the schematic cross-section of the position of the sample producing for the H profile steel for illustrating that one embodiment of the present invention is related to.
Fig. 2 is the flow chart of the manufacturing method for the H profile steel for indicating that one embodiment of the present invention is related to.
Specific embodiment
The preferred embodiments of the present invention is described in detail below.But the present invention is not only limited in this implementation Composition disclosed in mode can make various changes in the range for not departing from purport of the invention.In addition, in following numerical value It limits in range, lower limit value and upper limit value include in this range.It is expressed as the numerical value of " being greater than " or " being less than ", the value is not Included in numberical range." % " of content about each element refers to " quality % ".
As described above, so far, for flange with a thickness of the thick H profile steel of 20mm or more, it is desirable that in room temperature or Toughness at 0 DEG C at most.But now, it is contemplated that in the use of cold district etc., for thick H profile steel, it is desirable that- Excellent tenacity under 20 DEG C or so of more low temperature.Moreover, it is contemplated that the intensity of the per unit weight as structural material, for thickness H profile steel, also require yield stress (specifically, yield strength or σ0.2) it is 385MPa or more.
Therefore, the present inventor is about thick H profile steel (being denoted as steel sometimes below), especially with regard to as in H profile steel The flange at critically important position in structure, for steel composition (chemical component of steel) and structure of steel (metal structure of steel) to intensity It is studied with the influence that low-temperature flexibility is given, obtains following opinion.Furthermore in the present embodiment, intensity means to stretch Yield stress and stretching maximum intensity, low-temperature flexibility mean the absorption energy of the Charpy-type test at -20 DEG C.
Firstly, the rising of hardenability excessive as caused by the addition of alloying element, can encourage the martensite-in steel The generation of austenite mixed tissue (being recorded as MA below), causes the reduction of low-temperature flexibility.B especially among alloying element, It is significant to encourage the tendency that MA is generated, therefore, it is effective for initiatively not adding B and being limited in impurity level or less.
In addition, in order to realize high yield stress (yield strength or σ0.2), while the toughness at -20 DEG C is improved, It is effective for adding Nb.Since Nb rises the intensity of steel by precipitation strength, will not make hardenability exceedingly on It rises, the generation of MA can not be encouraged and increase the intensity of steel.In addition, Nb, which has, inhibits tying again for the austenite in hot rolling Crystalline substance accumulates the strain in the steel caused by rolling, the effect of the ferritic grain refined after bringing phase transformation.
In addition, addition V is effective in order to improve the toughness at -20 DEG C.V have as carbonitride (VC, VN or its compound) it is precipitated to play a role as ferritic karyogenesis site, bring the effect of ferritic grain refined Fruit.
In addition, intensity and low-temperature flexibility further increase by addition Mn.In turn, on the basis of controlling composition of steel, As structure of steel, controlling ferritic Line Integral rate, the Line Integral rate of MA, ferritic average crystal particle diameter etc. makes high intensity Have both aspect with low-temperature flexibility to be important.
In order to steadily control structure of steel, when carrying out hot rolling to the steel billet for controlling composition of steel, in tying again for austenite Brilliant temperature region and non-recrystallization temperature region are given adequately rolling strain respectively and are necessary.Specifically, being greater than 900 DEG C and be 1100 DEG C of temperature regions below, carry out accumulation reduction ratio be 20% or more hot rolling, it is in turn, below at 900 DEG C Temperature region carries out the hot rolling that accumulation reduction ratio is 15% or more.By greater than 900 DEG C at a temperature of rolling, by Ovshinsky Body crystal grain grain refined, reduces hardenability, the production quantity etc. of MA is suppressed to it is lower, by 900 DEG C of temperature below Rolling increases ferritic karyogenesis frequency, by ferrite grain refined to more strain is given in steel.
In addition, in order to steadily control structure of steel, when cooling after hot rolling, the preferably surface of steel and internal cooling The difference of speed is small.Quickly cooling is not added but and in the case where natural cooling in steel after hot rolling, the surface of steel and internal cooling Speed all becomes smaller, and difference also becomes smaller.For example, for thickness of flange is the H profile steel of 20mm, if after hot rolling by steel nature Cooling, then the surface of steel and the average cooling rate of inside from 800 DEG C to 500 DEG C all become 1 DEG C/sec or less.
In the case that cooling velocity after hot rolling is slow, generally, it is not easy to while ensuring yield stress and low-temperature flexibility. But by most preferably controlling composition of steel and manufacturing condition, it becomes able to have both yield stress and low-temperature flexibility.For example, conduct C content is set as 0.05%~0.160%, does not add B and be limited in impurity level hereinafter, initiatively adding by composition of steel Nb and V suitably controls the content of the alloying elements such as Mn, Ti, N, the range by carbon equivalent Ceq control 0.30~0.48.Into And manufacturing condition is most preferably controlled, as structure of steel, study and determine ferritic Line Integral rate, the Line Integral rate of MA, iron element The average crystal particle diameter etc. of body.As a result, becoming able to obtain the thick H profile steel of intensity and excellent in low temperature toughness.
H profile steel of the present embodiment is illustrated below.Firstly, being carried out to steel composition and its restriction reason detailed Explanation.
H profile steel of the present embodiment includes basic element as chemical component, as needed comprising selecting element, Surplus (rest part) includes Fe and impurity.
C, Si, Mn, Nb, V, Ti, N among the chemical component of H profile steel of the present embodiment are that basic element is (main Alloy element).
(C:0.05~0.160%)
C (carbon) is the effective element of reinforcing to steel.Therefore, the lower limit of C content is set as 0.05%.It is preferred that by C content Lower limit be set as 0.060%, 0.070% or 0.080%.On the other hand, when C content is greater than 0.160%, low temperature can be incurred The reduction of toughness.Therefore, the upper limit of C content is set as 0.160%.In order to further increase low-temperature flexibility, preferably by C content The upper limit be set as 0.140%, 0.130% or 0.120%.
(Si:0.01~0.60%)
Si (silicon) is deoxidant element, is the element for also contributing to the raising of intensity.Therefore, the lower limit of Si content is set as 0.01%.It is preferred that the lower limit of Si content is set as 0.05%, 0.10% or 0.15%.On the other hand, if Si content is greater than 0.60%, then the generation of MA is encouraged, the reduction of low-temperature flexibility is incurred.Therefore, the upper limit of Si content is set as 0.60%.In order to make Low-temperature flexibility further increases, and the upper limit of Si content is preferably set as 0.40% or 0.30%.
(Mn:0.80~1.70%)
Mn (manganese) contributes to the element of the raising of intensity.Therefore, the lower limit of Mn content is set as 0.80%.In order to more Intensity is improved, the lower limit of Mn content is preferably set as 1.0%, 1.1% or 1.2%.On the other hand, if Mn content is greater than 1.70%, then hardenability exceedingly rises, and encourages the generation of MA, damages low-temperature flexibility.Therefore, the upper limit of Mn content is set as 1.70%.It is preferred that the upper limit of Mn content is set as 1.60% or 1.50%.
(Nb:0.005~0.050%)
Nb (niobium) is the recrystallization for inhibiting austenite in hot rolling, by making accumulation processing in steel strain to facilitate Ferritic grain refined, and facilitate by precipitation strength the element of the raising of intensity.Therefore, the lower limit of Nb content is set as 0.005%.It is preferred that the lower limit of Nb content is set as 0.010%, is greater than 0.020%, 0.025% or 0.030%.But if Nb Content is greater than 0.050%, then incurs the reduction of significant low-temperature flexibility sometimes.Therefore, the upper limit of Nb content is set as 0.050%.It is preferred that the upper limit of Nb content is set as 0.045%, 0.043% or 0.040%.Furthermore it is not adding intentionally In the case where Nb, the Nb content contained as impurity is less than 0.005%.In order to make 0.005% or more Nb content, make steel In intentionally contain Nb.
(V:0.05~0.120%)
V (vanadium) is made as Carbonitride Precipitation as playing to ferritic phase change core with the intragranular in austenite With by the element of the effect of ferrite crystal grain miniaturization.Therefore, the lower limit of V content is set as 0.05%.It is preferred that by V content Lower limit is set as being greater than 0.05%, 0.06% or 0.07%.But if V content is greater than 0.120%, sometimes due to precipitate Coarsening and damage low-temperature flexibility.Therefore, the upper limit of V content is set as 0.120%.It is preferred that the upper limit of V content is set as 0.110% or 0.100%.
(Ti:0.001~0.025%)
Ti (titanium) is to form TiN, by the element that the N in steel is fixed.Therefore, the lower limit of Ti content is set as 0.001%.For Using the pinning effect of TiN by the further grain refined of austenite, the lower limit of Ti content is preferably set as 0.005%, 0.007% or 0.010%.On the other hand, it as Ti content is greater than 0.025%, then generates coarse TiN, damages low-temperature flexibility. Therefore, the upper limit of Ti content is set as 0.025%.It is preferred that by the upper limit of Ti content be set as 0.020%, 0.015% or 0.012%.
In addition, Ti plays a role as deoxidant element in the case where actively not adding Al, therefore generate not in conjunction with Ti N.But the N is core as V Carbonitride Precipitation using Ti oxide.That is, by Ti as deoxidant element play a role from And Ti oxide is precipitated, and can promote the precipitation of V carbonitride, can improve low-temperature flexibility.
(N:0.0001~0.0120%)
N (nitrogen) is to form TiN, VN, facilitates the grain refined of tissue and the element of precipitation strength.It therefore, will be under N content Limit is set as 0.0001%.It is preferred that the lower limit of N content is set as 0.0020%, 0.0035%, be greater than 0.0050% or 0.0060%.But if N content is greater than 0.0120%, low-temperature flexibility is reduced, and face crack when becoming casting and is produced The reason of bad material caused by strain-aging of steel.Therefore, the upper limit of N content is set as 0.0120%.It is preferred that N is contained The upper limit of amount is set as 0.0110%, 0.0100% or 0.0090%.
H profile steel of the present embodiment contains impurity as chemical component.Furthermore " impurity " refers in industrially preparing When making steel, it is mixed into from ore, the waste material as raw material or from the mixed ingredient such as manufacturing environment.Such as, it is intended that Al, B, P, S, O Etc. element.In order to give full play to the effect of present embodiment, Al and B among these impurity are preferably limited as described below System.In addition, not needing limitation lower limit value since the content of preferred impurity is few, the lower limit value of impurity can be 0%.
(Al:0.10% or less)
Al (aluminium) is the element used as deoxidant element, if but Al content be greater than 0.10%, oxide coarsening, at For the basic point of brittle break, low-temperature flexibility is reduced.It therefore, is 0.10% by the ceiling restriction of Al content.In addition, not making actively It is deoxidant element using in the case where Al, Ti plays a role as deoxidant element, and Ti oxide is precipitated in steel.The Ti oxide Karyogenesis site as V carbonitride plays a role, and ferrite crystal grain diameter is miniaturize, and facilitates the raising of low-temperature flexibility. Accordingly it is also possible to without using Al as deoxidant element and using Al be used as impurity thus by the ceiling restriction of Al content for less than 0.003%, 0.002% or 0.001%.It furthermore is typically to make 0.003% or more Al content and make intentionally to contain in steel There is Al.
(B:0.0003% or less)
B (boron) improves hardenability, encourages the generation of MA, reduces low-temperature flexibility.Therefore, in the present embodiment, do not lead It is dynamic to add B and be limited in impurity level or less.It is 0.0003% by the ceiling restriction of B content.It is preferred that by the upper limit of B content It is limited to less than 0.0003%, 0.0002% or 0.0001%.It furthermore is typically that B content is made to be greater than 0.0003% and make steel In intentionally contain B.
(P:0.03% or less, S:0.02% or less, O:0.005% or less)
P (phosphorus), S (sulphur) and O (oxygen) are impurity.Solidifying segregation occurs for P and S, weld crack is encouraged, in addition, keeping low temperature tough Property reduce.It is preferred that being 0.03%, 0.02% or 0.01% by the ceiling restriction of P content.Additionally, it is preferred that the upper limit of S content is limited It is made as 0.02% or 0.01%.O is dissolved in steel and reduces low-temperature flexibility, in addition, can be due to the coarsening of oxide particle Reduce low-temperature flexibility.It is preferred that being 0.005%, 0.004% or 0.003% by the ceiling restriction of O content.
H profile steel of the present embodiment can contain selection member other than above explained basic element and impurity Element.For example, it is also possible to containing Cr, Mo, Ni, Cu, W, Ca, Zr, Mg, and/or REM, alternatively member usually replaces above-mentioned surplus A part of the Fe of (rest part).As long as these selection elements contain according to its purpose.It therefore, there is no need to limit this The lower limit value of a little selection elements, lower limit value can be 0%.In addition, also not damaged even if these select element to contain as impurity Evil said effect.
(Cr:0~0.30%)
Cr (chromium) contributes to the element of the raising of intensity.Can according to need makes Cr content 0~0.30%.In order into One step improves intensity, and the lower limit of Cr content is preferably set as 0.01%, 0.05% or 0.10%.On the other hand, if Cr content is big In 0.30%, then the generation of MA is encouraged, reduces low-temperature flexibility sometimes.It is therefore preferable that the upper limit of Cr content is set as 0.30%, 0.25% or 0.20%.
(Mo:0~0.20%)
Mo (molybdenum) is the element for being dissolved to facilitate the raising of intensity in steel.Can according to need makes Mo content 0 ~0.20%.In order to further increase intensity, the lower limit of Mo content is preferably set as 0.01%, 0.05% or 0.10%.But It is, if Mo content is greater than 0.20%, to encourage the generation of MA, incur the reduction of low-temperature flexibility sometimes.It is therefore preferable that by Mo content The upper limit be set as 0.20%, 0.17% or 0.15%.
(Ni:0~0.50%)
Ni (nickel) is the element for being dissolved to facilitate the raising of intensity in steel.Can according to need makes Ni content 0 ~0.50%.In order to further increase intensity, the lower limit of Ni content is preferably set as 0.01%, 0.05% or 0.10%.But It is, if Ni content is greater than 0.50%, to improve hardenability, encourage the generation of MA, reduce low-temperature flexibility sometimes.It is therefore preferable that The upper limit of Ni content is set as 0.50%, 0.30% or 0.20%.
(Cu:0~0.35%)
Cu (copper) contributes to the element of the raising of intensity.Can according to need makes Cu content 0~0.35%.But The addition of Cu can encourage the generation of MA, and low-temperature flexibility reduces sometimes.It may be preferable to by Cu content be limited to 0.30% with Under, 0.20% or less, 0.10% or less or as impurity level less than 0.03% or less than 0.01%.
(W:0~0.50%)
W (tungsten) is the element for being dissolved to facilitate the raising of intensity in steel.Can according to need make W content 0~ 0.50%.It is preferred that the lower limit of W content is set as 0.001%, 0.01% or 0.10%.But if W content is greater than 0.50%, The generation for encouraging MA, reduces low-temperature flexibility sometimes.It is therefore preferable that by the upper limit of W content be set as 0.50%, 0.40% or 0.30%.Furthermore in the case where intentionally not adding W, the W content contained as impurity is less than 0.001%.To make W Content makes intentionally to contain W in steel for 0.001% or more.
(Ca:0~0.0050%)
Ca (calcium) is that the form control to sulfide is effective, inhibits the generation of coarse MnS, facilitates mentioning for low-temperature flexibility High element.Can according to need makes Ca content 0~0.0050%.It is preferred that the lower limit of Ca content is set as 0.0001%, 0.0005% or 0.0010%.On the other hand, if Ca content is greater than 0.0050%, low-temperature flexibility is reduced sometimes.Therefore, excellent The upper limit of Ca content is set as 0.0050%, 0.0040% or 0.0030% by choosing.
(Zr:0~0.0050%)
Zr (zirconium) is precipitated as carbide, nitride or its compound, and the element of precipitation strength is facilitated.It can root According to needing to make Zr content 0~0.0050%.It is preferred that by the lower limit of Zr content be set as 0.0001%, 0.0005% or 0.0010%.On the other hand, if Zr content is greater than 0.0050%, incur the coarsening of carbide and nitride of Zr etc., have When low-temperature flexibility reduce.It is therefore preferable that the upper limit of Zr content is set as 0.0050%, 0.0040% or 0.0030%.Furthermore In the case where intentionally not adding Zr, the Zr content contained as impurity is less than 0.0001%.To make Zr content 0.0001% or more and make intentionally to contain Zr in steel.
(Mg:0~0.0050%, REM:0~0.0050%)
What the toughness that Mg (magnesium) and REM (rare earth element) contributes to base metal tenacity and welding heat affected zone (HAZ) improved Element.Can according to need makes Mg content 0~0.0050%, REM content be 0~0.0050%.It is preferred that by under Mg content Limit be set as 0.0005%, 0.0010% or 0.0020%, the lower limit of REM content is set as to 0.0005%, 0.0010% or 0.0020%.On the other hand, the upper limit of Mg content is preferably set as 0.0040%, 0.0030% or 0.0025%, contains REM The upper limit of amount is set as 0.0040%, 0.0030% or 0.0025%.
(Ceq:0.30~0.48)
H profile steel of the present embodiment controls carbon equivalent Ceq from the viewpoint of ensuring intensity.Specifically, When Ceq is expressed as following formulas 1, C, Mn, Cr, Mo, V, Ni, Cu in the chemical component of H profile steel are met in terms of quality % 0.30≤Ceq≤0.48.If Ceq, less than 0.30, intensity is insufficient.Therefore, the lower limit of Ceq is set as 0.30.It is preferred that by Ceq's Lower limit is set as 0.32%, 0.34% or 0.35%.On the other hand, if Ceq is greater than 0.48, low-temperature flexibility is reduced.Therefore, will The upper limit of Ceq is set as 0.48.It is preferred that the upper limit of Ceq is set as 0.45%, 0.43% or 0.40%.Furthermore using following Formula 1 is come when calculating Ceq, about the content in steel in detection limit element below, as long as being updated to formula 1 as its value for 0 Calculate Ceq.
Ceq=C+Mn/6+ (Cr+Mo+V)/5+ (Ni+Cu)/15 (formula 1)
Above-mentioned composition of steel, as long as the common analysis method using steel measures.For example, composition of steel uses ICP- AES (Inductively Coupled Plasma-Atomic Emission Spectrometry) measurement.Furthermore C It is measured with S using burning-infrared absorption, N is measured using inert gas fusion-thermal conductivity method, and O uses inertia Gas fusion-non-dispersive type infrared absorption measurement.
Then, the structure of steel and its restriction reason of H profile steel of the present embodiment are described in detail.
In H profile steel of the present embodiment, structure of steel is in terms of Line Integral rate, comprising 60% more than and less than 100% Ferrite, the line and staff control MA of martensite and austenite is limited to 3.0% hereinafter, by the group other than ferrite and MA It knits and is limited to 37% or less.In addition, ferritic average grain diameter is set as 1 μm or more and 30 μm or less
(ferritic Line Integral rate: 60% more than and less than 100%)
Ferrite is the main composition phase in the structure of steel of H profile steel of the present embodiment.If ferritic area Divide rate less than 60%, then low-temperature flexibility reduces.Therefore, the lower limit of ferrite point rate is set as 60%.It is preferred that dividing ferrite to rate Lower limit be set as 65%, 70% or 75%.On the other hand, due to can with the generation of pearlite or bainite and physically It is difficult to control ferritic Line Integral rate at 100%.Therefore, the upper limit of ferrite point rate is set as less than 100%.In order to manage It controls intensity and low-temperature flexibility with thinking, the upper limit of ferrite point rate is preferably set as 90%, 85% or 80%.(the Line Integral of MA Rate: 3.0% or less)
If encouraging the generation of MA, low-temperature flexibility is reduced.In H profile steel of the present embodiment, the life of MA is not encouraged At and increase the intensity of steel.For this purpose, MA points of rate is limited to 3.0% or less.It is preferred that the upper limit of MA points of rate is set as 2.5%, 2.0% or 1.5%.Furthermore since MA divides rate the smaller the better, the lower limit of MA points of rate may be 0%.
(the Line Integral rate of the tissue other than ferrite and MA: 37% or less)
In the structure of steel of H profile steel of the present embodiment, as the tissue other than above-mentioned ferrite and MA, Include bainite, pearlite etc..If the tissue other than ferrite and MA excessively contains, low-temperature flexibility is reduced.Therefore, it will remove The Line Integral rate of tissue (rest part other than above-mentioned ferrite and MA) other than ferrite and MA is limited to 37% or less.It is preferred that by a point rate for the tissue other than ferrite and MA be set as 35% or less, 30% or less or 25% with Under.Furthermore divide rate the smaller the better due to the tissue other than ferrite and MA, lower limit may be 0%.
(ferritic average grain diameter: 1~30 μm)
Ferritic average grain diameter is preferably fine.If ferrite partial size is greater than 30 μm, low-temperature flexibility is reduced.Therefore, The upper limit of ferrite partial size is set as 30 μm.It is preferred that the upper limit of ferrite partial size is set as 25 μm, 22 μm or 18 μm.Another party Face is industrially difficult to ferrite size controlling be less than 1 μm.Therefore, the lower limit of ferrite partial size is set as 1 μm.It is preferred that The lower limit of ferrite partial size is set as 3 μm, 5 μm or 10 μm.
As long as above-mentioned structure of steel is differentiated by optical microphotograph sem observation.For example, Fig. 1 be H profile steel with rolling The orthogonal schematic cross-section in direction, structure of steel are nearby to observe at evaluation position 7 shown in FIG. 1 as viewing surface.Specifically For, in Fig. 1, by the thickness direction outside as the width direction end face 5a apart from flange for (1/6) F and apart from flange Face 5b be (1/4) t2Position evaluation position 7 nearby be used as viewing surface, to observe structure of steel.Furthermore the viewing surface is set as The face parallel with the width direction end face 5a of flange.
Above-mentioned viewing surface is ground and corroded, to observe structure of steel.Grinding proceeds to viewing surface as mirror surface and is Only, about corrosion, the corrosive liquid for the identification for being suitable for constituting phase is used.For example, if with nital to being processed into The viewing surface of mirror surface is corroded to show structure of steel, then since pearlite, bainite are coloured, can identify iron Ferritic, martensite and austenite.In addition, if being corroded to the viewing surface for being processed into mirror surface with Lepera corrosive liquid to make Structure of steel is shown, then due to other than martensite and austenite composition mutually by coloring black, can identify martensite with The line and staff control MA of austenite.
H profile steel of the present embodiment finds out ferrite and MA from the viewing surface corroded through nital Divide rate, and divide rate for surplus as the tissue of pearlite and bainite, asked from the viewing surface through Lepera corrosion corrosion MA divides rate out.Specifically, 200 times of the optical microscopy arrived in the viewing surface photographs corroded through nital On photo (as needed can be multiple visual fields), measuring point is configured with the unilateral clathrate for being 25 μm, is measured at least 1000 Point discriminates whether the quantity that will be deemed as ferrite or the measuring point of MA for ferrite or MA divided by obtained by total measuring point quantity To value divide rate as ferrite or MA.
Similarly, 200 times of the optical microscope photograph arrived in the viewing surface photographs through Lepera corrosion corrosion On (as needed can be multiple visual fields), measuring point be configured with the unilateral clathrate for being 25 μm, is sentenced at least 1000 measuring points Not whether to be not MA, will be deemed as the quantity of the measuring point of MA divided by total obtained value of measuring point quantity as MA points of rate.And And ferritic point of rate, by subtracting the total point of rate in the pearlite, bainite and MA points of rate that find out among the above from 100% To find out.
In addition, H profile steel of the present embodiment, using in the above-mentioned viewing surface corroded through nital 200 times of the optical microscope photograph that photographs arrive finds out ferrite by the patterning method according to JIS G0551 (2013) standard Average grain diameter.
Then, the mechanical property of H profile steel of the present embodiment is described in detail.
H profile steel of the present embodiment, from comprising as obtaining average mechanical property (intensity and low-temperature flexibility) Sample is produced in the region at the evaluation position 7 shown in FIG. 1 of position, to evaluate mechanical property.
Firstly, being illustrated to the evaluation position 7 in Fig. 1.Fig. 1 is the section signal orthogonal with rolling direction of H profile steel Figure.In Fig. 1, X-direction is defined as to the width direction of flange, Y-axis is defined as to the thickness direction of flange, by Z-direction It is defined as rolling direction.
As shown in Figure 1, the center at evaluation position 7, is being denoted as F for the width direction length of flange, is remembering the thickness of flange For t2When, it is face (1/4) t on the outside of width direction end face (1/6) F away from flange and the thickness direction away from flange2Position.Again Person, the face on the outside of the thickness direction of flange refers to a face of the thickness direction of flange, and is the face not contacted with web 6, is Face 5b shown in FIG. 1.In addition, the width direction end face of flange is end face 5a shown in FIG. 1.
Sample when low-temperature flexibility is evaluated by Charpy-type test, from the position at position 7 is evaluated with the length of sample The direction mode parallel with rolling direction is produced.In addition, forming the face of notch on sample as the width direction end face with flange 5a parallel any surface.In addition, said sample, as long as the width direction end face 5a apart from flange be (1/6) F's and distance Face 5b on the outside of the thickness direction of flange is (1/4) t2Position, then produce and be ok from which position.
Yield stress (yield strength or σ are evaluated by tension test0.2) and when tensile strength (stretch maximum intensity) Sample becomes the thickness direction center of sample with the position that the width direction end face 5a in Fig. 1 apart from flange is (1/6) F Mode is produced.As long as the length direction of sample sample is parallel with rolling direction and cuts the thickness direction whole of flange. Furthermore said sample, as long as the position that the width direction end face 5a apart from flange is (1/6) F, then produce all from which position It can be with.
H profile steel of the present embodiment, as mechanical property, yield stress at normal temperature reaches 385MPa or more, Tensile strength reaches 490MPa or more, and the Charpy impact absorption at -20 DEG C can reach 100J or more.If intensity is excessively high, Sometimes damage low-temperature flexibility, thus the upper limit of yield stress is preferably set as 530MPa, the upper limit of tensile strength is set as 690MPa. Can be greater than 500J in addition, being industrially difficult to make Charpy impact at -20 DEG C to absorb, therefore it can will be at -20 DEG C The upper limit that Charpy impact absorbs energy is set as 500J.Furthermore room temperature refers to 20 DEG C.
When evaluating the mechanical property of H profile steel of the present embodiment, tension test is marked according to JISZ2241 (2011) Standard carries out, and Charpy-type test is carried out according to JIS Z2242 (2005) standard.Furthermore it is answered what is obtained by tension test When seeing yield phenomenon on force-strain curve, find out yield strength as yield stress, load-deformation curve not When to yield phenomenon, σ is found out0.2As yield stress.
Then, the shape of H profile steel of the present embodiment is described in detail.
H profile steel of the present embodiment, by the thickness t of flange2It is set as 20~140mm.For example, in high building structure In object, as strength member, the H profile steel of demand thickness.Therefore, the lower limit of thickness of flange is set as 20mm.It is preferred that by thickness of flange Lower limit be set as 25mm, 40mm or 56mm.On the other hand, if the thickness t of flange2Greater than 140mm, then processing when hot-working Amount is insufficient, it is difficult to having both strength and low-temperature flexibility.Therefore, the upper limit of thickness of flange is set as 140mm.It is preferred that by thickness of flange The upper limit is set as 125mm, 89mm or 77mm.For example, the thickness t of flange2Preferably 25~140mm.Furthermore the web of H profile steel Thickness t1It is not specially provided, but preferably 20~140mm, more preferably 25~140mm.
In addition, using hot rolling to manufacture H profile steel, thickness of flange/web thickness ratio (t2/t1) preferably 0.5~2.0.As thickness of flange/web thickness ratio (t2/t1) more than 2.0 when, web is deformed into wavy shape sometimes. On the other hand, in thickness of flange/web thickness ratio (t2/t1) less than 0.5 in the case where, flange is deformed into wavy sometimes Shape.
In the prior art, the H profile steel of the thickness with a thickness of 20mm or more of flange is difficult to having both strength and toughness.But H profile steel of the present embodiment, the thick H profile steel for being 20mm or more despite thickness of flange, but due to most preferably controlling Composition of steel and structure of steel, therefore being capable of having both strength and low-temperature flexibility.
Then, the preferred manufacturing method of H profile steel of the present embodiment is described in detail.
The manufacturing method of H profile steel of the present embodiment, comprising: steel making working procedure, casting process, heating process, hot rolling Process and cooling process.
In steel making working procedure, adjusts the chemical component of molten steel and formed to make it above-mentioned steel.It, can in steel making working procedure To use the molten steel for carrying out converter refining and/or double refining and manufacturing, also can be used the molten steel that has been melted using electric furnace come As raw material.In steel making working procedure, it can according to need and carry out deoxidation treatment, Fruit storage.
In casting process, the molten steel after steel making working procedure is cast, to obtain steel billet.Casting is using continuous metal cast process, casting Ingot method etc. carries out.From the viewpoint of productivity, preferred continuous casting.The shape of steel billet is preferably close in the H profile steel to be manufactured Shape Hot Metal in Beam Blank (beam blank), but be not particularly limited.In addition, the thickness of steel billet, from the viewpoint of productivity, Preferably 200mm or more, if consider the reduction of segregation, carry out the homogenieity of heating temperature before hot rolling etc., preferably 350mm Below.
In heating process, by the heating steel billet after casting process to 1100~1350 DEG C.If the heating temperature of steel billet is small In 1100 DEG C, then deformation drag when finish rolling is got higher.Therefore, the lower limit of heating temperature is set as 1100 DEG C.In order to make Nb's etc. The element for forming carbide and nitride etc. is sufficiently dissolved, and the lower limit of heating temperature is preferably set as 1150 DEG C.On the other hand, if Heating temperature is greater than 1350 DEG C, then the oxide skin liquefaction of billet surface, will appear failure during manufacturing.Therefore, by heating temperature The upper limit be set as 1350 DEG C.Furthermore the uncolled steel billet to room temperature after casting process in heating process, can be used.
In hot-rolled process, for the steel billet after heating process, roughing, intermediate rolling, finish rolling are carried out.In roughing, into Shape when row is shaped so that with the section observation orthogonal with rolling direction becomes generally H shape.For the generally H shape Steel billet, steel surface temperature be greater than 900 DEG C and be 1100 DEG C of temperature regions below, carry out accumulation reduction ratio be 20% with On hot rolling be in turn 730 DEG C~900 DEG C of temperature region in the surface temperature of steel, carrying out accumulation reduction ratio is 15% or more Hot rolling.In the hot rolling, it is formed so that shape when with above-mentioned section observation finally becomes H shape.
It is being greater than 900 DEG C and is being 1100 DEG C of temperature regions below, in order to be reduced by the grain refined of austenite grain Accumulation reduction ratio is set as 20% or more by the production quantity of bainite, MA.It is preferred that 900 DEG C will be greater than and be 1100 DEG C below The lower limit of the accumulation reduction ratio of temperature region is set as 25%, 30% or 35%.Can according to need will be greater than 900 DEG C and be The upper limit of the accumulation reduction ratio of 1100 DEG C of temperature regions below is set as 60%.
In 730 DEG C~900 DEG C of temperature region, for ferritic grain refined, accumulation reduction ratio is set as 15% or more. It is preferred that the lower limit of the accumulation reduction ratio in 730 DEG C~900 DEG C of temperature region is set as 20%, 25% or 30%.It can basis The upper limit by the accumulation reduction ratio in 730 DEG C~900 DEG C of temperature region is needed to be set as 50%.
Furthermore if lower than 730 DEG C at a temperature of rolled, incur the reduction of low-temperature flexibility sometimes.Therefore, it rolls Finishing temperature (finishing temperature) is set as 730 DEG C or more by the land surface pyrometer of steel.It is preferred that the upper limit of finishing temperature is set as 750 ℃。
In hot-rolled process, carry out roughing, intermediate rolling, finish rolling, still, for example, be greater than 900 DEG C and for 1100 DEG C with Under temperature region rolling, with roughing, intermediate rolling, finish rolling which be ok.Similarly, 730 DEG C~900 DEG C temperature region rolling, with roughing, intermediate rolling, finish rolling which be ok.In H of the present embodiment In the manufacturing method of fashioned iron, as long as the accumulation reduction ratio in above-mentioned temperature region obtains control.
In addition, in the accumulation reduction ratio of above-mentioned temperature region, to be started from the width direction end face 5a of flange shown in FIG. 1 It is found out on the basis of the thickness of flange of position corresponding with (1/6) F.For example, being greater than 900 DEG C and being 1100 DEG C of temperature below The accumulation reduction ratio in region, which is set as, to be thickness of flange under 1100 DEG C of time point by the surface temperature in steel and will reach 900 The difference of thickness of flange before DEG C is come the reduction ratio that calculates.Similarly, it is depressed in the accumulation of 730 DEG C~900 DEG C of temperature region Thickness of flange under the time point that it is 900 DEG C by the surface temperature in steel that rate, which is set as, and convex in the case where it is 730 DEG C of time point The difference of edge thickness is come the reduction ratio that calculates.
The method of roughing, intermediate rolling, finish rolling in hot-rolled process is not particularly limited.For example, being opened as roughing Base (breakdown) rolling, rolls as centre, carries out universal rolling or wide (edging) rolling is adjusted to carry out ten thousand as finish rolling It can roll, thus so that the shape when section observation orthogonal with rolling direction shapes in a manner of becoming H-shaped.
In hot-rolled process, water cooling can also be carried out between rolling pass.Water cooling between rolling pass is than Austria The cooling carried out for the purpose of the temperature control of the high temperature region of the temperature of family name's body progress phase transformation.It will not be because between rolling pass Water cooling and in steel bainite, MA.
In addition, two hot rollings can be carried out in hot-rolled process.So-called two hot rolling is after primary rolling that steel billet is cooling To 500 DEG C hereinafter, then, heating steel billet to be carried out to the milling method of secondary rolling to 1100~1350 DEG C again.For two For hot rolling, the amount of plastic deformation in hot rolling is few, and the reduction of the temperature in rolling process also becomes smaller, therefore can make secondary Heating temperature is more slightly lower.
In cooling process, the hot-finished material after hot-rolled process is cooling.In the manufacture of H profile steel of the present embodiment In method, after hot rolling end of a period, as former state by hot-finished material natural cooling in an atmosphere.It is in an atmosphere that hot-finished material is naturally cold But in the case where, the surface of the steel from 800 DEG C to 500 DEG C and internal average cooling rate become 1 DEG C/sec or less.It is logical It crosses hot-finished material natural cooling in an atmosphere, the surface of steel and internal cooling velocity become uniformly, therefore by steel The deviation of mechanical property caused by position is inhibited.Furthermore in the manufacturing method of H profile steel of the present embodiment, from So cooling means cold in an atmosphere without compulsory cooling until steel temperature becomes 400 DEG C or less from hot rolling is complete But.
In the prior art, accelerate to cool down for intensity and having both for toughness and by hot-finished material, therefore in steel Surface and the internal deviation for generating mechanical property.On the other hand, in the manufacturing method of H profile steel of the present embodiment, Although, will not be due to most preferably controlling composition of steel and structure of steel by hot-finished material natural cooling in an atmosphere The surfaces of steel and the internal deviation for generating mechanical property can be realized having both for intensity and low-temperature flexibility.
The manufacturing method of H profile steel of the present embodiment does not need the steel-smelting technology of height and accelerates cooling, therefore energy Enough seek reduction, the shortening of duration of manufacture load.Therefore, H profile steel of the present embodiment, economy can not be damaged and Improve the reliability of large-scale fabrication.
Embodiment
Then, the effect of a technical solution of the invention, but the item in embodiment are described in more detail by embodiment Part is the condition example that uses in order to confirm exploitativeness and effect of the invention, and the present invention is not limited by the condition example System.The present invention without departing from the gist of the invention, reach the purpose of the present invention and can use various conditions.
Melting has the steel of chemical component shown in 1~table of table 3, has been manufactured by continuous casting with a thickness of 240~300mm's Steel billet.The melting of steel carries out in converter, carries out a deoxidation, and addition alloying element carrys out adjusting component, carries out as needed true Empty degassing process.Obtained steel billet is heated, hot rolling is carried out, has manufactured H profile steel.As the steel shown in ingredient No.1~48 Ingredient is found out and carrying out chemical analysis to the sample taken from each H profile steel after manufacture.Although being not shown in table, No matter being which embodiment is all: P is 0.03% or less, S is 0.02% or less, O is 0.005% or less.Furthermore the change in table The empty column studied point indicates that non-Xiang Gangzhong is initiatively added or content is below detection limit.
The manufacturing process of H profile steel is shown in Fig. 2.It is rolled comprising roughing mill 2a, intermediate roll mill 2b, the omnipotent of finishing mill 2c Hot rolling is carried out in the warmed-up steel billet of heating furnace 1 in device column processed.It is as former state that hot-finished material is naturally cold after hot rolling end of a period But become 400 DEG C or less to it.From the surface of hot-finished material of the temperature of hot-rolled end until 500 DEG C and internal average cooling Speed is all 1 DEG C/sec or less.In the case where carrying out water cooling between the passage of hot rolling, (rolled centre using in intermediate universal rolling machine Machine processed) 2b front and back setting water cooling plant 3 carry out flange outer sides face misting cooling.At this point, having carried out reversible (reverse) Rolling.
4~table of table 6 shows manufacturing condition and manufacture result.Reduction ratio when hot rolling shown in 4~table of table 6 is from Fig. 1 institute The width direction end face 5a of the flange shown starts the accumulation reduction ratio in each temperature region of position corresponding with (1/6) F.
About the H profile steel produced, as described above, using from the sample produced of evaluation position 7 shown in FIG. 1 ,- Charpy-type test is carried out at 20 DEG C, has rated low-temperature flexibility.In addition, the use of the width direction end face 5a apart from flange being (1/ 6) position of F becomes the sample at the center of thickness direction, carries out tension test under room temperature (20 DEG C), has rated tensile properties. Structure observation is nearby carried out for the sample of viewing surface with evaluation position 7 shown in FIG. 1 in addition, using, and has rated structure of steel.
Tension test is carried out according to JIS Z2241 (2005) standard.It shows and bends in the load-deformation curve of tension test In the case where taking behavior, yield stress is yield point, in the case where not showing yield behavior, yield stress σ0.2.Charpy punching Hit the progress of test basis JIS Z2242 (2005) standard.Charpy-type test carries out at -20 DEG C.
It about structure observation, adopts with the aforedescribed process, ferrite point rate, MA point is determined using optical microscope photograph Tissue other than rate and ferrite and MA divides rate.In addition, the tissue other than ferrite and MA is bainite or pearlite. In addition, being found out using the patterning method according to JIS G0551 (2013) standards ferritic flat using optical microscope photograph Equal partial size.
As tensile properties, by yield stress (YS) at normal temperature be 385MPa or more, tensile strength (TS) is The steel of 490MPa or more are judged as qualified.In addition, the Charpy impact at -20 DEG C is absorbed energy as low-temperature flexibility (vE-20) it is judged as qualified for the steel of 100J or more.
As shown in table 1~6, as manufacture No.1~8 of example of the present invention, manufacture No.11~18 and No.34~43 are manufactured, Composition of steel, structure of steel and mechanical property all meet the scope of the present invention.
On the other hand, as manufacture No.9~10 of comparative example, manufacture No.19~33 and manufacture No.44~50, steel at Divide, certain items in structure of steel and mechanical property are unsatisfactory for the scope of the present invention.
Manufacture No.9 be due to be greater than 900 DEG C and for 1100 DEG C of temperature regions below reduction ratio it is insufficient, Ferrite point rate in structure of steel becomes inadequate, and a point rate for the tissue other than ferrite and MA becomes excessive, at -20 DEG C Charpy impact absorb the example that can become inadequate.
Manufacturing No.10 is the ferrite partial size since the reduction ratio of the temperature region at 730 DEG C~900 DEG C is insufficient It becomes thick, the Charpy impact at -20 DEG C absorbs the example that can be become inadequate.
Manufacture No.19 be due to be greater than 900 DEG C and for 1100 DEG C of temperature regions below reduction ratio it is insufficient, Ferrite point rate becomes inadequate, and MA points of rate becomes excessive, and a point rate for the tissue other than ferrite and MA becomes excessive, -20 Charpy impact at DEG C absorbs the example that can be become inadequate.
Manufacture No.20 is since C content is more, manufacture No.25 is since Nb content is more, manufacture No.26 is due to V content More, manufacture No.28 is since Al content is more, manufacture No.29 is since Ti content is more, manufacture No.30 is since N content is more, system Making No.31 is that the Charpy impact due to Ceq excess, at -20 DEG C absorbs the example that can be become inadequate.
Manufacture No.21 is since C content is few, manufacture No.24 is since Mn content is few, manufacture No.32 is since Ceq does not fill Divide, manufacture No.46 is the example that YS and TS become inadequate since Si content is few.
Manufacture No.22 is since Si content is more, manufacture No.23 is since Mn content is more, MA points of rate is excessive, -20 Charpy impact at DEG C absorbs the example that can be become inadequate.
Manufacturing No.27 is since V content is few, and ferrite partial size becomes thick, and the Charpy impact at -20 DEG C is inhaled Receive the example that can be become inadequate.
It is since B content is more that manufacture No.33, which is since B content and Ceq are excessive, manufacture No.49, and MA points of rate became Amount, the Charpy impact at -20 DEG C absorb the example that can be become inadequate.
Manufacturing No.44 and manufacture No.45 is since V content is few, and ferrite partial size becomes thick, at -20 DEG C Charpy impact absorb the example that can become inadequate.
Manufacturing No.47 is since Nb content is few, and ferrite partial size becomes thick, and YS and TS become inadequate, Charpy impact at -20 DEG C absorbs the example that can be become inadequate.
Manufacturing No.48 is since Ti content is few, and ferrite partial size becomes thick, and the Charpy impact at -20 DEG C is inhaled Receive the example that can be become inadequate.
Manufacture No.50 is that the Charpy impact absorption since finishing temperature is low, at -20 DEG C can become inadequate Example.
Industrial availability
Above-mentioned technical proposal according to the present invention, be capable of providing intensity and excellent in low temperature toughness thick H profile steel and its Manufacturing method, thus industrially using height.
Description of symbols
1 heating furnace
2a roughing mill
Roll mill among 2b
2c finishing mill
Water cooling plant before and after 3 intermediate roll mills
4 H profile steels
5 flanges
The width direction end face of 5a flange
Face on the outside of the thickness direction of 5b flange
6 webs
The evaluation position of 7 tensile properties, low-temperature flexibility and steel tissue
The width direction length of F flange
H height
t1The thickness of web
t2The thickness of flange

Claims (7)

1. a kind of H profile steel, which is characterized in that contained in terms of quality % as the chemical component of steel
C:0.05~0.160%,
Si:0.01~0.60%,
Mn:0.80~1.70%,
Nb:0.005~0.050%,
V:0.05~0.120%,
Ti:0.001~0.025%,
N:0.0001~0.0120%,
Cr:0~0.30%,
Mo:0~0.20%,
Ni:0~0.50%,
Cu:0~0.35%,
W:0~0.50%,
Ca:0~0.0050%,
Zr:0~0.0050%,
Also, by Al be limited to 0.10% hereinafter, by B be limited to 0.0003% hereinafter,
Surplus includes Fe and impurity,
C, Mn, Cr, Mo, V, Ni, Cu in Ceq=C+Mn/6+ (Cr+Mo+V)/5+ (Ni+Cu)/15, in the chemical component Meet 0.30≤Ceq≤0.48,
As the metal structure of the steel, in terms of Line Integral rate, ferrite comprising 60% more than and less than 100%, by geneva The line and staff control MA of body and austenite is limited to 3.0% hereinafter, the tissue other than the ferrite and the MA is limited For 37% hereinafter,
The ferritic average grain diameter is 1~30 μm,
When observing the steel with the section orthogonal with rolling direction, shape is H-shaped, flange with a thickness of 20~140mm,
When the width direction length of the flange is denoted as F, in the position of width direction end face (1/6) F away from the flange, Stretching yield stress is 385~530MPa, and stretching maximum intensity is 490~690MPa,
The thickness of the flange is being denoted as t2When, in width direction end face (1/6) F away from the flange and away from the flange Face (1/4) t on the outside of thickness direction2Position, the absorption of the Charpy-type test at -20 DEG C can be 100J or more.
2. H profile steel according to claim 1, which is characterized in that as the chemical component of the steel, with quality % Meter containing Nb: greater than 0.02% and is 0.050% or less.
3. H profile steel according to claim 1, which is characterized in that as the chemical component of the steel, with quality % Meter containing N: greater than 0.005% and is 0.0120% or less.
4. H profile steel according to claim 1, which is characterized in that as the chemical component of the steel, with quality % Meter, is limited to less than 0.03% for Cu.
5. H profile steel according to claim 1, which is characterized in that as the chemical component of the steel, with quality % Meter, is limited to less than 0.003% for Al.
6. H profile steel according to claim 1, which is characterized in that the flange it is described with a thickness of 25~140mm.
7. a kind of manufacturing method of H profile steel is the method for described in any item H profile steels of manufacturing claims 1~6, feature It is have:
Obtain the steel making working procedure of the molten steel for the chemical component recorded in any one with Claims 1 to 5；
The molten steel after the steel making working procedure is cast, the casting process of steel billet is obtained；
By the heating process of the heating steel billet to 1100~1350 DEG C after the casting process；
For the steel billet after the heating process so that shape when with orthogonal with rolling direction section observation at For the hot-rolled process that the mode of H-shaped is rolled under the following conditions, the condition is: be greater than 900 DEG C and for 1100 DEG C with Under temperature region, the accumulation reduction ratio in the position of width direction end face (1/6) F away from flange is 20% or more, 730~ 900 DEG C of temperature region, the accumulation reduction ratio in the position are 15% or more, in 730 DEG C or more of at a temperature of end rolling； With
By the cooling process of the hot-finished material natural cooling after the hot-rolled process.
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