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CN110475889A - Hot rolled steel plate and steel forged part and its manufacturing method - Google Patents

Hot rolled steel plate and steel forged part and its manufacturing method Download PDF

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Publication number
CN110475889A
CN110475889A CN201780089321.5A CN201780089321A CN110475889A CN 110475889 A CN110475889 A CN 110475889A CN 201780089321 A CN201780089321 A CN 201780089321A CN 110475889 A CN110475889 A CN 110475889A
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CN
China
Prior art keywords
steel plate
less
rolling
hot rolled
rolled steel
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Pending
Application number
CN201780089321.5A
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Chinese (zh)
Inventor
横井龙雄
吉川伸麻
米村繁
大塚和也
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Japanese Style Stock Co
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Japanese Style Stock Co
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Publication date
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Publication of CN110475889A publication Critical patent/CN110475889A/en
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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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • C21D1/19—Hardening; Quenching with or without subsequent tempering by interrupted quenching
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • C21D1/19—Hardening; Quenching with or without subsequent tempering by interrupted quenching
    • C21D1/20—Isothermal quenching, e.g. bainitic hardening
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/008—Heat treatment of ferrous alloys containing Si
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/02—Hardening by precipitation
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/005—Modifying the physical properties by deformation combined with, or followed by, heat treatment of ferrous alloys
    • 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
    • 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
    • C21D8/0263—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
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0421—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the working steps
    • C21D8/0426—Hot rolling
    • C—CHEMISTRY; METALLURGY
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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
    • 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
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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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • C21D9/48—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals deep-drawing sheets
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
    • C—CHEMISTRY; METALLURGY
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    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—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
    • 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
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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
    • C22C38/50—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
    • C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/001—Austenite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/002—Bainite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/005—Ferrite
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    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/008—Martensite
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    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/009—Pearlite
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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Heat Treatment Of Steel (AREA)

Abstract

A kind of hot rolled steel plate, the chemical composition of steel plate with quality % be calculated as C:0.020-0.070%, Si:0.05-1.70%, Mn:0.60-2.50%, Al:0.010-1.000%, N > 0-0.0030%, P≤0.050%, S≤0.005%, Ti:0.015-0.170%, Nb:0-0.100%, V:0-0.300%, Cu:0-2.00%, Ni:0-2.00%, Cr:0-2.00%, Mo:0-1.00%, B:0-0.0100%, Mg:0-0.0100%, Ca:0-0.0100%, REM:0-0.1000%, Zr:0-1.000%, Co:0-1.000%, Zn:0-1.000%, W:0-1.000%, Sn:0-0.050%, surplus: Fe and impurity, the metallographic structure of steel plate is calculated as ferrite with area %: 5-70%, bainite: 30-95%, residual γ≤2%, martensite≤2%, pearlite≤1%, ferrite+bainite >=95%, and a number density of the fine Ti precipitate in ferrite crystal grain is 1.0 × 1016‑50.0×1016A/cm3, the average equivalent circular diameter of the TiN precipitate in steel plate is 1.0-10.0 μm, and the average value of the shortest distance between adjacent TiN precipitate is 10.0 μm or more, and the standard deviation of nano hardness is 1.00GPa or less.

Description

Hot rolled steel plate and steel forged part and its manufacturing method
Technical field
The present invention relates to hot rolled steel plate and steel forged part and its manufacturing methods.
Background technique
It is required high intensity from raising safety and light-weighted angle, the steel plate of the body construction for automobile With high press processability.For this requirement, propose a kind of than the excellent height of previous good hole scalability (high hole expandability) Strength steel sheet.For example, the steel plate excellent as hole scalability (λ value), it was recently reported that carried out by the nano-precipitation of Ti, Nb etc. The steel plate and its manufacturing method of the ferrite main phase of precipitation strength.
Patent document 1 discloses hot rolled steel plate a kind of high-intensitive and with excellent stretch flangeability.In addition, patent is literary It offers 2 and discloses a kind of high formability high-tension hot rolled steel plate that property uniform in material is excellent.In turn, patent document 3 discloses one kind Elongation and the high-tension hot rolled steel plate having excellent stretch flangeability.
Existing technical literature
Patent document
Patent document 1: Japanese Unexamined Patent Publication 2002-105595 bulletin
Patent document 2: Japanese Unexamined Patent Publication 2002-322540 bulletin
Patent document 3: Japanese Unexamined Patent Publication 2002-322541 bulletin
Summary of the invention
Problems to be solved by the invention
On the other hand, as the body construction of automobile complicates, component shape complicates, the processing of automotive sheet is not only It is only the element of previous press process, also plyability on the basis of previous press process element as plate forging etc. It is combined with new machining element.Previous press process element for example has deep-draw processing, hole extension, the convex forming of drum, bending The element of processing, thinned processing etc.
But for being forged to the press process of representative with plate in recent years, due to that can add in aforementioned previous compacting Further dispersion suppresses load, locally applies compressive load on the basis of work element, therefore the processing for being also attached with forging is wanted Element, for example, upsetting processing, thicken (thickenings) process etc machining element.That is, plate forging has plyability machining element Press process, also comprising forging processing except machining element of the plyability machining element in previous steel plate press process Distinctive machining element.
By carrying out this plate forging, based on previous press process side make steel plate plate thickness keep original plate thickness or Subtract thick (reducing wall thickness) side and steel plate deformed is subjected to shape components, also, adds being locally forged by compression force The part of work, the plate thickness of steel plate thicken (thickening), and thus, it is possible to the steel plates at the position needed for being expeditiously deformed into functionally Plate thickness, it can be ensured that the intensity of component.
But do not have completely in Patent Documents 1 to 3 for the processing comprising plyability machining element for being forged to representative with plate It refers to.In addition, the coiling condition described in Patent Document 1 for manufacturing hot rolled steel plate is very harsh and unrealistic.In turn, specially The hot rolled steel plate that sharp document 2 and 3 is recorded contains 0.07% or more the Alloy Elements Mo for belonging to valuableness, therefore there are production costs High problem.
Known high reaming steel shows good formability in previous press process.But investigation shows to belong to In the plate forging of manufacturing process in previous press process also comprising forging machining element, even few degree of finish, sometimes Steel plate can also occur to be cracked and be broken.
It is split that is, there is compacting in the part that plate thickness constriction (plate thickness of steel plate is reduced) occurs in previous press process Line, but investigation shows to forge as plate in this not processing with plate thickness constriction, cracking occurs there is also material and the feelings of fracture Condition, to be unable to get finished product.
And the limit that the cracking for being unaware of this plate forging occurs is to be dominated, how can just be mentioned by which kind of property of steel plate It is high.It is therefore desirable to which effectively application belongs to the deep-draw processability, hole scalability, the convex forming of drum of the function of previous high reaming steel These functions of processability and the high reaming steel that will not be broken carrying out plate forging and processing.
The present invention be to solve the above-mentioned problems made of, it is intended that provide be able to maintain that as high reaming steel Basic function and raising be locally forged by compression force processing part the crackle limit, plate forgeability it is excellent Different hot rolled steel plate.
The solution to the problem
Present invention seek to address that above-mentioned technical problem, with following hot rolled steel plates and steel forged part and its manufacturing method For purport.
(1) a kind of hot rolled steel plate, wherein
The chemical composition of steel plate is calculated as with quality %
C:0.020~0.070%,
Si:0.05~1.70%,
Mn:0.60~2.50%,
Al:0.010~1.000%,
N: greater than 0% and for 0.0030% or less,
P:0.050% or less,
S:0.005% or less,
Ti:0.015~0.170%,
Nb:0~0.100%,
V:0~0.300%,
Cu:0~2.00%,
Ni:0~2.00%,
Cr:0~2.00%,
Mo:0~1.00%,
B:0~0.0100%,
Mg:0~0.0100%,
Ca:0~0.0100%,
REM:0~0.1000%,
Zr:0~1.000%,
Co:0~1.000%,
Zn:0~1.000%,
W:0~1.000%,
Sn:0~0.050% and
Surplus: Fe and impurity,
In the section vertical with rolling direction of aforementioned steel plate, the width and thickness by aforementioned steel plate is respectively W and t When, the end face apart from aforementioned steel plate be 1/4W or 3/4W and the surface apart from aforementioned steel plate be 1/4t or the position of 3/4t at gold Phase constitution is calculated as with area %
Ferrite: 5~70%,
Bainite: 30~95%,
Retained austenite: 2% or less,
Martensite: 2% or less and
Pearlite: 1% hereinafter, also,
The summation of ferrite and bainite: 95% or more,
Aforementioned ferrite has the precipitate containing Ti in crystal grain,
A number density of the aforementioned precipitate containing Ti is 1.0 × 1016~50.0 × 1016A/cm3,
Contain TiN precipitate in aforementioned steel plate,
The average equivalent circular diameter of aforementioned TiN precipitate is 1.0~10.00 μm,
The average value of the shortest distance between adjacent aforementioned TiN precipitate is 10.00 μm or more,
The standard deviation of nano hardness is 1.00GPa or less.
(2) hot rolled steel plate according to above-mentioned (1), wherein the average equivalent circular diameter of the aforementioned precipitate containing Ti is 1.00~3.00nm.
(3) hot rolled steel plate according to above-mentioned (1) or (2), wherein
Tensile strength is 780MPa or more,
The product of uniform elongation and tensile strength is 7000MPa% or more,
The product of hole expansibility and tensile strength is 50000MPa% or more.
(4) a kind of manufacturing method of hot rolled steel plate is to manufacture hot-rolled steel described in any one of above-mentioned (1) to (3) The method of plate,
For the slab with chemical composition described in above-mentioned (1), successively implement heating process, continuously hot rolling process, the One cooling process, the second cooling process and coiling process,
In aforementioned heating process, aforementioned slab is heated to shown in following (i) formula SRTmin DEG C or more and 1260 DEG C Temperature below,
Aforementioned continuously hot rolling process includes the multistage finish rolling of roughing and 3 grades or more,
The end temperature of aforementioned roughing is 1100 DEG C or more,
The accumulation strain in last 3 grades of rolling in aforementioned multistage finish rolling is 0.01~0.10,
It is the Ar found out by following (ii) formulas that the rolling of aforementioned multistage finish rolling, which terminates temperature,3+ 30 DEG C or more of temperature,
In aforementioned first cooling process, after aforementioned multi-level oil rolls, begun to cool after 1.00~5.00s, from Aforementioned rolling terminates temperature and rises until 650~750 DEG C of temperature range, is carried out with the average cooling rate of 10 DEG C/s or more cold But, later, 1~10s is kept in an atmosphere,
In aforementioned second cooling process, after being kept in aforementioned atmosphere, from 600~740 DEG C of temperature range, with The average cooling rate of 10 DEG C/s or more is cooled down,
In aforementioned coiling process, batched with 450~650 DEG C of coiling temperature；
SRTmin=7000/ { 2.75-log (Ti × C) } -273 (i)
Ar3=970-325 × C+33 × Si+287 × P+40 × Al-92 × (Mn+Mo+Cu) -46 × (Cr+Ni) (ii)
Wherein, the symbol of element in above-mentioned formula indicates content (quality %) of each element in hot rolled steel plate, is not containing In the case where substitute into 0.
(5) a kind of steel forged part, the hot rolled steel plate as described in any one of above-mentioned (1) to (3) obtain.
(6) a kind of manufacturing method of steel forged part, wherein to hot rolling described in any one of above-mentioned (1) to (3) Steel plate at least implements forging processing.
The effect of invention
In accordance with the invention it is possible to obtain maintaining the good hole scalability of the basic function as high reaming steel and The excellent hot rolled steel plate of plate forgeability.
Detailed description of the invention
Fig. 1 is the schematic diagram for illustrating pure shear test.(a) of Fig. 1 is the figure for showing the test film of pure shear test.Fig. 1 (b) be the test film after showing pure shear test figure.
Specific embodiment
The inventors of the present invention are to solve aforementioned technical problem to have made intensive studies, and have obtained following understanding.
(a) equivalent plastic strain
Plate forging includes the change in the strain region (high strain region) beyond the breaking strain in previous tension test Shape.In addition, can not only be commented by tension test and shear test data merely since plate forging is plyability processing Valence.Therefore, the inventors of the present invention have imported " equivalent plastic strain " as index, and establish new evaluation method.
Stretching it was found that by using the equivalent plastic strain as index, when can be to fracture when carrying out tension test Stress and elongation strain and carry out shearing test when fracture when shear stress and shear strain carry out plyability evaluation.
Equivalent plastic strain be by pure shear test shear stress σ s and the relationship of shear plasticity strain stress sp be converted to Obtained from the relationship of tensile stress σ and elongation strain ε in the different one directional tensile test of mode of texturing.Also, pass through vacation The relationship for determining isotropic hardening law and plastic work done conjugation, used as the conversion coefficient (κ) of constant, so as to such as following formula It is converted in this way.Conversion coefficient (κ) is calculated by aftermentioned method, exports equivalent plastic strain on this basis.
Shear stress σ s × κ in tensile stress σ=pure shear test in one directional tensile test
Shear plasticity strain stress sp/ κ in elongation strain ε=pure shear test in one directional tensile test
(b) multistage shearing test
In order to find out equivalent plastic strain, need to obtain the tensile stress based on tension test and the relationship of elongation strain, And the relationship of the shear stress and shear strain based on shearing test.But plate forging includes the deformation in high strain region. It therefore,, can be from the portion for keeping test film on test film when being tested using usually used shearing test device 1 time Separately begin to generate cracking.As a result, cannot test in many cases the deformation for reaching high strain region.Therefore, it is necessary to The method that this processing for not generating subtracting for steel plate plate thickness thick (wall thickness reduces and constriction) is reproduced can be forged to plate.
Therefore, shearing test is divided into multistage progress, after shearing test at different levels, all in the part for keeping test film The starting point of the cracking of the test film of generation is machined, so that the cracking of test film is no longer in progress, by these shearing tests As a result it is together in series and test result is evaluated.By using the test method, can obtain until high strain region is cut Test result is cut, can be found out until the shear stress of high strain region and the relationship of shear strain.
On the other hand, previous stretching test method applicable for tensile stress and elongation strain.It is, for example, possible to use JIS5 test film based on (2011) JIS Z2241.
(c) mechanism that cracking occurs
By using above-mentioned multistage shearing test, the evaluation method for having used equivalent plastic strain and plate forging front and back Steel plate microcosmic investigation, following understanding has been obtained for the mechanism of production of cracking.
Excellent hole scalability in order to obtain, as the microscopic structure of high reaming steel, using to be based on the fine analysis such as Ti, Nb The ferrite (precipitation strength ferrite) of the precipitation strength of object is the tissue of main phase out.On the other hand, once addition Ti, then if Without using special preparation method, coarse TiN (TiN of precipitation is also referred to as " TiN " below) will be precipitated.This is because TiN is Thermodynamically highly stable compound, when casting in steel plate manufacturing process, when the heating of hot rolling or roughing initial stage is contour It, can preferential crystallization or precipitation relative to other compounds under temperature state.
TiN firmly extremely can be as the coating of cutting element, mechanical part, mould for plastics, sports goods, ornament etc. The degree that purposes uses, it is known that its hardness is Hv2000~2300 or so, is the precipitate of very hard.Therefore, receiving plate is forged When making the deformation in this Large strain domain, due to the deformability between parent phase tissue difference and cause on interface be easy Generate gap.
Due to the deformability between hard precipitate (TiN) and appropriate soft parent phase tissue (ferrite or bainite) Difference, gap (small cavity) can be generated in the interface of two-phase.Thereafter, empty while the strain of plate forging increases Gap growth, becomes to be cracked in conjunction with adjacent gap, until fracture.Then, gap generation and even if sky can be prevented by having been found that Gap growth also can inhibit it in conjunction with adjacent gap, then be able to suppress cracking.Wherein, it does not damage at this time as high reaming steel The function of script be also important.
Following item is had found by these understanding.
(i) average diameter of TiN is limited.
That is, the crystal boundary due to gap in the TiN of hard precipitate generates, by limiting the average diameter of TiN, energy Enough reduce the generation in gap.
(ii) the mutual distance of restricted T iN.
That is, the crystal boundary due to gap in TiN generates, by configuring TiN away from each other, gap can be made i.e. Growth is set also to be difficult to combine.
(iii) it is uneven to reduce nano hardness.
That is, the generation in gap can be reduced by the difference of hardness for reducing hard tissue Yu soft tissue to the greatest extent.
(iv) equivalent plastic strain when being broken is 0.90 (90%) or more.
Have confirmed that the condition by meeting aforementioned (i)~(iii), equivalent plastic strain when fracture reaches 0.90 (90%) More than, even if forging in this plyability processing in plate, it can also guarantee certain processability.
(d) effective accumulation strain
The tissue of above-mentioned (i)~(iv) in order to obtain is passing through 3 grades or more of the multistage (such as 6 grades or 7 grades) in hot rolling In the multistage finish rolling that continuous rolling carries out, need (to be expressed as sometimes below " effectively with the accumulation strain in last 3 grades of rolling Accumulation strain ") reach 0.01~0.10 mode and carries out final finish rolling.
Effective accumulation strain is the index for considering following factor: the pressure of temperature, rolling bring steel plate when rolling Recovery, recrystallization and the grain growth of crystal grain caused by rate.Therefore, when calculating effective accumulation strain, expression has been used to roll Static this structure law for restoring phenomenon occurred over time afterwards.Consider the static state that crystal grain occurs over time after rolling The phenomenon that recovery is because the release of energy of the accumulation in the crystal grain after rolling is by hot crystal grain dislocation in the form of strain Caused by static recovery caused by disappearing.Also, the disappearance of thermal potential mistake is elapsed time shadow after by rolling temperature and rolling Loud.Therefore, it while in view of the static state is restored, imports temperature when describing rolling in a manner of parameter, roll bring steel The index of time passage after the reduction ratio (logarithmic strain) of plate, rolling, is defined as " effective accumulation strain ".
In this way, target microscopic structure can be obtained by limiting effective accumulation strain, and nano hardness unevenness is reduced, because This is not cracked carrying out plate forging by inhibiting the interface of hard tissue and soft tissue to generate gap, thus It can obtain the excellent steel plate of plate forgeability.
The present invention is completed based on above-mentioned cognition.Hereinafter, each feature of the invention is described in detail.
(A) chemical composition
The restriction reason of each element is as described below.It should be noted that " % " of content involved in the following description refers to " quality % ".
C:0.020~0.070%
C can form precipitate with combinations such as Nb, Ti in steel plate, facilitate intensity by precipitation strength and improve.C content When less than 0.020%, it is unable to fully obtain above-mentioned effect bring effect.On the other hand, when C content is more than 0.070%, become The iron series carbide of crackle starting point when the extension processing of hole increases, the deterioration of hole expanding value.Therefore, C content be set as 0.020~ 0.070%.C content is preferably 0.025% or more, and more preferably 0.030% or more.In addition, C content be preferably 0.060% with Under, more preferably 0.050% or less.
Si:0.05~1.70%
Si has deoxidation effect, and has and inhibit the precipitation of iron series carbide such as cementite in material structure, facilitates Improve the effect of ductility and hole scalability.But content it is excessive when, be easy to happen ferrite transformation in high-temperature-range, exist therewith High-temperature-range is easy that the carbide containing Ti is precipitated.The precipitation of carbide in high-temperature-range is easy to produce the unevenness of amount of precipitation, as a result can The material of intensity, hole scalability etc. is brought to change.Therefore, Si content is set as 0.05~1.70%.
From the angle for inhibiting this oxide skin class defect of flakey, fusiform oxide skin to occur, Si content is preferably 0.06% or more, more preferably 0.08% or more.In addition, Si content is preferably 1.50% hereinafter, turning from chemistry is further increased The angle of corrosion resistance is set out after change treatability, coating, and more preferably 1.00% or less.
Mn:0.60~2.50%
Mn contributes to reinforced ferrite and improves the element of hardenability.On the other hand, a large amount of containing sometimes, hardenability will rise It more than needed for up to, is unable to fully ensure ferrite, in addition, slab crackle will be generated when casting.Therefore, Mn content is set as 0.60 ~2.50%.Mn content is preferably 1.00% or more, and more preferably 1.50% or more.In addition, Mn content be preferably 2.00% with Under, more preferably 1.80% or less.
Al:0.010~1.000%
Al has deoxidation effect in the same manner as Si and generates ferritic effect.On the other hand, can draw when content is excessive Embrittlement is played, and is easy blocking tundish nozzle in casting.Therefore, Al content is set as 0.010~1.000%.Al content is excellent It is selected as 0.015% or more or 0.020% or more, more preferably 0.025% or more or 0.030% or more.In addition, Al content is preferred For 0.800% hereinafter, 0.700% or less or 0.600% hereinafter, more preferably 0.500% or less or 0.400% or less.
N: greater than 0% and be 0.0030% or less
If N causes ductility to reduce containing much, can not only remain solid solution nitrogen, but also TiN, which can be precipitated, causes hole to extend Property decline.Therefore, N content is set as 0.0030% or less.N content is preferably 0.0025% or less.
P:0.050% or less
P is impurity contained in molten iron, local deteriorated ductility can be led to due to cyrystal boundary segregation, and keep weldability bad Change, therefore, it is desirable to few as far as possible.Therefore, P content is limited in 0.050% or less.P content is preferably 0.030% or less or 0.020% Below.It does not need to be particularly limited to lower limit, lower limit 0%.But the increased costs for excessively reducing content when will lead to refining, because This lower limit also can be set to 0.001%.
S:0.005% hereinafter,
S is also impurity contained in molten iron, and will form MnS causes local ductility and weldability to deteriorate, and therefore, it is desirable to as far as possible It is few.Therefore, S content is limited in 0.005% or less.In order to improve ductility or weldability, S content also can be set to 0.003% with It is lower or 0.002% or less.It does not need to be particularly limited to lower limit, lower limit 0%.But content is excessively reduced when will lead to refining Increased costs, therefore lower limit also can be set to 0.0005%.
Ti:0.015~0.170%
Ti has through carbonitride or is dissolved grain growth when Ti postpones hot rolling to keep the partial size of hot rolled plate fine Change, improves the effect of low-temperature flexibility.In addition, in the form of TiC in ferrite fine dispersion, to utilize precipitation strength And facilitate the high intensity of steel plate.But content it is excessive when, not only effect be saturated, but also be easy be precipitated belong to hard analysis The TiN of object out.Therefore, Ti content is 0.015~0.170%.Ti content be preferably 0.030% or more, 0.045% or more or 0.060% or more, more preferably 0.070% or more, 0.080% or more, 0.090% or more or 0.100% or more.In addition, Ti Content is preferably 0.160% or less, 0.150% or less, 0.140% or less, 0.130% or less or 0.120% or less.
Nb:0~0.100%
Nb has through carbonitride or is dissolved grain growth when Nb postpones hot rolling to keep the partial size of hot rolled plate fine Change, improves the effect of low-temperature flexibility.In addition, existing in the form of NbC, to facilitate steel plate using precipitation strength High intensity.Therefore, can contain as needed.But content it is excessive when, effect saturation and economy decline.Therefore, Nb contains Amount is set as 0.100% or less.As needed, Nb content can be 0.080% or less, 0.060% or less or 0.050% or less. Although its lower limit is 0%, in order to sufficiently obtain said effect, lower limit also can be set to 0.001% or 0.010%.
V:0~0.300%
V is the element improve by precipitation strength or solution strengthening with armor plate strength.It therefore, can be as needed Contain.But content it is excessive when, effect saturation and economy decline.Therefore, V content is set as 0.300% or less.According to need It wants, V content can be set to 0.200% hereinafter, 0.100% or less or 0.060% or less.Although its lower limit is 0%, in order to fill Get said effect, lower limit also can be set to 0.001% or 0.010%.
Cu:0~2.00%
Cu is the element improve by precipitation strength or solution strengthening with armor plate strength.It therefore, can be according to need Contain.But content it is excessive when, effect saturation and economy decline.Therefore, Cu content is set as 2.00% or less.In addition, When Cu content is big, the damage derived from oxide skin is generated on the surface of steel plate sometimes.Therefore, Cu content also can be set to 1.20% Below, 0.80% or less, 0.50% or less or 0.25% or less.Although its lower limit is 0%, in order to sufficiently obtain above-mentioned effect The lower limit of fruit, Cu content also can be set to 0.01%.
Ni:0~2.00%
Ni is the element improve by solution strengthening with armor plate strength.Therefore, can contain as needed.But It is that when content is excessive, effect is saturated and economy declines.Therefore, Ni content is set as 2.00% or less.In addition, Ni content is big When, it may cause deteriorated ductility.Therefore, Ni content also can be set to 0.60% or less, 0.35% or less or 0.20% or less.Though Its right lower limit is 0%, but in order to sufficiently obtain said effect, the lower limit of Ni content also can be set to 0.01%.
Cr:0~2.00%
Cr is the element improve by solution strengthening with armor plate strength.Therefore, can contain as needed.But It is that when content is excessive, effect is saturated and economy declines.Therefore, Cr content is set as 2.00% or less.In order to further increase Economy, the upper limit also can be set to 1.00%, 0.60% or 0.30%.Although its lower limit is 0%, in order to sufficiently obtain Effect is stated, the lower limit of Cr content also can be set to 0.01%.
Mo:0~1.00%
Mo is the element improve by precipitation strength or solution strengthening with armor plate strength.It therefore, can be according to need Contain.But content it is excessive when, effect saturation and economy decline.Therefore, Mo content is 1.00% or less.In order into One step improves economy, and the upper limit also can be set to 0.60%, 0.30% or 0.10%.Although its lower limit is 0%, in order to fill Get said effect, the lower limit of Mo content also can be set to 0.005% or 0.01%.
B:0~0.0100%
B can improve low-temperature flexibility and being segregated in crystal boundary, improving grain-boundary strength.Therefore, can contain as needed.But It is that when content is excessive, effect is saturated and economy declines.Therefore, B content is set as 0.0100% or less.In addition, B is strength Quenching element, when content is big, ferrite transformation is not carried out sufficiently in cooling sometimes, can not obtain enough retained austenites Body.Therefore, B content also can be set to 0.0050% or less, 0.0020% or less or 0.0015%.Although its lower limit is 0%, In order to sufficiently obtain said effect, the lower limit of B content also can be set to 0.0001% or 0.0002%.
Mg:0~0.0100%
Mg is the element that can control the form of non-metallic inclusion and improve processability, and the non-metallic inclusion will become The starting point of fracture becomes the reason of causing processability to deteriorate.Therefore, can contain as needed.But content it is excessive when, effect It is saturated and economy decline.Therefore, Mg content is set as 0.0100% or less.Although its lower limit is 0%, in order to sufficiently obtain Effect is stated, the lower limit of Mg content also can be set to 0.0001% or 0.0005%.
Ca:0~0.0100%
Ca is the element that can control the form of non-metallic inclusion and improve processability, and the non-metallic inclusion will become The starting point of fracture becomes the reason of causing processability to deteriorate.Therefore, can contain as needed.But content it is excessive when, effect It is saturated and economy decline.Therefore, Ca content is set as 0.0100% or less.Although its lower limit is 0%, in order to sufficiently obtain Effect is stated, Ca content is preferably 0.0005% or more.
REM:0~0.1000%
REM (rare earth element) is the element that can control the form of non-metallic inclusion and improve processability, the non-gold Belonging to field trash will become the starting point of fracture as the reason of causing processability to deteriorate.Therefore, can contain as needed.But When content is excessive, effect is saturated and economy declines.Therefore, REM content is set as 0.1000% or less.As needed, the upper limit Also it can be set to 0.0100% or 0.0060%.Although its lower limit is 0%, in order to sufficiently obtain said effect, REM content Lower limit also can be set to 0.0001% or 0.0005%.
Here, in the present invention, REM refers to 17 kinds of elements of total of Sc, Y and group of the lanthanides, the content of aforementioned REM refers to this The total content of a little elements.It should be noted that group of the lanthanides is industrially added in the form of mixed rare earth alloy.
Zr:0~1.000%
Co:0~1.000%
Zn:0~1.000%
W:0~1.000%
When having confirmed that Zr, Co, Zn and W are respectively 1.000% range below, without detriment to effect of the invention containing Fruit.Their upper limit also can be set to 0.300% or 0.10%.The total content of Zr, Co, Zn and W be preferably 1.000% or less or 0.100%.Containing for these elements is not required, lower limit 0%, but as needed, lower limit also can be set to 0.0001%.
Sn:0~0.050%
Without detriment to effect of the invention containing when having confirmed that Sn amount less.But once more than 0.05%, then hot rolling When there may be flaws.Therefore, Sn content is set as 0.050% or less.Containing for Sn is not required, lower limit 0%, but according to It needs, lower limit also can be set to 0.001%.
In the chemical composition of steel plate of the invention, surplus is Fe and impurity.
Here, " impurity " refers to: when industrial manufacture steel plate, by the raw materials such as ore, waste material, the various factors of manufacturing process Mixed ingredient is to the ingredient of the invention without allowing in the range of adverse effect.
(B) metallographic structure
The metallographic structure of steel plate of the invention is illustrated.It should be noted that metallographic structure is as follows in the present invention Tissue: in the section vertical with rolling direction of steel plate, when the width and thickness of steel plate is set to W and t, in distance The end face of the steel plate be 1/4W or 3/4W and the surface apart from the steel plate be 1/4t or the position of 3/4t at tissue.It needs to illustrate , in the following description, " % " expression " area % ".
Precipitation strength ferrite: 5~70%
It is ferrite obtained from pro-eutectoid ferrite precipitation strength (hereinafter also referred to " precipitation strength ferrite "), institute State pro-eutectoid ferrite to obtain as follows: with the nano-precipitation containing Ti, (carbide etc. of the Ti of fine precipitation, is also referred to as below For " fine Ti precipitate ") degree of supersaturation of the carbide of Ti when γ → α phase transformation occurs in cooling procedure after rolling makees For driving force, phase interface occurs in ferrite and is precipitated or generates homogeneous core for the carbide of Ti, thus fine point of the carbide of Ti Obtained from dissipating.Precipitation strength ferrite is excellent in order to balance uniform elongation and intensity and the tissue needed.
But the ferritic the area ratio of precipitation strength less than 5% when, it is difficult to take into account uniform elongation and intensity, another party Face, when more than 70%, although uniform elongation is excellent, local deteriorated ductility.Therefore, the ferritic the area ratio of precipitation strength is set It is 5~70%.From the angle for the balance for ensuring uniform elongation and intensity, the ferritic the area ratio of precipitation strength is preferably 7% or more, more preferably 10% or more.In addition, the ferritic the area ratio of precipitation strength is preferably 65% hereinafter, more preferably 60% or less.
Herein, in the present invention, precipitation strength ferrite refers to a number density of fine Ti precipitate contained in crystal grain It is 1.0 × 1016~50.0 × 1016A/cm3Ferrite.A number density of contained fine Ti precipitate in ferrite crystal grain Less than 1.0 × 1016A/cm3When, it is unable to fully obtain precipitation strength bring effect.On the other hand, of fine Ti precipitate Number density is more than 50.0 × 1016A/cm3When, not only intensity is saturated, but also ductility decrease.
That is, the ferritic the area ratio of precipitation strength is 5~70% to refer to: ferritic the area ratio is 5~70%, and iron element A number density of contained fine Ti precipitate is 1.0 × 10 in body crystal grain16~50.0 × 1016A/cm3。
In turn, the average equivalent circular diameter of fine Ti precipitate contained in the ferritic crystal grain of precipitation strength is preferably 1.00~3.00nm.This is because when the average equivalent circular diameter of fine Ti precipitate is less than 1.00nm, it is difficult to obtain being precipitated strong On the other hand the effect of change becomes coarse grain and average equivalent circular diameter is unable to ensure the fine of sufficient amount when being more than 3.00nm Ti precipitate.
Bainite: 30~95%
Bainite is the balance of intensity and local ductility and the tissue that needs in order to obtain, has the effect for inhibiting crevasse crack propagation Fruit.But bainite it is excessive when, ferrite is reduced, although local ductility is excellent, uniform elongation can be deteriorated significantly.Therefore, The area ratio of bainite is set as 30~95%.The area ratio of bainite is preferably 80% hereinafter, further paying attention to even elongation 70% or less is more preferably set as in the case where rate.
2% or less retained austenite:
High reaming steel is characterized in that existing by precipitation strength ferrite and bainite to ensure processability, and also Ensure high intensity, takes into account intensity and processability.But in the presence of there is no the thermodynamically stable of martensitic traoformation in steel plate In the case where retained austenite, the C concentration of the retained austenite is high, and when plate forges strain-induced transformation occurs for retained austenite And the hardness of the martensite generated can become excessively high, lead to the generation for encouraging gap.Therefore, retained austenite is advisable less as far as possible, Its area ratio is set as 2% or less.The area ratio of retained austenite is preferably 1.5% or less, 1% or less or 0.5% or less.It is not required to It is particularly limited to lower limit, lower limit 0%, 0% most preferably.
2% or less martensite:
High reaming steel is characterized in that, processability is ensured by the presence of precipitation strength ferrite and bainite, and It also assures high intensity, takes into account intensity and processability.But the area ratio of the martensite as hard tissue is when being more than 2%, with The strain of steel plate caused by plate forges increases, and martensite and ferritic boundary are easy to produce gap, become easy fracture.Cause This, the area ratio of martensite is set as 2% or less.The area ratio of martensite be preferably 1.5% or less, 1% or less or 0.5% with Under.It does not need to be particularly limited to lower limit, lower limit 0%.
1% or less pearlite:
Pearlite can become the starting point of fracture in hole extension forming, therefore its area ratio is set as 1% or less.Pearlite The area ratio is preferably 0.5% or less.The area ratio of pearlite preferably reduces as far as possible, and more preferably 0%.
The summation of precipitation strength ferrite and bainite: 95% or more
High reaming steel have take into account excellent uniform elongation and intensity precipitation strength ferrite and take into account intensity and The bainite of local ductility.Excellent intensity, uniform elongation and local ductility can be obtained as a result,.Precipitation strength ferrite When with the gross area rate of bainite less than 95%, these characteristics can be deteriorated.Therefore, precipitation strength ferrite and bainite Gross area rate is set as 95% or more.The gross area rate is preferably 97% or more, and more preferably 98% or more.
Herein, in the present invention, the area ratio of metallographic structure is found out as follows.As described above, first from the end apart from steel plate Face be 1/4W or 3/4W and the surface apart from steel plate be 1/4t or the position of 3/4t at acquire sample.Then, the sample is observed Rolling direction section (the so-called direction L section).
Specifically, carrying out the etching of nitric acid ethyl alcohol to sample, view of the optical microscopy at 300 μm of 300 μ m is used after etching It is observed Yezhong.Then, image analysis is carried out to obtained macrograph, obtains ferritic the area ratio A, pearly-lustre as a result, The gross area rate C of the area ratio B and bainite of body, martensite and retained austenite.
Then, LePera etching is carried out to the part of nitric acid ethyl alcohol etching, with optical microscopy at 300 μm of 300 μ m It is observed in the visual field.And image analysis is carried out to obtained macrograph, calculates retained austenite and martensite as a result, Gross area rate D.In turn, using the sample of 1/4 depth from rolling surface normal direction facing cut to plate thickness, pass through X-ray diffraction Measurement finds out the volume fraction of retained austenite.Since volume fraction is roughly equal with the area ratio, using aforementioned volume fraction as residual Stay the area ratio E of austenite.The area ratio that bainite is found out from the difference of the area ratio C and the area ratio D, from the area ratio E and the area ratio D Difference find out the area ratio of martensite.In this way, ferrite, bainite, martensite, retained austenite, pearl can be obtained The respective the area ratio of body of light.
In addition, the ferritic the area ratio of precipitation strength can be by being provided to EBSP-OIMTM (Electron Back Scatter Diffraction Pattern-Orientation Image Microscopy) Kernel Average Misorientation (core average orientation poor, KAM) method is found out.
Adjacent 6 (first approximate) and then its outside 12 of the KAM method to the pixel of some regular hexagon in measurement data Misorientation between a (second is approximate) or further 18 on the outside of it (third is approximate) pixel is averaged, by its average value As the pixel value at its center, this calculating is carried out to each pixel.Implementing the calculating in a manner of not across crystal boundary, The figure for showing the change in orientation in crystal grain can be produced.That is, the figure shows the strains changed based on local orientation in crystal grain Distribution.
About the ferritic analysis condition of precipitation strength in the present invention, in EBSP-OIMTM, come by third approximation in terms of Average orientation between adjacent pixel is poor, which is calculated as 1 ° of part below as precipitation strength ferrite.
Its reason are as follows: the ferritic carbonization for generating temperature field with Ti in the cooling after rolling of precipitation strength of the invention Using the degree of supersaturation of the carbide of Ti when γ → α phase transformation as driving force, the phase interface in ferrite is precipitated or is formed homogeneous to object The temperature field of core is consistent.Due to the pro-eutectoid ferrite of the polygon after phase transformation under high temperature be generated by diffusion phase transformation, thus Dislocation density is small, should tail off in crystal grain, therefore the intra-die difference of crystal orientation is small.Therefore, precipitation strength ferrite is also same It is small to become to sample crystal orientation difference.By the various investigation results of the implementations such as inventor so far it is found that being obtained by optical microphotograph sem observation To polygon ferrite the area ratio with as KAM method measure based on the approximate misorientation of third be 1 ° or less obtained from The area ratio in region is substantially uniform.
The measurement of the ferritic area fraction of precipitation strength progress specific as follows.It will be grasped in the same manner as described in structure observation The sample made and acquired is ground 30~60 minutes with colloidal silica abrasive, with 400 times of multiplying power, 256 μm of 160 μ m Region, the measuring condition implementation EBSP measurement for measuring 0.5 μm of step-length.EBSP-OIMTM method is by scanning electron microscope (SEM) it is carried out to the sample irradiating electron beam of high inclination, by the Kikuchi pattern that backscattering is formed with high-sensitivity camera in Shooting, by Computer Image Processing the short crystal orientation that point of irradiation is measured in device and software sharing.
The fine structure of bulk specimen surface and the quantitative resolution of crystal orientation, analysis area are able to carry out by EBSP method Domain is the region that can be observed with SEM, although also depending on the resolution ratio of SEM, minimum can be carried out with the resolution ratio of 20nm Analysis.Parsing takes hours, and is tens of thousands of equally spaced grid-like carry out by the area maps of desired analysis.If it is more Brilliant material is able to observe that the size of the crystal orientation distribution and crystal grain in sample.
In this way, 1 ° of part below is calculated as precipitation strength ferrite based on the approximate misorientation of third using above-mentioned, The ferritic area of precipitation strength is found out, finds out the ferritic the area ratio of precipitation strength relative to measurement area.
In addition, carrying out the observation of fine Ti precipitate as follows by three-dimensional atom probe mensuration.
Firstly, by cutting and electrolytic polishing method, and cooperate with electrolytic polishing method add with focused ion beam as needed Engineering method makes acicular sample by measurement object sample.In three-dimensional atom probe measurement, cumulative data can be constructed again, be made It is found out for the practical atom distributed image in real space.In the case where the fine Ti precipitate of Na-Cl structure, due to structure cell It is 4.33 angstroms, therefore the interatomic distance of Ti and Ti is 4.33 × √ 2=6.1 angstrom.
Therefore, these Ti atoms are judged there are in the case where multiple Ti atoms in substantially same coordinate position (7 angstroms or less) In same precipitate, it is judged as that the number of the Ti atom in same precipitate is counted to this, there are 50 for the number When above, which is defined as fine Ti precipitate.
The size of above-mentioned fine Ti precipitate is following value: it is assumed that fine Ti precipitate be it is spherical, observed by constituting The atomicity of the Ti of fine Ti precipitate and the lattice constant of fine Ti precipitate and calculated equivalent diameter.
The Ti atom number for the fine Ti precipitate that use described below is obtained by three-dimensional atom probe mensuration finds out analysis The method of equivalent diameter (diameter) R of object out.
Although the quantity N of whole atoms with three-dimensional atom probe mensuration measurement object sample, in fact, three-dimensional former Sub- probe measurement can not detect the quantity N of whole atoms of subject sample.Due to the atom inspection intrinsic there are each device It is existing former therefore to calculate supposition by actual measured value n by survey rate α (quantity/atom sum of=atom detected) The quantity N of son.That is, the total N=n/ α of atom.It should be noted that the verification and measurement ratio α of measuring device is 0.35 in the present invention.
Then, for the quantity N of the atom, in the case where the Ti precipitate of Na-Cl structure, if there are 8 in structure cell Ti atom calculates equivalent diameter by following formula in addition, setting the lattice constant a of Na-Cl structure as 4.33 angstroms.
Equivalent diameter (diameter) R={ (6/8) (1/ π) Na3}(1/3)
For example, equivalent diameter is substantially calculated as 1nm when Ti quantity is 50.In the present invention, any measurement 30 with The equivalent diameter (diameter) of upper fine Ti precipitate, finds out its average value.
A number density of fine Ti precipitate be using measure the visual field as denominator, using the quantity of fine Ti precipitate as point Son and find out.In the measurement of a number density, by 10nm (plate thickness direction t) × 40nm (board width direction W) × 60nm (plate Length direction L) 5 visuals field of perimetry more than, find out its number density (a/cm3) average value.
In addition, in the present invention, also being carried out to the existence of TiN defined below.
The average equivalent circular diameter of TiN: 1.0~10.0 μm
When TiN is big, the strain of steel plate caused by forging with plate increases, and gap existing for grain boundaries is easy to combine, therefore, The average equivalent circular diameter of TiN is 10.0 μm or less.In order to more reliably ensure these effects, the average equivalent circular diameter of TiN Preferably 8.0 μm hereinafter, more preferably 5.0 μm or less.
It should be noted that since TiN is smaller the more preferred, the average equivalent circular diameter of TiN is under no setting is required originally Limit.But in the observation method of aftermentioned TiN, when the equivalent diameter of TiN is less than 1.0 μm, identify whether to become for TiN It obtains difficult.Therefore, only equivalent diameter is 1.0 μm or more in the present invention and is considered as TiN as measurement object.Therefore, TiN Average equivalent circular diameter be 1.0 μm or more.
The average equivalent circular diameter (diameter) of TiN is found out in the following way.As described above, firstly, from apart from steel plate End face is 1/4W or 3/4W and the surface apart from steel plate are 1/4t or the station acquisition sample of 3/4t.Then, the sample is ground Rolling direction section (the so-called direction L section), is observed with the state not etched.Specifically, with optical microscopy with 1000 times of multiplying power shoots microstructure picture, passes through the observation microstructure picture such as range estimation or image processing apparatus.
In microstructure picture, for can determine that the tissue for TiN, its equivalent diameter (diameter) is found out, only by this etc. Effect circular diameter (diameter) is 1.0 μm or more and is considered as TiN.Also, by 60 μm (rolling direction L) × 40 μm (plate thickness direction t) The visual field observe 20 visuals field more than, value obtained from the equivalent diameter (diameter) to whole TiN is averaged is as TiN Average equivalent circular diameter (diameter).
The average value of the shortest distance between adjacent TiN: 10.0 μm or more
In order to avoid TiN and the Void growth of ferritic interface generation, gap be combined with each other and further become big sky Gap needs will ensure that the distance between a certain amount of TiN.Therefore, the average value of the distance between adjacent TiN be set as 10.0 μm with On.
From the angle being cracked caused by Void growth is inhibited, above-mentioned average value is preferably 15.0 μm or more, more Preferably 20.0 μm or more.Although the upper limit not especially setting, since the precipitation of a degree of TiN is inevitable, Therefore, the average value of the shortest distance between adjacent TiN is preferably set to 1000 μm or less.
The average value of the shortest distance between adjacent TiN is found out in the following way.Any 20 TiN are selected, are measured respectively It calculates its average value at a distance from immediate TiN.It should be noted that the measurement of the shortest distance between TiN and average The measurement of equivalent diameter similarly calculates.
(C) mechanical property
The standard deviation of nano hardness: 1.0GPa or less
Difference by reducing the deformability of hard tissue and soft tissue generates to reduce in the interface of two tissues Gap, and then by pulling open gapping interval, be able to suppress gap in conjunction with and be grown to cracking.For this purpose, hard by reducing as far as possible Nano hardness corresponding to difference phase of the matter tissue with the deformability of soft tissue is poor, is able to suppress gap generation.In this hair In bright, as the index of soft tissue and the difference of hardness of hard tissue, using the standard deviation of the nano hardness in specimen cross section.
The TriboScope/TriboIndenter that such as Hysitron company manufacture can be used in nano hardness is surveyed Amount.The nano hardness more than at 100 is arbitrarily measured with the load of 1mN, the standard deviation of nano hardness can be calculated by its result Difference.
In order to reduce the difference of hardness of soft tissue and hard tissue, gap be inhibited to generate, the standard deviation of nano hardness is small Person is preferred, and is set as 1.0GPa or less.The standard deviation of nano hardness is preferably 0.8GPa or less.
Tensile strength: 780MPa or more
Steel plate of the invention preferably has the tensile strength of the 780MPa or more same with previous high reaming steel.It stretches strong The upper limit of degree is not necessarily to special provision, can be set to 1200MPa, 1150MPa or 1000MPa.Wherein, tensile strength refers to JIS Z The tensile strength of 2241 (2011).
The product of uniform elongation and tensile strength: 7000MPa% or more
If uniform elongation is small, when compression moulding, is easy to happen the reduction of plate thickness caused by constriction, becomes compacting and splits The reason of line.In order to ensure press formability, uniform elongation (u-EL) and the product of tensile strength (TS) are preferably satisfied: TS × U-EL >=7000MPa%.Wherein, about uniform elongation, in the test as defined in JIS Z 2241 (2011), in nominal stress In the relationship of σ n and apparent strain ε n, by the nominal for the point that value when carrying out differential to nominal stress σ n with apparent strain ε n is 0 When strain is set as ε n0, indicated with following formula.
Uniform elongation (u-EL)=ln (ε n0+1)
The product of hole expansibility and tensile strength: 50000MPa% or more
If hole scalability is poor, material flowability is poor when stretch flange formability is processed, it is possible to create crackle.Therefore, in order to true Hole scalability is protected, hole expansibility (λ) and the product of tensile strength (TS) preferably satisfy: (TS) × (λ) >=50000MPa%.Wherein, Hole expansibility (λ) indicates (λ) for the hole expansibility that the test method according to JIS Z 2256 (2010) obtains.
Equivalent plastic strain: 0.9 or more
Equivalent plastic strain be by pure shear test shear stress σ s and the relationship of shear plasticity strain stress sp be converted to Obtained from the relationship of tensile stress σ in the different one directional tensile test of mode of texturing and elongation strain ε, assume that it is each to The relationship of same sex hardening law and plastic work done conjugation, and be converted to used as the conversion coefficient of constant (κ).
Here, isotropic hardening law refers to: it is assumed that the shape of yielding curve is not become straining progress Change the processing hardening law of (being expanded into similar shape).The relationship of plastic work done conjugation refers to: being expressed as only moulding in processing hardening No matter the function of property function, which kind of mode of texturing assign identical plastic work done (σ × ε), identical processing hardening amount is shown Relationship.
Thus, it is possible to by pure shear test shear stress and shear plasticity strain be respectively converted into one directional tensile test Tensile stress and elongation strain.The relationship is shown as follows.
Shear stress σ s × κ in tensile stress σ (conversion)=pure shear test in one directional tensile test
Shear plasticity strain stress sp/ κ in elongation strain ε (conversion)=pure shear test in one directional tensile test
Then, the side of the relationship of tensile stress and elongation strain is similar to the relationship of shear stress and shear plasticity strain Formula finds out conversion coefficient κ.For example, conversion coefficient κ can be found out according to sequence below.Firstly, finding out simple tension examination in advance The relationship of elongation strain ε (measured value) and tensile stress σ (measured value) in testing.Then, cutting in unidirectional shearing test is found out The relationship of shear strain ε s (measured value) and shear stress σ s (measured value).
Then, change κ, find out the elongation strain ε (conversion) acquired by shear stress ε s (measured value) in advance and by cutting The tensile stress σ (conversion) that shearing stress σ s (measured value) is acquired, and elongation strain ε (conversion) is found out positioned at 0.2% to uniformly stretching Tensile stress σ (conversion) when between long rate (u-EL).Find out tensile stress σ (conversion) at this time and tensile stress σ (actual measurement Value) error, find out the least κ of error using least square method.
Shear plasticity strain stress when equivalent plastic strain ε eq is defined as fracture in pure shear test using the κ found out Sp (fracture) is converted to the value when elongation strain ε in pure extension test.
Steel plate of the invention is characterized in that, good in the processing characteristics being forged under the high strain region of representative with plate, Meeting equivalent plastic strain ε eq is 0.50 or more.The equivalent plastic strain of previous TRIP steel is at maximum up to 0.30 or so, thus Confirm that the plate forgeability of steel plate of the invention is good.
(D) size
Plate thickness: 1.0~4.0mm
For steel plate of the invention mainly with automobile etc. for main application, plate thickness range is mainly 1.0~4.0mm.Therefore, Plate thickness range can be 1.0~4.0mm, and as needed, lower limit can be set to 1.2mm, 1.4mm or 1.6mm, and the upper limit can be set For 3.6mm, 3.2mm or 2.8mm.
(E) manufacturing method
Inventors etc. are confirmed by research so far, by carry out in order it is following shown in (a) to (f) manufacture work Sequence can manufacture hot rolled steel plate of the invention.Hereinafter, each manufacturing process is described in detail.
(a) melting process
Manufacturing method before hot rolling is not particularly limited.That is, the melting and then based on blast furnace or electric furnace etc. carries out Various double refinings, by become it is above-mentioned at being grouped as in a manner of be adjusted.Then, pass through common continuously casting, thin plate The methods of base casting manufacture slab.As long as using waste material in the feed at this point, can be controlled to composition range of the invention Deng even.
(b) heating process
Hot rolling is implemented to the slab of manufacture, hot rolled steel plate is made.When carrying out hot rolling, slab is heated first.In heating process In, by SRTmin DEG C or more shown in heating of plate blank to following (i) formula and 1260 DEG C of temperature below.The continuously casting the case where Under, it heats, can not also especially cool down, and then continuously casting is heated again after both being temporarily cooled to low temperature.In This, SRTmin refers to the solid solubility temperature of TiC.
SRTmin=7000/ { 2.75-log (Ti × C) } -273 (i)
Wherein, the symbol of element in above-mentioned formula indicates content (quality %) of each element in hot rolled steel plate, is not containing In the case where substitute into 0.
(c) continuously hot rolling process
After heating, roughing and multistage finish rolling later are implemented to the slab that takes out from heating furnace.In order to make the precipitation containing Ti Object is not precipitated, and the end temperature of roughing is set as 1100 DEG C or more.In addition, as described above, multistage finish rolling is with 3 grades or more of multistage The mode of (such as 6 grades or 7 grades) continuous rolling carries out.Also, (effectively accumulation is answered with the accumulation strain in last 3 grades of rolling Become) reach 0.01~0.10 mode and carries out multistage finish rolling.
As described above, effectively accumulation strain is the index for considering following factor: temperature, rolling bring steel when rolling The static crystal grain diameter restored occurs over time after rolling for the variation of crystal grain diameter caused by the reduction ratio of plate, crystal grain Variation.Effective accumulation strain (ε eff) can be found out by following formula.
Effective accumulation strain (ε eff)=Σ ε i (ti, Ti) (iii)
Σ in above formula (iii) indicates the summation for being directed to i=1~3.
Wherein, i=1 indicates the 1st grade of rolling (that is, final level rolling) reciprocal in multistage finish rolling, and i=2 indicates 2nd grade reciprocal Rolling, i=3 indicate 3rd level rolling reciprocal.
Here, ε i is expressed from the next in respectively rolling shown in i.
ε i (ti, Ti)=ei/exp ((ti/ τ R)2/3)···(iv)
Ti: the time (s) since i-stage reciprocal rolling until the primary cooling after final level rolling
Ti: the rolling temperature (K) of i-stage rolling reciprocal
Ei: logarithmic strain when being depressed in i-stage rolling reciprocal
Ei=| ln 1- (i-stage into side plate thickness-i-stage submitting side plate thickness)/(i-stage enters side plate Thickness) } |
=| ln { (the submitting side plate thickness of i-stage)/(the entrance side plate thickness of i-stage) } | (v)
τ R=τ 0exp (Q/ (RTi)) (vi)
0=8.46 × 10 τ-9(s)
Q: to constant=183200 (J/mol) of the mobile relevant activation evergy of the dislocation of Fe
R: gas constant=8.314 (J/ (Kmol))
By limiting effective accumulation strain derived in this way, target microscopic structure can be obtained, and reduce nano hardness It is uneven.As the Void growth that as a result, it is possible to inhibit to generate in the interface of hard tissue and soft tissue, can be realized i.e. Make Void growth also be difficult to combine, steel plate be not cracked carrying out plate and forging, that plate forgeability is excellent can be obtained.
For the end temperature of multistage finish rolling, i.e. the end temperature of continuously hot rolling process, found out using by following (ii) formulas Ar3, it is set as Ar3The temperature of+30 DEG C of (DEG C) or more is advisable.Because this makes it possible to obtain the precipitation in the present invention as target is strong Change ferrite and bainite.
Ar3=970-325 × C+33 × Si+287 × P+40 × Al-92 × (Mn+Mo+Cu) -46 × (Cr+Ni) (ii)
Wherein, the symbol of element in above-mentioned formula indicates content (quality %) of each element in hot rolled steel plate, is not containing In the case where substitute into 0.
(d) first (acceleration) cooling process
After multi-level oil rolls, start the cooling for carrying out resulting hot rolled steel plate after 1.00~5.00s.Also, from rolling System terminates temperature and starts until 650~750 DEG C of temperature, is cooled down with the average cooling rate of 10 DEG C/s or more, thereafter, 1~10s is kept in an atmosphere.
If begun to cool after continuously hot rolling process less than 1.00s, ferrite transformation is promoted, and is not only existed It is unable to get target bainite the area ratio, and precipitate coarsening in final microscopic structure, is unable to get effect of the invention Fruit.On the other hand, if it exceeds 5.00s is begun to cool, then ferrite transformation postpones, and is unable to get target precipitation strength ferrite The area ratio.
In addition, being easy to generate pearlite when the average cooling rate in the first cooling process is less than 10 DEG C/s.Another party The upper limit in face, cooling velocity is not particularly limited, but in order to avoid supercooling, is preferably set as 300 DEG C/s or less.In turn, big When holding temperature in gas is less than 650 DEG C, it is easy bainite, bainite the area ratio becomes larger.On the other hand, in an atmosphere When temperature being kept to be more than 750 DEG C, it is easy to generate pearlite.
It should be noted that as mentioned herein the air that includes hot rolled steel plate in cooling equipment of the holding in atmosphere it is cooling or Cooling is limited in minimum, at this time preferably the lower limit of cooling velocity is 0 DEG C/s, and the upper limit is 8 DEG C/s.
(e) second (acceleration) cooling process
In atmosphere keep after, from 600~740 DEG C of temperature range, with the average cooling rate of 10 DEG C/s or more into Row cooling.When cooling start temperature is less than 600 DEG C, ferrite transformation is underdeveloped, and the precipitation of fine Ti precipitate also becomes It is insufficient.On the other hand, when cooling start temperature is more than 740 DEG C, develops excessively there are ferrite transformation and generate pearlite The possibility for causing hole scalability to deteriorate.Additionally, there are the possibility that fine Ti precipitate coarsening causes intensity to decline.
In addition, there is also generate pearlite to lead to the possibility of hole scalability deterioration when average cooling rate is less than 10 DEG C/s. The upper limit of average cooling rate is not particularly limited, but as worrying that thermal strain caused by thermal deviation causes camber of sheet, Being set as 1000 DEG C/s or less is advisable.
(f) coiling process
Thereafter, cooling hot rolled steel plate is batched with 450~650 DEG C of coiling temperature.Condition after coiling process is not special It does not limit.
(F) steel forged part
The hot rolled steel plate plate forgeability obtained as described above is excellent, therefore by carrying out plate forging etc. to the hot rolled steel plate Forging processing can obtain the forged part of the high-intensitive complicated shape of the needs that can not be obtained in the past.
Hereinafter, carrying out more specific description to the present invention by embodiment, but the present invention is not limited to these Examples.
Embodiment 1
Melting has the steel of chemical composition shown in table 1, manufactures slab, after carrying out hot rolling with condition shown in table 2, carries out cold But, it then batches, manufactures hot rolled steel plate.The plate thickness of obtained hot rolled steel plate is as shown in table 3.
[table 1]
[table 2]
Table 2
*Indicate present invention provide that range outside
[table 3]
[metallographic structure]
Metallographic structure observation is carried out to obtained hot rolled steel plate, carries out the measurement of the area ratio of each tissue.Specifically, first First in the section vertical with the rolling direction of steel plate, apart from the steel plate when from the width and thickness for setting steel plate being respectively W and t The position that end face is 1/4W and the surface apart from the steel plate is 1/4t cuts the test film of metallographic structure observation.
Then, the etching of nitric acid ethyl alcohol, etching are carried out to the rolling direction section of above-mentioned test film (the so-called direction L section) It is observed in 300 μm of 300 μ m of the visual field with optical microscopy afterwards.Then, image analysis is carried out to gained macrograph, So as to find out the gross area of ferritic the area ratio A, the area ratio B of pearlite and bainite, martensite and retained austenite Rate C.
Then, Lepera etching is carried out to the part after the etching of nitric acid ethyl alcohol, with optical microscopy in 300 μ m, 300 μ It is observed in the visual field of m.Then, image analysis is carried out to gained macrograph, to calculate retained austenite and martensite Gross area rate D.In turn, it mills using from rolling surface normal direction surface to the sample of 1/4 depth of plate thickness, passes through X-ray Diffraction and the volume fraction for finding out retained austenite.Since volume fraction is almost equal with the area ratio, by aforementioned volume fraction The area ratio E as retained austenite.Difference based on the area ratio C and the area ratio D finds out the area ratio of bainite, is based on the area ratio The difference of E and the area ratio D finds out the area ratio of martensite.In this way, having found out ferrite, bainite, martensite, retained austenite The respective the area ratio of family name's body, pearlite.
The area ratio ferritic for precipitation strength, as described above, by above-mentioned test film colloidal silica abrasive After being ground, with 400 times of multiplying power, 160 × 256 μm of the visual field, the measuring condition progress EBSP survey for measuring 0.5 μm of step-length Amount, is found out by KAM method.
Also as described above for fine Ti precipitate, electrolytic polishing is carried out to above-mentioned test film, passes through three-dimensional atom probe Mensuration measures, and finds out its equivalent diameter, a number density.
Also as described above for TiN, 20 views are observed with 1000 times of multiplying power, 60 × 40 μm of the visual field to above-mentioned test film Open country finds out the average equivalent circular diameter of TiN by image procossing.In addition, metallurgical microscopes pair and survey of organization's phase with 500 times Same position is observed, and the mutual shortest distance of TiN is found out.
[mechanical property]
Tensile strength characteristics (tensile strength (TS), uniform elongation (u-EL), hole expansibility (λ)) in mechanical property are with such as Under type is evaluated: using times for being 1/4W or 3/4W apart from one end of plate when board width is set as W, on board width direction The 5 of the JIS Z 2241 (2011) acquired at one position with the direction (width direction) orthogonal with rolling direction for length direction Number test film, and evaluated according to JIS Z 2241 (2011).About hole expansibility, from the acquisition position phase with tension test sheet Same station acquisition test film is evaluated according to the test method recorded of JIS Z 2,256 2010.
In turn, pure shear test is carried out by following sequence, equivalent plastic strain is found out based on its result.
The test film of pure shear test be by the plate of steel plate is wide be set as W when, on plate width direction apart from one end of plate be 1/ It is acquired at any position of 4W or 3/4W with the direction (width direction) orthogonal with rolling direction for length direction.(a) of Fig. 1 In an example of test film is shown.For the test film of pure shear test shown in Fig. 1, in such a way that plate thickness is 2.0mm Equably be ground two sides and keep plate thickness consistent, be processed into the width direction of steel plate be 23mm, steel plate rolling direction on be The rectangular test piece of 38mm.
The long side (rolling direction) of test film is clamped from the clamping part 2 of two sides, the clamping part 2 of the two sides is in short side It is respectively 10mm on direction (width direction), in the shearing width (shear-deformable generating unit 1) of the center setting 3mm of test film. It should be noted that, without grinding, directly being tested in the case where plate thickness is less than 2.0mm with the plate thickness of script.Separately Outside, in the center of test film, upper linear mark is drawn along short side direction (width direction) with pen etc..
Then, with clamped long side mobile in a manner of mutually opposing in longitudinal direction (rolling direction), thus Shear stress σ s is loaded, test film is applied shear-deformable.It is shown in (b) of Fig. 1 and has carried out the one of shear-deformable test film A example.Shear stress σ s is the nominal stress found out by following formula.
Shear stress σ s=shearing force/(length × test film plate thickness of the test film of the rolling direction of steel plate)
It should be noted that the length of test film and plate thickness do not change in shearing test, it can be considered that shearing Nominal stress ≈ shears true stress.In shearing test, shot with the straight line that CCD camera describes test film center, Measure its gradient θ ((b) referring to Fig.1).Based on gradient θ, the shearing generated because shear-deformable is found out using following formula Strain stress s.
Shear strain ε s=tan (θ)
It should be noted that having used pure shear test machine (maximum displacement 8mm) in pure shear test.Therefore, it tests The stroke (displacement) of machine is limited.In addition, relying on sometimes and once cutting due to generating cracking in the end of test film or clamping part Test can not be carried out until test film is broken by cutting test.Therefore, repeat applying for shearing test load as described above, using The clamping part end of test film is cut off and the " more of sequence of operations such as applies again for straight line, load by load lotus, removal load Grade shear test method ".
In order to which the shearing test result of the multistage is together in series, commented as a continuous pure shear test result Valence finds out as follows and subtracts the shearing elasticity for considering modulus of shearing from the shear strain (ε s) that shearing test at different levels obtains and answer Become the strain of shear plasticity obtained from (ε se) (ε sp), shear plasticity strain (ε s) integration in each stage is connected as one.
Shear plasticity strain stress sp=shear strain ε s- shearing elasticity strain stress se
Shearing elasticity strain stress se=σ s/G
σ s: shear stress
G: modulus of shearing
Here, G=E/2 (1+ ν) ≈ 78000 (MPa).
E (Young's modulus (longitudinal elastic coefficient))=206000 (MPa)
Poisson's ratio (ν)=0.3
In pure shear test, test is carried out until test film fracture.In such manner, it is possible to track shear stress σ s and cut Cut the relationship of plastic strain ε sp.Also, shear plasticity strain when test film is broken is ε spf.
Shear plasticity strain stress spf when being broken based on shear stress σ s obtained in above-mentioned pure shear test and test film Relationship equivalent plastic strain ε eq is found out using conversion coefficient κ by preceding method.
Then, the measurement of the standard deviation of nano hardness is carried out.The test film of metallographic structure observation is regrind, with The load (apply load 10s, remove load 10s) of 1mN, for apart from surface of steel plate being plate in the section parallel with rolling direction The position (portion 1/4t) of 1/4 depth of thickness t, with the measured zone of 5 μm of 25 μm of 25 μ ms of interval measurement.It is calculated by its result The average value of nano hardness and the standard deviation of nano hardness.What the measurement of nano hardness was manufactured using Hysitron company TriboScope/TriboIndenter is implemented.
These measurement results are shown in table 3 together.
By table 3 it can also be seen that if it is hot rolled steel plate of the invention, then can obtain with tensile strength (TS) 780MPa Above, product (TS × u-EL) 7000MPa% or more, the hole expansibility λ of uniform elongation u-EL and tensile strength TS and stretching Product (TS × λ) 50000MPa% or more of intensity TS, hot rolled steel plate with equilibrium response.In addition, confirming this hair Bright hot rolled steel plate make equivalent plastic strain also above 0.90 (90%) and can also receiving plate forge the processing of contour strain domain Steel plate.
Industrial availability
In accordance with the invention it is possible to obtain maintaining the good hole scalability of the basic function as high reaming steel and The excellent hot rolled steel plate of plate forgeability.Therefore, hot rolled steel plate of the invention can be widely applied for mechanical part etc..Particularly by suitable Steel plate processing for plate forging etc. with the processing of Large strain domain, can obtain its significant effect.
Description of symbols
1: shear-deformable generating unit
2: clamping part

Claims (6)

1. a kind of hot rolled steel plate, wherein
The chemical composition of steel plate is calculated as with quality %
C:0.020~0.070%,
Si:0.05~1.70%,
Mn:0.60~2.50%,
Al:0.010~1.000%,
N: greater than 0% and for 0.0030% or less,
P:0.050% or less,
S:0.005% or less,
Ti:0.015~0.170%,
Nb:0~0.100%,
V:0~0.300%,
Cu:0~2.00%,
Ni:0~2.00%,
Cr:0~2.00%,
Mo:0~1.00%,
B:0~0.0100%,
Mg:0~0.0100%,
Ca:0~0.0100%,
REM:0~0.1000%,
Zr:0~1.000%,
Co:0~1.000%,
Zn:0~1.000%,
W:0~1.000%,
Sn:0~0.050% and
Surplus: Fe and impurity,
In the section vertical with rolling direction of the steel plate, when the width and thickness of the steel plate is set to W and t, End face apart from the steel plate be 1/4W or 3/4W and the surface apart from the steel plate be 1/4t or the position of 3/4t at metallographic Tissue is calculated as with area %
Ferrite: 5~70%,
Bainite: 30~95%,
Retained austenite: 2% or less,
Martensite: 2% or less and
Pearlite: 1% hereinafter, also,
The summation of ferrite and bainite: 95% or more,
The ferrite has the precipitate containing Ti in crystal grain,
A number density of the precipitate containing Ti is 1.0 × 1016~50.0 × 1016A/cm3,
Contain TiN precipitate in the steel plate,
The average equivalent circular diameter of the TiN precipitate is 1.0~10.0 μm,
The average value of the shortest distance between the adjacent TiN precipitate is 10.0 μm or more,
The standard deviation of the nano hardness of the hot rolled steel plate is 1.00GPa or less.
2. hot rolled steel plate according to claim 1, wherein the average equivalent circular diameter of the precipitate containing Ti is 1.00 ~3.00nm.
3. according to claim 1 or hot rolled steel plate as claimed in claim 2, wherein
Tensile strength is 780MPa or more,
The product of uniform elongation and tensile strength is 7000MPa% or more,
The product of hole expansibility and tensile strength is 50000MPa% or more.
It is manufacturing claims 1 to the hot rolling described in any one of claim 3 4. a kind of manufacturing method of hot rolled steel plate The method of steel plate, wherein
For the slab with chemical composition described in claim 1, successively implement heating process, continuously hot rolling process, first Cooling process, the second cooling process and coiling process,
In the heating step, by SRTmin DEG C or more shown in the heating of plate blank to following (i) formula and 1260 DEG C or less Temperature,
The continuously hot rolling process includes the multistage finish rolling of roughing and 3 grades or more,
The end temperature of the roughing is 1100 DEG C or more,
The accumulation strain in last 3 grades of rolling in the multistage finish rolling is 0.01~0.10,
It is the Ar found out by following (ii) formulas that the rolling of the multistage finish rolling, which terminates temperature,3+ 30 DEG C or more of temperature,
It in first cooling process, after the multi-level oil rolls, is begun to cool after 1.00~5.00s, from described Rolling terminates temperature and rises until 650~750 DEG C of temperature range, is cooled down with the average cooling rate of 10 DEG C/s or more, Later, 1~10s is kept in an atmosphere,
In second cooling process, after being kept in the atmosphere, from 600~740 DEG C of temperature range, with 10 DEG C/average cooling rate of s or more cooled down,
In the coiling process, batched with 450~650 DEG C of coiling temperature；
SRTmin=7000/ { 2.75-log (Ti × C) } -273 (i)
Ar3=970-325 × C+33 × Si+287 × P+40 × Al-92 × (Mn+Mo+Cu) -46 × (Cr+Ni) (ii)
Wherein, the symbol of element in above-mentioned formula indicates quality % content of each element in hot rolled steel plate, the case where not containing It is lower to substitute into 0.
5. a kind of steel forged part, the hot rolled steel plate as described in any one of claim 1 to claim 3 obtain.
6. a kind of manufacturing method of steel forged part, wherein
At least implement forging processing to hot rolled steel plate described in any one of claim 1 to claim 3.
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