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CN108350550A - The excellent high strength cold rolled steel plate of shearing and its manufacturing method - Google Patents

The excellent high strength cold rolled steel plate of shearing and its manufacturing method Download PDF

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Publication number
CN108350550A
CN108350550A CN201680067955.6A CN201680067955A CN108350550A CN 108350550 A CN108350550 A CN 108350550A CN 201680067955 A CN201680067955 A CN 201680067955A CN 108350550 A CN108350550 A CN 108350550A
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China
Prior art keywords
rolled steel
relational expression
shearing
steel plate
high strength
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Granted
Application number
CN201680067955.6A
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Chinese (zh)
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CN108350550B (en
Inventor
金成�
金成一
徐石宗
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Posco Holdings Inc
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Posco Co Ltd
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    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • 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
    • B21B1/02—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 heavy work, e.g. ingots, slabs, blooms, or billets, in which the cross-sectional form is unimportant ; Rolling combined with forging or pressing
    • B21B1/026—Rolling
    • 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
    • B21B1/22—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 plates, strips, bands or sheets of indefinite length
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    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
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    • 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
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    • 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
    • C21D8/0236—Cold rolling
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    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
    • C—CHEMISTRY; METALLURGY
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    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0421—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the working steps
    • C21D8/0436—Cold rolling
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    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0447—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment
    • C21D8/0463—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment following hot rolling
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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    • 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
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    • 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
    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
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    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
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    • 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
    • C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—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
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    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
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    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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    • 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
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    • 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
    • C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
    • 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
    • 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
    • B21B1/22—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 plates, strips, bands or sheets of indefinite length
    • B21B2001/225—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 plates, strips, bands or sheets of indefinite length by hot-rolling
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    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/004—Dispersions; Precipitations
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    • C21—METALLURGY OF IRON
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    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/005—Ferrite
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    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0405—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing of ferrous alloys
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    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0421—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the working steps
    • C21D8/0426—Hot rolling

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  • Metallurgy (AREA)
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  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Sheet Steel (AREA)

Abstract

One aspect of the present invention is related to the excellent high strength cold rolled steel plate of shearing, and in terms of weight %, the cold-rolled steel sheet includes：C：0.05~0.10%, Si：0.01~0.5%, Mn：1.2~2.0%, Al：0.01~0.1%, Cr：0.005~0.3%, B：0.0003~0.0010%, Mo：0.005~0.2%, P：0.001~0.05%, S：0.001~0.01%, N：0.001~0.01%, Nb：0.005~0.08%, Ti：0.005~0.13%, V：0.005~0.2%, the Fe of surplus and inevitable impurity, and meet following relational expressions (1) and relational expression (2), and include one or more of carbide, nitride and carbonitride.Relational expression (1)：2.0≤[Mn]+2.5 [Mo]+1.5 [Cr]+300 [B]≤2.5, relational expression (2)：0.2≤([Nb]/93+ [Ti]/48+ [V]/51)/([C]/12+ [N]/14)≤0.5 (wherein, the weight % of each element symbolic indication alloying element in the relational expression (1) and relational expression (2)).

Description

The excellent high strength cold rolled steel plate of shearing and its manufacturing method
Technical field
The present invention relates to the excellent high strength cold rolled steel plate of shearing and its manufacturing methods.
Background technology
In order to be used in automatic gearbox friction plate purposes etc., not only need reduce shearing caused by split The generation of line, and the propagation of crackle caused by inhibiting frictional heat is needed, and need high intensity and high rigidity.
It is existing for friction plate or for ensuring that the high strength cold rolled steel plate of hardness uses as disclosed in patent document 1 Using recovery annealing method (recovery annealing method) to medium carbon steel or the steel comprising a variety of alloying elements carries out The technology of annealing heat-treats is carried out after cold rolling.In addition, usually using the method for carrying out nodularization heat treatment procedure to high-carbon steel, and The technology of the secondary cold-rolling method using cold rolling-annealing-cold rolling is proposed in patent document 2.
But using the high-strength steel sheet of recovery annealing method with being difficult to manufacture the steel with high intensity the problem of, and Carrying out the technology of nodularization heat treatment and Double Cold Reduction Technology using high-carbon steel has the problem of needing high manufacturing cost.
In addition, just in order to manufacture the high-strength steel sheet of cold rolling and the alloying components such as main C, Si, Mn, Mo, Cr to be used and Speech when adding the amount of required content or more, can cause although effectively improving the intensity of steel plate by solid solution strengthening effect The segregation of alloying component is uneven with microstructure.In particular, the quenching degree of steel is increased while cooling, to can substantially prolong Slow ferritic phase transformation, and low-temperature phase (martensitic phase and austenite phase) is will produce, crystal boundary becomes uneven, to which shearing adds Working hour increases the generation of crackle, and crackle is easy to propagate when generating frictional heat during use, therefore will produce defect.
In addition, when the addition of the alloying components such as Ti, Nb, V for being used to further increase intensity is inappropriate, in crystal boundary Coarse carbide, nitride and precipitate are formed, the yield increase of crackle and shearing when to shearing When crackle be easy propagate the problem of.In addition, when the position by shearing generates frictional heat during use, have more The problem of easy ting produce the propagation of crackle.
(existing technical literature)
(patent document 1) application number KR1998-0059809
(patent document 2) application number DE2005-10031462
Invention content
Technical problems to be solved
The purpose of the present invention is to provide can inhibit cutting for crackle caused by crackle caused by shearing and frictional heat Cut the high strength cold rolled steel plate and its manufacturing method of excellent in workability.
In addition, the technical problems to be solved by the invention are not limited to above-mentioned content.Skill to be solved by this invention Art problem can be understood by the entire content of this specification, for general technical staff of the technical field of the invention Speech understands that the supplementary technology problem of the present invention is that milli is with no difficulty.
Technical solution
One aspect of the present invention is related to the excellent high strength cold rolled steel plate of shearing, described cold in terms of weight % Rolled steel plate includes：C：0.05~0.10%, Si：0.01~0.5%, Mn：1.2~2.0%, Al：0.01~0.1%, Cr： 0.005~0.3%, B：0.0003~0.0010%, Mo：0.005~0.2%, P：0.001~0.05%, S：0.001~ 0.01%, N：0.001~0.01%, Nb：0.005~0.08%, Ti：0.005~0.13%, V：0.005~0.2%, surplus Fe and inevitable impurity, and meet following relational expressions (1) and relational expression (2), and include carbide, nitride and One or more of carbonitride.
Another aspect of the present invention is related to the method for manufacturing the excellent high strength cold rolled steel plate of shearing comprising Following steps：Heating steel billet is to 1200~1350 DEG C, and in terms of weight %, the steel billet includes：C：0.05~0.10%, Si： 0.01~0.5%, Mn：1.2~2.0%, Al：0.01~0.1%, Cr：0.005~0.3%, B：0.0003~0.0010%, Mo：0.005~0.2%, P：0.001~0.05%, S：0.001~0.01%, N：0.001~0.01%, Nb：0.005~ 0.08%, Ti：0.005~0.13%, V：0.005~0.2%, the Fe of surplus and inevitable impurity, and meet following Relational expression (1) and relational expression (2)；At a temperature of 850~1150 DEG C of ranges, hot rolling is carried out to the steel billet by heating； The hot rolling postcooling to 550~750 DEG C of ranges temperature and wound；And pickling is carried out after the winding, and with 60 ~70% cold rolling reduction ratio carries out cold rolling.
Relational expression (1)：2.0≤[Mn]+2.5[Mo]+1.5[Cr]+300[B]≤2.5
Relational expression (2)：0.2≤([Nb]/93+[Ti]/48+[V]/51)/([C]/12+[N]/14)≤0.5
(wherein, the weight % of each element symbolic indication alloying element in the relational expression (1) and relational expression (2)).
Also, the technical solution does not list all features of the present invention.For the various features and root of the present invention According to the advantages of its and effect, it is referred to specific implementation mode below and is understood in more detail.
Advantageous effect
The present invention has the effect of being capable of providing the excellent high strength cold rolled steel plate of shearing and its manufacturing method, institute High intensity and high rigidity can not only be ensured by stating steel plate, and can be inhibited caused by crackle caused by shearing and frictional heat Crackle.
Description of the drawings
Fig. 1 is the chart of the value of the relational expression (1) and relational expression (2) that show embodiment.
Preferred forms
In the following, the preferred embodiment of the present invention will be described.But embodiments of the present invention can be changed into Other various forms, the scope of the present invention are not limited to embodiment described below.In addition, the embodiment party of the present invention Formula is to provide having the technical staff of average knowledge to be described more fully the present invention in the art.
In the following, the high strength cold rolled steel plate excellent to the shearing of the present invention is described in detail.It should be noted that Be following composition of alloy unit be weight %.
The excellent high strength cold rolled steel plate of shearing of the invention, in terms of weight %, including：C：0.05~ 0.10%, Si：0.01~0.5%, Mn：1.2~2.0%, Al：0.01~0.1%, Cr：0.005~0.3%, B：0.0003~ 0.0010%, Mo：0.005~0.2%, P：0.001~0.05%, S：0.001~0.01%, N：0.001~0.01%, Nb： 0.005~0.08%, Ti：0.005~0.13%, V：0.005~0.2%, the Fe of surplus and inevitable impurity, and it is full Foot states relational expression (1) and relational expression (2), and includes one or more of carbide, nitride and carbonitride.
C：0.05~0.10%
The C is the most economical and effective element for strengthening steel, precipitating reinforcing effect or bainite phase when increasing additive amount A point rate increased, so that tensile strength can be increased.When the content of C is less than 0.05%, precipitate is formed with Ti, Nb, V etc. Reaction reduce, to precipitation strength effect it is low.On the other hand, when the content of the C is more than 0.10 weight %, in crystal boundary When easy ting produce coarse carbide, and carrying out shearing, microcrack is generated on coarse carbide interface, to Shearing is deteriorated.It is therefore preferable that including the C with the content of 0.05~0.10 weight %.
Si：0.01~0.5%
The Si makes deoxidation of molten steel, and has solid solution strengthening effect, and postpones the formation of coarse carbide, to have Conducive to raising mouldability.But when the content of Si is less than 0.01%, the effect for postponing the formation of carbide is few, to be difficult to Mouldability is improved, when the content of Si is more than 0.5%, red oxidization skin caused by Si is formed in surface of steel plate when carrying out hot rolling, To not only make the quality of surface of steel plate become excessively poor, but also there is the problem of reducing ductility and weldability.Therefore, excellent Choosing includes the Si with 0.01~0.5% content.
Mn：1.2~2.0%
Identical as Si, the Mn is the effective element of solution strengthening to steel, and increases the quenching degree of steel, to weld It is easy to form bainite phase in welding heat affected zone afterwards.But it when the content of Mn is less than 1.2%, is unable to fully be added The effect caused by Mn.On the other hand, when the content of Mn is more than 2.0%, quenching degree is significantly increased and postpones ferrite Phase transformation, to can also reduce precipitating reinforcing effect, and in continuously casting process when block mid-depth portion it is inclined Analysis portion obtains substantially flourishing, and the microstructure that while being cooled down after hot rolling is formed in a thickness direction is uneven, to Carry out the generation that crackle is significantly increased when shearing.It is therefore preferable that including the Mn with 1.2~2.0% content.
Mo：0.005~0.2%
The Mo has solid solution strengthening effect to steel and increases the quenching degree of steel, to improve the intensity of steel.But work as Mo Content be less than 0.005% when, can not obtain addition Mo caused by the effect, when the content of Mo is more than 0.2%, due to Quenching degree is excessively increased, and postpones ferritic phase transformation, but also can reduce precipitating reinforcing effect.In addition, in economic aspect It is unfavorable and be harmful to weldability.Therefore, the content of the Mo is preferably limited to 0.01~0.2%.
Cr：0.005~0.3%
The Cr has solid solution strengthening effect to steel and increases the quenching degree of steel, to improve the intensity of steel.But work as Cr Content be less than 0.005% when, can not obtain addition Cr caused by the effect, when the content of Cr is more than 0.3%, excessively Postpone ferritic phase transformation, cause elongation to be deteriorated to form martensitic phase, and can also reduce precipitating reinforcing effect.This Outside, similar to Mn, the segregation portion in mid-depth portion obtains substantially prosperity, keeps the microstructure of thickness direction uneven, to lead Shearing is caused to be deteriorated.Therefore, the content of the Cr is preferably limited to 0.005~0.3%.
B：0.0003~0.0010%
B is the element for improving quenching degree addition is a small amount of in steel, when adding 0.0003% or more B, in height It is segregated in austenite grain boundary under temperature, so as to make crystal boundary stabilize and improve impact resistance, still, when the content of B is less than When 0.0003%, it is unable to fully obtain the effect.On the other hand, when addition is more than 0.0010% B, in the process of hot rolling Middle delay recrystallization causes to increase the crystal grain extended, and the ferritic phase transformation of delay during cooling, cause fine Tissue becomes uneven.In addition, precipitating reinforcing effect is also reduced, to be difficult to obtain required intensity, and initial stage hot rolled plate Microstructure inhomogeneities can become cold rolling when stress raisers the reason of, therefore, be unfavorable for the present invention.Therefore, institute The content for stating B is preferably limited to 0.0003~0.0010%.
P：0.001~0.05%
Identical as Si, the P has the effect of solution strengthening and promotes ferrite transformation simultaneously.But in order to be manufactured into P When content is less than 0.001%, high manufacturing expense is needed and unfavorable in economic aspect, and be unable to fully obtain intensity, when containing for P When amount is more than 0.05%, brittleness caused by cyrystal boundary segregation is generated, to easy to produce fine crackle when carrying out shearing, And it can substantially deteriorate ductility and impact resistance characteristic.Therefore, the content of the P is preferably limited to 0.001~0.05%.
S：0.001~0.01%
The S is the impurity being present in steel, when the content of S is more than 0.01%, with Mn etc. in conjunction with and formed nonmetallic Thus field trash has and easy tos produce fine crackle in the cutting processing of steel and stretch flangeability and impact resistance is greatly reduced Property the problem of, also, be less than 0.001% to be manufactured into S contents, need when steelmaking operations to take a substantial amount of time and reduce life Production property.It is therefore preferable that the content of S is limited to 0.001~0.01%.
Al：0.01~0.1%
The Al is primarily to deoxidation and the ingredient that adds.When the content of Al is less than 0.01%, the effect of Al is added It is insufficient.On the other hand, when the content of Al is more than 0.1%, Al is combined to form AlN with nitrogen, to the plate when carrying out continuously casting Chink is easy tod produce on base, and easy tos produce the defect caused by the formation of field trash in the portion the edge of hot rolled plate (Edge). Further, since carrying out the surface defect of generation when cold rolling after hot rolling, the problem of surface quality reduces may be will produce.Therefore, excellent The content of Al is limited to 0.01~0.1% by choosing.
N：0.001~0.01%
Together with C, the N is representative solution strengthening element, and N and Ti, Al etc. form coarse precipitation together Object.The solid solution strengthening effect of usual N is better than carbon, but with the increase of the N content in steel, has and asking for toughness is greatly reduced Topic.In addition, in order to which the content for being manufactured into N is less than 0.001%, need when steelmaking operations to take a substantial amount of time, to reduce Productivity.Therefore, in the present invention, the content of N is preferably limited to 0.001~0.01%.
Ti：0.005~0.13%
Together with Nb, V, the Ti is representative precipitation strength element, and Ti by the strong affinity with N in steel It is middle to form coarse TiN.TiN has the effect of inhibiting grain growth in the heating process for hot rolling.In addition, being reacted with nitrogen Remaining Ti is solid-solution in steel and is combined to form TiC precipitates with carbon afterwards, therefore Ti is the active ingredient for the intensity for improving steel.Cause This can not obtain the effect when the content of Ti is less than 0.05%, thick due to generating when the content of Ti is more than 0.13% Big TiN and there is the problem of making shearing be deteriorated when carrying out shearing.Therefore, in the present invention, preferably by Ti's Content is limited to 0.005~0.13%.
Nb：0.005~0.08%
Together with Ti, V, the Nb is representative precipitation strength element, postpones to tie again since Nb is precipitated in hot rolling The effect of crystal grain miniaturization caused by crystalline substance, Nb effectively improve the intensity and impact flexibility of steel.But when the content of Nb is less than It when 0.005%, is unable to fully obtain the effect, when the content of Nb is more than 0.08%, excessive deferral is tied again when due to hot rolling Crystalline substance results in the crystal grain of elongation and coarse miscible precipitate, therefore has the problem of making shearing be deteriorated.Therefore, originally In invention, the content of Nb is preferably limited to 0.005~0.08%.
V：0.005~0.2%
Together with Nb, Ti, the V is representative precipitation strength element, and Ti forms precipitate after being wound, to Effectively improve the intensity of steel.Therefore, it when the content of V is less than 0.005%, is unable to fully obtain the effect, when the content of V is super When 0.2%, forms coarse miscible precipitate and shearing is made to be deteriorated, and is also unfavorable in economic aspect.Therefore, originally In invention, the content of V is preferably limited to 0.005~0.2%.
The surplus ingredient of the present invention is iron (Fe).However, in common manufacturing process, it can not from raw material or ambient enviroment It is mixed into unexpected impurity with avoiding, therefore, it is impossible to be excluded.For the technical staff of common manufacturing process, These impurity be it is well known, therefore, its all the elements not specifically mentioned in the present specification.
In the present invention, the composition of alloy forms uniform when meeting following relational expressions (1) and relational expression (2), after hot rolling Steel microstructure, to which the generation of crackle can be inhibited when carrying out shearing after cold rolling.
Relational expression (1)：2.0≤[Mn]+2.5[Mo]+1.5[Cr]+300[B]≤2.5
Relational expression (2)：0.2≤([Nb]/93+[Ti]/48+[V]/51)/([C]/12+[N]/14)≤0.5
(wherein, the weight % of each element symbolic indication alloying element in the relational expression (1) and relational expression (2)).
Relational expression (1) is related to the quenching degree of steel and segregation, is solid solution strengthening effect and the microstructure for considering steel Inhomogeneities.
When relational expression (1) is less than 2.0, the solid solution strengthening effect of steel is insufficient, and sufficient height can not be obtained to have The problem of intensity.On the other hand, when relational expression (1) is more than 2.5, the microstructure of the thickness direction of steel forms uneven, And postpone ferritic phase transformation, to have the problem of precipitating reinforcing effect for reducing steel.
It is therefore preferable that being 2.0~2.5 by relational expression (1) control.
Relational expression (2) limits and the relevant ingredient of the formation of the precipitate of steel, formation and the composition of precipitate Ti, Nb, V and C, the content of N are related, and therefore, relational expression (2) is in order to which the additive amount of Ti, Nb, V alloy element to be set as according with Close the content of C, N.
When relational expression (2) is less than 0.2, precipitating reinforcing effect significantly reduces, to obtain required intensity and hard Yield strength is significantly increased due to forming a large amount of nano-precipitation when relational expression (2) is more than 0.5 in angle value, so as to cause Cold-rolling property is deteriorated, and the precipitate formed on plate thickness direction is uneven, tool when to carry out shearing after cold rolling There is leading to the problem of for crackle to become serious.
It is therefore preferable that being 0.2~0.5 by relational expression (2) control.
Meet the composition of alloy by control, the excellent high strength cold rolled steel plate of shearing can be obtained, it is described Steel plate can not only ensure high intensity and high rigidity, and can inhibit to split caused by crackle caused by shearing and frictional heat Line.
The cold-rolled steel sheet of the present invention is that the hot rolled plate with the microstructure of ferrite and fine pearlite is carried out cold rolling And obtain, therefore, there is the microstructure (microstructure of fully hard (Full Hard)) to rolling direction gross distortion.At this point, Although each phase that can not be in the specific microstructure by the steel plate of cold rolling, the iron of the steel plate by hot rolling before cold rolling The Line Integral rate of ferritic phase is 90% or more, and fine pearlite is mutually less than 5%, in addition to this it is possible to inevitably Including bainite phase.
The high strength cold rolled steel plate that the shearing of the present invention is excellent includes in carbide, nitride and carbonitride More than one.For example, can include TiN, TiC, NbC, NbN, (Ti, Nb) (C, N), (Ti, Mo, Nb) (C, N) and (Fe, Mn)3C, one or more of (Fe, Mn, Mo) C.
At this point, the mean size of the carbide, nitride and carbonitride is preferably 10~50nm.
When the mean size of carbide, nitride and carbonitride is less than 10nm, on the yield strength of hot rolled plate is excessive Rise, in the processing hardening deviation for easy tod produce when cold rolling locality, and the shearing for carrying out cold-reduced sheet with Crackle is easy tod produce when heat treatment.
But when the mean size of carbide, nitride and carbonitride is more than 50nm, have desired by being difficult to obtain Tensile strength and hardness number the problem of.
In addition, the tensile strength of the cold-rolled steel sheet can be 1200MPa or more, hardness number (micro Vickers, Micro- Vickers) it can be 340Hv or more.By meeting the tensile strength and hardness number, so as to be preferably applied to automobile Friction plate purposes of automatic transmission etc..
In addition, the length of maximum crackle is preferably in generated crackle when the cold-rolled steel sheet is carried out shearing 1mm or less.
The length of the maximum crackle is the circular die using a diameter of 10mm, and with 6% gap (Clearance) Condition punching press, after being then heat-treated one hour at 200 DEG C, measure the result of the length of maximum crackle generated on section.
This is because when the length of maximum crackle is more than 1mm, there is following problem：The yield of increase crackle, and It carries out crackle when shearing to be easy to propagate, when frictional heat leads to temperature rise, crackle is easier to propagate.
In the following, to another aspect of the present invention manufacture the excellent high strength cold rolled steel plate of shearing method into Row is described in detail.
The method of the excellent high strength cold rolled steel plate of manufacture shearing of another aspect of the present invention includes following Step：The steel billet for meeting the composition of alloy is heated with 1200~1350 DEG C；At a temperature of 850~1150 DEG C of ranges, to institute It states the steel billet by heating and carries out hot rolling；The hot rolling postcooling to 550~750 DEG C of ranges temperature and wound；And Pickling is carried out after the winding, and cold rolling is carried out with 60~70% cold rolling reduction ratio.
Heating stepses
The steel billet for meeting the composition of alloy is heated with 1200~1350 DEG C.
When heating temperature is less than 1200 DEG C, precipitate will not be fully dissolved again, to subtract in process after hot rolling The formation of few precipitate, and coarse TiN can be remained.On the other hand, when heating temperature is more than 1350 DEG C, austenite grain Abnormal grain growth (Abnormal Grain Growth) cause reduce intensity, it is therefore preferable that the relation reheating temperature is limited It is made as 1200~1350 DEG C.
At this point, the steel billet can be produced in being directly connected in the process of continuously casting process and hot-rolled process.
In order to which the precipitate of TiN, TiC, NbC, NbN, (Ti, Nb) (C, N), (Ti, Mo, Nb) (C, N) are dissolved again, by steel It is critically important that the temperature of base, which is set as 1200~1350 DEG C, it is thus possible to be enough preferably applied to directly link as described above in In continuously casting process and the process of hot-rolled process.
Hot-rolled step
At a temperature of 850~1150 DEG C of ranges, hot rolling is carried out to the steel billet by heating.
When starting hot rolling at a temperature of higher than 1150 DEG C, the temperature of hot rolled steel plate is got higher, to which grain size can become It is coarse, and the surface quality of hot rolled steel plate can be deteriorated.In addition, when terminating hot rolling at a temperature of less than 850 DEG C, recrystallization Excessive deferral leads to the prosperity of the crystal grain of elongation and obtains high yield ratio, to which cold-rolling property can be deteriorated, and shearing It can be deteriorated.
Cooling and winding step
The hot rolling postcooling to 550~750 DEG C of ranges temperature and wound.
When being cooled to 550 DEG C or less and being wound, bainite phase and martensitic phase are formed in steel, to the material of steel It can be deteriorated, when being cooled to 750 DEG C or more and being wound, form coarse ferrite crystal grain, and be easy to be formed coarse Carbide and nitride can be deteriorated to the material of steel.
At this point it is possible to be cooled down with 10~70 DEG C/sec of average cooling rate.
When being cooled down, when average cooling rate is less than 10 DEG C/sec, coarse ferrite crystal grain is formed, to fine Tissue can become uneven, when average cooling rate is more than 70 DEG C/sec, be easy to form bainite phase, and the thickness side of plate To microstructure can also become uneven, to which the shearing of steel can be deteriorated.
Cold rolling step
Pickling is carried out after the winding, and cold rolling is carried out with 60~70% cold rolling reduction ratio.
When cold rolling reduction ratio is less than 60%, sufficient drawing hardening effect can not be obtained, to be difficult to ensure the strong of steel Degree and hardness.On the other hand, when cold rolling reduction ratio is more than 70%, the quality in portion edge (Edge) of steel can be deteriorated, and cut Cutting processability can be deteriorated.
The cold-rolled steel sheet manufactured by the manufacturing method can not only ensure high intensity and high rigidity, and can inhibit Crackle caused by crackle caused by shearing and frictional heat.
In addition, including one in carbide, nitride and carbonitride by the cold-rolled steel sheet that the manufacturing method manufactures Kind or more, the mean size of carbide, nitride and carbonitride can be 10~50nm.In addition, tensile strength can be 1200MPa or more, hardness number can be 340Hv or more, and when shearing in generated crackle maximum crackle length Can be 1mm or less.
Specific implementation mode
In the following, carrying out more specific description to the present invention by embodiment.It is to be noted, however, that implementation below Example is of the invention and illustration just for the sake of being described in more detail, and is not intended to limit the interest field of the present invention.This be because Interest field for the present invention is determined by content described in claim and the content thus rationally derived.
Have at the steel billet being grouped as shown in following table 1 with 1250 DEG C of heating, and made using shown in following table 2 Make condition manufacture cold-rolled steel sheet.At this point, the cooling velocity after hot rolling is set as 20~30 DEG C/sec.
In addition, the value of the relational expression (1) and relational expression (2) for comparative example and example calculating is shown in following table 2, Finish rolling final temperature when FDT and CT indicates hot rolling respectively and winding temperature.
In addition, showing the result of the engineering properties and observation microstructure of example and comparative example in following Table 3.It is following In table 3, TS, Hv, maximum crack length indicate the tensile strength of cold-reduced sheet, micro Vickers (Micro-Vickers) hardness respectively Value, maximum crack length are the circular dies using a diameter of 10mm, and are carried out with the condition of 6% gap (Clearance) Punching press after being then heat-treated one hour at 200 DEG C, measures the result of the length of the maximum crackle generated on section.Crackle Length is measured according to the observation result of the light microscope of 100 multiplying powers.
For the size of the carbide, nitride and the carbonitride that are formed in steel, the hot rolled plate before cold rolling is analyzed.Steel The mean size of middle formation for the carbide of 10~50nm, nitride and carbonitride size and divide rate will not be by cold rolling It changes, and the microstructure of gross distortion has the problem of being difficult to its size of accurate observation and point rate after cold rolling, therefore, Hot rolled plate is analyzed.Carbide, nitride and carbon nitrogen is determined according to the result measured using transmission electron microscope The mean size of compound.Mean size is that 50,000 multiplying powers are utilized in the measurement of the carbide and nitride of 100nm or more Measurement result, mean size are that 100nm precipitates below are the measurement results that 100,000 multiplying power is utilized.Using will be opposite The test piece obtained on the basis of 0 ° of direction of the rolling direction of rolled plate and according to JIS5 standards has carried out tension test.
[table 1]
[table 2]
[table 3]
Comparative example 1 and comparative example 2 do not meet relational expression (1) and relational expression (2), and the content of the C of comparative example 1 does not have yet Meet the scope of the present invention.Two comparative examples do not obtain sufficient solid solution strengthening effect, and due to relatively low C content And relatively excessive Ti, Nb, V, it has been more than the upper limit of relational expression (2).Therefore, carbide, nitride and the analysis formed in steel The size for going out object is fine, but does not substantially ensure the intensity of steel.In addition, with more than the range controlled in the present invention to comparing Example 2 assign cold rolling reduction ratio as a result, slightly serious crackle is produced after punch process on shearing face, so as to Confirm the quality variation in shearing face.
Comparative example 3 and comparative example 5 are the case where being unsatisfactory for relational expression (1), and comparative example 3 has been more than the invention of relational expression (1) Range, to increase steel central part segregation generation, lead to the quality variation in shearing portion.In addition, comparative example 5 Content of Mn, Cr, B etc. is few, and to which the generation of segregation is few, thus the quality in shearing face is very good, but there is no To sufficient solid solution strengthening effect, therefore desired intensity and hardness number are not obtained.
Comparative example 4 and comparative example 6 are the case where being unsatisfactory for relational expression (2), and comparative example 4 remains remaining C, so as to form Coarse precipitate and carbide, and due to precipitating reinforcing effect deficiency, fail to obtain desired intensity and hardness number.
Comparative example 6 has been more than the invention scope of relational expression (2), so as to form a large amount of nano-precipitation, thus, it is possible to High intensity is obtained, but serious crackle is produced in shearing portion.
It is 1350MPa or more that comparative example 7, comparative example 8, comparative example 9, comparative example 10, which are with the tensile strength after cold rolling, hard Angle value is the steel that 355Hv or more is target manufacture, and comparative example 7 does not meet relational expression (1), but true by high cold rolling reduction ratio Desired physical property is protected.But because of high cold rolling reduction ratio, slightly serious crackle is produced in shearing portion.
Comparative example 8 and comparative example 9 are satisfied by relational expression (1) and relational expression (2), but cold rolling reduction ratio is not suitable for, to Fail the poor quality for obtaining desired physical property or shearing portion.Comparative example 10 be be unsatisfactory for relational expression (1) and The case where relational expression (2), the poor quality in shearing portion.
On the other hand, example is satisfied by the composition range proposed in the present invention and manufacturing condition and relational expression (1), closes It is formula (2), so as to ensure desired material, and is able to confirm that the quality in shearing portion is also excellent.
The relational expression (1) of example and comparative example, the maximum crackle of relational expression (2) and shearing portion are shown in Fig. 1 Length relationship.Hatched example areas in Fig. 1 corresponds to the scope of the present invention.
The embodiments of the present invention have been described in detail above, still, it's not limited to that for interest field of the invention, In the range of not departing from the technological thought of the present invention described in claim, a variety of modifications and changes can be carried out, this It is obvious for having usually intellectual in the art.

Claims (10)

1. the excellent high strength cold rolled steel plate of shearing, in terms of weight %, the cold-rolled steel sheet includes：C：0.05~ 0.10%, Si：0.01~0.5%, Mn：1.2~2.0%, Al：0.01~0.1%, Cr：0.005~0.3%, B：0.0003~ 0.0010%, Mo：0.005~0.2%, P：0.001~0.05%, S：0.001~0.01%, N：0.001~0.01%, Nb： 0.005~0.08%, Ti：0.005~0.13%, V：0.005~0.2%, the Fe of surplus and inevitable impurity,
And meet following relational expressions (1) and relational expression (2),
And including one or more of carbide, nitride and carbonitride,
Relational expression (1)：2.0≤[Mn]+2.5[Mo]+1.5[Cr]+300[B]≤2.5
Relational expression (2)：0.2≤([Nb]/93+[Ti]/48+[V]/51)/([C]/12+[N]/14)≤0.5
Wherein, the weight % of each element symbolic indication alloying element in the relational expression (1) and relational expression (2).
2. the excellent high strength cold rolled steel plate of shearing according to claim 1, which is characterized in that the carbonization The mean size of object, nitride and carbonitride is 10~50nm.
3. the excellent high strength cold rolled steel plate of shearing according to claim 1, which is characterized in that the cold-rolled steel The tensile strength of plate is 1200MPa or more, and hardness number is 340Hv or more.
4. the excellent high strength cold rolled steel plate of shearing according to claim 1, which is characterized in that when shearing The length of maximum crackle is 1mm or less in the crackle of generation.
5. the excellent high strength cold rolled steel plate of shearing according to claim 1, which is characterized in that the institute before cold rolling The area fraction for stating the ferritic phase of the microstructure of cold-rolled steel sheet is 90% or more, and the area fraction of fine pearlite phase is small Include inevitably bainite phase in addition in 5%.
6. the method for manufacturing the excellent high strength cold rolled steel plate of shearing comprising following steps：
Heating steel billet is to 1200~1350 DEG C, and in terms of weight %, the steel billet includes：C：0.05~0.10%, Si：0.01~ 0.5%, Mn：1.2~2.0%, Al：0.01~0.1%, Cr：0.005~0.3%, B：0.0003~0.0010%, Mo： 0.005~0.2%, P：0.001~0.05%, S：0.001~0.01%, N：0.001~0.01%, Nb：0.005~ 0.08%, Ti：0.005~0.13%, V：0.005~0.2%, the Fe of surplus and inevitable impurity, and meet following Relational expression (1) and relational expression (2)；
At a temperature of 850~1150 DEG C of ranges, hot rolling is carried out to the steel billet by heating；
The hot rolling postcooling to 550~750 DEG C of ranges temperature and wound；And
Pickling is carried out after the winding, and cold rolling is carried out with 60~70% cold rolling reduction ratio；
Relational expression (1)：2.0≤[Mn]+2.5[Mo]+1.5[Cr]+300[B]≤2.5
Relational expression (2)：0.2≤([Nb]/93+[Ti]/48+[V]/51)/([C]/12+[N]/14)≤0.5
Wherein, the weight % of each element symbolic indication alloying element in the relational expression (1) and relational expression (2).
7. the method for the manufacture excellent high strength cold rolled steel plate of shearing according to claim 6, which is characterized in that The steel billet is produced by continuously casting process.
8. the method for the manufacture excellent high strength cold rolled steel plate of shearing according to claim 6, which is characterized in that The cooling is carried out with 10~70 DEG C/sec of average cooling rate.
9. the method for the manufacture excellent high strength cold rolled steel plate of shearing according to claim 6, which is characterized in that The cold-rolled steel sheet includes one or more of carbide, nitride and carbonitride, carbide, nitride and carbonitride Mean size is 10~50nm.
10. the method for the manufacture excellent high strength cold rolled steel plate of shearing according to claim 6, feature exist In the tensile strength of the cold-rolled steel sheet is 1200MPa or more, and hardness number is 340Hv or more.
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