CN105886924A - Low-alloy steel high in strength and toughness performance and preparing method of low-alloy steel - Google Patents
Low-alloy steel high in strength and toughness performance and preparing method of low-alloy steel Download PDFInfo
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- CN105886924A CN105886924A CN201610273010.1A CN201610273010A CN105886924A CN 105886924 A CN105886924 A CN 105886924A CN 201610273010 A CN201610273010 A CN 201610273010A CN 105886924 A CN105886924 A CN 105886924A
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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
The invention discloses low-alloy steel high in strength and toughness performance and a preparing method of the low-alloy steel. The preparing method is a reasonable matching method for improving the strength and toughness performance in the manner that the aspects of component improvement, short-procedure design in which casting blank reheating is omitted, casting blank core part quality improvement, structure micronization control and rolling schedule optimization are taken into comprehensive consideration, the technical skill potential of modern material machining is fully reflected, and the actions of grain refinement, controlled rolling, rapid cooling and other technology means on steel strengthening and toughening are brought into play. It is ensured that brittle phase crack initiation of products of moderate-thickness plates is reduced and a new structure form is obtained so as to prevent crack expanding, and the breakthrough of the short-procedure technology of direct hot rolling of the ultrahigh strength and toughness steel casting blank is achieved.
Description
Technical field
The present invention relates to technical field of ferrous metallurgy, especially relate to low-alloy steel and the preparation side thereof of a kind of high-strength tenacity energy
Method.
Background technology
High performance steel (HPS) is to have higher intensity, more preferable toughness, solderable compared with a kind of with traditional mild steel
Property, cold formability and the steel of new generation of decay resistance, in actual application, brittle fracture resistance aspect has and significantly carries
High and improve, meet the high-end equipments such as ocean engineering, engineering machinery, bridge construction, pipe-line construction severe working environment,
The requirement to its functional attributes such as the high intensity of steel used, high-ductility toughening, weldability, crack arrest of the alternate load operating mode.
Under current entire society all pays close attention to the background of large-scale component safety, the range of high performance steel will constantly expand
Greatly.
The composition design system of most high performance steels of development is all that carbon containing is in the range of 0.06～0.17% at present
Peritectic steel, and selectively added micro alloying element Nb, V, Ti, Al etc.；General manufacture method generally comprises:
Smelting, refine, sheet billet continuous casting, slab cooling, slab reheating, roughing, finish rolling, quickly cooling (quenched etc.) etc.
Step.
Such as disclosed on 06 27th, 2012 Chinese patent application CN102517518A is recorded a kind of low cost high
Performance X80 pipe line steel and production method thereof, this production method comprises converter smelting, external refining, continuous casting, rolling process,
The reheating temperature of strand is 1170～1230 DEG C, and roughing uses recrystallization rolling, and finish rolling uses the rolling of non-recrystallization and shape
Become processing method acquisition acicular ferrite+bainite+M/A tissue that induction ferrite transformation rolling combines, thus reach
Improve pipeline steel strength, toughness, reduce the purpose of production cost.
Chinese patent application CN104711490A disclosed on 06 17th, 2015 has recorded a kind of low yield strength ratio height
Energy bridge steel and manufacture method thereof, its production method is that the steel billet meeted the requirements is again heated to 1200 DEG C of insulations 1～2h,
Steel billet is carried out two-phase control rolling, use immediately after rolling ultra-rapid cooling with obtain eurypalynous high temperature and low temperature bainite and
The Ma of refinement-Austria's island constituent element composition, while proof strength, it is achieved that high/low temperature toughness and low yield strength ratio target,
To low yield strength ratio high performance bridge steel.
Chinese patent application CN105200336A disclosed in December in 2015 30 days is recorded a kind of based on stress design
Area high-performance large-deformation-resistance pipeline steel and preparation method.This patent system Preparation Method include smelting molten steel, continuous-casting of steel billet,
The operations such as steel billet reheating, controlled rolling, relaxation cooling, acceleration cooling, are as cold as room temperature after steel billet experience continuous casting and reheat
Mode, played reheating system, two benches controlled rolling, accelerate cooling to Austenite Grain Refinement, phase transformation strengthening improve
The effect of the indexs such as product low-temperature flexibility, fracture toughness.
When using above-mentioned common manufacture method to produce this kind of high-performance micro alloyed steel, if not taking strand slighter compress, electricity
Magnetic stirring etc. prevents casting blank defect, improves the important technique measure of slab quality, and strand finally solidifies center can cause hole
The internal soundness problems such as gap, loose, component segregation, have influence on performance uniformity and the quality of final finished thickness direction
Level.
And be cooled in room temperature process at continuous casting, molten steel solidification, C, N compound in steel is concentrated in column crystal or Austria
The crystal boundary of family name's body separates out, and easily forms brittlement phase, and steel billet forms the 3rd brittle temperature zone；If subsequent technique such as steel billet adds again
Thermal system, rolling pattern etc. control lack of standardization, and the easily heredity of these brittlement phase remains in final steel panel products.Work as steel
When product bears the external stress far below its strength degree, parent metal is easily generated the defects such as brittle cracking, has influence on steel
Toughness and tenacity index, show as intensity low, low-temperature flexibility is poor, it is difficult to meet low temperature use environment, component maximization etc.
Requirement to safety.
Thus will be to gas in the steel of refining process and the technological parameter being mingled with in content control, casting process during actual production
The heating cycle that conservative control, slab reheat controls, rolls the control of rolling schedule and rolls rear quickly cooling system etc.
Factors proposes to be strict with, and causes high performance steel whole manufacturing operation length, produces control complexity, to production
Supportability requires height；Steel billet again reheats after being cooled to room temperature and causes manufacturing energy consumption height, the wasting of resources, occurs
The probability of defective work also improves, and eventually affects qualification rate and the profit space of finished product.
Therefore in the urgent need to exploitation a kind of energy shortened process, controlling unit, refinement stocking core structure, postponement are simplified
Or stop the germinating of micro-crack and extension, significantly improve the process control method of the toughness and tenacity of steel, it is achieved boats and ships, bridge,
Production platform and the Development in Domestic of other high-end equipment special-purpose steel iron material.
Summary of the invention
In view of this, it is an object of the invention to provide the low-alloy steel of a kind of high-strength tenacity energy, this low-alloy steel has higher
Toughness and tenacity.Additionally present invention also offers the preparation method of the low-alloy steel of a kind of high-strength tenacity energy, this preparation method
Creating the abbreviated system control method improving low-alloy steel toughness and tenacity, continuous casting billet can directly be become a useful person in hot rolling, changes
Strand rolls off the production line the traditional processing technology that cooling reheats again；Composition is unique with the formulation of technique, defines solely
Special composition design, strand temperature design, tissue miniaturization control, rolling schedule optimization guarantee to improve low-alloy steel obdurability
The practical control technology of energy；Develop low cost, short route, high-performance steel manufacturing technology, it is achieved high-performance steel continuous casting billet
Directly hot rolling is become a useful person technological break-through.Not only greatly reduce cost, improve production efficiency, and can meet well and criticize
Quantify the requirement produced.
For solving above-mentioned technical problem, the technical scheme that the present invention provides is:
The low-alloy steel of a kind of high-strength tenacity energy, including following components in percentage by weight: the C of 0.05%～0.12%；
The Si of 0.15%～0.50%；The Mn of 1.00%～1.80%；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 for the preparation method of the low-alloy steel of a kind of above-mentioned high-strength tenacity energy, comprises the following steps:
A) that complete to smelt, composition are reached the molten steel of requirement and are casting continuously to form the slab of 200-300mm thickness by continuous casting installation for casting,
Wherein the degree of superheat controls at 15-30 DEG C, pulling rate 0.8-1.2m/min, and straightening section casting blank surface temperature controls at 900-950
DEG C, central temperature 1300-1480 DEG C；
B) online quick descaling cooling after ejection, realizes rising again Homogenization Treatments followed by strand heart portion high temperature；
C) treat steel slab surface temperature recovery to 1050～1100 DEG C, steel billet is sent in the direct roughing of follow-up milling train, and control
Between base thickness be 3-4 times of finished product thickness；
D), after roughing deformation terminates, utilize roll mill cooling water that intermediate blank is carried out accelerated surface and cool, surface
Cool to bainitic transformation starting point Bs-50～100 DEG C of scopes；
E) finish rolling stage accumulation reduction ratio controls the scope at 70-75%；
F) specify according to concrete steel grade production technology, control after rolling to be cooled to require final cooling temperature.
Preferably, the molten steel composition smelted in described step (a) controls (Nb+Ti) × N ＜ 135 × 10-10。
Preferably, the beginning temperature that in described step (b), after ejection, casting billet surface water jet descaling is the coldest controls at 800-900
DEG C, when stopping cooling down, steel slab surface temperature is in bainitic transformation starting point Bs-50～100 DEG C of scopes.
Preferably, in described step (c) finishing temperature control of rough rolling step at recrystallization more than final temperature Tnr.
The Advantageous Effects of the present invention:
(1) unique Composition Control: refer to for obtaining the high Strengthening and Toughening performance of the low-alloy high-performance steel that the present invention relates to
Mark, steel necessarily adds some Nb, Ti microalloy element, steel plays obvious crystal grain thinning, disperse educt strong
Change, nitrogen fixation, it is to avoid the harm that nomadic nitrogen brings.Especially Nb can expand recrystallization temperature, makes the steel can be
Higher temperature range completes rolling, reduces the degree of dependence to milling train.
But substantial amounts of C, N compound at hot stage concentrates on the crystalline substance of column crystal or austenite in continuous casting, process of setting
Boundary separates out, and can form brittlement phase, has influence on the toughness of steel, and reduces the carbonization of useful Low-temperature Iron ferritic stage precipitation
The amount of thing, does not has an invigoration effect of due microalloy element, therefore the present invention by Nb, Ti, N content enter
Row controls, and then to C, N compound Secondary phase particle Precipitation Temperature, pattern, the control of quantity, forms direct hot rolling height
The Composition Control that energy steel is unique.
(2) strand on-line cooling system control: force cooling to start temperature, stop the formulation of temperature, quickly by de-scaling
Avoid the temperature range that continuous casting hot stage C, N compound separates out in a large number so that C, N compound has little time to separate out, then
Cold stage separates out with useful pattern, forms unique strand on-line cooling temperature control system.
(3) unique casting billet surface organizational controls: the cooling to slab of the online quick descaling after ejection, it is possible to achieve casting
Base near surface structure refinement.The more refinement of steel plate crystal grain, the crystal boundary that micro-crack runs into when extension is the most, prevents crackle
Branch, roundabout to extend and the slowest even stop, being more conducive to improving the crack arrest characteristic in whole thickness of slab direction；Again may be used
To utilize the high-temperature residual heat Homogenization Treatments in steel billet heart portion, eliminate the operation reheated after letting cool, improve the profit of heat energy
With, reduce heat consumption, form unique casting billet surface organizational controls.
(4) design of workpiece thickness size embodies the pressing to thickness of steel product direction, deformation osmosis, solves
Central tissue loosens problem, refines stocking core structure；Ensure the beneficial effect to performance of the heavy reduction rate at a temperature of Tnr,
It is embodied in the formation of steel plate microstructure thinning and substructure, dislocation strengthening and the contribution margin raising etc. of precipitation strength, improves
The performance uniformity of steel whole thickness section.
(5) after roughing, the quick cooling system of breast roll to semi-finished product can reduce steel when the stop in partial, re-crystallization district
Between, it is to avoid the generation of grain coarsening, reduces the impact on steel toughness that occurs of mixed crystal, and it is thin to improve surface texture further
Change effect.
Therefore the invention improves the abbreviated system control method of low-alloy steel toughness and tenacity, and continuous casting billet can be direct
Hot rolling is become a useful person, and changes strand and rolls off the production line the traditional processing technology that again reheats of cooling；Composition has solely with the formulation of technique
Characteristic, defines unique component design, strand temperature design, organizes miniaturization control, rolling schedule optimization to guarantee to improve
The practical control technology of low-alloy steel toughness and tenacity；Develop low cost, short route, high-performance steel manufacturing technology, it is achieved
The direct hot rolling of high-performance steel continuous casting billet is become a useful person technological break-through.Not only greatly reduce cost, improve production efficiency, and
The requirement of mass production can be met well.
Accompanying drawing explanation
Fig. 1 is the Q460E thickness of slab near surface metallographic structure figure that in the present invention, embodiment 1 obtains；
Fig. 2 is metallographic structure figure at the Q460E thickness of slab 1/4 that in the present invention, embodiment 1 obtains；
Fig. 3 is the X80M thickness of slab near surface metallographic structure figure that in the present invention, embodiment 2 obtains；
Fig. 4 is metallographic structure figure at the X80M thickness of slab 1/4 that in the present invention, embodiment 2 obtains；
Fig. 5 is the Q420qE thickness of slab near surface metallographic structure figure that in the present invention, embodiment 3 obtains；
Fig. 6 is metallographic structure figure at the Q420qE thickness of slab 1/4 that in the present invention, embodiment 3 obtains.
Detailed description of the invention
In order to be further appreciated by the present invention, below in conjunction with embodiment, the preferred embodiment of the invention is described, but should
Working as understanding, these descriptions simply further illustrate inventive feature and advantage rather than the limit to the claims in the present invention
System.
The low-alloy steel of a kind of high-strength tenacity energy, including following components in percentage by weight: the C of 0.05%～0.12%；
The Si of 0.15%～0.50%；The Mn of 1.00%～1.80%；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。
For obtaining the high Strengthening and Toughening performance indications of the low-alloy high-performance steel that the present invention relates to, steel necessarily adds
Nb, V, Ti microalloy element, plays obvious crystal grain thinning, disperse educt strengthening, nitrogen fixation in steel, it is to avoid
The harm that nomadic nitrogen brings.Especially Nb can expand recrystallization temperature, makes steel can complete in higher temperature range
Rolling, reduces the degree of dependence to milling train.
But substantial amounts of C, N compound at hot stage concentrates on the crystalline substance of column crystal or austenite in continuous casting, process of setting
Boundary separates out, and can form brittlement phase, has influence on the toughness of steel, and reduces the carbonization of useful Low-temperature Iron ferritic stage precipitation
The amount of thing, does not has the invigoration effect of due microalloy element, and therefore the present invention is by Nb, V, Ti, N content
It is controlled, and then to C, N compound Secondary phase particle Precipitation Temperature, pattern, the control of quantity, forms direct hot rolling high
The Composition Control that performance steel is unique.
The present invention also provides for the preparation method of the low-alloy steel of a kind of above-mentioned high-strength tenacity energy, comprises the following steps:
A) that complete to smelt, composition are reached the molten steel of requirement and are casting continuously to form the slab of 200-300mm thickness by continuous casting installation for casting,
Wherein the degree of superheat controls at 15-30 DEG C, pulling rate 0.8-1.2m/min, and straightening section casting blank surface temperature controls at 900-950
DEG C, central temperature 1300-1480 DEG C；
B) online quick descaling cooling after ejection, realizes rising again Homogenization Treatments followed by strand heart portion high temperature；
C) treat steel slab surface temperature recovery to 1050～1100 DEG C, steel billet is sent in the direct roughing of follow-up milling train, and control
Between base thickness be 3-4 times of finished product thickness；
D), after roughing deformation terminates, utilize roll mill cooling water that intermediate blank is carried out accelerated surface and cool, surface
Cool to Bs-50～100 DEG C of scopes；
E) finish rolling stage accumulation reduction ratio controls the scope at 70-75%；
F) specify according to concrete steel grade production technology, control after rolling to be cooled to require final cooling temperature.
Completing in above-mentioned steps a) is smelted, composition reaches the molten steel of requirement, including following components in percentage by weight:
The C of 0.05%～0.12%；The Si of 0.15%～0.50%；The Mn of 1.00%～1.80%；P≤0.015%；S≤0.005%；
Nb+Ti≤0.10%；Mo≤0.30%；Cu≤0.30%；Ni≤0.30%；Cr≤0.30%；Remaining is that Fe is with 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 after ejection, realizes rising again Homogenization Treatments followed by strand heart portion high temperature.Preferably,
The beginning temperature that in described step (b), after ejection, casting billet surface water jet descaling is the coldest controls at 800-900 DEG C, stops cooling
Time steel slab surface temperature in Bs-50～100 DEG C of scopes.Present invention improves over strand on-line cooling system control: pass through de-scaling
Force cooling to start temperature, stop the formulation of temperature, quickly avoid the temperature that continuous casting hot stage C, N compound separates out in a large number
Degree scope so that C, N compound has little time to separate out, then separates out with useful pattern at cold stage, forms uniqueness
Strand on-line cooling temperature control system.Present invention employs the casting billet surface organizational controls of uniqueness: online fast after ejection
The speed de-scaling cooling to slab, it is possible to achieve strand near surface structure refinement.The more refinement of steel plate crystal grain, micro-crack is in extension
Time the crystal boundary that runs into the most, prevent the branch of crackle, roundabout so that extend and the slowest even stop, being more conducive to carrying
The crack arrest characteristic in high whole thickness of slab direction；The high-temperature residual heat Homogenization Treatments in steel billet heart portion can be utilized again, eliminate and let cool
The operation of rear reheating, improves the utilization of heat energy, reduces heat consumption, forms unique casting billet surface organizational controls.
Treat steel slab surface temperature recovery to 1050～1100 DEG C, steel billet is sent into the direct roughing of follow-up milling train, and controls middle
Base thickness is 3-4 times of finished product thickness.Preferably, in above-mentioned steps (c) finishing temperature control of rough rolling step at Tnr
Above.In the present invention, the design of workpiece thickness size embodies the pressing to thickness of steel product direction, deformation osmosis,
Solve central tissue to loosen problem, refine stocking core structure；Ensure useful to performance of the heavy reduction rate at a temperature of Tnr
Effect, is embodied in the contribution margin raising etc. of the formation of steel plate microstructure thinning and substructure, dislocation strengthening and precipitation strength,
Improve the performance uniformity of steel whole thickness section.
After roughing deformation terminates, utilizing roll mill cooling water that intermediate blank is carried out accelerated surface and cool, surface is cold
But Bs-50～100 DEG C of scopes it are cooled to.In the present invention, after roughing, the quick cooling system of breast roll to semi-finished product can subtract
Few steel is in the time of staying in partial, re-crystallization district, it is to avoid the generation of grain coarsening, and that reduces mixed crystal the shadow to steel toughness occurs
Ring, and improve surface texture thinning effect further.
The invention provides a kind of from composition improve, omit strand reheat short route design, strand heart portion quality improve,
Tissue miniaturization control, rolling schedule optimization aspect consider the reasonably combined method 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 to steel
The effect of Strengthening and Toughening, it is ensured that cut deal product reduces brittlement phase crack initiation, obtains new tissue topography to stop crackle to expand
Exhibition, it is achieved the short route technological break-through of the direct hot rolling of ultra-high strength and toughness steel strand.
Raw material that the present invention does not elaborates, method and device etc. are prior art.
In order to be further appreciated by the present invention, below in conjunction with the low-alloy of a kind of high-strength tenacity energy that the present invention is provided by embodiment
Steel 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 addition is 0.032%, elemental gas N content is detected as the composition of 42ppm
The molten steel having reached Q460E requirement is casting continuously to form the steel billet of 250mm by continuous casting installation for casting, controls pouring temperature, pulling rate and two
The cooperation of cold water water distribution system, the strand straightening section surface temperature of detection is 913 DEG C, central temperature 1308 DEG C.
Then casting blank surface temperature starts de-scaling cooling when 825 DEG C, and when cooling stops, detection steel slab surface temperature is 610
℃。
Then strand cutting scale, waits that on roller-way steel billet returns red, and surface temperature goes back up to start when 1055 DEG C directly to roll
System, rough rolling step finishing temperature 965 DEG C, workpiece thickness 135mm, roughing afer bay roller continuous coo1ing is to 600 DEG C,
40mm steel plate is made in finish to gauge, is quickly cooled to 580 DEG C after rolling, and then carries out follow-up product inspection.
The Q460E steel obtaining the present embodiment carries out mechanical properties test, the results are shown in Table 1, and its metallographic structure figure is shown in Fig. 1
With Fig. 2.
Embodiment 2
By complete smelt, in steel, Nb+Ti addition is 0.051%, elemental gas N content is detected as the composition of 25ppm
The molten steel having reached X80M requirement is casting continuously to form the steel billet of 300mm by continuous casting installation for casting, controls pouring temperature, pulling rate and two
The cooperation of cold water water distribution system, the strand straightening section surface temperature of detection is 906 DEG C, central temperature 1475 DEG C.
Then casting blank surface temperature starts de-scaling cooling when 890 DEG C, and when cooling stops, detection steel slab surface temperature is 570
℃。
Then strand cutting scale, waits that on roller-way steel billet returns red, and surface temperature goes back up to start when 1098 DEG C directly to roll
System, rough rolling step finishing temperature 1000 DEG C, workpiece thickness 100mm, roughing afer bay roller continuous coo1ing to 580 DEG C,
Finally it is rolled into 26.4mm steel plate, after rolling, is quickly cooled to 280 DEG C, then carry out follow-up product inspection.
The X80M steel obtaining the present embodiment carries out mechanical properties test, the results are shown in Table 1, and its metallographic structure figure is shown in Fig. 3
With Fig. 4.
Embodiment 3
By complete smelt, in steel, Nb+Ti addition is 0.028%, elemental gas N content is detected as the composition of 37ppm
Reached the molten steel that Q420qE requires and be casting continuously to form the steel billet of 300mm by continuous casting installation for casting, control pouring temperature, pulling rate and
The cooperation of secondary cooling water water distribution system, the strand straightening section surface temperature of detection is 933 DEG C, central temperature 1421 DEG C.
Then casting blank surface temperature starts de-scaling cooling when 885 DEG C, and when cooling stops, detection steel slab surface temperature is 590
℃。
Then strand cutting scale, waits that on roller-way steel billet returns red, and surface temperature goes back up to start when 1077 DEG C directly to roll
System, rough rolling step finishing temperature 950 DEG C, workpiece thickness 120mm, roughing afer bay roller continuous coo1ing is to 550 DEG C,
32mm steel plate is made in finish to gauge, is quickly cooled to 500 DEG C after rolling, and then carries out follow-up product inspection.
The Q420qE steel obtaining 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 table 1 embodiment gained low-alloy steel
The explanation of above example is only intended to help to understand method and the core concept thereof of the present invention.It should be pointed out that, for
For those skilled in the art, under the premise without departing from the principles of the invention, it is also possible to the present invention is carried out
Some improvement and modification, these improve and modify in the protection domain also falling into the claims in the present invention.
Described above to the disclosed embodiments, makes professional and technical personnel in the field be capable of or uses the present invention.Right
Multiple amendment in these embodiments is apparent from for those skilled in the art, defined herein one
As principle can realize in other embodiments without departing from the spirit or scope of the present invention.Therefore, this
The bright the embodiments shown herein that is not intended to be limited to, and be to fit to and principles disclosed herein and features of novelty
Consistent widest range.
Claims (6)
1. a high-strength tenacity can low-alloy steel, it is characterised in that include following components in percentage by weight: 0.05%～
The C of 0.12%；The Si of 0.15%～0.50%；The Mn of 1.00%～1.80%；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 the most miscellaneous
Matter.
Low-alloy steel the most according to claim 1, it is characterised in that the percentage by weight numerical value of Nb, Ti and N
Meet (Nb+Ti) × N ＜ 135 × 10-10。
3. high-strength tenacity described in a claim 1 can the preparation method of low-alloy steel, it is characterised in that include with
Lower step:
A) that complete to smelt, composition are reached the molten steel of requirement and are casting continuously to form the slab of 200-300mm thickness by continuous casting installation for casting,
Wherein the degree of superheat controls at 15-30 DEG C, pulling rate 0.8-1.2m/min, and straightening section casting blank surface temperature controls at 900-950
DEG C, central temperature 1300-1480 DEG C；
B) online quick descaling cooling after ejection, realizes rising again Homogenization Treatments followed by strand heart portion high temperature；
C) treat steel slab surface temperature recovery to 1050～1100 DEG C, steel billet is sent in the direct roughing of follow-up milling train, and control
Between base thickness be 3-4 times of finished product thickness；
D), after roughing deformation terminates, utilize roll mill cooling water that intermediate blank is carried out accelerated surface and cool, surface
Cool to bainitic transformation starting point Bs-50～100 DEG C of scopes；
E) finish rolling stage accumulation reduction ratio controls the scope at 70-75%；
F) specify according to concrete steel grade production technology, control after rolling to be cooled to require final cooling temperature.
Preparation method the most according to claim 3, it is characterised in that the molten steel composition smelted in described step (a)
Middle control (Nb+Ti) × N ＜ 135 × 10-10。
Preparation method the most according to claim 3, it is characterised in that casting billet surface after ejection in described step (b)
The coldest beginning temperature of water jet descaling controls at 800-900 DEG C, and when stopping cooling, steel slab surface temperature is opened at bainitic transformation
Initial point Bs-50～100 DEG C of scopes.
Preparation method the most according to claim 3, it is characterised in that the finish to gauge of rough rolling step in described step (c)
Temperature controls at recrystallization more than final temperature Tnr.
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| CN110653352A (en) * | 2019-11-06 | 2020-01-07 | 湖南华菱湘潭钢铁有限公司 | Method for controlling surface crack of casting blank initiated by proeutectoid ferrite |
| CN112143959A (en) * | 2019-06-27 | 2020-12-29 | 宝山钢铁股份有限公司 | Steel plate with low yield ratio, high toughness and excellent weldability and manufacturing method thereof |
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| CN113667888A (en) * | 2021-07-14 | 2021-11-19 | 武汉钢铁有限公司 | 690 MPa-grade low-silicon corrosion-resistant bridge steel and preparation method thereof |
| CN114480976A (en) * | 2022-02-27 | 2022-05-13 | 湖南华菱湘潭钢铁有限公司 | High-temperature rolled Q420qE bridge structural steel plate and production method thereof |
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