CN106119702B - A kind of high reaming steel of 980MPa grades of hot-rolled high-strength and its manufacturing method - Google Patents
A kind of high reaming steel of 980MPa grades of hot-rolled high-strength and its manufacturing method Download PDFInfo
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- CN106119702B CN106119702B CN201610451291.5A CN201610451291A CN106119702B CN 106119702 B CN106119702 B CN 106119702B CN 201610451291 A CN201610451291 A CN 201610451291A CN 106119702 B CN106119702 B CN 106119702B
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/005—Heat treatment of ferrous alloys containing Mn
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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
- 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
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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
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/002—Bainite
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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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/008—Martensite
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Abstract
A kind of high reaming steel of 980MPa grades of hot-rolled high-strength and its manufacturing method, the steel chemical composition weight percent are：C：0.05~0.10%, Si：0.1~0.8%, Mn：1.5~2.5%, P≤0.015%, S≤0.005%, O≤0.003%, Al：0.02~0.08%, N≤0.005%, Ti：0.05~0.15%, Nb：0.02~0.06%, Cr：0.1~1.0%, V：0.01~0.10%, remaining is Fe and inevitable impurity, and 0.15%≤Nb+Ti+V≤0.25%, 0.01%≤(Ti 3.42N)/4+V/4.24≤0.06%.The microstructure of steel of the present invention is granular bainite+martensite, its yield strength >=900MPa, tensile strength >=980MPa, elongation percentage >=15%, hole expansibility >=50%, excellent intensity, plasticity and hole expandability matching are shown, automobile chassis, crossbeam, wheel etc. is can be applied to and needs the high-strength component being thinned and complexity shapes.
Description
Technical field
The invention belongs to hot-rolling high-strength steel fields, and in particular to a kind of high reaming steel of 980MPa grades of hot-rolled high-strength and its system
Make method.
Background technology
It is outstanding in automobile with the increasingly strict and national implementation to motor vehicle emission restriction of national environmental protection laws and regulations
It is passenger car field, and high-strength thinned or vehicle structure lightweight has become the important research of major automobile manufacturing company in the world
Direction.However, different from the high-strength thinned and lightweight trend of passenger car, commercial car lightweight, which is operated in, never to be formed
Gesture.Among these on the one hand since the universal surcharge ratio of commercial car is more serious, the designer of commercial car to the design margin of structure very
Greatly；Meanwhile commercial car itself and loading capacity are larger, after being thinned using high-strength steel, rigidity is difficult to ensure sometimes；Other one
Aspect is since commercial car is with respect to Price Sensitive customers are belonged to for passenger car, and it is generally desirable to the intensity raisings in steel plate by user
While price had better not improve too much, and at present commercial car processing factory's generally existing equipment more low side, be suitable only for
In the processing of common Medium And Low Strength Steels, to the no too many experience of processing and existing mold of high-strength steel be not suitable for high-strength steel processing and
It uses.Therefore, no matter born from the demand willingness used high-strength steel or the working ability of its own and price etc.
All so that high-strength be thinned of commercial car is made slow progress with weight reduction process.The lightweight of commercial car also will be a kind of hair in future
Exhibition trend.Therefore, it will be following development trend to develop the high-strength steel that has excellent performance.
Currently, tensile strength mainly adds microalloy first in the composition design of 980MPa or more grade high-strength steel using low-carbon
Element adds the method that lonneal is handled in technique using online or out-line quenching.Under normal conditions, quenching+lonneal it
The performance of steel plate is that yield strength and tensile strength ratio are higher afterwards, usually 0.90 or more even close to 1.0, and is extended
Rate according to the real data statistics produced greatly usually 13 ± 1%, and the current demand of user be keep tension 980MPa with
Elongation percentage is improved to 14% or more on the basis of upper.If this kind of hot rolling super-high strength steel is applied relative complex in automobile chassis etc.
Automobile structure on, it is also necessary to steel plate have good reaming performance.This adds lonneal martensite group to traditional quenching
Realization is practically impossible to for knitting.This is because if the ingredient of steel grade and technological design thinking are constant, it is final
Mechanical property be difficult to be greatly improved.From the point of view of documents and materials both domestic and external, it there is no 980MPa grades of hot-rolled high-strengths high-plastic
The super-high strength steel of property and high reaming performance, there are no the products produced greatly to emerge.
Invention content
The purpose of the present invention is to provide a kind of high reaming steel of 980MPa grades of hot-rolled high-strength and its manufacturing method, the hot rollings
Yield strength >=900MPa of the high reaming steel of high intensity, tensile strength >=980MPa, elongation percentage >=15%, hole expansibility >=50%,
Show excellent intensity, plasticity and hole expandability matching, can be applied to automobile chassis, crossbeam, wheel etc. need it is high-strength be thinned and
The component of complexity forming.
In order to achieve the above objectives, the technical scheme is that：
It is tiny to ensure a large amount of disperses are precipitated in ferrite in the hot rolling reeling stage that the Ti of high level is added in the present invention
Nano-carbide, play strong disperse educt and strengthen effect；Micro Nb main purposes, which are added, to be refined in the finish rolling stage
Austenite grain；Other than using TiC nano-particle precipitation strengths, micro alloying element V and C are additionally added in bainite ferrite
Form the precipitating reinforcing effect that nanometer VC further increases steel.It should make band with higher cooling rate after finish to gauge in course of hot rolling
Steel is quickly cooled to suitable coiling temperature, and strip is made to obtain by the tissue based on granular bainite and martensite, to obtain
980MPa grade high-strengths high-ductility and high reaming steel.
Specifically, a kind of high reaming steel of 980MPa grades of hot-rolled high-strengths of the present invention, chemical component weight percentage are：
C：0.05~0.10%, Si：0.1~0.8%, Mn：1.5~2.5%, P≤0.015%, S≤0.005%, O≤0.003%,
Al：0.02~0.08%, N≤0.005%, Ti：0.05~0.15%, Nb：0.02~0.06%, Cr：0.1~1.0%, V：
0.01~0.10%, remaining is Fe and inevitable impurity, and above-mentioned element need to meet following relationship simultaneously：0.15%≤Nb
+ Ti+V≤0.25%, 0.01%≤(Ti-3.42N)/4+V/4.24≤0.06%.
Preferably, in the chemical composition of the high reaming steel of the hot-rolled high-strength：Mn：1.8~2.2%, with weight percent
Meter.
Further, the microstructure of the high reaming steel of the hot-rolled high-strength is granular bainite+martensite, wherein bayesian
There are Nano-Scaled Carbide, crystallite dimension≤5 μm of bainite, Nano-Scaled Carbide sizes≤10nm in body ferrite.
Again, in the microstructure of the high reaming steel of the hot-rolled high-strength volume fraction shared by granular bainite be 70~
85%, volume fraction shared by martensite is 15~30%.
Yield strength >=900MPa of the high reaming steel of hot-rolled high-strength of the present invention, tensile strength >=980MPa extend
Rate >=15%, hole expansibility >=50%.
In the composition design of steel of the present invention：
Carbon：Carbon is the basic element in steel and one of the important element in the present invention.Carbon is former as the gap in steel
Son, the intensity to improving steel play very important effect, are influenced on the yield strength of steel and tensile strength maximum.The present invention is
The super-high strength steel that tensile strength reaches 980MPa grade is obtained, bainite crystallite dimension must be controlled, should usually be controlled at≤5 μm.This
Outside, it also needs to act on by the strong precipitation strength of tiny nanometer precipitated phase.The content of carbon is no at least 0.05% or more in steel
Then intensity is difficult to reach 980MPa grades；Simultaneously carbon content can not too high (≤0.1%), otherwise in hot-rolled high coiling process
In be easy to form the tissue of pearlite type, reduce the quantity for batching the nanometer precipitated phase formed in rear bainite, to
Reduce precipitating reinforcing effect.
The addition of carbon and the addition of Ti and V are closely related in the present invention, and the content of Ti, V and N need to be controlled certain
In range, guarantee forms sufficient amount of nanometer precipitation strength phase (size≤10nm).These nano-particles are after high temperature coiling
Slow cooling during can effectively inhibit bainite ferrite crystal grain to grow up, while playing precipitating reinforcing effect.Therefore, carbon
Content must control 0.10% hereinafter, and meeting following formula, i.e., 0.01%≤(Ti-3.42N)/4 between the content of Ti, V and N
+ V/4.24≤0.06%.To sum up, carbon content should be controlled 0.05~0.10% in steel of the present invention.
Silicon：Silicon is also the basic element in steel, but in the present invention, and silicon is not a key element, is being made steel
Journey plays the role of part deoxidation.Silicon can expand ferrite in steel and form range, be conducive to expand rolling mill practice window；Simultaneously
Silicon also has stronger solid solution strengthening effect.But silicon is easy the surface of steel plate after rolling and forms uneven distribution after being added in steel
Red iron sheet, these red iron sheets are difficult to thoroughly remove in subsequent acid cleaning process.Although with red iron sheet steel plate subsequent
There is no harmful effect to performance in process, but in the lacquering process of component, since the red iron sheet removal of surface of steel plate is not thorough
Bottom, component surface easy tos produce aberration after japanning, influences beauty.In addition, Si contents are higher than 0.8%, to the weldability of steel plate
Can be unfavorable, therefore the control of Si contents is 0.1~0.8% in steel of the present invention.
Manganese：Manganese is element most basic in steel, while being also one of most important element in the present invention.It is well known that manganese
It is the important element for expanding austenite phase field, the critical quenching rate of steel, stable austenite can be reduced, crystal grain thinning is postponed
Austenite from being transformed into perlite.In the present invention, to ensure that the intensity of steel plate, manganese content should be controlled 1.5% or more, manganese contains
Measure too low, overcooling austenite is not sufficiently stable, and is easy to be changed into the tissue of pearlite type；Meanwhile the content of manganese is generally also unsuitable
More than 2.5%, when steel-making, is easy to happen Mn segregations, while hot tearing easily occurring when sheet billet continuous casting.Therefore, in steel manganese Mn content control
System is 1.5~2.5%, and preferred scope is between 1.8~2.2%.
Phosphorus：Phosphorus is the impurity element in steel.In phosphorus easily segregation to crystal boundary, in steel when the content of phosphorus higher (>=0.1%),
Form Fe2P is precipitated around crystal grain, reduces the plasticity and toughness of steel, therefore the lower its content the better, and general control is 0.015%
Within preferably and do not improve steel-making cost.
Sulphur：Sulphur is the impurity element in steel.Sulphur in steel, which is usually combined with manganese, to be formed MnS and is mingled with, especially when sulphur sum
When content is higher, more MnS will be formed in steel, and MnS itself has certain plasticity, the MnS in the follow-up operation of rolling
Roll the transverse tensile property that steel plate is reduced to deforming in edge.Therefore the lower sulfur content the better in steel, when actual production, usually controls
Within 0.005%.
Aluminium：Aluminium be in steel in addition to five big element of C, Si, Mn, P, S another important alloying element.The base of aluminium in the present invention
This effect is mainly the deoxidation in steelmaking process.Aluminium content is generally not less than 0.02% in steel；Meanwhile if if aluminium content is more than
0.08%, the effect of crystal grain thinning weakens instead.According to the controlled level of aluminium content in actual production process, aluminium in steel is contained
Amount control is 0.02~0.08%.
Nitrogen：Nitrogen belongs to impurity element in the present invention, and the lower content the better.Nitrogen is also inevitable element in steel,
Under normal conditions, if without Special controlling in steelmaking process, the residual content of nitrogen in steel is usually≤0.005%.These are solid
Molten or free nitrogen must be fixed by forming certain nitride, otherwise impact flexibility of the free nitrogen-atoms to steel
It is very unfavorable, and the sawtooth for being readily formed during belt steel rolling overall length splits defect.Pass through addition in the present invention
Strong carbide or nitride forming element Ti form stable TiN to fixed nitrogen-atoms.Therefore, the content control of nitrogen exists
It is within 0.005% and more lower better.
Titanium：Titanium is one of the important element in the present invention.Titanium has very strong binding force with C, N atom in steel.The present invention's
Composition design thinking is primarily intended to obtain the nano-carbide of small and dispersed rather than nitride.The binding force of titanium and nitrogen is more than titanium
Binding force between carbon, in order to reduce the forming amount of TiN in steel to the greatest extent, the content of nitrogen in steel should control more lower better.Add
The titanium main purpose for entering high level is to, to during bainite transformation, be formed more in bainite ferrite in austenite
More Nano-Scaled Carbides.Similarly, it is also to be formed more to receive in bainite ferrite that suitable vanadium main purpose, which is added,
Rice vanadium carbide particle, further increases the effect of dispersion-strengtherning.
As described above, key element carbon, titanium and vanadium should meet certain relationship and could obtain high-strength high-plasticity in the present invention
Property microstructure.It is confirmed by a large number of experiments, carbon must meet certain relationship i.e. 0.01%≤(Ti- with titanium, content of vanadium
3.42N)/4+V/4.24≤0.06%, it is strong that the Nano-Scaled Carbide otherwise formed in steel cannot utmostly play disperse educt
Change in effect or steel and be likely to occur a small amount of pearlitic structrure so that the intensity of steel plate is difficult to reach the high intensity of 980MPa.It receives
The best Precipitation Temperature of meter level carbide is mainly closely related with the content of titanium and vanadium.It is confirmed by theoretical calculation and experiment,
In high temperature coiling temperature range (500~600 DEG C), titanium can play the content range of best precipitating reinforcing effect 0.05~
Between 0.15%.
Vanadium：Vanadium is one of the key element in the present invention.Solid solubility of the carbonitride of vanadium in austenite is larger and logical
Often it is precipitated in ferrite.There was only 800MPa or so using the high attainable maximum pulling strength of Ti steel institute of low-carbon, to continue
The intensity for improving nanometer precipitation strength steel needs to improve carbon content, but, it is that carbon content increase is brought the result is that group when high temperature coiling
The middle band-like pearlite of appearance is knitted, it is unfavorable to reaming performance；Vanadium is also a kind of carbide, and appropriate vanadium is added can be in shellfish
Tiny nanometer VC, pearl when further functioning as precipitating reinforcing effect, and also avoiding high temperature coiling are formed in family name's body ferrite
The formation of body of light.According to theory analysis and experimental study, the content of vanadium should control in 0.01~0.10% range, and with
Ti, N should meet certain relationship i.e. 0.01%≤(Ti-3.42N)/4+V/4.24≤0.06%.
Chromium：Chromium is one of the important element in the present invention.Nanometer precipitation strength type fine-grained steel one of performance characteristics be
Yield tensile ratio is high, usual yield tensile ratio 0.90 or more even close to 1.0, and chromium on the one hand can suitably be reduced by solution strengthening it is in the wrong
Intensity is taken, while can slightly improve tensile strength.The purpose that a small amount of chromium is added in the present invention is mainly bent using its reduction
Take the effect of intensity, reduce acting on when content reaches 1.0% for yield strength and be saturated, thus by chromium content control 0.10~
Between 1.0%.
Oxygen：It is inevitable element in steelmaking process, for the purpose of the present invention, after the content of oxygen is by aluminium deoxidation in steel
Can generally 30ppm be reached hereinafter, significant adverse will not be caused to influence the performance of steel plate.Therefore, by oxygen content in steel control
System is within 30ppm.
The manufacturing method of the high reaming steel of 980MPa grades of hot-rolled high-strength of the present invention comprising following steps：
1) it smelts, cast
It smelted, refined by above-mentioned chemical composition, being cast as strand or ingot casting；
2) strand or ingot casting heating
Heating temperature >=1230 DEG C, 1~2 hour heating time；
3) hot rolling+cooling+is batched
Start rolling temperature is 1080~1200 DEG C, carried out at 1000 DEG C or more 3~5 passage roughing and accumulative deflection >=
50%；Intermediate base waits for that temperature is 900~950 DEG C, then carries out 3~5 passage finish rolling and accumulative deflection >=70%；Finish to gauge temperature
Degree is 800~900 DEG C, is batched steel plate water cooling to 500~600 DEG C with the cooling rate of >=100 DEG C/s after finish to gauge, after batching with
The cooling rate of≤20 DEG C/h is cooled to room temperature.
The reasons why design and manufacture technology of the present invention, is as follows：
In rolling mill practice design, in order to coordinate the composition design of high Ti, the heating temperature of steel billet must it is sufficiently high (>=
1230 DEG C) to ensure to there are Ti atoms as much as possible to be solid-solubilized in slab；It is answered in the rhythm of roughing and finish rolling stage, the operation of rolling
It is rapidly completed as possible, avoids the Carbonitride Precipitation in roughing and finish rolling stage excessive Ti.It should be with compared with Gao Leng after finish to gauge
Fast (>=100 DEG C/s) quickly water cooling to coiling temperature.This is because if cooling velocity is slower after rolling, shape inside steel plate
The austenite of change can complete recrystallization process within a very short time, and austenite grain is grown up at this time.Relatively coarse Ovshinsky
For body when bainitic transformation occurs for subsequent cooling procedure, the bainite ferrite crystal grain of formation is more coarse, usually 5~20
It is unfavorable to the intensity of steel plate between μm.The microstructure mentality of designing of steel plate of the present invention is granular bainite, martensite and nanometer
Microstructure based on level carbide.
The high intensity of steel plate is from two aspects：When nanometer precipitation strength, second is that tiny bainite structure.According to classics
Orowan mechanism, Nano-Scaled Carbide is to the contribution of intensity about between 200~400MPa.Therefore, only nanometer is precipitated
Strengthen far from enough, the high intensity of steel plate must also come from tiny bainite structure.Since the present invention is mild steel, iron element
Body phase driving force is larger.Therefore, the cooling velocity after strip finish to gauge answers sufficiently fast (>=100 DEG C/s), avoids in continuous coo1ing
Form ferrite in the process, and should be during Slow cooling after strip coiling formed granular bainite, martensite and
Nano-Scaled Carbide.
For the high-strength steel of high Ti precipitation strengths type, heating temperature is a critically important technological parameter.With it is general
Logical high-strength steel is compared, and the high higher heating temperature of Ti steel (>=1230 DEG C) main purpose is dissolved as far as possible in the slab of heating
More Ti atoms.Since the carbonitride solid solubility temperature of Ti is usually very high (>=1300 DEG C), in steel-making or continuous casting and rolled
The different phase of journey can be precipitated, and the Ti contents that this allows for finally can be used to play the role of precipitation strength are just very low.Therefore, must
It must ensure that high heating temperature is possible to obtain more Nano-Scaled Carbides in final coiling process, therefore the present invention claims
The minimum heating temperature of steel plate is necessary >=and 1230 DEG C；The upper limit of heating temperature is actually accessible or can hold according to live heating furnace
The temperature received is limited, usually≤1300 DEG C.
For high Ti steel, the heating time of slab for heating temperature, influences much smaller.Theoretically
For, as long as heating temperature reaches the balance solution temperature of the carbonitride of Ti, solution rate is very fast.Therefore in this stage,
Heating time is mainly to ensure that slab can be grilled thoroughly uniformly as main target.Certainly, heating time can not be too long, otherwise
The carbonitride of the undissolved Ti of high temperature very likely occurs to be roughened and grow up, the carbonitride of these coarse Ti is in austenite
Grain boundaries are precipitated, and reduce the bond strength of crystal boundary, are easy slab during heating and disconnected base phenomenon occurs in heating furnace.Cause
This, according to slab thickness difference, heating temperature is normally controlled in 1~2 hour.
Slab, which is come out of the stove, to be started faster rhythm should be kept to be rolled when rolling, to reduce to the greatest extent in roughing and finish rolling stage
The precipitation of Ti.This is because be in austenitic area in roughing especially finish rolling, the Ti that this temperature range is precipitated carbide or
Carbonitride size is little to final precipitating reinforcing effect mostly at tens nanometers.Therefore, roughing and finish rolling stage should be as early as possible
Completion is precipitated with retaining more Ti atoms in coiling process.
The present invention coordinates existing hot continuous rolling process to can be obtained intensity, modeling by ingenious rational composition design
The 980MPa grade nanometer precipitation strength super-high strength steels that property and reaming are had excellent performance.Steel plate of the present invention be organized as granular bainite,
Martensite and Nano-Scaled Carbide, bainite crystallite dimension≤5 μm.While tensile strength reaches 980MPa high intensity,
The steel plate has >=15% high-elongation.In composition design, the addition main purpose of high Ti contents is in order in band coil of strip
The tiny Nano-Scaled Carbide of diffusion-precipitation during taking, plays strong precipitating reinforcing effect；A certain amount of V be added then be for
The quantity for further increasing nanometer precipitated phase, plays stronger dispersion-strengthened effect；And on the one hand the design of carbon content will be protected
Intensity is demonstrate,proved, while also to be matched with the content of Ti and V, by experimental study, the content of Nb, Ti, V need to meet 0.15%≤Nb
+ Ti+V≤0.25%；Meanwhile the content of N, Ti and V must satisfy following relationship：0.01%≤(Ti-3.42N)/4+V/4.24
≤ 0.06%.Only meet above-mentioned relation, while coordinating required rolling mill practice, finally obtains ferrite, granular bainite
Microstructure with based on horse Austria constituent element, could obtain this high-strength high-plasticity and the advanced high-strength steel of high hole expandability.
Beneficial effects of the present invention：
(1) present invention is in the composition design using relatively economical, while coordinating existing hot continuous rolling producing line that can produce
Provide the nanometer precipitation strength type high-strength high-plasticity of superhigh intensity and high-elongation and high hole expandability steel plate.
(2) present invention produces yield strength >=900MPa, tensile strength >=980MPa, elongation percentage >=15%, hole expansibility
>=50%, and the hot-rolled high-strength high-chambering steel plate of thickness≤6mm, the high-strength steel of the elongation percentage of the steel plate than current same levels
It is obviously improved, while there is 50% or more high hole expansibility, meet demand of the user to high-strength high-elongation ratio steel, can apply
The high-strength component being thinned and complexity shapes is needed in automobile chassis, crossbeam, wheel etc., is had a good application prospect.
Description of the drawings
Fig. 1 is the typical metallograph of 1 steel of the embodiment of the present invention.
Fig. 2 is the typical metallograph of 3 steel of the embodiment of the present invention.
Fig. 3 is the typical metallograph of 5 steel of the embodiment of the present invention.
Specific implementation mode
With reference to embodiment, the present invention will be further described.
Table 1 is the ingredient of steel of the embodiment of the present invention, and table 2 is the fabrication process parameters of steel of the embodiment of the present invention, and table 3 is this hair
The performance of bright embodiment steel.
Technological process of the embodiment of the present invention is：Converter or electric furnace smelting → vacuum drying oven double refining → strand or ingot casting → steel
Base (ingot) heating → hot rolling+roller repairing → coil of strip, wherein key process parameter is referring to table 2.
Fig. 1-Fig. 3 is respectively the typical metallograph that embodiment 1,3,5 tests steel.The present invention is can be seen that from Fig. 1-Fig. 3
The microscopic structure of steel plate is all tiny bainites of microscopic structure of steel plate and a small amount of martensite (Nano-Scaled Carbide
Can not be differentiated from metallograph), it is strong to assign steel plate superelevation just because of these tiny bainites and a large amount of Nano-Scaled Carbides
Degree and good plasticity.
As known from Table 3, the present invention can produce the high reaming steel of 980MPa grades of hot-rolled high-strengths, and the yield strength of the steel >=
900MPa, tensile strength >=980MPa, elongation percentage >=15%, hole expansibility >=50% show excellent intensity, plasticity and reaming
Property matching.
Claims (10)
1. a kind of high reaming steel of 980MPa grades of hot-rolled high-strength, chemical component weight percentage are：C：0.05~0.10%,
Si：0.1~0.8%, Mn：1.5~2.5%, P≤0.015%, S≤0.005%, O≤0.003%, Al：0.02~0.08%,
N≤0.005%, Ti：0.08~0.15%, Nb：0.02~0.06%, Cr：0.1~1.0%, V：0.01~0.10%, remaining
For Fe and inevitable impurity, and above-mentioned element need to meet following relationship simultaneously：0.15%≤Nb+Ti+V≤0.25%,
0.01%≤(Ti-3.42N)/4+V/4.24≤0.06%；
The manufacturing method of the high reaming steel of 980MPa grades of hot-rolled high-strength comprising following steps：
1) it smelts, cast
It smelted, refined by above-mentioned chemical composition, being cast as strand or ingot casting；
2) strand or ingot casting heating
Heating temperature >=1230 DEG C, 1~2 hour heating time；
3) hot rolling+cooling+is batched
Start rolling temperature is 1080~1200 DEG C, and 3~5 passage roughing and accumulative deflection >=50% are carried out at 1000 DEG C or more；
Intermediate base waits for that temperature is 900~950 DEG C, then carries out 3~5 passage finish rolling and accumulative deflection >=70%；Finishing temperature is
800~900 DEG C, steel plate water cooling is batched to 500~600 DEG C with the cooling rate of >=100 DEG C/s after finish to gauge, with≤20 after batching
DEG C/cooling rate of h is cooled to room temperature.
2. the high reaming steel of 980MPa grades of hot-rolled high-strength according to claim 1, which is characterized in that the hot-rolled high-strength
In the chemical composition of high reaming steel：Mn：1.8~2.2%, by weight percentage.
3. the high reaming steel of 980MPa grades of hot-rolled high-strength according to claim 1 or 2, which is characterized in that the hot rolling is high
The microstructure of the high reaming steel of intensity is granular bainite+martensite, wherein there are nanoscale carbonizations in bainite ferrite
Object, crystallite dimension≤5 μm of granular bainite, Nano-Scaled Carbide size≤10nm.
4. the high reaming steel of 980MPa grades of hot-rolled high-strength according to claim 3, which is characterized in that the hot-rolled high-strength
Volume fraction shared by granular bainite is 70~85% in the microstructure of high reaming steel, volume fraction shared by martensite is 15~
30%.
5. the high reaming steel of 980MPa grade hot-rolled high-strengths according to claim 1 or 2 or 4, which is characterized in that the hot rolling
Yield strength >=900MPa of the high reaming steel of high intensity, tensile strength >=980MPa, elongation percentage >=15%, hole expansibility >=50%.
6. the high reaming steel of 980MPa grades of hot-rolled high-strength according to claim 3, which is characterized in that the hot-rolled high-strength
Yield strength >=900MPa of high reaming steel, tensile strength >=980MPa, elongation percentage >=15%, hole expansibility >=50%.
7. the manufacturing method of the high reaming steel of 980MPa grades of hot-rolled high-strength as claimed in any one of claims 1 to 6 comprising such as
Lower step：
1) it smelts, cast
It smelted, refined by chemical composition described in claims 1 or 2, being cast as strand or ingot casting；
2) strand or ingot casting heating
Heating temperature >=1230 DEG C, 1~2 hour heating time；
3) hot rolling+cooling+is batched
Start rolling temperature is 1080~1200 DEG C, and 3~5 passage roughing and accumulative deflection >=50% are carried out at 1000 DEG C or more；
Intermediate base waits for that temperature is 900~950 DEG C, then carries out 3~5 passage finish rolling and accumulative deflection >=70%；Finishing temperature is
800~900 DEG C, steel plate water cooling is batched to 500~600 DEG C with the cooling rate of >=100 DEG C/s after finish to gauge, with≤20 after batching
DEG C/cooling rate of h is cooled to room temperature.
8. the manufacturing method of the high reaming steel of 980MPa grades of hot-rolled high-strength according to claim 7, which is characterized in that described
The microstructure of the high reaming steel of hot-rolled high-strength is granular bainite+martensite, wherein there are nanoscales in bainite ferrite
Carbide, crystallite dimension≤5 μm of granular bainite, Nano-Scaled Carbide size≤10nm.
9. the manufacturing method of the high reaming steel of 980MPa grades of hot-rolled high-strength according to claim 8, which is characterized in that described
Volume fraction shared by granular bainite is 70~85% in the microstructure of the high reaming steel of hot-rolled high-strength, volume shared by martensite
Score is 15~30%.
10. according to the manufacturing method of the high reaming steel of 980MPa grades of hot-rolled high-strengths of claim 7-9 any one of them, feature
It is, yield strength >=900MPa of the high reaming steel of hot-rolled high-strength, tensile strength >=980MPa, elongation percentage >=15%,
Hole expansibility >=50%.
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