CN103484763A - Vehicle shaft tube steel for high frequency induction welding, and production method thereof - Google Patents
Vehicle shaft tube steel for high frequency induction welding, and production method thereof Download PDFInfo
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Abstract
The present invention discloses a vehicle shaft tube steel for high frequency induction welding, wherein the vehicle shaft tube steel comprises, 0.07-0.09% of C, less than or equal to 0.04% of Si, 1.7-1.9% of Mn, 0.08-0.12% of Ti, 0.01-0.06% of Al, less than or equal to 0.02% of P, less than or equal to 0.01% of S, less than or equal to 0.008% of N, and the balance of Fe and inevitable impurities. The invention further discloses a method for producing the vehicle shaft tube steel for high frequency induction welding. According to the vehicle shaft tube steel for high frequency induction welding and the production method, the low cost component design is adopted, optimization of parameters of processes such as smelting, rolling, coiling and the like is combined, and grain refining reinforcement, precipitation reinforcement and other reinforcement effects are completely provided to produce the 750-850 MPa grade vehicle shaft tube hot rolling strip steel, wherein the steel has good elongation of more than 18%, a strength of 750-880 MPa, excellent cold bending performance and excellent welding property, and is suitable for high frequency induction welding and pipe production forming processes.
Description
Technical field
The present invention relates to the vehicle steel production technical field, particularly a kind of automobile shafts tube steel and production method thereof that is applicable to high frequency induction welding.
Background technology
The lightweight of automobile, be exactly under the prerequisite of the intensity that guarantees automobile and safety performance, the kerb weight of reduce automobile, thus the dynamic property of raising automobile reduces fuel consumption, reduces exhaust pollution.Make a general survey of the present situations such as China's energy shortage, road overload and conveying efficiency are low, due to environmental protection and energy-conservation needs, automotive light weight technology not only becomes the task of top priority of Domestic Automotive Industry development, also becomes the trend of world car development.Particularly, in heavily card and special-purpose vehicle, semitrailer industry, apply more high-intensity material and can alleviate significantly complete vehicle weight, improve load, improve the work-ing life of vehicle, the benefit of bringing to logistics company is to improve conveying efficiency, significantly reduces logistics cost, and the energy-saving and emission-reduction social benefit is remarkable.
For the automobile shafts tube steel, prior art generally adopts traditional axle tube steel or the weldless steel tube of intensity lower than 550MPa.In order to adapt to the requirement of automotive light weight technology, and fatigue strength and the torque resistant performance of raising material, some high-strength steel iron materials start to be applied on the automobile central siphon.A kind of high-strength semi-trailer shaft tube and production method thereof have been introduced in number of patent application 200910185786.8, the alloying constituent of steel pipe and percentage composition are: C:0.23～0.28, Si:0.15～0.30, Mn:1.30～1.45, P≤0.030, S≤0.035, Al≤0.01, Cu≤0.025, Ni≤0.25, Cr≤0.25, Mo≤0.15, surplus is iron; Production technique is raw material through steel billet processed, perforation, tube rolling, and hot size.
Aspect the starting material and production technology thereof of automobile shafts tube steel, existing production technology has following several respects deficiency at present:
(1) space that intensity rank still is improved, the high-strength material that tensile strength is greater than 750MPa is equally applicable to manufacture the automobile central siphon, and has higher fatigue strength and torque resistant performance.
(2) the automobile central siphon that the HFI welding mode is produced, flatten and the hole enlargement performance has much room for improvement, and requires material to have a good plastic deformation ability high-intensity simultaneously, and this just requires to improve the yield tensile ratio of material unit elongation and control material.
Summary of the invention
Technical problem to be solved by this invention is to provide a kind of intensity, torque resistant performance, fatigue property and unit elongation that can improve existing automobile shafts tube steel, can also reduce the automobile shafts tube steel and the production method thereof that are applicable to high frequency induction welding of existing automobile shafts tube steel yield tensile ratio simultaneously.
One aspect of the present invention, provide a kind of automobile shafts tube steel that is applicable to high frequency induction welding, C:0.07～0.09%; Si :≤0.04%; Mn:1.7～1.9%; Ti:0.08～0.12%; Al:0.01～0.06%; P :≤0.02%; S :≤0.01%; N :≤0.008%; All the other are Fe and inevitable impurity.
Another aspect of the present invention, provide a kind of above-mentioned method that is applicable to the automobile shafts tube steel of high frequency induction welding of producing, and comprising:
Molten iron is obtained to half molten steel through converter or electrosmelting;
After half molten steel is passed through to LF refining or RH vacuum-treat, carry out continuous casting and obtain slab;
Described slab is heated, heating and temperature control is at 1260～1300 ℃, soaking time is greater than 180 minutes, slab after heating again obtains hot-rolled sheet through roughing, finish rolling, the finish rolling temperature in is 1050 ℃～1100 ℃, finishing temperature is 860～900 ℃, then described hot-rolled sheet is carried out to laminar flow cooling, coils into finished product after cooling.
Further, it is cooling that described hot-rolled sheet employing leading portion cooling mode carries out laminar flow, and the target coiling temperature is 610 ℃～640 ℃.
Further, the chemical composition of described slab is by weight percentage: C:0.07～0.09%; Si :≤0.04%; Mn:1.7～1.9%; Ti:0.08～0.12%; Al:0.01～0.06%; P :≤0.02%; S :≤0.01%; N :≤0.008%; All the other are Fe and inevitable impurity.
A kind of automobile shafts tube steel and production method thereof that is applicable to high frequency induction welding provided by the invention, adopt low-cost Composition Design, in conjunction with smelting, rolling, the curling process parameter optimizing that waits, give full play to refined crystalline strengthening, the strengthening effects such as precipitation strength, produce 750MPa～effective hot rolled strip of 850MPa level automobile shafts, there is good unit elongation, intensity can reach 750MPa～880MPa, unit elongation is greater than 18%, clod wash and welding property are good, be applicable to HFI welding and tubulation moulding process, can be used for producing the automobile central siphon, effectively realize the attenuate of material thickness, can effectively realize lightweight under the prerequisite that guarantees vehicle safety, there is cost of alloy low, the rolling technology process is easy to the characteristics that realize.
Embodiment
A kind of automobile shafts tube steel that is applicable to high frequency induction welding that the embodiment of the present invention provides, its chemical composition is by weight percentage: C:0.07～0.09%; Si :≤0.04%; Mn:1.7～1.9%; Ti:0.08～0.12%; Al:0.01～0.06%; P :≤0.02%; S :≤0.01%; N :≤0.008%; All the other are Fe and inevitable impurity.
The embodiment of the present invention provides a kind ofly produces the above-mentioned method that is applicable to the automobile shafts tube steel of high frequency induction welding, specifically comprises the following steps:
Step S1: molten iron is obtained to half molten steel through converter or electrosmelting;
Step S2: after half molten steel is passed through to LF refining or RH vacuum-treat, carry out continuous casting and obtain slab, the chemical composition of slab is by weight percentage: C:0.07～0.09%; Si :≤0.04%; Mn:1.7～1.9%; Ti:0.08～0.12%; Al:0.01～0.06%; P :≤0.02%; S :≤0.01%; N :≤0.008%; All the other are Fe and inevitable impurity.
Step S3, described slab is heated, then obtained hot-rolled sheet through roughing, finish rolling, then described hot-rolled sheet is carried out to laminar flow cooling, coiled into hot rolled coil after cooling.
Wherein, step S3 is heated slab, then obtains hot-rolled sheet through roughing, finish rolling, then hot-rolled sheet is carried out to laminar flow cooling, coils into hot rolled coil after cooling to comprise the following steps:
Step S31, slab is heated, Heating temperature is 1260～1300 ℃;
Step S32: slab is obtained to needed width of plate slab, obtains intermediate blank through two roller roughing, four roller roughing again through fixed-width pressure machine.
Step S33: enable stay-warm case between roughing and finish rolling, guarantee the homogeneity of intermediate blank temperature, soaking time is greater than soaking time and is controlled at 180 minutes.
Step S34: intermediate blank is obtained to hot-rolled sheet through finishing train.The finish rolling temperature in is controlled at 1050 ℃～1100 ℃, and finishing temperature is controlled at 860～900 ℃; .
Step S35: hot-rolled sheet is coiled into to hot rolled coil by reeling machine after laminar flow is cooling.The cooling employing leading portion of laminar flow cooling mode, the target coiling temperature is 610 ℃～640 ℃.
Main alloy element effect of the present invention and limited range are as follows:
Carbon: carbon is to improve the most economical effective element of the strength of materials, is also the required element of TiC precipitation strength, but the C too high levels easily causes plasticity and weldability to descend.For producing the automobile shafts tube steel, consider that user's molding mode is high frequency induction welding, the carbon content setting range that the present invention adopts is 0.07%～0.09%.
Silicon: silicon is the solution strengthening element, but adding too high silicon can have a negative impact to the plasticity of material, reduce Si is of value to and avoids occurring surperficial red scale simultaneously, because part automobile factory does not carry out surface treatment in central siphon is used, therefore should guarantee former steel plate surface non-oxidation iron sheet.Therefore, to add silicone content be≤0.04% in the present invention.
Manganese: manganese has solution strengthening effect, can improve material hardening capacity, be to improve one of strength of materials important element, but manganese content adds too high easy generation segregation and can reduce toughness of material, degrade performance simultaneously.Should guarantee serious center segregation not occur for the automobile shafts tube steel, avoid ftractureing in follow-up use, therefore the Mn upper limit is set as to 1.9%, it is 1.70%～1.90% that the present invention adds manganese content.
Sulphur and phosphorus: the too high meeting of sulphur and phosphoric has disadvantageous effect to toughness of material and plasticity.The present invention defines sulphur content and should be controlled in 0.01%, and phosphorus content should be controlled in 0.02%.
Aluminium: aluminium is deoxidant element, has certain grain refining effect simultaneously.It is 0.01%～0.06% that the present invention defines aluminium content.
Titanium: the precipitating reinforcing effect that takes full advantage of Ti improves intensity.The present invention adds 0.08%～0.12% Ti and coordinates suitable production technique, obtains the precipitate of the TiC that a large amount of small and disperseds distribute, when keeping material to have good plasticity and toughness, has significantly improved strength level.But precipitation strength is greater than tensile strength to the contribution of material yield intensity, be easy to make the yield tensile ratio of steel to rise, therefore, the upper limit that this patent limits Ti is no more than 0.12%.
Nitrogen: nitrogen content too high can severe exacerbation plasticity and the toughness of material, particularly for Ti micro-alloyed high strength steel, due to N and Ti, at high temperature be combined the TiN of production large-size, affect toughness and the fatigue property of material.Therefore, the present invention limits nitrogen content and should be less than 0.008%.
The present invention has adopted a kind of low-alloy cost composition system: lower carbon and manganese content, do not add the precious alloy elements such as Nb, Mo, Ni, Cu, Cr, take full advantage of the precipitating reinforcing effect of Ti, obtain tiny, uniform ferrite crystal grain in conjunction with suitable cooling controlling and rolling controlling process, thereby make material there is good obdurability coupling, the composition system carbon equivalent that the present invention adopts all is controlled in 0.40, cooling cracks the susceptible index number is controlled in 0.20%, material has good welding property, is applicable to the high frequency induction welding of central siphon manufacturing processed.
The controlling of production process main points that the present invention adopts are that smelting process is strictly controlled P, S, N content, guarantees slab quality.The operation of rolling is strictly controlled each controlled rolling and cooling process parameter.
The Heating temperature that the present invention adopts is 1260 ℃～1300 ℃, and soaking time is greater than 180 minutes, adopts the purpose of higher Heating temperature to be to guarantee more abundant as the compound dissolution of the Ti that forms in strand of austenite homogenizing and alloying element; Correlation test of the present invention shows, when Heating temperature, during lower than 1250 ℃, TiC is back dissolving fully, reduces the intensity of final material;
Adopt the two-stage control rolling, it is 1050 ℃～1100 ℃ that finishing stands need strictly be controlled the finish rolling temperature according to the finished product thickness specification, and finishing temperature is 860～900 ℃; Higher rolling temperature is conducive to obtain good online plate shape, and the simultaneously raising of rolling temperature will reduce the anisotropic of hot continuously-rolled strip, reduce the transverse and longitudinal performance difference of material.
It is cooling that steel band goes out after finish rolling to adopt the leading portion cooling mode to carry out laminar flow, is conducive on the one hand to strengthen the build up after phase transformation, is conducive on the other hand strengthen precipitating reinforcing effect, obtains the tiny product of separating out in more ferrites, thereby effectively improve the strength of materials.The target coiling temperature that the present invention adopts is 610 ℃～640 ℃, and adopting higher coiling temperature is the key that obtains good yield strength and tensile strength coupling, is conducive to control the yield tensile ratio of material lower than 0.90%.
A kind of automobile shafts tube steel and production method thereof that is applicable to high frequency induction welding that the embodiment of the present invention provides, adopt low-cost Composition Design, in conjunction with smelting, rolling, the curling process parameter optimizing that waits, give full play to refined crystalline strengthening, the strengthening effects such as precipitation strength, produce 750MPa～effective hot rolled strip of 850MPa level automobile shafts, there is good unit elongation, intensity can reach 750MPa～880MPa, unit elongation is greater than 18%, clod wash and welding property are good, be applicable to HFI welding and tubulation moulding process, can be used for producing the automobile central siphon, effectively realize the attenuate of material thickness, can effectively realize lightweight under the prerequisite that guarantees vehicle safety, there is cost of alloy low, the rolling technology process is easy to the characteristics that realize.
Below in conjunction with embodiment, the present invention is further detailed explanation:
The embodiment of the present invention adopts 220 tons of converter smeltings, and 1580 hot continuous rolling production lines are rolled.
Embodiment 1:
To smelt in 220 tons of converters and become strand through the continuous casting of molten steel of external refining, its weight percent is C:0.07%, Si:0.03%, Mn:1.75%, P:0.012%, S:0.003%, Al:0.041%, Ti:0.09%, N:0.004%, and all the other are Fe and inevitable impurity.Slab thickness is 230mm.
At 1580 hot continuous rolling production lines, be rolled, Heating temperature is 1260 ℃, and the finish rolling temperature in is 1060 ℃, and finishing temperature is 860 ℃, and target thickness is 6mm, rolls by cooling 640 ℃ of the target coiling temperatures that are chilled to of laminar flow, batches rear air cooling to room temperature.
The high-strength steel yield strength Rel produced according to above method is 670MPa, and tensile strength is 750MPa, and unit elongation is 22%, clod wash D=1.5a surface flawless.
Embodiment 2:
To smelt in 220 tons of converters and become strand through the continuous casting of molten steel of external refining, its weight percent is C:0.075%, Si:0.001%, Mn:1.80%, P:0.002%, S:0.001%, Al:0.041%, Ti:0.10%, N:0.004%, and all the other are Fe and inevitable impurity.Slab thickness is 230mm.
At 1580 hot continuous rolling production lines, be rolled, Heating temperature is 1270 ℃, and the finish rolling temperature in is 1070 ℃, and finishing temperature is 880 ℃, and target thickness is 5mm, rolls by cooling 620 ℃ of the target coiling temperatures that are chilled to of laminar flow, batches rear air cooling to room temperature.
The high-strength steel yield strength Rel produced according to above method is 715MPa, and tensile strength is 800MPa, and unit elongation is 20%, clod wash D=1.5a surface flawless.
Embodiment 3:
To smelt in 220 tons of converters and become strand through the continuous casting of molten steel of external refining, its weight percent is C:0.082%, Si:0.0003%, Mn:1.82%, P:0.0025%, S:0.0013%, Al:0.051%, Ti:0.085%, N:0.0004%, and all the other are Fe and inevitable impurity.Slab thickness is 230mm.
At 1580 hot continuous rolling production lines, be rolled, Heating temperature is 1290 ℃, and the finish rolling temperature in is 1080 ℃, and finishing temperature is 890 ℃, and target thickness is 4mm, rolls by cooling 610 ℃ of the target coiling temperatures that are chilled to of laminar flow, batches rear air cooling to room temperature.
The high-strength steel yield strength Rel produced according to above method is 725MPa, and tensile strength is 810MPa, and unit elongation is 20%, clod wash D=1.5a surface flawless.
Embodiment 4:
To smelt in 220 tons of converters and become strand through the continuous casting of molten steel of external refining, its weight percent is C:0.09%, Si:0.04%, Mn:1.85%, P:0.013%, S:0.002%, Al:0.044%, Ti:0.11%, N:0.004%, and all the other are Fe and inevitable impurity.Slab thickness is 230mm.
At 1580 hot continuous rolling production lines, be rolled, Heating temperature is 1265 ℃, and the finish rolling temperature in is 1065 ℃, and finishing temperature is 865 ℃, and target thickness is 6mm, rolls by cooling 640 ℃ of the target coiling temperatures that are chilled to of laminar flow.
The high-strength steel yield strength Rel produced according to above method is 715MPa, and tensile strength is 795MPa, and unit elongation is 22%, clod wash D=1.5a surface flawless.
Embodiment 5:
To smelt in 220 tons of converters and become strand through the continuous casting of molten steel of external refining, its weight percent be identical with embodiment 4.Slab thickness is 230mm.
At 1580 hot continuous rolling production lines, be rolled, Heating temperature is 1270 ℃, and the finish rolling temperature in is 1070 ℃, and finishing temperature is 870 ℃, and target thickness is 5mm, rolls by cooling 630 ℃ of the target coiling temperatures that are chilled to of laminar flow.
The high-strength steel yield strength Rel produced according to above method is 745MPa, and tensile strength is 830MPa, and unit elongation is 21.5%, clod wash D=1.5a surface flawless.
Embodiment 6:
To smelt in 220 tons of converters and become strand through the continuous casting of molten steel of external refining, its weight percent be identical with embodiment 4.Slab thickness is 230mm.
At 1580 hot continuous rolling production lines, be rolled, Heating temperature is 1290 ℃, and the finish rolling temperature in is 1090 ℃, and finishing temperature is 895 ℃, and target thickness is 4mm, rolls by cooling 620 ℃ of the target coiling temperatures that are chilled to of laminar flow.
The high-strength steel yield strength Rel produced according to above method is 760MPa, and tensile strength is 850MPa, and unit elongation is 21%, clod wash D=1.5a surface flawless.
Embodiment 7:
To smelt in 220 tons of converters and become strand through the continuous casting of molten steel of external refining, its weight percent is C:0.085%, Si:0.03%, Mn:1.80%, P:0.013%, S:0.002%, Al:0.044%, Ti:0.10%, N:0.004%, and all the other are Fe and inevitable impurity.Slab thickness is 230mm.
At 1580 hot continuous rolling production lines, be rolled, Heating temperature is 1280 ℃, and the finish rolling temperature in is 1075 ℃, and finishing temperature is 860 ℃, and target thickness is 7mm, rolls by cooling 630 ℃ of the target coiling temperatures that are chilled to of laminar flow.
The high-strength steel yield strength Rel produced according to above method is 700MPa, and tensile strength is 780MPa, and unit elongation is 21%, clod wash D=1.5a surface flawless.
Embodiment 8:
To smelt in 220 tons of converters and become strand through the continuous casting of molten steel of external refining, its weight percent be identical with embodiment 7.Slab thickness is 230mm.
At 1580 hot continuous rolling production lines, be rolled, Heating temperature is 1300 ℃, and the finish rolling temperature in is 1100 ℃, and finishing temperature is 900 ℃, and target thickness is 3mm, rolls by cooling 620 ℃ of the target coiling temperatures that are chilled to of laminar flow.
The high-strength steel yield strength Rel produced according to above method is 755MPa, and tensile strength is 845MPa, and unit elongation is 20%, clod wash D=1.5a surface flawless.
It should be noted last that, above embodiment is only unrestricted in order to technical scheme of the present invention to be described, although with reference to example, the present invention is had been described in detail, those of ordinary skill in the art is to be understood that, can modify or be equal to replacement technical scheme of the present invention, and not breaking away from the spirit and scope of technical solution of the present invention, it all should be encompassed in the middle of claim scope of the present invention.
Claims (4)
1. an automobile shafts tube steel that is applicable to high frequency induction welding, is characterized in that, comprising:
C:0.07～0.09%; Si :≤0.04%; Mn:1.7～1.9%; Ti:0.08～0.12%; Al:0.01～0.06%; P :≤0.02%; S :≤0.01%; N :≤0.008%; All the other are Fe and inevitable impurity.
2. produce a kind of method that is applicable to the automobile shafts tube steel of high frequency induction welding as claimed in claim 1 for one kind, it is characterized in that, comprising:
Molten iron is obtained to half molten steel through converter or electrosmelting;
After half molten steel is passed through to LF refining or RH vacuum-treat, carry out continuous casting and obtain slab;
Described slab is heated, heating and temperature control is at 1260～1300 ℃, soaking time is greater than 180 minutes, slab after heating again obtains hot-rolled sheet through roughing, finish rolling, the finish rolling temperature in is 1050 ℃～1100 ℃, finishing temperature is 860～900 ℃, then described hot-rolled sheet is carried out to laminar flow cooling, coils into finished product after cooling.
3. the production method that is applicable to the automobile shafts tube steel of high frequency induction welding as claimed in claim 2 is characterized in that:
It is cooling that described hot-rolled sheet employing leading portion cooling mode carries out laminar flow, and the target coiling temperature is 610 ℃～640 ℃.
4. the production method that is applicable to the automobile shafts tube steel of high frequency induction welding as claimed in claim 2 is characterized in that:
The chemical composition of described slab is by weight percentage: C:0.07～0.09%; Si :≤0.04%; Mn:1.7～1.9%; Ti:0.08～0.12%; Al:0.01～0.06%; P :≤0.02%; S :≤0.01%; N :≤0.008%; All the other are Fe and inevitable impurity.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201310412944.5A CN103484763B (en) | 2013-09-11 | It is applicable to automobile shafts tube steel and the production method thereof of high frequency induction welding |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201310412944.5A CN103484763B (en) | 2013-09-11 | It is applicable to automobile shafts tube steel and the production method thereof of high frequency induction welding |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN103484763A true CN103484763A (en) | 2014-01-01 |
| CN103484763B CN103484763B (en) | 2016-11-30 |
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101624676A (en) * | 2009-07-15 | 2010-01-13 | 东北大学 | Hot-rolled beam steel with a tensile strength of more than 710MPa and preparation method thereof |
| CN102363858A (en) * | 2011-11-03 | 2012-02-29 | 首钢总公司 | High-strength steel for 750 to 880 MPa-level vehicles and production method thereof |
| WO2013011660A1 (en) * | 2011-07-20 | 2013-01-24 | Ｊｆｅスチール株式会社 | High-strength steel sheet for warm forming and process for producing same |
Patent Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101624676A (en) * | 2009-07-15 | 2010-01-13 | 东北大学 | Hot-rolled beam steel with a tensile strength of more than 710MPa and preparation method thereof |
| WO2013011660A1 (en) * | 2011-07-20 | 2013-01-24 | Ｊｆｅスチール株式会社 | High-strength steel sheet for warm forming and process for producing same |
| CN102363858A (en) * | 2011-11-03 | 2012-02-29 | 首钢总公司 | High-strength steel for 750 to 880 MPa-level vehicles and production method thereof |
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Address after: 100041 Shijingshan Road, Beijing, No. 68, No. Patentee after: Shougang Group Co. Ltd. Address before: 100041 Shijingshan Road, Beijing, No. 68, No. Patentee before: Capital Iron & Steel General Company |
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