CN106756612A - 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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- CN106756612A CN106756612A CN201611116358.6A CN201611116358A CN106756612A CN 106756612 A CN106756612 A CN 106756612A CN 201611116358 A CN201611116358 A CN 201611116358A CN 106756612 A CN106756612 A CN 106756612A
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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
- C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
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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
- 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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- 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
- C21D8/0247—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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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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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
-
- 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
-
- 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
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%, balance of Fe and inevitable impurity.The manufacture method of Ultra-low carbon ship steel is：Sheet billet continuous casting, low temperature are reheated, recrystallize pressure rolling big with non-recrystallization zone two benches, direct quenching DQ, coexistence region quenching 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 the characteristics of having production efficiency high, low production cost, process 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
Low-temperature flexibility higher, the especially stability requirement to the low-temperature flexibility in slab section are higher.
Conventional hulls structural steel is usually that Ni-Cr-Mo-V is used 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 because such steel carbon content is higher, the low-temperature flexibility not only to steel is very unfavorable, 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
Occur 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, needs to be preheated under higher temperature during welding, seriously constrains welding process.In recent years, to reduce manufacturing cost, while can again
Further improve the obdurability and weldability of ship steel, people devise the ageing strengthening containing Cu of a kind of low-carbon (LC) or Ultra-low carbon
Steel, this steel mainly reduces cost of alloy by reducing the noble element such as Ni, Cr, Mo content, is 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 with Cu simple substance particulate forms in ag(e)ing process, is made up so as to play certain precipitation enhancement
The loss of strength that carbon drop brings.
Conventional hulls structural steel, whether low-carbon (LC) (carbon content~0.20wt.%), the Ni-Cr-Mo-V systems alloying of early stage
Then steel, the low-carbon (LC) still developed in recent years or the Ultra-low carbon steel of ageing strengthening containing Cu is generally used after rolling using reheating
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 the effective particle size refinement after it can make phase transformation behind recrystallization zone and non-recrystallization zone two-phase control rolling
So as to be conducive to improving the obdurability of steel.Patent of invention such as Publication No. CN1651589A is prepared for one kind using the technique of QT
High strength weldable ageing hardening steel, but steel described in the 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.The patent of invention of Publication No. CN102021489A and CN104073731A describes one
The ultra high strength structural ship steel manufactured by DQT techniques is planted, 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 low stress damage.This requires that steel have enough toughness to store up in plastic failure
It is standby, particularly require that there is low-temperature flexibility higher 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 after phase transformation bainite/martensite substructure to reduce ductile-brittle transition temperature.Additionally, 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 of most of easy welding 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.Additionally, hull is used
Steel, offshore platform steel thickness specification are more, and slab in thickness direction there is Section Effect, the i.e. thickness direction in slab to occur
The phenomenon of unstable properties, particularly low-temperature flexibility it is unstable, have a strong impact on the overall performance of steel plate.
The present invention is to solve the above problems, there is provided a kind of easy laser welding hull plate steel of bainite/martensite/austenite high-ductility and
Manufacture method, meets 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, is rolled, Technology for Heating Processing by steel plate, is solved conventional hulls, ocean platform, petroleum pipeline steel and is faced
The problem that low-temperature flexibility is not enough, 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%, balance of Fe and inevitable
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%, balance of 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%, balance of 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 increases tough to steel low temperature in steel
Property and weldability are very unfavorable.Therefore designed using Ultra-low carbon in the present invention, C content is controlled in 0.02~0.06wt.%.
Cu：The crucial precipitation strength element of steel of the present invention, Cu is independent of by C, N element in steel in temper aging process
In separated out so as to produce significantly precipitation strength to act in nanocluster form, can make up reduces C and the loss of strength that causes, together
When Cu can also improve the sea water corrosion resistant of steel.To ensure that steel has certain intensity, the content control of Cu exists in the present invention
1.00~2.00wt.%.
Ni：Ni and Cu forms complex precipitates in ag(e)ing process, and Ni can promote the Precipitation Kinetics of Cu, in ag(e)ing process
The roughening of richness Cu phases can be suppressed, so that Reinforced Cu precipitating reinforcing effect.Additionally, quenching degree and low temperature that Ni can also improve steel are tough
Property, while having certain solution strengthening effect, moreover it is possible to prevent the hot-short effect of Cu, significantly improve the surface fire check containing Cu steel
Tendency.In view of the financial cost of steel, the control of Ni contents is in 1.50~3.00wt.% in the present invention.
Mo：Solid solution Mo can significantly improve the quenching degree of steel, also with certain solution strengthening effect, while Mo can be improved
Temper resistance, significantly reduces 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 having certain solution strengthening effect, A can be also reducedc3Temperature, makes
Obtain wider in the temperature window of non-recrystallization zone rolling, but during Mn too high levels, the corrosion resisting property reduction of steel, 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, steel matrix is present in solution
In, with certain solution strengthening effect, but the silicon of excess is unfavorable to the low-temperature flexibility of steel, the welding cold cracking of steel, fire check
Sensitiveness will increase, and Si contents of the present invention are controlled to 0.20~0.50wt.%.
Nb：The Nb of solid solution can improve the quenching degree of steel during high temperature soak, and deformation-induced precipitation Nb can suppress deformation Ovshinsky
The recrystallization of body so that when non-recrystallization zone is rolled, 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, austenite crystal during prevention soaking with N in steel
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, there is the work of the aged brittleness and crystal grain thinning that prevent steel
With.Al content control is in 0.010~0.050wt.% in the present invention.
P and S：Impurity element in steel, to the performance of steel, especially low-temperature flexibility is very unfavorable, to its content in steel of the present invention
Should strictly 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%, Martensite Volume Fraction in the microstructure of ship steel
It is 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 is：
(1) sheet billet continuous casting：Prepared by Low Superheat Pouring, the cast degree of superheat is not more than 20 DEG C, takes slighter compress and electromagnetic agitation skill
Art, to reduce steel plate center portion degree of segregation；
(2) low temperature is reheated：Continuous casting billet is carried out into 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) pressure rolling big with non-recrystallization zone two benches is recrystallized：2~5 roads 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, allow its center portion also most
Big degree ground is recrystallized, and the segregation of element is eliminated to a certain extent, and control is rolled speed and is not higher than 1.5m/s, draught per pass
It is 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；Roll the austenite pattern of rear steel plate 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 that
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 and is quenched by rolling after terminating, direct quenching temperature
It is 850~920 DEG C to spend, and 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 carried out immediately after being heated to two-phase section
Secondary quenching, hardening heat is 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 carries 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 forming a certain amount of adverse transformation austenite between bainite/martensite lath, can prevent crackle
Propagate 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
Inside carry out 5 passes, 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, cool time：90min.
Further, in step (5), the type of cooling is water-cooled during secondary quenching；Water quenching speed control in 1~2m/min,
Cooling rate >=20 DEG C/s, surface of steel plate final cooling temperature is not higher than 200 DEG C.
Further, in step (5), hardening heat：760 DEG C, 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 is relatively stable.
(3) compared with traditional processing technology, production technology of the invention is ensureing that it is excellent high-strength that low-carbon (LC) ship steel has
The matching of high-ductility, also with low-temperature impact fracture fibre ratio higher so that brittle failure is difficult 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.
Specific embodiment
The preferred embodiments of the present invention are specifically described below in conjunction with the accompanying drawings, wherein, accompanying drawing constitutes the application part, and
It is used to explain principle of the invention together with embodiments of the present invention.
Table 1 is the chemical composition of steel in the embodiment in the present invention, and 3 stoves are smelted 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 embodiment in the present invention with the specific rolling process of steel in comparative example.
Table 3 is the embodiment in the present invention and Heat-Treatment of Steel technical process in comparative example, is specifically shown in Table 3.
Table 4 is the embodiment in the present invention and the mechanical property of different-thickness gauge steel in comparative example, is specifically shown in Table 4.
The specific rolling process of steel in embodiment and comparative example in the present invention of table 2
Embodiment in the present invention of table 3 and Heat-Treatment of Steel technique in comparative example
The mechanical property of different-thickness gauge steel in embodiment and comparative example in the present invention of table 4
The above, the only present invention preferably specific embodiment, but protection scope of the present invention is not limited thereto,
Any one skilled in the art the invention discloses technical scope in, the change or replacement that can be readily occurred in,
Should all be included within the scope of the present invention.
Claims (10)
1. a kind of 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%, balance of 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。
2. the easy laser welding hull plate steel of a kind 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%, balance of Fe and inevitable impurity；The ship steel meets welding crack sensibility and refers to
Number：Pcm=C+Si/30+Ni/60+ (Mn+Cr+Cu)/20+Mo/15+V/10+5B≤0.25.
3. the easy laser welding hull plate steel of a kind of bainite/martensite/austenite high-ductility according to claim 2, 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%, balance of Fe and inevitable impurity；The ship steel meets welding crack sensibility and refers to
Number：Pcm=C+Si/30+Ni/60+ (Mn+Cr+Cu)/20+Mo/15+V/10+5B≤0.32.
4. the easy laser welding hull plate steel of a kind of bainite/martensite/austenite high-ductility according to claim 3, it is characterised in that
The microstructure of the ship steel is mainly made up of bainite, martensite, austenite, wherein bainite volume fraction be 70%~
90%, Martensite Volume Fraction is 10%~20%, and austenite volume fraction is 4%~10%；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 4, 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%.
6. the easy laser welding hull plate steel of a kind of bainite/martensite/austenite high-ductility according to claim 1-5 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 is reheated：Continuous casting billet is carried out into low-temperature heat, heating-up temperature is 1000~1150 DEG C, is incubated 60~180min；
(3) pressure rolling big with non-recrystallization zone two benches is recrystallized：2~5 passages are carried out in recrystallization zone temperature range big
Reduction ratio is rolled, 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 when the non-recrystallization zone is rolled, compression ratio is not less than 3；
(4) direct quenching DQ：Steel plate is quickly sent to press quenching machine and is quenched by rolling after terminating, and direct quenching temperature is
850~900 DEG C, the type of cooling is water-cooled 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：Being again heated to two-phase section to the steel plate after direct quenching carries out secondary quenching, and 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 carries out being air cooled to room temperature after tempering.
7. the manufacture method of the easy laser welding hull plate steel of a kind of bainite/martensite/austenite high-ductility according to claim 6,
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：1102 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 is rolled is 5.
8. the manufacture method of the easy laser welding hull plate steel of a kind of bainite/martensite/austenite high-ductility according to claim 7,
Characterized in that, in the step (4), direct quenching temperature：885 DEG C, cool time：90min.
9. the manufacture method of the easy laser welding hull plate steel of a kind of bainite/martensite/austenite high-ductility according to claim 8,
Characterized in that, in the step (5), the type of cooling is water-cooled 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 is not higher than 200 DEG C.
10. the manufacture method of the easy laser welding hull plate steel of a kind of bainite/martensite/austenite high-ductility according to claim 9,
Characterized in that, in the step (5), hardening heat：760 DEG C, cool time：120min；In the step (6), tempering temperature
Degree：654 DEG C, tempering time：70min.
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