CN103757538A - Wide-thick steel plate for high-Ti 700MPa-level engineering machine and production method - Google Patents
Wide-thick steel plate for high-Ti 700MPa-level engineering machine and production method Download PDFInfo
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Abstract
The invention discloses a wide-thick steel plate for a high-Ti 700MPa-level engineering machine and a production method and belongs to the technical field of high-strength welding structure steel. The wide-thick steel plate comprises the following chemical components in percentage by weight: 0.04-009% of C, 0.05-0.40% of Si, 1.80-2.30% of Mn, less than or equal to 0.013% of P, less than or equal to 0.003% of S, 0.06-0.13% of Ti, less than or equal to 0.0050% of N and the balance of Fe and inevitable impurities. The wide-thick steel plate disclosed by the invention has the advantages that the 700MPa-level 10-40mm wide-thick steel plate with excellent mechanical property is obtained by accurately controlling the content of Ti and combining a thermal-mechanical rolling technology and an online ultrafast cooling technology without need of subsequent thermal treatment, the yield strength is 586MPa-610MPa, the tensile strength is 707MPa-735MPa, the elongation is more than 18%, the impact energy at the temperature of minus 20 DEG C is more than or equal to 220J, and the impact energy at the temperature of minus 60 DEG C is more than or equal to 170J. Simultaneously, the steel plate has good welding performance, is short in production process and low in production cost and is green and environmentally friendly.
Description
Technical field
This patent belongs to high-strength welding structure steel technical field, particularly relates to a kind of high Ti700MPa level engineering machinery Wide and Heavy Plates and production method.
Background technology
At engineering machinery and field of steel structure, in recent years the high tensile steel plate demand of low yield strength ratio is increased gradually, the welding property to steel plate, cold-forming property etc. are had higher requirement simultaneously.
Ti is one of important microalloy element in Hi-Stren steel.According to the Ti content adding, be generally divided three classes: micro-Ti content (0.010%-0.020%), medium Ti content (0.020%-0.040%), high Ti content (0.040%-0.15%).
The important micro-Ti treatment process for steel of micro-Ti content, for improving billet quality, restriction heat-processed Austenite Grain Growth, improves the aspects such as low-temperature flexibility and has good effect.
Medium Ti content is mainly used in optimizing size and the distribution of the precipitate of TiN in welding process, improves Low Temperature Impact Toughness of Heat-affected Zone.
High Ti content mainly improves tissue and the performance of steel plate at the Precipitation of different steps by TiC particle and Ti (C, N) particle.Specifically can show as: stable TiN and Ti (C, N) particle during (1) heat-processed influence of high austenizing temp, suppresses austenitic and too grows up; (2) deformation induced the separating out of TiC and Ti (C, N) particle in high temperature rolling process, refine austenite recrystal grain obtains more tiny recrystal grain under the condition of identical deflection and texturing temperature; (3) roll the INTERPHASE CARBIDE PRECIPITATION of rear austenite/ferrite transformation process TiC particle and the precipitation strength effect that the supersaturation of follow-up TiC in ferritic phase separated out.
Titanium compound stability is successively decreased order for TiN → Ti
4c
2s
2→ Ti (CN) → TiC,, when titanium amount is lower, is almost all used to form TiN (ω (Ti) ≈ 3.4 × ω (N)), can not form Ti
4c
2s
2, the sulphur in steel exists with MnS form.And work as the increase of titanium amount, exceed 3.4 × ω (N), start to form Ti
4c
2s
2.Now MnS and Ti
4c
2s
2and deposit. when titanium content is increased to when the nitrogen in steel and element sulphur all can be fixed, during ω (Ti)=3.4 ω × (N)+3 × ω (s), MnS will be all by Ti
4c
2s
2institute replaces, and now the precipitation strength effect of titanium is very little.When titanium content continues to increase, unnecessary titanium will form TiC, and TiC particle is separated out after alternate or phase transformation in ferrite. and its size very tiny (below 10nm), can produce strong precipitation strength effect.The content of solid solution Ti when therefore its strengthening effect of steel plate of high Ti strengthening is decided by high temperature in steel, (effectively Ti content can be used following formula to estimate, Ti to be referred to as effective Ti content
eff=Ti
t-3.42 × N-3 × S, in formula, each element adopts weight percent to bring into).
The technique great majority that at present Ti adds as main reinforced alloys element are to use in during Hot Strip Rolling, and that in the Composition Design of plate of moderate thickness, as main alloying element, uses rarely has report.
If application number is all to have reported that a kind of use Ti is as main alloy element in the patent of CN200610123458.1, CN200910038833.6, CN201010034472.0, CN201210567654.3, the technology that adopts the curling technology of hot continuous rolling+high temperature to produce high-strength hot-rolled roll bending.Relate to the fields such as high-strength weather-proof steel plate, high strength dual phase steel, high-strength vehicle plate and steel for engineering machinery plate.
Application number is that the patent of CN200710031549.7 and CN200710032112.5 has provided respectively 700MPa and 550MPa level steel plate Ti adds method for determination of amount.To set up the experimental formula between Ti add-on, impurity content and armor plate strength based on hot-rolled coil production technique.
Publication number is to have provided a kind of high Ti microalloying plate of moderate thickness and preparation method thereof in the patent of CN102676927A.Wherein its Mn content is 0.30-1.80wt%, has detailed difference with the Mn constituent content in this patent.
Summary of the invention
The object of the present invention is to provide a kind of high Ti700MPa level engineering machinery Wide and Heavy Plates and production method, adopt Ti to substitute conventional Nb element in current steel, utilize similarly deformation induced original austenite grain refinement of separating out steel in effect promotion recrystallization process of itself and Nb; Adopt the precipitate of Ti to utilize precipitation strength to improve the intensity of steel as main strengthening element simultaneously.
High Ti content 700MPa level engineering machinery involved in the present invention by the chemical composition of Wide and Heavy Plates is: C:0.04～0.09%, Si:0.05～0.40%, Mn:1.80～2.30%, P :≤0.013%, S :≤0.003%, Ti:0.06～0.13%, N :≤0.0050%; Surplus is Fe and inevitable impurity.
Each element interaction in the present invention
Carbon (C): C, as interstitial atom, strengthens obvious solution strengthening effect in steel, can significantly improve the intensity of steel, but low-temperature impact toughness and the welding property of higher C content infringement steel.C can with steel in the element such as Mo, V, Nb, Ti form precipitate, by precipitation strength, improves steel ability intensity.Under strong water-cooled condition, C can improve the hardening capacity of steel, obtains high-intensity martensitic stucture.In the present invention, the Main Function of C element is to be combined with the Ti of solid solution element, in austenite/ferrite transformation process, generates TiC particle, considers low-temperature flexibility and the welding property of steel, and carbon content scope is set as 0.04～0.09%.
Silicon (Si): Si adds in steel as reductor, the Si atom of solid solution can obviously improve ferritic intensity, but Si content improves obviously reduction HAZ district toughness.Therefore this steel grade Si content is set as 0.05～0.40%.
Manganese (Mn): Mn element has certain solution strengthening effect in steel when Mn content reaches 1.8% when above, can obviously promote the generation of acicular ferrite, accurate Polygons iron element in soft steel.In the present invention, Mn content is set as 1.80～2.30%.
Titanium (Ti): Ti is the of paramount importance alloying element in the present invention, in the design deformation induced separate out and austenite/ferritic transformation process in the TiC particle of INTERPHASE CARBIDE PRECIPITATION as main precipitation strength factor.When Ti content is higher, remove TiN, the Ti of high-temperature zone and generation
4c
2s
2, Ti (C, N) outside particle, Ti form with TiC in lesser temps deformation process of residue solid solution is separated out (30-50nm) in deformed belt inside, thus the recrystal grain that can suppress steel grow up and improve steel plate non-recrystallization temperature, promote austenite flattening.At austenite, to TiC in ferrite transformation process, the solid solubility in ferrite reduces, and in phase transition process, forward position, austenite/ferritic phase interface TiC particle is point-like and separates out (< 10nm), and TiC precipitate is shown in Fig. 1.
Because the element bonding forces such as the Ti in steel and N, S are strong, the Ti element that has formed nitride and sulfide under high temperature cannot change useful TiC particle in subsequent process, therefore the actual Ti content in steel and play between effective Ti content of strengthening effect and have following relation, (Ti
eff=Ti
t-3.42 × N-3 × S, in formula, each element adopts weight percent to bring into).In steel, S element typical content is about 0.0020%, N element typical content and is about 0.0040%, by the known Ti of formula
eff=Ti
t-0.02(%), consider that in ferrite, approximately having 0.02% Ti cannot form TiC separates out, and the Ti that separates out of TiC form need to reach 0.02% and just can have good precipitation strength effect when above simultaneously, therefore the Ti content in steel adds and must be greater than 0.06%.When Ti content reaches 0.13% simultaneously, the TiC amount of separating out too much causes the precipitation strength in steel strong, significantly reduces the toughness of steel plate.Therefore in this design, the content of Ti is 0.06-0.13%.
Phosphorus (P): P is one of major impurity element in steel, and the increase meeting of P content significantly reduces plasticity and the welding property of steel, therefore for its P content of high strength grade steel plate, is mostly controlled at below 0.013%.
Sulphur (S): S can be combined with Mn and form MnS inclusion in common steel, is combined forms Ti in the steel of high Ti content when high temperature prior to Mn with Ti
4c
2s
2particle, thereby the content of effective Ti in reduction steel.Therefore S content≤0.003% in the design
Aluminium (Al): Al is the main deoxidant element in steel, and being combined obtained AlN particle with N element can refine austenite grain-size.But the AlN in steel is also one of main inclusion source, and therefore Al content general control is below 0.04%.
Nitrogen (N): N is combined and is formed nitride with the element such as Ti, Al in steel, becomes one of source of inclusion, reduces the toughness of steel.In the design, because the Ti content adding is apparently higher than common steel grade, the probability that forms macrobead TiN particle obviously improves, and therefore in the design, N content need to be controlled at below 0.005.
The technical parameter of production technique of the present invention and control thereof is as follows:
(1) smelting technology
Adopt desulfurizing iron → converter smelting → LF refining → RH refinery practice route.Strict slab composition C:0.04～0.09%, Si:0.05～0.40%, Mn:1.80～2.30%, the P :≤0.013%, S :≤0.003%, Ti:0.06～0.13%, N :≤0.0050% of controlling.
The present invention, by the strict interpolation opportunity of controlling Ti alloy, controls molten steel N content, is suppressed at the macrobead TiN particle generating in solidification of molten steel process.
The present invention, by the strict S content of controlling, makes sulfide inclusion be reduced to lower level, then by rational Ca/S ratio, makes remaining a small amount of sulfide inclusion nodularization.In the present invention, Ca/S is between 1.5-2.
Carry out LF refining and RH refining, RH treatment time 21min-23min, dark vacuum time >=18min, strictly controls [H] and [N] content in steel, guarantees molten steel cleanness.
(2) heating of plate blank technique
Employing continuously cast bloom is produced, 1150～1220 ℃ of heating of plate blanks, and soaking time 3～6 hours, had both guaranteed the fully solid solution of Ti alloy.
(3) rolling technology
Adopt recrystallization zone and non-recrystallization district two stage rolling.
First stage is recrystallization zone rolling, 1050 ℃～1150 ℃ of start rolling temperatures, guarantee that first stage rolling single pass draft increases gradually, and last three percentage pass reductions are that 25%-35% total reduction is greater than 60%, finishing temperature guarantees more than perfect recrystallization temperature.One-phase rolling is by the distortion of heavy reduction repeatedly, makes full use of deformation induced separating out and the interaction refinement high temperature austenite crystal grain of aximal deformation value.
Subordinate phase is the rolling of non-recrystallization district, and start rolling temperature is lower than austenite non-recrystallization temperature, and finishing temperature is higher than ferrite Precipitation Temperature.For 840 ℃～870 ℃ of this patent start rolling temperatures, 770～800 ℃ of finishing temperatures, treat that temperature thickness is 3～4.5 times of thickness of slab, two-stage rolling draft >=65%.
The large compression ratio distortion in finish rolling stage, promotes TiC to separate out in deformed belt and suppresses softening and subgrain grain growth of deformed belt; Multi-pass deformation forms a large amount of deformed belts in the original austenite of original promotion simultaneously, improves austenite subsurface defect density, improves ferrite transformation nucleation rate, as Fig. 2 thereby obtain the austenite crystal flattening.
(4) process for cooling
Rolling rear steel plate, to adopt online ultrafast cool equipment to carry out cooling, within the scope of rate of cooling 20-25 ℃/s, by quick process for cooling, steel plate is cooled in the scope of 500-600 ℃, obtains the mixed structure of quasi-polygonal ferrite+acicular ferrite, as Fig. 3.
LF refining time, guarantees that in steel, S content is controlled at below 20ppm, and the dark vacuum time >=18min of RH guarantees that in steel, N content is controlled at below 30ppm, and in control steel, remaining O content is below 15ppm.Guarantee effective Ti content (Ti in steel
eff) be not less than 0.06%(Ti
eff=Ti
t-3.42 × N-3 × S, in formula, each element adopts weight percent to bring into).
The present invention is by accurately controlling Ti content, in conjunction with thermo-mechanical rolling and online Ultra Fast Cooling, without by subsequent heat treatment, obtain the 700MPa rank 10-40mm specification Wide and Heavy Plates of excellent mechanical property, its tensile strength (Rm) 700-750MPa, yield strength (Rp0.2) 580-630MPa,-20 ℃ of ballistic work >=220J ,-60 ℃ of ballistic work >=170J, ductile-brittle transition temperature≤-75 ℃, ferrite grain size rating result >=13 grade, yield tensile ratio≤0.86.
The steel plate of production of the present invention has good low-temperature impact toughness and good welding property; Steel plate carries out oblique Y cold crack susceptibility and HAZ maximum hardness test, shows that steel plate still has good welding technological properties in the time of 0 ℃.
Beneficial effect of the present invention:
Only adopting economic Ti is main alloying element, by rational rolling and quick process for cooling, obtains mating of good tissue and precipitate, thereby the carbon equivalent of reduction steel, good welding property has reduced the production cost of steel plate simultaneously.
Accompanying drawing explanation
Fig. 1 is the TiC particle that in 1# steel, different steps obtains.
The original austenite tissue that Fig. 2 obtains for 2# steel.
The mixed structure of quasi-polygonal ferrite+acicular ferrite that Fig. 3 obtains for 2# steel.
Embodiment
The embodiment of the steel plate of producing according to production method of the present invention is as following table.Table 1 is the chemical composition of embodiment of the present invention steel, the processing condition that table 2 is the embodiment of the present invention, the mechanical property that table 3 is the embodiment of the present invention, the anti-hydrogen cracking performance processed that table 4 is the embodiment of the present invention.
Table 1 embodiment chemical composition, wt%
| Embodiment | Specification/mm | C | Si | Mn | P | S | Alsol | Ti | CEQ | N/ppm |
| 1 | 16 | 0.075 | 0.21 | 1.95 | 0.010 | 0.003 | 0.023 | 0.059 | 0.40 | 26 |
| 2 | 25 | 0.077 | 0.28 | 1.89 | 0.013 | 0.003 | 0.029 | 0.079 | 0.39 | 28 |
| 3 | 30 | 0.081 | 0.23 | 1.97 | 0.009 | 0.002 | 0.02 | 0.101 | 0.41 | 33 |
The processing condition of table 2 embodiment
The yield strength of measuring the embodiment of the present invention according to GB/T228 and GB/T229 is 586MPa～610MPa, tensile strength is 707MPa～735MPa, 18% ,-20 ℃ of ballistic work >=220J of unit elongation >,-60 ℃ of ballistic work >=170J, have good intensity and toughness coupling.
According to the oblique Y groove welding crack test of GB4675.1-84 < < method > > and GB4675.5-2008 < < solderability test-welded heat affecting zone maximum hardness test method > >, steel plate is carried out to welding cold crack sensitivity and maximum hardness test respectively.According to welding evaluation result, actual steel plate is implemented to butt welding test simultaneously, and measure the mechanical property of welding joint.Table 4 is that the welding qualification test processing parameter of 1# steel plate arranges; Table 5 is welding qualification test result;
Table 6 is the processing parameter of butt welding test; Table 7 is the mechanical property detection architecture of welding joint.
By test, show that steel plate has good welding property.
The mechanical property of table 3 embodiment of the present invention
The welding evaluation processing parameter of table 4 1# embodiment of the present invention
The welding qualification test result of table 5 1# embodiment of the present invention
The actual Plate Welding processing parameter of table 6 1# embodiment of the present invention
The actual Plate Welding joint mechanical property of table 7 1# embodiment of the present invention
Claims (2)
1. a high Ti700MPa level engineering machinery Wide and Heavy Plates, is characterized in that: steel plate chemical component weight percentage ratio is: C:0.04～0.09%, Si:0.05～0.40%, Mn:1.80～2.30%, P :≤0.013%, S :≤0.003%, Ti:0.06～0.13%, N :≤0.0050%; All the other are Fe and inevitable impurity.
2. a production method for steel plate described in claim 1, is characterized in that,
(1) smelting technology
Adopt desulfurizing iron → converter smelting → LF refining → RH refinery practice route.Strict slab composition C:0.04～0.09%, Si:0.05～0.40%, Mn:1.80～2.30%, the P :≤0.013%, S :≤0.003%, Ti:0.06～0.13%, N :≤0.0050% of controlling; Ca/S is between 1.5-2;
Carry out LF refining and RH refining, RH treatment time 21min-23min, dark vacuum time >=18min;
(2) heating of plate blank technique
Employing continuously cast bloom is produced, 1150～1220 ℃ of heating of plate blanks, and soaking time 3～6 hours, had both guaranteed Ti alloy solid solution;
(3) rolling technology
First stage is recrystallization zone rolling, and 1050 ℃～1150 ℃ of start rolling temperatures guarantee that first stage rolling single pass draft increases gradually, and last three percentage pass reductions are 25%-35%, and total reduction is greater than 60%;
Subordinate phase is the rolling of non-recrystallization district, 840 ℃～870 ℃ of start rolling temperatures, and 770～800 ℃ of finishing temperatures, treat that temperature thickness is 3～4.5 times of thickness of slab, two-stage rolling draft >=65%;
(4) process for cooling
Rolling rear steel plate, to adopt online ultrafast cool equipment to carry out cooling, and rate of cooling 20-25 ℃/s, steel plate is cooled in the scope of 500-600 ℃, obtain the mixed structure of quasi-polygonal ferrite+acicular ferrite.
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Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN109082493A (en) * | 2018-07-20 | 2018-12-25 | 邯郸钢铁集团有限责任公司 | Reduce the smelting process that TiN in high titanium microalloying high-strength steel is mingled with content |
| CN109161796A (en) * | 2018-08-31 | 2019-01-08 | 邯郸钢铁集团有限责任公司 | With favorable low-temperature impact toughness high-strength crossbeam steel 800L and its production method |
| CN113699457A (en) * | 2021-08-31 | 2021-11-26 | 重庆钢铁股份有限公司 | High-titanium-content high-strength low-alloy automobile structural steel and smelting process thereof |
| CN115161548A (en) * | 2022-05-25 | 2022-10-11 | 昆明理工大学 | Ti-Zr composite microalloyed 700 MPa-grade high-strength and high-toughness steel plate and preparation method thereof |
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| JPH02156021A (en) * | 1988-12-09 | 1990-06-15 | Nippon Steel Corp | Manufacture of high tensile steel sheet |
| CN101525717A (en) * | 2009-04-21 | 2009-09-09 | 广州珠江钢铁有限责任公司 | Ti microalloyed ultra-fine grain hot rolled steel at 700MPa class and production method thereof |
| CN102363858A (en) * | 2011-11-03 | 2012-02-29 | 首钢总公司 | High-strength steel for 750 to 880 MPa-level vehicles and production method thereof |
| CN102676927A (en) * | 2012-06-12 | 2012-09-19 | 钢铁研究总院 | High-Ti micro-alloyed medium thickness steel plate and preparation method thereof |
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| JPH02156021A (en) * | 1988-12-09 | 1990-06-15 | Nippon Steel Corp | Manufacture of high tensile steel sheet |
| CN101525717A (en) * | 2009-04-21 | 2009-09-09 | 广州珠江钢铁有限责任公司 | Ti microalloyed ultra-fine grain hot rolled steel at 700MPa class and production method thereof |
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Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN109082493A (en) * | 2018-07-20 | 2018-12-25 | 邯郸钢铁集团有限责任公司 | Reduce the smelting process that TiN in high titanium microalloying high-strength steel is mingled with content |
| CN109161796A (en) * | 2018-08-31 | 2019-01-08 | 邯郸钢铁集团有限责任公司 | With favorable low-temperature impact toughness high-strength crossbeam steel 800L and its production method |
| CN109161796B (en) * | 2018-08-31 | 2020-11-03 | 邯郸钢铁集团有限责任公司 | High-strength beam steel 800L with good low-temperature impact toughness and production method thereof |
| CN113699457A (en) * | 2021-08-31 | 2021-11-26 | 重庆钢铁股份有限公司 | High-titanium-content high-strength low-alloy automobile structural steel and smelting process thereof |
| CN115161548A (en) * | 2022-05-25 | 2022-10-11 | 昆明理工大学 | Ti-Zr composite microalloyed 700 MPa-grade high-strength and high-toughness steel plate and preparation method thereof |
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Address after: 100041 Shijingshan Road, Shijingshan District, Shijingshan District, Beijing Patentee after: Shougang Group Co. Ltd. Address before: 100041 Shijingshan Road, Shijingshan District, Shijingshan District, Beijing Patentee before: Capital Iron & Steel General Company |