CN107735505A - Steel plate and manufacture method - Google Patents

Steel plate and manufacture method Download PDF

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Publication number
CN107735505A
CN107735505A CN201680035011.0A CN201680035011A CN107735505A CN 107735505 A CN107735505 A CN 107735505A CN 201680035011 A CN201680035011 A CN 201680035011A CN 107735505 A CN107735505 A CN 107735505A
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steel plate
carbide
annealing
ferrite
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CN107735505B (en
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匹田和夫
桥本元仙
竹田健悟
高田健
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Nippon Steel Corp
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Nippon Steel Corp
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
    • 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
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/26—Methods of annealing
    • C21D1/32—Soft annealing, e.g. spheroidising
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/84—Controlled slow cooling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0257—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment with diffusion of elements, e.g. decarburising, nitriding
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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
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    • 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
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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
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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
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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    • 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
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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
    • C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
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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
    • C22C38/008—Ferrous alloys, e.g. steel alloys containing tin
    • 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
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    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23G—CLEANING OR DE-GREASING OF METALLIC MATERIAL BY CHEMICAL METHODS OTHER THAN ELECTROLYSIS
    • C23G1/00—Cleaning or pickling metallic material with solutions or molten salts
    • C23G1/02—Cleaning or pickling metallic material with solutions or molten salts with acid solutions
    • C23G1/08—Iron or steel
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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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/74—Methods of treatment in inert gas, controlled atmosphere, vacuum or pulverulent material
    • C21D1/76—Adjusting the composition of the atmosphere
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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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/004—Dispersions; Precipitations
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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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/005—Ferrite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/009—Pearlite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • 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
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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
    • C22C38/44—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

Abstract

A kind of steel plate, it is characterized in that, it is the steel plate for improving formability and wearability, formed with defined composition, the metal structure of steel plate meets the number of the carbide of ferrite grain boundaries relative to the ratio of the number of the carbide in ferrite crystal grain more than 1 and ferrite particle diameter is 5 μm~50 μm, wherein, the Vickers hardness of steel plate is 100HV~170HV.

Description

Steel plate and manufacture method
Technical field
The present invention relates to steel plate and its manufacture method.
Background technology
The automotive parts such as gear, clutch manufacture via manufacturing procedures such as punching, forging, punch process.Itself plus In work process, in order to seek the raising of product property, the reduction of stabilisation, manufacturing cost, it is desirable to improve the carbon as raw material The processability of steel plate.In addition, these parts it requires excellent through hardening due to being used after Q-tempering with high intensity Property.
In order to ensure carbon steel sheet processability and ensure quenching degree, in the past, give a large amount of motions.
Patent Document 1 discloses a kind of high carbon steel sheet of the tenacity excellent after processability, quenching degree, heat treatment, and it is special Sign is, contains C in terms of quality %：0.20~0.45%, Mn：0.40~1.50%, P：Less than 0.03%, S：0.02% with Under, P+S：More than 0.010%, Cr：0.01~0.80%, Ti：0.005~0.050%, B：0.0003~0.0050%, it is remaining Part is made up of Fe and inevitable impurity, further contains Sn：Less than 0.05%, Te：Less than 0.05%, and Sn+Te Total content be more than 0.005%, by the line and staff control or ferrite of ferrite and pearlite and the mixing group of cementite Knit to be formed.
In patent document 2, disclose a kind of manufacture method of high-hardenability high-carbon hot-rolled steel sheet, it is characterised in that to Quality % meters contain C：0.2~0.7%, Si：Less than 2%, Mn：Less than 2%, P：Less than 0.03%, S：Less than 0.03%, sol.Al：Less than 0.08%, N：Less than 0.01% and the steel that is made up of iron and inevitable impurity of remainder, in finish rolling temperature After more than degree (Ar3 transformation temperatures are -20 DEG C) carrying out hot rolling, more than 120 DEG C/sec and end temp is cooled down as 620 in cooling velocity Cooled down below DEG C, then, coiling temperature be less than 600 DEG C batched, control for volume fraction more than 20% After the tissue of bayesian body phase, after pickling, it is that below more than 640 DEG C and Ac1 transformation temperatures are annealed in annealing temperature, is made spherical Change tissue.
Prior art literature
Patent document
Patent document 1：No. 4319940 publications of Japanese Patent No.
Patent document 2：No. 3879459 publications of Japanese Patent No.
The content of the invention
Invent problem to be solved
But the high carbon steel sheet described in patent document 1 also using the high pearlite of hardness in raw material tissue, add Work may not be excellent.There is no the specific tissue morphology for recording excellent in workability in patent document 2.
The present invention in view of the present situation of conventional art, and it is an object of the present invention to provide making formability and wearability improve, particularly be adapted to The steel plate of the parts such as gear, clutch and its manufacture method are obtained in being shaped by heavy wall plate.
Means for solving the problems
It is appreciated that：In order to solve above-mentioned problem, the steel plate for being suitable to the raw material of drive component etc. is obtained, as long as In containing the steel plate for the C required for raising quenching degree, increase ferritic particle diameter, by carbide (predominantly cementite) Spheroidizing is carried out with appropriate particle diameter, reduces pearlitic structrure.This is to be based on the reasons why following.
The hardness of ferritic phase is low, and ductility is high.Therefore, by increasing its grain in the tissue using ferrite as main body Footpath, so as to improve raw material formability.
Carbide is due to by being suitably scattered in metal structure, so as to maintain raw material formability, and assigning Give excellent wearability, rotate tired characteristic, so being to the indispensable tissue of drive component.In addition, in steel plate Carbide be hinder slide firm particle, by making carbide be present in ferrite grain boundaries, so as to prevent from crossing The propagation of the slip of crystal crystal boundary, the formation for suppressing shear band, improve forging, while the formability of steel plate also improves.
But because cementite is hard and crisp tissue, if to be the state of pearlite with ferritic lamellar tissue In the presence of then steel can be hardened and become fragile, so must be with spherical presence.If it is considered that forging, forging when cracking generation, then its Particle diameter need to be appropriate scope.
However, for realizing that the manufacture method of above-mentioned tissue is not disclosed so far.Then, invention of the invention Persons are to for realizing that the manufacture method of above-mentioned tissue has made intensive studies.
The result is that, it was found that：It is small in order to which the metal structure of the steel plate after batching after hot rolling is formed in into piece interlamellar spacing Fine pearlite or tiny ferrite in be dispersed with the bainite structure that cementite forms, with relatively low temperature (400~ 550 DEG C) batched.By being batched with relatively low temperature, the cementite being scattered in ferrite also becomes easily spherical Change.Then, as the 1st section of annealing, cementite is carried out by the annealing at a temperature of immediately lower than Ac1 points partly spherical Change.Then, as the 2nd section of annealing, the temperature (two-phase region of so-called ferrite and austenite between Ac1 points and Ac3 points is passed through Domain) under annealing, make ferrite crystal grain a part residual, and make a part occur austenite phase transformation.Thereafter, progress is passed through Slow cool down and grown the ferrite crystal grain of residual, and make as core austenite that ferrite transformation occur, can Cementite is separated out in crystal boundary while big ferritic phase is obtained, realize above-mentioned tissue.
I.e., it was found that：For meeting the manufacture method of steel plate of quenching degree and formability simultaneously, even if to hot-rolled condition Or annealing conditions etc. are made single effort and are still difficult to, by being reached with a so-called coherent process such as hot rolling and annealing operation Optimize, can realize.
The present invention is completed based on above-mentioned opinion, and its purport is as follows.
(1) a kind of steel plate, it is characterised in that the steel plate contains C in terms of quality %：0.10~0.40%, Si：0.01~ 0.30%th, Mn：1.00~2.00%, P：Less than 0.020%, S：Less than 0.010%, Al：0.001~0.10%, N：0.010% Below, O：Less than 0.020%, Cr：Less than 0.50%, Mo：Less than 0.10%, Nb：Less than 0.10%, V：Less than 0.10%, Cu： Less than 0.10%, W：Less than 0.10%, Ta：Less than 0.10%, Ni：Less than 0.10%, Sn：Less than 0.050%, Sb：0.050% Below, As：Less than 0.050%, Mg：Less than 0.050%, Ca：Less than 0.050%, Y：Less than 0.050%, Zr：0.050% with Under, La：Less than 0.050% and Ce：Less than 0.050%, remainder is Fe and inevitable impurity, wherein, above-mentioned steel The metal structure of plate meets：The number of the carbide of ferrite grain boundaries relative to the number of the carbide in ferrite crystal grain ratio Rate is 5 μm~50 μm more than 1, ferrite particle diameter and the area occupation ratio of pearlite is less than 6%, the Vickers hardness of above-mentioned steel plate For 100HV~170HV.
(2) according to the steel plate of above-mentioned (1), it is characterised in that contain Ti instead of an above-mentioned Fe part：Less than 0.10% And B：1 kind in less than 0.010% or 2 kinds.
(3) a kind of manufacture method of steel plate, it is characterised in that it is the manufacturer for the steel plate for manufacturing above-mentioned (1) or (2) Method, wherein, the steel billet of the composition of above-mentioned (1) or (2) composition is implemented to complete finish rolling in 750 DEG C~850 DEG C of temperature province Hot rolling and hot rolled steel plate is made, above-mentioned hot rolled steel plate is batched at 400 DEG C~550 DEG C, to the hot rolled steel plate batched Implement pickling, the hot rolled steel plate to pickling is implemented to keep in 650 DEG C~720 DEG C of temperature province 3 hours~60 hours 1st section of annealing, then, hot rolled steel plate is implemented to keep the 2nd of 3 hours~50 hours the in 725 DEG C~790 DEG C of temperature province Section annealing, 650 DEG C are cooled to by the hot rolled steel plate after annealing with 1 DEG C/h~30 DEG C/h of cooling velocity.
Invention effect
In accordance with the invention it is possible to formability and excellent in abrasion resistance are provided, are especially suitable for shaping to obtain by heavy wall plate To the steel plate and its manufacture method of the parts such as gear, clutch.
Embodiment
Hereinafter, the present invention is described in detail.First, the restriction reason formed to the composition of steel plate of the present invention is said It is bright.Hereinafter, " % " of relevant composition refers to " quality % ".
[C：0.10~0.40%]
C is that carbide, the reinforcing for steel and the effective element of the miniaturization of ferrite crystal grain are formed in steel.In order to press down The generation of pears surface in refrigeration processing, the surface aesthetic of cold working part is ensured, it is necessary to suppress the coarsening of ferrite particle diameter, But during less than 0.10%, the volume fraction of carbide is insufficient, can not suppress the coarsening of the carbide in box annealing, therefore C is set It is set to more than 0.10%.Preferably more than 0.12.
On the other hand, if it exceeds 0.40%, then the volume fraction increase of carbide in instantaneity can be big during loaded load Amount generation is as the crackle for the starting point destroyed, and impact resistance characteristic reduces, therefore C is set as less than 0.40%.Preferably 0.38% Below.
[Si：0.01~0.30%]
Si is the element for working as deoxidier and being had an impact to the form of carbide.In order to obtain deoxidation effect Fruit, Si are set as more than 0.01%.Preferably more than 0.05%.
On the other hand, if it exceeds 0.30%, then ferritic ductility reduction, becomes easily to cause and splits in cold working Line, cold-workability reduces, therefore Si is set as less than 0.30%.Preferably less than 0.28%.
[Mn：1.00~2.00%]
Mn is the element for improving quenching degree, contributing to intensity to improve.During less than 1.00%, after the intensity and quenching after quenching Residual Carbides ensure to become difficult, therefore Mn is set as more than 1.00%.Preferably more than 1.09%.
On the other hand, if it exceeds 2.00%, then Mn segregations become the banding of extreme, and processability significantly reduces, therefore Mn It is set as less than 2.00%.Preferably less than 1.91%.
[Al：0.001~0.10%]
Al is to work as the deoxidier of steel, make the element of ferrite stabilization., can not be abundant during less than 0.001% Ground obtains additive effect, therefore Al is set as more than 0.001%.Preferably more than 0.004%.
On the other hand, if it exceeds 0.10%, then a large amount of generation field trashes, cold-workability reduces, therefore Al is set as Less than 0.10%.Preferably less than 0.08%.
Following element is impurity, it is necessary to control a certain amount of following.
[P：0.0001~0.020%]
P is the element formed in ferrite grain boundaries segregation, suppression grain boundary carbide.Although more few more preferred, but if In refining procedure, P is decreased below 0.0001%, then refining cost can be substantially increased, therefore P be set as 0.0001% with On.Preferably more than 0.0013%.
On the other hand, if it exceeds 0.020%, then the individual percentage of grain boundary carbide reduces, and cold-workability reduces, therefore P is set as less than 0.020%.Preferably less than 0.018%.
[S：0.0001~0.010%]
S is the impurity element to form the non-metallic inclusions such as MnS.Split because non-metallic inclusion can turn into cold working The starting point that line occurs, therefore S is more few more preferred, but if S is decreased below into 0.0001%, then refining cost can significantly on Rise, therefore S is set as more than 0.0001%.Preferably more than 0.0012%.
On the other hand, if it exceeds 0.010%, then cold-workability reduces, therefore S is set as less than 0.010%.Preferably Less than 0.007%.
[N：0.0001~0.010%]
N is to cause the brittle element of ferrite by largely containing, more few more preferred.N content can be 0, but If decreasing below 0.0001%, refining cost can be substantially increased, thus substantial lower limit be 0.0001~ 0.0006%.On the other hand, if it exceeds 0.010%, then ferrite is brittle, and cold-workability reduces, therefore N is set as Less than 0.010%.Preferably less than 0.007%.
[O：0.0001~0.020%]
O is that the element of thick oxide is formed in steel by largely containing, preferably less.O content can Think 0, but if decreasing below 0.0001%, then refining cost can be substantially increased, therefore substantial lower limit is 0.0001 ~0.0011%.On the other hand, if it exceeds 0.020%, then thick oxide is generated in steel, turns into cold working and split The starting point of line, therefore O is set as less than 0.020%.Preferably less than 0.017%.
[Sn：0.001~0.050%]
Sn is from steel raw material (waste material) mixed element.Due in cyrystal boundary segregation, causing the individual percentage of grain boundary carbide Reduction, it is therefore more few more preferred.Sn content can be 0, but if decreasing below 0.001%, then refining cost is significantly Increase, therefore substantial lower limit is more than 0.001~0.002%.On the other hand, if it exceeds 0.050%, then ferrite is crisp Change, cold-workability reduces, therefore Sn is set as less than 0.050%.Preferably less than 0.040%.
[Sb：0.001~0.050%]
Sb is from steel raw material (waste material) mixed element in the same manner as Sn.Due in cyrystal boundary segregation, causing grain boundary carbide Individual percentage reduction, it is therefore more few more preferred.Sb content can be 0, but if decreasing below 0.001%, then smart It is smelt and is originally significantly increased, therefore substantial lower limit is more than 0.001~0.002%.On the other hand, if it exceeds 0.050%, Then ferrite is brittle, and cold-workability reduces, therefore Sb is set as less than 0.050%.Preferably less than 0.040%.
[As：0.001~0.050%]
As is from steel raw material (waste material) mixed element in the same manner as Sn, Sb.Due in cyrystal boundary segregation, causing crystal boundary to be carbonized The reduction of the individual percentage of thing, thus it is more few more preferred.As content can be 0, but if decreasing below 0.001%, then Refining cost is significantly increased, therefore substantial lower limit is more than 0.001~0.002%.On the other hand, if it exceeds 0.050%, then the individual percentage reduction of grain boundary carbide, cold-workability reduces, therefore As is set as less than 0.050%.It is preferred that For less than 0.040%.
Steel plate of the present invention using above-mentioned element as basis, and then, in order to improve the forging of steel plate, can also contain Following element.Due to following element be not be in order to obtain the effect of the present invention necessary to, therefore content can also be 0。
[Cr：Less than 0.50%]
Cr is the element for improving quenching degree, contributing to intensity to improve, and is to be concentrated on carbide, even in austenite phase In can also form the element of stable carbide.In order to obtain additive effect, Cr is preferably set to more than 0.001%.More preferably For more than 0.007%.On the other hand, if it exceeds 0.50%, then carbide can stabilize, in quenching the dissolving of carbide prolong Late, it is possible to required quenching intensity can not be reached, therefore Cr is set as less than 0.50%.Preferably less than 0.45%.
[Mo：Less than 0.10%]
Mo is to the effective element of morphology Control of carbide in the same manner as Mn.In order to obtain additive effect, Mo is preferably set It is set to more than 0.001%.More preferably more than 0.010%.On the other hand, if it exceeds 0.10%, then respectively to different in the face of r values Property deteriorate, cold-workability reduces, therefore Mo is set as less than 0.10%.Preferably less than 0.08%.
[Nb：Less than 0.10%]
Nb is the effective element of morphology Control to carbide, and makes tissue miniaturization and contribute to toughness to improve Element.In order to obtain additive effect, Nb is preferably set to more than 0.001%.More preferably more than 0.002%.On the other hand, such as Fruit then largely separates out fine Nb carbide more than 0.10%, and intensity excessively rises, in addition, the individual percentage of grain boundary carbide Reduce, cold-workability reduces, therefore Nb is set as less than 0.10%.Preferably less than 0.08%.
[V：Less than 0.10%]
V is also to the effective element of morphology Control of carbide in the same manner as Nb, and is to make tissue miniaturization and help In the element that toughness improves.In order to obtain additive effect, V is preferably set to more than 0.001%.More preferably more than 0.004%. On the other hand, if it exceeds 0.10%, then fine V carbide is largely separated out, intensity excessively rises, in addition, grain boundary carbide Individual percentage reduce, cold-workability reduces, therefore V is set as less than 0.10%.Preferably less than 0.08%.
[Cu：Less than 0.10%]
Cu be ferritic crystal cyrystal boundary segregation and form fine precipitate and contribute to intensity improve member Element.In order to obtain additive effect, Cu is preferably set to more than 0.001%.More preferably more than 0.005%.On the other hand, if More than 0.10%, then red brittleness is produced, the productivity ratio in hot rolling reduces, therefore Cu is set as less than 0.10%.Preferably Less than 0.08%.
[W：Less than 0.10%]
W is also to the effective element of morphology Control of carbide in the same manner as Nb, V.In order to obtain additive effect, W is preferred It is set as more than 0.001%.More preferably more than 0.003%.On the other hand, if it exceeds 0.10%, then largely separate out fine W carbide, intensity excessively rises, in addition, the individual percentage of grain boundary carbide reduces, cold-workability reduces, therefore W is set as Less than 0.10%.Preferably less than 0.08%.
[Ta：Less than 0.10%]
Ta is also to the effective element of morphology Control of carbide in the same manner as Nb, V, W.In order to obtain additive effect, Ta It is preferably set to more than 0.001%.More preferably more than 0.005%.On the other hand, it is if it exceeds 0.10%, then a large amount of to separate out Fine W carbide, intensity excessively rise, in addition, the individual percentage of grain boundary carbide reduces, cold-workability reduces, therefore Ta It is set as less than 0.10%.Preferably less than 0.08%.
[Ni：Less than 0.10%]
Ni is to improve effective element to the toughness of part.In order to obtain additive effect, Ni be preferably set to 0.001% with On.More preferably more than 0.004%.On the other hand, if it exceeds 0.10%, then the individual percentage of grain boundary carbide reduces, cold Processability reduces, therefore Ni is set as less than 0.10%.Preferably less than 0.08%.
[Mg：Less than 0.050%]
Mg is the element that the form of sulfide can be controlled by micro addition.In order to obtain additive effect, Mg is excellent Choosing is set as more than 0.0001%.More preferably more than 0.0008%.On the other hand, if it exceeds 0.050%, then ferrite is crisp Change, cold-workability reduces, therefore Mg is set as less than 0.050%.Preferably less than 0.040%.
[Ca：Less than 0.050%]
Ca is the element with the Mg forms that can control sulfide likewise by micro addition.In order to be added Effect, Ca are preferably set to more than 0.001%.More preferably more than 0.003%.On the other hand, if it exceeds 0.050%, then Thick Ca oxides are generated, the starting point occurred in cold working as crackle, therefore Ca is set as less than 0.050%.It is preferred that For less than 0.040%.
[Y：Less than 0.050%]
Y is the element with Mg, Ca form that can control sulfide likewise by micro addition.In order to be added Add effect, Y is preferably set to more than 0.001%.More preferably more than 0.003%.On the other hand, if it exceeds 0.050%, then Thick Y oxides are generated, the starting point occurred in cold working as crackle, therefore Y is set as less than 0.050%.Preferably Less than 0.035%.
[Zr：Less than 0.050%]
Zr is the element with Mg, Ca, Y form that can control sulfide likewise by micro addition.In order to obtain Additive effect is obtained, Zr is preferably set to more than 0.001%.More preferably more than 0.004%.On the other hand, if it exceeds 0.050%, then thick Zr oxides are generated, the starting point occurred in cold working as crackle, therefore Zr is set as 0.050% Below.Preferably less than 0.045%.
[La：Less than 0.050%]
La be by micro addition and the effective element of morphology Control to sulfide, but be also led in cyrystal boundary segregation The element for causing the individual percentage of grain boundary carbide to reduce.In order to obtain additive effect, La is preferably set to more than 0.001%.More Preferably more than 0.004%.On the other hand, if it exceeds 0.050%, then the individual percentage of grain boundary carbide reduces, cold working Property reduce, therefore La is set as less than 0.050%.Preferably less than 0.045%.
[Ce：Less than 0.050%]
Ce is the element with the La forms that can control sulfide likewise by micro addition, but is also in crystal boundary The element for being segregated and causing the individual percentage of grain boundary carbide to reduce.In order to obtain additive effect, Ce is preferably set to 0.001% More than.More preferably more than 0.004%.On the other hand, if it exceeds 0.050%, then the individual percentage of grain boundary carbide reduces, Cold-workability reduces, therefore Ce is set as less than 0.050%.Preferably less than 0.046%.
The remainder of the composition composition of steel plate of the present invention is Fe and inevitable impurity.
, can also be containing a kind in Ti and B or 2 kinds in addition, instead of an above-mentioned Fe part.
[Ti：Less than 0.10%]
Ti is the effective element of morphology Control to carbide, and is also to make tissue miniaturization and contribute to toughness to improve Element.In order to obtain additive effect, Ti is preferably set to more than 0.001%.More preferably more than 0.005%.On the other hand, If it exceeds 0.10%, then thick Ti oxides are generated, in cold working as the starting point of crackle, therefore Ti is set as Less than 0.10%.Preferably less than 0.08%.
[B：0.0001~0.010%]
B be improve part heat treatment when quenching degree and make microstructure homogenization, contribute to toughness improve element.In order to obtain Additive effect is obtained, B is preferably set to more than 0.0001%.More preferably more than 0.0006%.On the other hand, if it exceeds 0.010%, then thick B oxides are generated, in cold working as the starting point of crackle, therefore B is set as less than 0.010%. Preferably less than 0.009%.
Next, the tissue of the steel plate of the present invention is illustrated.
The tissue of steel plate of the present invention is the tissue being substantially made up of ferrite and carbide.Carbide is except being iron and carbon Compound be cementite (Fe3C beyond), or the Fe atoms in cementite is replaced with alloying elements such as Mn, Cr and obtained Compound, alloy carbide (M23C6、M6C, [the M such as MC：Fe and other metallic elements as alloy addition]).
When being defined shape by steel formability, shear band is formed in the macrostructure of steel plate, near shear band Concentrate to produce and slide deformation.Hyperplasia of the deformation along with dislocation is slided, the high region of dislocation density is formed near shear band. Along with the increase of the dependent variable assigned to steel plate, slide deformation and be promoted, dislocation density increase.
In cold forging, implement equivalent strain and force work more than 1.Therefore, for conventional steel plate, can not prevent adjoint Dislocation density increase and space and/or crackle occurs, for conventional steel plate, the raising of forging is difficult.For The solution of the problem, the formation of shear band when suppressing to shape is effective.
From the viewpoint of microscopic structure, the formation of shear band can be understood as the caused slip in some crystal grain and get over Cross crystal crystal boundary and continuously propagate to the phenomenon of adjacent crystal grain.Thus, in order to suppress the formation of shear band, it is necessary to prevent from getting over Cross the propagation of the slip of crystal crystal boundary.
Carbide in steel plate is to hinder the firm particle slided, by making carbide be present in ferrite grain boundaries, from And can prevent from crossing the propagation of the slip of crystal crystal boundary and suppressing the formation of shear band, make it possible that forging improves.Together When, the formability of steel plate also improves.
The formability of steel plate is heavily dependent on accumulation (accumulation of dislocation) of the strain into crystal grain, if in crystal Grain boundaries prevent propagation of the strain to neighboring die, then the dependent variable increase in crystal grain.As a result, work hardening rate increases, Formability improves.
If based on theoretical and principle, then it is assumed that cold-workability consumingly by ferrite grain boundaries carbide coverage rate Influence, it is therefore desirable to the high-precision measuring coverage rate.
In order to determine the coverage rate of the carbide in ferrite grain boundaries in three dimensions, in scanning electron microscope It is required to be repeated using the serial section SEM observations or three-dimensional EBSP observations of FIB sample cutting and observation, and this is needed Huge minute is wanted, and the accumulation of technical know-how becomes indispensable.The inventors of the present invention have understood fully this thing, obtain The conclusion gone out is：General analysis method is not suitable for.
Therefore, simple and high precision evaluation index is explored, as a result, present inventors have discovered that：If Using the number of the carbide of ferrite grain boundaries relative to the ratio of the number of the carbide in ferrite crystal grain as index, then can Cold-workability is enough evaluated, if the number of the carbide of ferrite grain boundaries is relative to the number of the carbide in ferrite crystal grain Ratio is more than 1, then cold-workability significantly improves.
Further, since the buckling of steel plate caused by cold working, fold into, convolution be by with formation of shear bands should Become caused by localization, therefore by making carbide be present in ferrite grain boundaries, so as to relax the formation of shear band and The localization of strain, effectively suppress buckle, fold into, the generation of convolution.
If the spherical rate of the carbide on crystal crystal boundary is less than 80%, strains and partly concentrate on bar-shaped or tabular Carbide, become easily to produce space and/or crackle, therefore the spherical rate of the carbide on crystal crystal boundary is preferably 80% More than, more preferably more than 90%.
If the average grain diameter of carbide is less than 0.1 μm, the hardness of steel plate dramatically increases, and processability reduces, therefore carbon The average grain diameter of compound is preferably more than 0.1 μm.More preferably more than 0.17 μm.On the other hand, if the average grain of carbide Footpath is more than 2.0 μm, then the carbide thick in cold working turns into starting point and produce cracking, and cold-workability reduces, therefore is carbonized The average grain diameter of thing is preferably less than 2.0 μm.More preferably less than 1.95 μm.
The observation of carbide is carried out with scanning electron microscope.Before observation, the sample of structure observation is passed through Wet lapping using sand paper and the diamond abrasive grain with 1 μm of average particle size are ground, by sightingpiston finishing Work is etched into after minute surface using 3% nitric acid-ethanol solution to tissue.The multiplying power of observation is that selection can in 3000 times Distinguish the multiplying power of ferrite and carbide.With the multiplying power of selection, 40 μm of 30 μ m at 8 1/4 layer of thicknesss of slab is randomly shot Visual field.
For resulting organization chart picture, the image point for representative with three paddy business Co. Ltd. systems (Win ROOF) is used Analysis software determines the area of each carbide contained in the region in detail.Equivalent diameter is obtained by the area of each carbide (=2 × √ (area/3.14)), are averaged value as carbide particle diameter.In addition, the spherical rate of carbide is by carbide It is approximately homalographic and the equal ellipse of the moment of inertia, calculates maximum length and the ratio of the maximum length of its right angle orientation less than 3 Oval ratio and obtain.
It it is 0.01 μm by area in addition, in order to suppress the influence of the evaluated error as caused by noise2Following carbide from Excluded in the object of evaluation.The number of carbide present on ferrite grain boundaries is counted, subtracted by whole carbide numbers Carbide number on crystal boundary and obtained the carbide number in ferrite crystal grain.Number based on measure, ferrite crystalline substance is obtained The individual percentage of Carbide Phases in boundary for the carbide in ferrite crystal grain.
In the tissue after cold-rolled steel sheet is annealed, by the way that ferrite particle diameter is set as into more than 5.0 μm, so as to change Kind cold-workability.If ferrite particle diameter is less than 5 μm, hardness increase, in cold working, become easily to produce cracking, crackle, Therefore ferrite particle diameter is set as more than 5 μm.Preferably more than 7 μm.
On the other hand, if it exceeds 50 μm, then the number for suppressing to slide the carbide on the crystal crystal boundary propagated is reduced, cold Processability reduces, therefore ferrite particle diameter is set as less than 50 μm.Preferably less than 37 μm.
Ferrite particle diameter is after the sightingpiston of sample is ground into minute surface by above-mentioned Ginding process, with 3% nitric acid-second Alcoholic solution is etched, and the tissue of sightingpiston is observed with light microscope or scanning electron microscope, to shooting Image application segment method and be measured.
In addition, it is hard and crisp tissue that the carbide of iron, which is cementite, if to be pearly-lustre with ferritic lamellar tissue The state of body is present, then steel, which is hardened, becomes fragile.Therefore, pearlite needs strongly to reduce, in the steel plate of the present invention, in terms of area occupation ratio It is set as less than 6%.
Pearlite can be strictly discriminated by SEM, observation by light microscope due to distinctive lamellar structure Not.By calculating the region of lamellar structure in arbitrary section, so as to obtain the area occupation ratio of pearlite.
And then by the way that the Vickers hardness of steel plate is set as into 100HV~170HV, so as to improve cold-workability.If Vickers hardness is less than 100HV, then becomes easily to produce in cold working and buckle, therefore Vickers hardness is set as more than 100HV.It is excellent Elect more than 110HV as.
On the other hand, if Vickers hardness ductility reduction, becomes easily in generation more than 170HV in cold working Portion's crackle, therefore Vickers hardness is set as below 170HV.Preferably below 168HV.
Next, manufacture method of the present invention is illustrated.
The basic thought of manufacture method of the present invention is, the steel billet formed using above-mentioned composition, to hot-rolled condition and moves back Fiery condition is consistently managed to carry out the organizational controls of steel plate.
First, the steel billet molten steel continuously casting that required composition forms formed is for hot rolling.Casting after continuously casting Base can be directly for hot rolling, again for hot rolling after can also being heated after cooling down for the time being.
Heated after steel billet is cooled down for the time being and for hot rolling in the case of, heating-up temperature is preferably 1000 DEG C~ 1250 DEG C, the heat time is preferably 0.5 hour~3 hours.In the case where the steel billet after by continuously casting is directly for hot rolling, Temperature for the steel billet of hot rolling is preferably set to 1000 DEG C~1250 DEG C.
If steel billet temperature or billet heating temperature are more than 1250 DEG C or the heating steel billet time was more than 3 hours, from steel The decarburization on base top layer becomes notable, and during heating before carburizing and quenching, the austenite crystal on steel plate top layer grows singularly, resistance to punching Hitting property reduces.Therefore, steel billet temperature or billet heating temperature are preferably less than 1250 DEG C, and the heat time is preferably less than 3 hours. More preferably less than 1200 DEG C, less than 2.5 hours.
If steel billet temperature or billet heating temperature are less than 1000 DEG C or the heat time is less than 0.5 hour, because of casting And microscopic segregation, the gross segregation generated will not eliminate, in the area that the alloying element part concentration such as inside steel billet, Si, Mn forms Domain remaining is got off, and impact resistance reduces.Therefore, steel billet temperature or billet heating temperature are preferably more than 1000 DEG C, the heat time Preferably more than 0.5 hour.More preferably more than 1050 DEG C, more than 1 hour.
Finish rolling in hot rolling is completed in 750 DEG C~850 DEG C of temperature province.If final rolling temperature is less than 750 DEG C, steel The deformation drag increase of plate, rolling load significantly rises, in addition, roller wear extent increases, productivity ratio reduces, and in order to improve modeling Recrystallizing and will not be sufficiently carried out needed for property anisotropy, therefore final rolling temperature is set as more than 750 DEG C.Promoting to tie again On this brilliant aspect, preferably more than 770 DEG C.
If final rolling temperature is more than 850 DEG C, the relatively thicker oxidation of generation in steel plate is made by runout table (ROT) Skin, scar is produced in surface of steel plate due to the oxide skin, after cold forging and carburizing and quenching tempering, be applied with impact load When, cracking easily is produced using scar as starting point, therefore the impact resistance of steel plate reduces.Therefore, final rolling temperature is set as 850 Below DEG C.Preferably less than 830 DEG C.
When the hot rolled steel plate after by finish rolling is cooled down in ROT, cooling velocity is preferably 10 DEG C/sec~100 DEG C/sec. If cooling velocity is less than 10 DEG C/sec, relatively thicker oxide skin is generated in way is cooled down, the scar due to this can not be suppressed Generation, impact resistance reduces, therefore cooling velocity is preferably more than 10 DEG C/sec.More preferably more than 20 DEG C/sec.
If from the top layer of steel plate until inside is cooled down with the cooling velocity more than 100 DEG C/sec, most skin section meeting It is cooled excessively, produces the low temperature phase change tissues such as bainite, martensite.After batching, the hot rolling of room temperature will be cooled to from 100 DEG C When steel plate coiled material uncoiling utilizes, fine crack is produced in low temperature phase change tissue.The fine crack is difficult to by pickling and cold rolling To remove.
Also, if cold forging and carburizing and quenching tempering after to steel plate apply impact load, then cracking using fine crack as Starting point and develop, therefore impact resistance reduce.Therefore, in order to which the most skin section suppressed in steel plate produces bainite, martensite etc. Low temperature phase change tissue, cooling velocity are preferably less than 100 DEG C/sec.More preferably less than 90 DEG C/sec.
In addition, above-mentioned cooling velocity refer to the hot rolled steel plate after finish rolling by without behind water filling section, from water filling section by Start at the time of water cooling during untill the target temperature batched is cooled on ROT, from each water filling section Cooling capacity acquired by cooling device, rather than represent being averaged untill the temperature that water filling start time to the machine of being taken up batches Cooling velocity.
Coiling temperature is set as 400 DEG C~550 DEG C.This is the temperature lower than in general coiling temperature, is special containing in C In the case that amount is high generally without condition.By by the hot rolled steel plate manufactured under the conditions described above in the temperature range Batched, the bainite group that carbide is dispersed with tiny ferrite and is formed so as to turn into the tissue of steel plate Knit.
If coiling temperature is less than 400 DEG C, the austenite phase of non-phase transformation is changed into harder martensite before batching, in heat When the uncoiling of steel rolling coiled material utilizes, cracked on the top layer of hot rolled steel plate, impact resistance reduces.
Further, when from austenite to ferritic recrystallization, because recrystallization driving force is small, therefore ferrite is recrystallized The orientation of crystal grain becomes consumingly to be influenceed by austenite crystal orientation, and the randomization of texture becomes difficult.Therefore, temperature is batched Degree is set as more than 400 DEG C.Preferably more than 430 DEG C.
If coiling temperature more than 550 DEG C, the larger pearlite of generation piece interlamellar spacing, high suitable of generation heat endurance Thick acicular carbide.The acicular carbide also remains after 2 sections of annealing.When cold forging of steel plate etc. shapes, with the needle-like carbon Compound produces cracking as starting point.
In addition, when ferrite is by austenite recrystallization, on the contrary, recrystallization driving force becomes too much, in such case Under, it can also turn into the recrystallization ferrite crystal grain for being strongly depend on austenite crystal orientation, the randomization of texture can not be carried out.Cause This, coiling temperature is set as less than 550 DEG C.Preferably less than 520 DEG C.
The uncoiling of hot rolled steel plate coiled material is utilized, after implementing pickling, implements 2 sections kept in 2 temperature provinces The annealing (2 sections of annealing) of step type.By implementing 2 sections of annealing to hot rolled steel plate, so as to control the stability of carbide, promote iron The generation of the carbide of ferritic grain boundaries.
If cold rolling, ferrite crystal grain miniaturization, therefore steel plate are implemented to the steel plate after pickling before annealing Become to be difficult to softening.Therefore, in the present invention, it is undesirable to implement cold rolling before the anneal, is not preferably entered after pickling Row cold rolling is implemented to make annealing treatment.
1st section of annealing is at 650~720 DEG C, preferably in Ac1Carried out in the following temperature province of point.By the annealing, from And make carbide coarsening, part spherical, and make alloying element concentration in carbide, improve the thermostabilization of carbide Property.
In the 1st section of annealing, firing rate (hereinafter referred to as " the 1st section of the firing rate ") setting untill annealing temperature For 30 DEG C/h~150 DEG C/h.If the 1st section of firing rate is less than 30 DEG C/h, heating needs the time, productivity ratio Reduce, therefore the 1st section of firing rate is set as more than 3 DEG C/h.Preferably more than 10 DEG C/h.
On the other hand, if the 1st section of firing rate is more than 150 DEG C/h, in hot rolled steel plate coiled material peripheral part with it is interior The temperature difference increase in portion, the scar as caused by thermal expansion difference is produced, burns and glues, bumps are formed in surface of steel plate.Shaped in cold forging etc. When, the bumps turn into starting point and produce cracking, and the impact resistance after forging reduction, formability and carburizing and quenching tempering reduces, Therefore the 1st section of firing rate is set as less than 150 DEG C/h.Preferably less than 130 DEG C/h.
Annealing temperature (hereinafter referred to as " the 1st section of annealing temperature ") in 1st section of annealing is set as 650 DEG C~720 DEG C.If 1st section of annealing temperature is less than 650 DEG C, then the stabilisation of carbide is insufficient, when annealing for the 2nd section, carbide is remained in Austria Become difficult in family name's body.Therefore, the 1st section of annealing temperature is set as more than 650 DEG C.Preferably more than 670 DEG C.
On the other hand, if the 1st section of annealing temperature is more than 720 DEG C, generated before the stability of carbide rises difficult to understand Family name's body, the control of above-mentioned tissue change becomes difficult, therefore the 1st section of annealing temperature is set as less than 720 DEG C.Preferably 700 DEG C with Under.
Annealing time (hereinafter referred to as " the 1st section of annealing time ") in 1st section of annealing is set as 3 hours~60 hours.Such as The 1st section of annealing time of fruit is less than 3 hours, then the stabilisation of carbide is insufficient, when annealing for the 2nd section, remains in carbide Become difficult in austenite.Therefore, the 1st section of annealing time is set as more than 3 hours.Preferably more than 5 hours.
On the other hand, if the 1st section of annealing time can not expect the further stabilization of carbide more than 60 hours Change, and then productivity ratio reduces, therefore the 1st section of annealing time is set as less than 60 hours.Preferably less than 55 hours.
Then, 725~790 DEG C are warming up to, is preferably Ac1Point~A3The temperature province of point, makes austenite give birth in the tissue Into.Now, the carbide in fine ferrite crystal grain dissolves in austenite, but passes through the 1st section of coarsening of annealing Carbide is remaining in austenite.
In the case where being cooled down without the 2nd section of annealing, ferrite particle diameter will not become big, can not obtain ideal Tissue.
Firing rate (hereinafter referred to as " the 2nd section of firing rate ") untill the annealing temperature of the 2nd section of annealing is set as 1 DEG C/h~80 DEG C/h.When annealing for the 2nd section, austenite is generated by ferrite grain boundaries and is grown.Now, it is straight by slowing down Firing rate untill annealing temperature, so as to suppress the karyogenesis of austenite, in the group formed by the slow cool down after annealing In knitting, the crystal boundary coverage rate for improving carbide is possibly realized.
Therefore, the 2nd section of firing rate is preferably relatively slow, but if less than 1 DEG C/h, then heating needs the time, productivity ratio drop It is low, therefore the 2nd section of firing rate is set as more than 1 DEG C/h.Preferably more than 10 DEG C/h.
If the 2nd section of firing rate is more than 80 DEG C/h, in hot rolled steel plate coiled material, peripheral part and internal temperature Difference increase, produce due to the scar of larger thermal expansion difference as caused by phase transformation, burn and glue, bumps are formed in surface of steel plate.Cold During forging, cracking is produced by starting point of the bumps, forging and formability reduce, in addition, the impact resistance after carburizing and quenching tempering Property also reduces, therefore the 2nd section of firing rate is set as less than 80 DEG C/h.Preferably less than 70 DEG C/h.
Annealing temperature (hereinafter referred to as " the 2nd section of annealing temperature ") in 2nd section of annealing is set as 725 DEG C~790 DEG C.If 2nd section of annealing temperature is less than 725 DEG C, then the growing amount of austenite tails off, after the cooling after the 2nd section of annealing, ferrite grain boundaries The number of the carbide at place is reduced, in addition, ferrite particle diameter diminishes.Therefore, the 2nd section of annealing temperature is set as more than 725 DEG C.It is excellent Elect more than 735 DEG C as.
On the other hand, if the 2nd section of annealing temperature is more than 790 DEG C, carbide is remained in austenite becomes difficult, group The control for knitting change becomes difficult, therefore the 2nd section of annealing temperature is set as less than 790 DEG C.Preferably less than 770 DEG C.
Annealing time (the 2nd section of annealing time) in 2nd section of annealing was set as 3 hours less than 50 hours.If 2nd section of annealing time is less than 3 hours, then the growing amount of austenite is few, also, the dissolving of the carbide in ferrite crystal grain will not It is sufficiently carried out, makes the number increase of the carbide of ferrite grain boundaries become difficult, in addition, ferrite particle diameter diminishes.Therefore, 2 sections of annealing times are set as more than 3 hours.Preferably more than 5 hours.
On the other hand, if the 2nd section of annealing time was more than 50 hours, carbide is remained in austenite becomes tired Difficulty, in addition, manufacturing cost also increases, therefore the 2nd section of annealing time is set at less than 50 hours.Preferably less than 40 hours.
After 2 sections of annealing, steel plate is cooled to 650 DEG C with 1 DEG C/h~30 DEG C/h of cooling velocity.
The austenite generated in the 2nd section of annealing is subjected to slow cool down by using slow cool down, so as to mutually be changed into ferrite While carbon atom adsorb carbide in austenite is remained in, carbide and austenite cover ferrite grain boundaries, finally The tissue that carbide is largely present in ferrite grain boundaries can be turned into.
Therefore, cooling velocity is preferably relatively slow, but if less than 1 DEG C/h, then required time increase, productivity ratio are cooled down Reduce, therefore cooling velocity is set as more than 1 DEG C/h.Preferably more than 10 DEG C/h.
On the other hand, if cooling velocity is more than 30 DEG C/h, austenite phase is changed into pearlite, and the hardness of steel plate increases Add, forging reduce, in addition, carburizing and quenching tempering after impact resistance reduce, therefore cooling velocity be set as 30 DEG C/h with Under.Preferably less than 20 DEG C/h.
And then the steel plate that will be cooled to 650 DEG C is cooled to room temperature.Cooling velocity now is simultaneously not limited.
Atmosphere in 2 sections of annealing is not particularly limited to specific atmosphere.For example, it may be the atmosphere of more than 95% nitrogen, Any atmosphere in the atmosphere of more than 95% hydrogen, air atmosphere.
As described above, hot-rolled condition and annealing conditions consistently manage to carry out steel according to the present invention The manufacture method of the organizational controls of plate, it can manufacture and be had excellent formability and when being combined with drawing, thickening the cold forging of shaping to oozing The excellent steel plate of quenching degree needed for the raising of impact resistance after carbon Q-tempering.
Embodiment
Next, embodiment is illustrated, but the level of embodiment is to confirm the exploitativeness and effect of the present invention Fruit and the example of condition used, the present invention are not limited to the condition example.The present invention can use various conditions, only Do not depart from the purport of the present invention and reach the purpose of the present invention.
For the evaluation of cold-workability, by thickness of slab be 3mm annealed condition JIS5 tension test sheets acquired for materials Lai Tension test is carried out, pair is evaluated with rolling direction into 0 ° of direction and with the percentage of total elongation in rolling direction direction in 90 °, two Individual direction is the difference of the percentage of total elongation of more than 35% and all directions | Δ EL | in the case of being less than 4%, depending on thinking cold working Property is superior.
It is 1.5mm by annealed condition material removal to the thickness of slab that thickness of slab is 3mm, in vacuum for the evaluation of quenching degree The holding of 880 DEG C × 10 minutes is carried out in atmosphere, is quenched with 30 DEG C/sec of cooling velocity, if a point rate for martensite is More than 60%, then depending on thinking that quenching degree is superior.
(embodiment 1)
After the continuously casting strand (steel ingot) that composition shown in table 1 forms is heated 1.8 hours at 1240 DEG C, for Hot rolling, after terminating smart hot rolling at 890 DEG C, batched at 510 DEG C, manufactured the coils of hot rolled that thickness of slab is 3.0mm.To heat Roll coiled material and carry out pickling, coils of hot rolled is loaded in box annealing stove, is the nitrogen of 95% hydrogen -5% by control climate, heated from room temperature To 705 DEG C, kept for 36 hours at 705 DEG C and make the temperature distribution homogenization in coils of hot rolled, be then heated to 760 DEG C, Maintained at 760 DEG C 10 hours.
Then, 650 DEG C are cooled to 10 DEG C/h of cooling velocity, then, are furnace-cooled to room temperature, have made evaluating characteristics Sample.In addition, the tissue of sample is determined by above-mentioned method.
Table 1
Show the Vickers hardness to manufactured sample, the number of carbide on ferrite grain boundaries relative to iron in table 2 Ratio, pearlite area occupation ratio, cold-workability, the quenching degree of the number of carbide in ferritic crystal grain are determined or evaluated As a result.
Table 2
As shown in table 2, B-1, E-1, F-1, H-1, J-1, K-1, L-1, M-1, N-1, P-1, R- of invention steel 1st, T-1, W-1, X-1, Y-1, Z-1, AB-1 and AC-1 are：The number of the carbide of ferrite grain boundaries is relative to ferrite crystal grain For the ratio of the number of interior carbide more than 1, Vickers hardness is below 170HV, and cold-workability and quenching degree are excellent.
On the other hand, it is high to compare steel G-1 C amounts, cold-workability reduction.Compare steel O-1 because Mo amounts and Cr amounts are high, carbonization The stability of thing is high, therefore carbide does not dissolve in quenching, and austenite growing amount is few, and quenching degree is inferior.
Compare steel Q-1 and AD-1 because Si, Al amount are high, A3 points are high, therefore austenite growing amount is few in quenching, through hardening Property is inferior.Comparative example U-1 S amounts are high, thick MnS generated in steel, cold-workability is low.Comparative examples A A-1 Mn amounts are low, quench Permeability is inferior.
The final rolling temperature of the hot rolling of Comparative Example I -1 is low, and productivity ratio reduces.The final rolling temperature of the hot rolling of Comparative Example D -1 is high, Surface of steel plate generates oxide skin scar.The coiling temperature of comparative example C-1 and S-1 hot rolling is low, the low temperature such as bainite, martensite Phase-change organization becomes more and brittle, is frequently cracked when the uncoiling of coils of hot rolled utilizes, and productivity ratio reduces.
The coiling temperature of Comparative examples A -1 and V-1 hot rolling is high, and the relatively thicker pearly-lustre of sheet gap is generated in hot rolling microstructure The thick carbide of body and the high needle-like of heat endurance, the carbide are also remained in steel plate after 2 sections of steps are annealed, it is cold plus Work reduces.
(embodiment 2)
In order to investigate the influence of annealing conditions, it is small that the steel billet that the composition shown in table 1 forms is heated 1.8 at 1240 DEG C Shi Hou, for hot rolling, after terminating smart hot rolling at 820 DEG C, 520 DEG C are cooled to 45 DEG C/sec of cooling velocity on ROT, Batched at 510 DEG C, the coils of hot rolled that manufacture thickness of slab is 3.0mm, implement 2 sections of step types with the annealing conditions shown in table 3 Box annealing, made thickness of slab be 3.0mm sample.
Shown in table 3 the carbide diameter to manufactured sample, ferrite particle diameter, Vickers hardness, on ferrite grain boundaries Carbide number relative to the ratio of the number of the carbide in ferrite crystal grain, pearlite area occupation ratio, cold-workability, quench The result that permeability is determined or evaluated.
Table 3
As shown in table 3, B-2, C-2, E-2, F-2, H-2, I-2, J-2, K-2, M-2, N-2, R- of invention steel 2nd, S-2, V-2, Z-2 and AC-2 are：The number of the carbide of ferrite grain boundaries is relative to the carbide in ferrite crystal grain For the ratio of number more than 1, Vickers hardness is below 170HV, and cold-workability and quenching degree are excellent.
On the other hand, it is high to compare steel G-1 C amounts, cold-workability reduction.It is high to compare steel O-1 Mo amounts and Cr amounts, cold working Property reduce.Further, since the stability of carbide is high, therefore carbide does not dissolve in quenching, and austenite growing amount is few, quenches Permeability is inferior.
Compare steel Q-1 because Si amounts are high, ferritic hardness is high, therefore processability reduces.Further, since A3 points are high, because In quenching, austenite growing amount is few for this, and quenching degree is inferior.Comparing steel AD-1 because Al amounts are high, A3 points are high, therefore in quenching Austenite growing amount is few, and quenching degree is inferior.It is high to compare steel U-1 S amounts, thick MnS is generated in steel, cold-workability reduces. Compare that steel AA-1 Mn amounts are low, and quenching degree is inferior.
Keeping temperature when comparing the 1st section of annealing of box annealing of the steel T-2 due to 2 sections of step types is low, below Ac1 temperature Carbide coarsening processing it is insufficient, the heat stability of carbide is insufficient, so as to the 2nd section anneal when remaining carbonization Thing is reduced, and can not suppress pearlitic transformation in the tissue after slow cool down, and cold-workability reduces.
Keeping temperature when comparing the 1st section of annealing of the box annealing of steel A-2 2 sections of step types is high, is generated in annealing Austenite, the stability of carbide can not be improved, the carbide of remaining is reduced when annealing for the 2nd section, the tissue after slow cool down In can not suppress pearlitic transformation, cold-workability reduces.
Retention time when comparing the 1st section of annealing of box annealing of the steel L-2 due to 2 sections of step types is short, below Ac1 temperature Carbide coarsening processing it is insufficient, the heat stability of carbide is insufficient, so as to the 2nd section anneal when remaining carbonization Thing is reduced, and can not suppress pearlitic transformation in the tissue after slow cool down, and cold-workability reduces.
Compare steel W-2 2 sections of steps annealing when the 1st section annealing when retention time length, productivity ratio reduce.Compare steel X- 2 because keeping temperature when the 2nd section when 2 sections of steps are annealed is annealed is low, and the growing amount of austenite is few and can not increase grain boundaries Carbide number ratio, therefore cold-workability reduce.
Keeping temperature when comparing the 2nd section of annealing of box annealing of the steel AB-2 due to 2 sections of step types is high, promotes carbide Dissolving, therefore the carbide of remaining is reduced, and can not suppress pearlitic transformation, Cold Forging drop in the tissue after slow cool down It is low.
Keeping temperature when comparing the 2nd section of annealing of the box annealing of steel P-2 2 sections of step types is low, the generation of austenite Amount is few, can not increase the number ratio of the carbide at ferrite grain boundaries, and cold-workability reduces.Compare steel Y-2 due to 2 sections of steps Retention time length during the 2nd section of annealing of the box annealing of type, promotes the dissolving of carbide, therefore the carbide of remaining is reduced, Pearlitic transformation can not be suppressed in tissue after slow cool down, Cold Forging reduces.
Compare cooling velocity of the end of the 2nd section of annealing of box annealing of the steel D-2 from 2 sections of step types untill 650 DEG C Greatly, pearlitic transformation is caused in cooling, cold-workability reduces.
Industrial applicability
As described above, in accordance with the invention it is possible to manufacture and provide formability and the steel plate of excellent in abrasion resistance.The present invention's Steel plate due to be it is suitable as the automotive part manufactured via manufacturing procedures such as punching, bending, punch process, cutter, its The steel plate of the raw material of his mechanical part, therefore the utilizability of the present invention industrially is high.

Claims (3)

1. a kind of steel plate, it is characterised in that the steel plate is contained in terms of quality %：
C：0.10~0.40%,
Si：0.01~0.30%,
Mn：1.00~2.00%,
P：Less than 0.020%,
S：Less than 0.010%,
Al：0.001~0.10%,
N：Less than 0.010%,
O：Less than 0.020%,
Cr：Less than 0.50%,
Mo：Less than 0.10%,
Nb：Less than 0.10%,
V：Less than 0.10%,
Cu：Less than 0.10%,
W：Less than 0.10%,
Ta：Less than 0.10%,
Ni：Less than 0.10%,
Sn：Less than 0.050%,
Sb：Less than 0.050%,
As：Less than 0.050%,
Mg：Less than 0.050%,
Ca：Less than 0.050%,
Y：Less than 0.050%,
Zr：Less than 0.050%,
La：Less than 0.050%,
Ce：Less than 0.050%,
Remainder is Fe and inevitable impurity,
Wherein, the metal structure of the steel plate meets：
The number of the carbide of ferrite grain boundaries relative to the ratio of the number of the carbide in ferrite crystal grain more than 1,
Ferrite particle diameter is 5 μm~50 μm, and
The area occupation ratio of pearlite is less than 6%,
The Vickers hardness of the steel plate is 100HV~170HV.
2. steel plate according to claim 1, it is characterised in that contain Ti instead of a part of the Fe：0.10% with Lower and B：1 kind in less than 0.010% or 2 kinds.
A kind of 3. manufacture method of steel plate, it is characterised in that it is the manufacture method of the steel plate described in manufacturing claims 1 or 2,
Wherein, the steel billet that the composition described in claim 1 or 2 forms is implemented to complete in 750 DEG C~850 DEG C of temperature province The hot rolling of finish rolling and hot rolled steel plate is made,
The hot rolled steel plate is batched at 400 DEG C~550 DEG C,
Pickling is implemented to the hot rolled steel plate batched,
Hot rolled steel plate to pickling is implemented to keep in 650 DEG C~720 DEG C of temperature province the 1st section of 3 hours~60 hours Annealing, then,
Hot rolled steel plate is implemented to be kept for the 2nd section of 3 hours~50 hours anneal in 725 DEG C~790 DEG C of temperature province,
Hot rolled steel plate after annealing is cooled to 650 DEG C with 1 DEG C/h~30 DEG C/h of cooling velocity.
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Families Citing this family (13)

* Cited by examiner, † Cited by third party
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JP6070912B1 (en) * 2015-04-10 2017-02-01 新日鐵住金株式会社 Steel sheet excellent in cold workability during forming and method for producing the same
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Citations (9)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH1161272A (en) * 1997-08-26 1999-03-05 Sumitomo Metal Ind Ltd Manufacture of high carbon cold-rolled steel plate excellent in formability
JPH1180884A (en) * 1997-09-08 1999-03-26 Nisshin Steel Co Ltd Medium-or high-carbon steel sheet excellent in local ductility and hardenabiltiy
JPH11269552A (en) * 1998-03-25 1999-10-05 Nisshin Steel Co Ltd Manufacture of medium/high carbon steel sheet excellent in stretch-flange formability
WO2007088965A1 (en) * 2006-02-03 2007-08-09 Nikon Corporation Image processing device, image processing method, and image processing program
JP2007270330A (en) * 2006-03-31 2007-10-18 Jfe Steel Kk Steel plate superior in fine blanking workability, and manufacturing method therefor
WO2007116599A1 (en) * 2006-03-31 2007-10-18 Jfe Steel Corporation Steel plate having excellent fine blanking processability and method for manufacture thereof
JP2007270331A (en) * 2006-03-31 2007-10-18 Jfe Steel Kk Steel sheet superior in fine blanking workability, and manufacturing method therefor
CN103469089A (en) * 2013-09-11 2013-12-25 马鞍山市安工大工业技术研究院有限公司 Cake-shaped crystal grain deep-draw double-phase steel plate and preparation method thereof
CN107614728A (en) * 2015-05-26 2018-01-19 新日铁住金株式会社 Steel plate and its manufacture method

Family Cites Families (20)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH09316540A (en) * 1996-05-27 1997-12-09 Aichi Steel Works Ltd Manufacture of steel for machine structural use for contour induction hardening, excellent in cold forgeability, and manufacture of cold forged part
JPH10265840A (en) * 1997-03-25 1998-10-06 Aichi Steel Works Ltd Production of cold forging parts
JP3909939B2 (en) * 1997-09-08 2007-04-25 日新製鋼株式会社 Manufacturing method for medium and high carbon steel sheets with excellent stretch flangeability
JP2001073033A (en) * 1999-09-03 2001-03-21 Nisshin Steel Co Ltd Production of medium-high carbon steel sheet excellent in local ductility
JP3879459B2 (en) 2001-08-31 2007-02-14 Ｊｆｅスチール株式会社 Manufacturing method of high hardenability high carbon hot rolled steel sheet
US20050199322A1 (en) * 2004-03-10 2005-09-15 Jfe Steel Corporation High carbon hot-rolled steel sheet and method for manufacturing the same
JP4319940B2 (en) 2004-04-27 2009-08-26 新日本製鐵株式会社 High carbon steel plate with excellent workability, hardenability and toughness after heat treatment
JP5194454B2 (en) * 2006-01-31 2013-05-08 Ｊｆｅスチール株式会社 Steel plate excellent in fine blanking workability and manufacturing method thereof
EP1980635B1 (en) * 2006-01-31 2012-01-11 JFE Steel Corporation Steel sheet with excellent suitability for fine blanking and process for producing the same
JP5292698B2 (en) * 2006-03-28 2013-09-18 Ｊｆｅスチール株式会社 Extremely soft high carbon hot-rolled steel sheet and method for producing the same
JP4992274B2 (en) 2006-03-31 2012-08-08 Ｊｆｅスチール株式会社 Steel plate excellent in fine blanking workability and manufacturing method thereof
JP5262012B2 (en) * 2006-08-16 2013-08-14 Ｊｆｅスチール株式会社 High carbon hot rolled steel sheet and manufacturing method thereof
JP5652844B2 (en) * 2009-03-30 2015-01-14 日新製鋼株式会社 High formability carburized steel sheet
JP5521931B2 (en) * 2010-09-14 2014-06-18 新日鐵住金株式会社 Soft medium carbon steel plate with excellent induction hardenability
JP6108924B2 (en) * 2013-04-08 2017-04-05 株式会社神戸製鋼所 Manufacturing method of steel for cold forging
ES2744909T3 (en) * 2013-06-07 2020-02-26 Nippon Steel Corp Heat treated steel material and method of manufacture thereof
JP6439248B2 (en) * 2013-12-18 2018-12-19 新日鐵住金株式会社 Medium / high carbon steel sheet with excellent punchability and method for producing the same
JP6070912B1 (en) * 2015-04-10 2017-02-01 新日鐵住金株式会社 Steel sheet excellent in cold workability during forming and method for producing the same
CN107614726B (en) * 2015-05-26 2020-02-07 日本制铁株式会社 Steel sheet and method for producing same
MX2017015016A (en) * 2015-05-26 2018-04-13 Nippon Steel & Sumitomo Metal Corp Steel sheet and method for producing same.

Patent Citations (9)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH1161272A (en) * 1997-08-26 1999-03-05 Sumitomo Metal Ind Ltd Manufacture of high carbon cold-rolled steel plate excellent in formability
JPH1180884A (en) * 1997-09-08 1999-03-26 Nisshin Steel Co Ltd Medium-or high-carbon steel sheet excellent in local ductility and hardenabiltiy
JPH11269552A (en) * 1998-03-25 1999-10-05 Nisshin Steel Co Ltd Manufacture of medium/high carbon steel sheet excellent in stretch-flange formability
WO2007088965A1 (en) * 2006-02-03 2007-08-09 Nikon Corporation Image processing device, image processing method, and image processing program
JP2007270330A (en) * 2006-03-31 2007-10-18 Jfe Steel Kk Steel plate superior in fine blanking workability, and manufacturing method therefor
WO2007116599A1 (en) * 2006-03-31 2007-10-18 Jfe Steel Corporation Steel plate having excellent fine blanking processability and method for manufacture thereof
JP2007270331A (en) * 2006-03-31 2007-10-18 Jfe Steel Kk Steel sheet superior in fine blanking workability, and manufacturing method therefor
CN103469089A (en) * 2013-09-11 2013-12-25 马鞍山市安工大工业技术研究院有限公司 Cake-shaped crystal grain deep-draw double-phase steel plate and preparation method thereof
CN107614728A (en) * 2015-05-26 2018-01-19 新日铁住金株式会社 Steel plate and its manufacture method

Cited By (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN109963959A (en) * 2018-10-02 2019-07-02 日本制铁株式会社 The manufacturing method of carburizing steel plate and carburizing steel plate
CN111394654A (en) * 2020-04-23 2020-07-10 辽宁科技学院 Hot-press forming steel plate added with L a microalloy and preparation method thereof
CN112080697A (en) * 2020-09-08 2020-12-15 北京首钢股份有限公司 Steel for clutch driven disc, preparation method of steel and clutch driven disc
CN114763590A (en) * 2021-01-11 2022-07-19 宝山钢铁股份有限公司 Wear-resistant steel with high uniform elongation and manufacturing method thereof
CN114763590B (en) * 2021-01-11 2023-03-14 宝山钢铁股份有限公司 Wear-resistant steel with high uniform elongation and manufacturing method thereof

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