CN101348885B - 1000MPa grade cold rolling hot dip galvanizing two-phase steel and manufacturing method thereof - Google Patents
1000MPa grade cold rolling hot dip galvanizing two-phase steel and manufacturing method thereof Download PDFInfo
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Abstract
The invention provides 1,000 MPa cold-rolled hot-dip galvanized dual-phase steel and a manufacturing method thereof, belonging to the technical field of cold-rolled hot-dip galvanized high-strength steel plates. The chemical components in mass percentage of the cold-rolled hot-dip galvanized dual-phase steel are: 0.06 to 0.18 percent of C, less than or equal to 0.1 percent of Si, 1.2 to 2.5 percent of Mn,0.05 to 0.5 percent of Mo, 0.05 to 0.6 percent of Cr, 0.005 to 0.05 percent of Al, 0.01 to 0.06 percent of Nb, 0.01 to 0.05 percent of Ti, less than or equal to 0.02 percent of P, less than or equal to 0.01 percent of S, less than or equal to 0.005 percent of N, the balance being Fe and inevitable impurities. The manufacturing method adopts Cr or Mo to replace Si, so as to enlarge an austenitic and ferritic two-phase region and improve the hardenability of the dual-phase steel, and meanwhile, the manufacturing method improves the strength of toughness of the steel by adding Nb or Ti refined grains, so as to ensure that the steel has good weldability and usability, and the strength grade of the steel can reach over 1,000 Mpa.
Description
Technical field
The present invention relates to cold rolling hot dip galvanizing High Strength Steel Plate technical field, a kind of 1000MPa grade cold rolling hot dip galvanizing dual phase steel and manufacture method thereof are provided.
Background technology
In order to alleviate automotive dead weight, realize its energy-saving and environmental protection, purpose of safety, the research and development of advanced high-strength steel such as dual phase steel become various countries scholars' the focus of attention.Dual phase steel has advantages such as low yield tensile ratio, high initial manufacture cementation index, higher collision energy absorption capability, good intensity and ductile coupling, is the good high-strength novel punching press steel of a kind of plasticity.Dual phase steel all has more application in the auxiliary component of automobile, body structure, suspension, chassis etc., wherein with the consumption maximum of body structure.At ULSAB plan and ULSAB-AVC in the works, dual phase steel accounts for 74% of whole body structure.
Steel plate galvanized can guarantee that automobile has good corrosion resistant perforation ability, and over past ten years, the usage quantity on body of a motor car increases considerably, particularly high-strength vehicle deep-draw steel plate galvanized.Inside and outside plate of automobile and structural part use steel plate galvanized in large quantities, and its usage quantity on average accounts for more than 80%, many hundred-percent use galvanized sheets of vehicle.For a long time, because China's galvanized sheet production remains in problems, China's car mostly is import with galvanized sheet, especially the galvanized sheet of high-grade car.Therefore, for satisfying the active demand of China's automobile industry to high-quality steel plate galvanized, the exploitation of especially advanced high-strength hot-dip zinc-coated dual phase steel is quite necessary.At present, intensity rank is that the cold rolling hot dip galvanizing dual phase steel of 1000MPa still belongs to blank at home.
Summary of the invention
The object of the present invention is to provide a kind of 1000MPa grade cold rolling hot dip galvanizing dual phase steel and manufacture method thereof, adopt Cr, Mo to replace Si,, improve the hardening capacity of dual phase steel to enlarge austenite+ferrite two-phase region.Simultaneously, improve intensity, the toughness of steel, make steel have good weldability, usability by adding Nb, Ti crystal grain thinning.
The present invention is directed to the hot galvanizing line process characteristic, add a small amount of Cr element in steel, the hardening capacity on formed austenite island promotes that carbon spreads to austenite when improving intercritical annealing, reduce ferritic yield strength, more help obtaining the dual phase steel of low yield strength ratio.Simultaneously, an amount of microalloy element Nb of compound interpolation and Ti form tiny two-phase particle in steel, refining grain size, thus improve the steel plate mechanical property.
Can effectively utilize alloying element by formulating reasonable technological parameter, improve the over-all properties of dual phase steel to greatest extent, so the formulation of the composition design and craft parameter of high strength dual phase steel should mutually combine.
Galvanizing line is compared with continuous annealing production line, and cooling power is lower, but also will pass through the zinc pot, has tangible difference so dual phase steel moves back in cold rolling hot dip galvanizing dual phase steel and cold rolling company on alloy designs.It mainly is C-Si-Mn system that dual phase steel moves back in traditional cold rolling company, and because the speed of cooling of continuous annealing production line is enough big, can improve hardening capacity by the interpolation of Si, Mn fully.The following problem of the main consideration of composition design of cold rolling hot dip galvanizing dual phase steel: the one, the alloying element that add q.s improves the hardening capacity of substrate, satisfies the speed of cooling of galvanizing line; The 2nd, consider the platability and the welding property of substrate, the number of elements of interpolation and kind strengthen, and will have influence on the weldability of material, increase production cost.
The present invention adopts Cr, Mo to replace Si, to enlarge austenite+ferrite two-phase region, improves the hardening capacity of dual phase steel.Chemical ingredients mass percent of the present invention:
C:0.06%～0.18%, Si≤0.10%, Mn:1.20%～2.50%, Mo:0.05%～0.50%, Cr:0.05%～0.60%, Al:0.005%～0.05%, Nb:0.01%～0.06%, Ti:0.01%～0.05%, P≤0.02%, S≤0.01%, N≤0.005%, surplus is iron and inevitable impurity.
Further be optimized for (mass percent): C:0.08%～0.14%, Si≤0.06%, Mn:1.60%～2.10%, Mo:0.15%～0.40%, Cr:0.20%～0.40%, Al:0.005%～0.03%, Nb:0.01%～0.03%, Ti:0.01%～0.02%, P≤0.015%, S≤0.008%, N≤0.004%, surplus is iron and inevitable impurity.
The reasons are as follows of design of alloy of the present invention:
C: carbon is important solution strengthening element, is the assurance that obtains high strength dual phase steel.If its content is low excessively, austenitic content will reduce during annealing, and the martensite volume of generation also reduces thereupon, is difficult to reach the 1000MPa level, so its content can not be lower than 0.08%.And carbon content is too high, and the reaction of iron-zinc will be violent, and the weight loss of iron strengthens, and the zinc coating adhesivity is degenerated and easily causes zinc surface the list edge defective to occur thereby iron-zinc alloy layer is thick more simultaneously.So its content generally is no more than 0.14%.
Si: silicon can enlarge the α+γ district of Fe-C phasor, and the temperature range that the critical zone is handled is widened, and improves the processing performance of dual phase steel, helps keeping the stability and the circulation ratio of performances such as dual phase steel intensity, ductility.Yet high Si content is harmful to the plate surface quality, for hot dip galvanized dual phase steel, can directly influence the platability of substrate when Si content is too high, and this element also is the one of the chief elements that is subjected to the weldability restriction simultaneously.By restriction Si content, also can avoid red squama occurring at hot rolling surface, its content is preferably≤and 0.06%.
Mn: be preferably 1.60%～2.10%.Manganese is the element that enlarges the austenitic area, postpones the formation of perlite and bainite in the middle slow cooling stage, improves the hardening capacity of steel, thereby forms martensite in the pressure process of cooling of promotion after slow cooling finishes.But when manganese content was low, the residual austenite instability behind the ferrite transformation became bainite structure easily mutually in process of cooling, can not obtain the ferrite and the martensitic stucture of dual phase steel requirement; If manganese content is too high, undue stable austenite suppresses the effect that element silicon promotes that ferrite is separated out, and it is few to make ferrite separate out quantitative change, and the carbon content of residual austenite reduces, and has reduced the hardening capacity of steel after the slow cooling on the contrary.Mn understands the oxidized and deposition in steel strip surface in annealing process, excessive Mn will worsen zinc-plated wetting property, so also must add other elements.
Mo: molybdenum is preferably 0.15%～0.40%, replaces Si, Mn with part.Can improve the hardening capacity that formed austenite island is heated in the critical zone, restraining effect to perlitic transformation is very obvious, for hot dip galvanized dual phase steel, Mo other interpolation elements relatively has many good qualities: at first, because the standard Gibbs free energy of formation of Mo oxide compound is than the height of oxide compounds such as Mn, Si, P, so when pot galvanize is annealed, be difficult for surface oxidation takes place, there is not the surface segregation phenomenon yet, therefore can not influence the wetting property of zinc liquid; Secondly, Mo can not postpone the alloying reaction of galvanized sheet, and it can be carried out at a lower temperature, thereby can reduce the efflorescence amount that reaches coating mutually in the alloying coating; At last, add Mo the CCT curve is obviously moved to right, and enlarge the ferrite zone, thereby perlitic transformation takes place when having avoided cooling, help in Continuous Hot Dip Galvanizing Line, successfully obtaining the martensite dual-phase steel tissue.
Cr: be preferably molybdenum 0.20%～0.40%, replace Si, Mn with part.Cr is middle strong carbide forming element, significantly improves the hardening capacity of steel, can not only postpone perlitic transformation and bainite transformation strongly, and has enlarged " batching window ".Though Cr is weak solution strengthening element, can increase and austeniticly cross cold energy power, thereby thinning microstructure, effect is strengthened.Cr is the effective elements of temperature range that enlarges austenite metastable region window.
Al: when aluminium heats the critical zone influence of austenite form similar to Si, Al can also form AlN and separate out, and plays certain crystal grain thinning effect.
Nb: niobium is a kind of strong carbide forming element, the avidity of niobium and carbon is greater than vanadium, niobium commonly used carries out microalloying in ferrous materials, mainly be to utilize niobium to combine to form dispersing carbide with carbon, this carbide formation temperature that contains niobium is higher, may in high-temperature molten steel, exist, and its lattice parameter is close with austenite, can be used as austenitic crystallization nuclei, the niobium that adds trace can thinning solidification structure, in heat treatment process, separate out niobium carbide in addition and generally be the small and dispersed distribution, help dispersion-strengthened, and can stop high temperature austenite to be grown up.
Ti: the effect of titanium is similar to niobium, is the strong carbide element, helps crystal grain thinning.
S: sulphur is as remnants and harmful element, and is except the machinability that can improve steel, all very unfavorable to extension, impelling strength and the hot-work of steel.So S must be controlled at below 0.008%.
P: phosphorus is a kind of harmful element, has seriously destroyed the impelling strength of steel, and is also unfavorable to the hot-work and the weldability of steel.Equally, P also will be strict controlled in below 0.015%.
Preparation technology of the present invention is: at first smelt according to designing chemical composition, casting ingot forges into slab, carries out hot rolling, and hot rolling finishing temperature is 800～900 ℃, and preferred finishing temperature is 860～890 ℃, and coiling temperature is 600～700 ℃; Hot-rolled sheet is cold rolling one-tenth cold rolled sheet after overpickling, and cold rolling draft selects 60%～75%; Cold-rolled steel sheet is made steel plate after simulating zinc-plated annealing, annealing temperature is 780～840 ℃, and annealing time is 40～100s, and the speed of cooling CR1 that is chilled to zinc pond temperature from annealing temperature is 10～20 ℃/s; Zinc-plated section temperature is 450～470 ℃, and the zinc-plated time is 5～20s, and the speed of cooling CR2 after zinc-plated is that 8～20 ℃/s is cooled to room temperature, thereby obtains the cold rolling hot dip galvanizing dual phase steel of 1000MPa level.
The preferred finishing temperature of the present invention is 860～880 ℃, and preferred hot rolling reeling temperature is 650～690 ℃; Preferred annealing temperature is 800～830 ℃; Preferred annealing time is 40～80s; Cooling rate CR1 from annealing temperature to zinc pond temperature is preferably 12～17 ℃/s; The zinc-plated time is preferably 5～10s; Speed of cooling CR2 after zinc-plated is preferably 10～15 ℃/s.
Description of drawings
Fig. 1 is an annealing process synoptic diagram of the present invention.
Embodiment
The embodiments of the invention chemical ingredients is as shown in table 1.
Table 1 chemical ingredients (mass percent)
| Numbering | C | Si | Mn | P | S | Al | Cr | Mo | Nb | Ti | N |
| 1 | 0.12 | 0.05 | 1.81 | 0.006 | 0.005 | 0.01 | 0.33 | 0.33 | 0.026 | 0.015 | 0.0035 |
| 2 | 0.10 | 0.05 | 1.90 | 0.010 | 0.004 | 0.02 | 0.40 | 0.30 | 0.030 | 0.016 | 0.0040 |
Table 2 main technologic parameters and mechanical property
| Embodiment | Annealing temperature/℃ | Soaking time/s | Surrender strong/MPa | Tensile strength/MPa | Yield tensile ratio | Unit elongation |
| 1 | 820 | 80 | 598 | 1022 | 0.58 | 9.5％ |
| 2 | 820 | 40 | 688 | 1156 | 0.59 | 10.0％ |
| 3 | 820 | 60 | 655 | 1084 | 0.60 | 11.3％ |
| 4 | 820 | 80 | 680 | 1106 | 0.60 | 12.2％ |
The recrystallization annealing temperature of dual phase steel of the present invention is preferably 820 ℃ as shown in Figure 1.Temperature is too low, and carbide is not dissolved in the austenite fully, influences the ductility of hardening capacity and substrate, and the Ovshinsky scale of construction reduces simultaneously, and martensite volume also reduces thereupon, and then influences intensity.And annealing temperature raises, and the content of austenite interalloy element and C descends, and also can influence its hardening capacity.
Soaking time of the present invention is 80s.Soaking time is too short, and the Ovshinsky scale of construction of generation is very few, and in process of cooling subsequently, the martensite volume fraction is also few, and then intensity does not reach 1000MPa; And soaking time prolongs, and can increase production cost.On general industry is produced, should under the prerequisite that guarantees the dual phase steel superperformance, adopt short soaking time as far as possible.
Speed of cooling CR1 from annealing temperature to zinc pond temperature is greater than 12 ℃.Cooling rate is too small, and perlitic transformation takes place easily, reduces the intensity of substrate; The excessive bainite that generates easily again of cooling rate influences the ductility of substrate.Speed of cooling CR2 after zinc-plated is preferably more than 10 ℃/s.The little easy generation bainite transformation of cooling rate produces non-martensite microstructure, reduces the intensity of substrate.
Claims (8)
1. a 1000MPa grade cold rolling hot dip galvanizing dual phase steel is characterized in that the chemical ingredients mass percent is: C:0.10～0.12, Si≤0.06%, Mn:1.81～1.90, Mo:0.30～0.33, Cr:0.33～0.40, Al:0.01～0.02, Nb:0.026～0.030, Ti:0.015～0.016, P≤0.02%, S≤0.01%, N≤0.005%; Surplus is iron and inevitable impurity.
2. method of making the described hot dip galvanized dual phase steel of claim 1: preparation technology is: it is characterized in that, at first smelt according to the chemical ingredients of design, casting ingot forges into slab, carries out hot rolling, hot rolling finishing temperature is 800～900 ℃, and coiling temperature is 600～700 ℃; Hot-rolled sheet is cold rolling one-tenth cold rolled sheet after overpickling, and cold rolling draft selects 60%～75%; Cold-rolled steel sheet is made steel plate after simulating zinc-plated annealing, annealing temperature is 780～840 ℃, and annealing time is 40～100s, and the speed of cooling CR1 that is chilled to zinc pond temperature from annealing temperature is 10～20 ℃/s; Zinc-plated section temperature is 450～470 ℃, and the zinc-plated time is 5～20s, and the speed of cooling CR2 after zinc-plated is that 8～20 ℃/s is cooled to room temperature, thereby obtains the cold rolling hot dip galvanizing dual phase steel of 1000MPa level;
The chemical ingredients mass percent is: C:0.10～0.12, Si≤0.06%, Mn:1.81～1.90, Mo:0.30～0.33, Cr:0.33～0.40, Al:0.01～0.02, Nb:0.026～0.030, Ti:0.015～0.016, P≤0.02%, S≤0.01%, N≤0.005%; Surplus is iron and inevitable impurity.
3. manufacture method as claimed in claim 2 is characterized in that, finishing temperature is 860～880 ℃.
4. manufacture method as claimed in claim 2 is characterized in that, the hot rolling reeling temperature is 650～690 ℃.
5. manufacture method as claimed in claim 2 is characterized in that, annealing temperature is 800～830 ℃, and annealing time is 40～80s.
6. manufacture method as claimed in claim 2 is characterized in that, the cooling rate CR1 from annealing temperature to zinc pond temperature is 12～17 ℃/s.
7. manufacture method as claimed in claim 2 is characterized in that, the zinc-plated time is 5～10s.
8. manufacture method as claimed in claim 2 is characterized in that, the speed of cooling CR2 after zinc-plated is 10～15 ℃/s.
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