CN107130191B - A kind of air-cooled dual phase steel of ferrite and bainite plate of low yield strength ratio and its production method - Google Patents
A kind of air-cooled dual phase steel of ferrite and bainite plate of low yield strength ratio and its production method Download PDFInfo
- Publication number
- CN107130191B CN107130191B CN201710196297.7A CN201710196297A CN107130191B CN 107130191 B CN107130191 B CN 107130191B CN 201710196297 A CN201710196297 A CN 201710196297A CN 107130191 B CN107130191 B CN 107130191B
- Authority
- CN
- China
- Prior art keywords
- steel plate
- ferrite
- steel
- plate
- air
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Active
Links
Classifications
-
- 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
- C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
-
- 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
-
- 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
-
- 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
-
- 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
-
- 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
-
- 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
-
- 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
- C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
-
- 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
- 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
-
- 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
-
- 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
- C21D2211/005—Ferrite
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Heat Treatment Of Steel (AREA)
Abstract
The present invention provides a kind of air-cooled dual phase steel of ferrite and bainite plate of low yield strength ratio and its production methods, the chemical component of steel plate includes: C 0.04%~0.10% by weight percentage, Si 0.18%~0.25%, Mn 1.06%~2.02%, Cr 0.12%~0.40%, Ni 0.20%~0.68%, Mo 0.10%~0.37%, Cu≤0.28%, Nb 0.009%~0.046%, V≤0.041%, Ti 0.001%~0.03%, Alt 0.0216%~0.0319%, P≤0.0104%, S≤0.0075%, and 1.71%≤Mn+Mo+Cr≤2.74%, 0.035% ≤ Nb+V+Ti≤0.097%, Ni/Cu >=2.4, remaining is Fe and inevitable impurity.The production method of steel plate is rolled using two-stage control, and uses lower finishing temperature, and less finish rolling drafts reduces the yield tensile ratio of steel plate with pressure passage, and rolling rear air-cooled obtained tissue is ferrite+bainite duplex structure.The present invention not only simple production process, at low cost, lumber recovery is high, but also produce steel plate have excellent welding performance, welding cold cracking sensitivity coefficient Pcm≤ 0.20, application prospect is very wide.
Description
Technical field
The invention belongs to low-alloy high-strength steel manufacturing fields, are related to a kind of air-cooled dual phase steel of ferrite and bainite of low yield strength ratio
Plate and its production method.
Background technique
Recently as the continuous development of high-strength steel, for obtaining the steel plate with low yield strength ratio security performance, increasingly
It is important.Simultaneously for the steel plate of thin gauge, using rear water cooling is rolled often caused by steel plate template is poor, performance is unstable.Therefore,
Develop one that there is the steel plate that low yield strength ratio is high-intensitive and template is preferable, performance is stable to have become iron and steel enterprise's primary study
Direction.
Had a large amount of patents in relation to low yield strength ratio high-strength steel at present, chemically the characteristics of ingredient from the point of view of, patent
CN103981452A discloses a kind of economical air-cooled two-phase low yield strength ratio steel plate and its production technology, using high Si-Mn-Cr at
Fission system, although alloying component is simple and does not add microalloy element Nb, V, Ti and compared with noble element Mo etc., shortcoming is
The yield strength R of finished steel platep0.2Maximum value only has 440MPa, and elongation percentage lower limit value is lower.Mo adds in patent JP2077523A
Dosage is larger (0.4%~0.7%), because Mo is noble element, causes that the production cost increases.The range of microalloy element compared with
Width, the mass percent as shared by Ti, V is 0.005%~0.10%, but the low strength of steel plate, only 235MPa~440MPa,
And yield tensile ratio≤0.80 is higher.Patent JP11021622A discloses a kind of low yield ratio weathering resistant steel plate and its manufacturing method, chemistry
The design of the ingredient of ingredient and this patent is closest, is disadvantageous in that steel plate yield strength and tensile strength obtained are inclined
It is low, and yield tensile ratio≤0.80 is higher.From the point of view of production technology characteristic, the development or production of most low yield strength ratio high-strength steel are all
Using online water cooling or multiple water cooling, such as CN101545079A, CN101775552A, CN101775561A, CN1524976A
Deng, disadvantage is that the cooling device after rolling increases production cost, and biggish cooling rate can tissue to steel plate it is equal
Even property causes large effect, poor so as to cause the stability of plate property, water steel plate template difficulty control after cooling, serious to go back
Straightener leveling is needed, cost is increased.There are also some patents to use heat-treated offline process, high-strength to obtain low yield strength ratio
The purpose of steel, such as CN1786246A, CN10132856A, CN101613828A, CN101111621A, CN102011068A etc., no
Foot place is that increasing heat treatment procedure makes the production cycle elongated, and the production cost increases, and production efficiency is low.
Summary of the invention
The purpose of the present invention is to provide a kind of air-cooled dual phase steel of ferrite and bainite plate of low yield strength ratio and its production method,
By the rational design to alloying component, 1.71%≤Mn+Mo+Cr≤2.74% is controlled, 0.035%≤Nb+V+Ti≤
0.097%, Ni/Cu >=2.4,14.9≤Mn/C≤50.5 using two-phase control rolling, and use lower finishing temperature, compared with
Few finish rolling drafts reduces the yield tensile ratio of steel plate with pressure passage, and rolling rear air-cooled obtained tissue is ferrite+bainite
Duplex structure.
For achieving the above object, the present invention adopts the following technical scheme:
A kind of chemical component of the air-cooled dual phase steel of ferrite and bainite plate of low yield strength ratio includes: C by weight percentage
0.04%~0.10%, Si 0.18%~0.25%, Mn 1.06%~2.02%, Cr 0.12%~0.40%, Ni
0.20%~0.68%, Mo 0.10%~0.37%, Cu≤0.28%, Nb 0.009%~0.046%, V≤0.041%, Ti
0.001%~0.03%, Alt 0.0216%~0.0319%, P≤0.0104%, S≤0.0075%, and 1.71%≤Mn+
Mo+Cr≤2.74%, 0.035%≤Nb+V+Ti≤0.097%, Ni/Cu >=2.4,14.9≤Mn/C≤50.5, remaining is Fe
And inevitable impurity.
Below the effect to contained component in air-cooled low yield strength ratio high-strength ferritic bainite steel plate of the invention and its
The selection concrete analysis of dosage is as follows:
C:C is the most frequently used, most cheap alloying element, on the one hand C has the work for expanding austenite phase field, stable austenite
With on the other hand a small amount of C is remarkably improved the intensity of steel.But with the raising of C content, the low-temperature impact toughness of steel, weldability
Energy and anti-lamellar tearing penalty.Therefore the content of C is selected 0.04%~0.10% in the present invention.
Si:Si is common and cheap alloying element, there is solution strengthening, moreover it is possible to pearlitic transformation is postponed, it is right
Strength enhancing is advantageous.But Si too high levels can have larger impact to continuous casting, while the ductile-brittle transition temperature of steel can be made to increase.
Therefore the content of Si is selected 0.18%~0.25% in the present invention.
The typical among the austenite stabilizing elements of Mn:Mn promote bainitic transformation, play the role of solution strengthening, steel can be improved
Harden ability, and the influence to the yield tensile ratio of steel is smaller, and high Mn content is mentioned under conditions of low C has significant work to the intensity of steel
With.But Mn content can excessively make continuous casting process difficulty control, and Mn is easy to the elements such as P, S and forms segregation, deteriorate impact flexibility and
Welding performance.The content of Mn is selected 1.06%~2.02% in the present invention.
Al:Al is one of effective deoxidant element, and nitride can be formed with microalloy element to refine crystal grain, originally
The content of Al is selected 0.0216%~0.0319% in invention.
P, S: being the harmful element in steel, content height can deteriorate the toughness plasticity and welding performance of steel, so reducing to the greatest extent
P, S content in steel, therefore in P≤0.0104%, the content of S is controlled in S≤0.0075% for the content control of P in the present invention.
Nb:Nb is strong carbonitride-forming elements, and addition Nb is recrystallized after preventing austenite deformation in steel, improves Ovshinsky
The non-recrystallization temperature of body, Nb can also inhibit ferritic transformation, refine crystal grain.The content selection of Nb exists in the present invention
0.009%~0.046%.
V:V mainly plays precipitation strength in steel, can hinder Austenite Grain Growth, fining austenite grains；In phase
VC precipitate can be used as the core of ferrite forming core during change, increase nucleation rate；After VC precipitate can also hinder phase transformation
Ferrite crystal grain is grown up, to refine crystal grain after phase transformation.The content of V is selected in V≤0.041% in the present invention.
Main function of the Ti:Ti in steel is solid N, complete deoxidation and forms carbonitride, there is refinement crystal grain and be precipitated strong
The effect of change can also improve intensity, improve low-temperature impact toughness, but excessive Ti content will cause the toughness decline of steel, and
It is unfavorable to the yield tensile ratio for reducing steel plate.Therefore the content of Ti is controlled 0.001%~0.03% in the present invention.
Mo:Mo can significantly improve the intensity of steel, harden ability of the steel plate in process air cooler be improved, to fine bainite
It is formed with facilitation.But too high levels can be unfavorable to welding performance.In the present invention content control of Mo 0.10%~
0.37%.
Cr:Cr important alloying element, but CCT curve moves to right, and promotes bainitic transformation, plays solution strengthening effect, Cr
There is smaller segregation to be inclined to compared with Mn, but Cr too high levels, for the toughness for reducing steel, increases welding crack sensibility.Therefore it is of the invention
The content of middle Cr is controlled 0.12%~0.40%.
Solid solubility of the Cu:Cu in steel is little, does not form carbide with C, usually exists with tiny precipitation particles state
Yu Gangzhong plays the role of precipitation strength, and the intensity of steel can be improved.But Cu too high levels will cause steel billet and heat or roll
It is cracked in the process, therefore the content of Cu is controlled in Cu in the present invention :≤0.28%.
Ni:Ni can improve the low-temperature impact toughness and welding heat affected zone impact flexibility of steel, while can also improve steel
Intensity, therefore in the present invention Ni content control 0.20%~0.68%.
The production method of the high-intensitive air-cooled dual phase steel of ferrite and bainite plate of above-mentioned low yield strength ratio includes the chemistry by steel plate
Composition by weight percent is smelted in vaccum sensitive stove, and is cast into blank, then carries out roughing, cold rolling and cooling,
In:
(1) slab is heated before rolling starts, heating temperature is 1180 DEG C~1200 DEG C；
(2) use two-phase control rolling, roughing start temperature be 1020 DEG C~1050 DEG C, roughing end temp be 960 DEG C~
990 DEG C, roughing overall reduction is 60%~75%, is 1.3~1.6 to warm coefficient t then to temperature；Entrance finishing temperature is 800
DEG C~820 DEG C, it is 770 DEG C~800 DEG C that finish rolling, which terminates temperature, and finish rolling overall reduction is 25%~40%；
(3) steel plate, which rolls, is placed on cold bed and is air-cooled to room temperature.
Further, the steel of the production method production of the high-intensitive air-cooled dual phase steel of ferrite and bainite plate of the low yield strength ratio
The tissue of plate is ferrite+bainite duplex structure, plate thickness≤15mm.
Further, the steel of the production method production of the high-intensitive air-cooled dual phase steel of ferrite and bainite plate of the low yield strength ratio
The yield strength R of platep0.2420MPa~550MPa, tensile strength Rm>=640MPa, elongation after fracture >=20%, yield tensile ratio
(Rp0.2/Rm)≤0.70, welding cold cracking sensitivity coefficient Pcm=C+Si/30+Mn/20+Cu/20+Ni/60+Cr/20+Mo/15+
V/10+5B≤0.20。
In production technology of the present invention, finish rolling uses 800 DEG C~820 DEG C of lower start rolling temperature, lower finish rolling overall reduction
25%~40% and lesser to warm coefficient 1.3~1.6, it is because lower final rolling temperature can make microalloy element in steel plate
Precipitating reinforcing effect enhancing, increases the nucleation point of phase transformation, refines crystal grain；It lower overall reduction and lesser can be shown to warm coefficient
The yield tensile ratio and toughness for improving steel plate are write, while advantageous to the control of template, moreover it is possible to reduce milling train zerolling load.
Compared with prior art, the present invention at least has the following beneficial effects:
1. being by being adequately precipitated using lower final rolling temperature, lesser drafts and to warm coefficient in the present invention
The lesser drafts of invigoration effect cooperation, mill load when obtaining the purpose of high-strength low-yield ratio, while reducing zerolling,
Improve productivity.
2. the present invention does not need to roll rear water cooling plant, it is double air-cooled need to only to can be prepared by a kind of low yield strength ratio ferrite-bainite
Phase steel plate can save water cooling plant cost, and with short production cycle, concise in technology, and the template of air-cooled rear steel plate is excellent, tissue
Uniformly, high production efficiency.
3. the present invention is by reasonable ingredient and design, under the premise of low C, 1.71%≤Mn+Mo+Cr of control≤
Bainitic transformation occurs in 2.74% certifiable steel plate process air cooler, control 0.035%≤Nb+V+Ti≤0.097% can guarantee
Roll the existing higher intensity of rear air-cooled steel plate, but will not because being precipitated toughness that is excessive and deteriorating steel plate, control Ni/Cu >=
2.4, which can effectively reduce element Cu, gives steel plate bring crackle hidden danger, using control bundle+air-cooled technique, can get yield tensile ratio Rp0.2/Rm
≤ 0.70, yield strength Rp0.2420MPa~550MPa, tensile strength Rm>=640MPa, the ferrite of elongation after fracture >=20%
Bainite steel plate.
Detailed description of the invention
The microstructure picture that Fig. 1 is 200 times at 1 light plate longitudinal section 1/4 of embodiment；
The microstructure picture that Fig. 2 is 200 times at 2 light plate longitudinal section 1/4 of embodiment；
The microstructure picture that Fig. 3 is 200 times at 3 light plate longitudinal section 1/4 of embodiment.
Specific embodiment
Technical solution of the present invention is described in further detail with reference to the accompanying drawings and embodiments, but not limited to this.
Embodiment 1
The chemical component of steel plate includes: C 0.04%, Si 0.25%, Mn 2.02%, Cr by weight percentage
0.30%, Ni 0.41%, Mo 0.37%, Cu 0.02%, Nb 0.046%, V 0.021%, Ti 0.029%, Alt
0.0319%, P 0.0104%, S 0.0024%, Pcm=0.20, and Mn+Mo+Cr=2.69%, Nb+V+Ti=0.096%,
Ni/Cu=20.5, Mn/C=50.5, remaining is Fe and inevitable impurity.
The production method of above-mentioned steel plate includes that smelting is carried out in vaccum sensitive stove by the chemical component weight percentage of steel plate
Refining, and it is cast into blank, then carry out roughing, cold rolling and cooling.Wherein:
1) slab is heated before rolling starts, heating temperature is 1185 DEG C；
2) use two-phase control rolling, 1025 DEG C of roughing start temperature, 980 DEG C of roughing end temp, roughing overall reduction
62.5%, then to temperature, to warm coefficient 1.6；800 DEG C of entrance finishing temperature, finish rolling terminates 770 DEG C of temperature, finish rolling overall reduction
37.5%, it rolls and is placed on cold bed and is air-cooled to room temperature.
The steel plate plate thickness of production is 15mm, and 200 times of microstructure picture is as shown in Figure 1, steel plate at steel plate longitudinal section 1/4
Tissue be ferrite+bainite duplex structure.The mechanical property of steel plate such as table 1.
Embodiment 2
The chemical component of steel plate includes: C 0.06%, Si 0.21%, Mn 1.06%, Cr by weight percentage
0.40%, Ni 0.68%, Mo 0.22%, Cu 0.28%, Nb 0.021%, V 0.001%, Ti 0.013%, Alt
0.0273%, P 0.0066%, S 0.0075%, Pcm=0.18, and Mn+Mo+Cr=1.68%, Nb+V+Ti=0.035%,
Ni/Cu=2.4, Mn/C=17.67, remaining is Fe and inevitable impurity.
The production method of above-mentioned steel plate includes that smelting is carried out in vaccum sensitive stove by the chemical component weight percentage of steel plate
Refining, and it is cast into blank, then carry out roughing, cold rolling and cooling.Wherein:
1) slab is heated before rolling starts, heating temperature is 1190 DEG C；
2) use two-phase control rolling, 1030 DEG C of roughing start temperature, 970 DEG C of roughing end temp, roughing overall reduction
75%, then to temperature, to warm coefficient 1.3；810 DEG C of entrance finishing temperature, finish rolling terminates 790 DEG C of temperature, finish rolling overall reduction
25%, it rolls and is placed on cold bed and is air-cooled to room temperature.
The steel plate plate thickness of production is 18mm, and 200 times of microstructure picture is as shown in Fig. 2, steel plate at steel plate longitudinal section 1/4
Tissue be ferrite+bainite duplex structure.The mechanical property of steel plate such as table 1.
Embodiment 3
The chemical component of steel plate includes: C 0.10%, Si 0.18%, Mn 1.49%, Cr by weight percentage
0.12%, Ni 0.20%, Mo 0.10%, Cu 0.01%, Nb 0.009%, V 0.041%, Ti 0.001%, Alt
0.0216%, P 0.0077%, S 0.0022%, Pcm=0.20, and Mn+Mo+Cr=1.71%, Nb+V+Ti=0.051%,
Ni/Cu=20, Mn/C=14.9, remaining is Fe and inevitable impurity.
The production method of above-mentioned steel plate includes that smelting is carried out in vaccum sensitive stove by the chemical component weight percentage of steel plate
Refining, and it is cast into blank, then carry out roughing, cold rolling and cooling.Wherein:
1) slab is heated before rolling starts, slab is heated, heating temperature is 1200 DEG C；
2) use two-phase control rolling, 1040 DEG C of roughing start temperature, 990 DEG C of roughing end temp, roughing overall reduction
66.7%, then to temperature, to warm coefficient 1.5；820 DEG C of entrance finishing temperature, finish rolling terminates 800 DEG C of temperature, finish rolling overall reduction
33.3%, it rolls and is placed on cold bed and is air-cooled to room temperature.
The steel plate plate thickness of production is 12mm, and 200 times of microstructure picture is as shown in figure 3, steel plate at steel plate longitudinal section 1/4
Tissue be ferrite+bainite duplex structure.The mechanical property of steel plate such as table 1.
The mechanical property of 1 1-3 light plate of the embodiment of the present invention of table
Although the open section Example of the present invention, is not for limiting the present invention.The present invention can also have other more
Kind embodiment, those skilled in the art can be made into various corresponding changes according to the present invention, but these corresponding changes are all answered
Belong to the protection scope of appended claims of the present invention.
Claims (4)
1. a kind of air-cooled dual phase steel of ferrite and bainite plate of low yield strength ratio, which is characterized in that the chemical component of steel plate is with weight hundred
Point than meter include: C 0.04%~0.10%, Si 0.18%~0.25%, Mn 1.06%~2.02%, Cr 0.12%~
0.40%, Ni 0.20%~0.68%, Mo 0.10%~0.37%, Cu≤0.28%, Nb 0.009%~0.046%, V≤
0.041%, Ti 0.001%~0.03%, Alt 0.0216%~0.0319%, P≤0.0104%, S≤0.0075%, and
1.71%≤Mn+Mo+Cr≤2.74%, 0.035%≤Nb+V+Ti≤0.097%, Ni/Cu >=2.4,14.9≤Mn/C≤
50.5, remaining is Fe and inevitable impurity.
2. a kind of production method of the air-cooled dual phase steel of ferrite and bainite plate of low yield strength ratio, which is characterized in that the producer of steel plate
Method includes being smelted in vaccum sensitive stove by the chemical component weight percentage of steel plate, and the chemical component of steel plate is with weight hundred
Point than meter include: C 0.04%~0.10%, Si 0.18%~0.25%, Mn 1.06%~2.02%, Cr 0.12%~
0.40%, Ni 0.20%~0.68%, Mo 0.10%~0.37%, Cu≤0.28%, Nb 0.009%~0.046%, V≤
0.041%, Ti 0.001%~0.03%, Alt 0.0216%~0.0319%, P≤0.0104%, S≤0.0075%, and
1.71%≤Mn+Mo+Cr≤2.74%, 0.035%≤Nb+V+Ti≤0.097%, Ni/Cu >=2.4,14.9≤Mn/C≤
50.5, remaining is Fe and inevitable impurity, and is cast into blank, then carries out roughing, cold rolling and cooling, in which:
(1) slab is heated before rolling starts, heating temperature is 1180 DEG C~1200 DEG C；
(2) two-phase control rolling is used, roughing start temperature is 1020 DEG C~1050 DEG C, and roughing end temp is 960 DEG C~990
DEG C, roughing overall reduction is 60%~75%, is 1.3~1.6 to warm coefficient t then to temperature；Entrance finishing temperature is 800 DEG C
~820 DEG C, it is 770 DEG C~800 DEG C that finish rolling, which terminates temperature, and finish rolling overall reduction is 25%~40%；
(3) steel plate, which rolls, is placed on cold bed and is air-cooled to room temperature.
3. the production method of the air-cooled dual phase steel of ferrite and bainite plate of low yield strength ratio according to claim 2, feature exist
In the tissue of the steel plate of the production method production is ferrite+bainite duplex structure, plate thickness≤15mm.
4. the production method of the air-cooled dual phase steel of ferrite and bainite plate of low yield strength ratio according to claim 2, feature exist
In the yield strength R of the steel plate of the production method productionp0.2420MPa~550MPa, tensile strength Rm>=640MPa breaks
Elongation >=20% afterwards, yield tensile ratio (Rp0.2/Rm)≤0.70, welding cold cracking sensitivity coefficient Pcm≤0.20。
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201710196297.7A CN107130191B (en) | 2017-03-29 | 2017-03-29 | A kind of air-cooled dual phase steel of ferrite and bainite plate of low yield strength ratio and its production method |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201710196297.7A CN107130191B (en) | 2017-03-29 | 2017-03-29 | A kind of air-cooled dual phase steel of ferrite and bainite plate of low yield strength ratio and its production method |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN107130191A CN107130191A (en) | 2017-09-05 |
| CN107130191B true CN107130191B (en) | 2019-05-31 |
Family
ID=59721480
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201710196297.7A Active CN107130191B (en) | 2017-03-29 | 2017-03-29 | A kind of air-cooled dual phase steel of ferrite and bainite plate of low yield strength ratio and its production method |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN107130191B (en) |
Families Citing this family (9)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN109628840B (en) * | 2019-02-12 | 2020-03-31 | 鞍钢股份有限公司 | 550 MPa-grade cold-rolled corrosion-resistant dual-phase steel and manufacturing method thereof |
| CN109576591B (en) * | 2019-02-12 | 2020-03-31 | 鞍钢股份有限公司 | 700 MPa-grade cold-rolled corrosion-resistant dual-phase steel and manufacturing method thereof |
| CN111979481B (en) * | 2020-07-23 | 2021-08-24 | 张家港宏昌钢板有限公司 | Thin-gauge low-yield-ratio high-strength bridge steel and production method thereof |
| CN112322995B (en) * | 2020-11-11 | 2022-01-14 | 江苏省沙钢钢铁研究院有限公司 | Low-yield-ratio high-toughness TMCP (thermal mechanical control processing) type bridge steel plate and production method thereof |
| CN112921242B (en) * | 2021-01-25 | 2022-03-04 | 广西柳钢华创科技研发有限公司 | Q460 grade building steel with low yield ratio and high toughness under air cooling |
| CN114686765B (en) * | 2022-03-31 | 2023-03-03 | 鞍钢股份有限公司 | 420 MPa-grade high-toughness extra-thick plate and manufacturing method thereof |
| CN115233102B (en) * | 2022-07-26 | 2023-05-26 | 张家港宏昌钢板有限公司 | Low-yield-ratio high-strength steel plate and production method thereof |
| CN115652055B (en) * | 2022-12-14 | 2023-03-28 | 江苏省沙钢钢铁研究院有限公司 | Hot-rolled steel plate and production method thereof |
| CN116005078A (en) * | 2023-01-14 | 2023-04-25 | 重庆大学 | Manufacturing method of lamellar heterogeneous structure high-strength steel |
Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101619423A (en) * | 2008-06-30 | 2010-01-06 | 鞍钢股份有限公司 | Steel plate for high-strength high-toughness low-yield easily-welding structure and method for manufacturing same |
| CN101660099A (en) * | 2009-10-16 | 2010-03-03 | 江苏省沙钢钢铁研究院有限公司 | High strength low alloy hot rolling ferrite bainite weathering resistant steel and production method thereof |
| CN101775561A (en) * | 2010-03-19 | 2010-07-14 | 江苏省沙钢钢铁研究院有限公司 | Low-yield-ratio and high strength thick plate and preparation process thereof |
| CN102912250A (en) * | 2012-10-23 | 2013-02-06 | 鞍钢股份有限公司 | Economical low-yield-ratio steel for pipe fittings for oil and gas transmission and method for producing economical low-yield-ratio steel |
-
2017
- 2017-03-29 CN CN201710196297.7A patent/CN107130191B/en active Active
Patent Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101619423A (en) * | 2008-06-30 | 2010-01-06 | 鞍钢股份有限公司 | Steel plate for high-strength high-toughness low-yield easily-welding structure and method for manufacturing same |
| CN101660099A (en) * | 2009-10-16 | 2010-03-03 | 江苏省沙钢钢铁研究院有限公司 | High strength low alloy hot rolling ferrite bainite weathering resistant steel and production method thereof |
| CN101775561A (en) * | 2010-03-19 | 2010-07-14 | 江苏省沙钢钢铁研究院有限公司 | Low-yield-ratio and high strength thick plate and preparation process thereof |
| CN102912250A (en) * | 2012-10-23 | 2013-02-06 | 鞍钢股份有限公司 | Economical low-yield-ratio steel for pipe fittings for oil and gas transmission and method for producing economical low-yield-ratio steel |
Also Published As
| Publication number | Publication date |
|---|---|
| CN107130191A (en) | 2017-09-05 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN107130191B (en) | A kind of air-cooled dual phase steel of ferrite and bainite plate of low yield strength ratio and its production method | |
| CN108486466B (en) | A kind of yield strength 550MPa grade high ductility weather-resistant steel plate and preparation method thereof | |
| CN101613828B (en) | Super-thick steel plate for low yield ratio buildings with 460 MPa grade yield strength and manufacturing method | |
| CN103014554B (en) | Low-yield-ratio high-tenacity steel plate and manufacture method thereof | |
| CN106811698B (en) | A kind of high strength steel plate and its manufacture method based on tissue precise controlling | |
| CN106282831B (en) | A kind of high-strength container weather resisting steel and its manufacturing method | |
| CN106319390B (en) | A kind of X70 large-deformation-resistance pipeline steels and manufacture method | |
| CN103422025B (en) | The low yield strength ratio structural steel of yield strength >=690MPa and production method thereof | |
| CN103422021B (en) | Low-yield-ratio structural steel with yield ratio equal to or larger than 550MPa and manufacturing method thereof | |
| CN107779740B (en) | Yield strength 700MPa grade atmospheric corrosion resistant hot rolled strip and manufacturing method | |
| CN109136482A (en) | Inexpensive yield strength >=960Mpa high intensity cut deal and its production method | |
| CN105039870B (en) | A kind of preparation method of X80M pipe line steel of low temperature resistant big strain and application | |
| US20180355452A1 (en) | Steel plate with yield strength at 890mpa level and low welding crack sensitivity and manufacturing method therefor | |
| CN104928580A (en) | Low-Mn hot rolled steel and preparation method thereof | |
| CN109385576A (en) | A kind of inexpensive X65 pipe line steel and its manufacturing method based on magnesium processing | |
| CN105088096B (en) | X80 pipeline steel with high stress ratio and high arrest toughness and preparation method and application of X80 pipeline steel | |
| CN109898016A (en) | 500MPa grades or more high reaming hot rolling acid-cleaning steel plate and its manufacturing method | |
| CN106319387B (en) | A kind of X80 large-deformation-resistance pipeline steels and manufacturing method | |
| CN104372257A (en) | Low-alloy high-strength middle-thickness plate capable of utilizing self-tempering waste heat to improve toughness and preparation method of low-alloy high-strength middle-thickness plate | |
| CN109898017A (en) | 1000MPa grades of cold-bending properties excellent cold-rolled biphase steel and production method | |
| EP3097214A1 (en) | Hot-rolled ultrahigh strength steel strip product | |
| CN101812642A (en) | Ultrafine crystal bainite high-strength steel and manufacturing method thereof | |
| CN102899561A (en) | High-strength cold forming steel sheet and manufacturing method thereof | |
| CN107034413B (en) | The wear-resisting strip of low quenching degree and its manufacturing method | |
| CN108728729B (en) | A kind of high-intensitive quenching and tempering type container steel and its production method of low yield strength ratio |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| PB01 | Publication | ||
| PB01 | Publication | ||
| SE01 | Entry into force of request for substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| GR01 | Patent grant | ||
| GR01 | Patent grant |