CN104018072A - Cold-rolled steel sheet and preparation method thereof - Google Patents
Cold-rolled steel sheet and preparation method thereof Download PDFInfo
- Publication number
- CN104018072A CN104018072A CN201410272442.1A CN201410272442A CN104018072A CN 104018072 A CN104018072 A CN 104018072A CN 201410272442 A CN201410272442 A CN 201410272442A CN 104018072 A CN104018072 A CN 104018072A
- Authority
- CN
- China
- Prior art keywords
- cold
- weight
- temperature
- steel sheet
- rolling
- 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.)
- Granted
Links
Abstract
The invention discloses a preparation method of a cold-rolled steel sheet. The method comprises the steps of sequentially carrying out hot rolling, reeling, cold rolling, annealing, finishing and tension leveling on a sheet blank, wherein the sheet blank is composed of 0.003-0.01wt% of C, less than or equal to 0.06wt% of Si, 0.2-0.7wt% of Mn, 0.005-0.02wt% of P, 0.005-0.02wt% of S, 0.04-0.1wt% of Nb, 0.01-0.08wt% of Al and the balance of Fe and unavoidable impurities. The invention also discloses a cold-rolled steel sheet prepared by using the method. The obtained steel sheet is the cold-rolled steel sheet with relatively favorable strength (ReL is 190-240MPa, and Rm is 340-400MPa) and forming property so as to have favorable market prospects.
Description
Technical field
The present invention relates to a kind of cold-rolled steel sheet and preparation method thereof.
Background technology
Along with the development of automobile industry, market improves constantly with the requirement of plate automobile, and in order to meet the forming requirements of market deep-drawing, it is further urgent that the demand of special ultra-deep punching cold-rolling steel sheet seems.
At present, as the method for the special ultra-deep punching cold-rolling steel sheet of preparation, CN101514392A discloses the continuous annealing process of a kind of deep-draw and extra-deep drawing sheet steel.This technique comprises: steel plate through cleaning, enters continuous annealing furnace before annealing, and speed 150～350m/min adopts nitrogen hydrogen mixeding gas ejection surface of steel plate, to steel plate protect, anti-oxidation, make steel billet temperature be heated to 120～180 DEG C simultaneously; Again, to steel plate heating, make its temperature reach 750～780 DEG C, and be incubated 40～70s; Then steel plate is cooled to 400～460 DEG C, and is incubated 60～300s and carries out overaging processing, be cooled to subsequently normal temperature.Owing to adopting overaging annealing process, the carbide in steel is fully separated out, ensure household electrical appliances steel plate and auto sheet punching performance and super deep drawability.But, this technique do not control well reinforcing process, can not obtain the cold-rolled steel sheet that intensity and forming property have concurrently, and cost is higher.
Summary of the invention
The object of the invention is to overcome existing cold-rolled steel sheet preparation method and be difficult to obtain cold-rolled steel sheet and the higher defect of cost that intensity and forming property have concurrently, provide a kind of and can obtain intensity and forming property is better and the preparation method of lower-cost cold-rolled steel sheet and the cold-rolled steel sheet of preparation thereof.
The present inventor finds by deep research: by controlling the operations such as slab moiety, hot rolling, cold rolling, annealing, particularly in the control of the control to speed of cooling, cold rolling middle draft in hot rolling, continuous annealing process, the temperature of each processing section is controlled, refinement is also stablized ferrite crystalline size, thereby it is good to obtain finished product mechanical property, the particularly good cold-rolled steel sheet of intensity and forming property, thus the present invention completed.
That is, the invention provides a kind of preparation method of cold-rolled steel sheet, the method comprises: by slab successively through hot rolling, batch, cold rolling, annealing, polishing and straightening, wherein,
After described hot rolling and before described batching, first with the speed of cooling of 70-90 DEG C/s by the intermediate slab obtaining after hot rolling to 700-750 DEG C, then air cooling is to the temperature of batching;
Described temperature of batching is 580-630 DEG C;
Described cold rolling draft is 65-80%;
The mode of described annealing is continuous annealing, in the process of described annealing, the intermediate slab obtaining after cold rolling is passed through heating zone successively, soaking zone, a cooling section, low temperature keeps section, overaging section and secondary cooling section, the described intermediate slab obtaining after cold rolling is in described heating zone, described soaking zone, a described cooling section, described low temperature keeps section, terminal temperature in described overaging section and described secondary cooling section is respectively 730-780 DEG C, 800-850 DEG C, 160-230 DEG C, 280-340 DEG C, 260-300 DEG C, below 100 DEG C, the residence time is respectively 30-80s, 30-50s, 260-480s, 60-100s, 200-310s, 120-180s,
Consisting of of described slab: C:0.003-0.01 % by weight, Si :≤0.06 % by weight, Mn:0.2-0.7 % by weight, P:0.005-0.02 % by weight, S:0.005-0.02 % by weight, Nb:0.04-0.1 % by weight, Al:0.01-0.08 % by weight, surplus is Fe and inevitable impurity.
The present invention also provides the cold-rolled steel sheet of being prepared by aforesaid method.
The cold-rolled steel sheet that adopts preparation method of the present invention to prepare, its finished product mechanical property reaches yield strength R
eLfor 190-240MPa, tensile strength R
mfor 340-400MPa, elongation after fracture A
80>=35%, plastic strain ratio r
90>=2.2, work hardening exponent n
90>=0.19, be a kind of steel plate that is specially adapted to manufacture the component such as the car extending bracket of automotive field, there is market potential prospect.
Other features and advantages of the present invention are described in detail the embodiment part subsequently.
Brief description of the drawings
Accompanying drawing is to be used to provide a further understanding of the present invention, and forms a part for specification sheets, is used from explanation the present invention, but is not construed as limiting the invention with embodiment one below.In the accompanying drawings:
Fig. 1 is the microstructure picture of the cold-rolled steel sheet prepared of the embodiment of the present invention 1.
Fig. 2 is the microstructure picture of the cold-rolled steel sheet prepared of the embodiment of the present invention 2.
Fig. 3 is the microstructure picture of the cold-rolled steel sheet prepared of the embodiment of the present invention 3.
Fig. 4 is the microstructure picture of the cold-rolled steel sheet prepared of comparative example 1 of the present invention.
Fig. 5 is the microstructure picture of the cold-rolled steel sheet prepared of comparative example 2 of the present invention.
Fig. 6 is the microstructure picture of the cold-rolled steel sheet prepared of comparative example 3 of the present invention.
Fig. 7 is the microstructure picture of the cold-rolled steel sheet prepared of comparative example 4 of the present invention.
Embodiment
Below the specific embodiment of the present invention is elaborated.Should be understood that, embodiment described herein only, for description and interpretation the present invention, is not limited to the present invention.
The invention provides a kind of preparation method of cold-rolled steel sheet, the method comprises: by slab successively through hot rolling, batch, cold rolling, annealing, polishing and straightening, wherein, after described hot rolling and before described batching, first with the speed of cooling of 70-90 DEG C/s by the intermediate slab obtaining after hot rolling to 700-750 DEG C, then air cooling is to the temperature of batching, described temperature of batching is 580-630 DEG C, described cold rolling draft is 65-80%, the mode of described annealing is continuous annealing, in the process of described annealing, the intermediate slab obtaining after cold rolling is passed through heating zone successively, soaking zone, a cooling section, low temperature keeps section, overaging section and secondary cooling section, the described intermediate slab obtaining after cold rolling is in described heating zone, described soaking zone, a described cooling section, described low temperature keeps section, terminal temperature in described overaging section and described secondary cooling section is respectively 730-780 DEG C, 800-850 DEG C, 160-230 DEG C, 280-340 DEG C, 260-300 DEG C, below 100 DEG C, the residence time is respectively 30-80s, 30-50s, 260-480s, 60-100s, 200-310s, 120-180s, consisting of of described slab: C:0.003-0.01 % by weight, Si :≤0.06 % by weight, Mn:0.2-0.7 % by weight, P:0.005-0.02 % by weight, S:0.005-0.02 % by weight, Nb:0.04-0.1 % by weight, Al:0.01-0.08 % by weight, surplus is Fe and inevitable impurity.
In the present invention, although just can obtain the cold-rolled steel sheet of better intensity and better forming property in the time that the composition of slab is in above-mentioned scope, but in order to obtain the performance of the cold-rolled steel sheet that enhancing obtains, under preferable case, consisting of of described slab: C:0.004-0.009 % by weight, Si:0.01-0.04 % by weight, Mn:0.3-0.7 % by weight, P:0.006-0.02 % by weight, S:0.008-0.015 % by weight, Nb:0.06-0.09 % by weight, Al:0.03-0.07 % by weight, surplus is Fe and inevitable impurity.The moiety of described slab is in above-mentioned scope time, can through hot rolling of the present invention, batch, after cold rolling, annealing, polishing and straightening technique, will make the cold-rolled steel sheet that intensity and forming property are more good.
In the present invention, consider the over-all properties of purity of steel and product, the carbon content in described slab need to be controlled in above-mentioned scope, if carbon (C) content exceedes 0.01 % by weight, and the Plasticity Decreasing of steel plate, forming property worsens; Moreover the content of silicon (Si) need to be controlled at lower scope; Manganese (Mn) can increase the intensity of described slab, and can be combined into MnS with sulphur (S), prevents the thermal crack causing because of FeS simultaneously, but Mn too high levels, the welding property that can affect steel, therefore, need to be controlled at the content of Mn in above-mentioned scope.In addition, phosphorus (P), as strengthening element, need to be added in above-mentioned scope.Consider the economy of steel making working procedure and the effect of calcium processing, S is controlled under the scope of 0.005-0.02 % by weight.Aluminium (Al) mainly adds as deoxidant element, realize complete deoxidation, its content requirement is more than 0.01 % by weight, but too high aluminium will affect welding property and the coating adhesion and uneconomical of steel, therefore, Al content is chosen as 0.01-0.08 % by weight and is advisable.The main fixed interval (FI) of niobium (Nb) C atom, is removed interstitial atom, obtains pure ferrite matrix.
Described slab can adopt the known method of preparing continuously cast bloom of this area to be prepared, for example can be by obtaining continuously cast bloom after blast furnace ironmaking, hot metal pretreatment, converter smelting, steel ladle deoxidation, alloying furnace rear refining, LF electrically heated, RH vacuum-treat and sheet billet continuous casting as described slab of the present invention.The condition of its concrete preparation is well known in the art.
In addition, in the present invention, the thickness of described slab can be 190-210mm left and right.
According to the present invention, described hot rolling comprises roughing and finish rolling.The start rolling temperature of described roughing can be 1185-1230 DEG C, is preferably 1190-1220 DEG C; The finishing temperature of described roughing can be 1145-1190 DEG C, is preferably 1155-1180 DEG C.In addition, the thickness of the intermediate slab after described roughing can be 33-37mm, is preferably 33-35.5mm.
In addition, the start rolling temperature of described finish rolling can be 1130-1170 DEG C, is preferably 1135-1160 DEG C; The finishing temperature of described finish rolling can be 870-930 DEG C, is preferably 890-920 DEG C; The thickness of the intermediate slab after described finish rolling can be 2-5mm, is preferably 3-4.5mm.In order to reach the needed bundle temperature of opening of roughing of hot rolling, can before roughing, first continuously cast bloom be heated in heater to the required bundle temperature of opening when being heated to continuously cast bloom and carrying out roughing.The thickness of the intermediate slab obtaining after described hot rolling is the thickness of the intermediate slab after the described finish rolling here, and after referring to after described hot rolling that finish rolling completes.
According to the present invention, after described hot rolling and before described batching, the intermediate slab obtaining is carried out to two steps cooling after hot rolling.Under preferable case, first with the speed of cooling of 70-85 DEG C/s, the intermediate slab obtaining after hot rolling is cooled to 710-750 DEG C (adopting the type of cooling of ultrafast cold water), then with air cooling to the temperature of batching.Preferably, the time of described air cooling is 20-30s.
According to the present invention, under preferable case, described in the temperature of batching be 605-630 DEG C.
According to the present invention, under preferable case, described cold rolling draft is 68-75%.
According to the present invention, under preferable case, the described intermediate slab obtaining after cold rolling keeps terminal temperature in section, described overaging section and described secondary cooling section to be respectively 750-780 DEG C, 815-850 DEG C, 200-230 DEG C, 300-340 DEG C, 260-290 DEG C, 70-100 DEG C at described heating zone, described soaking zone, a described cooling section, described low temperature, and the residence time is respectively 40-80s, 40-60s, 280-450s, 70-90s, 220-250s, 140-170s.
At this, the terminal temperature of described heating zone refers to temperature when the described intermediate slab obtaining after cold rolling enters described soaking zone through described heating zone; The terminal temperature of described soaking zone refers to temperature when the described intermediate slab obtaining after cold rolling enters a described cooling section through described soaking zone; The terminal temperature of a described cooling section refers to that the described intermediate slab obtaining after cold rolling enters through a described cooling section temperature that described low temperature keeps section; Described low temperature keeps the terminal temperature of section to refer to temperature when the described intermediate slab obtaining after cold rolling keeps section to enter described overaging section through described low temperature; The terminal temperature of described overaging section refers to temperature when the described intermediate slab obtaining after cold rolling enters described secondary cooling section through described overaging section; The terminal temperature of described secondary cooling section refers to temperature when the described intermediate slab obtaining after cold rolling enters next step and processes through secondary cooling section.
According to the present invention, the type of heating of described heating zone can various heating means known in the field, for the present invention, preferably adopt the heating means of flame (anaerobic heating).
According to the present invention, the type of heating of described soaking zone can various heating means known in the field, for example, can adopt the heating means with electrically heated radiator tube.
According to the present invention, the type of cooling of a described cooling section can be various method of cooling known in the field, for example can be with mobile cooling gas, as jet cooling with blower fan.Cooling gas used can be usually used in jet cooling gas for this area, for example, the mixed gas of nitrogen and hydrogen, wherein the volume percent of hydrogen is 2-8%.
According to the present invention, the intermediate blank of a described cooling section enters into this low temperature and keeps, in section, the temperature with lower is carried out to heat temperature raising, and type of heating can various heating means known in the field, for example, can adopt the heating means of use electrically heated radiator tube.
According to the present invention, the method for the temperature of described control overaging section can be conventional temperature control method, is in the scope of 260-300 DEG C as long as described overaging section makes the temperature of slab.For example the method for the temperature of described control overaging section is for to heat overaging section with electrically heated radiator tube and/or to adopt gas blower to lower the temperature.
According to the present invention, the type of cooling of described secondary cooling section can be various method of cooling known in the field, for example above-mentioned jet cooling.
According to the present invention, under preferable case, the unit elongation of described polishing is 0.5-0.9%, more preferably 0.6-0.9%.
According to the present invention, under preferable case, the unit elongation of described straightening is 0.1-0.7%, more preferably 0.35-0.65%.
According to the present invention, by making the unit elongation of described polishing and the unit elongation of described straightening in above-mentioned scope, can there is the plate surface quality of guarantee and the good effect of plate shape.
The cold-rolled steel sheet that the present invention also provides above-mentioned preparation method to prepare.
Cold-rolled steel sheet provided by the invention has good mechanical property, the yield strength R of described cold-rolled steel sheet
eLfor 190-240MPa, be preferably 200-235MPa; Tensile strength R
mfor 340-400MPa, be preferably 350-390MPa; Elongation after fracture A
80>=35%, be preferably 36-40%; Plastic strain ratio r
90>=2.2, be preferably 2.3-2.7; Work hardening exponent n
90>=0.19, be preferably 0.2-0.24.
The microstructure of cold-rolled steel sheet provided by the invention is 100% ferritic structure, and ferrite grain size is more than 6.5 grades, is preferably 6.5-8 level, and ferrite grain size is 20-35 μ m, is preferably 22-33 μ m.
By method of the present invention, can control the yield strength R of gained cold-rolled steel sheet
eLwithin the scope of 190-240MPa and tensile strength R
mwithin the scope of 340-400MPa, there is good forming property (elongation after fracture A simultaneously
80>=35%, plastic strain ratio r
90>=2.2, work hardening exponent n
90>=0.19), be a kind of steel plate that is specially adapted to manufacture the component such as the car extending bracket of automotive field, there is market potential prospect.
Below will describe the present invention by embodiment.
In following examples and comparative example, the measuring method of the mechanical property of cold-rolled steel sheet is: yield strength R
eL, tensile strength R
m, elongation after fracture A
80testing method carry out according to GBT228-2002 metallic substance tensile testing at ambient temperature; Plastic strain ratio r
90testing method carry out according to the measuring method of GBT5027-2007 metal sheet and strip plastic strain ratio (r value); Work hardening exponent n
90testing method carry out according to GBT5028-2008 metal sheet and strip tension strain hardenability value (n value) test method.
The continuous annealing unit using in following examples and comparative example comprises that heating zone, soaking zone, cooling section, a low temperature keep section, overaging section and secondary cooling section successively.Described heating zone is that non-oxidation furnace (NOF) heats by the straight fire of coal gas, and described soaking zone heats by electrically heated radiator tube; A described cooling section by jet carry out cooling; Described low temperature keeps section to heat by electrically heated radiator tube; Described overaging section is by carrying out temperature control with electrically heated radiator tube and gas blower; Described secondary cooling section by jet carry out cooling.
Embodiment 1-3
The present embodiment is used for illustrating cold-rolled steel sheet of the present invention and preparation method thereof.
Converter smelting, through LF stove Ca process, RH decarburization and continuous casting obtain continuously cast bloom of the present invention (thickness is 200mm), its moiety is in table 1.This continuous casting steel billet is heated to opening of roughing in process furnace to be pricked temperature and enters reversible roughing unit, intermediate blank after roughing enters Coil Box, make to be with steel toe, tail to be exchanged, then carry out finish rolling, after finish rolling and according to the speed of cooling of specifying, be quickly cooled to final cooling temperature, then after online air cooling for some time, under coiling temperature, batch (hot rolling technology and process for cooling carry out according to the condition in table 2).According to the cold rolling and continuous annealing process shown in table 3, slab is carried out to cold rolling and anneal again, be about to slab after batching is bundled into appointed thickness on cold-rolling mill cold-reduced sheet with the cold rolling draft of specifying, and then the unit speed of controlling continuous annealing machine is annealed to this cold-rolled steel sheet, heating zone (NOF) is passed through in described continuous annealing successively, soaking zone (RTH), a cooling section (GJS), low temperature keeps section (LTH), overaging section section (OAS) and secondary cooling section (FCS), then after being cooled to room temperature, carry out polishing and straightening according to the technique in table 3 again.The mechanical property of the cold-rolled steel sheet finally obtaining and the data of microstructure are in table 4, and Fig. 1-3 are shown in respectively by the photo of its microstructure.
Comparative example 1
According to the method described in embodiment 1, described different, at converter smelting, different through the moiety of the continuously cast bloom that LF stove Ca processes, RH decarburization and continuous casting obtain, be shown in Table 1, the performance test results that obtains steel plate is shown in Table 4, and Fig. 4 is shown in by the photo of its microstructure.
Comparative example 2
According to the method described in embodiment 1, difference is, the speed of cooling of taking in hot rolling technology is 50 DEG C/s, and the performance test results that obtains steel plate is shown in Table 4, and Fig. 5 is shown in by the photo of its microstructure.
Comparative example 3
According to the method described in embodiment 1, difference is, the cold rolling draft of taking in cold-rolling process is 50%, and the performance test results that obtains steel plate is shown in Table 4, and Fig. 6 is shown in by the photo of its microstructure.
Comparative example 4
According to the method described in embodiment 1, difference is, the control difference of continuous annealing process is as shown in table 3, and the performance test results that obtains steel plate is shown in Table 4, and Fig. 7 is shown in by the photo of its microstructure.
Table 1
Table 2
Table 3
Table 4
Note: "---" in table represents not perfect recrystallization of steel plate, when tension test, sample is disconnected in advance, cannot measure n, r value; And microstructure is perfect recrystallization not, cannot pass judgment on according to metallographic structure standard.
Can find out by the data in table 1-4, adopt preparation method of the present invention, can obtain yield strength R
eLfor 190-240MPa, tensile strength R
mfor 340-400MPa, elongation after fracture A
80>=35%, plastic strain ratio r
90>=2.2, work hardening exponent n
90>=0.19, and the microstructure ferritic structure that is 100%, ferrite grain size is more than 6.5 grades, ferrite grain size is the cold-rolled steel sheet of 20-35 μ m.
More than describe the preferred embodiment of the present invention in detail; but the present invention is not limited to the detail in above-mentioned embodiment, within the scope of technical conceive of the present invention; can carry out multiple simple variant to technical scheme of the present invention, these simple variant all belong to protection scope of the present invention.
It should be noted that in addition, each concrete technical characterictic described in above-mentioned embodiment, in reconcilable situation, can combine by any suitable mode, for fear of unnecessary repetition, the present invention is to the explanation no longer separately of various possible array modes.
In addition, also can carry out arbitrary combination between various embodiment of the present invention, as long as it is without prejudice to thought of the present invention, it should be considered as content disclosed in this invention equally.
Claims (12)
1. a preparation method for cold-rolled steel sheet, the method comprises: by slab successively through hot rolling, batch, cold rolling, annealing, polishing and straightening, it is characterized in that,
After described hot rolling and before described batching, first with the speed of cooling of 70-90 DEG C/s, the intermediate slab obtaining after hot rolling is cooled to 700-750 DEG C, then air cooling is to the temperature of batching;
Described temperature of batching is 580-630 DEG C;
Described cold rolling draft is 65-80%;
The mode of described annealing is continuous annealing, in the process of described annealing, the intermediate slab obtaining after cold rolling is passed through heating zone successively, soaking zone, a cooling section, low temperature keeps section, overaging section and secondary cooling section, the described intermediate slab obtaining after cold rolling is in described heating zone, described soaking zone, a described cooling section, described low temperature keeps section, terminal temperature in described overaging section and described secondary cooling section is respectively 730-780 DEG C, 800-850 DEG C, 160-230 DEG C, 280-340 DEG C, 260-300 DEG C, below 100 DEG C, the residence time is respectively 30-80s, 30-50s, 260-480s, 60-100s, 200-310s, 120-180s,
Consisting of of described slab: C:0.003-0.01 % by weight, Si :≤0.06 % by weight, Mn:0.2-0.7 % by weight, P:0.005-0.02 % by weight, S:0.005-0.02 % by weight, Nb:0.04-0.1 % by weight, Al:0.01-0.08 % by weight, surplus is Fe and inevitable impurity.
2. preparation method according to claim 1, wherein, after described hot rolling and before described batching, first with the speed of cooling of 70-85 DEG C/s by the intermediate slab obtaining after hot rolling to 710-750 DEG C, then air cooling is to the temperature of batching.
3. preparation method according to claim 1, wherein, described in the temperature of batching be 605-630 DEG C.
4. preparation method according to claim 1, wherein, described cold rolling draft is 68-75%.
5. preparation method according to claim 1, wherein, the described intermediate slab obtaining after cold rolling keeps terminal temperature in section, described overaging section and described secondary cooling section to be respectively 750-780 DEG C, 815-850 DEG C, 200-230 DEG C, 300-340 DEG C, 260-290 DEG C, 70-100 DEG C at described heating zone, described soaking zone, a described cooling section, described low temperature, and the residence time is respectively 40-80s, 40-60s, 280-450s, 70-90s, 220-250s, 140-170s.
6. preparation method according to claim 1, wherein, consisting of of described slab: C:0.004-0.009 % by weight, Si:0.01-0.04 % by weight, Mn:0.3-0.7 % by weight, P:0.006-0.02 % by weight, S:0.008-0.015 % by weight, Nb:0.06-0.09 % by weight, Al:0.03-0.07 % by weight, surplus is Fe and inevitable impurity.
7. method according to claim 1, wherein, described hot rolling comprises roughing and finish rolling; The start rolling temperature of described roughing is 1185-1230 DEG C, and the finishing temperature of described roughing is 1145-1190 DEG C; The opening of described finish rolling pricks that to roll temperature be 1130-1170 DEG C, and the finishing temperature of described finish rolling is 870-930 DEG C.
8. method according to claim 1, wherein, the time of described air cooling is 20-30s.
9. preparation method according to claim 1, wherein, the unit elongation of described polishing is 0.5-0.9%; The unit elongation of described straightening is 0.1-0.7%.
10. the cold-rolled steel sheet of preparing according to the preparation method described in any one in claim 1-9.
11. cold-rolled steel sheet according to claim 10, wherein, the yield strength R of described cold-rolled steel sheet
eLfor 190-240MPa, tensile strength R
mfor 340-400MPa, elongation after fracture A
80>=35%, plastic strain ratio r
90>=2.2, work hardening exponent n
90>=0.19.
12. according to the cold-rolled steel sheet described in claim 10 or 11, wherein, the ferritic structure that the microstructure of described cold-rolled steel sheet is 100%, ferrite grain size is more than 6.5 grades, ferrite grain size is 20-35 μ m.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201410272442.1A CN104018072B (en) | 2014-06-18 | 2014-06-18 | A kind of cold-rolled steel sheet and preparation method thereof |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201410272442.1A CN104018072B (en) | 2014-06-18 | 2014-06-18 | A kind of cold-rolled steel sheet and preparation method thereof |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN104018072A true CN104018072A (en) | 2014-09-03 |
| CN104018072B CN104018072B (en) | 2016-03-09 |
Family
ID=51435061
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201410272442.1A Active CN104018072B (en) | 2014-06-18 | 2014-06-18 | A kind of cold-rolled steel sheet and preparation method thereof |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN104018072B (en) |
Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2002003993A (en) * | 2000-06-20 | 2002-01-09 | Nkk Corp | High strength steel sheet and high strength galvanized steel sheet |
| CN101956133A (en) * | 2010-10-29 | 2011-01-26 | 攀钢集团钢铁钒钛股份有限公司 | Low-yield strength anti-ageing continuous annealing cold-roll steel sheet and production method thereof |
| CN103045833A (en) * | 2011-10-11 | 2013-04-17 | 攀钢集团攀枝花钢铁研究院有限公司 | Steel plate and galvanizing steel plate, and preparation method thereof |
-
2014
- 2014-06-18 CN CN201410272442.1A patent/CN104018072B/en active Active
Patent Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2002003993A (en) * | 2000-06-20 | 2002-01-09 | Nkk Corp | High strength steel sheet and high strength galvanized steel sheet |
| CN101956133A (en) * | 2010-10-29 | 2011-01-26 | 攀钢集团钢铁钒钛股份有限公司 | Low-yield strength anti-ageing continuous annealing cold-roll steel sheet and production method thereof |
| CN103045833A (en) * | 2011-10-11 | 2013-04-17 | 攀钢集团攀枝花钢铁研究院有限公司 | Steel plate and galvanizing steel plate, and preparation method thereof |
Non-Patent Citations (1)
| Title |
|---|
| 尹红国 等: "《退火方式对390MPa级高强IF钢组织及性能的影响》", 《轧钢》 * |
Also Published As
| Publication number | Publication date |
|---|---|
| CN104018072B (en) | 2016-03-09 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN103993148B (en) | A kind of ultralow carbon cold-rolled steel plate and preparation method thereof | |
| CN103993147B (en) | A kind of cold-rolled steel sheet and preparation method thereof | |
| CN103993226B (en) | Cold-rolled steel sheet of a kind of high strength and preparation method thereof | |
| CN111996467A (en) | 980 MPa-grade galvanized high-strength steel and preparation method thereof | |
| CN104611535A (en) | Cold-rolled steel sheet and preparation method thereof | |
| CN103993227B (en) | A kind of cold-rolled steel sheet and preparation method thereof | |
| CN106636899A (en) | Manufacturing method of 1000MPa-grade high-reaming type cold-rolled bainite steel | |
| CN103667907A (en) | Hot-rolled high-strength sheet steel having tensile strength of 510MPa, and production method thereof | |
| CN103993225B (en) | A kind of cold-rolled steel sheet and preparation method thereof | |
| CN104060070B (en) | A kind of cold-rolled steel sheet and its preparation method | |
| CN104060161B (en) | A kind of hot continuous-milling steel plate and production method thereof | |
| CN104017970B (en) | A kind of cold-rolled steel sheet and preparation method thereof | |
| CN104120345B (en) | Cold-rolled steel sheet and preparation method thereof and hot-dip galvanizing sheet steel and preparation method thereof | |
| CN104120346B (en) | Cold-rolled steel sheet and preparation method thereof and hot-dip galvanizing sheet steel and preparation method thereof | |
| CN104120231B (en) | A kind of cold-rolled steel sheet and preparation method thereof | |
| CN104060072B (en) | Cold-rolled steel sheet and preparation method thereof and hot-dip galvanizing sheet steel and preparation method thereof | |
| CN104131223B (en) | A kind of cold-rolled steel sheet and preparation method thereof | |
| CN104018072B (en) | A kind of cold-rolled steel sheet and preparation method thereof | |
| CN104018079B (en) | Cold-rolled steel sheet and preparation method thereof and hot-dip galvanizing sheet steel and preparation method thereof | |
| CN104017969B (en) | Cold-rolled steel sheet and preparation method thereof and hot-dip galvanizing sheet steel and preparation method thereof | |
| CN104060166B (en) | Cold-rolled steel sheet and preparation method thereof and hot-dip galvanizing sheet steel and preparation method thereof | |
| CN104018077B (en) | A kind of cold-rolled steel sheet and preparation method thereof | |
| CN104120347B (en) | A kind of cold-rolled steel sheet and preparation method thereof | |
| CN104120343B (en) | A kind of cold-rolled steel sheet and preparation method thereof | |
| CN104120344B (en) | A kind of cold-rolled steel sheet and preparation method thereof |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| C06 | Publication | ||
| PB01 | Publication | ||
| C10 | Entry into substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| C14 | Grant of patent or utility model | ||
| GR01 | Patent grant |