CN104789898A - Production method of ultrahigh-strength anti-cracking thick steel plate - Google Patents
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Abstract
The invention relates to a production method of an ultrahigh-strength anti-cracking thick steel plate. The steel comprises the following chemical components in percentage by weight: at most 0.10% of C,0.10%-0.50% of Si, 1.40%-1.80% of Mn, at most 0.015% of P, at most 0.005% of S, 0.02%-0.05% of Nb, 0.008%-0.02% of Ti, 0.015%-0.05% of Al, 0.2%0-0.50% of Ni, at most 0.35% of Cu, at most 0.25% of Gr, at most 0.25% of Mo, and the balance of Fe and inevitable impurities. The production method comprises the following key steps: smelting, continuous casting, heating, rolling and cooling. By adopting the low-carbon high-manganese Nb-Ti-Ni multielement microalloying component design system in combination with LF+VD (ladle furnace+vacuum degasser) compound refining and ultra-fast cooling techniques, the ultra-thick steel plate with the yield strength of 400 MPa above and the maximum thickness of 80mm can be produced. The -40-DEG C impact toughness of the steel plate core can reach 250J above, the nil ductility transition temperature is -80 DEG C below, and the high-strength steel plate has higher toughness, weldability and cracking resistance.
Description
Technical field
The invention belongs to metallurgical technology field, relate to a kind of production method of superstrength crack arrest Plate Steel.
Technical background
Along with expanding economy, the increasing of volume of trade, container-ship is gradually towards the future development maximized, container-ship deck superstructure bearing load is also increasing, its some key positions, as positions such as main deck, sheer-strake, hatchway coamings, owing to requiring high strength, high tenacity and high crack arrest characteristic, general high strength steel plate for ship building can not meet service requirements.For 16000TEU super-container vessel the biggest in the world at present, hatchway coaming thickness reaches 80mm, and only crack arrest steel EH47 steel using amount is about more than 2000 tons/ship.Japan started to research and develop crack arrest steel plate as far back as the nineties in 20th century, and 2008, Nippon Steel and Mitsubishi Heavy Industries Ltd cooperated, and successfully developed a kind of novel high-tensile strength strengthening steel---" HTS47 ", and used this steel plate in Japan shipbuilding factory first.2013, the development Experience of international shipping federation (IACS) and some surveying society's Japaneses, the special container-ship plate specification having formulated 47 feather weight for van container deck of boat key position, and the method brittle fracture tests such as ESSO test and double tension being classified as inspection steel plate crack arrest characteristic.
" the excellent high-strength steel plate of crack arrest is " mainly through controlling the difference of steel plate in the tissue of thickness direction, grain boundary density and texture for Chinese patent CN 101341269 A, make steel plate different thickness position direction of crack propagation when ftractureing produce difference, thus make the expansion resistance increase of crackle to improve the crack arrest characteristic of steel plate.But essence is that its slab cooling power of producing is inadequate, and thickness of slab 1/2 position is friable tissues, has an impact to the crack arrest of steel plate.This method is little to the raising of crack arrest, does not fundamentally improve the toughness tissue of 1/2 position.Chinese patent CN 102994874 A " yield strength 500Mpa level high arrest toughness steel plate and production method thereof " discloses a kind of by being cooled fast to the method for carrying out finish rolling near Ar3 transformation temperature to carry out crystal grain thinning after roughing again, the method for Anticrack.But the method adopts low-temperature impact toughness and NDT ductile-brittle transition temperature to weigh the crack arrest characteristic of steel plate, do not possess science and preciseness, can only illustrate that the toughness of steel plate is better, can not prove that the crack arrest characteristic of steel plate is excellent, and only have ESSO test or double tension test to be only the standard test of the measurement steel plate crack arrest characteristic of international endorsement.
Summary of the invention
The present invention aims to provide a kind of production method of superstrength crack arrest Plate Steel, it represents steel grade EH47 maximum ga(u)ge and reaches 80mm, yield strength is at more than 460MPa, tensile strength is at 570 ~ 720MPa, low temperature-40 DEG C of heart portion impelling strength reach more than 200J, and nil-ductility temperature, below-80 DEG C, is checked through the double tension test of gradient temperature type, its-10 DEG C of crack arrest COEFFICIENT K ca >=6000N/mm3/2, can be good at the user demand meeting super-container vessel key position crack arrest steel plate.
The technical scheme of invention:
A production method for superstrength crack arrest Plate Steel, the chemical constitution weight percent of steel is: C≤0.10%, Si=0.10% ~ 0.50%, Mn=1.40% ~ 1.80%, P≤0.015%, S≤0.005%, Nb=0.02% ~ 0.05%, Ti=0.008% ~ 0.02%, Al=0.015% ~ 0.05%, Ni=0.2%0 ~ 0.50%, Cu≤0.35%, Gr≤0.25%, Mo≤0.25%, all the other are Fe and inevitable impurity; Critical process step comprises:
Smelt: converter tapping P≤0.008%, C≤0.005%, adopt LF+VD refinery practice, the omnidistance Argon of LF stove refining, slag making deoxidation, white slag hold-time >=20min, refining slag basicity CaO/SiO2 >=2.5; VD Fruit storage, at below vacuum tightness 0.5tor, vacuum hold-time 18 ~ 25min, departures molten steel N≤45ppm, H≤2ppm, O≤20ppm;
Continuous casting: adopt whole process protection casting, middle bag superheating temperature target value 15 ~ 25 DEG C, slab thickness >=260mm;
Heating: between slab heating temperature 1180 ~ 1220 DEG C, soaking time >=30min;
Rolling: adopt two-phase control rolling, first stage finishing temperature >=980 DEG C, last three percentage pass reduction >=16%, subordinate phase finishing temperature control is at 780 ~ 840 DEG C;
Cooling: roll rear steel plate and directly enter water cooling, the Plate Steel for thickness >=50mm adopts the DQ high-pressure hydraulic pump of Mulpic to force cooling, and rate of cooling >=6 DEG C/S, until final cooling temperature is at 300 ~ 400 DEG C.
In the chemical constitution of described steel, in order to make the yield strength >=400Mpa of steel plate, and improve Plate Steel hardening capacity, in composition, alternative adds Cu=0.15% ~ 0.35%, Gr=0.15% ~ 0.25%, more than one elements in Mo=0.15% ~ 0.25%.
In described milling step, subordinate phase finishing temperature is optimized for 800 ~ 820 DEG C.
In described cooling step, the Plate Steel for thickness >=50mm adopts the DQ high-pressure hydraulic pump of Mulpic to force cooling, and rate of cooling is optimized for 6 ~ 15 DEG C/S, until final cooling temperature is optimized for 320 ~ 380 DEG C.
Inventive principle:
The present invention on Composition Design to improve the hardening capacity of steel plate, again by forcing cooling or ultrafast refrigeration technique improve the rate of cooling of Plate Steel and reduce final cooling temperature, thus increase thickness direction particularly steel plate center toughness organize the ferritic content of fine acicular, increase the crack arrest characteristic of steel plate.
Chemical composition design of the present invention considers to have low-carbon-equivalent and low Pcm value while requiring high strength and good low-temperature toughness to its crack arrest and weldability emphasis.The toughness tissue that organization design is then is matrix with fine acicular ferrite, with the addition of the element of multiple crystal grain thinning and raising hardening capacity.
Adopt the Composition Design of low-carbon high-manganese.Although the raising of C content can improve intensity and reduce Ar3 temperature, worsen the low-temperature flexibility of steel, crack arrest characteristic and welding property, therefore control final carbon content≤0.10% by means such as converter tapping C≤0.005%; Manganese is weak carbide forming element, and it can reduce austenite transformation temperature, fining ferrite grains, to raising armor plate strength and toughness useful, therefore, when Composition Design, manganese design lower limit 1.40%, but when content is more than 1.80%, center segregation increases the weight of, and causes crack arrest characteristic severe exacerbation.
In order to ensure crack arrest characteristic and welded thin-wall box component toughness, molten steel must have higher purity.P, S are detrimental impurity element, P≤0.008% during by controlling converter tapping, and by LF+VD composite refining technique, white slag hold-time>=20min, refining slag basicity CaO/SiO
2>=2.5, VD stove is protected the means such as vacuum time 18 ~ 25min and is controlled, and makes end phosphorus content P≤0.015%, sulphur content S≤0.005%, and reduces other impurity and obnoxious flavour content in molten steel.
In order to improve crack arrest characteristic and don't affect welding property, on the basis of C-Mn steel solution strengthening, compound adds the alloying elements such as Nb, Ti, Ni, gives full play to crystal grain thinning, precipitation strength and phase transformation strengthening etc. and does in order to reach high-strong toughness, high crack arrest and excellent welding property object.
Nb, as a kind of important microalloy element, adds the Nb of more than 0.02%, can form tiny carbide and nitride, suppress growing up of austenite crystal, and in conjunction with first stage finishing temperature >=980 DEG C, the means such as last three percentage pass reduction >=16%, refinement original austenite grains; By subordinate phase finishing temperature control at 800 ~ 820 DEG C, suppress austenitic recrystallize, keep deformation effect thus crystal grain thinning.But when Nb content is greater than 0.05%, niobium carbonitrides etc. can separate out and grow up in a large number in steel plate, remarkably influenced steel plate crack arrest characteristic and cause the alligatoring etc. of heat affected zone crystal grain in welding process.
Micro-Ti process is carried out in steel, the Ti adding more than 0.008 be conducive to Heating temperature between 1180 DEG C ~ 1220 DEG C time form TiN pinning crystal boundary, suppress austenite crystal too grow up, and in the operation of rolling crystal grain thinning, improve the effect of steel plate crack arrest characteristic and welding property; But when Ti content is greater than 0.02%, meeting forming section Ti complex inclusion, becomes the fracture origin in steel on the contrary, very harmful to the crack arrest characteristic of steel.
Ni is also particularly crucial to the crack arrest characteristic improving steel plate, can effectively improve steel plate hardening capacity and improve low-temperature flexibility.When content is greater than 0.2%, the ultrafast cold technique of the DQ in conjunction with Mulpic, controls roller repairing speed at 6 ~ 15 DEG C/S, final cooling temperature is between 320 ~ 380 DEG C, form the tissue being matrix with fine acicular ferrite, effectively can suppress the expansion of crackle, improve crack arrest characteristic; But Ni is expensive, too much interpolation can increase manufacturing cost, therefore the upper limit is set as 0.5%.
In order to make the yield strength >=400Mpa of steel plate, and improve Plate Steel hardening capacity, in steel plate, alternative adds Cu=0.15% ~ 0.35%, Gr=0.15% ~ 0.25%, more than one elements in Mo=0.15% ~ 0.25%, but the crack arrest characteristic of steel plate and welding property can be reduced when add-on is too much and increase manufacturing cost.
Beneficial effect of the present invention:
A. the present invention is from creating low-carbon high-manganese, Nb-Ti-Ni multicomponent microalloying Composition Design system, LF+VD multiple refining technologies, the purity of strict control P, S content and molten steel, and adopt the series rooling new technologies such as the large pressure of high temperature, TMCP controlled rolling and ultra-rapid cooling, high-strong toughness, high crack arrest super-thick steel plate that successfully to develop with fine acicular ferritic structure be body, for the production domesticization of crack arrest steel plate is laid a good foundation.
B. the present invention breaks through TMCP technological limits, substitute traditional thermal treatment process, give full play to equipment advantage, production yield strength is at the ultra-thick steel plates of more than 400Mpa, maximum ga(u)ge can reach 80mm, while guarantee quality product, reduce alloy content and production cost, advance the research and development process of Economy In China type, low-carbon environment-friendly steel new variety.
C. the present invention utilizes steel mill's existing installation and processing condition, neither increases investment and production cost, turn improves production efficiency, energy-saving consumption-reducing.
D. product of the present invention can be widely used in multiple fields such as shipbuilding, bridge, pressurized vessel, building and engineering machinery, improves the crack arrest ability of steel plate.
Accompanying drawing explanation
Accompanying drawing 1 is the steel plate arrest toughness of the embodiment of the present invention 1 and the graph of a relation of crack arrest temperature.
Embodiment
Below in conjunction with embodiment, the invention will be further described:
Embodiment 1:
The present embodiment is a kind of production method of high strength crack arrest Plate Steel, and the chemical constitution weight percent of steel is: C=0.06%, Si=0.21%, Mn=1.62 %, P=0.009%, S=0.0017%, Nb=0.039%, Ti=0.015%, Al=0.044%, Ni=0.48%, Cu=0.28%, Gr=0.18%, all the other are Fe and inevitable impurity.Critical process step comprises:
Smelt: converter tapping P=0.006%, C=0.0028%, adopt LF+VD refinery practice, the omnidistance Argon of LF stove refining, slag making deoxidation, white slag hold-time 21min, refining slag basicity CaO/SiO
2=3.5; VD Fruit storage, at below vacuum tightness 0.5tor, vacuum hold-time 23min, departures molten steel N=42ppm, H=1.5ppm, O=16ppm.
Continuous casting: adopt whole process protection casting, middle bag superheating temperature 23 DEG C, slab thickness 301mm.
Heating: temperature 1190 ~ 1200 DEG C, soaking time 35min.
Rolling: first stage finishing temperature 1023 DEG C, last three percentage pass reductions 16.1%, 17.5%, 18.2%; Subordinate phase finishing temperature is at 815 ~ 825 DEG C.
Cooling: roll rear steel plate and directly enter water cooling, adopts the DQ high-pressure hydraulic pump of Mulpic to force cooling, rate of cooling 6 ~ 8 DEG C/S, final cooling temperature 350 ~ 360 DEG C.
Mechanical property of steel plate is shown in Table 1.
Embodiment 2:
The present embodiment is a kind of production method of high strength crack arrest Plate Steel, and the chemical constitution weight percent of steel is: C=0.07%, Si=0.18%, Mn=1.60 %, P=0.011%, S=0.0025%, Nb=0.035%, Ti=0.018%, Al=0.039%, Ni=0.42%, Cu=0.25%, Gr=0.16%, all the other are Fe and inevitable impurity.Critical process step comprises:
Smelt: converter tapping P=0.008%, C=0.0041%, adopt LF+VD refinery practice, the omnidistance Argon of LF stove refining, slag making deoxidation, white slag hold-time 22min, refining slag basicity CaO/SiO
2=3.8; VD Fruit storage, at below vacuum tightness 0.5tor, vacuum hold-time 22min, departures molten steel N=40ppm, H=1.5ppm, O=18ppm.
Continuous casting: adopt whole process protection casting, middle bag superheating temperature 18 DEG C, slab thickness 300mm.
Heating: slab heating temperature 1192 DEG C, soaking time 30min.
Rolling: adopt two-phase control rolling, first stage finishing temperature 1048 DEG C, last three percentage pass reductions 16.2%, 18.1%, 20.5%; Subordinate phase finishing temperature 823 DEG C.
Cooling: roll rear steel plate and directly enter water cooling, adopts the DQ high-pressure hydraulic pump of Mulpic to force cooling, rate of cooling 7 ~ 10 DEG C/S, final cooling temperature 368 DEG C.
Mechanical property of steel plate is shown in Table 1.
Example 3:
The present embodiment is a kind of production method of high strength crack arrest Plate Steel, and the chemical constitution weight percent of steel is: C=0.07%, Si=0.22%, Mn=1.58 %, P=0.010%, S=0.0015%, Nb=0.038%, Ti=0.017%, Al=0.038%, Ni=0.35%, Cu=0.18%, Gr=0.15%, all the other are Fe and inevitable impurity.Critical process step comprises:
Smelt: converter tapping P=0.006%, C=0.0036%, adopt LF+VD refinery practice, the omnidistance Argon of LF stove refining, slag making deoxidation, white slag hold-time 22min, refining slag basicity CaO/SiO
2=3.6; VD Fruit storage, at below vacuum tightness 0.5tor, vacuum hold-time 20min, departures molten steel N=38ppm, H=2ppm, O=16ppm.
Continuous casting: adopt whole process protection casting, middle bag superheating temperature 21 DEG C, slab thickness 300mm.
Heating: slab heating temperature 1198 DEG C, soaking time 31min.
Rolling: adopt two-phase control rolling, first stage finishing temperature 1033 DEG C, last three percentage pass reductions 16.1%, 17.3%, 18.2%; Subordinate phase finishing temperature 828 DEG C.
Cooling: roll rear steel plate and directly enter water cooling, adopts the DQ high-pressure hydraulic pump of Mulpic to force cooling, rate of cooling 6 ~ 7 DEG C/S, final cooling temperature 330 ~ 340 DEG C.
Mechanical property of steel plate is shown in Table 1.
Embodiment 4:
The present embodiment is a kind of production method of high strength crack arrest Plate Steel, and the chemical constitution weight percent of steel is: C=0.05%, Si=0.22%, Mn=1.52 %, P=0.008%, S=0.0023%, Nb=0.035%, Ti=0.015%, Al=0.045%, Ni=0.25%, Cu=0.15%, Gr=0.15%, all the other are Fe and inevitable impurity.Critical process step comprises:
Smelt: converter tapping P=0.008%, C=0.0032%, adopt LF+VD refinery practice, the omnidistance Argon of LF stove refining, slag making deoxidation, white slag hold-time 21min, refining slag basicity CaO/SiO
2=3.4; VD Fruit storage, at below vacuum tightness 0.5tor, vacuum hold-time 20min, departures molten steel N=45ppm, H=1.5ppm, O=18ppm.
Continuous casting: adopt whole process protection casting, middle bag superheating temperature target value 22 DEG C, slab thickness 260mm.
Heating: slab heating temperature 1185 DEG C, soaking time 30min.
Rolling: adopt two-phase control rolling, first stage finishing temperature 1053 DEG C, last three percentage pass reductions 16.3%, 18.5%, 23.2%; Subordinate phase finishing temperature control is at 812 DEG C.
Cooling: roll rear steel plate and directly enter water cooling, adopt the DQ high-pressure hydraulic pump of Mulpic to force cooling, rate of cooling requires 8 ~ 12 DEG C/S, final cooling temperature 384 DEG C.
Mechanical property of steel plate is shown in Table 1.
The mechanical property of steel in table 1 embodiment
From table 1 test result, adopt the steel plate that method of the present invention is produced, when thickness reaches 80mm, yield strength still can reach more than 400Mpa, and-40 DEG C, heart portion impelling strength can reach more than 250J.Steel plate employing P-2 sample carries out NDTT assay and can find out, the nil-ductility temperature of steel plate is below-80 DEG C, and steel plate has lower nil-ductility temperature.Adopt the crack arrest of gradient temperature type double tension crack arrest test to 80mm steel plate to test, as shown in Figure 1 ,-10 DEG C of arrest toughness Kca values reach 6500N/mm
3/2above, steel plate has higher crack arrest characteristic, can be good at the user demand meeting super-container vessel key position.
Claims (4)
1. a production method for superstrength crack arrest Plate Steel, is characterized in that: the chemical constitution mass percent of steel is: C≤0.10%, Si=0.10% ~ 0.50%, Mn=1.40% ~ 1.80%, P≤0.015%, S≤0.005%, Nb=0.02% ~ 0.05%, Ti=0.008% ~ 0.02%, Al=0.015% ~ 0.05%, Ni=0.2%0 ~ 0.50%, Cu≤0.35%, Gr≤0.25%, Mo≤0.25%, all the other are Fe and inevitable impurity; Critical process step comprises:
Smelt: converter tapping P≤0.008%, C≤0.005%, adopt LF+VD refinery practice, the omnidistance Argon of LF stove refining, slag making deoxidation, white slag hold-time >=20min, refining slag basicity CaO/SiO2 >=2.5; VD Fruit storage, at below vacuum tightness 0.5tor, vacuum hold-time 18 ~ 25min, departures molten steel N≤45ppm, H≤2ppm, O≤20ppm;
Continuous casting: adopt whole process protection casting, middle bag superheating temperature target value 15 ~ 25 DEG C, slab thickness >=260mm;
Heating: between slab heating temperature 1180 ~ 1220 DEG C, soaking time >=30min;
Rolling: adopt two-phase control rolling, first stage finishing temperature >=980 DEG C, last three percentage pass reduction >=16%, subordinate phase finishing temperature 780 ~ 840 DEG C;
Cooling: roll rear steel plate and directly enter water cooling, the Plate Steel for thickness >=50mm adopts the DQ high-pressure hydraulic pump of Mulpic to force cooling, and rate of cooling requires >=6 DEG C/S, until final cooling temperature is between 300 ~ 400 DEG C.
2. superstrength crack arrest Plate Steel production method according to claim 1, is characterized in that: in the chemical constitution of steel, copper 0.15% ~ 0.35%, chromium 0.15% ~ 0.25%, at least containing more than one elements in molybdenum 0.15% ~ 0.25%.
3. superstrength crack arrest Plate Steel production method according to claim 1, it is characterized in that: in milling step, subordinate phase finishing temperature is 800 ~ 820 DEG C.
4. superstrength crack arrest Plate Steel production method according to claim 1, it is characterized in that: in described cooling step, Plate Steel for thickness >=50mm adopts the DQ high-pressure hydraulic pump of Mulpic to force cooling, rate of cooling is optimized for 6 ~ 15 DEG C/S, until final cooling temperature is optimized for 320 ~ 380 DEG C.
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Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101177760A (en) * | 2007-11-27 | 2008-05-14 | 湖南华菱湘潭钢铁有限公司 | High-strength shipbuilding section and production method thereof |
-
2015
- 2015-05-07 CN CN201510227313.5A patent/CN104789898A/en active Pending
Patent Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101177760A (en) * | 2007-11-27 | 2008-05-14 | 湖南华菱湘潭钢铁有限公司 | High-strength shipbuilding section and production method thereof |
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Application publication date: 20150722 |