CN101096739A - Stamping high-strength heating galvanized steel with excellent welding performance and method for manufacturing the same - Google Patents
Stamping high-strength heating galvanized steel with excellent welding performance and method for manufacturing the same Download PDFInfo
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- CN101096739A CN101096739A CNA2006100282450A CN200610028245A CN101096739A CN 101096739 A CN101096739 A CN 101096739A CN A2006100282450 A CNA2006100282450 A CN A2006100282450A CN 200610028245 A CN200610028245 A CN 200610028245A CN 101096739 A CN101096739 A CN 101096739A
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- 229910001335 Galvanized steel Inorganic materials 0.000 title claims abstract description 12
- 239000008397 galvanized steel Substances 0.000 title claims abstract description 12
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 12
- 238000000034 method Methods 0.000 title claims abstract description 12
- 238000010438 heat treatment Methods 0.000 title claims abstract description 7
- 238000003466 welding Methods 0.000 title abstract description 5
- 229910052799 carbon Inorganic materials 0.000 claims abstract description 17
- 238000000137 annealing Methods 0.000 claims abstract description 14
- 238000005098 hot rolling Methods 0.000 claims abstract description 11
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims abstract description 11
- 229910052742 iron Inorganic materials 0.000 claims abstract description 5
- 238000003723 Smelting Methods 0.000 claims abstract description 4
- 238000007670 refining Methods 0.000 claims abstract description 3
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims description 14
- 238000005097 cold rolling Methods 0.000 claims description 4
- 229910052751 metal Inorganic materials 0.000 claims description 3
- 239000002184 metal Substances 0.000 claims description 3
- 229910052729 chemical element Inorganic materials 0.000 claims description 2
- 238000005554 pickling Methods 0.000 claims description 2
- 229910052748 manganese Inorganic materials 0.000 abstract description 6
- 229910052698 phosphorus Inorganic materials 0.000 abstract description 5
- 229910052758 niobium Inorganic materials 0.000 abstract description 4
- 229910052710 silicon Inorganic materials 0.000 abstract description 4
- 229910052719 titanium Inorganic materials 0.000 abstract description 4
- 239000012535 impurity Substances 0.000 abstract description 3
- 238000005096 rolling process Methods 0.000 abstract description 3
- 239000002253 acid Substances 0.000 abstract 1
- 238000004140 cleaning Methods 0.000 abstract 1
- 238000007796 conventional method Methods 0.000 abstract 1
- 229910000831 Steel Inorganic materials 0.000 description 28
- 239000010959 steel Substances 0.000 description 28
- 239000011572 manganese Substances 0.000 description 21
- 239000010936 titanium Substances 0.000 description 11
- 239000000463 material Substances 0.000 description 10
- HCHKCACWOHOZIP-UHFFFAOYSA-N Zinc Chemical compound [Zn] HCHKCACWOHOZIP-UHFFFAOYSA-N 0.000 description 8
- 239000010955 niobium Substances 0.000 description 8
- 239000011701 zinc Substances 0.000 description 8
- 229910052725 zinc Inorganic materials 0.000 description 8
- 239000013078 crystal Substances 0.000 description 7
- 238000005516 engineering process Methods 0.000 description 7
- 238000010010 raising Methods 0.000 description 6
- 230000000052 comparative effect Effects 0.000 description 4
- 238000001953 recrystallisation Methods 0.000 description 4
- 239000006104 solid solution Substances 0.000 description 4
- 229910045601 alloy Inorganic materials 0.000 description 3
- 239000000956 alloy Substances 0.000 description 3
- 150000001875 compounds Chemical class 0.000 description 3
- 238000013461 design Methods 0.000 description 3
- 239000000203 mixture Substances 0.000 description 3
- 239000002244 precipitate Substances 0.000 description 3
- 238000012545 processing Methods 0.000 description 3
- 239000000047 product Substances 0.000 description 3
- 238000005728 strengthening Methods 0.000 description 3
- 229910020012 Nb—Ti Inorganic materials 0.000 description 2
- 229910001069 Ti alloy Inorganic materials 0.000 description 2
- DBIMSKIDWWYXJV-UHFFFAOYSA-L [dibutyl(trifluoromethylsulfonyloxy)stannyl] trifluoromethanesulfonate Chemical compound CCCC[Sn](CCCC)(OS(=O)(=O)C(F)(F)F)OS(=O)(=O)C(F)(F)F DBIMSKIDWWYXJV-UHFFFAOYSA-L 0.000 description 2
- 238000005275 alloying Methods 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 230000002349 favourable effect Effects 0.000 description 2
- AMWRITDGCCNYAT-UHFFFAOYSA-L hydroxy(oxo)manganese;manganese Chemical compound [Mn].O[Mn]=O.O[Mn]=O AMWRITDGCCNYAT-UHFFFAOYSA-L 0.000 description 2
- 239000004615 ingredient Substances 0.000 description 2
- 229910052757 nitrogen Inorganic materials 0.000 description 2
- 239000010703 silicon Substances 0.000 description 2
- 239000000126 substance Substances 0.000 description 2
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 1
- OAICVXFJPJFONN-UHFFFAOYSA-N Phosphorus Chemical compound [P] OAICVXFJPJFONN-UHFFFAOYSA-N 0.000 description 1
- 229910000676 Si alloy Inorganic materials 0.000 description 1
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 description 1
- 239000005864 Sulphur Substances 0.000 description 1
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 1
- 239000000853 adhesive Substances 0.000 description 1
- 230000001070 adhesive effect Effects 0.000 description 1
- 229910000905 alloy phase Inorganic materials 0.000 description 1
- 238000004458 analytical method Methods 0.000 description 1
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 239000011248 coating agent Substances 0.000 description 1
- 238000000576 coating method Methods 0.000 description 1
- 238000009749 continuous casting Methods 0.000 description 1
- 230000006866 deterioration Effects 0.000 description 1
- 238000011161 development Methods 0.000 description 1
- 238000009792 diffusion process Methods 0.000 description 1
- 238000005246 galvanizing Methods 0.000 description 1
- 239000007788 liquid Substances 0.000 description 1
- 239000011159 matrix material Substances 0.000 description 1
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 description 1
- 229910052760 oxygen Inorganic materials 0.000 description 1
- 239000001301 oxygen Substances 0.000 description 1
- 239000011574 phosphorus Substances 0.000 description 1
- 238000007747 plating Methods 0.000 description 1
- 238000004886 process control Methods 0.000 description 1
- 238000005204 segregation Methods 0.000 description 1
- 239000000243 solution Substances 0.000 description 1
- 229910052717 sulfur Inorganic materials 0.000 description 1
- 238000004381 surface treatment Methods 0.000 description 1
- 238000012360 testing method Methods 0.000 description 1
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Abstract
The invention relates to a high-intensity hot-dip galvanized steel with good weld ability for stamping and the manufacturing method, which solves the technique problem of the prior high-intensity hot-dip galvanized steel without the high intensity, the good stamping and the good weld ability. The high-intensity hot-dip galvanized steel comprises the following parts: 0.005%-0.015%C, <=0.2% Si, 0.5%-1.5% Mn, <=0.015% P, 0.01%-0.10% Al, 0.03%-0.10%Ti, 0.005%-0.02%Nb, the rest Fe and unavoidable impurity. The method comprises the following steps: preconditioning iron melt; smelting by changing the furnace; refining; hot-rolling; cleaning with the acid; rolling coldly; annealing; getting the product coil ( the heating temperature is less than 1270Deg. C, the final rolling temperature is more than 860Deg. C, the welding temperature is from 580Deg. C to 680Deg. C, the annealing temperature is from 750Deg. C to 850Deg. C, the other proceeds according to the conventional technique). The invention is used for the parts of the cars.
Description
Technical field: the present invention relates to a kind of hot-galvanized steel and manufacture method thereof, particularly a kind ofly be used to make automobile with excellent weldability, good high-strength hot-dip zinc-coated steel and the manufacture method thereof of stampability.
Background technology:
Along with developing of automobile industry, people are to the raising of automobile environment-protection consciousness, have lightness and security, processibility requires the material development very fast, such material had both required certain intensity, require deep drawability good simultaneously, deep-draw high-strength steel in the past mainly is to add Si on the IF steel matrix, Mn, elements such as P improve intensity can reach 390Mpa, the 440Mpa level, but owing to a large amount of add alloys to have brought for coating surface quality and deep drawability unfavorable, also unfavorable to welding simultaneously, heavy addition Mn in the past particularly, high-strength IF steel about the 440Mpa of chemical ingredientss such as P is difficult to satisfy the user of welding requirements strictness.The high-strength hot-dip zinc-coated steel of external manufacturer production its composition weight percent by analysis is C:0.002%, Si:0.05%, Mn:1.8%, P:0.095%, S:0.007%, Al:0.047%, Ti:0.026%, Nb:0.02%, all the other are iron and unavoidable impurities.This high-strength galvanizing production mainly adopts high Mn (greater than 1.5%), high P (greater than 0.06%) solution strengthening, and this sample ingredient is the cost height not only, and processing characteristics, weldability, surface quality etc. are all relatively poor by contrast.And its carbon adopts Ultra-low carbon, the also corresponding increase of feasible smelting difficulty.
Summary of the invention: the purpose of this invention is to provide a kind of be used to make automobile excellent weldability, good high-strength hot-dip zinc-coated steel and the manufacture method thereof of stampability.Solve mainly that existing high-strength hot-dip zinc-coated steel can't guarantee to have high strength simultaneously, the technical problem of good deep drawing quality, good weldability.The weight percent of its chemical element moiety of high-strength hot-dip zinc-coated steel is:
C：≤0.005％~0.015％
Si：≤0.2％
Mn：0.5％~1.5％
P：0.02％~0.07％
S：≤0.015％
Al：0.01％~0.10％
Ti：0.03％~0.10％
Nb：0.005％~0.02％
All the other are iron and unavoidable impurities.
Automobile high-strength hot-galvanized steel manufacture method, is processed into the finished product volume through pot galvanize at, hot rolling concise behind hot metal pretreatment, converter smelting, stove by the said ratio material, pickling, cold rolling, annealing.Controlling hot rolling wherein: Heating temperature≤1270 ℃, finishing temperature: 〉=860 ℃, coiling temperature 〉=580 ℃～680 ℃; Annealing temperature: 750 ℃～850 ℃; Other routinely technology carry out.The performance that obtains product is: tensile strength: 390Mpa ~ 490Mpa, r 〉=1.4.
Composition design of the present invention and controlling of production process principle are: because the automobile high-strength hot-galvanized steel not only needs certain intensity, and characteristics such as stampability, superior weldability, secondary processing embrittlement temperature that need be good be low, great surface quality, according to this characteristic and requirement, key design one cover chemical ingredients, hot rolling, cold rolling, annealed technology are to reach certain material pressworkability and good surface quality, abide by (1) formula in order to ensure the design of excellent weldability material composition simultaneously and carry out, carbon equivalent (Pcm) should be less than 0.24%.
Pcm＝C+Si/30+Mn/20+2P+4S (1)
Therefore steel grades control principle of the present invention is as follows:
Carbon: add C at steel grade and can improve intensity, but the increase of the C of solid solution can make the r value descend significantly, so technology should reduce carbon content in the steel for high-strength IF steel in the past as far as possible.Thereby the present invention replaces alloy to add raising weldability, favourable surface imperfection minimizing etc. to add trace carbon.But too high stampability of carbon and weldability variation, so carbon can not be too high.The present invention's corresponding raisings Ti alloy content when increasing along with carbon in addition, if carbon content is too high, corresponding Ti alloy adds too much, and is also unfavorable to material property, cost.Therefore carbon is controlled at 0.005 ~ 0.015%.
Manganese: Mn is bigger to the tension intensity effect, along with the raising intensity increase of Mn.Mn and C coexistence form the C-Mn dipole check thereby the generation of 111} texture nuclear hinders growing up of crystal grain, and Mn separates out to react with oxygen on steel plate and generates MnO, that is: Mn+H
2O=MnO+H
2, manganese oxide generates thick more also big more to galvanized influence, the bonderizing variation, and the Mn addition is how unfavorable to weldability simultaneously, and Mn adds many more r values low more (situation that particularly has C).For this reason in the adding that guarantees to reduce under the intensity prerequisite Mn as far as possible.
Phosphorus: P is cheap strengthening element, and P is little to r value influence, to r value influence degree less than Mn, and bigger to intensity effect since IF steel crystal boundary a little less than, add P segregation on crystal boundary, precipitate is FePTi, so it is unfavorable and bring secondary embrittlement problem to unit elongation too much to add affiliation.P interpolation simultaneously is too much unfavorable to welding and alloying efficient.
Silicon: Si is a strengthening element, and Si high strength more is high more, but the high more r value of Si is low more, and moreover and can separate out at surface of steel plate and produce oxide film and influence surface treatment, and Si generates SiO at surface of steel plate
x, SiO
xThe increase of growing amount reduces the moistening adhesive tension of steel plate and liquid zinc.Si interpolation simultaneously is too much unfavorable to weldability, makes Si content few as far as possible so the present invention controls the Si alloy.Silicon is smaller or equal to 0.2%.
Sulphur: S is bigger to weldability influence, so that S will try one's best is low.General S is controlled at below 0.015%.
Titanium: Ti adds as the alloy of fixation of C, N element, and Ti＞3.4 * N+1.5 * S+4 * C just can accomplish to eliminate interstitial atom, and it is favourable to processing characteristics to remain some Ti, but Ti can not be too high, otherwise unfavorable to hot-dip galvanized alloyization, bonderizing etc.
Cross and take advantage of Ti
*: Ti
*(4 * C+3.4 * N+1.5 * S)＞0 (2) for=Ti-
Calculate the Ti controlled contents according to (2) formula.
Niobium: material of the present invention adopts the compound addition manner of Nb-Ti, and purpose reduces DBTT, and Nb-Ti compound IF steel has lower DBTT than conventional Ti-IF steel.Simultaneously because residual solid solution carbon on the Nb-Ti-IF steel crystal boundary, stoped to resemble the Ti-IF iron from the rapid diffusion of crystal boundary, thereby than the control of Ti-IF steel alloying easily, but recrystallization temperature improves the material property deterioration along with Nb increases simultaneously.Therefore Nb generally is controlled at 0.005% ~ 0.02%.
Steel grade of the present invention is made slab through continuous casting, then carries out hot rolling.Hot rolling, cold-rolling process control principle are as follows:
(1) finishing temperature:
Rolling and cause organizing the generation of mixed crystal in order not make material enter two-phase region, finishing temperature requires more than Ar3, 〉=860 ℃;
(2) coiling temperature:
Low solid solution Nb of coiling temperature and tiny NbC and AL, N influence recrystallization temperature, be that solid solution Nb spread coefficient is little, thereby the mobile difficulty of recrystallization nucleus, the tiny precipitate that distributes of disperse simultaneously suppresses moving of crystal boundary, improving coiling temperature can make precipitate separate out and grow up, recrystallization temperature is reduced, thereby intensity reduce, unit elongation improves.But coiling temperature is too high, and is bigger to the product intensity influence.General coiling temperature is controlled at 580 ℃ ~ 680 ℃.
(3) annealing temperature:
Along with annealing temperature reduces tensile strength raising, n value, the reduction of r value.In order to prevent that the zinc layer from not plating and reduce not galvanized size, preferably annealing temperature is too not low, at high density H
2Oxide compound along with annealing temperature raising Mn under the condition is reduced into metal M n, generally easily is reduced to MnO more than 750 ℃, thereby reduces not zinc-plated.So it is 750 ℃～850 ℃ that the present invention controls annealing temperature.
The invention has the beneficial effects as follows: the present invention is by controlling a certain amount of carbon content, add a certain amount of Ti and Nb simultaneously, because TiC, NbC disperse distribute and make grain refining and dispersion-strengthened obtain the high-strength hot-dip zinc-coated steel greater than 390Mpa, significantly reduce the interpolation of Mn, P, thereby avoided the influence of the interpolation of high Mn, P the material weldability.Stamping high-strength hot-galvanized steel of the present invention has characteristics such as good weldability, good stampability, anti-secondary workability, great surface quality.The present invention add alloy phase to less, produce easily, steady quality, be fit to all kinds of producers suitability for industrialized production.
Description of drawings:
Accompanying drawing is tensile strength 440Mpa level steel of the present invention and comparative steel Pcm contrast.
Embodiment: three embodiment of the present invention and a comparative example see the following form 1:
| Project | C | Si | Mn | P | S | Al | Ti | Nb | Pcm | Unit elongation | Tensile strength | r |
| ％ | ％ | ％ | ％ | ％ | ％ | ％ | ％ | ％ | ％ | Mpa | ||
| The present invention | 0.005 ～ 0.015 | ≤0.2 | 0.5 ～ 1.5 | 0.02~ 0.07 | ≤ 0.015 | 0.01 ～ 0.10 | 0 03 ～ 0.10 | 0.005~ 0.02 | ≤ 0.24 | |||
| Embodiment A | 0.012 | 0.12 | 0.8 | 0.060 | 0.008 | 0.056 | 0.065 | 0.010 | 0.21 | 36 | 462 | 1.65 |
| Embodiment B | 0.008 | 0.18 | 1.1 | 0.062 | 0.005 | 0.041 | 0.061 | 0.015 | 0.21 | 37 | 451 | 1.57 |
| Embodiment C | 0.008 | 0.08 | 0.7 | 0.060 | 0.004 | 0.053 | 0.067 | 0.020 | 0.18 | 39 | 397 | 1.78 |
| Comparative steel | 0.002 | 0.05 | 1.8 | 0.095 | 0 007 | 0.047 | 0.026 | 0.020 | 0.31 | 35 | 448 | 1.35 |
The technology controlling and process of embodiment A is: controlling hot rolling: Heating temperature :≤1270 ℃, and finishing temperature: 860 ℃, coiling temperature: 600 ℃; 770 ℃ of annealing temperatures.
The technology controlling and process of Embodiment B is: controlling hot rolling: Heating temperature :≤1270 ℃, and finishing temperature: 930 ℃, coiling temperature: 650 ℃; 820 ℃ of annealing temperatures.
The technology controlling and process of Embodiment C is: controlling hot rolling: Heating temperature :≤1270 ℃, and finishing temperature: 890 ℃, coiling temperature: 680 ℃; 840 ℃ of annealing temperatures.
Hardness in the table 1 and tensile property adopt general GB standard testing.Steel of the present invention and comparative steel Pcm contrast are with reference to accompanying drawing.
Claims (3)
1, a kind of stamping high-strength hot-galvanized steel of excellent weldability, the weight percent of its chemical element moiety is:
C：≤0.005％~0.015％
Si：≤0.2％
Mn：0.5％~1.5％
P：0.02％~0.07％
S：≤0.015％
Al：0.01％~0.10％
Ti：0.03％~0.10％
Nb：0.005％~0.02％
All the other are iron and inevitably are mingled with.
2, the stamping high-strength hot-galvanized steel of excellent weldability according to claim 1 is characterized in that, carbon equivalent Pcm is less than 0.24%, Pcm=C+Si/30+Mn/20+2P+4S.
3, the manufacture method of the stamping high-strength hot-galvanized steel of the described excellent weldability of claim 1, may further comprise the steps: hot metal pretreatment, converter smelting, furnace rear refining, hot rolling, pickling, cold rolling, annealing, pot galvanize, be processed into finished product volume, it is characterized in that: hot rolling Heating temperature≤1270 ℃, finishing temperature is controlled at 〉=and 860 ℃, 580 ℃～680 ℃ of coiling temperatures, annealing temperature are controlled at 750 ℃～850 ℃.
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| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CNB2006100282450A CN100473743C (en) | 2006-06-28 | 2006-06-28 | Stamping high-strength heating galvanized steel with excellent welding performance and method for manufacturing the same |
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| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CNB2006100282450A CN100473743C (en) | 2006-06-28 | 2006-06-28 | Stamping high-strength heating galvanized steel with excellent welding performance and method for manufacturing the same |
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| Publication Number | Publication Date |
|---|---|
| CN101096739A true CN101096739A (en) | 2008-01-02 |
| CN100473743C CN100473743C (en) | 2009-04-01 |
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Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102154586A (en) * | 2011-01-29 | 2011-08-17 | 首钢总公司 | Method for preventing surface of Ti-IF steel from forming crack defects |
| CN102787271A (en) * | 2012-07-17 | 2012-11-21 | 马钢(集团)控股有限公司 | Production method of 460MPa grade high-surface quality structural hot dipped galvanized steel plate and its product |
| CN105510093A (en) * | 2014-09-24 | 2016-04-20 | 上海宝钢工业技术服务有限公司 | Non-aging hardness standard sample production method |
| CN107829030A (en) * | 2017-11-13 | 2018-03-23 | 北京首钢冷轧薄板有限公司 | A kind of 440MPa levels cold-strip steel and its production method |
-
2006
- 2006-06-28 CN CNB2006100282450A patent/CN100473743C/en active Active
Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102154586A (en) * | 2011-01-29 | 2011-08-17 | 首钢总公司 | Method for preventing surface of Ti-IF steel from forming crack defects |
| CN102787271A (en) * | 2012-07-17 | 2012-11-21 | 马钢(集团)控股有限公司 | Production method of 460MPa grade high-surface quality structural hot dipped galvanized steel plate and its product |
| CN105510093A (en) * | 2014-09-24 | 2016-04-20 | 上海宝钢工业技术服务有限公司 | Non-aging hardness standard sample production method |
| CN107829030A (en) * | 2017-11-13 | 2018-03-23 | 北京首钢冷轧薄板有限公司 | A kind of 440MPa levels cold-strip steel and its production method |
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