CN109957716A - Steel plate and preparation method thereof is precipitated in a kind of single ferrite of the high hole expandability of high intensity - Google Patents
Steel plate and preparation method thereof is precipitated in a kind of single ferrite of the high hole expandability of high intensity Download PDFInfo
- Publication number
- CN109957716A CN109957716A CN201711400577.1A CN201711400577A CN109957716A CN 109957716 A CN109957716 A CN 109957716A CN 201711400577 A CN201711400577 A CN 201711400577A CN 109957716 A CN109957716 A CN 109957716A
- Authority
- CN
- China
- Prior art keywords
- steel plate
- steel
- precipitated
- ferrite
- hole expandability
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Pending
Links
Classifications
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0226—Hot rolling
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium 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
- C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium 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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/005—Ferrite
Landscapes
- 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)
Abstract
The present invention discloses a kind of single ferrite of the high hole expandability of high intensity and steel plate and preparation method thereof is precipitated.Contain C:0.05%~0.12%, Si:0.1%~0.7%, Mn:0.8%~2.2%, Ti:0.05%~0.10%, P < 0.035%, S < 0.035%, Als:0.015%~0.060% in steel, Ca:0.0015%~0.0050%, Mg < 0.0050%, N < 0.005%, also contain at least one of Cr:0.15%~0.3%, Mo:0.05%~0.3% and at least one of Nb:0.02%~0.06%, V:0.05%~0.25%, remaining is Fe and inevitable impurity.Feed silico-calcium linear velocity >=3.5m/s, molten steel overheat≤30 DEG C；1150~1250 DEG C of slab heating temperature, multi- pass rolling total reduction >=80%, 850~950 DEG C of hot rolling finishing temperature, 15~45 DEG C/s of cooling velocity after rolling, 550~650 DEG C of coiling temperature.Finished steel plate has good reaming performance.
Description
Technical field
The invention belongs to steel manufacturing technology fields, and in particular to a kind of using controlled rolling and control type of cooling production
The method that steel is precipitated in reaming ferrite of good performance.
Background technique
Prospect in Modern Auto Manufacture Industry is dedicated to improving safety and the collision performance of automobile, fuel consumption is reduced, to improve
The influence of riding safety and reduction to environment.The research and development application of high-strength automobile steel is the effective means of automobile lightweight,
The development trend for meeting young mobile energy conservation, consumption reduction, environmental protection and safety is the dominant direction of prospective material technology development.But
It is the increasingly raising with Automobile Design requirement, part shape is more complicated, elongation percentage and reaming performance requirement to material
Increase therewith.It is well known that the obdurability of steel material is conflicting, therefore have both intensity and formability and hole expandability
The novel steel material of energy is the important species of autobody sheet.
It is 590MPa hot rolling high-chambering steel plate that the patent application of publication number CN101928881A, which discloses a kind of tensile strength,
Production method.The chemical component of the invention steel grade are as follows: C:0.02%~0.10%, Si:0~1.6%, Mn:0.8%~
2.0%, P: < 0.035%, S: < 0.010%, Al:0.025%~0.060%, N≤0.0060%, Nb 0~0.10%, Ti:0
~0.04%, Ca:0~0.0050%, remaining is Fe and inevitable impurity.By being added in C-Si-Mn component system
Nb, Ti element use sub-sectional cooling mode after hot rolling, and high reaming steel tensile strength obtained is in 590MPa or more, hole expansibility
It is 75% or more.Hole expansibility is functional, is suitable for manufacturing complex-shaped Automobile Chassis Parts.But the intensity of the steel grade is inclined
It is low, and two-part section cooling is used after the patent hot rolling, each section of cooling rate is required strictly, and in actual production, hot rolling
Strip belt speed changes greatly, is unable to accurately control each section of cooling rate, and the fluctuation of steel plate actual temperature is big, and it is uneven to easily lead to the logical volume performance of coil of strip
Even, head, middle and end performance inconsistency is big.
The patent of invention of publication number CN103602895A discloses a kind of system of tensile strength 780MPa grades of high-chambering steel plates
Make method.The invention contains Si, Mn, Nb, Ti, ingredient using low-carbon, without the elements such as Mo, Cr, by control purity of steel and
Using the method for refined crystalline strengthening, the high reaming steel of uniform ferrite homogeneous structure, tensile strength > 780MPa, reaming have been obtained
Rate >=50%.Single form ferritic structure yield strength, tensile strength and hole expansibility are lower.
The patent of invention of publication number CN102676926A discloses a kind of complex phase steel plate and its manufacturing method, the patent disclosure
A kind of production method of bainite+martensite (a small amount of ferrite may be contained) complex phase steel plate.The steel grade is by using cheap
Silicon addition, Mn and a small amount of Nb, make full use of the stronger water cooling ability of modern Hot Rolling Mill and a variety of water cooling modes, strictly
The cooling velocity in cooling procedure and cooling time are controlled, bainite+martensite (a small amount of ferrite may be contained) complex phase is obtained
Tissue, so that the yield tensile ratio of steel is lower, mouldability is preferable.Product thickness is 1.8~6mm, and yield strength >=625MPa, tension is strong
Degree >=900MPa, elongation percentage A80mm>=10%.But the patent needs ingredient to merge needs to cooling speed with effectively matching for technique
Degree is precisely controlled with temperature, higher to actual production equipment requirement, though product associated counterbore performance indicator is not referred to, according to
It organizes to infer that its reaming performance is not high.
The patent of invention of publication number CN103380217A disclose a kind of hot rolled steel plate product made of Multiphase Steel and its
Manufacturing method proposes a kind of tensile strength >=1100MPa and the Multiphase Steel with good ductility energy and good deformability
The production method of hot-rolled product.Its chemical component be C:0.13%~0.20%, Si:0.70%~1.3%, Mn:1.8%~
2.5%, (Mo may be selected in P: < 0.10%, S: < 0.01%, Al:0.01%~0.10%, Cr 0.25%~0.70%；To this
Cr, Mo content add up to 0.25%~0.70%), Ti:0.08%~0.2%, B:0.0005%~0.005%, remaining is Fe
With inevitable impurity.Its production technology is that heating temperature is 1150~1350 DEG C, and finishing temperature is 800~950 DEG C, after rolling
Cooling velocity > 30 DEG C/s, coiling temperature are 400~570 DEG C.Austria that steel is respectively < 10% by volume fraction is precipitated in the ferrite
Family name's body, 10%~60% martensite,<30% ferrite and>10% bainite every organizational composition.The patent does not mention
And product associated counterbore performance indicator, but organized to infer that its reaming performance is not high according to it.Although the patented product tensile strength
It is higher, and simple production process, but its<10% austenite, 10%~60% martensite,<30% ferrite and>
10% bainite structure contains the different phase of too many intensity in constituting, and is unfavorable for improving reaming performance.
The patent of invention of publication number CN 103667948A discloses a kind of Multiphase Steel and preparation method thereof, using C-Si-Mn
It is strong to obtain surrender by phase transformation strengthening and refined crystalline strengthening for the Design of Chemical Composition that a small amount of Cr, Ti element is added in alloy system
Degree is 430~590MPa, and tensile strength reaches 600~700MPa, and elongation percentage reaches 20~35%, and hole expansibility reaches 80% or more
Ferrite be precipitated structure of steel.Its tissue characteristic is a certain amount of bainite structure of Dispersed precipitate based on polygonal ferrite
And martensite.Polygonal ferrite tissue intensity of the invention is lower, and the bainite structure of Dispersed precipitate and martensitic structure
Its reaming performance can be reduced.
Summary of the invention
It is 780MPa grades the object of the present invention is to provide a kind of intensity, steel heat is precipitated in reaming single ferrite of good performance
Roll plate and its production method.By adding the microalloys such as Cr, Mo element and Nb, V, Ti into low-carbon ferritic steel, and use
Heavy reduction rate rolling generates a large amount of dislocations in the ferrite matrix of refinement, makes in conjunction with high temperature coiling technique in ferrite matrix
It is upper that a large amount of microalloy carbide particles are precipitated, to obtain enough intensity.Single ferritic structure has good extension
Rate and hole expansibility can thus obtain a kind of reaming high-strength ferritic precipitation steel plate of good performance.The steel grade has both high
Intensity and good mouldability are suitble to the components such as manufacture structural part of automotive chassis, reinforcer, safety member, as bumper, B column add
Strong part.
Specific technical solution is:
A kind of single ferrite precipitation steel plate of the high hole expandability of high intensity, chemical component is by weight percentage are as follows: C:
0.05%~0.12%, Si:0.1%~0.7%, Mn:0.8%~2.2%, Ti:0.05%~0.10%, P < 0.020%, S <
0.010%, Als:0.015%~0.060%, Ca:0.0015~0.0050%, Mg:0.0015%~0.0050%, N <
0.005%, also contain at least one of Cr:0.15%~0.3%, Mo:0.05%~0.3% element and Nb:0.02%
~0.06%, at least one of V:0.05%~0.25% element, remaining is Fe and inevitable impurity, the tissue of steel plate
By all single ferrites of volume percentage, wherein quasi-polygonal ferrite accounts for 55% or more, and the tensile strength of steel plate reaches
780MPa grades or more.
The mechanism of action of chemical component is as follows in the present invention:
Carbon: ensure the key element of steel plate tissue and intensity.When C content is greater than 0.12%, it on the one hand can cause weldability
The deterioration of energy, on the other hand easily generates pearlitic structrure, influences reaming performance.It is strong for tensile strength 780MPa of the invention
It spends grade ferrite to be precipitated for steel plate, carbon content control is suitable 0.05%~0.12%.
Silicon: being a kind of cheap alloying element, it dissolves in as ferrite former and play solution strengthening in ferrite
Effect, and improve the superplasticity of superhigh carbon steel.But silicone content is excessively high, will lead to and rolls rear surface of steel plate and red scale occur,
Deteriorate surface quality.The welding performance and paintability of steel grade are damaged, therefore control silicone content 0.1% in the present invention~
0.7%.
Manganese: the element energy stable austenite tissue, ability are only second to elemental nickel, are cheap stable austenite and reinforcing
Alloying element.Its presence can be such that the C curve of steel elapses to the right, strongly increase harden ability, be easy to generate under lower cooling rate
Quasi-polygonal ferrite.But manganese segregation tendency with higher, so its content cannot be too high, it is contemplated that the intensity level of steel grade
Not, comprehensively considering its content should control 0.8%~2.2%, easily form brittlement phase higher than upper limit Shi Gangzhong, deteriorate performance.
Chromium: being carbide former, can postpone perlitic transformation.Chromium content is excessively high, can make processing, the mouldability of material
It is deteriorated.The selection principle of chrome content is to promote the formation of quasi-polygonal ferrite, and avoid the formation pair of excessive martensitic structure
Elongation percentage and reaming performance have an adverse effect, therefore the selection of chromium content of the invention is in 0.15%~0.3% range.
Molybdenum: Mo is significant offer harden ability element, postpones pearlite and generates, and is conducive to the shape of quasi-polygonal ferrite
At.Therefore, the present invention controls molybdenum content for Mo:0.05%~0.30%.
Niobium: niobium is remarkably improved the recrystallization temperature of steel and realizes crystal grain refinement.The carbide of niobium can in the hot rolling
Hinder the recrystallization of deformed austeaite.The element be added can further fining ferrite steel microscopic structure, improve the strong of steel
Toughness.The present invention controls the content of niobium 0.02%~0.06%.
Titanium: being carbide, and micro Ti is added in steel and is conducive to the N fixed in steel, is formed by TiN
Austenite grain when heating steel billet can be made not grow up excessively, to play the purpose of refinement original austenite grains.Titanium is in steel
Can exist in the form of second phase particles, reinforced ferrite phase plays precipitation enhancement.Titanium additive amount is in the present invention
0.05%~0.10%.
Vanadium: the addition of the element can further refinement microstructure, improve the precipitation strength performance of steel.The too high tissue meeting of vanadium
A large amount of carbide are formed, and reduce carbon content in matrix, so that intensity, which reduces, influences reaming performance.The present invention contains vanadium
Amount control is in 0.05%~0.25% range.
Aluminium: belong to strong deoxidant element.By the aluminium element for adding certain content, it is ensured that the oxygen content in steel is as far as possible
It is low.Extra aluminium can form AlN precipitate with the nitrogen in steel after deoxidation, improve armor plate strength, and heat in heat treatment
When refine steel autstenitic grain size.Therefore, Als content is controlled 0.015%~0.060% in the present invention.
P and s are impurity element, are essentially more lower better, it is contemplated that cost, the present invention control the content of p and s
For P≤0.020%, S≤0.010%.
Calcium: the form of sulfide in changeable steel improves the plasticity and toughness of steel plate, helps to improve the reaming of steel plate
Rate.The present invention controls calcium content for Ca:0.0015%~0.0050%.
Magnesium: the addition of micro Mg becomes the shape of TiN, TiC precipitate so that generating tiny MgO, MgS precipitate in steel
Epipole plays dispersion and refinement TiN, TiC precipitate, can improve steel plate hole expansibility.The present invention controls content of magnesium for Mg:
0.0015%~0.0050%.
Nitrogen: being tramp element, and nitrogen reacts to form the precipitation of TiN particle under the high temperature conditions with titanium, and excessive TiN particle can become
The induction point of steel plate local deformation micro-crack, influences hole expansibility, it is necessary to control the nitrogen content of molten steel, nitrogen content is less than
0.005%.
The invention further relates to the production methods that steel hot-rolled sheet is precipitated in a kind of ferrite of high expansion rate, including smelting, continuous casting, heat
It rolls, batch.Molten steel carries out Calcium treatment after RH and LF Fruit storage, feeds silico-calcium linear velocity >=3.5m/s, carries out after line feeding
Soft argon blowing processing, Argon amount≤100l/min, molten steel overheat≤30 DEG C, and electromagnetic agitation and slighter compress are put into, prevent slab
Segregation causes product hole expansibility to decline, and is casting continuously to form continuous casting billet later；The heating temperature of continuous casting billet is 1150~1250 DEG C, after heating
Multi- pass rolling, total reduction >=80% are carried out on milling train, hot rolling finishing temperature is 850~950 DEG C, whole cooling velocity after rolling
15~45 DEG C/s, 550~650 DEG C of coiling temperature, it is air-cooled to room temperature.
Present invention process designs reason:
In manufacturing method of the present invention, molten steel is handled, it is ensured that S content is lower than by converter smelting by RH and LF
0.035%, the quantity that is mingled with of steel plate is reduced, and carry out Ca processing to improve oxide morphology, the MnS of strip is made to be mingled with conversion balling-up
The CaS of shape is mingled with, and reducing MnS is the nonmetal inclusion of representative to the successional destruction of matrix, improves the hole expansibility of product.And
Apply electromagnetic agitation and slighter compress in steelmaking process, keeps materials microstructure uniform, prevent banded structure and center segregation, avoid steel
Plate cracks in reaming procedure, improves hole expansibility.
Heating temperature is lower than 1150 DEG C, and microalloy element dissolution is insufficient, fails the effect for making full use of microalloy element,
Strength reduction, is higher than 1250 DEG C of crystal grain and is easy roughening, and to improving, steel plate toughness is unfavorable.
Slab carries out roughing in austenite recrystallization area, passes through the recrystallization softening austenite grain after rolling deformation, steel
The deflection of plate refines crystal grain, and high density dislocation is generated in ferritic structure 85% or more, improves intensity, reaches
780MPa or more, finishing temperature control is at 850~950 DEG C of austenite Unhydrated cement, by austenite low-temperature space rolling deformation,
So that austenite crystal intragranular is formed Zona transformans and because of the carbonitride precipitates of strain-induced microalloy element, refines the phase transformation of austenite
Product improves steel plate toughness.
Steel plate is cooled to 550~650 DEG C with the cooling velocity of 15~45 DEG C/s after finish to gauge, if coiling temperature is lower than 550 DEG C,
It is easy to appear bainite in steel plate microstructure, is unfavorable for improving hole expandability, is air-cooled to room temperature after batching.And temperature is batched herein
Degree section easily generates the Carbide Precipitation particle of Nano grade, improves product strength and hole expansibility.
The high-chambering steel plate of chemical component and fabrication process according to the invention has high-intensitive and high tenacity
Match, and there is very high hole expansibility, so that the excellent cold-workability exhibiting of steel plate of the present invention, is manufacturing complex-shaped high intensity
When auto parts, there is original advantage.
The utility model has the advantages that
The present invention compared with the existing technology, has the beneficial effect that:
(1) present invention by addition content be 0.02%~0.05% niobium element, 0.05%~0.25% vanadium,
0.05%~0.10% titanium elements realize ferritic structure in steel is precipitated in ferrite refined crystalline strengthening and precipitation strength, lead to
Ferrite form can be improved for 0.15%~0.3% chromium, 0.05%~0.3% molybdenum element by crossing addition content, be increased
Grain boundary area reinforced ferrite matrix strength, and by single ferrite build up, improve the reaming that steel is precipitated in ferrite
Performance and elongation.
(2) quasi-polygonal ferrite accounts for 55% or more in steel produced by the invention, the institutional framework of quasi-polygonal ferrite
Product strength is improved, single phase constitution avoids steel plate, and difference of hardness causes to crack between different phases during local deformation
The phenomenon that, improve reaming performance and elongation.When steel plate thickness is 2.0~6.0mm, tensile strength >=780MPa, reaming
Rate reaches 60% or more, elongation >=15%.
(3) steel produced by the invention are processed due to having had both high-intensitive and good stretch flangeability in manufacture
Mouldability requires stringent, and when automobile body part of the high high load type of intensity rank has unique advantage, is suitble to manufacture knot
The components such as component, reinforcer, safety member, such as bumper, B column reinforcer.
Detailed description of the invention
Fig. 1 is the metallographic structure of embodiment 1；Tissue is entirely by tiny polygonal ferrite and quasi-polygonal ferrite
The single ferrite of composition.
Specific embodiment
For following embodiment for illustrating the content of present invention, these embodiments are only the general description of the content of present invention,
The content of present invention is not limited.
Table 1 is the mass percentage of each chemical element in embodiment steel；Table 2 is that the manufacturing process of embodiment steel plate is joined
Number；Table 3 is the microscopic structure and mechanical property of embodiment steel plate.
The mass percentage (wt%) of each chemical element in 1 embodiment steel of table
| Embodiment | C | Si | Mn | P | S | Cr | Mo | Nb | Ti | Ca | Mg | V | N | Als |
| 1 | 0.05 | 0.22 | 2.10 | 0.014 | 0.0055 | 0.28 | 0.1 | 0.03 | 0.05 | 0.0019 | 0.0019 | 0.13 | 0.003 3 | 0.04 2 |
| 2 | 0.08 | 0.61 | 1.80 | 0.011 | 0.0058 | 0.22 | 0.05 | 0.02 | 0.08 | 0.0032 | 0.0032 | 0.002 9 | 0.04 2 | |
| 3 | 0.10 | 0.25 | 2.15 | 0.012 | 0.0042 | 0.3 | 0.05 | 0.10 | 0.0021 | 0.0021 | 0.001 7 | 0.03 5 | ||
| 4 | 0.12 | 0.20 | 1.28 | 0.013 | 0.0051 | 0.2 | 0.07 | 0.0041 | 0.0041 | 0.2 | 0.004 1 | 0.02 9 | ||
| 5 | 0.12 | 0.18 | 1.90 | 0.011 | 0.0055 | 0.3 | 0.06 | 0.0017 | 0.0017 | 0.25 | 0.001 5 | 0.04 0 |
The fabrication process parameters of 2 embodiment steel plate of table
The microscopic structure and mechanical property of 3 embodiment steel plate of table
By Biao Ke get, ferrite precipitation steel plate produced by the invention, yield strength > 680MPa, tensile strength >=
790MPa, elongation percentage A80mm>=15%, hole expansibility >=65% has good reaming performance.
Claims (4)
1. steel plate is precipitated in a kind of single ferrite of the high hole expandability of high intensity, which is characterized in that chemical component presses quality percentage in steel
Than are as follows: C:0.05%~0.12%, Si:0.1%~0.7%, Mn:0.8%~2.2%, Ti:0.05%~0.10%, P <
0.020%, S < 0.010%, Als:0.015%~0.060%, Ca:0.0015%~0.0050%, Mg:0.0015%~
0.0050%, N < 0.005%, also containing at least one of Cr:0.15%~0.3%, Mo:0.05%~0.3% element with
And at least one of Nb:0.02%~0.06%, V:0.05%~0.25% element, remaining for Fe and inevitably it is miscellaneous
Matter.
2. steel plate is precipitated in a kind of single ferrite of the high hole expandability of high intensity as described in claim 1, which is characterized in that steel plate
The tissue of tensile strength >=780MPa, steel plate presses all single ferrites of volume percentage, wherein quasi-polygonal ferrite
Account for 55% or more.
3. the preparation method of steel plate, steel plate is precipitated in a kind of single ferrite of the high hole expandability of high intensity as claimed in claim 1 or 2
Production technology are as follows: smelting, hot rolling, is batched continuous casting, which is characterized in that
Molten steel carries out Calcium treatment after RH and LF Fruit storage, feeds silico-calcium linear velocity >=3.5m/s, molten steel overheat≤30
DEG C, and electromagnetic agitation and slighter compress are carried out, it is casting continuously to form continuous casting billet；
Continuous blank heating temperature is 1150~1250 DEG C, carries out multi- pass rolling after heating on milling train, total reduction >=80%,
Hot rolling finishing temperature is 850~950 DEG C, and whole cooling velocity after rolling is 15~45 DEG C/s, and coiling temperature is 550~650 DEG C, air-cooled
To room temperature.
4. the preparation method that steel plate is precipitated in the high-intensitive high single ferrite of hole expandability as claimed in claim 3, which is characterized in that
Soft argon blowing processing, Argon amount≤100l/min are carried out after line feeding.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201711400577.1A CN109957716A (en) | 2017-12-22 | 2017-12-22 | Steel plate and preparation method thereof is precipitated in a kind of single ferrite of the high hole expandability of high intensity |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201711400577.1A CN109957716A (en) | 2017-12-22 | 2017-12-22 | Steel plate and preparation method thereof is precipitated in a kind of single ferrite of the high hole expandability of high intensity |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CN109957716A true CN109957716A (en) | 2019-07-02 |
Family
ID=67018881
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201711400577.1A Pending CN109957716A (en) | 2017-12-22 | 2017-12-22 | Steel plate and preparation method thereof is precipitated in a kind of single ferrite of the high hole expandability of high intensity |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN109957716A (en) |
Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN111172474A (en) * | 2020-03-18 | 2020-05-19 | 本钢板材股份有限公司 | Production process of low-brittleness 590 MPa-level high-strength steel for automobile rims |
| CN113106337A (en) * | 2021-03-18 | 2021-07-13 | 唐山科技职业技术学院 | High-reaming-hole steel with pressure of 980MPa or above and production method thereof |
| EP3925771A1 (en) * | 2020-06-16 | 2021-12-22 | SSAB Technology AB | High strength steel product and method of manufacturing the same |
| EP3926064A1 (en) * | 2020-06-16 | 2021-12-22 | SSAB Technology AB | High strength steel product and method of manufacturing the same |
| CN114107789A (en) * | 2020-08-31 | 2022-03-01 | 宝山钢铁股份有限公司 | 780 MPa-grade high-surface high-performance high-stability ultrahigh-hole-expansion steel and manufacturing method thereof |
| WO2022042733A1 (en) * | 2020-08-31 | 2022-03-03 | 宝山钢铁股份有限公司 | 780 mpa grade high-surface ultra-high reaming steel and manufacturing method therefor |
Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1394237A (en) * | 2000-10-31 | 2003-01-29 | 日本钢管株式会社 | High tensile hot rolled steel sheet and method for production thereof |
| CN101772584A (en) * | 2007-07-31 | 2010-07-07 | 杰富意钢铁株式会社 | High-strength steel sheet |
| CN101999007A (en) * | 2008-04-10 | 2011-03-30 | 新日本制铁株式会社 | High-strength steel sheets which are extremely excellent in the balance between burring workability and ductility and excellent in fatigue endurance, zinc-coated steel sheets, and processes for production of both |
-
2017
- 2017-12-22 CN CN201711400577.1A patent/CN109957716A/en active Pending
Patent Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1394237A (en) * | 2000-10-31 | 2003-01-29 | 日本钢管株式会社 | High tensile hot rolled steel sheet and method for production thereof |
| CN101772584A (en) * | 2007-07-31 | 2010-07-07 | 杰富意钢铁株式会社 | High-strength steel sheet |
| CN101999007A (en) * | 2008-04-10 | 2011-03-30 | 新日本制铁株式会社 | High-strength steel sheets which are extremely excellent in the balance between burring workability and ductility and excellent in fatigue endurance, zinc-coated steel sheets, and processes for production of both |
Cited By (11)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN111172474A (en) * | 2020-03-18 | 2020-05-19 | 本钢板材股份有限公司 | Production process of low-brittleness 590 MPa-level high-strength steel for automobile rims |
| EP3925771A1 (en) * | 2020-06-16 | 2021-12-22 | SSAB Technology AB | High strength steel product and method of manufacturing the same |
| EP3926064A1 (en) * | 2020-06-16 | 2021-12-22 | SSAB Technology AB | High strength steel product and method of manufacturing the same |
| WO2021254722A1 (en) * | 2020-06-16 | 2021-12-23 | Ssab Technology Ab | High strength steel product and method of manufacturing the same |
| WO2021254719A1 (en) * | 2020-06-16 | 2021-12-23 | Ssab Technology Ab | High strength steel product and method of manufacturing the same |
| CN115698363A (en) * | 2020-06-16 | 2023-02-03 | 瑞典钢铁技术有限公司 | High strength steel product and method for manufacturing same |
| CN114107789A (en) * | 2020-08-31 | 2022-03-01 | 宝山钢铁股份有限公司 | 780 MPa-grade high-surface high-performance high-stability ultrahigh-hole-expansion steel and manufacturing method thereof |
| WO2022042727A1 (en) * | 2020-08-31 | 2022-03-03 | 宝山钢铁股份有限公司 | 780 mpa-grade ultra-high reaming steel having high surface quality and high performance stability, and manufacturing method therefor |
| WO2022042733A1 (en) * | 2020-08-31 | 2022-03-03 | 宝山钢铁股份有限公司 | 780 mpa grade high-surface ultra-high reaming steel and manufacturing method therefor |
| CN113106337A (en) * | 2021-03-18 | 2021-07-13 | 唐山科技职业技术学院 | High-reaming-hole steel with pressure of 980MPa or above and production method thereof |
| CN113106337B (en) * | 2021-03-18 | 2022-08-09 | 唐山科技职业技术学院 | High-reaming-hole steel with pressure of 980MPa or above and production method thereof |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN108486466B (en) | A kind of yield strength 550MPa grade high ductility weather-resistant steel plate and preparation method thereof | |
| CN109023036B (en) | Ultrahigh-strength hot-rolled complex-phase steel plate and production method thereof | |
| CN101701316B (en) | Automobile beam steel with tensile strength of 590MPa and manufacturing method thereof | |
| CN109957716A (en) | Steel plate and preparation method thereof is precipitated in a kind of single ferrite of the high hole expandability of high intensity | |
| CN101624676B (en) | Hot-rolled beam steel with a tensile strength of more than 710MPa and preparation method thereof | |
| CN113416890B (en) | High-hole-expansion high-plasticity 980 MPa-grade cold-rolled continuous annealing steel plate and preparation method thereof | |
| CN108070779A (en) | A kind of solderable fine grain, high strength degree structural steel and iron and its production method | |
| CN102363858A (en) | High-strength steel for 750 to 880 MPa-level vehicles and production method thereof | |
| CN113549823B (en) | 900 MPa-grade hot-rolled and pickled multiphase steel with low yield ratio and high hole expansion rate and production method thereof | |
| CN109207849A (en) | High-strength high-plasticity 1000MPa level hot rolled steel plate and preparation method | |
| CN112210727B (en) | Hot-rolled complex phase steel with tensile strength of 850MPa and production method thereof | |
| CN113528944B (en) | 1000MPa easily-formed wear-resistant steel plate and preparation method thereof | |
| CN106609335A (en) | Tensile strength 700 MPa-grade high broaching hot-rolled steel plate and manufacturing method thereof | |
| CN109898016A (en) | 500MPa grades or more high reaming hot rolling acid-cleaning steel plate and its manufacturing method | |
| CN102676926A (en) | Complex phase steel plate and manufacturing method thereof | |
| CN109898017A (en) | 1000MPa grades of cold-bending properties excellent cold-rolled biphase steel and production method | |
| CN108315662B (en) | A kind of yield strength 900MPa level hot rolled steel plate and its production technology | |
| CN105506476A (en) | 600 MPa-grade highly-chambered steel plate for automotive chassis and manufacturing method thereof | |
| CN101353757A (en) | Hot rolling high reaming steel plate having 440MPa grade of tensile strength and manufacturing method thereof | |
| CN102260824A (en) | Hot-rolled steel plate with yield strength of 550 MPa for hot forming and manufacturing method thereof | |
| CN106917055B (en) | Tough automobile steel of a kind of third generation height and preparation method thereof | |
| CN114214563B (en) | High-toughness hot stamping steel rolled by sheet billet with Rm more than or equal to 1500MPa and production method | |
| CN114150227B (en) | High-toughness hot stamping steel rolled by medium and thin slabs with Rm more than or equal to 1500MPa and production method | |
| CN105543666A (en) | Automobile beam steel with 960 MPa yield strength and production method thereof | |
| CN107400834A (en) | A kind of reaming hot rolling complex phase steel plate of good performance and its production method |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| PB01 | Publication | ||
| PB01 | Publication | ||
| SE01 | Entry into force of request for substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| WD01 | Invention patent application deemed withdrawn after publication | ||
| WD01 | Invention patent application deemed withdrawn after publication |
Application publication date: 20190702 |