CN102021482A - Cold-rolled galvanized duplex steel and manufacturing method thereof - Google Patents
Cold-rolled galvanized duplex steel and manufacturing method thereof Download PDFInfo
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Abstract
The invention relates to a cold-rolled galvanized duplex steel, wherein the substrate thereof comprises the following components by weight percentage: 0.08 to 0.18 wt.% of C, 0.50 to 1.50 wt.% of Si, 1.50 to 2.5 wt.% of Mn, 0.10 to 1.0 wt.% of Cr, 0.02 to 0.5 wt.% of Mo, 0.005 to 0.05 wt.% of Nb, 0.005 to 0.05 wt.% of Ti, 0.002 to 0.05 wt.% of T.Al, less than or equal to 0.02 wt.% of P, less than or equal to 0.01 wt.% of S and less than or equal to 0.006 wt.% of N, and the balance of Fe. The manufacturing method thereof comprises the steps of: smelting in an oxygen top-blown convertor, refining in a heating steel ladle, continuously casting into a slab, and then conventionally hot rolling, pickling tandem rolling, galvanizing and annealing, wherein the critical annealing temperature is between 760 and 840 DEG C; the annealing is finished in the two-phase area of ferrite and austenite; 1CR section cooling has a cooling speed of 1 to 40 DEG C/S from the annealing temperature to the zinc pool, putting the substrate into the zinc pool having a temperature of 450 to 465 DEG C so as to galvanize; and 2a CR section cooling has a cooling speed more than 3 DEG C/S. The steel of the invention has the advantages of high tensile strength, low yield ratio, capable of being press formed, excellent matching between strength and toughness, high rate of initially work-hardening and being free from yield extending.
Description
Technical field
The present invention relates to low-alloy high-strength steel, particularly 1180Mpa cold rolling hot dip galvanizing dual phase steel and manufacture method thereof.
Background technology
Automobile industry development energy-conservation loss of weight, increases security, improves car body solidity to corrosion etc. and become the target that people pursue so far, and therefore, adopting high strength and steel plate galvanized is the inexorable trend of automobile steel development.
Dual phase steel is the high-strength steel that present automobile industry is most widely used, automobile has hot-rolled dual-phase steel, cold-rolled biphase steel and cold rolling hot dip galvanizing dual phase steel with the dual phase steel branch, comparatively sophisticated at present is cold-rolled biphase steel, the commercialization of cold rolling hot dip galvanizing dual phase steel, the tensile strength rank mainly contains 500MPa, 600MPa, 800MPa, and the visible report of the cold rolling hot dip galvanizing dual phase steel of 980MPa is few, and particularly 1180MPa cold rolling hot dip galvanizing dual phase steel has not yet to see report and relevant patent documentation.
US 7311789B2, JP 2006283071A, JP 2006052445A, EP 2028282A1, CN200410084680.6, CN200380109234.X etc., composition 0.12～0.18%C of setting forth of EP 2028282A1 wherein, 0.2～0.4%Si, also add simultaneously a small amount of B etc., by the minimum 580MPa that reaches of pot galvanize annealing yield strength, tensile strength can reach 1000MPa, and unit elongation (A80) can reach 10%; Patent JP 2006283071A is a kind of manufacture method of producing hot dip galvanized dual phase steel, chemical ingredients Si content is higher, utilized in the hot galvanizing process before advancing the zinc pot at surface of steel plate flash one deck very thin Ni and Ni-Fe, improved surface of steel plate because the plating leakage phenomenon that elements Si, Mn surface enrichment cause; Patent JP 2006052445A has set forth a kind of equipment that has the high speed cooling power that can take into account production TRIP and DP steel, and speed of cooling can be produced high-strength steel at 10～100 ℃/s by adopting different cooling; What patent CN200410084680.6 showed is a kind of dual phase steel of the Si of nothing composition, from annealing temperature to 5～16 ℃/s of zinc pond cooling rate, cooling rate is greater than 7 ℃/s after going out the zinc pot, obtain the dual phase steel of tensile strength, have favorable surface quality owing to not containing the Si element simultaneously greater than the low yield strength ratio of 800MPa.
At present, the hot-rolled dual-phase steel maximum intensity can reach 980MPa, cold-rolled biphase steel is the highest 1200MPa, and the highest at present 980MPa that accomplishes of hot dip galvanized dual phase steel, because must be in the hot dip galvanizing annealing process by 460 ℃ zinc liquid temperature, bainite transformation easily takes place under this temperature, obtains two-phase steel organization and becomes difficult.
Summary of the invention
The purpose of this invention is to provide a kind of cold rolling hot dip galvanizing dual phase sheet steel, the substrate before it is zinc-plated is a cold-reduced sheet, and to become strengthening mechanism mutually, microtexture is to add high-intensity martensite on the flexible ferrite matrix.This steel grade has the tensile strength height, and greater than 1180MPa, yield tensile ratio is low, but impact briquetting; Intensity and toughness match; Initial manufacture hardening rate height; No yield extension has been avoided the wrinkling premium properties that waits of piece surface after the moulding.Can be used for some automobile structures, anti-striker etc.And considered the weldability of substrate.
Because the singularity of hot dip galvanizing process, cold rolling hot dip galvanizing dual phase sheet steel for the 1180MPa level, the composition design is most important, at first, it and cold-rolled biphase steel have two differences on alloy designs, the annealing of cold-rolled biphase steel is to finish on continuous annealing production line, when speed of cooling enough big, main with inexpensive Si in composition, Mn is the hardening capacity that main Canadian dollar usually improves steel, and the production of cold rolling hot dip galvanizing dual phase steel is finished on galvanizing line, will be through the zinc pond about 460 ℃, thus there are two problems to need to consider, the one, add the alloying element of q.s, further improve the hardening capacity of substrate, satisfy the speed of cooling of galvanizing line, the 2nd, consider the platability of substrate, Si, in annealing process, easily form enrichment when the Mn element is too much on the surface, influence the wetting property of substrate when zinc-plated, cause zinc-plated defectives such as plating leakage, this just needs to use Cr, the Mo element partly substitutes Si, elements such as Mn reduce its addition.On the other hand, in order to reach the intensity of 1180MPa, the number of elements of interpolation and kind will strengthen, and these all will certainly influence the weldability of material, increase production cost etc.
During the cold rolling hot dip galvanizing dual phase steel is produced, partly substitute these alloy designs principles such as Si, Mn with Cr, Mo and become common recognition, and because the restriction that Si, Mn add makes hot dip galvanized dual phase steel scope in the cold rolling hot dip galvanizing dual phase steel of 450～980MPa always to be difficult to break through again high intensity rank.The invention reside in to reaching the intensity of 1180MPa level, substrate is a cold-reduced sheet, the coating branch has pot galvanize and zinc-iron alloy heat-transmission zinc-plated, adopt direct combustion technology in the hot dip galvanizing annealing process in the heating zone, make and also can obtain satisfied galvanizing surface quality under the high Si content, and adopt cooling, the zincincation of corresponding optimization at substrate composition of the present invention, obtaining microtexture is that ferrite adds martensite and a small amount of bainite, martensite content is 30～50%, tensile strength is greater than 1180MPa, yield strength 690～850MPa, breaking elongation is greater than 8% (50 gauge length).
According to cold rolling hot dip galvanizing dual phase steel of the present invention, the chemical ingredients by weight percentage of its substrate is: C:0.08～0.18%, Si:0.50～1.50%, Mn:1.50～2.5%, Cr:0.10～1.0%, Mo:0.02～0.5%, Nb:0.005～0.05%, Ti:0.005～0.05%, T.Al (total aluminium): 0.02～0.05%, P :≤0.02%, S :≤0.01%, N :≤0.006%, Fe: surplus.
For hit rate and the stability that further satisfies mechanical property, preferably, C:0.095～0.12%, Si:0.8～1.2%, Mn:1.90～2.5%, Cr:0.40～0.60%, Mo:0.04～0.30%, Nb:0.005～0.025%, Ti:0.01～0.05%, P :≤0.01%, S :≤0.006%, N :≤0.003%.
The reasons are as follows of alloy designs of the present invention:
C:C is important solution strengthening element, be to obtain high-intensity assurance, when C content is too low, Ovshinsky scale of construction when same critical annealing is heated in ferrite and the austenite two-phase region reduces, the also corresponding minimizing of the martensite volume that obtains is difficult to guarantee the intensity of 1180MPa, when C content is too high, reduce toughness on the one hand, influence weldability simultaneously.Controlling C in the present invention is 0.08～0.18%, and preferred C is 0.095～0.12%.
Si:Si is a ferrite solution strengthening element, the strong intensity that improves, but generally for hot dip galvanized dual phase steel, can directly influence the platability of substrate when Si content is too high, special annealing technology is adopted in this case, can eliminate the influence of Si element to platability, can suitably improve content when making the design of hot dip galvanized dual phase steel composition, further reduce cost, improve unit elongation.Controlling Si in the present invention is 0.50～1.50%, and preferred Si is 0.8～1.2%.
Mn:Mn can improve hardening capacity strongly, improves work hardening ability, and Mn content is crossed when hanging down, and is difficult to form the martensite of q.s in the tissue, and strengthening effect is poor, can influence the weldability of substrate when too high equally.Controlling Mn in the present invention is 1.50～2.5%, and preferred Mn is 1.90～2.5%.
Austenitic hardening capacity when Cr and Mo:Cr can improve critical annealing when steel grade C content increases, can further increase martensite quantity, and in addition, Cr can promote that C spreads to austenite, reduces ferritic yield strength.But will destroy ductility during too high levels.Mo is a carbide forming element, and most dissolvings effectively improve austenitic hardening capacity in critical heating zone, help obtaining the dual phase steel of obdurability coupling.Cr, Mo element are the substitute element of Si, Mn element, during too high levels, can increase production cost, general Cr+Mo＜0.8%.
Ti and Nb:Ti are the strong carbide elements, precipitation strength, crystal grain thinning.The effect of Nb is similar to Ti, but stronger than Ti, and Nb, Ti element are not dominant element in dual phase steel, and content is unsuitable too high.Control Nb:0.005～0.05% in the present invention, Ti:0.005～0.05%; Nb:0.005～0.025% preferably, Ti:0.01～0.05%.
T.Al (total aluminium): the major function of Al in dual phase steel is reductor, should not be low excessively, but influence continuous casting production when too high.Controlling T.Al in the present invention is 0.02～0.05%.
P:P is a kind of inexpensive solution strengthening element, and for dual phase steel, certain an amount of P is useful to intensity, but influences weldability when too high.Control P≤0.02% in the present invention, be preferably P≤0.01%.
S:S easily forms MnS in steel, cause hot-shortly, influences weldability simultaneously, so few more good more.Control S≤0.01% in the present invention, preferred S≤0.006%.
N: N is few more good more in dual phase steel.Control N≤0.006% in the present invention, preferred N≤0.003%.
The present invention also provides the manufacture method of cold rolling hot dip galvanizing dual phase steel.
The present invention can smelt in top-blown oxygen converter, and refining in the heating ladle, casts slab by continuous casting then, routinely hot rolling and sour tandem rolling.
Hot dip galvanizing annealing process afterwards as shown in Figure 1, annealing temperature is the of paramount importance technological factor of control cold rolling hot dip galvanizing dual phase steel performance, the critical annealing temperature of steel grade of the present invention is 760～840 ℃, finish at ferrite and austenite two-phase region, temperature is too low, carbide is not dissolved in the austenite fully, influences the ductility of hardening capacity and substrate, and martensite quantity reduces simultaneously influences intensity; When annealing temperature was too high, along with austenitic volume fraction increases, C content in the austenite and alloying element content descended, and also can influence hardening capacity, and the cooling back easily produces non-martensite microstructure.Better annealing temperature is 780～820 ℃.
Cooling rate from annealing temperature to the zinc pond generally in 1～40 ℃/S (1CR section the figure), is preferably≤20 ℃/S, and cooling rate is too small, is easy to generate pearlitic transformation, reduces the intensity of substrate, easily produces bainitic transformation when cooling rate is excessive, influences the ductility of substrate.
After finishing the cooling of 1CR section, substrate enters 450～465 ℃ zinc pond and finishes zinc-plated processing, zinc-plated temperature can be at 400～500 ℃, be preferably in 460～490 ℃, zinc-plated time 35～180s, if pot galvanize product, then begin the cooling of 2aCR section afterwards, guarantee this cooling rate greater than 3 ℃/S, better greater than 7 ℃/S, 7～20 ℃/S most preferably, can prevent effectively that austenite is to bainite transformation, to reduce the generation of non-martensite microstructure, should adopt maximum cooling rate on the production line as far as possible, and note adjusting cooling rate according to thickness of slab.
If produce zinc-iron alloy heat-transmission galvanizing production, then the steel plate back reheat to 480～550 ℃ that comes out from the zinc pond carries out about 8～15 seconds Alloying Treatment, the alloying temperature is low more, required time is long more, the big production of industry is difficult to realize, temperature is too high, may cause the coating iron level higher, causes the coating efflorescence.
Carry out the cooling of 2bCR section after the Alloying Treatment, cooling rate greater than 3 ℃/s, is preferably greater than 7 ℃/s, more preferably 7～20 ℃/s with the 2aCR section.
The formulation of composition design of the present invention and hot dip galvanizing annealing process is the simulation to the big production status condition of industry, so can realize in the big production of industry.
Description of drawings
Fig. 1 is the hot dip galvanizing annealing process synoptic diagram.
Fig. 2 is the metallographic structure figure (* 1000) of one embodiment of the present of invention (steel grade H5) cold rolling hot dip galvanizing dual phase steel.
Fig. 3 is the metallographic structure figure (* 1000) of one embodiment of the present of invention (steel grade H7) cold rolling hot dip galvanizing dual phase steel.
Embodiment
Below by specific embodiment the present invention is described in more detail.
The composition of embodiment sees Table 1.
Operating path is steel-making, ingot casting → forging, sawing → hot rolling → pickling → cold rolling → CGL (continuous hot galvanizing line process) → Performance Detection.
The chemical ingredients of table 1 embodiment
| Sample | C | Mn | Mo | Cr | Si | Nb | Ti | P | T.Al | S | N |
| H5 | 0.11 | 1.99 | 0.20 | 0.50 | 0.60 | 0.015 | 0.030 | 0.0088 | 0.035 | 0.0028 | 0.003 |
| H6 | 0.12 | 2.12 | 0.15 | 0.60 | 0.99 | 0.020 | 0.040 | 0.006 | 0.043 | 0.0017 | 0.002 |
| H7 | 0.095 | 2.25 | 0.24 | 0.46 | 1.20 | 0.014 | 0.051 | 0.006 | 0.036 | 0.0031 | 0.003 |
| H8 | 0.12 | 1.90 | 0.04 | 0.60 | 1.4 | 0.025 | 0.01 | 0.006 | 0.040 | 0.0020 | 0.005 |
| H9 | 0.095 | 2.12 | 0.24 | 0.45 | 1.0 | 0.005 | 0.050 | 0.006 | 0.025 | 0.0030 | 0.004 |
Forging process heating 1230 ℃ * 1 hour is opened and is forged 1150 ℃ of temperature, 900 ℃ of final forging temperatures, and forging stock is of a size of thickness 25 * width 195 * length L mm, is of a size of thickness 25 * width 195 * long 70mm through the last hot rolling base of sawing.Hot rolling reheat 1200 ℃ * 1 hour, 890 ℃ of finishing temperatures are rolled the back water-cooled, 550 ℃～650 ℃ of coiling temperatures, hot-rolled sheet thickness 3.2mm, the total draft 25 → 3.2mm of hot rolling (85.6%), cold rolling after the pickling, Cold Rolled Plate Thickness 1.4mm, cold rolling total draft 3.2 → 1.4mm (56%).
After above-mentioned technology again through the pot galvanize anneal, move back simulation test machine simulation hot dip galvanizing annealing process with connecting, according to JIS 5# standard test mechanical property, use the observation by light microscope metallographic structure down at 1000 times, microscopic test is with the etch of Lepera method, and with optics picture processing instrument mensuration martensite content.Mechanical property after the pot galvanize annealing sees Table 2, and Fig. 3 is seen in metallographic structure.
Table 2 hot dip galvanizing annealing process and mechanical property
In the table, σ s: yield strength, σ b: tensile strength, δ
50: breaking elongation (50 gauge length), U.EL (%), uniform elongation.
Fig. 2 (H5) and Fig. 3 (H7) are the metallographic structures (* 1000) of cold rolling hot dip galvanizing dual phase steel of the present invention.
Test shows, cold rolling hot dip galvanizing dual phase steel of the present invention is organized as ferrite and adds martensite and a small amount of bainite, and martensite content is 30～50%, and tensile strength is greater than 1180MPa, and yield tensile ratio is low, has good galvanizing surface quality simultaneously.
More than by specific embodiment the present invention is carried out comparatively detailed explanation, but be not limited only to this, without departing from the inventive concept of the premise can also more changeableization or improved other embodiment, and these changes and improvements all belong to scope of the present invention.
Claims (11)
1. cold rolling hot dip galvanizing dual phase sheet steel, the chemical ingredients by weight percentage of its substrate is: C:0.08～0.18%, Si:0.50～1.50%, Mn:1.50～2.5%, Cr:0.10～1.0%, Mo:0.02～0.5%, Nb:0.005～0.05%, Ti:0.005～0.05%, T.Al:0.02～0.05%, P :≤0.02%, S :≤0.01%, N :≤0.006%, surplus is Fe.
2. cold rolling hot dip galvanizing dual phase sheet steel as claimed in claim 1, it is characterized in that C:0.095～0.12%, Si:0.8～1.2%, Mn:1.90～2.5%, Cr:0.40～0.60%, Mo:0.04～0.30%, Nb:0.005～0.025%, Ti:0.01～0.05%, P :≤0.01%, S :≤0.006%, N :≤0.003%.
3. cold rolling hot dip galvanizing dual phase sheet steel as claimed in claim 1 or 2 is characterized in that, in the chemical ingredients of its substrate, and Cr+Mo＜0.8%.
4. as the arbitrary described cold rolling hot dip galvanizing dual phase sheet steel of claim 1～3, its tensile strength is 1180Mpa.
5. the manufacture method of a cold rolling hot dip galvanizing dual phase sheet steel substrate comprises: smelts in the top-blown oxygen converter, and refining in the heating ladle, cast slab by continuous casting then, routinely hot rolling and sour tandem rolling.
6. the manufacture method of a cold rolling hot dip galvanizing dual phase sheet steel comprises: smelts in the top-blown oxygen converter, and refining in the heating ladle, cast slab by continuous casting then, routinely hot rolling and sour tandem rolling; Hot dip galvanizing annealing process;
Wherein, the critical annealing temperature is 760～840 ℃, finishes at ferrite and austenite two-phase region;
The cooling of 1CR section: the cooling rate from annealing temperature to the zinc pond is 1～40 ℃/S;
Then, substrate enters 450～465 ℃ zinc pond and finishes zinc-plated processing;
Afterwards, the cooling of beginning 2aCR section, cooling rate is greater than 3 ℃/S.
7. the manufacture method of cold rolling hot dip galvanizing dual phase sheet steel as claimed in claim 6 is characterized in that, the critical annealing temperature is 780～820 ℃.
8. as the manufacture method of claim 6 or 7 described cold rolling hot dip galvanizing dual phase sheet steels, it is characterized in that the cooling rate from annealing temperature to the zinc pond≤20 ℃/S.
9. as the manufacture method of the arbitrary described cold rolling hot dip galvanizing dual phase sheet steel of claim 6～8, it is characterized in that zinc-plated temperature is at 400～500 ℃, preferably at 460～490 ℃, zinc-plated time 35～180s.
10. as the manufacture method of the arbitrary described cold rolling hot dip galvanizing dual phase sheet steel of claim 6～9, it is characterized in that 2aCR section cooling rate is greater than 7 ℃/S.
11. manufacture method as the arbitrary described cold rolling hot dip galvanizing dual phase sheet steel of claim 6～10, it is characterized in that, when the pot galvanize product was zinc-iron alloy heat-transmission galvanizing production, the steel plate back reheat to 480～550 ℃ that comes out from the zinc pond carried out about 8～15 seconds Alloying Treatment; Carry out the cooling of 2bCR section after the Alloying Treatment, its cooling rate is greater than 3 ℃/S, and preferred cooling rate is greater than 7 ℃/S.
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| EP1612288B9 (en) * | 2003-04-10 | 2010-10-27 | Nippon Steel Corporation | A method for producing a hot-dip zinc coated steel sheet having high strength |
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