CN103484763B - It is applicable to automobile shafts tube steel and the production method thereof of high frequency induction welding - Google Patents
It is applicable to automobile shafts tube steel and the production method thereof of high frequency induction welding Download PDFInfo
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- CN103484763B CN103484763B CN201310412944.5A CN201310412944A CN103484763B CN 103484763 B CN103484763 B CN 103484763B CN 201310412944 A CN201310412944 A CN 201310412944A CN 103484763 B CN103484763 B CN 103484763B
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 54
- 239000010959 steel Substances 0.000 title claims abstract description 54
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 25
- 238000003466 welding Methods 0.000 title claims abstract description 24
- 230000001939 inductive effect Effects 0.000 title claims abstract description 17
- 238000005096 rolling process Methods 0.000 claims abstract description 41
- 229910052710 silicon Inorganic materials 0.000 claims abstract description 16
- 238000003723 Smelting Methods 0.000 claims abstract description 15
- 229910052757 nitrogen Inorganic materials 0.000 claims abstract description 15
- 229910052717 sulfur Inorganic materials 0.000 claims abstract description 15
- 229910052782 aluminium Inorganic materials 0.000 claims abstract description 14
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 14
- 229910052698 phosphorus Inorganic materials 0.000 claims abstract description 13
- 229910052719 titanium Inorganic materials 0.000 claims abstract description 12
- 239000012535 impurity Substances 0.000 claims abstract description 11
- 239000000203 mixture Substances 0.000 claims abstract description 7
- 238000001816 cooling Methods 0.000 claims description 27
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 23
- 229910052742 iron Inorganic materials 0.000 claims description 5
- 238000010438 heat treatment Methods 0.000 claims description 4
- 230000014759 maintenance of location Effects 0.000 claims description 4
- 239000000126 substance Substances 0.000 claims description 4
- 238000009749 continuous casting Methods 0.000 claims description 3
- 238000000034 method Methods 0.000 abstract description 11
- 238000005728 strengthening Methods 0.000 abstract description 10
- 230000000694 effects Effects 0.000 abstract description 6
- 238000001556 precipitation Methods 0.000 abstract description 5
- 238000000465 moulding Methods 0.000 abstract description 4
- 239000000463 material Substances 0.000 description 26
- 239000010936 titanium Substances 0.000 description 17
- 239000011572 manganese Substances 0.000 description 14
- 238000007670 refining Methods 0.000 description 9
- 238000005266 casting Methods 0.000 description 8
- 238000005516 engineering process Methods 0.000 description 8
- IJGRMHOSHXDMSA-UHFFFAOYSA-N nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 6
- OKTJSMMVPCPJKN-UHFFFAOYSA-N carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 5
- 229910052799 carbon Inorganic materials 0.000 description 5
- 229910045601 alloy Inorganic materials 0.000 description 4
- 239000000956 alloy Substances 0.000 description 4
- 239000010703 silicon Substances 0.000 description 4
- 229910034327 TiC Inorganic materials 0.000 description 3
- 238000005275 alloying Methods 0.000 description 3
- REDXJYDRNCIFBQ-UHFFFAOYSA-N aluminium(3+) Chemical class [Al+3] REDXJYDRNCIFBQ-UHFFFAOYSA-N 0.000 description 3
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminum Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 3
- PWHULOQIROXLJO-UHFFFAOYSA-N manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 3
- 230000001376 precipitating Effects 0.000 description 3
- 239000000047 product Substances 0.000 description 3
- 230000003014 reinforcing Effects 0.000 description 3
- NINIDFKCEFEMDL-UHFFFAOYSA-N sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 description 3
- 239000011593 sulfur Substances 0.000 description 3
- 230000001808 coupling Effects 0.000 description 2
- 238000010168 coupling process Methods 0.000 description 2
- 238000005859 coupling reaction Methods 0.000 description 2
- 238000009413 insulation Methods 0.000 description 2
- 229910000529 magnetic ferrite Inorganic materials 0.000 description 2
- OAICVXFJPJFONN-UHFFFAOYSA-N phosphorus Chemical compound [P] OAICVXFJPJFONN-UHFFFAOYSA-N 0.000 description 2
- 239000011574 phosphorus Substances 0.000 description 2
- 239000002994 raw material Substances 0.000 description 2
- 238000005204 segregation Methods 0.000 description 2
- 229910000859 α-Fe Inorganic materials 0.000 description 2
- 241000219307 Atriplex rosea Species 0.000 description 1
- 230000002411 adverse Effects 0.000 description 1
- 238000004458 analytical method Methods 0.000 description 1
- 229910001566 austenite Inorganic materials 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 229910052804 chromium Inorganic materials 0.000 description 1
- 150000001875 compounds Chemical class 0.000 description 1
- 229910052802 copper Inorganic materials 0.000 description 1
- 238000004090 dissolution Methods 0.000 description 1
- 238000009826 distribution Methods 0.000 description 1
- 238000004134 energy conservation Methods 0.000 description 1
- 230000005713 exacerbation Effects 0.000 description 1
- 238000005755 formation reaction Methods 0.000 description 1
- 239000000446 fuel Substances 0.000 description 1
- 238000000265 homogenisation Methods 0.000 description 1
- 238000005098 hot rolling Methods 0.000 description 1
- 239000004615 ingredient Substances 0.000 description 1
- 229910052750 molybdenum Inorganic materials 0.000 description 1
- 229910052759 nickel Inorganic materials 0.000 description 1
- 230000003647 oxidation Effects 0.000 description 1
- 238000007254 oxidation reaction Methods 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 238000010791 quenching Methods 0.000 description 1
- 230000000171 quenching Effects 0.000 description 1
- ATJFFYVFTNAWJD-UHFFFAOYSA-N tin hydride Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 description 1
- RTAQQCXQSZGOHL-UHFFFAOYSA-N titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 1
- 230000001131 transforming Effects 0.000 description 1
- 238000009785 tube rolling Methods 0.000 description 1
Abstract
The invention discloses a kind of automobile shafts tube steel being 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%；Remaining is Fe and inevitable impurity.The invention also discloses a kind of method producing the above-mentioned automobile shafts tube steel being applicable to high frequency induction welding, a kind of automobile shafts tube steel being applicable to high frequency induction welding of present invention offer and production method thereof, use the design of low cost composition, in conjunction with smelting, rolling, the process parameter optimizings such as curling, give full play to refined crystalline strengthening, the strengthening effect such as precipitation strength, produce 750MPa～the 850MPa effective hot-strip of level automobile shafts, there is good elongation percentage, intensity is up to 750MPa～880MPa, elongation percentage is more than 18%, clod wash and welding performance are excellent, it is applicable to HFI welding and tubulation moulding process.
Description
Technical field
The present invention relates to vehicle steel production technical field, particularly to a kind of vapour being applicable to high frequency induction welding
Axletree tube steel and production method thereof.
Background technology
The lightweight of automobile, it is simply that on the premise of the intensity ensureing automobile and security performance, drop as much as possible
The kerb weight of low automobile, thus improve the dynamic property of automobile, reduce fuel consumption, reduce exhaust pollution.
Make a general survey of the present situations such as China's energy shortage, road overload and conevying efficiency are low, due to environmental protection and energy-conservation needs,
Automotive light weight technology the most not only becomes the task of top priority of Domestic Automotive Industry development, also becomes world car development
Trend.Particularly in heavy truck and special-purpose vehicle, semitrailer industry, the material of application higher intensity can significantly subtract
Light complete vehicle weight, improves load, improves the service life of vehicle, has the advantage that raising to logistics company
Conevying efficiency, is greatly reduced logistics cost, and energy-saving and emission-reduction social benefit is notable.
For automobile shafts tube steel, the commonly used intensity of prior art less than 550MPa traditional axle tube steel or
Seamless steel pipe.In order to adapt to the requirement of automotive light weight technology, and improve fatigue strength and the torque resistant performance of material,
Some high strength steel iron materials start to be applied on automobile central siphon.Number of patent application 200910185786.8
In describe a kind of high-strength semi-trailer shaft tube and production method, the alloying component of steel pipe and content percentage
Ratio is: 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 ferrum；Production technology is raw material
Through steel billet processed, perforation, tube rolling and hot size.
At present in terms of the raw material and production technology thereof of automobile shafts tube steel, existing production technology has following several
Aspect is not enough:
(1) space that intensity rank is still improved, the tensile strength high-strength material more than 750MPa is same
It is applicable to manufacture automobile central siphon, and there is higher fatigue strength and torque resistant performance.
(2) the automobile central siphon that HFI welding mode produces, flattens and expanding performance has much room for improvement, it is desirable to
Material has good plastic deformation ability while high intensity, and this just requires to improve material elongation percentage and control
The yield tensile ratio of prepared material.
Summary of the invention
The technical problem to be solved be to provide a kind of can improve existing automobile shafts tube steel intensity,
Torque resistant performance, fatigue behaviour and elongation percentage, can also reduce the suitable of existing automobile shafts tube steel yield tensile ratio simultaneously
Automobile shafts tube steel and production method thereof for high frequency induction welding.
One aspect of the present invention, it is provided that a kind of automobile shafts tube steel being 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%；Remaining is Fe and inevitable impurity.
Another aspect of the present invention, it is provided that a kind of produce the above-mentioned automobile central siphon being applicable to high frequency induction welding
By the method for steel, including:
Molten iron is obtained half molten steel through converter or electric furnace smelting；
After half molten steel is passed through LF refine or RH application of vacuum, carry out continuous casting and obtain slab；
Being heated by described slab, heating and temperature control is at 1260～1300 DEG C, and temperature retention time is more than 180
Minute, then will heating after slab through roughing, finish rolling obtain hot rolled plate, entry temperature at finishing be 1050 DEG C～
1100 DEG C, finishing temperature is 860～900 DEG C, then described hot rolled plate is carried out section cooling, rolls up after cooling
Take into finished product.
Further, described hot rolled plate uses leading portion refrigerating mode to carry out section cooling, and target coiling temperature is
610 DEG C～640 DEG C.
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%；Remaining is Fe and inevitable impurity.
A kind of automobile shafts tube steel being applicable to high frequency induction welding of present invention offer and production method thereof, use
Low cost composition designs, in conjunction with smelting, roll, the process parameter optimizing such as curling, give full play to refined crystalline strengthening,
The strengthening effect such as precipitation strength, produces 750MPa～the 850MPa effective hot-strip of level automobile shafts, has
Good elongation percentage, intensity is more than 18% up to 750MPa～880MPa, elongation percentage, clod wash and weldability
Can be excellent, it is adaptable to HFI welding and tubulation moulding process, can be used for producing automobile central siphon, the most in fact
Now material thickness is thinning, can effectively realize lightweight on the premise of ensureing vehicle safety, has alloy
This is low, the feature that rolling process is easily achieved.
Detailed description of the invention
A kind of automobile shafts tube steel being applicable to high frequency induction welding that the embodiment of the present invention provides, its chemical composition
It 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%；Remaining be
Fe and inevitable impurity.
A kind of side producing the above-mentioned automobile shafts tube steel being applicable to high frequency induction welding that the embodiment of the present invention provides
Method, specifically includes following steps:
Step S1: molten iron is obtained half molten steel through converter or electric furnace smelting；
Step S2: after half molten steel is passed through LF refine or RH application of vacuum, carries out continuous casting and obtains slab, plate
The chemical composition of base 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%；
Remaining is Fe and inevitable impurity.
Step S3, described slab is heated, then obtain hot rolled plate, then by institute through roughing, finish rolling
State hot rolled plate and carry out section cooling, after cooling, coil into hot rolled coil.
Wherein, slab is heated by step S3, then obtains hot rolled plate, then by heat through roughing, finish rolling
Roll plate and carry out section cooling, coil into hot rolled coil after cooling and comprise the following steps:
Step S31, being heated by slab, heating-up temperature is 1260～1300 DEG C；
Step S32: by slab through fixed-width pressure machine obtain required for width of plate slab, again through two roller roughing,
Four roller roughing obtain intermediate blank.
Step S33: enable thermal insulation cover between roughing and finish rolling, it is ensured that the uniformity of intermediate blank temperature, insulation
Time controls at 180 minutes more than temperature retention time.
Step S34: intermediate blank is obtained hot rolled plate through mm finishing mill unit.Entry temperature at finishing controls
1050 DEG C～1100 DEG C, finishing temperature control is at 860～900 DEG C；.
Step S35: hot rolled plate is coiled into hot rolled coil by coiling machine after section cooling.Section cooling uses
Leading portion refrigerating mode, target coiling temperature is 610 DEG C～640 DEG C.
Main alloy element effect of the present invention and the scope of restriction are as follows:
Carbon: carbon is to improve the most economical effective element of the strength of materials, is also element needed for TiC precipitation strength,
But C content is too high is easily caused plasticity and solderability decline.For producing automobile shafts tube steel, it is contemplated that user
Molding mode is high frequency induction welding, and the carbon content set point that the present invention uses is 0.07%～0.09%.
Silicon: silicon is solution strengthening element, but add too high silicon and the plasticity of material can be had a negative impact, with
Time reduce Si and be of value to and avoid the occurrence of surface red scale, due to partial automobile factory in central siphon uses also
Do not carry out surface process, therefore should ensure that former surface of steel plate non-oxidation iron sheet.Therefore, the present invention adds silicon and contains
Amount is for≤0.04%.
Manganese: manganese has solution strengthening effect, can improve material quenching degree simultaneously, is that the raising strength of materials is important
One of element, but Fe content adds too high easy generation segregation and can reduce toughness of material, deteriorates performance.Right
Should ensure that in automobile shafts tube steel and occur without serious center segregation, it is to avoid follow-up use is ftractureed, therefore by Mn
The upper limit is set as 1.9%, and it is 1.70%～1.90% that the present invention adds Fe content.
Sulfur and phosphorus: toughness of material and plasticity are adversely affected by sulfur and the too high meeting of P elements.Present invention defines
Sulfur content should control within 0.01%, and phosphorus content should control within 0.02%.
Aluminum: aluminum is deoxidant element, has certain grain refining effect simultaneously.Present invention defines aluminum content
It is 0.01%～0.06%.
Titanium: the precipitating reinforcing effect making full use of Ti improves intensity.The present invention adds 0.08%～0.12%
Ti coordinates suitable production technology, obtains the precipitate of the TiC of a large amount of small and dispersed distribution, is keeping material
While there are good plasticity and toughness, intensity level is greatly improved.But precipitation strength is to material yield strength
Contribution is more than tensile strength, it is easy to make the yield tensile ratio of steel increase, and therefore, this patent limits the upper limit of Ti and do not surpasses
Cross 0.12%.
Nitrogen: the plasticity of nitrogen content too high meeting severe exacerbation material and toughness is high especially for Ti microalloying
Qiang Gang, is at high temperature combined the TiN producing large-size, affects toughness and the fatigue of material due to N with Ti
Performance.Therefore, the present invention limits nitrogen content and should be less than 0.008%.
Present invention employs a kind of low-alloy cost ingredients system: relatively low carbon and manganese content, without Nb,
The expensive alloying elements such as Mo, Ni, Cu, Cr, make full use of the precipitating reinforcing effect of Ti, in conjunction with suitably
Cooling controlling and rolling controlling process obtains ferrite crystal grain tiny, uniform, so that material has good obdurability
Coupling, the component system carbon equivalent that the present invention uses all controls within 0.40, and cooling cracks the susceptible index number controls
Within 0.20%, material has good welding performance, it is adaptable to the high frequency induction welding of central siphon manufacture process.
The controlling of production process main points that the present invention uses are that smelting process strictly controls P, S, N content, protect
Card slab quality.The operation of rolling strictly controls each controlled rolling and cooling process parameter.
The heating-up temperature that the present invention uses is 1260 DEG C～1300 DEG C, and temperature retention time is more than 180 minutes, uses
The purpose of higher heating-up temperature is to ensure the Ti of formation in austenite homogenization and alloying element such as strand
Compound dissolution more abundant；The correlation test of the present invention shows, when heating-up temperature is less than 1250 DEG C,
TiC can not back dissolving completely, reduce the intensity of final material；
Employing two-stage control rolls, and finishing stands need to strictly control finish rolling entrance temperature according to finished product thickness specification
Degree is 1050 DEG C～1100 DEG C, and finishing temperature is 860～900 DEG C；Higher rolling temperature is conducive to obtaining good
Good online plate shape, the raising of rolling temperature simultaneously, the anisotropic of hot-continuous-rolling strip steel will be reduced, reduce material
The transverse and longitudinal performance difference of material.
Steel band uses leading portion refrigerating mode to carry out section cooling after going out finish rolling, after being on the one hand conducive to strengthening phase transformation
Build up, on the other hand be conducive to strengthening precipitating reinforcing effect, obtain the tiny analysis in more ferrite
Go out product, thus be effectively improved the strength of materials.The target coiling temperature that the present invention uses is 610 DEG C～640 DEG C,
Using higher coiling temperature is to obtain good yield strength and the key of tensile strength coupling, is conducive to controlling
The yield tensile ratio of material is less than 0.90%.
A kind of automobile shafts tube steel being applicable to high frequency induction welding of embodiment of the present invention offer and producer thereof
Method, uses the design of low cost composition, in conjunction with smelting, roll, the process parameter optimizing such as curling, gives full play to
The strengthening effect such as refined crystalline strengthening, precipitation strength, produces 750MPa～the 850MPa effective hot rolling of level automobile shafts
Strip steel, has good elongation percentage, and intensity is up to 750MPa～880MPa, and elongation percentage is more than 18%, cold
Curved excellent with welding performance, it is adaptable to HFI welding and tubulation moulding process, can be used for producing automobile shafts
Pipe, effectively realizes the thinning of material thickness, can effectively realize lightweight on the premise of ensureing vehicle safety,
There is cost of alloy low, the feature that rolling process is easily achieved.
Below in conjunction with embodiment, the present invention is further detailed explanation:
The embodiment of the present invention uses 220 tons of converter smeltings, and 1580 hot continuous rolling production lines roll.
Embodiment 1:
Smelting in 220 tons of converters the molten steel through external refining are casting continuously to form strand, and its percentage by weight 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%, remaining is Fe and inevitable impurity.Slab thickness is 230mm.
Rolling at 1580 hot continuous rolling production lines, heating-up temperature is 1260 DEG C, and entry temperature at finishing is
1060 DEG C, finishing temperature is 860 DEG C, and target thickness is 6mm, is cooled to target through section cooling and batches after rolling
Temperature 640 DEG C, batches rear air cooling to room temperature.
High-strength steel yield strength Rel produced according to above method is 670MPa, and tensile strength is 750MPa,
Elongation percentage is 22%, clod wash D=1.5a surface flawless.
Embodiment 2:
Smelting in 220 tons of converters the molten steel through external refining are casting continuously to form strand, and its percentage by weight 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%, remaining is Fe and inevitable impurity.Slab thickness is 230mm.
Rolling at 1580 hot continuous rolling production lines, heating-up temperature is 1270 DEG C, and entry temperature at finishing is
1070 DEG C, finishing temperature is 880 DEG C, and target thickness is 5mm, is cooled to target through section cooling and batches after rolling
Temperature 620 DEG C, batches rear air cooling to room temperature.
High-strength steel yield strength Rel produced according to above method is 715MPa, and tensile strength is 800MPa,
Elongation percentage is 20%, clod wash D=1.5a surface flawless.
Embodiment 3:
Smelting in 220 tons of converters the molten steel through external refining are casting continuously to form strand, and its percentage by weight 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%, remaining is Fe and inevitable impurity.Slab thickness is 230mm.
Rolling at 1580 hot continuous rolling production lines, heating-up temperature is 1290 DEG C, and entry temperature at finishing is
1080 DEG C, finishing temperature is 890 DEG C, and target thickness is 4mm, is cooled to target through section cooling and batches after rolling
Temperature 610 DEG C, batches rear air cooling to room temperature.
High-strength steel yield strength Rel produced according to above method is 725MPa, and tensile strength is 810MPa,
Elongation percentage is 20%, clod wash D=1.5a surface flawless.
Embodiment 4:
Smelting in 220 tons of converters the molten steel through external refining are casting continuously to form strand, and its percentage by weight 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%, remaining is Fe and inevitable impurity.Slab thickness is 230mm.
Rolling at 1580 hot continuous rolling production lines, heating-up temperature is 1265 DEG C, and entry temperature at finishing is
1065 DEG C, finishing temperature is 865 DEG C, and target thickness is 6mm, is cooled to target through section cooling and batches after rolling
Temperature 640 DEG C.
High-strength steel yield strength Rel produced according to above method is 715MPa, and tensile strength is 795MPa,
Elongation percentage is 22%, clod wash D=1.5a surface flawless.
Embodiment 5:
Smelting in 220 tons of converters the molten steel through external refining are casting continuously to form strand, its percentage by weight and reality
Execute example 4 identical.Slab thickness is 230mm.
Rolling at 1580 hot continuous rolling production lines, heating-up temperature is 1270 DEG C, and entry temperature at finishing is
1070 DEG C, finishing temperature is 870 DEG C, and target thickness is 5mm, is cooled to target through section cooling and batches after rolling
Temperature 630 DEG C.
High-strength steel yield strength Rel produced according to above method is 745MPa, and tensile strength is 830MPa,
Elongation percentage is 21.5%, clod wash D=1.5a surface flawless.
Embodiment 6:
Smelting in 220 tons of converters the molten steel through external refining are casting continuously to form strand, its percentage by weight and reality
Execute example 4 identical.Slab thickness is 230mm.
Rolling at 1580 hot continuous rolling production lines, heating-up temperature is 1290 DEG C, and entry temperature at finishing is
1090 DEG C, finishing temperature is 895 DEG C, and target thickness is 4mm, is cooled to target through section cooling and batches after rolling
Temperature 620 DEG C.
High-strength steel yield strength Rel produced according to above method is 760MPa, and tensile strength is 850MPa,
Elongation percentage is 21%, clod wash D=1.5a surface flawless.
Embodiment 7:
Smelting in 220 tons of converters the molten steel through external refining are casting continuously to form strand, and its percentage by weight 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%, remaining is Fe and inevitable impurity.Slab thickness is 230mm.
Rolling at 1580 hot continuous rolling production lines, heating-up temperature is 1280 DEG C, and entry temperature at finishing is
1075 DEG C, finishing temperature is 860 DEG C, and target thickness is 7mm, is cooled to target through section cooling and batches after rolling
Temperature 630 DEG C.
High-strength steel yield strength Rel produced according to above method is 700MPa, and tensile strength is 780MPa,
Elongation percentage is 21%, clod wash D=1.5a surface flawless.
Embodiment 8:
Smelting in 220 tons of converters the molten steel through external refining are casting continuously to form strand, its percentage by weight and reality
Execute example 7 identical.Slab thickness is 230mm.
Rolling at 1580 hot continuous rolling production lines, heating-up temperature is 1300 DEG C, and entry temperature at finishing is
1100 DEG C, finishing temperature is 900 DEG C, and target thickness is 3mm, is cooled to target through section cooling and batches after rolling
Temperature 620 DEG C.
High-strength steel yield strength Rel produced according to above method is 755MPa, and tensile strength is 845MPa,
Elongation percentage is 20%, clod wash D=1.5a surface flawless.
It should be noted last that, above detailed description of the invention only in order to technical scheme to be described rather than
Limiting, although being described in detail the present invention with reference to example, those of ordinary skill in the art should manage
Solve, technical scheme can be modified or equivalent, without deviating from the technology of the present invention side
The spirit and scope of case, it all should be contained in the middle of scope of the presently claimed invention.
Claims (2)
1. a production is applicable to the method for automobile shafts tube steel of high frequency induction welding, it is characterised in that including:
Molten iron is obtained half molten steel through converter or electric furnace smelting；
After half molten steel is passed through LF refine or RH application of vacuum, carry out continuous casting and obtain slab, described slab
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%；Its
Remaining is Fe and inevitable impurity；
Being heated by described slab, heating and temperature control is at 1260～1300 DEG C, and temperature retention time is more than 180
Minute, then will heating after slab through roughing, finish rolling obtain hot rolled plate, entry temperature at finishing be 1060 DEG C～
1100 DEG C, finishing temperature is 860～900 DEG C, then described hot rolled plate is carried out section cooling, rolls up after cooling
Take into finished product.
2. the method producing the automobile shafts tube steel being applicable to high frequency induction welding as claimed in claim 1, its
It is characterised by:
Described hot rolled plate use leading portion refrigerating mode carry out section cooling, target coiling temperature be 610 DEG C～
640℃。
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 CN103484763A (en) | 2014-01-01 |
| CN103484763B true CN103484763B (en) | 2016-11-30 |
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Citations (2)
| 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 |
Patent Citations (2)
| 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 |
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