CN102260833B - Stainless steel for high-performance B4003M truck - Google Patents
Stainless steel for high-performance B4003M truck Download PDFInfo
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- CN102260833B CN102260833B CN2010101840573A CN201010184057A CN102260833B CN 102260833 B CN102260833 B CN 102260833B CN 2010101840573 A CN2010101840573 A CN 2010101840573A CN 201010184057 A CN201010184057 A CN 201010184057A CN 102260833 B CN102260833 B CN 102260833B
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Abstract
The invention relates to stainless steel for a high-performance B4003M truck. The stainless steel comprises the following components in percentage by mass: 0.010 to 0.015 percent of C, 0.20 to 0.60 percent of Si, 0.80 to 2.5 percent of Mn, 11.0 to 13.0 percent of Cr, less than or equal to 0.040 percent of P, less than or equal to 0.010 percent of S, 0.60 to 1.5 percent of Ni, less than or equal to 0.020 percent of N, less than or equal to 0.20 percent of Cu, less than or equal to 0.0050 percent of O, 0.10 to 0.30 percent of Ti, less than or equal to 0.030 percent of C and N, and the balance of Fe and inevitable impurities. The yield strength of the stainless steel reaches over 350MPa, and the elongation reaches over 25 percent. In the length of the whole strip steel, the performance of the strip steel is very uniform; and the yield of the finished strip steel is improved.
Description
Technical field
The present invention relates to the stainless steel strip rolling technique, particularly ferritic stainless steel hot-rolling production and stainless steel hot treatment technology.
Background technology
Generally, the ferrite stainless strip steel yield strength is on the low side, is 260～290MPa.In order to manufacture the lorry stainless steel, those skilled in the art often improve the intensity of steel by the content that improves the elements such as Mn, Cr in steel.As the publication number application that is CN101410543, disclose a kind of stainless steel sheet for structural members of excellent in impact-absorbing characteristics, the content of its Cr, Ni, Mn, Cu is all higher, although improved intensity, but make its welding property and low temperature impact properties reduce, can not meet the needs of deformation processing.
In order to improve the welding property of steel, those skilled in the art often adopt the method that adds alloying element.As the patent that publication number is EP1323841, a kind of thin plate of the Martensite Stainless Steel for rail vehicle is disclosed, wherein add alloy to improve the welding property of material, but also greatly increased cost simultaneously.
In addition, common ferritic stainless steel adopts the slab heating temperature of 1100～1180 ℃, approximately 930 ℃ of the finishing temperatures of hot rolled strip.Cooling temperature before strip coiling is higher, after hot strip rolling completes, does not do special cooling process.With the coiling temperature general control of steel at 750～850 ℃.After this type of ferrite stainless strip steel hot rolling, also need further to be cold-rolled to thin specification, can be for the manufacture of railway freight-car, thereby make the manufacturing process relative complex, increased manufacturing cost.
Therefore, need badly and a kind ofly possess high strength and welding property, and the lower lorry stainless steel of production cost.
Summary of the invention
The object of the present invention is to provide a kind of ferrite stainless steel material of high-yield strength, high-wearing feature, the comprehensive corrosion of anti-generality for railway freight-car.
For achieving the above object, steel provided by the present invention, its composition quality degree is: C:0.010～0.015, Si:0.20～0.60, Mn:0.80～2.5, Cr:11.0～13.0, P :≤0.040, S :≤0.010, Ni:0.60～1.5, N :≤0.020, Cu :≤0.20, O :≤0.0050, Ti:0.10～0.30, C+N :≤0.030, all the other are Fe and inevitable impurity.
For achieving the above object, the present invention also further provides a kind of stainless steel, and its composition quality degree is: C:0.010～0.015, Si:0.20～0.60, Mn:1.40～1.60, Cr:11.5～12.5, P :≤0.040, S :≤0.010, Ni:0.80～1.0, N:0.007～0.015, Cu :≤0.20, O :≤0.0050, Ti:0.15～0.25, C+N :≤0.030, all the other are Fe and inevitable impurity.
In addition, the present invention also provides a kind of manufacture method of above-mentioned steel, comprises successively smelting, continuous casting, hot rolling, annealing, pickling.
Preferably, described hot rolling comprises heating, roughing, finish rolling, cooling and batch successively.
Preferably, described annealing is carried out in bell furnace, and temperature is 700～750 ℃; Heat-up rate is 200 ℃/hs; Soaking time is 30mm/ hour.
Preferably, described heating comprises heat-recovery section, preheating section, heating I section, heating II section and soaking zone successively.
Preferably, described roughing deformation rate is 75%～85%, and extreme trace time rolling deformation velocity range is 8s
-1～12s
-1, temperature out is greater than 980 ℃.
Preferably, the extreme trace of described finish rolling time rolling deformation velocity range is 60s
-1～90s
-1, temperature out is greater than 950 ℃.
Preferably, described speed of cooling is controlled at 30～60 ℃/S.
Preferably, described coiling temperature is 760 ℃.
Preferably, described heat-recovery section temperature is 700 ℃～900 ℃, and be 45～55 minutes heat-up time.
Preferably, described preheating section temperature is 700 ℃～900 ℃, and be 30～40 minutes heat-up time.
Preferably, described heating I section temperature is 900～1000 ℃, and be 30～40 minutes heat-up time.
Preferably, described heating II section temperature is 1000～1100 ℃, and be 30～40 minutes heat-up time.
Preferably, described soaking zone temperature is 1090～1100 ℃, and soaking time is 30～40 minutes.
Below will further illustrate the present invention.
In steel of the present invention, the content of C is lower, and has added the Ni of less than 1%, makes in high-temperature steel the austenite structure ratio higher, at air cooling, to room temperature condition, can obtain ferrite+martensite duplex structure.Define this steel grade according to the tissue after the stainless steel air cooling, belong to ferrite+martensite duplex stainless steel.
Below the design of composition of steel of the present invention is described:
C:C is the important element in stainless steel, the invention belongs to low-carbon (LC) Fe-Cr stainless steel, and C has the effect that enlarges austenitic area in steel, can improve the intensity of iron, but significantly reduces the moulding of steel, toughness.Yet the increase of C is easy to Cr in steel and is combined, and at crystal boundary, forms rich chromium carbide, cause the Cr dilution and cause intergranular corrosion and corrosion proof decline.Therefore, controlling C quality percentage composition is 0.010～0.015.
The increase of Si:Si content, can make the moulding of steel, toughness descend, and solidity to corrosion reduces, thereby affects the weldability of steel.Therefore, should reduce as far as possible silicone content in steel.It is 0.20～0.60 that the present invention controls its quality percentage composition.
Mn:Mn is austenite former, can be used to replace Ni element expensive in steel, but only limits to organizationally as obtaining the austenite Ni of anti-the generation, can not be for nickel aspect solidity to corrosion.It is unhelpful that the add-on of Mn is crossed multipair solidity to corrosion.
Cr: along with Cr content in steel increases, Susceptibility To Intergranular Corrosion descends, and the intensity of steel also can improve, but the plasticity of steel, toughness and cold formability etc. can decrease.Cr can significantly improve stainless oxidation-resistance, anti-cure and hot strength.
P:P is impurity element in steel, harmful to the moulding of steel, toughness, the performance such as anti-corrosion, reduces as far as possible in process of production P content in steel, reduces its deleterious effect.
S:S is impurity element in steel, all unfavorable to high-temp plastic, toughness, the corrosion resisting property of steel, reduces as far as possible in process of production S content in steel, reduces its deleterious effect.
Ni:Ni is austenite former.May promote the stability of passivation film on stainless steel surface, some stainless temperature limit of brittleness of the transition temperature that can make to enbrittle move down.Ni can improve cold formability and the weldability of steel.
N:N is austenite former, can improve the intensity of steel, but the low-temperature impact ability of ferritic stainless steel is existed to disadvantageous effect.Separating out of nitride be unfavorable for stabilizing and increasing of steel intergranular corrosion resistance ability containing promoting in the stainless steel of Nb, Ti.
Cu: along with the increase of Cu content in steel, stainless thermoplasticity reduces, thereby affects the hot workability of steel.Therefore controlling its quality percentage composition is≤0.20.
O:O has disadvantageous effect to the purity of steel, along with oxide inclusion in the raising steel of O content increases, affects surface quality and the performance of steel.Therefore in steel, O content is controlled lower level as far as possible.Controlling O content is mainly to consider that oxygen content in steel and inclusion content have relation, controls total O content and can reduce as far as possible inclusion content, improves formability.
Ti:Ti is stabilizing element, is again ferrite former, strong with the bonding force of carbon, nitrogen in steel, by the combination with C, forms TiC, has avoided the formation of Cr carburet thing, has improved the ability of the intergranular corrosion resistance of steel.But too much adding of Ti, can make the surface quality of steel worsen.The preferred mass percentage composition is 0.15～0.25, has both guaranteed the corrosion resistance nature of steel, and main consideration guarantees the material surface quality again.
C+N: avoid C, N element in the too high reduction that causes the low-temperature flexibility of steel of the total amount of steel.During C+N content in steel≤0.030, by technology controlling and process, can make more than-40 ℃ of ballistic works of steel reach 40J.
Simultaneously, the present invention controls stainless fabrication process condition:
Complete hot strip rolling in the austenitic area of steel (950～1100 ℃), can avoid the disadvantageous effect of second-phase tissue to thermal distortion.
After hot strip rolling completes, be cooled to rapidly 760 ℃ can leave strip steel rolling deformation process in fully the crystal grain state, the disperse distribution of precipitate, the high dislocation state in tissue of refinement, for the product yield strength that improves steel lays a good foundation.
The band steel completes and batches at 760 ℃, and air cooling completed the transformation of part austenite to ferritic structure to room temperature, for next step thermal treatment of band steel lays the foundation.
Hot rolled strip is anneal in bell furnace.Bell type annealing furnace is with inside and outside cover, and coil of strip is vertically placed on inner cover, uses gas heating between inside and outside cover.But the vertical stack of coil of strip, a stove can be piled up neatly and puts 3～4 coil of strips, fills bell furnace with coil of strip and is as the criterion.There is the forced convection blower fan stove inside, is convenient to the temperature in even stove, improves the rate of heating of coil of strip.Belt steel thickness can be 3～30mm, and width is not limit, and band steel coil of strip weight is less than 30t.After the temperature that is heated to 700～750 ℃ through integral body with the steel coil of strip, soaking time 20～30 hours, concrete soaking time is pressed calculating in 30mm/ hour.Then coil of strip cools to 500 ℃ with the furnace, removes outer cover, after continuing to be cooled to below 400 ℃, can remove inner cover.After heat treatment, the band steel mechanical property can reach target call to coil of strip, and makes the strip property homogenizing.
With existing hot rolling thermoforming, with steel plate, compare, the present invention has following beneficial effect:
Adopt processing method of the present invention, can take full advantage of hot-rolled production process, by hot rolling technology and heat treatment phase combination, realized the strip property homogenizing, improved band steel yield strength and unit elongation performance level.And created good base material condition for the raising with the welding property of steel.
Method of the present invention can make the composition of steel be utilized effectively, obtaining under identical high-intensity condition, reduced the production cost with the steel finished product, saved the alloy raw material resource, change the ferrite stainless hardness of steel and be difficult to the technical bottleneck improved, make low-cost ferrite-Martensite Stainless Steel obtain higher yield strength and tensile strength properties after thermal treatment, and plasticity is preferably arranged, meet the needs of deformation processing.
B4003M lorry through this explained hereafter is organized the abundant refinement of grain fineness number with stainless steel, and crystal grain diameter reaches 2～8 μ m.Titaniferous compound in steel, niobide disperse educt, because thermal treatment temp is lower, larger with the dislocation desity in structure of steel, amid all these factors, the disperse educt of grain refining, titanium niobide, larger dislocation desity have all played the effect made with hardness of steel, and have guaranteed that the band steel has extension property preferably.
More than band steel yield strength of the present invention reaches 350MPa, unit elongation reaches more than 25%.On whole band steel length, strip property is very even, has improved the lumber recovery of finished strip.
Embodiment
According to the chemical composition requirement of steel grade of the present invention, through smelting, continuous casting, hot rolling, annealing, pickling to manufacture the steel sample of different size.The chemical composition that table 1 is the embodiment steel, table 2 is control temperature of technological process, table 3 is that the embodiment steel is incubated the mechanical property after 20 hours at described temperature, according to GB GB/T 228-2002 metallic substance tensile test at room temperature method, records.
The chemical composition of table 1 embodiment (wt%)
| Sequence number | C | Si | Mn | P | S | Cr | Ni | N | Ti |
| 1 | 0.010 | 1.00 | 2.50 | 0.040 | 0.010 | 11.0 | 0.60 | 0.020 | 0.10 |
| 2 | 0.011 | 0.80 | 2.00 | 0.030 | 0.005 | 11.5 | 0.70 | 0.015 | 0.15 |
| 3 | 0.012 | 0.60 | 1.80 | 0.020 | 0.003 | 12.5 | 0.80 | 0.013 | 0.20 |
| 4 | 0.013 | 0.40 | 1.30 | 0.010 | 0.001 | 13.0 | 0.90 | 0.010 | 0.25 |
| 5 | 0.015 | 0.20 | 0.80 | 0.025 | 0.002 | 12.0 | 1.0 | 0.007 | 0.30 |
Table 2 technological process is controlled temperature
| Sequence number | Soaking temperature | Final rolling temperature | Coiling temperature |
| 1 | 1070 | 950 | 760 |
| 2 | 1080 | 960 | 750 |
| 3 | 1090 | 970 | 740 |
| 4 | 1100 | 955 | 770 |
| 5 | 1110 | 965 | 780 |
Table 3 embodiment steel mechanical property
Claims (9)
1. a high-performance B4003M lorry stainless steel, its composition quality degree is:
C： 0.010～0.015
Si： 0.20～0.60
Mn： 0.80～2.5
Cr： 11.0～13.0
P： ≤0.040
S： ≤0.010
Ni： 0.60～1.5
N： ≤0.020
Cu： ≤0.20
O： ≤0.0050
Ti： 0.10～0.30
C+N： ≤0.030
All the other are Fe and inevitable impurity;
Described stainless steel is the method manufacture by comprising following steps:
Smelting, continuous casting, hot rolling, annealing, pickling, described hot rolling comprises heating, roughing, finish rolling, cooling and batch successively;
Described heating comprises heat-recovery section, preheating section, heating I section, heating II section and soaking zone successively;
Described hot rolling is carried out at 950-1100 ℃;
Described cooling, speed control is at 30～60 ℃/s;
Described batching, temperature is 760 ℃;
Described annealing is carried out in bell furnace, and temperature is 700～750 ℃; Heat-up rate is 200 ℃/hs; Soaking time is 30mm/ hour.
2. high-performance B4003M lorry stainless steel as claimed in claim 1, wherein
C： 0.010～0.015
Si： 0.20～0.60
Mn： 1.40～1.60
Cr： 11.5～12.5
Ni： 0.80～1.00
N： 0.007～0.015
Ti： 0.15～0.25。
3. high-performance B4003M lorry stainless steel as claimed in claim 1, is characterized in that, described roughing deformation rate is 75%～85%, and extreme trace time rolling deformation velocity range is 8s
-1～12s
-1, temperature out is greater than 980 ℃.
4. high-performance B4003M lorry stainless steel as claimed in claim 1, is characterized in that, the extreme trace of described finish rolling time rolling deformation velocity range is 60s
-1～90s
-1, temperature out is greater than 950 ℃.
5. high-performance B4003M lorry stainless steel as claimed in claim 1, is characterized in that, described heat-recovery section temperature is 700 ℃～900 ℃, and be 45～55 minutes heat-up time.
6. high-performance B4003M lorry stainless steel as claimed in claim 1, is characterized in that, described preheating section temperature is 700 ℃～900 ℃, and be 30～40 minutes heat-up time.
7. high-performance B4003M lorry stainless steel as claimed in claim 1, is characterized in that, described heating I section temperature is 900～1000 ℃, and be 30～40 minutes heat-up time.
8. high-performance B4003M lorry stainless steel as claimed in claim 1, is characterized in that, described heating II section temperature is 1000～1100 ℃, and be 30～40 minutes heat-up time.
9. high-performance B4003M lorry stainless steel as claimed in claim 1, is characterized in that, described soaking zone temperature is 1070～1120 ℃, and soaking time is 30～40 minutes.
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| Publication number | Priority date | Publication date | Assignee | Title |
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| CN102534425A (en) * | 2012-01-29 | 2012-07-04 | 宝山钢铁股份有限公司 | Low-cost high-strength ferritic stainless steel and manufacturing method thereof |
| CN102586580A (en) * | 2012-03-12 | 2012-07-18 | 溧阳市宏大机械设备有限公司 | Bell-type furnace annealing process for BSYE-N steel belt |
| CN107557696B (en) * | 2016-06-30 | 2019-02-26 | 郑州永通特钢有限公司 | A kind of stainless structural steel of antidetonation |
| CN113166831B (en) * | 2018-12-11 | 2022-11-01 | 杰富意钢铁株式会社 | Ferritic stainless steel sheet and method for producing same |
| CN109930083B (en) * | 2019-03-26 | 2020-07-03 | 山西太钢不锈钢股份有限公司 | Low-nickel low-chromium stainless steel and manufacturing method thereof |
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| CN101135028A (en) * | 2006-08-30 | 2008-03-05 | 宝山钢铁股份有限公司 | High-strength stainless steel and thermal treatment process |
| CN201083461Y (en) * | 2007-07-19 | 2008-07-09 | 宝山钢铁股份有限公司 | Heat accumulation type bar plate heating stove |
| CN101538684A (en) * | 2008-09-23 | 2009-09-23 | 山西太钢不锈钢股份有限公司 | Stainless steel tube for brake system of rail vehicle and method for producing same |
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