CN1210431C - Steel series with high linear energy and low weld crack sensitivity and its preparing process - Google Patents
Steel series with high linear energy and low weld crack sensitivity and its preparing process Download PDFInfo
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Abstract
The present invention relates to 60kg and 70kg grade series high strength steel with high linear energy and low welding crack sensitivity, and a production method thereof, which belongs to the field of low alloy steel manufacture. The steel of the present invention adopts low carbon, Ti-Nb-B composite addition, and composite addition of two or more than two elements of Ni, V, Cu, Mo, Zr and RE; Pcm is respectively to be controlled to be smaller than or equal to 0.21%, and be smaller than or equal to 0.23%; modification thermal treatment is adopted to obtain tempered sorbite tissues with high obdurability; Ti, Nb, O and N are utilized to form second phase mass points with high melting points, and composite precipitated phases to suppress welding coarse grain zones to grow up. Through rolling and modification thermal treatment, the steel of the present invention has excellent combination performance, cold and hot working performance, and welding performance resisting 50 to 150 kJ/cm of high linear energy; manual arc welding, hidden arc welding, gas protective welding, slag welding or electrogas welding is used for welding, which can effectively reduce the welding procedure intensity and can greatly enhance the welding efficiency. The steel of the present invention can be used in industries of petrifaction, chemical industries, metallurgy, urban construction, energy resource, traffic, machinery, hydroelectricity, shipping, etc.
Description
Affiliated technical field
The present invention relates to the production method of a kind of 60kg and 70kg level series with high linear energy and low weld crack sensitivity high-strength steel, belong to low alloy steel and make the field.
Background technology
Before the present invention, just like the patent (JP08232043) of Kawasaki, Japan application " by hot rolling, air quicken cooling form ferrite, perlite and (or) the large-line energy weldable steel that is used for shipbuilding, bridge, pressurized vessel etc. of bainite structure ", the patent (JP04346636) of Japanese Nippon Steel application " contain C, Mn, P, S, Al, B, N, Ni and (or) HAZ of Cu has the high manganese super-high strength steel of flexible ", (JP2704810, JP06049586) " form method that the MnS compound particles is made the large-line energy welding high-strength steel by the complete deoxidation of Al ".Though above-mentioned three's weak point is that steel plate all possesses the large-line energy welding property, does not all possess low-welding crack-sensitive.The patent (JP10008193) of and for example Japanese NKK application " contains the ultrahigh-strength steel that C, Si, Mn, Cu, Ni, Nb, Al, Ti, Cr, B are used to make steel construction such as bridge, storehouse and buildings ".Its weak point is, has added the Cr up to 0.30～0.80% in the steel, has increased production cost, and high Cr can cause temper crack, the toughness of reduction steel.In addition, because B content is very few in the steel, be unfavorable for the steel plate through hardening, thereby the armor plate strength level is not high, its tensile strength lower value is 570MPa only, does not reach 60kg and 70kg level level.
The patent (JP08209238) of NKK application " contains the manufacture method that Si, Mn, Mo, Ni, V, Al, Ti, B obtain the high-strength steel of excellent welding crack sensibility by heating " for another example, though this patent light plate possesses low-crackle sensitive and Chinese People's Anti-Japanese Military and Political College's heat input welding property simultaneously, but Nb, V content in the steel are limited with formula 625Nb+250V+210Ceq=40+t (t is steel plate thickness mm), different with the composition mentality of designing of steel of the present invention, and this patent does not illustrate the concrete intensity rank of steel plate.
Summary of the invention
The production method that the purpose of this invention is to provide a kind of steel series with high linear energy and low weld crack sensitivity, armor plate strength reach 60kg and 70kg level respectively, and steel plate possesses large-line energy weldability and two kinds of excellent properties of low-welding crack-sensitive simultaneously.The production method that provides is simple, is fit to big production operation.
The present invention in order to achieve the above object, designed a kind of steel series with high linear energy and low weld crack sensitivity, the chemical ingredients that it is characterized in that steel percentage ratio meter by weight contains C:0.02～0.13, Si:0.10～0.60, Mn:0.60～1.80, P :≤0.020, S :≤0.010, Al :≤0.01, Ti:0.005～0.025, N:0.0020～0.0060, B:0.0005～0.0020, Nb 0.008～0.040, and Ni≤0.55, V≤0.10, Cu≤0.65, Mo≤0.50, Zr≤0.040, in RE≤0.020 two or more, surplus are Fe and inevitably are mingled with.
A kind of steel series with high linear energy and low weld crack sensitivity of the present invention, armor plate strength are respectively two kinds of 60kg level and 70kg levels, it is characterized in that:
The chemical ingredients of 60kg level steel also must satisfy:
(1)4.0C+Mn≤2.0
(2)0.0020≥N-Ti/3.4-B/0.77≥0
(3)Pcm＝C+Si/30+Mn/20+Cu/20+Ni/60+Cr/20+Mo/15+V/10+5B≤0.21％
The chemical ingredients of 70kg level steel must satisfy:
(1)4.0C+Mn≤2.1
(2)B-0.435×(N-Ti/3.4)≤0.0005
(3)Pcm＝C+Si/30+Mn/20+Cu/20+Ni/60+Cr/20+Mo/15+V/10+5B≤0.23％。
Details are as follows for the reason of C, Si, Mn, P, S, Al, Ti, N, B, Ni, Nb, V, Cu, Mo, RE limited amount among the present invention:
C content of the present invention is chosen in 0.02～0.13%, and C is one of element of indispensable raising steel strength in the steel, along with the increase of carbon content, and Fe in the steel
3C increases, and hardenability also increases, and the tensile strength of steel and yield strength can improve and the decline of unit elongation notch shock toughness.Every increase by 0.1% tensile strength of carbon content approximately improves 90MPa, and yield strength approximately improves 40-50MPa.When the higher steel of welding C content, also the phenomenon of hardening can appear at welded heat affecting zone, the tendency of generation cold cracking when this will aggravate welding.C is the principal element that influences Pcm, control steel Pcm value and should be not more than 0.21% and 0.23% respectively, make it have low welding crack sensibility, C content should be not more than 0.13% in the steel, in this scope, not only improve the intensity of steel but also be fit to production operation, improve its suitability and feasibility in big production.
Si content of the present invention is chosen in 0.10%～0.60%, and Si mainly improves the intensity of steel with the solution strengthening form, but can not too high levels, in order to avoid reduce the toughness of steel.
Mn content of the present invention is chosen in 0.60%～1.80%, when C content during in low scope, it is particularly important that the solution strengthening in the steel just seems, Mn improves the tensile strength of steel and the element of yield strength, it does not worsen the deformability of steel, contains 1% Mn and can improve tensile strength 100MPa approximately.In general, Mn content is favourable in the toughness of 2% following butt welded seam metal, therefore, in low-carbon high strength steel, generally improves the content of Mn, reaches as high as 2%.
P of the present invention≤0.020%, S≤0.010%, this is because P, S content in the steel must be controlled at lower scope, has only the smelting Clean Steel, could guarantee the performance of steel of the present invention.
Al content of the present invention is chosen in≤and 0.010%, Al is the main deoxidant element in the steel, and the maxima solubility in pure γ iron is about 0.6%, and it only faintly increases hardening capacity after dissolving in austenite.So think that Al not have influence substantially to the welding hydrogen induced cracking, when the Al that adds in the steel 0.050% when following, can not have a negative impact to welding hydrogen induced cracking, when the Al too high levels, cause easily to be mingled with in the steel and increase, be unfavorable for the toughness of steel.
Ti content of the present invention is chosen in 0.005%～0.025%, and Ti is a kind of intensive carbide and nitride forming element, and it can improve the room temperature strength and the hot strength of steel significantly, because Ti can play crystal grain thinning, so also can improve the toughness of steel.An amount of Ti can improve the toughness of weld metal, but excessive Ti can make it again to reduce.Consider from the toughness that improves weld metal that in low-alloy high-strength steel it is comparatively suitable that add-on is no more than 0.02% Ti.The second phase particle TiN, the Ti (CN) etc. that utilize Ti to form stop in the large-line energy welding process grain growth of coarse grain zone in the heat affected zone, make grain refining, the low-temperature flexibility of raising steel.
N content of the present invention is chosen in 0.0020～0.0060%, N itself is unfavorable to the obdurability of steel, N in an amount of scope by with other elements (as Ti, Nb, Al, V etc.) form second mutually particle in steel, play important advantageous effect, but its content can not be too high.
B content of the present invention is chosen in 0.0005%～0.0020%, B is the element that improves hardening capacity strongly, the adding of B can effectively suppress the forming core and the generation of proeutectoid ferrite, because the non-equilibrium segregation of B on austenite grain boundary, strongly inhibited γ-α phase transformation, impel austenite when quenching, to form the martensite of tiny low-carbon (LC), thereby improve the yield strength and the tensile strength of steel, in addition, the interaction of B and N can obviously improve the low-temperature flexibility of testing steel.But the B too high levels can make the processing that eliminates stress (SR processing) back " B phase " be netted and separate out generation SR crackle in the steel.B easily forms carbide and nitride, and easily is collected at original austenite crystal prevention, impels in the neighbourhood that dislocation desity increases, and can be used as the trap of hydrogen in partial area, thereby impels the crystal boundary cracking takes place herein.
The effect of Nb is similar to Ti, but much stronger than Ti.Nb also is a kind of element of crystal grain thinning, the Nb (0.03%) that contains denier is remarkable refinement steel crystal grain and improve the room temperature tensile strength of steel just, but Nb is also easy and elements such as Fe, C form the low melting point eutectic things, thereby increase the tendency that weld metal produces thermal crack, thereby its content is controlled at below 0.040%.
Also contain among Ni, V, Cu, Mo, Zr, the RE two or more among the present invention.
Ni has certain strengthening effect, and the Ni of adding 1% can improve the about 20MPa of steel strength.Ni can also improve the toughness, particularly low-temperature flexibility of steel significantly.No matter add Ni in the steel, be base material, still simulates welded heat affecting zone and all improved low-temperature flexibility significantly.But during too high levels, cause the steel plate iron scale to be difficult to come off, so the upper limit is controlled at 0.55%.
V is a kind of suitable intensive carbide forming element.It can improve the normal temperature and the hot strength of steel by the formation of crystal grain thinning and carbide, when V and Cr, Mo exist simultaneously, then can form complicated carbide and reduce the plasticity and toughness of welding joint in drawing process.It is higher to the susceptibility of crackle when handling that the welding joint of the ben Cr of being, Mo, V steel thick-walled vessel carries out stress-removal at postwelding, therefore for guarantee plasticity and toughness also or stress-removal avoid crackle to produce all must measuring (being limited in below 0.10%) by strict control V.
Cu mainly plays the precipitation strength effect in steel, help obtaining good low-temperature flexibility in addition, increases the antifatigue crack propagation ability of steel.During too high levels, the steel plate welding heat influence area toughness reduces, and produces check crack in the steel plate rolling process, so its upper limit is controlled at 0.65%.
The Mo element can improve steel strength, and particularly hot strength is higher than Mn, Cr, simultaneously it also be strengthen the anti-Hydrogen Energy power of steel one of the chief elements.The Mo of adding 0.5% can make the high temperature creep strength of steel improve 75%, a spot of Mo (about 0.2%) can also improve the toughness of weld metal, but add the hardenability that Mo also can improve steel, thereby improve the susceptibility of steel, so the upper limit of Mo is controlled at 0.50% to welding cold cracking.
Zr content was at 0.005% o'clock, and the RE addition all helps to improve steel plate Chinese People's Anti-Japanese Military and Political College heat input welding property when about 250g/t.
The invention belongs to low alloy steel and make the field, low alloy steel is Fe base steel, and the present invention is except that containing above-mentioned chemical ingredients, and surplus is Fe and inevitably is mingled with.
The production method of 60kg of the present invention and 70kg level series with high linear energy and low weld crack sensitivity high-strength steel adopts the desulfurizing iron technology, the converter top and bottom blowing, vacuum depths reason and trimming, be rolled by common ultra-clean steel technology, thermal treatment, it is characterized in that: the chemical ingredients of steel percentage ratio is by weight counted C:0.02～0.13, Si:0.10～0.60, Mn:0.60～1.80, P :≤0.020, S :≤0.010, Al :≤0.01, Ti:0.005～0.025, N:0.0020～0.0060, B:0.0005～0.0020, Nb:0.008～0.040, and Ni≤0.55, V≤0.10, Cu≤0.65, Mo≤0.50, Zr≤0.040, in RE≤0.020 two or more, surplus is Fe and inevitably is mingled with, the start rolling temperature of steel 〉=1180 ℃, three roads, controlled rolling end accumulative total draft 〉=40%, finishing temperature≤870 ℃; The employing quenching-and-tempering process is produced, and quenching temperature is 910～960 ℃, and soaking time is: 30～40 minutes+thickness of slab (mm) * 1 minute/mm; 600～660 ℃ of tempering temperatures, soaking time are 40～55 minutes+thickness of slab (mm) * 1 minute/mm.
Steel of the present invention has following advantage:
1. this steel possesses low-welding crack-sensitive, and the welding property excellence can be simplified weldprocedure, has reduced cost, adapts to big production requirement.
2. this steel can bear the large-line energy welding, thereby has increased substantially the welding efficiency and the construction speed of product.
3. under large-line energy (50-100kJ/cm) welding conditions, HAZ has good obdurability, thereby has guaranteed the safe reliability of product.
Embodiment
Embodiment 1: according to composition of steel requirement of the present invention, smelted steel of the present invention at vacuum induction furnace, steel ingot is heated to 1280 ℃ comes out of the stove rolling, start rolling temperature is respectively 1180 ℃, 1200 ℃, 1220 ℃, last three passages accumulative total draft 40%～45%, finishing temperature is respectively 830,850,870 ℃.Rolled sheet material thickness difference 16,20,24mm.60kg level steel quenching temperature is respectively 910,930,950 ℃, and soaking time was respectively 50,54,58 minutes; Tempering temperature is respectively 600,630,660 ℃, tempering insulation time was respectively 60,64,68 minutes, 70kg level steel quenching temperature and tempering temperature are the same, but Quenching Soaking Time was respectively 52,56,60 minutes, tempering insulation time was respectively 66,70,74 minutes, subsequently various steel plates have been carried out mechanical property test, tested-40 ℃ of steel plate impelling strength and the welding of the 60kJ/cm large-line energy impelling strength of-40 ℃ of HAZ afterwards, and contrast with corresponding comparative steel, data see Table 1 and table 2.
-40 ℃ impelling strength and compared steel are in same level before steel of the present invention and the compared steel welding heat simulation test, but after 60kJ/cm large-line energy welding, and the HAZ impelling strength of steel of the present invention-40 ℃ is higher than compared steel far away.
From table 1 and table 2 as seen, steel of the present invention adopts the compound oxynitride of Ti-Nb-B to obtain Chinese People's Anti-Japanese Military and Political College's heat input in composition design, and (〉=50kJ/cm) welding property by reducing carbon, adopts special microalloying, improve the purity of steel simultaneously, thereby guarantee that this steel has good low-temperature flexibility.Steel of the present invention all can be implemented at each smelter, can improve the welding efficiency of large-scale steel structure greatly, reduces manufacturing cost.
Table 1 steel of the present invention (60kg level) contrasts with the chemical ingredients and the HAZ impelling strength of compared steel:
| Invention steel 1 | Comparative steel | Invention steel 2 | Comparative steel | Invention steel 3 | Comparative steel | ||
| Composition | C | 0.07 | 0.08 | 0.06 | 0.07 | 0.08 | 0.08 |
| Si | 0.25 | 0.24 | 0.26 | 0.23 | 0.24 | 0.26 | |
| Mn | 1.45 | 1.46 | 1.47 | 1.48 | 1.43 | 1.50 | |
| P | 0.015 | 0.015 | 0.016 | 0.017 | 0.018 | 0.016 | |
| S | 0.005 | 0.006 | 0.005 | 0.006 | 0.006 | 0.005 | |
| Ti | 0.012 | -- | 0.010 | -- | 0.013 | -- | |
| B | 0.0008 | 0.0007 | 0.0009 | 0.0007 | 0.0007 | 0.0005 | |
| Al | 0.004 | 0.020 | 0.003 | 0.032 | 0.005 | 0.034 | |
| O | 0.0028 | 0.0026 | 0.0032 | 0.0030 | 0.0036 | 0.0028 | |
| N | 0.0049 | 0.0040 | 0.0048 | 0.0041 | 0.0048 | 0.0040 | |
| Ni | 0.20 | 0.21 | 0.21 | 0.23 | 0.19 | 0.22 | |
| Nb | 0.015 | -- | 0.010 | -- | 0.011 | -- | |
| V | 0.04 | 0.04 | 0.05 | 0.06 | 0.04 | 0.05 | |
| Cu | 0.15 | 0.14 | 0.17 | 0.15 | 0.16 | 0.15 | |
| Mo | 0.10 | 0.13 | 0.11 | 0.12 | 0.12 | 0.14 | |
| Zr | 0.008 | -- | 0.007 | -- | 0.008 | -- | |
| RE | 200(g/t) | -- | 200(g/t) | -- | 200(g/t) | -- | |
| Armor plate strength (MPa) | 640 | 650 | 630 | 635 | 650 | 655 | |
| Steel plate toughness (J) | 98 | 85 | 97 | 87 | 89 | 87 | |
| HAZ toughness (J) | 65 | 10 | 63 | 9 | 62 | 7 | |
Table 2 steel of the present invention (70kg level) contrasts with the chemical ingredients and the HAZ impelling strength of compared steel:
| Invention steel 1 | Comparative steel | Invention steel 2 | Comparative steel | Invention steel 3 | Comparative steel | ||
| Composition | C | 0.08 | 0.09 | 0.09 | 0.10 | 0.09 | 0.11 |
| Si | 0.28 | 0.30 | 0.30 | 0.31 | 0.31 | 0.29 | |
| Mn | 1.48 | 1.49 | 1.49 | 1.52 | 1.50 | 1.47 | |
| P | 0.015 | 0.016 | 0.015 | 0.015 | 0.016 | 0.0016 | |
| S | 0.005 | 0.005 | 0.005 | 0.006 | 0.005 | 0.005 | |
| Ti | 0.013 | -- | 0.011 | -- | 0.012 | -- | |
| B | 0.0007 | 0.0010 | 0.0008 | 0.0009 | 0.0007 | 0.0009 | |
| Al | 0.006 | 0.023 | 0.004 | 0.025 | 0.005 | 0.035 | |
| O | 0.0026 | 0.0025 | 0.0032 | 0.0028 | 0.0036 | 0.0026 | |
| N | 0.0043 | 0.0038 | 0.0046 | 0.0041 | 0.0045 | 0.0037 | |
| Ni | 0.23 | 0.26 | 0.25 | 0.27 | 0.26 | 0.28 | |
| Nb | 0.019 | -- | 0.017 | -- | 0.018 | -- | |
| V | 0.05 | 0.06 | 0.06 | 0.07 | 0.05 | 0.07 | |
| Cu | 0.17 | 0.16 | 0.17 | 0.14 | 0.18 | 0.20 | |
| Mo | 0.12 | 0.14 | 0.10 | 0.15 | 0.13 | 0.14 | |
| Zr | 0.006 | -- | 0.008 | -- | 0.007 | -- | |
| RE | 200(g/t) | -- | 200(g/t) | -- | 200(g/t) | -- | |
| Armor plate strength (MPa) | 720 | 735 | 730 | 740 | 730 | 760 | |
| Steel plate toughness (J) | 87 | 85 | 84 | 86 | 91 | 83 | |
| HAZ toughness (J) | 54 | 9 | 54 | 8 | 60 | 10 | |
Annotate: the RE in table 1, the table 2 (g/t), represent to add in the steel per ton RE amount 200 grams; The impelling strength of HAZ when the impelling strength of steel plate when steel plate toughness is-40 ℃, HAZ toughness are welded back-40 ℃ for the 60kJ/cm large-line energy.
Steel of the present invention can be widely used in industries such as petrochemical industry, chemical industry, metallurgy, urban construction, the energy, traffic, machinery, water power and boats and ships, has extremely wide application prospect.
Claims (1)
1. the production method of a series with high linear energy and low weld crack sensitivity high-strength steel, adopt the desulfurizing iron technology, the converter top and bottom blowing, vacuum depths reason and trimming, be rolled by common ultra-clean steel technology, thermal treatment, it is characterized in that: the chemical ingredients of steel percentage ratio is by weight counted C:0.02～0.13, Si:0.10～0.60, Mn:0.60～1.80, P :≤0.020, S :≤0.010, Al :≤0.01, Ti:0.005～0.025, N:0.0020～0.0060, B:0.0005～0.0020, Nb:0.008～0.040, and Ni≤0.55, V≤0.10, Cu≤0.65, Mo≤0.50, Zr≤0.040, in RE≤0.020 two or more, surplus is Fe and inevitably is mingled with, the start rolling temperature of steel 〉=1180 ℃, three roads, controlled rolling end accumulative total draft 〉=40%, finishing temperature≤870 ℃; The employing quenching-and-tempering process is produced, and quenching temperature is 910～960 ℃, and soaking time is: 30～40 minutes+thickness of slab (mm) * 1 minute/mm; 600～660 ℃ of tempering temperatures, soaking time are 40～55 minutes+thickness of slab (mm) * 1 minute/mm.
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Families Citing this family (12)
| Publication number | Priority date | Publication date | Assignee | Title |
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| CN100396809C (en) * | 2005-09-12 | 2008-06-25 | 鞍钢股份有限公司 | Thick steel plate with great line energy and low welding crack sensitivity and its production process |
| CN100463994C (en) * | 2005-11-07 | 2009-02-25 | 鞍钢股份有限公司 | Nb-Ti microalloying steel suitable for large line energy welding and smelting method therefor |
| CN101418416B (en) * | 2007-10-26 | 2010-12-01 | 宝山钢铁股份有限公司 | Low welding crack sensitivity steel plate with yield strength of 800MPa grade and method for producing the same |
| CN101476080B (en) * | 2008-12-26 | 2011-01-26 | 首钢总公司 | Low welding crack sensitivity, quenching and tempering, high rigid plate and manufacturing method thereof |
| CN101812634B (en) * | 2009-02-23 | 2012-03-28 | 宝山钢铁股份有限公司 | Low-carbon low-welding crack-sensitive high-strength steel and steel plate and manufacture method thereof |
| CN101812639A (en) * | 2010-04-20 | 2010-08-25 | 马鞍山钢铁股份有限公司 | Steel used for welding hull with high strength and high input energy and production method thereof |
| CN101899613B (en) * | 2010-07-15 | 2012-07-18 | 南京钢铁股份有限公司 | Method for reducing surface cracks of medium carbon niobium-containing steel |
| CN102605287B (en) * | 2012-03-09 | 2013-07-31 | 武汉钢铁(集团)公司 | Steel for high-ductility anti-seismic structure with yield ratio smaller than or equal to 0.70 and production method of steel |
| CN104532148A (en) * | 2014-12-10 | 2015-04-22 | 南京钢铁股份有限公司 | 800MPa grade low-welding crack sensitive tempering type hydroelectric steel plate |
| CN108603267B (en) * | 2016-02-03 | 2021-02-23 | 杰富意钢铁株式会社 | Steel material for high heat input welding |
| CN106755868B (en) * | 2016-12-13 | 2019-01-18 | 钢铁研究总院 | A kind of low cost can Large Heat Input Welding high-strength and high ductility steel plate manufacturing method |
| CN107475622B (en) * | 2017-09-05 | 2019-10-08 | 武汉钢铁有限公司 | Steel plate and its manufacturing method with good thermal processability energy |
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