CN109642296B - Rolled h-section steel beam and its manufacturing method - Google Patents

Rolled h-section steel beam and its manufacturing method Download PDF

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CN109642296B
CN109642296B CN201780053617.1A CN201780053617A CN109642296B CN 109642296 B CN109642296 B CN 109642296B CN 201780053617 A CN201780053617 A CN 201780053617A CN 109642296 B CN109642296 B CN 109642296B
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wing
edge
less
rolled
section steel
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CN109642296A (en
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伊藤荣利
山下浩
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Japanese Style Stock Co
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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
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
    • 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
    • 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
    • C21D7/00—Modifying the physical properties of iron or steel by deformation
    • C21D7/13—Modifying the physical properties of iron or steel by deformation by hot working
    • 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
    • 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
    • C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
    • 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
    • C22C38/18—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
    • 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
    • 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
    • B21B27/00—Rolls, roll alloys or roll fabrication; Lubricating, cooling or heating rolls while in use
    • B21B27/02—Shape or construction of rolls
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/008—Heat treatment of ferrous alloys containing Si
    • 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

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  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Heat Treatment Of Steel (AREA)
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  • Rod-Shaped Construction Members (AREA)

Abstract

A kind of rolled h-section steel beam, it is characterized in that, preceding 5% average value of the Mn concentration in the most brittle portion on the edge of a wing is 1.6 times or less of the Mn concentration of following position, the position are as follows: the distance of the end face away from flange width direction on flange width direction is 1/6 position of flange width, it and is 1/4 position that being located at a distance from the surface of web opposite side away from the edge of a wing is edge of a wing thickness on the thickness direction of the edge of a wing, preceding 5% average value of the Mn concentration in the center segregation portion of the rolled h-section steel beam is 1.1 times or more and 1.6 times or less of the Mn concentration of following position, the position are as follows: the distance of the end face away from flange width direction on flange width direction is 1/6 position of flange width, and be on the thickness direction of the edge of a wing being located at a distance from the surface of web opposite side for the wing away from the edge of a wing 1/4 position of edge thickness, the center segregation part are dispersed in the region within an end face from the center of flange width towards flange width direction or two end face 15mm or more and thickness direction top flange surface layer 2mm.

Description

Rolled h-section steel beam and its manufacturing method
Technical field
(cross-reference to related applications)
The application, will based on the August 29th Japanese Patent Application 2016-166535 CLAIM OF PRIORITYs to Japanese publication in 2016 Its content is incorporated herein.
The present invention relates to the rolled h-section steel beams and its manufacturing method that carry out hot rolling to steel billet and manufacture.
Background technique
H profile steel is widely used as the blank of building/building/marine structure etc. all the time, in the form of various sections It is used.Especially manufactured using the slab of the rectangular section obtained by the high continuous casting of productivity as steel blank and by hot rolling H profile steel manufacturing cost it is low, be applied in many fields.It in the past, is by Fig. 1 (a) institute by the H profile steel that slab manufactures The edging method manufacture shown.Edging method is following milling method: firstly, setting is for guiding steel to rolling on slab end The slot in the pass center of roller, is then rolled along the width direction of slab, extends slab end along the thickness direction of slab, To form edge of a wing portion.The alloying element using Mn as representative is enriched in the center segregation portion formed when block.By rolling Side method is rolled, and the part that center segregation portion is referred to as " fillet part " in web part staggered with the edge of a wing, i.e. sometimes is poly- Collection generates adverse effect to toughness.
In view of such problems, the steel billet before proposing a kind of pair of hot rolling implements heat-treating methods, proposes to disappear Except gross segregation (aggregation in center segregation portion), by heat at high temperature certain time make the diffusions such as Mn be it is effective (for example, Referring to patent document 1).It is reheated in addition, proposing before one kind rolls after carrying out roughing to steel billet and among implementing Method, propose to promote to spread, after applying strain by rolling, keep being effective (for example, with reference to special at high temperature Sharp document 2 and 3).
In addition, in addition to heat treatment, it is also proposed that other eliminate the method for gross segregation (for example, with reference to 4 He of patent document 5).Patent document 4 discloses a kind of method depressed before complete solidification in continuous casting.And patent document 5 discloses one kind The edging pass of the width of plate slab of roughing mill is formed as to the method for the flat box pass in pass bottom, this method is referred to as wedge shape Method.
Existing technical literature
Patent document
Patent document 1: Japanese Unexamined Patent Publication 2012-180584 bulletin
Patent document 2: Japanese Unexamined Patent Publication 6-122921 bulletin
Patent document 3: Japanese Unexamined Patent Publication 6-122922 bulletin
Patent document 4: Japanese Unexamined Patent Publication 5-305395 bulletin
Patent document 5: Japanese Unexamined Patent Publication 7-88502 bulletin
Summary of the invention
Problems to be solved by the invention
As described above, all the time, in order to inhibit the toughness of fillet part of the rolled h-section steel beam as caused by gross segregation to drop It is low, propose various countermeasures.But all countermeasures are all in the presence of the production that can damage the edging method as the prior art The problem of rate.
Therefore, it is an object of the present invention to be based on such actual conditions, providing one kind will not damage as the prior art Edging method productivity, alleviate fillet part gross segregation rolled h-section steel beam and its manufacturing method.
The solution to the problem
The present invention is characterized in that having following process: by being formed with for the width direction to rolled material vertically The appearance for forming the protrusion of notch forms notch with pass, is gradually bent with this as the starting point.Process in this way, by When slab forms the edge of a wing, center segregation portion is dispersed to the entire edge of a wing, inhibits in fillet part with capable of not damaging productivity The aggregation in heart segregation portion.
Purport of the invention is as follows.
[1] a kind of rolled h-section steel beam, which is characterized in that with following chemical composition in terms of quality %:
C:0.01~0.25%,
Si:0.05%~0.50%,
Mn:0.40~2.50%,
P:0.050% or less,
S:0.050% or less,
N:0.020% or less,
Cu:0.70% or less,
Ni:0.70% or less,
Cr:0.50% or less,
V:0.12% or less,
Mo:0.30% or less,
Nb:0.08% or less,
Ti:0.05% or less,
Al:0.07% or less,
REM:0.010% or less,
Ca:0.0050% or less,
Surplus be Fe and inevitable impurity,
Preceding 5% average value of the Mn concentration in the most brittle portion on the edge of a wing of the rolled h-section steel beam is the Mn of following position 1.6 times of concentration are hereinafter, the position are as follows: the distance of the end face away from flange width direction on flange width direction is that the edge of a wing is wide 1/6 position of degree and be on the thickness direction of the edge of a wing being located at a distance from the surface of web opposite side for the edge of a wing away from the edge of a wing 1/4 position of thickness；Preceding 5% average value of the Mn concentration in the center segregation portion of the rolled h-section steel beam is following position 1.1 times or more and 1.6 times of Mn concentration hereinafter, the position are as follows: the end away from flange width direction on flange width direction The distance in face be flange width 1/6 position and be on the thickness direction of the edge of a wing away from the edge of a wing be located at and web opposite side The distance on surface is 1/4 position of edge of a wing thickness, and the center segregation part is dispersed in from the center of flange width towards the edge of a wing In region within one end face of width direction or two end face 15mm or more and thickness direction top flange surface layer 2mm.
[2] a kind of manufacturing method of rolled h-section steel beam, be by the heating steel billet of rectangular section to 1100~1350 DEG C and according to It is secondary to carry out roughing operation, intermediate rolling process, finishing rolling step to manufacture the manufacturing method of rolled h-section steel beam described in [1], feature It is, is provided on the milling train for carrying out aforementioned roughing operation for the multiple of 3 or more to the progress appearance of rolled material Pass, at least one of aforesaid plurality of pass is formed for notch uses pass, and aforementioned cut formation is located to be formed with pass and is used for The width direction of rolled material is vertically formed on the roll a pair of up and down of the protrusion of notch, hole is used in aforementioned cut formation The back segment of type is equipped with the appearance pass for will gradually be bent using the notch formation with the segmentaion position that pass is formed.
[3] manufacturing method of the rolled h-section steel beam according to [2], which is characterized in that be formed in aforementioned cut formation hole The top angle of protrusion in type is 40 ° or less.
[4] manufacturing method of the rolled h-section steel beam according to [2] or [3], which is characterized in that pass through aforementioned protrusion shape At the length H of notch, aforementioned rectangular section steel billet thickness T and the rolled h-section steel beam formed by finishing rolling step the edge of a wing Width F meet following formulas (1).
H≥0.5F-0.5T···(1)
The effect of invention
In accordance with the invention it is possible to the H profile steel of the excellent tenacity of fillet part is obtained by simple process, it is pre- without carrying out The special heat treatments such as reheating or temperature holding after heating, rolling.Therefore, the present invention is with can not damaging economy into one Step improves the reliability etc. of the steel structure using rolled h-section steel beam as component, contribution highly significant of the present invention to industry.
Detailed description of the invention
Fig. 1 is to schematically illustrate figure compared with " splitting point-score " for " edging method ".
Fig. 2 is the figure for showing the relationship of degree of segregation and Charpy transition temperature difference Δ vTrs.
Fig. 3 is to show the position of the observation that carries out mechanical test and metallographic structure to schematically illustrate figure.
Fig. 4 is to show the manufacturing process of H profile steel that embodiments of the present invention are related to schematically illustrate figure.
Fig. 5 is to show the shape of roll and rolled material for roughing to schematically illustrate figure.
Specific embodiment
Hereinafter, the embodiments of the present invention will be described with reference to the drawings.It should be noted that in the specification and drawings In, the constituent element constituted to function substantially having the same marks identical appended drawing reference, to omit repeated explanation.
The inventors of the present invention's discovery is manufactured by forming notch and cambered aerofoil edge when forming edge of a wing portion, can be made Segregation is dispersed in the entire edge of a wing, improves the aggregation of the segregation at fillet part.Firstly, this discovery is briefly described.
It should be noted that cambered aerofoil edge of the present embodiment to be carried out to the H-type of rolling appearance in this specification The manufacturing method of steel is known as " splitting point-score ".
Firstly, the summary of above-mentioned " splitting point-score " is briefly described referring to Fig.1.Fig. 1 is for as the existing of H profile steel Manufacturing method in roughing method a kind of so-called " edging method " and manufacturer as H profile steel of the present embodiment What so-called " the splitting point-score " of the roughing method in method was compared schematically illustrates figure.
As shown in (a) of Fig. 1, edging method be following method: by slab manufacture H profile steel when roughing when, at slab end For portion's setting for guiding the slab to the slot in pass center, the concave roll by being installed on roughing mill carries out the side of hot rolling Method.It will be rolled in the width direction by the slab of heating stove heating, extend slab end along the thickness direction of slab, thus shape At edge of a wing portion.It is real in order to further critically adjust shape, the size etc. of product to the rolled material for being formed with edge of a wing portion in this way The intermediate rolling by intermediate mill is applied, by finish rolling of finishing mill etc., to manufacture final H profile steel product.
On the other hand, as shown in (b) of Fig. 1, split in point-score, by slab manufacture H profile steel when roughing when, pass through notch The deeper slot of depth (notch) compared with above-mentioned edging method is arranged in formation pass on slab end face.Then, using being formed with For expanding the concave roll of the appearance pass of the protrusion of the slot, rolling appearance is carried out to the slot of formation, so that as dividing The slab end for cutting position, which is split, to be separated.Edge of a wing portion is formed for example, by the such splitting rolling appearance of angle progress is varied multiple times Method be to split point-score.Intermediate rolling, finish rolling etc. are further implemented to the rolled material for being formed with edge of a wing portion in this way, to make Make final H profile steel product.
The inventors of the present invention are conceived to present in the slab when to edging method shown in FIG. 1 with splitting point-score and being compared The highly concentrated position mainly Mn, i.e. center segregation portion, discovery pass through in roughing and the roughing by splitting point-score of edging method, plate There is very big difference in the aggregation in the center segregation portion of base or the state of dispersion.
That is, as shown in (a) of Fig. 1, it is known that when slab being rolled in the width direction by concave roll in edging method, center Segregation portion can assemble in fillet part.And as shown in (b) of Fig. 1, it splits in point-score, since it is not using substantially by slab edge Width direction rolls but splits method as point edge of a wing portion, therefore, with center segregation portion can be scattered in entire edge of a wing portion and The mode for not being gathered in fillet part is rolled.It especially finds: the protrusion top angle by making the pass of notch 40 ° of acute angles below, are able to suppress the aggregation in center segregation portion.
Also, the inventors of the present invention have found: by splitting point-score, at the F/6 of the average mechanical characteristics of display H profile steel, and vTrs (Charpy transition temperature) is 0 DEG C hereinafter, as shown in Fig. 2, by center segregation portion, can will deteriorate the most crisp of most serious with toughness The difference control of the vTrs in change portion is within 40 DEG C.Speculate this is because inhibiting inclined by being present in the highly concentrated center mainly Mn MnS in analysis portion, the island-like martensite (MA) as hard phase, embrittlement caused by upper bainite.
Hereinafter, being carried out specifically to rolled h-section steel beam of the present embodiment and its manufacturing method based on above-mentioned discovery It is bright.It should be noted that in the following description, as long as no special instructions, " % " about ingredient indicates " quality % ".
Firstly, being illustrated to H profile steel at being grouped as (chemical composition).
(C:0.01~0.25%)
C can promote the MA in fillet part to generate, and reduce toughness.But since C can inexpensively improve intensity, and making C is completely removed in the process of steel will lead to the increase of cost, therefore C amount is set as 0.01% or more.On the other hand, if C amount is more than 0.25%, then MA will increase at the position that the center segregation portion of fillet part assembles, and toughness can reduce, and therefore, C amount is limited to 0.25% or less.C amount is preferably set to 0.20% hereinafter, being more preferably set as less than 0.17%.
(Si:0.05% or more and 0.50% or less)
Si is deoxidant element, although also contributing to the raising of intensity, same as C is the element that can generate MA.Si amount If the generation of hard phase will lead to base material and the toughness of welding heat affected zone and reduce more than 0.50%, therefore, Si amount is limited It is 0.50% or less.Si amount is preferably set to 0.30% hereinafter, being more preferably set as 0.20% hereinafter, being further preferably set as 0.10% Below.But if being free of Si, the process cost of deoxidation be will increase, therefore contain 0.05% or more Si.
(Mn:0.40~2.50%)
The center segregation portion of the slab of the H profile steel manufactured by edging method is gathered in fillet part.Mn, which is particularly susceptible, to be gathered in The concentration rising in center segregation portion, local Mn can promote the formation for the MA for belonging to brittle phase, belong to the upper shellfish of coarse tissue The increase of hardness caused by the increase of family name's body, the increase of MnS, the rising of harden ability.As a result, toughness can significantly reduce.Especially If being that can damage base material and welding heat affected zone due to increase of field trash etc. in fillet part containing the Mn for having more than 2.50% Toughness.Therefore, Mn amount is limited to 2.50% or less.Mn amount be preferably set to 2.00% hereinafter, more preferably be set as 1.80% with Under.On the other hand, due to the effective element of miniaturization that Mn is to crystallization particle diameter, it is made to contain 0.40% or more.
(P:0.050% or less)
P is weld crack caused by solidifying segregation, toughness reduction reason for it, therefore should be reduced to the greatest extent.It is preferred that by P amount 0.050% is limited to hereinafter, further preferably 0.010% or less.In addition, for lower limit, if due to removing it to deficiency 0.001%, then steel cost processed will increase dramatically, therefore can be 0.001% or more.
(S:0.050% or less)
S can form MnS in the center segregation portion formed by solidifying segregation, can not only cause weld crack, toughness to reduce, also It will lead to hydrogen embrittlement crackle etc., therefore should reduce to the greatest extent.It is preferred that S amount is limited to 0.050% hereinafter, further preferred 0.010% Below.In addition, for its lower limit, if steel cost processed will increase dramatically, therefore can due to removing it to less than 0.001% Think 0.001% or more.
In turn, for the purpose for improving intensity and toughness, 1 in Cu, Ni, Cr, V, Mo, Nb, Ti, Al, N can also be contained It plants or two or more is as any addition element.It should be noted that due to any addition element it is not necessary to addition, because The lower limit value of the content of this each any addition element is 0%.
(Cu:0.70% or less)
Cu contributes to improve the element of intensity.But if Cu amount is more than 0.70%, intensity can be improved excessively, toughness It can reduce, therefore Cu amount is limited to 0.70% or less.Cu amount be preferably set to 0.50% hereinafter, more preferably be set as 0.30% with Under, be further preferably set as 0.10% or less.The lower limit of Cu amount is preferably 0.01%.
(Ni:0.70% or less)
Ni is for improving intensity and the extremely effective element of toughness.But Ni is expensive element, in order to inhibit alloy The rising of cost, by Ni amount be limited to 0.70% hereinafter, be preferably set to 0.50% hereinafter, more preferably be set as 0.30% hereinafter, into One step is preferably set to 0.10% or less.Ni amount is preferably set to 0.01% or more, is more preferably set as 0.02% or more.
(Cr:0.50% or less)
Cr is also the element for helping to improve intensity.But if addition is more than 0.50% Cr, carbonization is generated sometimes Object damages toughness, therefore Cr amount is limited to 0.50% hereinafter, being preferably set to 0.30% or less.The lower limit of Cr amount is preferably set to 0.01%.
(V:0.12% or less)
V is the element to form nitride (VN), in order to improve the intensity of base material, can contain 0.01% or more.V amount is preferred It is set as 0.02% or more, is more preferably set as 0.03% or more.On the other hand, since V is expensive element, by the upper of V amount It is limited to 0.12%, is preferably limited to 0.08%.
(Mo:0.30% or less)
Mo is the element for improving harden ability, helping to improve intensity.But if addition is more than 0.30% Mo, sometimes It can promote Mo carbide (Mo2C precipitation), especially deteriorates the toughness of welding heat affected zone at the generation of the MA in fillet part, Therefore Mo amount is limited to 0.30% hereinafter, being preferably set to 0.15% or less.The lower limit of Mo amount is preferably 0.01%.
(Nb:0.08% or less)
Nb is the element for making ferrite miniaturization, improving toughness.It, can extra-inhibitory but if adding more than 0.08% Ferrite transformation promotes the generation of MA, therefore Nb amount is limited to 0.08% hereinafter, being preferably set to 0.05% hereinafter, further It is preferably set to 0.03% or less.
(Ti:0.05% or less)
Ti is the element to form TiN, if Ti amount becomes the starting point of brittle break more than 0.05%, TiN meeting coarsening, Therefore Ti amount is limited to 0.05% or less.Ti amount is preferably set to 0.03% hereinafter, being more preferably set as 0.02% or less.Ti amount Lower limit can be 0%, but since fine TiN facilitates the miniaturization of tissue, can also contain 0.005% or more.
(Al:0.07% or less)
Although Al is deoxidant element, if Al amount is more than 0.07%, field trash will lead to base material and welding heat affected zone Toughness reduce, therefore Al amount is limited to 0.07% or less.Al amount is preferably set to 0.05% hereinafter, being more preferably set as 0.04% Hereinafter, being further preferably set as 0.03% or less.The lower limit of Al amount is not limited, can be 0%, but Al is useful deoxidation Element can also contain 0.01% or more.
(N:0.020% or less)
N is the element for reducing the toughness of base material and welding heat affected zone.If N amount more than 0.020%, is dissolved N, coarse The formation of precipitate can damage low-temperature flexibility, therefore N amount is limited to 0.020% or less.N amount is preferably set to 0.010% or less, More preferably it is set as 0.007% or less.On the other hand, if being reduced to N amount less than 0.002%, steel cost processed be will increase, therefore N amount or 0.002% or more.From the angle of cost, N amount or 0.003% or more.
It in turn, can also be containing a kind or 2 kinds in REM, Ca as any for the purpose of the form of control field trash Addition element.
(REM:0.010% or less, Ca:0.0050% or less)
REM and Ca is deoxidant element, it helps controls the form of sulfide, therefore can add.But due to REM, The oxide of Ca is easy to float in molten steel, therefore the REM amount contained in steel is limited to 0.010% or less, limits Ca amount It is 0.0050% or less.The lower limit of REM amount and Ca amount is preferably set to 0.0005%.
Next, the metallographic structure and characteristic to rolled h-section steel beam of the present invention are illustrated.Fig. 3 is to show progress The position of the observation of mechanical test and metallographic structure schematically illustrates figure.Hereinafter, main explanation is in the position shown in fig. 3 The result that metallographic structure, characteristic are verified.
As shown in figure 3, the distance about the end face in the edge of a wing away from flange width direction on flange width direction is 1/6 Position and being located at away from the edge of a wing is 1/4 at a distance from the surface (that is, lateral surface) of web opposite side on the thickness direction of the edge of a wing Position, the top flange and temperature that temperature is easily reduced when being located at hot rolling are not easy the centre of reduced edge of a wing central portion.In addition, Center segregation portion will not be observed at the position.It is therefore contemplated that the position can show being averaged for H profile steel according to Temperature Distribution Chemical component and mechanical property.
It should be noted that the position is expressed as " F/6-t/ using flange width F and edge of a wing thickness t in this specification 4”。
H profile steel of the present embodiment inhibits the material deviation in the edge of a wing.Therefore, the F/ of H profile steel shown in Fig. 3 Each position in most brittle portion and F/6-t/4 near 2-3t/4 cuts the sight that coupons carry out the metallographic structure of H profile steel respectively Examine the measurement with mechanical property (intensity and Charpy impact energy (Charpy absorbed energy)).
Situation when according to edge of a wing roughing is different, and the position in most brittle portion is relative to the left and right directions of figure, i.e. flange width Direction is not necessarily.Therefore, on the basis of the part apparent for assembling center segregation portion by nital, The position (3t/4) that will indicate that being located at a distance from the surface of web opposite side away from the edge of a wing is 3/4 on the thickness direction of the edge of a wing The part that straight line intersects with the part that aforesaid central segregation portion assembles is determined as the position in most brittle portion.From having determined position most Brittle portion cuts coupons, implements to the observation of metallographic structure and the measurement of mechanical property.
This hair is carried out by optical microscopy, scanning electron microscope (SEM) and electron probe microanalyzer (EPMA) The evaluation of the metallographic structure of bright rolled h-section steel beam.By optical microscopy, determine centered on most brittle portion shown in Fig. 3 The visual field of 10mm × 10mm.In determining visual field, acceleration voltage 20kV, beam shape are 20 μm of length after electrolytic polishing Under conditions of 20 μm of band-like, step pitch (step), the Mn concentration in the position in determining most brittle portion is measured.In visual field 500 points × 500 points in, find out 12500 points of the average value (being referred to as " preceding 5% average value ") of the value for preceding 5% or more, As the Mn concentration (CMn-max) in most brittle portion.
On the other hand, sample will be cut and according to JIS G0404 (version in 2014) to the sample from the position of F/6-t/4 Chemical component is analyzed and the value of Mn concentration that finds out is as the Mn concentration (CMn) at the position of F/6-t/4.In turn, will (CMn-max) value (CMn-max)/(CMn) obtained divided by (CMn) is evaluated as degree of segregation.
The target value of the intensity of rolled h-section steel beam of the present invention is the Standard of steel used based on European Region EN10225 setting.It is desirable that the yield point measured at normal temperature using the coupons cut from the position of F/6-t/4 (YP) or 0.2% yield strength is 325MPa or more, tensile strength (TS) is 450MPa or more.The target value of toughness is set as Δ vTrs≤40℃。
Fig. 2 is the figure for showing the relationship of degree of segregation and Charpy transition temperature difference Δ vTrs in H profile steel.Referring to Fig. 3, Fig. 2 In degree of segregation refer to above-mentioned most brittle portion and the position of F/6-t/4 Mn concentration ratio.
As shown in Fig. 2, degree of segregation is more than 1.6 in the case where the rolled h-section steel beam manufactured by previous edging method, And the Charpy transition temperature difference Δ vTrs of most brittle portion and the position of F/6-t/4 is more than 40 DEG C.In this state, most brittle portion Place Mn can be more segregated, and thus resulted in MnS, the island-like martensite (MA) for belonging to hard phase, upper bainite etc., become nothing Method inhibits embrittlement.
On the other hand, about the rolled h-section steel beam by splitting point-score manufacture, the summer of the position of most brittle portion and F/6-t/4 Δ vTrs poorer than transition temperature is 40 DEG C or less.That is, center segregation portion assembles in the state that degree of segregation is 1.6 or less To inhibition, the excellent rolled h-section steel beam of homogeneity in the section compared with previous product in the edge of a wing can be obtained.
It should be noted that whens the steel construction used under the conditions of general temperature is by seismic force etc., in order to Make the H profile steel of component meet as defined in mechanical property without brittle break, it is generally desirable to the vTrs of the position of F/6-t/4 is 0 DEG C or less.
As described above, degree of segregation shown in Fig. 2 is preferably 1.6 or less in rolled h-section steel beam of the present invention.In turn, Since degree of segregation is lower, the aggregation in center segregation portion can more be inhibited, and embrittlement characteristic is better, therefore more preferably 1.5 or less. In addition, degree of segregation is not less than 1.0 in numerical characteristic, preferably such as 1.0 or more or 1.1 or more.
Next, being illustrated to the manufacturing method of H profile steel of the present embodiment.In present embodiment, in Fig. 4 institute In the process shown, the steel billet of the rectangle excellent to productivity is heated, and is implemented by roughing operation, intermediate rolling process, finish rolling The hot rolling that process is constituted carries out acceleration cooling by water cooling plant, manufactures H profile steel.In hot rolling, split shown in (b) by Fig. 1 Point-score carries out roughing.
In steel process processed (upstream side of the heating furnace in Fig. 4), is cast, obtained after adjusting the chemical component of molten steel The steel billet (also referred to as so-called " slab ") of rectangle.From the angle of productivity, casting is preferably continuous casting.In addition, from production The angle of rate is set out, and the thickness of steel billet is preferably set to 200mm or more, it is contemplated that the reduction of segregation, heating temperature in hot rolling Uniformity etc., preferably 350mm or less.
Next, carrying out hot rolling using heating stove heating steel billet.Next, carrying out (b) using Fig. 1 using roughing mill Shown in split the roughing of point-score.Then, intermediate rolling is carried out using intermediate universal mill (intermediate mill) and water cooling plant.It connects down Come, finish rolling is carried out using finishing mill, to complete hot rolling.At this point, water cooling can also be carried out to H profile steel at necessary time point. Hereinafter, being illustrated to the condition etc. in each process.
(heating temperature of steel billet: 1100~1350 DEG C)
The heating temperature of steel billet is set as 1100~1350 DEG C.When heating temperature is low, deformation drag can be got higher, therefore, in order to Ensure the appearance in hot rolling, is set to 1100 DEG C or more.On the other hand, if the heating temperature of steel billet is more than 1350 DEG C, Sometimes the oxide as the surface of the steel billet of blank can melt and cause to damage to inside heating furnace.In order to sufficiently be dissolved Nb etc. The element for forming precipitate, is preferably set as 1150 DEG C or more for the lower limit of the heating temperature of steel billet.Especially, when the plate thickness of product Bao Shi, accumulation reduction ratio can become larger, therefore the heating temperature of steel billet is preferably set as 1200 DEG C or more.In order to keep tissue fine, It is preferred that the upper limit of the heating temperature of steel billet is set as 1300 DEG C or less.
(restriction of the incision length H in roughing operation)
In using the roughing for splitting point-score, incision length H can also be set, so that the thickness of the steel billet of rectangular section Spend T, by finishing rolling step formed rolled h-section steel beam the edge of a wing width F, with Fig. 5 in based on defined pass top angle The incision length H of the pass of (the protrusion top angle of pass inner circumferential) meets following formula (1).
H≥0.5F-0.5T···(1)
As shown in above-mentioned formula (1), the lower limit of incision length H is set as the thickness T of the steel billet relative to rectangular section and is led to The width F for crossing the edge of a wing of the rolled h-section steel beam of finishing rolling step formation is 0.5F-0.5T or more.This is for the wing after roughing It carries out thus inhibiting to be based on center segregation portion using the rolling appearance for splitting point-score until edge width is identical as the flange width of product It is easy the drafts of the pass at the obtuse angle of aggregation.The upper limit of incision length H is not particularly limited, if but more than 0.8F- 0.5T then may require that excessive edging rolling when intermediate rolling, productivity can decline, therefore preferably 0.8F-0.5T or less.
(the protrusion top angle in pass when notch)
(b), pass top shown in fig. 5 angle (the protrusion top angle of pass inner circumferential) for Fig. 1, as long as being set as The angle of enough acute angles for being used to form notch, such as its upper limit can be set as 40 °.This is because pass top If angle, more than 40 °, the center segregation portion of slab will not be scattered in the edge of a wing, and can be rolled with edging shown in Fig. 1 (a) Similarly it is gathered in fillet part.By making 40 ° of pass top angle hereinafter, such as the splitting shown in point-score of (b) of Fig. 1, When rolling based on notch formation pass, center segregation portion will not assemble in the edge of a wing but be dispersed, and be able to suppress fillet The reduction of toughness in portion.
The lower limit of pass top angle is not particularly limited, if but lower than 25 °, roll may be rolled over when rolling Damage, therefore preferably 25 ° or more.
It should be noted that at this point, the center segregation portion of slab may not be the dispersion as shown in (b) of Fig. 1 In the left and right edge of a wing under I form, and it is dispersed in any one the edge of a wing of left and right.
Point-score is split according to shown in (b) of Fig. 1, when manufacture such as flange width is the rolled h-section steel beam of 150mm or more, Center segregation portion can be dispersed in the portion of the edge of a wing, remain in the following region in the edge of a wing: from the immediate vicinity direction of flange width One end face in flange width direction or two end face 15mm or more and thickness direction top flange surface layer is (in edge of a wing thickness direction On away from being located at edge of a wing face with web opposite side) in region within 2mm.Point-score manufacture rolling is split according to shown in (b) of Fig. 1 When H profile steel, the center segregation portion for being dispersed to edge of a wing portion can remain in defined length range in this region.It is scattered in this Center segregation portion near surface layer is periodically likely to occur above-mentioned by nital really.
5% mean concentration before the Mn being scattered in the center segregation portion near surface layer is set as (CMn-surface), it should It is ideal that degree of segregation (CMn-surface)/(CMn) in position, which is 1.1 or more and 1.6 or less,.Split point-score and edging method phase Than the degree of segregation on edge of a wing surface layer is in the trend got higher.For degree of segregation if 1.1 or more, then surface can be confirmed by visual observation by having Crackle, check easy advantage, can also be to the products of multiple manufactures respectively with individual in addition, the crackle based on surface Form is tracked.On the other hand, if the degree of segregation is more than 1.6, easily there are a large amount of crackles, therefore, degree of segregation in flange surfaces Preferably 1.1 or more and 1.6 or less.It should be noted that preceding 5% mean concentration in (CMn-surface) finds out method With preceding 5% mean concentration in above-mentioned (CMn-max) to find out method consistent.That is, only sample cut position difference, numerical value It is essentially identical to find out method.
(intermediate rolling process)
In the intermediate rolling process of hot rolling, the controlled rolling based on intermediate universal mill can be carried out.Controlled rolling is The manufacturing method that rolling temperature and reduction ratio are controlled.In the intermediate rolling of hot rolling, the road of 1 passage or more is preferably implemented Water cooling rolling processing between secondary.Between passage in water cooling rolling processing, the table on the edge of a wing is assigned by carrying out water cooling between rolling pass Layer portion and internal temperature differential, are rolled.Water cooling rolling processing is for example by the water cooling between rolling pass, by the edge of a wing between passage Surface temperature water cooling is to the manufacturing method after 700 DEG C or less, rolled in heat recovery process.
When carrying out water cooling rolling processing between passage, it is preferable to use be arranged in the water cooling plant of the front and back of intermediate universal mill into Water cooling between row rolling pass, the misting cooling for preferably repeating the edge of a wing lateral surface based on water cooling plant and reversely rolling. Between passage in water cooling rolling processing, even if processing strain can be also directed into the inside of plate thickness in the case where reduction ratio is low. In addition, by the way that rolling temperature is reduced in a short time using water cooling, additionally it is possible to improve productivity.
Alternatively, it is also possible to directly pass through and be arranged in essence after the hot rolling as intermediate rolling process and finishing rolling step The water cooling plant of the outlet side of milling train is implemented to accelerate cooling to the inner surface and the outer surface on the edge of a wing.The surfaces externally and internally on the edge of a wing as a result, Cooling velocity become uniformly, material and form accuracy to can be improved.For the upper surface of the web after roughing operation, table thereon Surface side is cooled by the cooling water for being injected in the inner surface on the edge of a wing.It, can also be under web in order to inhibit the warpage of web Surface is cooled down.
It, can be in the rolled h-section steel beam that the manufacturing method of the H profile steel by present embodiment described above manufactures Make not assemble in fillet part in the existing center segregation portion in the slab before appearance that rolls, but disperse, is made to complete rolling Shape.Specifically, can manufacture Δ vTrs is 40 DEG C of rolled h-section steel beams below, degree of segregation in the edge of a wing rolled after appearance For 1.6 or less (referring to fig. 2).
Such rolled h-section steel beam can be special to toughness, embrittlement to avoid the center segregation portion aggregation at the fillet part on the edge of a wing Property generate adverse effect.That is, can be realized the manufacture of the excellent H profile steel product of toughness, embrittlement characteristic.In addition, being scattered in the edge of a wing Although center segregation portion in can remain in the edge of a wing, from the center of flange width towards an end face in flange width direction Or two end face 15mm or more and on the thickness direction of the edge of a wing away from being located at a distance from the surface of web opposite side within 2mm In region, but speculate due to not assembling, toughness, embrittlement characteristic will not substantially be had an impact.In turn, in the past in order to The internal state on the edge of a wing is investigated and sought various inspection/experiments etc., but in the H profile steel product of present embodiment, It can investigate by visual observation positioned at the flange surfaces with web opposite side.
More than, an example of embodiments of the present invention is illustrated, but the present invention is not limited to diagrams Mode.Various modifications or fixed case can be used in the scope of the design documented by claims, it will be understood that these Scheme is it is also apparent that fall within protection scope of the present invention.
Embodiment
As the embodiment of the present invention, manufactured with manufacturing condition illustrated by above embodiment at being grouped as from meeting Rolled h-section steel beam in cut sample, to the sample carry out chemical analysis.On the other hand, as comparative example, from being unsatisfactory for above-mentioned reality It applies and cuts sample at being grouped as in the rolled h-section steel beam of any one with manufacturing condition illustrated by mode, carry out same chemistry Analysis.Hereinafter, being illustrated to the comparison of detailed embodiment, comparative example.
(embodiment)
Firstly, as embodiment No.1~13,28, melting has shown in table 1 at being grouped as (unit: quality %) Steel manufactures the steel billet with a thickness of 250~300mm by continuous casting.The melting of steel carries out in converter, carries out a deoxidation, addition Alloy adjusting component, and Fruit storage is carried out as needed.Then, to obtained steel under the manufacturing condition shown in table 2 Base carries out hot rolling.In hot rolling, after carrying out roughing, using intermediate universal mill and the water cooling plant that is arranged in front of and after it, according to need The misting cooling for implementing edge of a wing lateral surface and the water cooling after reversed rolling and rolling.
[table 1]
[table 2]
Then, from most brittle portion and each position (referring to Fig. 3) of F/6-t/4, using rolling direction as length direction Test film is cut, mechanical property is measured.As mechanical property, yield point (YP), tensile strength (TS), vTrs are measured.Stretch examination It tests and is carried out according to JIS Z 2241 (version in 2011), Charpy-type test is carried out according to JIS Z 2242 (version in 2005).In addition, Sample is cut from most brittle portion and each position of F/6-t/4, the 10mm (length direction) assembled for center segregation portion × Region in the square of 10mm (edge of a wing thickness direction) is measured and is calculated respectively (CMn-max) by EPMA and according to JIS The method measurement and calculate (CMn) that G 0404 (version in 2014) is recorded.
In addition, from the center of flange width towards at least one end face 15mm or more and surface layer 2mm in flange width direction Within region in remain center segregation, as the Mn concentration of surface section, to without containing in parallel with edge of a wing thickness direction The region (referring to Fig. 3) of 10mm, is measured and is calculated (CMn- by EPMA under heart segregation and thickness direction top flange surface layer surface)。
Measurement/calculated result is shown in following tables 3.
[table 3]
Wherein, the target value as each characteristic for the H profile steel that should be manufactured, yield point (YP) or 0.2% surrender under room temperature Intensity is 335MPa or more, and tensile strength (TS) is 450MPa or more, and Δ vTrs is 40 DEG C or less.
As shown in table 3, No.1~13 of embodiment, 28 room temperature intensity in target zone, and Δ vTrs meet 40 DEG C or less as target value.In addition, the degree of segregation of Mn is 1.6 or less.The degree of segregation of Mn is preferably 1.5 hereinafter, more Preferably 1.4 or less.
(comparative example)
For No.14~27 as comparative example, melting has shown in table 4 into the steel being grouped as, according to above-mentioned reality The same method manufacture of example is applied with a thickness of the steel billet of 250~300mm.Then, to obtained steel under the manufacturing condition shown in table 5 Base carries out hot rolling.
Wherein, the part in following table 4 and table 5 with underscore is this hair for being unsatisfactory for illustrating in above embodiment It is bright at the part being grouped as with manufacturing condition.
[table 4]
[table 5]
Then, from most brittle portion and the position F/6-t/4 (referring to Fig. 3), examination is cut using rolling direction as length direction Piece is tested, mechanical property is measured in the same manner as above-described embodiment.As mechanical property, measure yield point (YP), tensile strength (TS), vTrs.In addition, cutting sample from each position of most brittle portion, surface section and F/6-t/4, divide in the same manner as above-described embodiment It is not measured by EPMA and calculates (CMn-max) and (CMn-surface), and is recorded according to JIS G0404 (version in 2014) Method measurement and calculate (CMn).
Measurement/calculated result is shown in following tables 6.It should be noted that having the part of underscore in following tables 6 It is the numerical value of the target value of each characteristic for the H profile steel for being unsatisfactory for manufacture.
[table 6]
As shown in table 6, No.14,16,18 due to C, Mn, Si amount less and intensity is insufficient.The C amount of No.15 is more, the Si of No.17 Amount is more, and increase and coarsening due to hard phase cause the vTrs at F/6-t/4 to be 0 DEG C or more, the toughness at most brittle portion It reduces.The Mn amount of No.19 is more, and the vTrs at F/6-t/4 is 0 DEG C or more, and the center segregation degree at most brittle portion deteriorates, due to MnS, MA cause toughness to deteriorate.The P amount of No.20 is more, and the S amount of No.21 is more, and toughness reduces.Pass top of the No.22 due to roughing Angle is more than 40 °, and central segregation of slab portion does not disperse and assembled, therefore the toughness in most brittle portion reduces.No.23,24 Due to the curtailment of notch, central segregation of slab portion does not disperse and is assembled, therefore the toughness in most brittle portion reduces. The Nb amount of No.25 is more, and the Mo amount of No.26 is more, and the REM amount of No.27 is more, and the toughness in most brittle portion reduces.
Industrial availability
The present invention is suitable for the rolled h-section steel beam and its manufacturing method manufactured to steel billet progress hot rolling.

Claims (4)

1. a kind of rolled h-section steel beam, which is characterized in that with following chemical composition in terms of quality %:
C:0.01~0.25%,
Si:0.05%~0.50%,
Mn:0.40~2.50%,
P:0.050% or less,
S:0.050% or less,
N:0.020% or less,
Cu:0.70% or less,
Ni:0.70% or less,
Cr:0.50% or less,
V:0.12% or less,
Mo:0.30% or less,
Nb:0.08% or less,
Ti:0.05% or less,
Al:0.07% or less,
REM:0.010% or less,
Ca:0.0050% or less,
Surplus: Fe and inevitable impurity,
Preceding 5% average value of the Mn concentration in the most brittle portion on the edge of a wing of the rolled h-section steel beam is the Mn concentration of following position 1.6 times hereinafter, the position are as follows: the distance of the end face away from flange width direction on flange width direction is flange width 1/6 position and be on the thickness direction of the edge of a wing being located at a distance from the surface of web opposite side for edge of a wing thickness away from the edge of a wing 1/4 position,
Preceding 5% average value of the Mn concentration in the center segregation portion of the rolled h-section steel beam is the 1.1 of the Mn concentration of following position Times or more and 1.6 times hereinafter, the position are as follows: the distance of the end face away from flange width direction on flange width direction be the edge of a wing 1/6 position of width and be on the thickness direction of the edge of a wing being located at a distance from the surface of web opposite side for the wing away from the edge of a wing 1/4 position of edge thickness, the center segregation part are dispersed in one from the center of flange width towards flange width direction In region within end face or two end face 15mm or more and thickness direction top flange surface layer 2mm,
The most brittle portion on the edge of a wing refers to: indicating the surface being located at web opposite side on the thickness direction of the edge of a wing away from the edge of a wing Distance be edge of a wing thickness 3/4 position the part intersected with the part that center segregation portion assembles of straight line,
Preceding 5% average value of the Mn concentration is following average value: determine the visual field of 10mm × 10mm, 500 in visual field In point × 500 point, become 12500 points of average value of preceding 5% or more value.
2. a kind of manufacturing method of rolled h-section steel beam,
It is that the heating steel billet of rectangular section to 1100~1350 DEG C and is successively carried out to roughing operation, intermediate rolling process, essence Roll the manufacturing method that process carrys out rolled h-section steel beam described in manufacturing claims 1, which is characterized in that
3 or more multiple holes for carrying out appearance to rolled material are provided on milling train for carrying out the roughing operation Type,
At least one of the multiple pass be notch formed use pass, the notch formation be located at pass be formed with for pair The width direction of rolled material is vertically formed on the roll a pair of up and down of the protrusion of notch,
The back segment of the notch formation pass be equipped with for will using the notch formation pass formed segmentaion position by The appearance pass gradually bent.
3. the manufacturing method of rolled h-section steel beam according to claim 2, which is characterized in that be formed in the notch and form use The top angle of protrusion on pass is 40 ° or less.
4. the manufacturing method of rolled h-section steel beam according to claim 2 or 3, which is characterized in that formed using the protrusion The length H of notch, the rectangular section steel billet thickness T and the edge of a wing of the rolled h-section steel beam formed by finishing rolling step Width F meets following formulas (1),
H≥0.5F-0.5T···(1)。
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CN108642381B (en) * 2018-05-16 2020-02-18 山东钢铁股份有限公司 Hot-rolled high-toughness low-temperature-resistant H-shaped steel with yield strength of 460MPa and preparation method thereof
CN110527915B (en) * 2019-09-25 2020-12-01 马鞍山钢铁股份有限公司 460 MPa-level hot-rolled H-shaped steel and production method thereof
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CN110629112A (en) * 2019-09-25 2019-12-31 马鞍山钢铁股份有限公司 Hot-rolled H-shaped steel with yield strength of 550MPa and production method thereof
CN110592479B (en) * 2019-09-25 2020-12-01 马鞍山钢铁股份有限公司 Hot-rolled H-shaped steel and production method thereof
CN112458364B (en) * 2020-11-04 2021-09-03 马鞍山钢铁股份有限公司 Ultra-thick hot-rolled H-shaped steel and production method thereof
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CN113234995B (en) * 2021-04-14 2022-04-26 马鞍山钢铁股份有限公司 Ultra-thick hot-rolled H-shaped steel with yield strength of 600MPa and production method thereof
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