CN102618790B - High-strength low-Cr ferrite stainless steel and manufacturing method thereof - Google Patents
High-strength low-Cr ferrite stainless steel and manufacturing method thereof Download PDFInfo
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Abstract
The invention relates to ferrite stainless steel which comprises the following chemical constituents by weight percent: 0.006 to 0.02 percent of C, 0 to 0.015 percent of N, 0.25 to 1.0 percent of Mn, 0.25 to 1.0 percent of Si, 11.0 to 14.0 percent of Cr, 0 to 0.3 percent of Ni, 0 to 0.3 percent of Cu, 0 to 0.1 percent of V, 0.10 to 0.15 percent of Ti, 0.05 to 0.20 percent of Nb, 0 to 0.035 percent of P, 0 to 0.0030 percent of S, and Fe and unavoidable impurities in balancing amount, wherein the total content of Ti and Nb ranges from 0.15 to 0.30 percent, the total content of Ti and V ranges from 0.10 to 0.20 percent, and the total content of Ti, V and Nb ranges from 0.20 to 0.40 percent. The manufacturing method of the ferrite stainless steel comprises the following steps: carrying out smelting and continuous casting to obtain continuous casting billets, wherein the proportion of medium axialite is not lower than 60 percent; heating the continuous casting billets to be 1050 to 1150 DEG C; carrying out 5 to 7 times of rough rolling at the temperature ranging from 1080 to 900 DEG C, wherein the total reduction ratio is not lower than 85 percent each time; and carrying out 5 to 7 times of rough rolling under the temperature ranging from 980 to 750 DEG C, wherein the total reduction ratio is not lower than 85 percent each time, and the reeling temperature ranges from 500 to 650 DEG C. According to the manufacturing method, a hot rolled stainless steel plate, of which the thickness ranges from 3.0 to 8.0 mm, the shear strength is larger than 350 Mpa, the tensile strength is larger than 500 MPa, the base metal full-scale impact power is larger than 200 J, and the base metal extensibility is larger than 20 percent, is obtained. Therefore, the ferrite stainless steel is suitable for automobile frames.
Description
Technical field
The present invention relates to ferritic stainless steel and manufacture method thereof, particularly relate to the high-intensity ferritic stainless steel of a kind of low chromium and manufacture method.
Technical background
Containing C and the lower ultra-low carbon and nitrogen ferritic stainless steel of N composition, because it is compared with strong corrosion resistant performance, meanwhile, this stainless steel has higher economy because having saved the Ni of high price, makes this stainless steel be widely applied to every field.As, automobile exhaust system is almost all used corrosion resistant ferritic stainless steel with stainless steel.Along with improving constantly of environmental requirement, the environment-friendly advantage of electromobile is more and more favored.Particularly, for city bus bus automobile, relatively short because of its road that travels, route is fixed, more and more electromobiles of selecting.Such electronic bus reaches 12-15 to the general requirement in work-ing life of vehicle body, therefore, uses the good stainless steel of solidity to corrosion to become first-selection.
Conventional SUS304 stainless steel processing characteristics is better, but because add higher Ni to make manufacturing cost higher, there is no advantage.And the ferritic stainless steel of high anti-corrosion becomes optimal selection.Meanwhile, consider the collision requirement of transportation and communication, general requirement will possess higher yield strength for the material of vehicle frame processing, evades the risk of collision that use procedure occurs.Low chrome ferritic stainless steel in routine, such as 0Cr11 and 0Cr17 etc., although can meet the demands on corrosion resistance nature, but its yield strength is lower, generally below 250-300MPa, and ballistic work is low, can not meet requirement and the high-ductility (unit elongation be greater than 20%) of communications and transportation device to its high strength (yield strength is generally greater than 350MPa), ballistic work (30 ℃ of full-scale ballistic works are greater than 20J), and the higher ferritic stainless steel of Cr content inevitably increases material cost.
CN1182458A relates to the ferritic stainless steel using in exhaust system equipment of vehicle.Wherein C is not more than 0.005%, N and is not more than 0.008%, C+N and is not more than 0.009%, Si and is not more than 0.45%, Mn to be not more than 1%, Cr be 10-12.5%, and Nb is 0.05-0.3%, and Ti is 8 * (C+N)～0.3%, and all the other are iron and inevitable impurity.Its normal temperature plasticity and hot strength are all fine, are suitable for automobile exhaust system, but are not suitable as vehicle frame steel.
Unexamined Patent 7-145453A relates to automobile exhaust system menifold ferritic stainless steel.This ferritic stainless steel, for automobile exhaust system temperature end, below C:0.015%, Si:0.80-1.50%, Mn:0.20-0.60%, Cr:11.0-14.0%, below Ni:0.50%, below N:0.015%, Ti:0-0.20%, S:0-0.10%, Mo:0-1.5%, Al:0-0.20%, Ca, Y, La, Ce etc. a kind of and more than, add up to 0-0.10%, C+N≤0.025%, all the other are iron and inevitable impurity.Its 900 ℃ above excellent scale resistance, hot strength, thermal fatigue characteristics, also excellent to the high temperature resistant salt damage corrodibility in outside, be suitable for automobile gas exhausting manifold branch, but be not suitable as vehicle frame steel.
EP1930461A1 relates to stainless steel and welded tube for automobile exhaust system.Wherein below C:0.03%, below Si:1.0%, below Mn:1.5%, Cr:10.0-20%, below Nb:0.5%, below Ni:0.6%, below N:0.03%, Ti:0.05-0.30%, S:0-0.10%, Mo:0-1.5%, Al:0.03-0.12%, Cu:1-2%, below V:0.2%, B:0.0005-0.02%, below O:0.01%, all the other are iron and inevitable impurity.Nb≥8X(C+N)，0.02≤Al-(54/48)O≤0.1。Its hot strength and welding tenacity excellent, be suitable for automobile exhaust pipe, but be not suitable as vehicle frame steel.
At present still need to provide a kind of low chrome ferritic stainless steel of the low-cost high-strength for automobile frame.
Goal of the invention
The object of the present invention is to provide a kind of low chrome ferritic stainless steel of low-cost high-strength.This stainless steel has higher yield strength, high room temperature ballistic work and unit elongation, and meanwhile, this stainless steel also has higher erosion resistance, is applicable to the use of vehicle body frames that intensity and shock resistance are had relatively high expectations.In addition, this stainless steel adopts conventional industrialized producing technology path just can obtain the hot-rolled steel sheet that meets performance requriements, and material manufacturing process is simple, and cost is low.
For achieving the above object, high-intensity low chrome ferritic stainless steel of the present invention, its chemical composition is by weight percentage: C:0.006-0.02%, N≤0.015%, Mn:0.25-1.0%, Si:0.25-1.0%, Cr:11.0-14.0%, Ni≤0.3%, Cu≤0.3%, V≤0.1%, Ti:0.10-0.15%, Nb:0.05-0.20%, and 0.15%≤Ti+Nb≤0.30%, 0.10%≤Ti+V≤0.20%, 0.20%≤Ti+V+Nb≤0.40%, P≤0.035%, S≤0.0030%, all the other are Fe and inevitable impurity.
The manufacture method that another object of the present invention is to provide above-mentioned high-intensity low chrome ferritic stainless steel, the method comprises the steps:
Through smelting and continuous casting, obtain continuously cast bloom, in continuously cast bloom, proportion of equiaxed grain is not less than 60%;
Continuously cast bloom is heated to 1050-1150 ℃;
The temperature range of 1080-900 ℃, carry out the roughing of 5-7 passage, total draft is all not less than 85%;
The temperature range of 980-750 ℃, carry out the finish rolling of 5-7 passage, total draft is all not less than 85%;
Coiling temperature is 500-650 ℃.
Thickness of the present invention is that the hot-rolled stainless steel plate yield strength of 3.0-8.0mm is more than 350MPa, and more than tensile strength reaches 500Mpa, the full-scale ballistic work of mother metal is greater than 200J, and mother metal unit elongation is greater than 20%.Hot-rolled sheet coil of the present invention can obtain the stainless steel plate needing after direct pickling.In addition, by continuous casting and control As rolled and organize, not only can obtain desirable mechanical property, meanwhile, acquisition organize the coarsening of organizing that is also conducive to suppress subsequent weld.
The present invention had both considered the rotproofness of stainless steel necessity, and simultaneously by techniques such as reasonably smelting, rollings, make this stainless steel is ferrite under use state, but its intensity is far away higher than conventional ferritic stainless steel.Meanwhile, the full-scale ballistic work of the mother metal under this stainless steel normality surpasses 200J, and the full-scale ballistic work of subzero 30 degree weld seam is higher than 20J.Steel of the present invention is particularly suitable for the processing and manufacturing of new-energy automobile vehicle frame.
Embodiment
Below in conjunction with embodiment, the features and advantages of the invention are described in detail.
In the present invention, unless otherwise, content all refers to weight percent content.
In order to meet the intensity of steel, the requirement of weldability, erosion resistance and shock resistance, provides the object of the invention of high-intensity low chrome ferritic stainless steel, and each elemental composition is controlled as follows:
C and N: steel grade of the present invention belongs to the ferritic stainless steel of ultra-low carbon nitrogen, therefore, in steel of the present invention, carbon and nitrogen belong to the control element of special concern, and wherein, N is mainly that impurity element need to reduce its content as far as possible.And the too low intensity that is unfavorable for guaranteeing material of C content, the too high corrosion resistance nature that can affect material of C, so the span of control of C of the present invention is 0.006-0.02%.At present smelting equipment can be controlled at total amount by carbon and nitrogen and is less than 0.025% than being easier to meet in the situation that guaranteeing throughput, reaches the requirement of carbon amount 0.006-0.02%, nitrogen amount≤0.015% simultaneously.Reducing nitrogen content is mainly to reduce as far as possible stabilizing element consumption, particularly reduces the use of Ti, improves the surface quality of product and improves corrosion among crystalline grains.
Cr: be the main alloy element that improves solidity to corrosion and intensity.Cr improves stainless steel solidity to corrosion, improves the local corrosion abilities such as its atmospheric corrosion resistance and crevice corrosion.Cr improves the intensity of steel, but the plasticity of too high reduction steel is unfavorable to moulding and weldability.Too lowly be unfavorable for improving its corrosive nature.Therefore, Cr content range of the present invention is 11.0-14.0%, is preferably 11.2-13.0%.
Si: add in steel and play deoxidation and the corrosion proof effect of improvement, can also further improve the intensity of material simultaneously.When too low, be unfavorable for desoxydatoin and improve intensity, therefore, Si content is greater than 0.25%.If silicone content is greater than 1.0%, unfavorable to processing and toughness, also unfavorable to normal temperature compacted under.Consider overall performance, in the present invention, controlling silicone content is 0.25-1.0%, is preferably 0.26-0.9%.
Mn: be weak austenite element, Mn can suppress the deleterious effect of sulphur in stainless steel in the present invention, improves thermoplasticity.But when too low, be unfavorable for improving its thermoplasticity, be also unfavorable for improving the processability under normal temperature, when too high, be unfavorable for guaranteeing its erosion resistance.In the present invention, in order to guarantee intensity and the plasticity of steel, the scope of Mn content is 0.25-1.0%, is preferably 0.26-0.90%.
Cu:Cu mainly comes from stainless steel steel scrap, generally guaranteeing not add Cu under use properties prerequisite, add copper both to increase material cost, also cause steel scrap handling cost to increase simultaneously, therefore,, in the present invention, meeting under corrosive nature condition, remaining Cu content is controlled at and is no more than 0.3%, is preferably no more than 0.2%.
Ni:Ni equally belongs to Cu the impurity element that needs are controlled in ferritic stainless steel of the present invention, is reduced to as far as possible suitable.In the present invention, control the amount of bringing Ni into because of scrap smelting, total amount is no more than 0.30%, is preferably no more than 0.20%.
V:V is useful to improving the intensity of material, but that content is difficult for is too high, when too high, can cause the strength of materials and much higher hard, is unfavorable for forming process.In the present invention, in order to improve the strength of materials, control V≤0.1% in steel, be preferably 0.02-0.08%.
Ti and Nb:Ti and Nb are mainly used in preventing that chromium concn that in steel, chromium and carbon cause in conjunction with forming chromium carbide from reducing causes erosion resistance to reduce, and particularly cause intergranular corrosion; Ti can also be in steel sulphur be combined and form TiC
2s compound is to prevent the caused spot corrosion of MnS.In stainless steel, Ti and nitrogen avidity are greater than Nb, and Nb and carbon avidity are greater than Ti.Ti and Nb can improve stainless room temperature and hot strength, improve antifatigue and cold formability and the weldability of ferritic stainless steel, and the too high brittle transition temperature to steel of Nb is unfavorable.The nitride (TiN) that Ti and nitrogen form can affect surface and the inner quality of steel as inclusion, and the nitride (NbN) that Nb and nitrogen form also can reduce the thermoplasticity of steel.The TiN that TI formed in the continuous casting stage can also play the effect of forming core particle, is conducive to further improve the ratio of equiax crystal, improves processed-type energy.DeGrain when Ti content is less than 0.10%, but too much can produce surface imperfection, be generally no more than 0.20%.DeGrain when Nb content is less than 0.05%, surpasses 0.30% and can too much cause forming thick Fe because of Nb
2nb, is unfavorable for forming materials performance and welding impact property.Consider C in the present invention, N content, selects two kinds of Nb and Ti to add element as stabilization, and its content range is: Ti:0.10-0.15%; Nb:0.05-0.20%; And 0.15%≤Ti+Nb≤0.35%.Meanwhile, take into account the effect of considering V, also control 0.10%≤Ti+V≤0.20% and 0.20%≤Ti+V+Nb≤0.40%.
P and S: in ferritic stainless steel, p and s can have a strong impact on stainless solidity to corrosion and processing characteristics, must strictly control, and is controlled at P≤0.035%, S≤0.003% in the present invention.Preferably, P≤0.030%.
Above-mentioned high strength low chrome ferritic stainless steel of the present invention is manufactured by the following method:
To design according to mentioned component, and by Electric furnace steel making, AOD decarburization, VOD deoxidation three-step approach, make steel and after VOD finishes, feed titanium silk and process, after comprehensive composition meets design requirement, just can obtain the molten steel that meets composition requirement.By controlling casting process pulling rate (0.9-1.1m/min), strengthening induction stirring (electric current 1000-1600 ampere) and make molten steel obtain proportion of equiaxed grain in continuously cast bloom and continuously cast bloom through continuous casting in conjunction with composite technologies such as stabilizing elements being not less than 60%, continuously cast bloom is with warm figuring of surface, reconditioning starting temperature is not less than 360 ℃, and reconditioning finishing temperature is not less than 150 ℃.
After reconditioning, be with temperature to send process furnace to heat and be incubated certain hour and carry out hot rolling.Heating temperature is 1050-1150 ℃.First hot rolling is carried out 5-7 passage roughing (temperature range 1080-900 ℃) and is removed surface scale, and roughed bloom is all not less than 85% through 5-7 passage finish rolling (temperature range 980-750 ℃), roughing and the total draft of finish rolling.Control finish to gauge and coiling temperature, particularly (finishing temperature is 750-850 ℃ to the control by finish to gauge and coiling technique parameter, coiling temperature is 500-650 ℃), make hot-rolled sheet coil there is the mechanical property of above-mentioned requirements, be that yield strength is more than 350MPa, more than tensile strength reaches 500Mpa, the full-scale ballistic work of mother metal is greater than 200J, and mother metal unit elongation is greater than 20%.Hot-rolled sheet coil can obtain the stainless steel plate needing after direct pickling.In addition, by continuous casting and control As rolled, organize, not only can obtain desirable mechanical property.Meanwhile, acquisition organizes the coarsening of organizing that is also conducive to suppress subsequent weld.
According to method of the present invention, can obtain thickness is the hot-rolled stainless steel plate of 3.0-8.0mm.
The composition of some embodiments of the present invention steel is in Table 1, and the major control point of manufacture method is in Table 2.
The main control parameters of table 2 embodiment of the present invention steel
Test example 1: mechanical property
The mechanical property of measuring embodiment of the present invention steel according to GB (GB/T 228-2002) method, it the results are shown in Table 3.
The mechanical property of table 3 embodiment of the present invention steel
Low chrome ferritic stainless steel of the present invention has been controlled the element of enhanced tissue mechanical property especially, as C, Mn, Si, V etc.Particularly compare with conventional ferritic stainless steel, the content of C is controlled at more than 0.006%, and adds the appropriate strengthening elements such as V, to can directly just can obtain the mechanical property of requirement by hot rolling, by adding Ti and Nb, improves corrosive nature.
Low chrome ferritic stainless steel of the present invention, meeting under the prerequisite of corrosion and mechanical property, omits the precious metal alloys such as Mo, can further reduce costs.By Si deoxidation, omit Al deoxidization technique.Although Al deoxidation can effectively reduce the oxygen level of finished product,, the greatest problem of Al deoxidation is easily to form Al
2o
3oxide compound, cause oxide inclusion, affect final finished quality.Meanwhile, also omitted rare earth element as Y, La, Ce etc., these rare earth elements, because addition is little, are not easy homogenizing simultaneously, are also very easy to cause being mingled with, and affect final product quality.
Low chrome ferritic stainless steel of the present invention has omitted Al, Cu and B element, and meanwhile, other elements are not done requirement as Mo etc. yet.The interpolation of Al easily causes causing material to be mingled with in the residual steel of Al oxide compound.Cu adds can improve corrodibility, but easily causes high temperature process plasticity to worsen.B is conducive to improve intensity, but because the amount adding is less, is difficult to evenly, causes material property uneven.The design's high-strength ferritic stainless steel is mainly for vehicle frame manufacture, meanwhile, the processing of also will painting of stainless steel outside surface, the Cr of conventional 11.0-14.0% just can meet the demands, and is not required to be to improve erosion resistance and carry out special Alloying Treatment.By saving alloying element, in conjunction with hot rolling technology, obtain necessary armor plate strength.
The stainless steel thickness that the present invention obtains is that 3-6mm is main, and this stainless steel only carries out hot rolling, does not carry out cold rolling processing.In the smelting stage, by induction stirring, in conjunction with stabilizing element, add, obtain proportion of equiaxed grain and surpass 60% continuously cast bloom tissue, thereby guarantee the homogeneity of structure of hot-rolled sheet.Meanwhile, in course of hot rolling, further control depressing than more than 85% of roughing and finish rolling, further optimizing tissue.Finishing stands is controlled cooling temperature and curling temperature, can obtain the hot-rolled sheet that mechanical property meets the demands.This hot-rolled sheet needn't carry out anneal only by conventional pickling, just can obtain the stainless steel coiled sheet needing.
Compare with traditional stainless steel processing, the present invention, by controlling alloy designs and hot rolling technology, has not only omitted annealing operation, has also guaranteed the ballistic work of necessary intensity, unit elongation and mother metal and weld seam simultaneously.Meet the requirement of body of a motor car, vehicle frame use properties completely.
Claims (16)
1. ferritic stainless steel, its chemical composition is by weight percentage: C:0.006-0.02%, N≤0.015%, Mn:0.25-1.0%, Si:0.25-1.0%, Cr:11.0-14.0%, Ni≤0.3%, Cu≤0.3%, V≤0.1%, Ti:0.10-0.15%, Nb:0.05-0.20%, and 0.15%≤Ti+Nb≤0.30%, 0.10%≤Ti+V≤0.20%, 0.20%≤Ti+V+Nb≤0.40%, P≤0.035%, S≤0.0030%, all the other are Fe and inevitable impurity.
2. ferritic stainless steel as claimed in claim 1, is characterized in that, C:0.008-0.018%.
3. ferritic stainless steel as claimed in claim 1 or 2, is characterized in that, Si:0.26-0.90%.
4. ferritic stainless steel as claimed in claim 1 or 2, is characterized in that, Mn:0.26-0.90%.
5. ferritic stainless steel as claimed in claim 1 or 2, is characterized in that, Cr:11.2-13.0%.
6. ferritic stainless steel as claimed in claim 1 or 2, is characterized in that, Ni≤0.20%.
7. ferritic stainless steel as claimed in claim 1 or 2, is characterized in that, Cu≤0.20%.
8. ferritic stainless steel as claimed in claim 1 or 2, is characterized in that, V:0.02-0.08%.
9. ferritic stainless steel as claimed in claim 1 or 2, is characterized in that, P:0.01-0.03%.
10. ferritic stainless steel as claimed in claim 1 or 2, is characterized in that, N≤0.012%.
11. the ferritic stainless steel manufacture method as described in as arbitrary in claim 1-10, comprises the steps:
Through smelting and continuous casting, obtain continuously cast bloom, in continuously cast bloom, proportion of equiaxed grain is not less than 60%;
Continuously cast bloom is heated to 1050-1150 ℃;
The temperature range of 1080-900 ℃, carry out the roughing of 5-7 passage, total draft is all not less than 85%;
The temperature range of 980-750 ℃, carry out the finish rolling of 5-7 passage, total draft is all not less than 85%;
Coiling temperature is 500-650 ℃.
12. methods as claimed in claim 11, is characterized in that, smelting comprises:
According to described composition, by Electric furnace steel making, AOD decarburization, VOD deoxidation three-step approach, make steel and after VOD finishes, feed titanium silk and process.
13. methods as described in claim 11 or 12, is characterized in that, in continuous casting, pulling rate is 0.9-1.1m/min.
14. methods as described in claim 11 or 12, is characterized in that, in continuous casting, the electric current of induction stirring is 1000-1600 ampere.
15. methods as described in claim 11 or 12, is characterized in that, finishing temperature is 750-850 ℃.
16. methods as described in claim 11 or 12, is characterized in that, continuously cast bloom, before heating rolling, is with warm figuring of surface, and reconditioning starting temperature is not less than 360 ℃, and reconditioning finishing temperature is not less than 150 ℃.
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| CN104785521A (en) * | 2015-04-21 | 2015-07-22 | 山东泰山钢铁集团有限公司 | Method and system for rolling 410S ferrite stainless steel |
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| WO2020017123A1 (en) * | 2018-07-18 | 2020-01-23 | Ｊｆｅスチール株式会社 | Ferrite stainless steel sheet and manufacturing method thereof |
| CN112400031B (en) * | 2018-07-18 | 2022-03-01 | 杰富意钢铁株式会社 | Ferritic stainless steel sheet and method for producing same |
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| CN1241221A (en) * | 1997-08-05 | 2000-01-12 | 川崎制铁株式会社 | Ferritic stainless steel plate of high deep drawability and ridging resistance and method of mfg. same |
| CN1572895A (en) * | 2003-06-04 | 2005-02-02 | 日新制钢株式会社 | Ferritic stainless steel sheet excellent in formability and its manufacturing method |
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| Publication number | Priority date | Publication date | Assignee | Title |
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| CN1241221A (en) * | 1997-08-05 | 2000-01-12 | 川崎制铁株式会社 | Ferritic stainless steel plate of high deep drawability and ridging resistance and method of mfg. same |
| CN1572895A (en) * | 2003-06-04 | 2005-02-02 | 日新制钢株式会社 | Ferritic stainless steel sheet excellent in formability and its manufacturing method |
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