CN105886924B - A kind of low-alloy steel of high-strength tenacity energy and preparation method thereof - Google Patents
A kind of low-alloy steel of high-strength tenacity energy and preparation method thereof Download PDFInfo
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- CN105886924B CN105886924B CN201610273010.1A CN201610273010A CN105886924B CN 105886924 B CN105886924 B CN 105886924B CN 201610273010 A CN201610273010 A CN 201610273010A CN 105886924 B CN105886924 B CN 105886924B
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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
- C22C38/18—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
- 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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- 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
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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
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
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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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- 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
- C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
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Abstract
Low-alloy steel the invention discloses a kind of high-strength tenacity energy and preparation method thereof, the preparation method improves from composition, omit the short route design that strand is reheated, strand center portion quality improves, tissue miniaturization control, rolling schedule optimization aspect considers the reasonably combined method for improving toughness and tenacity, fully demonstrate the technology potentiality of modern material processing, play crystal grain refinement, controlled rolling, the effects of the process meanses to steel Strengthening and Toughening such as quick cooling, ensure that cut deal product reduces brittlement phase crack initiation, new tissue topography is obtained with Anticrack, realize the short route technological break-through of the ultra-high strength and toughness direct hot rolling of steel strand.
Description
Technical field
The present invention relates to technical field of ferrous metallurgy, low-alloy steel and its preparation more particularly, to a kind of high-strength tenacity energy
Method.
Background technology
High performance steel (HPS) is that a kind of have intensity higher, more preferable toughness, solderable compared with traditional mild steel
Property, the steel of new generation of cold formability and decay resistance, brittle fracture resistance aspect is significantly improved in actual application
And improvement, meet severe operating environment, the alternating download of the high-end equipment such as ocean engineering, engineering machinery, bridge construction, pipe-line construction
Requirement of the lotus operating mode to its functional attributes such as high intensity, high-plastic toughening, weldability, the crack arrest of steel used.Current whole
Under society's all backgrounds of concern large-scale component security, the use scope of high performance steel will constantly expand.
The composition design system of most high performance steels of development is all carbon containing in 0.06~0.17% scope at present
Interior peritectic steel, and selectively added micro alloying element Nb, V, Ti, Al etc.；General manufacture method is generally comprised：Smelting
The steps such as refining, refining, sheet billet continuous casting, slab cooling, slab reheating, roughing, finish rolling, quick cooling (quenched etc.).
A kind of low cost is recorded within such as 06 month 2012 in Chinese patent application CN102517518A disclosed in 27 days high
Performance X80 pipe line steels and its production method, the production method include converter smelting, external refining, continuous casting, rolling process, strand
Relation reheating temperature be 1170~1230 DEG C, roughing using recrystallization roll, finish rolling using it is non-recrystallization rolling and it is deformation induced
The processing method that ferrite transformation rolling is combined obtains acicular ferrite+bainite+M/A tissues, so as to reach raising pipeline
Hardness of steel, toughness, reduce the purpose of production cost.
A kind of low yield strength ratio property high is recorded in Chinese patent application CN104711490A disclosed in 17 days within 06 month 2015
Energy bridge steel and its manufacture method, its production method are that the steel billet that will be meeted the requirements is again heated to 1200 DEG C of 1~2h of insulation, to steel
Base carries out two-phase control rolling, uses ultra-rapid cooling after rolling immediately to obtain high temperature and low temperature bainite and the refinement of polymorphic type
Ma-Austria's island constituent element composition, while proof strength, realizes high/low temperature toughness and low yield strength ratio target, obtains low yield strength ratio
High performance bridge steel.
Record a kind of based on stress design in Chinese patent application CN105200336A disclosed in 30 days December in 2015
Area high-performance large-deformation-resistance pipeline steel and preparation method.The patent preparation method includes smelting molten steel, continuous-casting of steel billet, steel billet
The operations such as reheating, controlled rolling, relaxation cooling, acceleration cooling, are as cold as the mode of normal temperature reheating, hair after steel billet experience continuous casting
Waved reheating system, two benches controlled rolling, accelerate cooling Austenite Grain Refinement, phase transformation strengthening are improved product low-temperature flexibility,
The effect of the indexs such as fracture toughness.
When producing this kind of high-performance micro alloyed steel using above-mentioned common manufacture method, if do not take strand slighter compress,
Electromagnetic agitation etc. prevents casting blank defect, improves the important technique measure of slab quality, and strand finally solidifies center can cause hole
The internal soundness problem such as gap, loose, component segregation, has influence on the performance uniformity and quality water of final finished thickness direction
It is flat.
And in continuous casting, molten steel solidification are cooled to room temperature process, C, N compound in steel are concentrated in column crystal or Ovshinsky
The crystal boundary of body is separated out, and easily forms brittlement phase, and steel billet forms the 3rd brittle temperature zone；If subsequent technique such as steel billet reheats system
Degree, rolling pattern etc. control are lack of standardization, and the easy heredity of these brittlement phases is remained into final steel sheet product.When product made from steel bears
Far below its strength degree external stress when, parent metal is also easy to produce the defects such as brittle cracking, has influence on the toughness and tenacity of steel
Index, shows as low intensity, and low-temperature flexibility is poor, it is difficult to meet the requirement to security such as low temperature use environment, component maximization.
Thus gas in the steel of refining process and the technique being mingled with content control, casting process are joined during actual production
Count reasonable control, the heating cycle that slab is reheated controls, rolls the control of rolling schedule and rolls rear quick cooling system etc.
Factors propose to be strict with, and cause high performance steel entirely to manufacture operation long, production control complexity, ensured to production
Capability Requirement is high；Steel billet to be cooled to after room temperature reheat again and causes to manufacture high energy consumption, the wasting of resources, defective work occurs
Probability also improve, eventually affect the qualification rate and profit space of finished product.
Therefore in the urgent need to exploitation one kind can shorten technological process, simplify control link, refinement stocking core structure, postponement
Or prevent micro-crack germinating and extension, significantly improve steel toughness and tenacity process control method, realize ship, bridge, adopt
The Development in Domestic of oily platform and other high-end special ferrous materials of equipment.
The content of the invention
In view of this, it is an object of the invention to provide a kind of high-strength tenacity can low-alloy steel, the low-alloy steel have compared with
Toughness and tenacity high.The preparation method of the other low-alloy steel present invention also offers a kind of high-strength tenacity energy, the preparation method
The abbreviated system control method for improving low-alloy steel toughness and tenacity is created, continuous casting billet can directly become a useful person, change in hot rolling
Strand is offline to cool down the traditional processing technology for reheating again；Composition is unique with the formulation of technique, form it is unique into
Setting up meter, strand temperature design, tissue miniaturization control, rolling schedule optimization separately ensures to improve the practicality of low-alloy steel toughness and tenacity
Control technology；Low cost, short route, high-performance steel manufacturing technology are developed, realizes that the direct hot rolling of high-performance steel continuous casting billet is become a useful person
Technological break-through.Cost is not only greatly reduced, production efficiency is improve, and can well meet the requirement of mass production.
To solve above-mentioned technical problem, the technical scheme that the present invention is provided is：
A kind of low-alloy steel of high-strength tenacity energy, including following components in percentage by weight：0.05%~0.12% C；
0.15%~0.50% Si；1.00%~1.80% Mn；P≤0.015%；S≤0.005%；Nb+Ti≤0.10%；Mo
≤ 0.30%；Cu≤0.30%；Ni≤0.30%；Cr≤0.30%；Remaining is Fe and inevitable impurity.
Preferably, the percentage by weight numerical value of Nb, Ti and N meets (Nb+Ti) × N ＜ 135 × 10-10。
The present invention also provides a kind of preparation method of the low-alloy steel of above-mentioned high-strength tenacity energy, comprises the following steps：
A) molten steel that smelt completion, composition reaches requirement is casting continuously to form the thick slabs of 200-300mm by continuous casting installation for casting,
Wherein at 15-30 DEG C, pulling rate 0.8-1.2m/min, straightening section casting blank surface temperature is controlled at 900-950 DEG C for degree of superheat control, in
1300-1480 DEG C of heart temperature；
B) online quick descaling cooling after ejection, Homogenization Treatments of rising again are realized followed by strand center portion high temperature；
C) steel slab surface temperature recovery to 1050~1100 DEG C is treated, steel billet is sent into the direct roughing of follow-up milling train, and control
Workpiece thickness is 3-4 times of finished product thickness；
D) after roughing deformation terminates, accelerated surface is carried out to middle base using roll mill cooling water and is cooled, table
Face cools to bainitic transformation starting point Bs-50~100 DEG C scope；
E) scope of the finish rolling stage accumulation reduction ratio control in 70-75%；
F) specified according to specific steel grade production technology, control is cooled to and requires final cooling temperature after rolling.
Preferably, (Nb+Ti) × N ＜ 135 × 10 are controlled in the molten steel composition smelted in the step (a)-10。
Preferably, the strong cold started temperature of casting billet surface water jet descaling is controlled in 800-900 after ejection in the step (b)
DEG C, steel slab surface temperature is in bainitic transformation starting point Bs-50~100 DEG C scope when stopping cooling down.
Preferably, the finishing temperature control of rough rolling step is recrystallizing more than final temperature Tnr in the step (c).
Advantageous Effects of the invention：
(1) unique Composition Control：For the Strengthening and Toughening performance high for obtaining low-alloy high-performance steel of the present invention refers to
Mark, necessarily added in steel some Nb, Ti microalloy elements, obvious crystal grain thinning, disperse educt reinforcing, solid is played in steel
Nitrogen is acted on, it is to avoid the harm that nomadic nitrogen brings.Especially Nb can expand recrystallization temperature, allow steel in temperature model higher
Completion rolling is enclosed, the degree of dependence to milling train is reduced.
But the crystalline substance of column crystal or austenite is concentrated in continuous casting, process of setting in substantial amounts of C, N compound of hot stage
Boundary separates out, and can form brittlement phase, has influence on the toughness of steel, and reduces the carbide that the beneficial low temperature ferrite stage separates out
Amount, does not have an invigoration effect of due microalloy element, thus the present invention by Nb, Ti, N content be controlled, and then
To C, N compound Secondary phase particle Precipitation Temperature, pattern, quantity control, form the unique Composition Control of direct hot rolling high-performance steel.
(2) strand on-line cooling system control：Cooling started temperature is forced by de-scaling, stops the formulation of temperature, quickly
Avoid the temperature range that continuous casting hot stage C, N compound are largely separated out so that C, N compound have little time to separate out, then in low temperature rank
Section is separated out with beneficial pattern, forms unique strand on-line cooling temperature control system.
(3) unique casting billet surface organizational controls：The cooling of online quick descaling after ejection to slab, it is possible to achieve casting
Base near surface structure refinement.Steel plate crystal grain gets over refinement, and the crystal boundary that micro-crack runs into extension is more, prevents dividing for crackle
Branch, it is roundabout so that extension it is slower in addition stop, being more conducive to improving the crack arrest characteristic in whole thickness of slab direction；Can utilize again
The high-temperature residual heat Homogenization Treatments of steel billet center portion, eliminate the operation reheated after letting cool, and improve the utilization of heat energy, reduce heat
Amount consumption, forms unique casting billet surface organizational controls.
(4) design of workpiece thickness size embodies pressing, the deformation osmosis to thickness of steel product direction, in solution
The loose problem of heart tissue, refines stocking core structure；Ensure beneficial effect of the heavy reduction rate at a temperature of Tnr to performance, embody
In the formation of steel plate microstructure thinning and substructure, contribution margin raising of dislocation strengthening and precipitation strength etc. improves steel whole
The performance uniformity of individual thickness section.
(5) steel can be reduced to the quick cooling system of breast roll of semi-finished product after roughing in the stop in partial, re-crystallization area
Between, it is to avoid the generation of grain coarsening, reduces influence of the appearance of mixed crystal to steel toughness, and further improve surface texture refinement effect
Really.
Therefore the invention improves the abbreviated system control method of low-alloy steel toughness and tenacity, and continuous casting billet can be straight
Connect hot rolling to become a useful person, change the traditional processing technology that the offline cooling of strand is reheated again；Composition has only with the formulation of technique
Characteristic, foring unique component design, strand temperature design, tissue miniaturization control, rolling schedule optimization ensures to improve low conjunction
The practical control technology of golden steel toughness and tenacity；Low cost, short route, high-performance steel manufacturing technology are developed, high-performance steel is realized
The direct hot rolling of continuous casting billet is become a useful person technological break-through.Cost is not only greatly reduced, production efficiency is improve, and can meet well
The requirement of mass production.
Brief description of the drawings
Fig. 1 is the Q460E thickness of slab near surface metallographic structure figures that embodiment 1 is obtained in the present invention；
Fig. 2 is metallographic structure figure at embodiment 1 is obtained in the present invention Q460E thicknesss of slab 1/4；
Fig. 3 is the X80M thickness of slab near surface metallographic structure figures that embodiment 2 is obtained in the present invention；
Fig. 4 is metallographic structure figure at embodiment 2 is obtained in the present invention X80M thicknesss of slab 1/4；
Fig. 5 is the Q420qE thickness of slab near surface metallographic structure figures that embodiment 3 is obtained in the present invention；
Fig. 6 is metallographic structure figure at embodiment 3 is obtained in the present invention Q420qE thicknesss of slab 1/4.
Specific embodiment
For a further understanding of the present invention, the preferred embodiment of the invention is described with reference to embodiment, but
It should be appreciated that these descriptions simply further illustrate feature of the invention and advantage, rather than the limit to the claims in the present invention
System.
A kind of low-alloy steel of high-strength tenacity energy, including following components in percentage by weight：0.05%~0.12% C；
0.15%~0.50% Si；1.00%~1.80% Mn；P≤0.015%；S≤0.005%；Nb+Ti≤0.10%；Mo
≤ 0.30%；Cu≤0.30%；Ni≤0.30%；Cr≤0.30%；Remaining is Fe and inevitable impurity.Preferably, Nb,
The percentage by weight numerical value of Ti and N meets (Nb+Ti) × N ＜ 135 × 10-10。
To obtain the Strengthening and Toughening performance indications high of low-alloy high-performance steel of the present invention, necessarily added in steel
Nb, V, Ti microalloy element, play obvious crystal grain thinning, disperse educt reinforcing, nitrogen fixation, it is to avoid nomadic nitrogen band in steel
The harm for coming.Especially Nb can expand recrystallization temperature, steel is completed rolling in temperature range higher, reduce to rolling
The degree of dependence of machine.
But the crystalline substance of column crystal or austenite is concentrated in continuous casting, process of setting in substantial amounts of C, N compound of hot stage
Boundary separates out, and can form brittlement phase, has influence on the toughness of steel, and reduces the carbide that the beneficial low temperature ferrite stage separates out
Amount, does not have the invigoration effect of due microalloy element, therefore the present invention is controlled by Nb, V, Ti, N content, enters
And to C, N compound Secondary phase particle Precipitation Temperature, pattern, quantity control, formed direct hot rolling high-performance steel it is unique into sub-control
System.
The present invention also provides a kind of preparation method of the low-alloy steel of above-mentioned high-strength tenacity energy, comprises the following steps：
A) molten steel that smelt completion, composition reaches requirement is casting continuously to form the thick slabs of 200-300mm by continuous casting installation for casting,
Wherein at 15-30 DEG C, pulling rate 0.8-1.2m/min, straightening section casting blank surface temperature is controlled at 900-950 DEG C for degree of superheat control, in
1300-1480 DEG C of heart temperature；
B) online quick descaling cooling after ejection, Homogenization Treatments of rising again are realized followed by strand center portion high temperature；
C) steel slab surface temperature recovery to 1050~1100 DEG C is treated, steel billet is sent into the direct roughing of follow-up milling train, and control
Workpiece thickness is 3-4 times of finished product thickness；
D) after roughing deformation terminates, accelerated surface is carried out to middle base using roll mill cooling water and is cooled, table
Face cools to Bs-50~100 DEG C scope；
E) scope of the finish rolling stage accumulation reduction ratio control in 70-75%；
F) specified according to specific steel grade production technology, control is cooled to and requires final cooling temperature after rolling.
Completion in above-mentioned steps a) is smelted, composition reaches the molten steel of requirement, including following components in percentage by weight：
0.05%~0.12% C；0.15%~0.50% Si；1.00%~1.80% Mn；P≤0.015%；S≤
0.005%；Nb+Ti≤0.10%；Mo≤0.30%；Cu≤0.30%；Ni≤0.30%；Cr≤0.30%；Remaining be Fe and
Inevitable impurity.Preferably, the percentage by weight numerical value of Nb, Ti and N meets (Nb+Ti) × N ＜ 135 × 10-10。
Online quick descaling cooling, Homogenization Treatments of rising again are realized followed by strand center portion high temperature after ejection.Preferably,
The strong cold started temperature of casting billet surface water jet descaling is controlled at 800-900 DEG C after ejection in the step (b), stops plate during cooling
Base surface temperature is in Bs-50~100 DEG C scope.Present invention improves over strand on-line cooling system control：Force cold by de-scaling
But started temperature, the formulation of stopping temperature, quickly avoid the temperature ranges that continuous casting hot stage C, N compound are largely separated out so that
C, N compound have little time to separate out, then are separated out with beneficial pattern in cold stage, form unique strand on-line cooling temperature control
System.Present invention employs unique casting billet surface organizational controls：The cooling of online quick descaling after ejection to slab, can
To realize strand near surface structure refinement.Steel plate crystal grain gets over refinement, and the crystal boundary that micro-crack runs into extension is more, prevents and splits
It is the branch of line, roundabout so that extension is slower or even stops, and is more conducive to improving the crack arrest characteristic in whole thickness of slab direction；Again may be used
Using the high-temperature residual heat Homogenization Treatments of steel billet center portion, to eliminate the operation reheated after letting cool, the utilization of heat energy is improve,
Heat consumption is reduced, unique casting billet surface organizational controls is formed.
Steel slab surface temperature recovery to 1050~1100 DEG C is treated, steel billet is sent into the direct roughing of follow-up milling train, and in control
Between base thickness be 3-4 times of finished product thickness.Preferably, in above-mentioned steps (c) rough rolling step finishing temperature control Tnr with
On.In the present invention, the design of workpiece thickness size embodies pressing, deformation osmosis to thickness of steel product direction, solves
The loose problem of central tissue, refines stocking core structure；Ensure beneficial effect of the heavy reduction rate at a temperature of Tnr to performance, body
Contribution margin raising of the formation of present steel plate microstructure thinning and substructure, dislocation strengthening and precipitation strength etc., improves steel
The performance uniformity of whole thickness section.
After roughing deformation terminates, accelerated surface is carried out to middle base using roll mill cooling water and is cooled, surface
Cool to Bs-50~100 DEG C scope.In the present invention, the quick cooling system of breast roll after roughing to semi-finished product can subtract
Residence time of few steel in partial, re-crystallization area, it is to avoid the generation of grain coarsening, influence of the appearance of mixed crystal to steel toughness is reduced,
And further improve surface texture thinning effect.
Change the invention provides a kind of short route design for improving, omitting strand reheating from composition, strand center portion quality
Kind, tissue miniaturization control, rolling schedule optimization aspect consider the reasonably combined method for improving toughness and tenacity, fully demonstrate
The technology potentiality of modern material processing, play the process meanses such as crystal grain refinement, controlled rolling, quick cooling tough to steel
The effect of change, it is ensured that cut deal product reduces brittlement phase crack initiation, obtains new tissue topography with Anticrack, realizes
The short route technological break-through of the direct hot rolling of ultra-high strength and toughness steel strand.
Raw material, method and device that the present invention is not elaborated etc. is prior art.
For a further understanding of the present invention, a kind of low conjunction of high-strength tenacity energy provided the present invention with reference to embodiment
Jin Gang and preparation method thereof is described in detail, and protection scope of the present invention is not limited by the following examples.
Embodiment 1
By complete smelt, in steel Nb+Ti additions be 0.032%, elemental gas N content is detected as the composition of 42ppm
The molten steel for having reached Q460E requirements is casting continuously to form the steel billet of 250mm, control pouring temperature, pulling rate and secondary cooling water by continuous casting installation for casting
Cooperation with water system, the strand straightening section surface temperature of detection is 913 DEG C, 1308 DEG C of central temperature.
Then casting blank surface temperature starts de-scaling cooling at 825 DEG C, and detection slab surface temperature is 610 when cooling stops
℃。
Then strand cuts scale, waits steel billet to return on roller-way red, and surface temperature starts directly when going back up to 1055 DEG C
Rolling, 965 DEG C of rough rolling step finishing temperature, workpiece thickness 135mm, roughing afer bay roller continuous coo1ing to 600 DEG C, most finish to gauge
40mm steel plates are made, 580 DEG C are quickly cooled to after rolling, then carry out follow-up product inspection.
The Q460E steel obtained to the present embodiment carries out mechanical properties test, the results are shown in Table 1, its metallographic structure figure see Fig. 1 with
Fig. 2.
Embodiment 2
By complete smelt, in steel Nb+Ti additions be 0.051%, elemental gas N content is detected as the composition of 25ppm
The molten steel for having reached X80M requirements is casting continuously to form the steel billet of 300mm by continuous casting installation for casting, and control pouring temperature, pulling rate and secondary cooling water are matched somebody with somebody
The cooperation of water system, the strand straightening section surface temperature of detection is 906 DEG C, 1475 DEG C of central temperature.
Then casting blank surface temperature starts de-scaling cooling at 890 DEG C, and detection slab surface temperature is 570 when cooling stops
℃。
Then strand cuts scale, waits steel billet to return on roller-way red, and surface temperature starts directly when going back up to 1098 DEG C
Rolling, 1000 DEG C of rough rolling step finishing temperature, workpiece thickness 100mm, roughing afer bay roller continuous coo1ing to 580 DEG C, finally
26.4mm steel plates are rolled into, 280 DEG C are quickly cooled to after rolling, then carry out follow-up product inspection.
The X80M steel obtained to the present embodiment carries out mechanical properties test, the results are shown in Table 1, its metallographic structure figure see Fig. 3 with
Fig. 4.
Embodiment 3
By complete smelt, in steel Nb+Ti additions be 0.028%, elemental gas N content is detected as the composition of 37ppm
The molten steel for having reached Q420qE requirements is casting continuously to form the steel billet of 300mm, control pouring temperature, pulling rate and secondary cooling water by continuous casting installation for casting
Cooperation with water system, the strand straightening section surface temperature of detection is 933 DEG C, 1421 DEG C of central temperature.
Then casting blank surface temperature starts de-scaling cooling at 885 DEG C, and detection slab surface temperature is 590 when cooling stops
℃。
Then strand cuts scale, waits steel billet to return on roller-way red, and surface temperature starts directly when going back up to 1077 DEG C
Rolling, 950 DEG C of rough rolling step finishing temperature, workpiece thickness 120mm, roughing afer bay roller continuous coo1ing to 550 DEG C, most finish to gauge
32mm steel plates are made, 500 DEG C are quickly cooled to after rolling, then carry out follow-up product inspection.
The Q420qE steel obtained to the present embodiment carries out mechanical properties test, the results are shown in Table 1, and its metallographic structure figure is shown in Fig. 5
With Fig. 6.
The mechanical properties test data of the embodiment of table 1 gained low-alloy steel
The explanation of above example is only intended to help and understands the method for the present invention and its core concept.It should be pointed out that right
For those skilled in the art, under the premise without departing from the principles of the invention, the present invention can also be carried out
Some improvement and modification, these are improved and modification is also fallen into the protection domain of the claims in the present invention.
The foregoing description of the disclosed embodiments, enables professional and technical personnel in the field to realize or uses the present invention.
It is for those skilled in the art it will be apparent that defined herein one for various modifications of these embodiments
As principle can realize in other embodiments without departing from the spirit or scope of the present invention.Therefore, the present invention will
Will not be intended to be limited to the embodiments shown herein, and be to fit to consistent with principles disclosed herein and features of novelty
Widest range.
Claims (4)
1. a kind of high-strength tenacity can low-alloy steel preparation method, it is characterised in that comprise the following steps：
A) molten steel that smelt completion, composition reaches requirement is casting continuously to form the thick slabs of 200-300mm by continuous casting installation for casting, wherein
At 15-30 DEG C, pulling rate 0.8-1.2m/min, straightening section casting blank surface temperature is controlled in 900-950 DEG C, center temperature for degree of superheat control
1300-1480 DEG C of degree；
The molten steel includes following components in percentage by weight：0.05%~0.12% C；0.15%~0.50% Si；
1.00%~1.80% Mn；P≤0.015%；S≤0.005%；Nb+Ti≤0.10%；Mo≤0.30%；Cu≤0.30%；
Ni≤0.30%；Cr≤0.30%；Remaining is Fe and inevitable impurity；
B) online quick descaling cooling after ejection, Homogenization Treatments of rising again are realized followed by strand center portion high temperature；
C) steel slab surface temperature recovery to 1050~1100 DEG C is treated, steel billet is sent into the middle of the direct roughing of follow-up milling train, and control
Base thickness is 3-4 times of finished product thickness；
D) after roughing deformation terminates, accelerated surface is carried out to middle base using roll mill cooling water and is cooled, surface is cold
But it is cooled to bainitic transformation starting point Bs-50~100 DEG C scope；
E) scope of the finish rolling stage accumulation reduction ratio control in 70-75%；
F) specified according to specific steel grade production technology, control is cooled to and requires final cooling temperature after rolling.
2. preparation method according to claim 1, it is characterised in that controlled in the molten steel composition smelted in the step a)
(Nb+Ti) × N ＜ 135 × 10-10。
3. preparation method according to claim 1, it is characterised in that casting billet surface water spray is removed after ejection in the step b)
The strong cold started temperature of squama is controlled at 800-900 DEG C, and steel slab surface temperature is in bainitic transformation starting point Bs-50 when stopping cooling down
~100 DEG C of scopes.
4. preparation method according to claim 1, it is characterised in that the finishing temperature control of rough rolling step in the step c)
System is in recrystallization more than final temperature Tnr.
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