CN106756612B - A kind of easy laser welding hull plate steel of bainite/martensite/austenite high-ductility and manufacture method - Google Patents
A kind of easy laser welding hull plate steel of bainite/martensite/austenite high-ductility and manufacture method Download PDFInfo
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
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- 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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/18—Hardening; Quenching with or without subsequent tempering
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- 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
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- 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
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
- C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
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- 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
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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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
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
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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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
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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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/001—Austenite
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/002—Bainite
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/008—Martensite
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Abstract
The present invention provides a kind of easy laser welding hull plate steel of bainite/martensite/austenite high-ductility and manufacture method, and each component is by mass percentage in ship steel：C：0.020%~0.060%, Ni：1.50%~3.50%, Cu：1.00%~2.00%, Mo：0.10%~0.60%, Cr：0.20%~0.60%, Mn：0.80%~1.20%, Si：0.20%~0.50%, Nb：0.040%~0.080%, Ti：0.005%~0.020%, Al：0.010%~0.050%, P≤0.006%, S≤0.001%, surplus are Fe and inevitable impurity.The manufacture method of Ultra-low carbon ship steel is：Sheet billet continuous casting, low temperature reheat, recrystallization and the big pressure rolling of non-recrystallization zone two benches, direct quenching DQ, coexistence region quench L, tempering heat treatment.This method can significantly improve the low-temperature flexibility of steel, 84 DEG C of Charpy v-notch ballistic work >=150J, and uniform in the different cross section position low-temperature flexibility of 20~57mm slabs, while have the characteristics of production efficiency is high, production cost is low, technique is simple.
Description
Technical field
The present invention relates to ship steel field, a kind of bainite/martensite/Austria of ship and ocean engineering is specifically provided
The easy laser welding hull plate steel of family name's body high-ductility and manufacture method.
Background technology
With world's shipbuilding industry and marine settings industry develop rapidly, to the machine of the structural steels such as hull, ocean platform
Tool performance and security performance propose higher and higher requirement.Because being on active service in specific marine environment, to hull, ocean platform
With structural steel in addition to requiring to reach certain intensity, good weldability, resistance to air and corrosive properly, also require that it has
Higher low-temperature flexibility, the especially stability requirement to the low-temperature flexibility in slab section are higher.
Conventional hulls structural steel is usually to use Ni-Cr-Mo-V on the basis of mild steel (carbon content~0.20wt.%)
It is alloying process and tempered martensite is obtained by Q-tempering Technology for Heating Processing realizes good of high-strength and high ductility
Match somebody with somebody.But it is not only very unfavorable to the low-temperature flexibility of steel because such steel carbon content is higher, and the welding crack sensibility of steel refers to
Number Pcm (Pcm=C+Si/30+Ni/60+ (Mn+Cr+Cu)/20+Mo/15+V/10+5B) is also higher, to avoid steel plate postwelding from existing
Occurs cold crack at welding point, steel plate needs to be preheated before weldering, therefore can improve welding sequence cost, increase welding consumption
When.The patent of invention of Application No. 200710094178 describes a kind of high-strength steel and its manufacture method, but due to carbon equivalent compared with
Height, need to preheat under higher temperature during welding, seriously constrain welding process.In recent years, it is reduction manufacturing cost, while and can
Further improve the obdurability and weldability of ship steel, people devise the ageing strengthening containing Cu of a kind of low-carbon or Ultra-low carbon
Steel, this steel mainly reduce cost of alloy by reducing the noble element such as Ni, Cr, Mo content, are dropped by Ultra-low carbon design
Low-carbon-equivalent, so as to improve welding performance.Such steel roll it is latter as through solid solution plus aging strengthening model, Cu is all solid during solution treatment
It is dissolved in matrix, is separated out in ag(e)ing process with Cu simple substance particulate forms, so as to play certain precipitation enhancement to make up
The loss of strength that carbon drop is brought.
Conventional hulls structural steel, the whether low-carbon (carbon content~0.20wt.%) of early stage, Ni-Cr-Mo-V systems alloying
Steel, the low-carbon still developed in recent years or the Ultra-low carbon steel of ageing strengthening containing Cu, generally then used using reheating after rolling
Quenching, tempering heat treatment process, i.e. QT techniques, or by rolling rear direct quenching and then being tempered thermal process, i.e. DQT techniques, come
Tempered martensite/bainite structure is obtained to realize the matched well of high-strength and high ductility.Not only manufacturing process flow is short for DQT techniques,
It is energy-saving, and by the way that after recrystallization zone and non-recrystallization zone two-phase control rolling the effective particle size after phase transformation can refine
So as to be advantageous to improve the obdurability of steel.Patent of invention such as Publication No. CN1651589A is prepared for one kind using QT technique
High strength weldable ageing hardening steel, but steel described in this method yield strength it is relatively low be 520MPa, toughness examination temperature also compared with
It is low, it is desirable to -40 DEG C of ballistic work >=160J.Publication No. CN102021489A and CN104073731A patent of invention describe one
Kind by DQT techniques come the ultra high strength structural ship steel that manufactures, but its yield strength investigates ballistic work temperature also in 520MPa or so
It is not less than -60 DEG C.Under the Service Environment of ocean, hull structural steel and offshore platform steel need to bear the dynamic of a series of complex
The role and influence of the factors such as the stress caused by state load and hull construction and assembling, therefore, improving the same of steel strength
When, it is necessary to consider how steel avoid that low stress damage occurs.This requires steel to have enough toughness storages in plastic failure
It is standby, particularly require that there is higher low-temperature flexibility at a temperature of very low marine environment.
The method for improving toughness in the prior art has two kinds, is on the one hand to improve upper mounting plate ballistic work, is on the other hand drop
Low ductile-brittle transition temperature.By further investigation, people in recrystallization zone and non-recrystallization zone heavy reduction rolling by obtaining
Flat austenite, so as to refine bainite/martensite substructure after phase transformation, to reduce ductile-brittle transition temperature.In addition, also by
A two-phase section quenching is carried out between quenching and tempering process, to realize the partition of among the austenite stabilizing elements, is obtained in tempering
A certain amount of adverse transformation austenite increases substantially the low-temperature flexibility of steel, i.e. QLT techniques.But recrystallization zone and non-recrystallization zone
The technique that direct quenching DQ and two-phase section quenching add-back fire LT are combined after heavy reduction rolling is also more rare.
The impact flexibility temperature for easily welding most of steel technology examination that existing height is tough is not less than -60 DEG C, and this is not
Military service feature of the steel of the purposes such as conventional hulls, ocean platform in severe cold low temperature marine environment can be met.In addition, hull is used
Steel, offshore platform steel thickness specification are more, and slab has Section Effect in thickness direction, i.e., occurs in the thickness direction of slab
The unstable phenomenon of performance, particularly low-temperature flexibility is unstable, has a strong impact on the overall performance of steel plate.
The present invention to solve the above problems, provide a kind of easy laser welding hull plate steel of bainite/martensite/austenite high-ductility and
Manufacture method, meet military service feature of the steel in severe cold low temperature marine environment.
The content of the invention
Object of the present invention is to provide a kind of easy laser welding hull plate steel of bainite/martensite/austenite high-ductility and manufacture
Method, by being rolled to steel plate, Technology for Heating Processing, solve conventional hulls, ocean platform, petroleum pipeline and faced with steel
The problem of low-temperature flexibility is insufficient, slab section toughness is unstable.
The technical scheme is that：
A kind of easy laser welding hull plate steel of bainite/martensite/austenite high-ductility, each component is by mass percentage in ship steel
Meter：C：0.020%~0.060%, Ni：1.50%~3.00%, Cu：1.00%~2.00%, Mo：0.10%~0.60%,
Cr：0.20%~0.60%, Mn：0.80%~1.50%, Si：0.20%~0.50%, Nb：0.040%~0.080%, Ti：
0.005%~0.020%, Al：0.010%~0.050%, P≤0.006%, S≤0.001%, surplus is for Fe and unavoidably
Impurity；Ship steel meets welding crack sensibility index：
Pcm=C+Si/30+Ni/60+ (Mn+Cr+Cu)/20+Mo/15+V/10+5B≤0.34.
Further, each component is by mass percentage in ship steel：C：0.023%~0.037%, Ni：1.73%~
2.01%, Cu：1.09%~1.76%, Mo：0.13%~0.367%, Cr：0.24%~0.36%, Mn：0.85%~
1.13%, Si：0.24%~0.39%, Nb：0.043%~0.062%, Ti：0.0053%~0.012%, Al：0.012%
~0.034%, P≤0.004%, S≤0.0008%, surplus are Fe and inevitable impurity；Ship steel meets weld crack
Sensitivity indices：Pcm=C+Si/30+Ni/60+ (Mn+Cr+Cu)/20+Mo/15+V/10+5B≤0.25.
Further, each component is by mass percentage in ship steel：C：0.041%~0.056%, Ni：2.15%~
2.87%, Cu：1.81%~1.93%, Mo：0.38%~0.57%, Cr：0.38%~0.52%, Mn：1.213%~
1.479%, Si：0.41%~0.49%, Nb：0.065%~0.078%, Ti：0.013%~0.018%, Al：0.036%
~0.048%, P≤0.003%, S≤0.0007%, surplus are Fe and inevitable impurity；Ship steel meets weld crack
Sensitivity indices：Pcm=C+Si/30+Ni/60+ (Mn+Cr+Cu)/20+Mo/15+V/10+5B≤0.32.
The effect of each element of the present invention and proportioning are according to as follows：
C：With significant solid solution strengthening effect, and the quenching degree of steel can be improved, but C content increase is tough to steel low temperature in steel
Property and weldability are very unfavorable.Therefore designed in the present invention using Ultra-low carbon, C content is controlled in 0.02~0.06wt.%.
Cu：The crucial precipitation strength element of steel of the present invention, Cu can be in steel in temper aging process independent of C, N element
In in the form of nanocluster separate out so as to produce significantly precipitation strength effect, can make up reduce C and caused by loss of strength, together
When Cu can also improve the sea water corrosion resistant of steel.To ensure that steel has certain intensity, in the present invention Cu content control exist
1.00~2.00wt.%.
Ni：Ni and Cu form complex precipitates in ag(e)ing process, and Ni can promote Cu Precipitation Kinetics, in ag(e)ing process
The roughening of rich Cu phases can be suppressed, so as to Reinforced Cu precipitating reinforcing effect.In addition, Ni can also improve steel quenching degree and low temperature it is tough
Property, while there is certain solution strengthening effect, moreover it is possible to Cu hot-short effect is prevented, significantly improves the surface fire check of the steel containing Cu
Tendency.In view of the financial cost of steel, Ni contents are controlled in 1.50~3.00wt.% in the present invention.
Mo：Solid solution Mo can significantly improve the quenching degree of steel, and also with certain solution strengthening effect, while Mo can be improved
Temper resistance, significantly reduce temper brittleness.The control of Mo contents is in 0.100~0.60wt.% in the present invention.
Cr：The quenching degree that solid solution Cr can significantly improve steel (has reduction A concurrentlyc3Temperature and raising overcooling austenite stability
Effect), while Cr easily forms the corrosion resistance that dense oxidation film is remarkably improved steel.In the present invention control of Cr contents 0.20~
0.60wt.%.
Mn：The quenching degree of steel is remarkably improved, while there is certain solution strengthening effect, can also reduce Ac3Temperature, make
It is wider to obtain the temperature window rolled in non-recrystallization zone, but during Mn too high levels, the corrosion resisting property of steel reduces, and in welding hot shadow
Ring area and easily form thick M/A islands, have a strong impact on the low-temperature flexibility of welding heat affected zone.The control of Mn contents exists in the present invention
0.800~1.500wt.%.
Si：One of deoxidant element in steel, while silicon is also non-carbide formation element, is present in steel matrix with solution
In, there is certain solution strengthening effect, but excessive silicon is unfavorable to the low-temperature flexibility of steel, the welding cold cracking of steel, fire check
Sensitiveness will increase, and Si contents control of the present invention is 0.20~0.50wt.%.
Nb：The Nb being dissolved during high temperature soak can improve the quenching degree of steel, and deformation-induced precipitation Nb can suppress deformation Ovshinsky
The recrystallization of body so that when being rolled in non-recrystallization zone, flat austenite can be obtained.The too low above-mentioned effect of Nb contents is not notable,
Too high levels have detrimental effect to the toughness of welding heat affected zone.The control of Nb contents is in 0.040~0.080wt.% in the present invention.
Ti：Strong carbonitride-forming elements, micro Ti can combine to form TiN with N in steel, austenite crystal when preventing soaking
Growing up for grain, can also prevent growing up for austenite crystal, so as to improve weldability in welding heat affected zone.Ti contains in the present invention
Amount control is in 0.005~0.020wt.%.
Al：It is strong deoxidant element, can also combines to form AlN with N, the work for having the aged brittleness for preventing steel and crystal grain thinning
With.Al content control is in 0.010~0.050wt.% in the present invention.
P and S：Impurity element in steel, it is very unfavorable to the performance especially low-temperature flexibility of steel, to its content in steel of the present invention
Should strictly it control, respectively no higher than 0.01wt.% and 0.001wt.%.
Further, the microstructure of ship steel is mainly made up of bainite, martensite, austenite, wherein bainite body
Fraction is 70%~90%, and Martensite Volume Fraction is 10%~20%, and austenite volume fraction is 4%~10%；It is above-mentioned
Component sum is 100%.
Further, bainite volume fraction is 76%~85% in the microstructure of ship steel, Martensite Volume Fraction
For 13%~19%, austenite volume fraction is 6%~8%；Said components sum is 100%.
A kind of manufacture method of the easy laser welding hull plate steel of bainite/martensite/austenite high-ductility, concrete technology step are：
(1) sheet billet continuous casting：Prepared by Low Superheat Pouring, the cast degree of superheat are not more than 20 DEG C, take slighter compress and electromagnetic agitation skill
Art, to reduce steel plate center portion degree of segregation；
(2) low temperature reheats：Continuous casting billet is subjected to low-temperature heat so that steel plate has relatively fine autstenitic grain size,
Heating-up temperature is 1000~1150 DEG C, is incubated 60~180min；
(3) recrystallization rolls with the big pressure of non-recrystallization zone two benches：2~5 are carried out in recrystallization zone temperature range
Secondary heavy reduction rate rolling, start rolling temperature：1000~1150 DEG C, finishing temperature：980~1100 DEG C, single pass rolling reduction during rolling
It is big and roll fast slow so that steel plate has larger rolling penetration, while allowing its surface to recrystallize, allows its center portion also most
Recrystallize to big degree, eliminate the segregation of element to a certain extent, control rolls speed and is not higher than 1.5m/s, draught per pass
Not less than 15%；3~10 passages " the big pressure of low temperature " rolling, start rolling temperature are carried out in non-recrystallization zone temperature range：920~
1000 DEG C, finishing temperature：850~920 DEG C.The above-mentioned big pressure rolling overall compression ratio of two benches is not less than 8, is rolled in non-recrystallization zone
Compression ratio is not less than 3 when processed；The austenite pattern for rolling rear steel plate is in flat, the grain boundary area of flattening austenite compared with etc. shaft-like
The grain boundary area of austenite is more, can for follow-up direct quenching when bainite/martensite phase transformation more nucleation sites are provided, so as to
So that the substructure size of bainite/martensite is more tiny, more the substructure of fine size is lath beam or lath block, is steel
Strengthening and Toughening control unit, therefore the obdurability of steel can be increased substantially, especially improve low-temperature flexibility.
(4) direct quenching DQ：Steel plate is quickly sent to press quenching machine after terminating and quenched by rolling, direct quenching temperature
Spend for 850~920 DEG C, water quenching speed control is not higher than 200 in 1~2m/min, cooling rate >=20 DEG C/s, surface of steel plate final cooling temperature
℃；
(5) two-phase section quenching L：Two-phase section is again heated to the steel plate after quenching, is heated to carrying out immediately after two-phase section
Secondary quenching, hardening heat are 740~780 DEG C, and 60~90min of soaking time, above-mentioned two-phase section refers to austenite/ferrite
Area；
(6) tempering heat treatment：Steel plate after secondary quenching is tempered in heat-treatment furnace, temperature be 500~
670 DEG C, 60~120min of tempering time, carry out being air-cooled to room temperature after tempering；The a large amount of disperse educts of precipitated phase in steel, play significantly
Ground precipitation enhancement, while a certain amount of adverse transformation austenite is formed between bainite/martensite lath, crackle can be prevented
Propagation or apparatus with shock absorbing, so as to significantly improve low-temperature flexibility.
Further, in step (3), 3 passage heavy reduction rate rollings, open rolling temperature are carried out in recrystallization zone temperature range
Degree：1120 DEG C, finishing temperature：1000 DEG C, roll speed：1.5m/s, draught per pass：21%；In non-recrystallization zone temperature range
5 passes of interior progress, start rolling temperature：950 DEG C, finishing temperature：870 DEG C, roll speed：1.3m/s, draught per pass：
18.7%.
Further, in step (4), direct quenching temperature：885 DEG C, the cool time：90min.
Further, in step (5), the type of cooling is water cooling during secondary quenching；Water quenching speed control in 1~2m/min,
Cooling rate >=20 DEG C/s, surface of steel plate final cooling temperature are not higher than 200 DEG C.
Further, in step (5), hardening heat：760 DEG C, the cool time：120min.
Further, in step (6), temperature：654 DEG C, tempering time：70min.
The advantage of the invention is that：
(1) steel plate yield strength >=590MPa of the present invention, -84 DEG C of Charpy v-notch ballistic work (KV2-84℃) >=150J is (single
Value), and fracture fibre ratio (FA-84℃) >=60% (monodrome).
(2) the thickness x cross sectional stable performance of steel plate of the present invention, especially low-temperature flexibility are relatively stable.
(3) compared with traditional processing technology, production technology of the invention is ensureing that it is excellent high-strength that low-carbon ship steel has
The matching of high-ductility, also there is higher low-temperature impact fracture fibre ratio so that brittle failure is not easy when steel is on active service at low temperature, is more had
Safety guarantee.
Brief description of the drawings
Fig. 1 is the scanning electron microscope (SEM) photograph of steel of the present invention；
Fig. 2 is the rolling Technology for Heating Processing figure of steel of the present invention；
Fig. 3 is X-ray diffraction measure result schematic diagram when austenite volume fraction is 4% in steel of the present invention.
Embodiment
The preferred embodiments of the present invention are specifically described below in conjunction with the accompanying drawings, wherein, accompanying drawing forms the application part, and
It is used for the principle for explaining the present invention together with embodiments of the present invention.
Table 1 is the chemical composition of steel in the embodiment in the present invention, smelts 3 stoves altogether by different Ni, Cu contents, 3 stove steel
Carbon content is the ultra-low-carbon steel less than 0.06%；Specifically it is shown in Table 1.
The chemical composition (wt.%) of steel in embodiment in the present invention of table 1
Table 2 is specifically shown in Table 2 for the specific rolling process of steel in the embodiment and comparative example in the present invention.
Table 3 is Heat-Treatment of Steel technical process in the embodiment and comparative example in the present invention, is specifically shown in Table 3.
Table 4 is the mechanical property of different-thickness gauge steel in the embodiment and comparative example in the present invention, is specifically shown in Table 4.
The specific rolling process of steel in embodiment and comparative example in the present invention of table 2
Heat-Treatment of Steel technique in embodiment and comparative example in the present invention of table 3
The mechanical property of different-thickness gauge steel in embodiment and comparative example in the present invention of table 4
The foregoing is only a preferred embodiment of the present invention, but protection scope of the present invention be not limited thereto,
Any one skilled in the art the invention discloses technical scope in, the change or replacement that can readily occur in,
It should all be included within the scope of the present invention.
Claims (9)
- A kind of 1. easy laser welding hull plate steel of bainite/martensite/austenite high-ductility, it is characterised in that each component in the ship steel By mass percentage：C：0.020%~0.060%, Ni：1.50%~3.00%, Cu：1.00%~2.00%, Mo： 0.10%~0.60%, Cr：0.20%~0.60%, Mn：0.80%~1.50%, Si：0.20%~0.50%, Nb： 0.040%~0.080%, Ti：0.005%~0.020%, Al：0.010%~0.050%, P≤0.006%, S≤ 0.001%, surplus is Fe and inevitable impurity；The ship steel meets welding crack sensibility index：Pcm=C+Si/30 +Ni/60+(Mn+Cr+Cu)/20+Mo/15+V/10+5B≤0.34；The microstructure of the ship steel is mainly by bainite, horse Family name's body, austenite are formed, and wherein bainite volume fraction is 70%~90%, and Martensite Volume Fraction is 10%~20%, difficult to understand Family name's body volume fraction is 4%~10%；Said components sum is 100%.
- A kind of 2. easy laser welding hull plate steel of bainite/martensite/austenite high-ductility according to claim 1, it is characterised in that Each component is by mass percentage in the ship steel：C：0.023%~0.037%, Ni：1.73%~2.01%, Cu： 1.09%~1.76%, Mo：0.13%~0.367%, Cr：0.24%~0.36%, Mn：0.85%~1.13%, Si： 0.24%~0.39%, Nb：0.043%~0.062%, Ti：0.0053%~0.012%, Al：0.012%~0.034%, P ≤ 0.004%, S≤0.0008%, surplus are Fe and inevitable impurity；The ship steel meets that welding crack sensibility refers to Number：Pcm=C+Si/30+Ni/60+ (Mn+Cr+Cu)/20+Mo/15+V/10+5B≤0.25.
- A kind of 3. easy laser welding hull plate steel of bainite/martensite/austenite high-ductility according to claim 1, it is characterised in that Each component is by mass percentage in the ship steel：C：0.041%~0.056%, Ni：2.15%~2.87%, Cu： 1.81%~1.93%, Mo：0.38%~0.57%, Cr：0.38%~0.52%, Mn：1.213%~1.479%, Si： 0.41%~0.49%, Nb：0.065%~0.078%, Ti：0.013%~0.018%, Al：0.036%~0.048%, P ≤ 0.003%, S≤0.0007%, surplus are Fe and inevitable impurity；The ship steel meets that welding crack sensibility refers to Number：Pcm=C+Si/30+Ni/60+ (Mn+Cr+Cu)/20+Mo/15+V/10+5B≤0.32.
- A kind of 4. easy laser welding hull plate steel of bainite/martensite/austenite high-ductility according to claim 1, it is characterised in that Bainite volume fraction is 76%~85% in the microstructure of the ship steel, and Martensite Volume Fraction is 13%~19%, Austenite volume fraction is 6%~8%；Said components sum is 100%.
- 5. the easy laser welding hull plate steel of a kind of bainite/martensite/austenite high-ductility according to claim 1-4 any one Manufacture method, it is characterised in that concrete technology step is：(1) sheet billet continuous casting：Prepared by Low Superheat Pouring is taken, the cast degree of superheat is not more than 20 DEG C, takes slighter compress and electromagnetic agitation skill Art；(2) low temperature reheats：Continuous casting billet is subjected to low-temperature heat, heating-up temperature is 1000~1150 DEG C, is incubated 60~180min；(3) recrystallization rolls with the big pressure of non-recrystallization zone two benches：It is big that 2~5 passages are carried out in recrystallization zone temperature range Reduction ratio rolls, start rolling temperature：1000~1150 DEG C, finishing temperature：980~1000 DEG C, roll speed and be not higher than 1.5m/s, every time Drafts is not less than 15%；3~10 passage heavy reduction rate rollings, start rolling temperature are carried out in non-recrystallization zone temperature range：920 ~1000 DEG C, finishing temperature：850~900 DEG C, roll speed and be not higher than 1.5m/s, draught per pass is not less than 10%；Two rank The big pressure rolling overall compression ratio of section is not less than 8, and in the non-recrystallization zone rolling, compression ratio is not less than 3；(4) direct quenching DQ：Steel plate is quickly sent to press quenching machine after terminating and quenched by rolling, and direct quenching temperature is 850~900 DEG C, the type of cooling is water cooling after direct quenching, and water quenching speed control is in 1~2m/min, cooling rate >=20 DEG C/s, steel plate Surface final cooling temperature is not higher than 200 DEG C；(5) two-phase section quenching L：Two-phase section is again heated to the steel plate after direct quenching and carries out secondary quenching, hardening heat is 740~780 DEG C, 60~90min of soaking time, above-mentioned two-phase section refers to austenite/ferrite area；(6) tempering heat treatment：Steel plate after secondary quenching is tempered in heat-treatment furnace, temperature is 500~670 DEG C, 60~120min of tempering time, carry out being air-cooled to room temperature after tempering.
- 6. a kind of manufacture method of the easy laser welding hull plate steel of bainite/martensite/austenite high-ductility according to claim 5, Characterized in that, in the step (3), 3 passage heavy reduction rate rollings, start rolling temperature are carried out in recrystallization zone temperature range： 1120 DEG C, finishing temperature：1000 DEG C, roll speed：1.5m/s, draught per pass：21%；Enter in non-recrystallization zone temperature range The passage heavy reduction rate rolling of row 5, start rolling temperature：950 DEG C, finishing temperature：870 DEG C, roll speed：1.3m/s, draught per pass： 18.7%, compression ratio when the non-recrystallization zone rolls is 5.
- 7. a kind of manufacture method of the easy laser welding hull plate steel of bainite/martensite/austenite high-ductility according to claim 6, Characterized in that, in the step (4), direct quenching temperature：885 DEG C, the cool time：90min.
- 8. a kind of manufacture method of the easy laser welding hull plate steel of bainite/martensite/austenite high-ductility according to claim 7, Characterized in that, in the step (5), the type of cooling is water cooling during secondary quenching；Water quenching speed control is cold in 1~2m/min Speed >=20 DEG C/s, surface of steel plate final cooling temperature are not higher than 200 DEG C.
- 9. a kind of manufacture method of the easy laser welding hull plate steel of bainite/martensite/austenite high-ductility according to claim 8, Characterized in that, in the step (5), hardening heat：760 DEG C, the cool time：120min；In the step (6), tempering temperature Degree：654 DEG C, tempering time：70min.
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| CN108179351A (en) * | 2018-01-23 | 2018-06-19 | 东北大学 | A kind of cupric low carbon high-strength high-ductility offshore platform steel and preparation method thereof |
| CN112680667B (en) * | 2020-12-17 | 2021-09-21 | 南京工程学院 | Ship and maritime work profile steel and preparation method and application thereof |
| CN113151650A (en) * | 2021-04-10 | 2021-07-23 | 河南科技大学 | Heat treatment process for low alloy steel |
| CN115198175B (en) * | 2022-06-17 | 2023-04-07 | 鞍钢集团北京研究院有限公司 | 960MPa grade ultra-high strength steel plate with marine organism adhesion resistance and manufacturing method thereof |
| CN115717220B (en) * | 2022-11-29 | 2024-03-08 | 钢铁研究总院有限公司 | 590 MPa-grade polar region ship body structural steel with low-temperature toughness and preparation method thereof |
| CN116377348B (en) * | 2023-03-27 | 2024-02-13 | 鞍钢股份有限公司 | Cu-containing low-alloy high-strength steel with yield strength of 1000MPa and manufacturing method thereof |
| CN118979196B (en) * | 2024-10-22 | 2025-02-18 | 钢铁研究总院有限公司 | High-strength and high-toughness easily-welded flat-bulb steel and preparation method thereof |
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