CN102127704B - 900MPa-level high-strength high-plasticity medium-carbon hot rolled steel and manufacturing method thereof - Google Patents
900MPa-level high-strength high-plasticity medium-carbon hot rolled steel and manufacturing method thereof Download PDFInfo
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Abstract
The invention discloses 900MPa-level high-strength high-plasticity medium-carbon hot rolled steel and a manufacturing method thereof. The hot rolled steel comprises the following chemical components in percentage by weight: 0.45 to 0.80 percent of C, 20 to 30 percent of Mn, 0.01 to 0.20 percent of Si, 0.02 to 0.10 percent of Al, less than or equal to 0.015 percent of P, less than or equal to 0.015 percent of S and the balance of Fe and inevitable impurities. The manufacturing method of the hot rolled steel comprises the following steps of: smelting raw materials; casting a steel blank; heating a plate blank; performing hot rolling; and cooling, wherein the molten steel tapping end temperature for casting of the steel blank is controlled to be between 1,700 and 1,900 DEG C; the heating temperature of the plate blank is controlled to be between 1,150 and 1,230 DEG C; and the rough rolling temperature during hot rolling is controlled to be between 1,010 and 1,110 DEG C, the finished rolling temperature is controlled to be between 700 and 800 DEG C, and the coiling temperature is controlled to be between 500 and 600 DEG C. Practices prove that the steel has high strength, a high elongation rate, high impact work, a low brittle transition temperature and high welding performance and forming performance, and the manufacturing method of the hot rolled steel has a simple process flow and is low in production cost.
Description
Technical field
The invention belongs to the high-strength steel production technical field, refer to carbon HRS and method of manufacture thereof in a kind of 900MPa grade high-strength high-ductility particularly.
Background technology
About having the steel plate research of high-strength high-plasticity, mainly contain Thyssen Krupp iron and steel stock company, Usinor and Korea S HYUNDAI auto maker etc. abroad.Is " production possesses the method for the very high strength and the austenitic iron/carbon/manganese steel plate of elongation performance and excellent homogeneity " patent of invention of 200580042631.9 like Usinor at Chinese application number, discloses a kind of hot rolling austenitic iron/carbon/manganese steel plate, and its nominal chemical constitution comprises; Content is by weight: 0.85%≤C≤1.05%, 16%≤Mn≤19%, Si≤2%; Al≤0.05%, S≤0.03%, P≤0.50%; N≤0.1%, and optional one or more are selected from following element: Cr≤1%, Mo≤1.50%; Ni≤1%, Cu≤5%, Ti≤0.50%; Nb≤0.50%, V≤0.50%, the surplus of this composition is made up of the unavoidable impurities that the can melting produces.The intensity of this steel plate is greater than 1200MPa; Its product P (intensity (MPa) * elongation at break (%)) is greater than 65000MPa%; But this steel is regulated its microstructure and is caused production cost to increase through adding a large amount of alloying elements; And its carbon element content is higher, and steel plate plasticity-is on the low side, influences its range of application.Domestic one tame research institution discloses the patent of invention that name is called " ultra-low carbon twin crystal induction plastic steel of high-strength high-plasticity ", and its application number is 200810032388.8, this steel consist of C:0.005～0.03%; Si:2～3%, Mn:20～32%, Al:2～4%; Surplus is Fe; This steel through add high Si, high Al comes the balance stacking fault energy, makes it to produce twin crystal inducing plasticity, makes material finally reach the purpose of high-ductility.But, have so high Si and Al content in the steel plate, exist the steel-making of suitability for industrialized production and problem and the shortcoming that steel rolling is difficult to carry out, bring very large difficulty for steel-making and steel rolling, can stop up mold gap like steel-making, the hot rolling meeting produces severe edge fracture.Simultaneously, above-mentioned steel plate for the over-all properties heavy addition of regulating steel microalloy element, thereby the steel plate cost is risen significantly.
Summary of the invention
The object of the invention will provide carbon HRS and method of manufacture thereof in a kind of 900MPa grade high-strength high-ductility exactly.This steel has HS, high-elongation, HI high impact merit, low brittle transition temperature and good welding property and forming property, and its manufacturing approach craft flow process is simple, low production cost.
For realizing above-mentioned purpose, the present invention designs carbon HRS in the 900MPa grade high-strength high-ductility, and its chemical ingredients percentage ratio is by weight counted: C:0.45～0.80%; Mn:20～30%; Si:0.01～0.20%, Al:0.02～0.10%, P≤0.015%; S≤0.015%, surplus are Fe and unavoidable impurities.
Further, its chemical ingredients percentage ratio meter by weight is preferably: C:0.50～0.70%, and Mn:21.0～25.0%, Si:0.02～0.18%, Al:0.02～0.10%, P≤0.015%, S≤0.015%, surplus is Fe and unavoidable impurities.
The method of manufacture of carbon HRS is undertaken by common Clean Steel technology in the 900MPa grade high-strength high-ductility of the present invention, comprises the step of raw material smelting, casting steel billet, slab heating, hot rolling, processing under cooling, and its special character is:
The molten steel tapping end temp of said casting steel billet is controlled at 1700～1900 ℃;
Said slab heating temperature is controlled at 1150～1230 ℃;
The roughing temperature is controlled at 1010～1110 ℃ during said hot rolling, and finishing temperature is controlled at 700～800 ℃, and coiling temperature is controlled at 500～600 ℃.
Further, it is rolling in the hot rolling technology rolled piece to be carried out 5～7 passages.
The control soaking time was between 160～250min when further, slab heated.
The present invention is in order to guarantee the premium properties of high-strength HRS product, and carbon and high manganese element and minor amount of silicon content and small amount of aluminum element in the composition design of steel, adopting do not add other valuable alloy element.Wherein each constituent content qualification ultimate principle is following:
The C element can the stable austenite tissue and is utilized solid solution hardening to strengthen matrix.The solid solubility of C in austenite is than high many in ferritic, and for this reason, the present invention has adopted the control scheme of middle C content.If C content is low excessively, the intensity of steel is difficult to guarantee; The C too high levels, the plasticity of steel and impact property can reduce, and for this reason, the present invention is controlled at 0.45～0.80% with the weight percentage of C, is preferably 0.50～0.70%.
Mn is an austenite stabilizer element; Mn content is higher than at 20% o'clock, and ferrous materials can keep single austenite structure, and high Mn austenitic steel can produce twin crystal inducing plasticity (TWIP) effect under the effect of mechanical load; Produce high unit elongation, material has high-ductility.The mechanical property of austenitic steel depends primarily on stacking fault energy, and stacking fault energy is determining the main deformational mechanism type, and the martensite that causes like slippage, friendship slippage, slippage, twinning deformation or the strain of partial dislocation transforms.Under given texturizing condition, stacking fault energy only depends on chemical ingredients.Along with increasing of Mn content, stacking fault energy increases, and twin strengthens the contribution of plasticity, and it is main strengthening mechanism gradually that twin is strengthened, but manganese content is too high, can increase raw materials cost.When the Mn content in the steel less than 20% the time; Under common cooling conditions, stacking fault energy is low excessively, and is unstable during mechanical load; Martensitic transformation takes place under the effect of stress; Steel can not keep single austenite structure, and the twin crystal inducing plasticity effect is affected, and the plasticity of steel can't reach the high-ductility level of full austenite twin crystal inducing plasticity steel.For this reason, the weight percentage of Mn of the present invention is controlled at 20～30%, is preferably 21.0～25.0%.
The Si element is strong to reduce austenitic stacking fault energy, and Si can the solution strengthening austenitic matrix, suppresses the friendship slippage of dislocation.The Si too high levels, material surface is of poor quality, promotes material generation martensitic transformation simultaneously, also be prone to produce the limit during steel hot rolling and splits phenomenon, and the present invention's weight percentage of controlling Si is controlled to be 0.01～0.20% for this reason, is preferably 0.02～0.18% low scope.
The Al element increases austenitic stacking fault energy, but can suppress martensitic transformation.The Al too high levels during suitability for industrialized production, can serious be stopped up mold gap in the steel making working procedure, simultaneously, the Al too high levels, when hot rolling since with the acting in conjunction of Si element, produce the severe edge fracture phenomenon.In order to obtain the full austenite steel, Al content of the present invention is controlled at 0.02～0.10% low scope.
P, S content are low more good more in steel, avoid the disadvantageous effect that ferrous materials of the present invention is cracked and welds.In addition, sulphur content is higher can to consume too much manganese element, influences the highly malleablized effect of material, or increases the cost of material.
The method of manufacture of carbon HRS combines the middle carbon of steel and the composition characteristic of manganese element and minor amount of silicon content and a small amount of Al element in the 900MPa grade high-strength high-ductility of the present invention; The cooling controlling and rolling controlling process that adopts pure steel to smelt mode and adopt heat, low temperature finish to gauge and low temperature to batch obtains hot rolling attitude tissue; The room temperature texture that obtains is an austenite; Simultaneously there are a large amount of twins in the austenite, help inventing material and have high-strength high-plasticity and good plasticity and good welding property.Reduce harmful elements such as sulphur and phosphorus in the raw material smelting process during manufacturing as far as possible and obtain pure steel, element sulphur often exists with the manganese sulfide form in the steel, and this sulfide inclusion is very unfavorable to the low-temperature impact toughness of steel, and causes anisotropy of material to strengthen.Molten steel tapping end temp during the casting steel billet is controlled at 1700～1900 ℃ of scopes, adopts argon shield casting measure, and it is not oxidized to help molten steel.Because the Mn constituent content of high-strength steel of the present invention is high, need usually during the slab heating to adopt the long soaking time of 160～250min and need slab heating temperature be remained on 1150～1230 ℃ of scopes, make the abundant solid solution of Mn element.Because of C of the present invention, Mn constituent content all very high; And these two elements all are the elements that enlarges the austenitic area; Just can guarantee under lower finishing temperature that promptly the austenite one phase district is rolling to obtain uniform grain-size; The roughing temperature is controlled at 1010～1110 ℃ of scopes during hot rolling, and finishing temperature is controlled in 700～800 ℃ of scopes.The coiler plate temperature design can effectively guarantee thin grain-size in 500～600 ℃ of scopes.
HRS of the present invention is master's chemical composition design with middle C and high Mn; Auxiliary a small amount of Si and a small amount of Al element of adding; Do not add other valuable alloy element; Make being organized as in full austenite and the tissue of superelevation heat-flash of the present invention steel rolling that a large amount of twins sub-structure arranged, strong guarantee the HS of product made from steel, high-ductility, also ensured simultaneously the welding property that product made from steel is good; HRS of the present invention is through relying on the twin crystal inducing plasticity principle; When ensureing the HS of steel; Greatly improved extension property and forming property, made product made from steel have low yield tensile ratio and high impelling strength, guaranteed that material has fabulous energy absorption capability.Even the civilian and war products that HRS of the present invention is processed are damaged; Can guarantee that also product has good safety performance; In addition, the crisp/ductility transmition temperature of HRS of the present invention is very low, under the ugly weather environment of cold, uses; Be unlikely to brittle failure, other hot-rolling high-strength steel of this point is difficult to guarantee.And the manufacturing approach craft of HRS of the present invention is simple, does not add other valuable alloy element in the steel, has reduced the cost of producing steel, Composition Control technology difficulty when having reduced steel-making simultaneously.
Description of drawings
Fig. 1 is the metallographic microstructure structure iron of carbon HRS in the 900MPa grade high-strength high-ductility of the present invention.
Embodiment
Below in conjunction with accompanying drawing and specific embodiment carbon HRS and method of manufacture thereof in the 900MPa grade high-strength high-ductility of the present invention are done further explain.
Table 1 has been listed the chemical component weight percentage composition (surplus is Fe and unavoidable impurities) of the embodiment of the invention 1～10 HRS.
Table 1
| Embodiment | C | Si | Mn | Al | P | S |
| 1 | 0.45 | 0.20 | 30.0 | 0.10 | 0.013 | 0.008 |
| 2 | 0.50 | 0.16 | 28.0 | 0.08 | 0.015 | 0.008 |
| 3 | 0.50 | 0.18 | 25.0 | 0.10 | 0.012 | 0.007 |
| 4 | 0.60 | 0.15 | 23.5 | 0.08 | 0.012 | 0.006 |
| 5 | 0.55 | 0.12 | 22.8 | 0.07 | 0.012 | 0.005 |
| 6 | 0.61 | 0.10 | 21.5 | 0.05 | 0.010 | 0.006 |
| 7 | 0.65 | 0.08 | 21.2 | 0.05 | 0.013 | 0.007 |
| 8 | 0.70 | 0.02 | 21.0 | 0.02 | 0.009 | 0.005 |
| 9 | 0.76 | 0.01 | 20.8 | 0.04 | 0.012 | 0.008 |
| 10 | 0.80 | 0.04 | 20.0 | 0.02 | 0.010 | 0.007 |
HRS in the foregoing description 1～10 is produced by common Clean Steel technology; Step through raw material smelting, casting steel billet, slab heating, hot rolling, processing under cooling; Wherein, the molten steel tapping end temp of casting steel billet is 1700～1900 ℃, adopts argon shield casting measure; Slab heating temperature remains 1150～1230 ℃ of scopes and controls soaking time between 160～250min; Hot rolling roughing temperature is controlled at 1010～1110 ℃ of scopes; Finishing temperature is in 700～800 ℃ of scopes; It is rolling in the hot rolling technology rolled piece to be carried out 5～7 passages, and thickness of slab is controlled at 2.5～5.0mm, and coiling temperature is controlled at 500～600 ℃.
The metallurgical structure of the hot-rolled steel sheet material object that obtains is as shown in Figure 1, is single austenite, and austenite is polygonized structure, and there is twins sub-structure in intracrystalline.Then the foregoing description 1～10 hot-rolled steel sheet is carried out mechanical properties such as ys, tensile strength, elongation, ballistic work and test, test result is seen table 2.
Table 2
Table 2 data presentation; The mechanical property of HRS of the present invention under the specification as thin as a wafer of 2.5～5.0mm, its ys be in the scope of 400～500MPa, tensile strength all >=900MPa; The ratio of their ys and tensile strength is in 0.44～0.51 scope; Be starkly lower than the lower value 0.70 of conventional high-strength steel, mean that the crystallized ability of material is good, and anti-fracture energy be strong.This index, the high-strength steel of using for drawing is even more important, because if ys is high, then corresponding forming mould requirement of strength is higher, brings pressure for the cost of mould.Simultaneously, ferrous materials elongation (A of the present invention
80Mm%)>=47%, be higher than other hot-rolling high-strength steel far away, and the unit elongation of other hot-rolling high-strength steel can not surpass 30%.Crisp/ductility transmition the temperature of steel especially of the present invention through detect for≤-80 ℃, ballistic work (a
Kv)>=200J/cm
2High, can guarantee material welding performance, forming property, these guarantee highly beneficial for the product performance of processing with steel of the present invention.For example the wheel of this steel plate manufacturing has plasticity and intensity and welding property and the low temperature usability that is superior to other hot-rolling high-strength steel, has increased the safety in utilization of manufacturing product greatly, and can the acclimatization environmental change.Thereby HRS of the present invention can be used for remedying traditional high-strength steel unit elongation deficiency and impact property is on the low side and the shortcoming of energy absorption difference.
Claims (2)
1. carbon HRS in the 900MPa grade high-strength high-ductility, its chemical ingredients percentage ratio is by weight counted: C:0.5%, Mn:28%, Si:0.16%, Al:0.08%, P:0.015%, S:0.008%, surplus is Fe and unavoidable impurities; Its method of manufacture comprises that raw material is smelted, the step of casting steel billet, slab heating, hot rolling, processing under cooling, wherein:
The molten steel tapping end temp of said casting steel billet is controlled at 1700 ~ 1900 ℃;
Said slab heating temperature is controlled at 1150 ~ 1230 ℃;
The roughing temperature is controlled at 1010 ~ 1110 ℃ during said hot rolling, and finishing temperature is controlled at 700 ℃, and coiling temperature is controlled at 500 ~ 600 ℃;
It is rolling during said hot rolling rolled piece to be carried out 5 ~ 7 passages.
2. according to carbon HRS in the said 900MPa grade high-strength of claim 1 high-ductility, it is characterized in that: in its method of manufacture, when said slab heated, the control soaking time was between 160 ~ 250min.
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| CN101432456A (en) * | 2006-12-27 | 2009-05-13 | Posco公司 | High manganese high strength steel sheets with excellent crashworthiness, and method for manufacturing of it |
| CN101429590A (en) * | 2008-12-19 | 2009-05-13 | 北京科技大学 | Process for producing twin crystal inducement plastic steel material with high carbon content |
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| CN101432456A (en) * | 2006-12-27 | 2009-05-13 | Posco公司 | High manganese high strength steel sheets with excellent crashworthiness, and method for manufacturing of it |
| CN101429590A (en) * | 2008-12-19 | 2009-05-13 | 北京科技大学 | Process for producing twin crystal inducement plastic steel material with high carbon content |
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