CN102758143A - Hot-dip galvanized steel sheet with tensile strength higher than 1180MPa, and manufacturing method thereof - Google Patents
Hot-dip galvanized steel sheet with tensile strength higher than 1180MPa, and manufacturing method thereof Download PDFInfo
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- CN102758143A CN102758143A CN201110103690XA CN201110103690A CN102758143A CN 102758143 A CN102758143 A CN 102758143A CN 201110103690X A CN201110103690X A CN 201110103690XA CN 201110103690 A CN201110103690 A CN 201110103690A CN 102758143 A CN102758143 A CN 102758143A
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Abstract
The invention discloses a hot-dip galvanized steel sheet with tensile strength higher than 1180MPa. The hot-dip galvanized steel sheet comprises chemical components of, by weight: 0.08-0.12% of C; 0.50-1.50% of Si; 1.80-2.5% of Mn; 0.1-0.8% of Cr; no more than 0.5% of Mo; 0.005-0.05% of Nb; 0.005-0.05% of Ti; 0.02-0.05% of T.Al; 0.006-0.02% of P; no more than 0.01% of S; and balance of Fe and inevitable impurities. A microstructure of a substrate is ferrite + martensite, wherein the content of martensite is 40-60wt%. Correspondingly, the invention discloses a manufacturing method of the hot-dip galvanized steel sheet. According to the invention, a unique hot-dip galvanizing annealing process is adopted, and the strength of the galvanized steel sheet is substantially improved.
Description
Technical field
The invention belongs to the hot-dip galvanizing sheet steel preparing technical field, belong to superelevation heat-flash steel plate galvanized and preparation method thereof or rather.
Background technology
High-strength hot-dip zinc-coated steel sheet is a kind of application metallurgic product very widely, because its intensity is high, through being usually used in automobile manufacturing field, as is used to make automobile structure, anti-striker etc.At present, the intensity rank of high-strength hot-dip zinc-coated steel sheet has 590MPa, 780MPa, 800MPa, 980MPa, 1000MPa etc.
Open day is on February 25th, 2009, and publication number is EP 2028282A1, and name is called " a kind of dual phase steel and adopt steel plate that this dual phase steel makes and the method for manufacture of this steel plate " (Dual-phase steel; Flat product made of such dual-phase steel and method for manufacturinga flat product) european patent document discloses a kind of dual phase steel; 0.12～0.18% C is arranged in this steel, and 0.2～0.4% Si also adds a small amount of B simultaneously; Anneal through pot galvanize; The minimum 580MPa that reaches of ys, tensile strength can reach 1000MPa, and unit elongation (A80) can reach 10%.
Open day is on October 19th, 2006; Publication number is JP 2006283071A; The Japanese documentation that name is called " method of manufacture of pot galvanize high tensile steel plate " (METHOD FOR PRODUCING GALVANNEALED HIGHSTRENGTH STEEL SHEET EXCELLENT IN WORKABILITY) discloses a kind of method of manufacture of hot dip galvanized dual phase steel; Si content is higher in the chemical ingredients of this hot dip galvanized dual phase steel; Utilize in the hot galvanizing process and advance the zinc pot before at surface of steel plate flash one deck very thin Ni and Ni-Fe alloy layer, improved the plating leakage phenomenon that steel plate causes because of alloying element Si, Mn surface enrichment at the band steel.
Open day is on February 23rd, 2006; Publication number is JP 2006052445A; The Japanese documentation that name is called " device of making hot dip galvanized high strength steel sheet " (APPARATUS FOR MANUFACTURING HOT-DIPGALVANIZED HIGH-TENSILE-STRENGTH STEEL SHEET) discloses a kind of equipment that has the high speed cooling power that can take into account production TRIP steel and DP steel; Its speed of cooling can be produced different types of advanced high-strength steel at 10～100 ℃/s through adopting different cooling.
Open day is on June 7th, 2006; Publication number is CN1782116; The Chinese patent document that name is called " a kind of 800MPa cold rolling hot dip galvanizing dual phase steel and method of manufacture thereof " discloses a kind of dual phase steel of the Si of nothing alloying element; It is 5～16 ℃/s through the average cooling rate from annealing soaking temperature zinc liquid temperature to the zinc pond, go out the zinc pot after cooling rate greater than 7 ℃/s, can access the dual phase steel of tensile strength greater than the low yield strength ratio of 800MPa.
Summary of the invention
The purpose of this invention is to provide hot-dip galvanizing sheet steel and the method for manufacture thereof of a kind of tensile strength greater than the 1180MPa level, this hot-dip galvanizing sheet steel that makes through this method has superpower tensile strength, and cheap for manufacturing cost, is Eco-power super-high strength steel plate.
According to the foregoing invention purpose, the invention provides the hot-dip galvanizing sheet steel of a kind of tensile strength greater than 1180MPa, the chemical constitution weight percent proportioning of the substrate of said hot-dip galvanizing sheet steel is:
C：0.08～0.12％
Si：0.50～1.50％
Mn：1.80～2.5％
Cr：0.1～0.8％
Mo：≤0.5％
Nb：0.005～0.05％
Ti：0.005～0.05％
T.Al：0.02～0.05％
P：0.006～0.02％
S：≤0.01％
Surplus is Fe and other unavoidable impurities;
The microtexture of said substrate is ferritic+martensite, and wherein martensitic content is 40～60wt%.
Preferably, the P:0.006 of the substrate of said hot-dip galvanizing sheet steel～0.01%, S≤0.006%.
Correspondingly, the present invention also provides the method for manufacture of this tensile strength greater than the hot-dip galvanizing sheet steel of 1180MPa, and it comprises the following steps:
(1) raw material is smelted and refining, cast the substrate slab then;
(2) hot rolling of substrate slab, acid are rolled;
(3) carry out the zinc-plated annealing of substrate heat according to following step:
(3a) adopt the mode of straight fire heating that substrate is heated to 500～750 ℃ at preheating section;
(3b) adopt the mode of radiator tube heating substrate to be continued to be heated to 760～840 ℃ of soaking temperatures, soaking slow cooling then (traditional technology that soaking in the present technique scheme and retarded cooling process all adopt);
(3c) substrate being carried out speed of cooling is that the high hydrogen of 40～150 ℃/s is jet cold soon;
(3d) immerse in the zinc pot substrate zinc-plated;
(3e) hot-dip galvanizing sheet steel adopts aerosol to cool off quick cooling zone steel after going out the zinc pot at once, and speed of cooling is 20～300 ℃/s.
Preferably, the soaking temperature in the said step (3b) is 780～820 ℃.
Preferably, it is jet cold soon to adopt in the said step (3c) hydrogen content to be that the shielding gas of 80～90% (volume percent) carries out high hydrogen.
Preferably, the zinc pot temperature in the said step (3d) is 450～465 ℃.
The principle of design of the chemical composition of hot-galvanized steel base board is following in the present technique scheme:
C is important solution strengthening element, is that steel plate obtains high-intensity assurance.When C content is too low; Ovshinsky scale of construction when same critical annealing is heated in ferritic and the austenite two-phase region reduces, and the also corresponding minimizing of the martensite volume that obtains is difficult to guarantee that tensile strength is greater than 1180MPa; The words that guarantee its intensity then will be added more alloying element, have increased cost; When C content is too high, toughness can be reduced on the one hand, also weldableness can be influenced on the other hand.
Si is a ferritic solution strengthening element, and it can improve intensity strongly, but generally for hot dip galvanized dual phase steel; Can directly influence the platability of substrate when Si content is too high, technical scheme of the present invention can be eliminated the detrimentally affect of Si element to platability through adopting unique annealing process; The feasible content that can suitably improve Si element in the hot dip galvanized dual phase steel; Corresponding expensive Cr and the content of Mo of reducing further reduces cost, and improves unit elongation.
Mn can improve the hardening capacity of steel strongly, improves work hardening ability.For the present technique scheme, Mn content is crossed when hanging down, and is difficult to form the martensite of q.s, causes strengthening effect poor, can influence the weldableness of substrate when too high.
The hardening capacity of supercooled austenite when Cr can improve critical annealing when the C content in the steel grade increases, can further increase martensite quantity, and in addition, Cr can promote that C spreads to austenite, reduces ferritic ys simultaneously.But the Cr of too high levels will destroy the ductility of steel.
Mo is a carbide forming element, and most dissolvings can improve austenitic hardening capacity very effectively 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 cause the increase of production cost.
Ti and Nb:Ti are the strong carbide forming elements, and the effect of tangible precipitation strength and the effect of crystal grain thinning are arranged.The effect of Nb is similar with Ti, but stronger than Ti, and price is also higher, and Nb, Ti element are not dominant element in dual phase steel, and content is unsuitable too high.
The major function of Al in dual phase steel is reductor, should not be low excessively, but can influence continuous casting production when too high.
P is a kind of inexpensive solution strengthening element, and as far as the present technique scheme, an amount of P is useful to improving intensity, but too highly also can influence weldableness.
S be prone to form MnS in steel, cause hot-shortly, influences weldableness simultaneously, so few more good more.
The technological principle of the method for manufacture of hot-dip galvanizing sheet steel of the present invention is specific as follows:
Hot dip galvanized dual phase steel and cold-rolled biphase steel are having difference on the design of alloy: the annealing of cold-rolled biphase steel is that the thermal zone steel with austenitizing directly is cooled to below the Ms point; In the ferrous materials design of alloy mainly with add inexpensive Si, the Mn alloying element is main, to improve the hardening capacity of steel; And the substrate of hot dip galvanized dual phase steel is had to and will be carried out pot galvanize through the zinc liquid about 460 ℃ insulation; The supercooled austenite of high-strength steel substrate is prone to take place bainite transformation under this temperature; Significantly reduced the supercooled austenite that is used for martensitic transformation, so bring very big difficulty for the production of hot dip galvanized dual phase steel.So under conventional hot dip galvanizing production process condition, in order to reach intensity index, the substrate of hot dip galvanized dual phase steel need add the alloying element of q.s; Hardening capacity with further raising substrate; Satisfy the cooling curve requirement of superstrength dual phase steel, but Si in the hot dip galvanizing substrate, when Mn element addition is too much, in annealing process; Be prone to form the enrichment of Si, Mn alloying element at substrate surface; The wellability of substrate when influencing pot galvanize (reducing the platability of substrate) causes hot galvanizing surface defectives such as plating leakage, and this just need be with the Si in the partly alternative substrate of Cr, Mo element of costliness, Mn element to eliminate it in the detrimentally affect aspect the platability.So under traditional hot dip galvanizing annealing process condition, the alloying element content of hot dip galvanized dual phase steel will be apparently higher than the alloying element of cold-rolled biphase steel.In addition, owing to can not unrestrictedly add a large amount of alloying elements in the substrate, so the maximum intensity rank of pot galvanize also is restricted, the hardness of present hot dip galvanized dual phase steel plate both domestic and external all is lower than 1000MPa.
The preparation method of hot dip galvanized dual phase steel plate of the present invention; Adopt the mode of straight fire heating in the basal plate preheating stage (or being called first section heating zone); Be in order fast substrate to be heated to about 500～750 ℃; Purpose is to make substrate surface produce preoxidation (or being called low-level oxidation), hinders Si, the Mn alloying element enrichment at substrate surface, then in follow-up soaking and process of cooling, under the reducing atmosphere condition; Reduction is generated the good unsalted surface of wettability by the substrate surface of low-level oxidation.So method of manufacture of the present invention and common process compared with techniques; Improved the platability of the substrate of high-strength hot-dip zinc-coated dual phase sheet steel greatly; Like this when the composition design of carrying out steel grade; Can increase cheap Si, the interpolation of Mn alloying element, and reduce the interpolation of valuable alloying element (Cr, Mo), thereby realize the purpose that significantly reduces production costs.
The cooling step of method of manufacture of the present invention after soaking adopted the jet fast cold technology of high hydrogen; The speed of cooling of 40～150 ℃/s can fully be avoided " C " curve of substrate supercooled austenite; Strengthened the stability of substrate supercooled austenite tissue; Prevent that supercooled austenite is transformed into perlite and bainite structure in process of cooling; Thereby improved the hardening capacity of high-strength steel substrate supercooled austenite effectively, made supercooled austenite in last process of cooling, be transformed into intensity and the very high martensite of hardness more, made the interpolation that further reduces expensive alloy element become possibility.If this speed of cooling is too small, be easy to generate pearlitic transformation, reduce the intensity of substrate.And in the conventional method of manufacture, this speed of cooling has only 7～15 ℃/s, therefore can only improve the hardening capacity and the intensity of high-strength steel substrate through increase substrate expensive alloy element content, and the effect of its raising is limited.
Method of manufacture of the present invention adopts the quick cooling metal sheets of aerosol refrigerative mode at once after hot-dip galvanizing sheet steel goes out the zinc pot, its cooling rate is at 20～300 ℃/s.In general, the zinc liquid temperature in the zinc pot is 460 ℃, the band steel go out the zinc pot through air knife winding-up back temperature generally about 420 ℃, this just the supercooled austenite in the high-strength steel substrate be prone to the temperature range of generation bainitic transformation.The present technique scheme is through going out aerosol cooling at once behind the zinc pot at hot-dip galvanizing sheet steel; The substrate that has guaranteed hot-dip galvanizing sheet steel can effectively be avoided its bainite transformation temperature range; The supercooled austenite of being convenient in the substrate is cooled fast to below the Ms point; The martensitic transformation of expectation takes place, thereby significantly improves armor plate strength.
Do not produce the plating leakage defective in order to reduce coating surface, method of manufacture of the present invention adopts straight fire heating earlier at preheating section, and straight fiery Heating temperature scope is 500～750 ℃.If be lower than this TR, then straight fire burns DeGrain, and if be higher than this TR and can produce over oxidation, influence the substrate surface quality.Be heated to soaking temperature with common radiator tube type of heating again after the straight fire heating; And soaking temperature is the of paramount importance technological factor of performance of control hot-dip galvanizing sheet steel, in the present technique scheme soaking temperature is controlled at 760～840 ℃, because all thermal process is to accomplish at ferritic and austenite two-phase region; Therefore; If soaking temperature is too low, can cause carbide not to be dissolved into fully in the austenite, austenite quantity is also few; And can influence the ductility of austenitic hardening capacity and substrate, cause martensite quantity to reduce simultaneously and influence its intensity; If soaking temperature is too high; Along with austenitic volume(tric)fraction increases, the ferritic volume(tric)fraction of low C and low alloyed element content reduces, and must make that C content and the alloying element content in the austenite descends; Also can influence the hardening capacity of steel, the cooling back is prone to produce non-martensite microstructure.In the present technique scheme soaking temperature is controlled at 780～820 ℃ better.
Method of manufacture of the present invention through " straight fire heating+high hydrogen jet cold soon+plating after aerosol cold soon " process integration; Make that the addition of valuable alloying element reduces greatly in the substrate of hot-dip galvanizing sheet steel; Also improve the intensity of hot-dip galvanizing sheet steel simultaneously greatly, made the intensity of this hot-dip galvanizing sheet steel to reach more than the 1180MPa.In addition, it has also improved welding property, forming property and the surface quality of hot-dip galvanizing sheet steel.
Description of drawings
Fig. 1 is the process curve synoptic diagram of the pot galvanize annealing steps in the method for manufacture of hot-dip galvanizing sheet steel of the present invention.
Fig. 2 is the metallographic structure photo of substrate in embodiment 2 of hot-dip galvanizing sheet steel of the present invention.
Fig. 3 is the metallographic structure photo of substrate in embodiment 5 of hot-dip galvanizing sheet steel of the present invention.
The surface quality photo of Fig. 4 hot-dip galvanizing sheet steel of the present invention in embodiment 1.
Embodiment
Make hot-dip galvanizing sheet steel according to the following step, each detailed process parameter among the embodiment 1-5 and the product performance of doing kind are seen table 2:
(1) raw material is smelted and refining, cast the substrate slab then;
(2) hot rolling of substrate slab, acid are rolled;
(3) carry out the zinc-plated annealing of substrate heat according to process curve as shown in Figure 1:
Adopt the mode of straight fire heating that substrate is heated to 500～750 ℃ at preheating section A; The mode that adopts the radiator tube heating at heating zone B continues to be heated to 760～840 ℃ of soaking temperatures in soaking zone C soaking with substrate, and D carries out slow cooling in the slow cooling section then; Cooling section E adopt hydrogen content be 80～90vt% (volume percent (and shielding gas substrate is carried out the high hydrogen jet cold soon (adopting " 1CR " expression in the table 2) that speed of cooling is 40～150 ℃/s; Substrate is immersed in the zinc pot zinc-plated at zinc-plated section then; Hot-dip galvanizing sheet steel adopts ultrafine aerial fog going out zinc pot cooling section G rapid cooling thermal steel plate galvanized after going out the zinc pot at once, and speed of cooling is 20～300 ℃/s (adopting " 2CR " expression in the table 2).
The chemical element component of each substrate among the embodiment 1-5 is seen table 1.
Table 1. (surplus is Fe)
| Embodiment | C | Si | Mn | Cr | Mo | Nb | Ti | T.Al | P | S |
| 1 | 0.12 | 0.50 | 1.99 | 0.50 | 0.20 | 0.005 | 0.030 | 0.021 | 0.0088 | 0.0028 |
| 2 | 0.095 | 0.99 | 2.12 | 0.10 | 0.15 | 0.020 | 0.040 | 0.043 | 0.006 | 0.0017 |
| 3 | 0.095 | 1.48 | 2.45 | 0.45 | 0.24 | 0.014 | 0.050 | 0.036 | 0.0120 | 0.0031 |
| 4 | 0.082 | 0.55 | 1.80 | 0.60 | 0.45 | 0.015 | 0.060 | 0.025 | 0.010 | 0.01 |
| 5 | 0.080 | 0.72 | 1.95 | 0.75 | 0.05 | 0.045 | 0.005 | 0.045 | 0.02 | 0.0050 |
Table 2.
Can find out that from last table hot-dip galvanizing sheet steel tensile strength of the present invention can reach about 1200MPa, ys reaches more than the 800MPa, and has extraordinary ductility.
Can find out that from Fig. 2 and Fig. 3 the substrate microtexture of hot-dip galvanizing sheet steel is martensite+ferritic.
As can beappreciated from fig. 4, hot dip galvanized dual phase steel plate of the present invention has extraordinary surface quality.
Be noted that above enumerate be merely specific embodiment of the present invention, obviously the invention is not restricted to above embodiment, many similar variations are arranged thereupon.If those skilled in the art all should belong to protection scope of the present invention from all distortion that content disclosed by the invention directly derives or associates.
Claims (6)
1. a tensile strength is characterized in that greater than the hot-dip galvanizing sheet steel of 1180MPa the chemical constitution weight percent proportioning of the substrate of said hot-dip galvanizing sheet steel is:
C：0.08～0.12％
Si：0.50～1.50％
Mn：1.80～2.5％
Cr：0.1～0.8％
Mo：≤0.5％
Nb：0.005～0.05％
Ti：0.005～0.05％
T.Al：0.02～0.05％
P：0.006～0.02％
S：≤0.01％
Surplus is Fe and other unavoidable impurities;
The microtexture of said substrate is ferritic+martensite, and wherein martensitic content is 40～60wt%.
2. tensile strength as claimed in claim 1 is characterized in that greater than the hot-dip galvanizing sheet steel of 1180MPa: P:0.006～0.01%, S≤0.006%.
3. according to claim 1 or claim 2 tensile strength is characterized in that greater than the method for manufacture of the hot-dip galvanizing sheet steel of 1180MPa, comprises the following steps:
(1) raw material is smelted and refining, cast the substrate slab then;
(2) hot rolling of substrate slab, acid are rolled;
(3) carry out the zinc-plated annealing of substrate heat according to following step:
(3a) adopt the mode of straight fire heating that substrate is heated to 500～750 ℃ at preheating section;
(3b) adopt the mode of radiator tube heating that substrate is continued to be heated to 760～840 ℃ of soaking temperatures, soaking is slow cooling then;
(3c) substrate being carried out speed of cooling is that the high hydrogen of 40～150 ℃/s is jet cold soon;
(3d) immerse in the zinc pot substrate zinc-plated;
(3e) hot-dip galvanizing sheet steel adopts aerosol to cool off quick cooling zone steel after going out the zinc pot at once, and speed of cooling is 20～300 ℃/s.
4. tensile strength as claimed in claim 3 is characterized in that greater than the method for manufacture of the hot-dip galvanizing sheet steel of 1180MPa the soaking temperature in the said step (3b) is 780～820 ℃.
5. tensile strength as claimed in claim 4 is characterized in that greater than the method for manufacture of the hot-dip galvanizing sheet steel of 1180MPa, and it is jet cold soon to adopt hydrogen content to be that the shielding gas of 80～90% (volume percent) carries out high hydrogen in the said step (3c).
6. tensile strength as claimed in claim 5 is characterized in that greater than the method for manufacture of the hot-dip galvanizing sheet steel of 1180MPa the zinc pot temperature in the said step (3d) is 450～465 ℃.
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| JP2014005514A (en) * | 2012-06-26 | 2014-01-16 | Jfe Steel Corp | High-strength hot-dip galvanized steel sheet having excellent fatigue characteristic and ductility, and small in-plane anisotropy of ductility, and manufacturing method of the same |
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| JP2014005514A (en) * | 2012-06-26 | 2014-01-16 | Jfe Steel Corp | High-strength hot-dip galvanized steel sheet having excellent fatigue characteristic and ductility, and small in-plane anisotropy of ductility, and manufacturing method of the same |
| KR102100727B1 (en) | 2012-11-15 | 2020-04-14 | 바오샨 아이론 앤 스틸 유한공사 | High-formability and super-strength hot galvanizing steel plate and manufacturing method thereof |
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