CN107881420A - A kind of tensile strength 550Mpa level hot rolled steel plates and its manufacture method - Google Patents
A kind of tensile strength 550Mpa level hot rolled steel plates and its manufacture method Download PDFInfo
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- CN107881420A CN107881420A CN201610866363.2A CN201610866363A CN107881420A CN 107881420 A CN107881420 A CN 107881420A CN 201610866363 A CN201610866363 A CN 201610866363A CN 107881420 A CN107881420 A CN 107881420A
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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
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0226—Hot rolling
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/005—Ferrite
-
- 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
- C21D2211/009—Pearlite
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- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
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- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Heat Treatment Of Sheet Steel (AREA)
- Heat Treatment Of Steel (AREA)
Abstract
The present invention relates to a kind of tensile strength 550Mpa level hot rolled steel plates and its manufacture method, solves existing car wheel with the tensile strength of hot rolled steel plate is low, manufacturing cost is high, the technical problem of wheel rear wheel fatigue behaviour deficiency is made of it.Tensile strength 550Mpa level hot rolled steel plates provided by the invention, the percentage by weight of its chemical composition are：C：0.05%~0.08%, Si：0.05%~0.15%, Mn：1.35%~1.55%, P≤0.012%, S≤0.003%, Nb：0.013%~0.023%, Ti：0.015%~0.025%, Mg：0.0005%~0.0015%, Alt:0.02%~0.05%, remaining is Fe and inevitable impurity.The tensile strength of hot rolled steel plate of the present invention is 550MPa~650MPa；It is mainly used in making car wheel.
Description
Technical field
The present invention relates to a kind of hot rolled steel plate, more particularly to a kind of tensile strength 550Mpa level hot rolled steel plates and its manufacturer
Method, in particular to a kind of tensile strength 550Mpa level high fatigue property hot rolled steel plates and its manufacture method, the hot rolled steel plate
Mainly for the manufacture of car wheel, belong to technical field of iron-base alloy.
Background technology
With the continuous development and growth of auto industry, steel for automobile wheel is continuously increased, and automotive wheel steel is wanted
Seek also more and more higher.In the prior art, automotive wheel is tyre tube wheel, and its wheel wheel is process using shaped steel more, this
Kind technique falls behind, and wheel dead weight is big, and most of wheel uses the wheel steel of tension 380Mpa or 490Mpa rank
Manufacture, such steel tensile strength is not high, and fatigue performance is poor.With the requirement of the energy-saving and environmental protection of auto industry, wheel-use steel material will
Ask and develop to the good direction of high intensity, high fatigue property direction, easy processing, welding performance.
Application publication number is CN102400042A, the Chinese patent document of entitled high-strength hot rolled steel plate and its manufacture method
For Mn, Nb content peak under conditions of more than the present invention, the yield strength of final material is minimum in disclosed technical scheme
410Mpa, the minimum 500Mpa of tensile strength, elongation after fracture minimum 24%, minimum 100,000 times of fatigue life；Fatigability
The key of energy is Control and Inclusion Removal, and the patent application Control and Inclusion Removal core process is Calcium treatment, and calcium control range is 15-
25ppm, main purpose are inclusion modification is floated, but often due to inevitable oxygen between different heats in industrial practice
The fluctuation of content, causes Calcium treatment to tend not to make inclusion modification float, make field trash because Denaturing is unsatisfactory on the contrary and
Staying in turns into fatigue crack source in steel, such case is extremely harmful for wheel-use steel material, because wheel is the safety of vehicle
Part, the fatigue process constantly loaded during military service, unloaded, if a large amount of field trashes, large-sized inclusions, crackle in steel be present
It can germinate at field trash, cause Wheel Fatigue to fail, cause security incident；High-strength hot rolled steel plate tension disclosed in this application
Intensity, fatigue life can not meet the new requirement in market.
Application publication number is CN102127706A, a kind of entitled high intensity high fatigue life heavy truck steel for automobile wheel and
The C content of technical scheme light plate disclosed in the Chinese patent document of its manufacture method is 0.12%~0.14%, welding performance
It is the performance that wheel-use steel material must take into consideration, therefore whole wheel part is to be connected to one by welding manner by wheel and wheel rim
Rise, if carbon equivalent is high, finally easily cause the probability that weld seam nearby occurs failing to greatly increase, for this security of wheel
Do not allow for part, the welding performance of the heavy truck steel for automobile wheel of the patent application publication can not meet that market is new
It is required that.
Application publication number is CN102586678A, entitled Wheel steel for high-strength long-fatigue-life heavy-duty truck and its place
The alloy of steel is designed in the suitable alloy design condition of other elements in technical scheme disclosed in the Chinese patent document of science and engineering skill
Under, also expensive alloy element Mo：0.01%~0.2%, Ni：≤ 1.5%, V：0.01%~0.2%, the material of acquisition resists
Tensile strength is not less than 500Mpa wheel-use steel material；The manufacturing cost of the heavy load truck wheel steel of the patent application publication is high.
The content of the invention
It is an object of the invention to provide a kind of tensile strength 550Mpa level hot rolled steel plates and its manufacture method, solves existing sedan-chair
Car wheel is with the tensile strength of hot rolled steel plate is low, manufacturing cost is high, the technology of wheel rear wheel fatigue behaviour deficiency is made of it
Problem.
The technical solution adopted by the present invention is：A kind of tensile strength 550Mpa level hot rolled steel plates, its chemical component weight hundred
Point ratio is：C：0.05%~0.08%, Si：0.05%~0.15%, Mn：1.35%~1.55%, P≤0.012%, S≤
0.003%th, Nb：0.013%~0.023%, Ti：0.015%~0.025%, Mg：0.0005%~0.0015%, Alt:
0.02%~0.05%, remaining is Fe and inevitable impurity.
The metallographic structure of tensile strength 550Mpa level hot rolled steel plates of the present invention is fine grain ferrite+a small amount of pearlite, institute
It is 10-11 levels to state ferritic grain size in tissue；The upper yield strength R of 3.0~5.0mm thickness hot rolled steel plateseL>=450MPa, resist
Tensile strength RmFor 550MPa~650MPa, elongation after fracture A >=25%；According to《The passenger car wheel performances of GB/T5334-2005
It is required that-minimum the cycle-index of wheel dynamic cornering fatigue test》Flexible life is more than or equal to 150,000 (loading moments
3327Nm), hot rolled steel plate of the present invention is mainly used in the making of car wheel, and wheel rear wheel tool is made using steel plate of the present invention
There is the feature that fatigue behaviour is excellent.
The reasons why chemical composition of tensile strength 550Mpa level hot rolled steel plates of the present invention limits within the above range
It is as follows：
Carbon：Carbon is the essential element for the obdurability for influenceing High-Strength Low-Alloy high strength steel, and carbon increase can improve by force
Degree, but reduce toughness；And in view of the welding process requirement of wheel-use steel material, carbon design is more low better, and the C that the present invention is set contains
Measure as 0.05%~0.08%.
Silicon：Silicon has very strong solution strengthening effect after being dissolved in ferrite, often increases by 0.1% percentage by weight in carbon steel
Silicon, the tensile strength of hot-rolled steel can be made to improve 7.8Mpa~8.8Mpa, yield strength improves 3.9Mpa~4.9Mpa.But silicon contains
Amount significantly increases to toughness and surface quality adverse effect later more than 0.2%, hot rolled steel plate is generated red iron sheet, warp
Leave pit in surface of steel plate after continuous pickling, turn into the formation of crack of Wheel Fatigue process, thus the Si contents that set of the present invention as
0.05%~0.15%.
Manganese：Manganese is the substantially alloyed element of High-Strength Low-Alloy high strength steel, is played a role by solution strengthening, manganese
Addition can reduce the addition of carbon so that steel plate has high intensity, the Mn contents that the present invention is set as 1.35%~
1.55%.
Phosphorus, sulphur：Phosphorus easily brings segregation in High-Strength Low-Alloy high strength steel and deteriorates the adverse effect of toughness, phosphorus meeting
Cause steel " cold short ", the present invention limits P≤0.012%.
Sulphur easily forms manganese sulfide inclusion with manganese, reduces the toughness of steel, and turns into formation of crack in Wheel Fatigue process, because
In this high-strength wheel steel try one's best sulfur content.The present invention refines manganese sulfide inclusion, is scattered, reducing using the processing of magnesium line is fed
Its unfavorable influence to fatigue behaviour.The present invention limits S≤0.003%.
Niobium：Niobium is the main micro alloying element of High-Strength Low-Alloy high strength steel, mainly plays refined crystalline strengthening.One side
Face Nb can significantly improve the recrystallization temperature Tnr of steel, enable the large deformation of course of hot rolling less than its recrystallization temperature Tnr with
Lower progress, so as to obtain austenite structures tiny, containing a large amount of Zona transformans, make the austenite structure before phase transformation as far as possible thin
Change；On the other hand control niobium carbonitrides tiny in cooling procedure to be separated out during controlled rolling and controlled cooling, play precipitation strength work
With improving the intensity of steel.The present invention limits Nb contents as 0.013%~0.023%.
Titanium：Titanium in low-carbon micro steel-alloy, add titanium can crystal grain thinning and precipitation strength, can improve steel yield strength and
Toughness.The improvement of this performance mainly can improve austenite recrystallization temperature and austenite Coarsening Temperature with titanium, so as to the company of raising
Casting is relevant with autstenitic grain size in heating process；NbC precipitation incubation period can be extended by being added while adding Ti in Nb steel,
Make the precipitation time started of the carbide in Nb-Ti clad steels late compared with Nb steel, so that precipitate is more tiny, disperse；By
In titanium at high temperature, TiN high temperature refractory particles can be formed with N, therefore the addition of titanium can also improve the crystal grain of welding heat affected zone
Degree, so as to improve the toughness of the welding heat affected zone of wheel steel weld seam.The present invention limits Ti contents as 0.015%~0.025%.
Magnesium：Steel makes steel inclusion be changed into magnesium aluminate spinel or pure magnesia, chi by aluminum oxide after magnesium is handled
It is very little to be down to 1~2 μm from 3~5 μm, the size of field trash is greatly reduced, reduction prevents wheel-use steel material from being pressed from both sides in fatigue process
Stress concentration causes tired premature failure at debris, greatly promotes the fatigue behaviour of wheel-use steel material.The present invention limit Mg contents as
0.0005%~0.0015%.
Aluminium：The effect of aluminium in the present invention is to play a part of deoxidation, and aluminium is strong oxidizing property formation element, and oxygen shape in steel
Into Al2O3Removed in steel-making.Aluminium is too high to form excessive Al2O3It is mingled with, Al2O3It is mingled with for wheel-use steel material fatigability energy loss
Evil is very big, and wheel-use steel material must be to Al2O3It is mingled with and is controlled.The present invention limits Al content as 0.02%~0.05%.
A kind of manufacture method of tensile strength 550Mpa level hot rolled steel plates, this method include：
Molten steel obtains continuous casting steel billet through continuous casting, wherein the percentage by weight of the ladle chemistry is：C：0.05%~
0.08%th, Si：0.05%~0.15%, Mn：1.35%~1.55%, P≤0.012%, S≤0.003%, Nb：0.013%~
0.023%th, Ti：0.015%~0.025%, Mg：0.0005%~0.0015%, Alt:0.02%~0.05%, surplus is iron
Be unavoidably mingled with；
Continuous casting steel billet carries out hot rolling, described hot rolling is two-part in 1200 DEG C~1240 DEG C after heating 180~240min
Rolling mill practice, roughing are 6 passage tandem rollings, are rolled more than austenite recrystallization temperature, roughing end temp be 1020 DEG C~
1050℃；Finish rolling is 7 passage tandem rollings, is rolled in austenite non-recrystallization humidity province, and finish rolling end temp is 840~880 DEG C；Essence
After rolling, steel plate thickness is 3.0~5.0mm, and section cooling is cooled down using leading portion, section cooling speed cooling velocity >=30 DEG C/s,
Coiling temperature batches to obtain coils of hot-rolled steel when being 560~600 DEG C.
The reasons why hot rolling technology system that the present invention takes, is as follows：
1st, the setting of continuous casting steel billet heating-up temperature and heat time
Continuous casting steel billet tapping temperature and being set at for time ensure Nb, Ti microalloy carbon thick in continuous casting billet, nitridation
The dissolving of composition granule, technical solution of the present invention Nb, Ti content, can be separated out in continuous casting steel billet cooling procedure Nb, Ti microalloy carbon,
Nitride particles, Nb, Ti microalloy carbon now separated out, nitride particles are thick, without invigoration effect；Need before hot rolling
During heating of plate blank, thick Nb, Ti microalloy carbon, nitride are fully dissolved, Nb, Ti element of compound state could so be consolidated
Dissolve in austenite, alternate precipitation is formed in subsequent hot rolling and the phase transformation of cooling procedure, reinforced ferrite, this is for this
Inventive technique scheme is extremely important；Temperature is too low and the heat time is too short, original thick Nb, Ti microalloy in continuous casting steel billet
Carbon, nitride particles can not fully dissolve, and temperature is too high, and the heat time is long, and steel slab surface oxidation and decarbonization is serious, is unfavorable for steel
Plate final performance and surface quality, while also consume the energy.Therefore the present invention set continuous casting steel billet heating-up temperature as 1200 DEG C~
1240 DEG C, the heat time is 180min~240min.
2nd, roughing end temp is set
Rolling process of rough rolling control rolls more than austenite recrystallization temperature, it is ensured that austenite is by repeated deformation and again
Crystallization, obtain uniformly tiny austenite crystal.By theoretical calculation, the lower recrystallization temperature of present component design is 1000 DEG C
Near, therefore the present invention sets roughing end temp as 1020 DEG C~1050 DEG C.
3rd, finish rolling end temp is set
The final rolling temperature of the present invention acts on of both being set with, and is on the one hand rolled, obtained by austenite Unhydrated cement
There is the flat austenite crystal of Zona transformans to inside, it is brilliant to be transformed into tiny ferrite in subsequent laminar cooling process
Grain, plays the effect of refined crystalline strengthening.Crystal grain refinement of the present invention is critically important, and refined crystalline strengthening can not reduce intensity while realize height
Toughness.Another aspect final rolling temperature can not be too low, and too low final rolling temperature easily induces Nb, Ti microalloy carbon, nitride exists
Austenitic state in the operation of rolling separates out, and causes do not have enough precipitates in follow-up phase transition process, influences to separate out by force
Change effect.The lower Ar of present component design3Temperature is 830 DEG C, therefore finish rolling end temp is set as 840 DEG C~880 DEG C.
4th, after finish rolling section cooling mode and cooling velocity setting
The hot rolled steel plate of the present invention, it is that crystal grain is suppressed using fast section cooling speed the purpose of cooling after finish rolling
Grow up with Nb, Ti microalloy carbonitride high temperature section precipitation, therefore the type of cooling be leading portion cooling.By quickly cooling down suppression
Nb, Ti microalloy carbonitride particle processed is in the precipitation of austenite, reservation solid solution Nb, Ti element in deformed austeaite so that
Nb, Ti microalloy carbonitride that small and dispersed is separated out between ferrite area at a lower temperature are possibly realized；Cooling velocity mistake
Slowly, in advance precipitation of Nb, Ti microalloy carbonitride in high temperature deformation austenite can not be suppressed.Therefore present invention setting laminar flow
Cooling stage is cold by force using leading portion, cooling velocity >=30 DEG C/S.
5th, the setting of hot-rolling coiling temperature
Hot-rolling coiling temperature mainly influences materials microstructure, performance.There are Nb, Ti in the present invention, according to the titanium micro-alloyed member of niobium
The optimal Precipitation Temperature of element, 560 DEG C~600 DEG C are designed as by coiling temperature.If coiling temperature be less than 560 DEG C, it will cause Nb,
Ti microalloys carbon, nitride precipitation is suppressed and intensity is insufficient；If coiling temperature is higher than 600 DEG C, it will causes Nb, Ti micro-
Alloy carbonitride precipitation is roughened and causes toughness insufficient, and subsequent user bending, punching press waited cracking problem.
The tensile strength 550Mpa level hot rolled steel plates of the inventive method production, its metallographic structure are fine grain ferrite+few
Pearlite is measured, ferritic grain size is 10-11 levels in the tissue；The upper yield strength R of 3.0~5.0mm thickness hot rolled steel plateseL
>=450MPa, tensile strength RmFor 550MPa~650MPa, elongation after fracture A >=25%.
The inventive method production hot rolled steel plate manufacture car wheel according to《The passenger car wheels of GB/T5334-2005
Can requirement-minimum cycle-index of wheel dynamic cornering fatigue test》Flexible life is more than or equal to 150,000 (loading moments
3327N·m)。
The present invention has following good effect compared with prior art：1st, the present invention passes through suitable composition design and Hot-roller
Skill is designed, and the hot rolled steel plate of the inventive method production is made after wheel while with high intensity with fatigue behaviour and welding
Performance, meet Factory wheel-use steel material plate high intensity is thinned, the demand of high fatigability and weldability.2nd, it is of the invention
Composition design is coordinated conventional TMCP techniques, can be obtained fine grain granulated iron element using low C, middle Mn, low Nb, low Ti component system
Body+a small amount of pearlite, ensure to obtain high intensity and elongation.3rd, present component design is using low C, middle Mn, low Nb, low Ti
Component system, steel plate is set to possess good welding performance.4th, the present invention makes alumina inclusion by suitable field trash handling process
And manganese sulfide inclusion, size is tiny and Dispersed precipitate, reduces the possibility of crackle during fatigue test from field trash crack initiation,
Greatly promote the fatigue behaviour of steel plate.
Brief description of the drawings
Fig. 1 is the metallographic structure photo of the hot rolled steel plate of the embodiment of the present invention 1.
Embodiment
With reference to embodiment 1~3, the present invention will be further described.
Table 1 is the chemical composition (by weight percentage) of steel of the embodiment of the present invention, and surplus is Fe and inevitable impurity.
The chemical composition of the steel of the embodiment of the present invention of table 1, unit：Percentage by weight.
The molten steel for meeting chemical composition requirement is obtained by converter melting, molten steel blows Ar through LF ladle refining furnace refining procedures
Processing, RH stoves carry out vacuum circulation degassing processing and trimming, and the rear sheet billet continuous casting that carries out obtains continuous casting steel billet；Continuous casting steel billet is thick
It is 900~1600mm to spend for 210~230mm, width, and length is 8500~11000mm.
The scale slab of STEELMAKING PRODUCTION delivers to heating furnace reheating, and hot tandem rolling is delivered to after de-scaling of coming out of the stove.Pass through
Roughing and finish rolling Continuous mill train controlled rolling, are batched, section cooling takes leading portion to cool down, and output is qualified after section cooling
Coils of hot-rolled steel.The thickness of hot rolled steel plate is 3.0~5.0mm.Hot rolling technology control parameter is shown in Table 2.
The hot rolling technology control parameter of the embodiment of the present invention of table 2
The tensile strength 550Mpa level hot rolled steel plates obtained using the above method, referring to Fig. 1, the metallographic structure of hot rolled steel plate
For fine grain ferrite+a small amount of pearlite, ferritic grain size is 10-11 levels in the tissue, the upper surrender of hot rolled steel plate
Intensity ReL>=450MPa, tensile strength RmFor 550MPa~650MPa, elongation after fracture A >=25%.
By the obtained hot rolled steel plate of the present invention according to《GB/T228.1-2010 metal material stretching test part 1s：Room temperature
Test method》Tension test is carried out, its mechanical property is shown in Table 3.
The mechanical property of the hot rolled steel plate of the embodiment of the present invention of table 3
| Performance indications | Steel plate thickness/mm | Upper yield strength/Mpa | Tensile strength/Mpa | Elongation after fracture A/% |
| The present invention | 3.0~5.0 | ≥450 | 550-650 | ≥25 |
| Embodiment 1 | 3.0 | 520 | 573 | 30 |
| Embodiment 2 | 3.6 | 515 | 567 | 34 |
| Embodiment 3 | 4.5 | 502 | 568 | 27.5 |
By the car wheel that the obtained hot rolled steel plate of the present invention makes according to《The passenger car wheel performances of GB/T5334-2005
It is required that-minimum the cycle-index of wheel dynamic cornering fatigue test》Flexible life is more than or equal to 150,000 (loading moments
3327N·m)。
In addition to the implementation, the present invention can also have other embodiment.It is all to use equivalent substitution or equivalent transformation shape
Into technical scheme, all fall within the protection domains of application claims.
Claims (5)
1. a kind of tensile strength 550Mpa level hot rolled steel plates, its chemical component weight percentage are：C：0.05%~0.08%,
Si：0.05%~0.15%, Mn：1.35%~1.55%, P≤0.012%, S≤0.003%, Nb：0.013%~
0.023%th, Ti：0.015%~0.025%, Mg：0.0005%~0.0015%, Alt:0.02%~0.05%, remaining is Fe
With inevitable impurity；The metallographic structure of hot rolled steel plate is fine grain ferrite+a small amount of pearlite, ferrite in the tissue
Grain size be 10-11 levels.
2. tensile strength 550Mpa level hot rolled steel plates as claimed in claim 1, it is characterized in that, 3.0~5.0mm thickness hot rolled steel plates
Upper yield strength ReL>=450MPa, tensile strength RmFor 550MPa~650MPa, elongation after fracture A >=25%.
3. tensile strength 550Mpa level hot rolled steel plates as claimed in claim 1, it is characterized in that, the sedan-chair that the hot rolled steel plate makes
The flexible life of car wheel >=150,000 time.
4. a kind of manufacture method of tensile strength 550Mpa level hot rolled steel plates, this method include：
Molten steel obtains continuous casting steel billet through continuous casting, wherein the percentage by weight of the ladle chemistry is：C：0.05%~
0.08%th, Si：0.05%~0.15%, Mn：1.35%~1.55%, P≤0.012%, S≤0.003%, Nb：0.013%~
0.023%th, Ti：0.015%~0.025%, Mg：0.0005%~0.0015%, Alt:0.02%~0.05%, surplus is iron
Be unavoidably mingled with；
Continuous casting steel billet carries out hot rolling, described hot rolling rolls for two-part in 1200 DEG C~1240 DEG C after heating 180~240min
Technique, roughing are 6 passage tandem rollings, are rolled more than austenite recrystallization temperature, and roughing end temp is 1020 DEG C~1050 DEG C；
Finish rolling is 7 passage tandem rollings, is rolled in austenite non-recrystallization humidity province, and finish rolling end temp is 840~880 DEG C；Layer after finish rolling
Stream cooling is cooled down using leading portion, and section cooling speed cooling velocity >=30 DEG C/s, coiling temperature batches when being 560~600 DEG C
Coils of hot-rolled steel.
5. the manufacture method of tensile strength 550Mpa level hot rolled steel plates as claimed in claim 4, it is characterized in that, after finish rolling, control
Steel plate thickness processed is 3.0~5.0mm.
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Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN110938771A (en) * | 2018-09-21 | 2020-03-31 | 上海梅山钢铁股份有限公司 | Hot-rolled steel plate for wheel with tensile strength of 630MPa and manufacturing method thereof |
| CN111321340A (en) * | 2018-12-17 | 2020-06-23 | 上海梅山钢铁股份有限公司 | Hot rolled steel plate with yield strength of 450MPa and manufacturing method thereof |
| CN111378893A (en) * | 2018-12-28 | 2020-07-07 | 上海梅山钢铁股份有限公司 | Hot-rolled steel plate for longitudinal welded pipe with yield strength of 290MPa |
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| CN113969372A (en) * | 2021-10-14 | 2022-01-25 | 北京科技大学 | Low-carbon anti-fatigue steel plate for wind power and preparation method |
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