CN104630628B - A kind of tensile strength >=800MPa grades of welded structural steel and production method - Google Patents
A kind of tensile strength >=800MPa grades of welded structural steel and production method Download PDFInfo
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- CN104630628B CN104630628B CN201510099430.8A CN201510099430A CN104630628B CN 104630628 B CN104630628 B CN 104630628B CN 201510099430 A CN201510099430 A CN 201510099430A CN 104630628 B CN104630628 B CN 104630628B
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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
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0226—Hot rolling
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
Abstract
A kind of tensile strength >=800MPa grades of welded structural steel, its component and wt% are：C：0.002~0.02%、Si：0.03~0.15%、Mn：1.70~2.00%、P：≤0.018%、S：≤0.006%、Ti：0.20~0.35%、N：0.002~0.005%、B：≤0.0005%、Als：0.025~0.05%；Production stage：Base is cast into after being smelted through converter and vacuum drying oven；To heating strand；Roughing；Finish rolling；Section cooling；Batch.The present invention makes elongation percentage A% >=20% on the premise of more than tensile strength 800MPa, yield strength 700MPa is ensured, 40 DEG C of Charpy-V impact power >=70J, and with good welding performance and cold forming capability.
Description
Technical field
The present invention relates to a kind of steel for welded structures and production method, a kind of tensile strength >=800MPa grades is specifically belonged to
Welded structural steel and production method, it is the tensile strength >=800MPa grades of welded structural steel of 2 ~ 12mm to be particularly well-suited to produce thickness
And production method.
Background technology
From the point of view of the development of mechanical engineering field, developed to structure high strengthening, material lightweight.When various machineries set
After the intensity of standby and engineering structure part steel plate is doubled, the thickness of steel plate used can be greatly reduced, so as to reduce steel
Material is consumed, and reduces manufacturing cost.With the development of this trend, its strength character, toughness, weldering to engineering machinery construction material
The requirement for connecing performance cold formability is more prominent, and from for the field prior art situation, some intensity ranks can meet requirement,
But toughness, welding performance cold formability seem not enough, or requirement can be met in performance, but production cost is higher, without
Ji, does not meet industrial policy, through its reason of analyzing and researching, it is believed that one is not make strict control to Ti/C, Ti/N, and two is in hot rolling
Section cooling afterwards uses one section or two-stage cooling mode, but it is shorter that interval time is stagnated in the middle of two-stage cooling.
Through retrieval：
China Patent Publication No. is the document of CN1280206A, it discloses a kind of Ultra-low carbon of 800MPa level yield strengths
Microalloy high strength steel, but the strength fluctuation of steel is larger, and stability is poor, and elongation percentage is not high, and tough implementations are not embodied.
China Patent Publication No. is the document of CN101525717A, it discloses 700MPa grades that a kind of thickness is 3 ~ 6mm
Ti microalloyed ultra-fine grains steel and its production method, it uses CSP casting and rolling process, does not have the cooling of strand and reheated
Journey.The present invention is 800MPa grades of steel for using 2 ~ 12mm of conventional hot continuous rolling machine technique productions, continuous casting steel billet have passed through cooling with
Reheating process, therefore tissue is evenly, performance is more stable.
China Patent Publication No. is the document of CN101768698A, high-strength it discloses a kind for the treatment of of 700MPa grades of Micro Alloying
Steel plate and its manufacture method, its technique are processed 30 ~ 40 minutes in refining furnace, impurity and gas content in strict control steel,
Carry out with the addition of substantial amounts of Cr in controlled rolling and controlled cooling, but the steel again after being casting continuously to form strand.
The content of the invention
It is an object of the invention to overcome the deficiencies in the prior art, there is provided a kind of in guarantee more than tensile strength 800MPa,
On the premise of yield strength 700MPa, and make elongation percentage A% >=20%, -40 DEG C of Charpy-V impact power >=70J, and with good weldering
Connect the welded structural steel and production method of performance and cold forming capability.
Realize the measure of above-mentioned purpose：
A kind of tensile strength >=800MPa grades of welded structural steel, its component and weight percent content are：C：0.002~
0.02%、Si：0.03~0.15%、Mn：1.70~2.00%、P：≤0.018%、S：≤0.006%、Ti：0.20~0.35%、N：0.002
~0.005%、B：≤0.0005%、Als：0.025 ~ 0.05%, remaining is Fe and inevitable impurity；And meet：20≤Ti/C
≤ 50,40≤Ti/N≤70；Metallographic structure is the ferrite group of the ultra-fine black needle-like lower bainite and surplus for being not less than 70%
Knit.
Produce a kind of method of tensile strength >=800MPa grades of welded structural steel, its step：
1）Base is cast into after being smelted through converter and vacuum drying oven；
2）To heating strand, heating-up temperature is incubated 1.5 ~ 2.0h at this temperature at 1320 ~ 1380 DEG C；
3）Roughing is carried out, controls its start rolling temperature at 1080 ~ 1120 DEG C, finishing temperature is 960 ~ 980 DEG C, and rolling pass is
5 ~ 7 passages, make overall compression ratio be not less than 80% after roughing；
4）Finish rolling is carried out, it is 930 ~ 950 DEG C to control its start rolling temperature, and its end temp is 850 ~ 890 DEG C, and rolling pass is
7 passages, the average draught per pass of last 4 passage is controlled 30 ~ 50%；
5）Section cooling, cooling two-stage cooling before and after are carried out, and 20 ~ 50s is spaced between two sections of coolings；Leading portion
Cooling velocity is controlled to 30 ~ 70 DEG C/s, and strength purging surface of steel plate is water stain and is cooled to 680 ~ 720 DEG C, back segment cooling velocity control
5 ~ 20 DEG C/s is made as, 400 ~ 550 DEG C of coiling temperature is cooled to；And purge to steel plate face water stain-free；
6）Batched.
Each element of the present invention and the effect of main technique control：
C：Carbon can improve the intensity of steel, hardness, be main gap solution strengthening element.Using Ultra-low carbon composition design
The Dynamic Precipitation and dynamic recrystallization of strain induced ferrite, fining austenite grains is conducive to obtain ultrafine-grained (UFG) microstructure, so that
Improve the intensity and toughness of steel.And reduction and the reduction of carbon equivalent with carbon content, micro alloyed steel can be enable to keep
Good welding performance and low ductile-brittle transition temperature, therefore C content is not higher than 0.02%.
N:Nitrogen can separate out TiN in high temperature with the titanium in steel, and effectively pin austenite crystal prevents it from growing up, and refinement is difficult to understand
Family name's body crystal grain, below 720 DEG C, the Precipitation nanoscale Ti from steel（C, N) etc. second phase particles, can effectively pin dislocation,
Significantly improve the intensity of steel, but the too high plasticity and toughness for severe exacerbation material of nitrogen content.Therefore the present invention limits nitrogen content as 0.002
~0.005%。
Mn：Manganese can reduce phase transition temperature of the austenite to ferritic transformation, and austenite is to the phase transformation of ferritic transformation
The reduction of temperature has refining effect to the ferrite grain size of rolled, therefore, manganese is already as in high strength microalloy steel
Main alloy element and be widely used.The too high crack sensitivity that will dramatically increase steel of manganese, too low then solution strengthening effect
Not substantially, so as to influence the strength character of steel.Therefore the content of manganese of the present invention is 1.7 ~ 2.0%.
Si:Silicon can be solid-solution in ferrite and austenite, improve intensity, hardness, the elasticity of steel, but add too high silicon
The plasticity and surface quality of material can be had a negative impact.Therefore the content of silicon of the present invention is
0.03~0.15%。
S、P:Sulphur and P elements are too high can produce very detrimental effect to material plasticity and toughness.Therefore phosphorus content of the present invention should be controlled
Within 0.018%, sulfur content should be controlled within 0.006% system.
Ti:Titanium is most important micro alloying element in the present invention, and TiN, effectively pin austenite crystal are separated out during high temperature
It is prevented to grow up, fining austenite grains.Below 720 DEG C, the Precipitation nanoscale Ti from steel（C, N) etc. the second phase grain
Son, can effectively pin dislocation, significantly improve the intensity of steel.When experiment shows that it is less than 0.05%, precipitating reinforcing effect is not obvious,
The high temperature thermoplasticity of steel is poor during higher than 0.35%, and surface is also easy to produce crackle during slab cooling.Therefore Ti content of the present invention be 0.05 ~
0.38%。
N:Nitrogen can separate out TiN in high temperature with the titanium in steel, and effectively pin austenite crystal prevents it from growing up, and refinement is difficult to understand
Family name's body crystal grain, below 720 DEG C, the Precipitation nanoscale Ti from steel（C, N) etc. second phase particles, can effectively pin dislocation,
Significantly improve the intensity of steel.
Al:Aluminium is deoxidant element, while having certain Grain Refinement Effect.Therefore be present invention defines aluminium content
0.025~0.05%。
Why 20≤Ti/C≤50 and 40≤Ti/N≤70 are strictly controlled, be in order to ensure steel separates out TiN in high temperature
Deng second phase particles, pinning austenite crystal prevents it from growing up, fining austenite grains, and below 720 DEG C, from steel
Precipitation nanoscale Ti（C, N) etc. second phase particles, can effectively pin dislocation, significantly improve the intensity of steel.
Why the present invention proposes that after hot rolling section cooling two-stage cooling before and after, leading portion cooling velocity is controlled
It is 30 ~ 70 DEG C/s, and is cooled to 680 ~ 720 DEG C of transformation finish temperature, is in order to avoid thick Ti（C、N）Particle is in austenite
Being separated out between ferritic phase reduces armor plate strength and toughness, when cooldown rate is higher than 70 DEG C/s, easily causes steel plate along thickness side
To inhomogeneous cooling, cause steel plate stretching to be layered, reduce the integrated performance index of steel；20 ~ 50s is spaced between two sections of coolings, is had
Beneficial to the Ti of small and dispersed in steel（C、N）Particle is separated out in the ferrite that phase transformation terminates, and improves steel strength；Back segment cooling speed
Degree is controlled to 5 ~ 20 DEG C/s, is cooled to the type of cooling of 400 ~ 550 DEG C of coiling temperature, it is therefore an objective to adjust the carbonitride of titanium
Amount of precipitation and separate out granular size, and obtain no less than 70% ultra-fine black needle-like lower bainite+no more than 30% a small amount of iron
Ferritic tissue, improves the toughness of steel, and coiling temperature ferrite content too high and black needle-like lower bainite amount can be reduced, and cause tissue
Reinforcing is insufficient.
The present invention compared with prior art, with following significant advantage and effect：
1）C content be 0.002 ~ 0.010%, using Ultra-low carbon design, be conducive to strain induced ferrite Dynamic Precipitation and
Dynamic recrystallization, fining austenite grains significantly improve the intensity of steel.
2）Present invention employs inexpensive composition design, the alloying element of Ti contents higher instead of high cost is only added
Cr, Ni, Mo etc., are acted on by the precipitation strengths such as Ti (C, N) second phase particles and build up, reach the tensile strength of steel
More than 800MPa.Therefore, the comparing of the alloys such as Cr, Ni, Mo is with the addition of with other, only by Ti composition designs, cost reduction is obvious,
Ton steel cost can reduce by 150 ~ 200 yuan through preresearch estimates（According to the cubage of comparative example Nb and Cr）.
3）Steel plate of the present invention has a small amount of ferrite of ultra-fine black needle-like lower bainite+no more than 20% no less than 70%
Tissue, makes material while ensureing to have higher-strength, and compared with similar Ti-containing steel, its elongation percentage A% improves 3 percentage points
More than.
4）Preferably, ductile-brittle transition temperature is less than -80 DEG C to the low-temperature flexibility of material；- 40 DEG C of Charpy-V impact powers are not less than 70J,
Impact flexibility than similar Ti-containing steel improves more than 80%.
5）The high strength steel plate type of cooling of the present invention is front and rear two-stage cooling, and 20 ~ 50s is spaced between two sections of coolings；
Leading portion cooling velocity is controlled to 30 ~ 70 DEG C/s, and is cooled to 680 ~ 720 DEG C, and back segment cooling velocity is controlled to 5 ~ 20 DEG C/s, cooling
To 400 ~ 550 DEG C of coiling temperature；So that the dispersion-strengtherning of the Ti-containing steel performed to build up effect it is ultimate attainment.
6）High strength steel plate of the present invention can reach following combination property：More than tensile strength 800MPa, yield strength 700MPa
More than, elongation percentage >=20%, -40 DEG C of Charpy-V impact power >=70J, while having good welds performance and cold forming capability.
Specific embodiment
The present invention is described in detail below：
Table 1 is the component comparative example of various embodiments of the present invention and comparative example；
Table 2 is the main technologic parameters list of various embodiments of the present invention and comparative example；
Table 3 is various embodiments of the present invention and comparative example performance text list.
Various embodiments of the present invention are produced according to following steps：
1）Base is cast into after being smelted through converter and vacuum drying oven；
2）To heating strand, heating-up temperature is incubated 1.5 ~ 2.0h at this temperature at 1320 ~ 1380 DEG C；
3）Roughing is carried out, controls its start rolling temperature at 1080 ~ 1120 DEG C, finishing temperature is 960 ~ 980 DEG C, and rolling pass is
5 ~ 7 passages, make overall compression ratio be not less than 80% after roughing；
4）Finish rolling is carried out, it is 930 ~ 950 DEG C to control its start rolling temperature, and end temp is 850 ~ 890 DEG C, and rolling pass is 7
Passage, the average draught per pass of last 4 passage is controlled 30 ~ 50%；
5）Section cooling, cooling two-stage cooling before and after are carried out, and 20 ~ 50s is spaced between two sections of coolings；Leading portion
Cooling velocity is controlled to 30 ~ 70 DEG C/s, and strength purging surface of steel plate is water stain and is cooled to 680 ~ 720 DEG C, back segment cooling velocity control
5 ~ 20 DEG C/s is made as, 400 ~ 550 DEG C of coiling temperature is cooled to；And purge to steel plate face water stain-free；
6）Batched.
The chemical composition list of the embodiment of the present invention of table 1 and comparative example（wt%）
The various embodiments of the present invention of table 2 and the control list of comparative example technique major parameter（One）
The various embodiments of the present invention of table 2 and the control list of comparative example technique major parameter（Two）
The various embodiments of the present invention of table 3 and comparative example performance text list
From table 3 it can be seen that tensile strength is in more than 800MPa, yield strength in more than 700MPa, elongation percentage 20% with
On, -40 DEG C of Charpy-V impact power >=70J.Through budget, the cost of steel per ton is than 150 ~ 200 yuan of existing steel grade reduction.
This specific embodiment is only most preferably to enumerate, not to the restricted implementation of technical solution of the present invention.
Claims (2)
1. a kind of tensile strength >=800MPa grades of welded structural steel, its component and weight percent content are：C：0.002~
0.018%、Si：0.03~0.09%、Mn：1.70~2.00%、P：≤0.018%、S：≤0.006%、Ti：0.22~0.35%、N：
0.002~0.005%、B：≤0.0005%、Als：0.025 ~ 0.05%, remaining is Fe and inevitable impurity；And meet：20≤
Ti/C≤50,40≤Ti/N≤70；Metallographic structure is the ferrite of the ultra-fine black needle-like lower bainite and surplus for being not less than 70%
Tissue.
2. a kind of method of tensile strength >=800MPa grades of welded structural steel, its step are produced：
The component and weight percent content of tensile strength >=800MPa grades of welded structural steel be：C：0.002~0.018%、Si：
0.03~0.09%、Mn：1.70~2.00%、P：≤0.018%、S：≤0.006%、Ti：0.22~0.35%、N：0.002~0.005%、
B：≤0.0005%、Als：0.025 ~ 0.05%, remaining is Fe and inevitable impurity；And meet：20≤Ti/C≤50,40≤
Ti/N≤70；
1）Base is cast into after being smelted through converter and vacuum drying oven；
2）To heating strand, heating-up temperature is incubated 1.5 ~ 2.0h at this temperature at 1320 ~ 1380 DEG C；
3）Roughing is carried out, controls its start rolling temperature at 1080 ~ 1120 DEG C, finishing temperature is 960 ~ 980 DEG C, and rolling pass is 5 ~ 7
Passage, makes overall compression ratio be not less than 80% after roughing；
4）Finish rolling is carried out, it is 930 ~ 950 DEG C to control its start rolling temperature, and its end temp is 850 ~ 890 DEG C, and rolling pass is 7 roads
Secondary, the average draught per pass of last 4 passage is controlled 30 ~ 50%；
5）Section cooling, cooling two-stage cooling before and after are carried out, and 20 ~ 50s is spaced between two sections of coolings；Leading portion is cooled down
Speed control is 30 ~ 70 DEG C/s, and strength purging surface of steel plate is water stain and is cooled to 680 ~ 720 DEG C, and back segment cooling velocity is controlled to 5
~ 20 DEG C/s, it is cooled to 400 ~ 550 DEG C of coiling temperature；And purge to steel plate face water stain-free；
6）Batched.
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| CN1928130A (en) * | 2006-09-25 | 2007-03-14 | 攀枝花新钢钒股份有限公司 | Process for manufacturing low yield strength ultrafine grain belt steel |
| CN101191174B (en) * | 2006-11-20 | 2010-05-12 | 宝山钢铁股份有限公司 | Hot-rolling phase change induction plasticity steel with 750MPa-level extension strength and preparation method thereof |
| CN101279330A (en) * | 2008-01-25 | 2008-10-08 | 北京科技大学 | Method for producing hot rolling two-phase steel plate at 700MPa level of tensile strength |
| CN101864542B (en) * | 2009-04-16 | 2011-09-28 | 上海梅山钢铁股份有限公司 | Steel for high-frequency resistance straight weld oil well pipe and production method thereof |
| CN103122435A (en) * | 2011-11-18 | 2013-05-29 | 江苏省沙钢钢铁研究院有限公司 | Hot-rolled titaniferous high-strength steel plate with yield strength higher than 700MPa and production method thereof |
| JP5825189B2 (en) * | 2012-04-24 | 2015-12-02 | 新日鐵住金株式会社 | High-strength hot-rolled steel sheet excellent in elongation, hole expansibility and low-temperature toughness, and method for producing the same |
| CN102703807B (en) * | 2012-06-25 | 2013-07-31 | 武汉钢铁(集团)公司 | Steel with minus 80-degree C impact absorbing energy no less than 100J for ocean engineering and production method thereof |
| JP5867444B2 (en) * | 2013-04-15 | 2016-02-24 | Ｊｆｅスチール株式会社 | High strength hot rolled steel sheet with excellent toughness and method for producing the same |
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Effective date of registration: 20170712 Address after: 430083 Qingshan District, Hubei, Wuhan factory before the door No. 2 Patentee after: Wuhan iron and Steel Company Limited Address before: 430080 Wuhan, Hubei Friendship Road, No. 999, Wuchang Patentee before: Wuhan Iron & Steel (Group) Corp. |