CN101586209B - Hot rolling wire rod of 1800 MPa level for low-alloy structure and manufacture method thereof - Google Patents
Hot rolling wire rod of 1800 MPa level for low-alloy structure and manufacture method thereof Download PDFInfo
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- CN101586209B CN101586209B CN2008100379169A CN200810037916A CN101586209B CN 101586209 B CN101586209 B CN 101586209B CN 2008100379169 A CN2008100379169 A CN 2008100379169A CN 200810037916 A CN200810037916 A CN 200810037916A CN 101586209 B CN101586209 B CN 101586209B
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Abstract
The invention provides a hot rolling wire rod of 1800 MPa level for a low-alloy structure and a manufacture method thereof. The hot rolling wire rod of 1800 MPa level for the low-alloy structure comprises the following chemical components by weight percentage: 0.30 to 0.40 percent of C, 2.0 to 3.0 percent of Si, 2.5 to 4.0 percent of Mn, 0.30 to 0.40 percent of Mo, and the balance of Fe and unavoidable impurities. The invention adopts Mn-Si-Mo line components, and produces a medium carbon hot rolling wire rod which takes fine acicular martensite structure as the characteristic through purification smelting, rough rolling, finish rolling and the controlled cooling technology. The hot rolling wire rod has the steel yield strength no less than 1600 Mpa, the tensile strength no less than 1800 Mpa, the yield ratio no less than 0.80 percent, the elongation no less than 9.0 percent and the reduction of area no less than 40 percent.
Description
Technical field
The present invention relates to plow-steel and method of manufacture thereof, specifically, the present invention relates to 1800MPa level low alloy structure with hot rolling wire and method of manufacture thereof.
Background technology
In recent years, when industry such as bridge, automobile and machinofacture rapidly increases, for realizing economizing on resources and protecting the Sustainable development of environment, to the increasing demand increase of high-strength wire material and bar steel.The major technique of current raising wire rod and bar hardness of steel is alloying and raising carbon content.
Alloying process be improve at present steel strength the method that generally adopts.This method is through adding microalloy elements such as alloying element such as Ni, Cr, Mo, Si and Mn and Nb, V, Ti; Utilize alloying strengthening to improve the intensity and the toughness of steel; Represent steel grade to mainly contain spring steel, bolting steel etc., for example 60Si2CrVA, 50CrV4,55SiCr6 and 54SiCrV6 etc.The intensity of this type steel generally can reach 1500MPa, can reach 1800MPa through modifier treatment, and has toughness preferably.Yet the shortcoming of alloying strengthening technology is: add a large amount of alloy elements and can improve material cost, make metallurgical technology become complicated simultaneously.
Improve the intensity that carbon content also can improve the steel cord, represent steel grade to mainly contain 82MnQL, 87MnQL and 82 steel cords etc.Carbon content in this type steel all >=0.80%, its intensity can reach about 1200MPa, can reach 1700MPa.But along with intensity improves, the toughness of steel reduces, and the hydrogen embrittlement susceptibility of steel wire increases, and twisting property descends, and is organized as the lamella perlite after the cold-drawn.Therefore this type steel in use often shows the toughness deficiency, and this can shorten the work-ing life of steel, and the raising of its intensity also is restricted in addition, restricts applying of this type of steel.
Improve the toughness of plow-steel, have and smelt and two kinds of methods of controlled rolling and controlled cooling.
Start with from smelting, improve the cleanliness factor and the tissue homogeneous degree of steel, reduce carbon content, the inclusion that is difficult to remove is carried out modification or harmless treatment is the prerequisite and the basis of realizing the high malleableize of plow-steel.
Through controlled rolling, controlled chilling (being TMCP) technology, make the material microstructure super-refinement, thereby realize high malleableize, high-intensity purpose.The microstructure super-refinement is at present uniquely not only to improve intensity but also improve flexible steel schedule of reinforcement.Carry out structure refinement for perlite and ferritic steel, can obtain high toughness, little but its intensity improves; Martensitic steel has higher intensity, but the structure refinement of martensite lath is relatively more difficult, and technology is more complicated also.Therefore, refinement martensitic stucture is to improve difficult point of martensitic steel flexible.
Through retrieval, find Japanese documentation (JP2003105485), the chemical ingredients of its disclosed spring steel is C:0.4～0.9%, Si:0.5～3%, Mn:0.1～2%, P :≤0.020%, S :≤0.010%, all the other are iron and unavoidable impurities; Tensile strength is 1800～2400MPa.But the microstructure of this spring steel is sheet martensite and ferritic mixed structure, and its carbon content is higher, belongs to the medium high carbon spring steel; This steel rolls the back and adopts 20～200 ℃/s quenching cooling fast, carries out 200 ℃ of following low-temperaturetemperings subsequently and handles; It is more that alloying element is added in this invention, and cost is higher; This steel adopts cooling fast and low-temperaturetempering to handle, and plasticity is relatively poor; In addition, quench, temper makes complex manufacturing.
For addressing the above problem; Contriver of the present invention combines alloying strengthening and microstructure super-refinement mechanism; In middle low carbon steel, add elements such as Mn, Si and low levels Mo; Through control and the simplification to rolling technology, obtaining a kind of is that the 1800MPa level low alloy structure of characteristic is used hot rolling wire with the fine acicular martensitic stucture.
One object of the present invention is to provide a kind of 1800MPa level low alloy structure to use hot rolling wire.
Another object of the present invention is to provide the method for manufacture of said hot rolling wire.
Summary of the invention
First aspect of the present invention provides a kind of 1800MPa level low alloy structure to use hot rolling wire; Its chemical ingredients comprises by weight percentage: C:0.30～0.40%, Si:2.0～3.0%, Mn:2.5～4.0%, Mo:0.30～0.40%, surplus are Fe and unavoidable impurities.
In a preferred implementation: in said unavoidable impurities, S≤0.010%, P≤0.020%, O, N, H total amount＜50mg/kg.
In another preferred implementation: the microstructure of said wire rod is a fine acicular martensite, and the martensite lath width dimensions is about 0.1～0.5 μ m.
The alloying element content of steel of the present invention is few, has both saved resource, has reduced production cost again.Metallurgical technology is simple simultaneously, can realize through controlled rolling and controlled cooling, does not need extra modified hot-work to handle.
Below, the chemical ingredients of hot rolling wire of the present invention is done as being described in detail.
C: because the obdurability of steel depends primarily on its carbon content and weave construction thereof, have quite high intensity and good toughness, the carbon content in the steel is had certain restriction, so carbon content is controlled between 0.30～0.40% generally in order to guarantee steel.
The effect of Si:Si in steel mainly is solution strengthening.The Si of high level can improve the hardening capacity of steel, adds intensity and the toughness that Si helps improving steel in the general steel.In addition, Si can increase the austenite quantity that reduces the hydrogen velocity of diffusion, and makes the steel can be in tempering under the higher temperature.Therefore, the present invention is restricted to 2.0～3.0% with Si content.
The effect of Mn:Mn in steel is solution strengthening and the hardening capacity that improves steel wire, but the segregation of Mn tendency is higher, thus Mn content be difficult for too high, so be controlled between 2.5～4.0%.
Mo: improve the solidity to corrosion of steel, can play the effect of precipitation strength in addition, because Mo is relatively more expensive, so the present invention only need add a small amount of Mo, add-on is 0.30～0.40%.
Second aspect of the present invention provides the method for manufacture of said wire rod; This method comprises smelting, casting, heating, roughing, finish rolling and controlled chilling; Wherein in said controlled chilling process, adopt stelmor controlled chilling method that wire rod is cooled off fast, rate of cooling is 5 ± 1 ℃/s.
Wherein, in said heat-processed, preferred 1220～1270 ℃ of Heating temperature, preferred 120～140 minutes of soaking time; In said roughing process, roughing begins preferred 1140～1180 ℃ of TR, rolls preferred 1130～1160 ℃ of back TR, rolls into the bar of φ 22 ± 0.5mm; In said finish rolling process, Heating temperature is preferred >=1050 ℃, and preferred 1000～1050 ℃ of rolling temperature scope rolls into the wire rod of φ 9 ± 0.3mm on continuous mill; In said controlled chilling process, through stelmo line the finish rolling wire rod to be cooled off fast, purpose is for the excellent fine acicular martensitic stucture of obtained performance.Ys >=the 1600MPa of gained wire rod, tensile strength >=1800MPa, yield tensile ratio >=0.80, unit elongation >=9.0%, relative reduction in area >=40%.
Beneficial effect of the present invention is:
1, steel grade of the present invention adopts the Mn-Si-Mo set member, and alloy species is common and consumption is few, and production cost is lower.
2, through the cooperation of composition design and rolling technology, obtain the fine acicular martensitic stucture, guarantee that the wire rod plate has higher strength and toughness.
3, because composition and technological design are reasonable, and from implementation result, process system is looser, technical process is simplified, can be on common production line stably manufactured.
Description of drawings
Fig. 1 is the microstructure metallograph (1000 *) of the embodiment of the invention 2;
Fig. 2 is the microstructure martensite TEM pattern of the embodiment of the invention 2.
Embodiment
Below combine accompanying drawing that the present invention is made more detailed description with embodiment.These embodiment only are the descriptions to best mode for carrying out the invention, scope of the present invention are not had any restriction.
Comparative Examples
Press the smelting molten steel in the vacuum electromagnetic induction furnace of the chemical ingredients shown in the table 1, and be cast into continuously cast bloom or steel ingot, continuously cast bloom or steel ingot are heated to 1220～1270 ℃, be incubated homogeneous microstructure processing in 120 minutes; Carry out roughing then, roughing begins 1140～1180 ℃ of TRs, and rolling the back TR is 1130～1160 ℃, rolls into the bar of φ 22 ± 0.5mm.Finish rolling subsequently, the final rolling temperature scope is 1000～1050 ℃, on continuous mill, rolls into the wire rod of φ 9 ± 0.3mm.Roll after stelmo line cools off fast.
Embodiment 1
Press the smelting molten steel in the vacuum electromagnetic induction furnace of the chemical ingredients shown in the table 1, and be cast into continuously cast bloom or steel ingot, continuously cast bloom or steel ingot are heated to 1220～1270 ℃, be incubated 125 minutes; Carry out roughing then, roughing begins 1140～1180 ℃ of TRs, and rolling the back TR is 1130～1160 ℃, rolls into the bar of φ 22 ± 0.5mm.Finish rolling subsequently, the final rolling temperature scope is 1000～1050 ℃, on continuous mill, rolls into the wire rod of φ 9 ± 0.3mm.Roll after the stelmo line controlled chilling, rate of cooling is 5 ℃/s.
Embodiment 2
Embodiment is with embodiment 1, and wherein Heating temperature is 1220～1270 ℃, is incubated 130 minutes; Roughing begins 1140～1180 ℃ of TRs, rolls into the bar of φ 22 ± 0.5mm.Finish rolling Heating temperature >=1050 ℃, the rolling temperature scope is 1000～1050 ℃, on continuous mill, rolls into the wire rod of φ 9 ± 0.3mm.Roll after the stelmo line controlled chilling, rate of cooling is 4 ℃/s.
Embodiment 3
Embodiment is with embodiment 1, and wherein Heating temperature is 1220 ℃～1270 ℃, is incubated 140 minutes; Roughing begins 1140～1180 ℃ of TRs, rolls into the bar of φ 22 ± 0.5mm.Finish rolling Heating temperature >=1050 ℃, the rolling temperature scope is 1000～1050 ℃, on continuous mill, rolls into the wire rod of φ 9 ± 0.3mm.Roll after the stelmo line controlled chilling, rate of cooling is 6 ℃/s.
The chemical ingredients (wt%) of the hot rolling wire of table 1 Comparative Examples of the present invention and embodiment 1-3
| C | Si | Mn | Mo | Fe and impurity | |
| Comparative Examples | 0.20 | 1.50 | 1.5 | 0.15 | Surplus |
| Embodiment 1 | 0.30 | 2.0 | 2.5 | 0.20 | Surplus |
| Embodiment 2 | 0.35 | 2.50 | 3.0 | 0.35 | Surplus |
| Embodiment 3 | 0.40 | 3.0 | 4.0 | 0.40 | Surplus |
According to GB/T228-2002 the present invention is carried out Mechanics Performance Testing to the hot rolling wire of Comparative Examples and embodiment 1-3, test result is seen table 2.
The mechanical property of the hot rolling wire of table 2 Comparative Examples of the present invention and embodiment 1-3
| Embodiment | Ys (MPa) | Tensile strength (MPa) | Yield tensile ratio | Relative reduction in area (%) | Unit elongation (%) |
| Comparative Examples | 1300 | 1620 | 0.80 | 53.5 | 9.8 |
| Embodiment 1 | 1655 | 1847 | 0.89 | 53 | 9.7 |
| Embodiment 2 | 1701 | 1925 | 0.88 | 52 | 9.5 |
| Embodiment 3 | 1803 | 2071 | 0.87 | 51.4 | 9.4 |
In conjunction with Fig. 1,2 and table 2 can find out; 1800MPa level low alloy structure of the present invention uses the microtexture of hot rolling wire to be fine acicular martensite, and its ys reaches more than the 1600MPa, and yield tensile ratio is higher; Have good toughness simultaneously, can be used as high-strength wire material and the bar steel is used steel.
Claims (5)
1. a 1800MPa level low alloy structure is used hot rolling wire, it is characterized in that, by weight percentage; Its chemical ingredients comprises: C:0.30～0.40%, Si:2.0～3.0%, Mn:2.5～4.0%, Mo:0.30～0.40%, surplus are Fe and unavoidable impurities, in said impurity; S≤0.010%, P≤0.020%, O, N, H total amount＜50mg/kg; The microstructure of said wire rod is a fine acicular martensite, and the martensite lath width dimensions is 0.1～0.5 μ m.
2. a 1800MPa level low alloy structure is with the method for manufacture of hot rolling wire, and by weight percentage, said wire rod chemical ingredients comprises: C:0.30～0.40%, Si:2.0～3.0%, Mn:2.5～4.0%, Mo:0.30～0.40%; Surplus is Fe and unavoidable impurities, in said impurity, and S≤0.010%; P≤0.020%; O, N, H total amount＜50mg/kg, the microstructure of said wire rod is a fine acicular martensite, the martensite lath width dimensions is 0.1～0.5 μ m; Said method comprises smelting, casting, heating, roughing, finish rolling and controlled chilling
It is characterized in that in said controlled chilling process, wire rod is through the cooling of stelmor cooling line, rate of cooling is 5 ± 1 ℃/s.
3. method of manufacture as claimed in claim 2 is characterized in that, in said heat-processed, Heating temperature is 1220～1270 ℃, and soaking time is 120～140 minutes.
4. method of manufacture as claimed in claim 2 is characterized in that, in said roughing process, it is 1140～1180 ℃ that roughing begins TR, and rolling the back TR is 1130～1160 ℃, rolls into the bar of φ 22 ± 0.5mm.
5. method of manufacture as claimed in claim 2 is characterized in that, in said finish rolling process, and 1050～1100 ℃ of Heating temperature scopes, the rolling temperature scope is 1000～1050 ℃, rolls into the wire rod of φ 9 ± 0.3mm.
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| Application Number | Priority Date | Filing Date | Title |
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| CN2008100379169A CN101586209B (en) | 2008-05-23 | 2008-05-23 | Hot rolling wire rod of 1800 MPa level for low-alloy structure and manufacture method thereof |
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| Application Number | Priority Date | Filing Date | Title |
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| CN2008100379169A CN101586209B (en) | 2008-05-23 | 2008-05-23 | Hot rolling wire rod of 1800 MPa level for low-alloy structure and manufacture method thereof |
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| CN101586209A CN101586209A (en) | 2009-11-25 |
| CN101586209B true CN101586209B (en) | 2012-03-28 |
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| CN106706412B (en) * | 2016-12-09 | 2019-04-30 | 武汉钢铁有限公司 | A kind of method of determining gren rod yield tensile ratio |
Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1282381A (en) * | 1997-12-19 | 2001-01-31 | 埃克森美孚上游研究公司 | Ultra-high strength steels with excellent cryogenic temp. toughness |
| US20040096351A1 (en) * | 2000-06-14 | 2004-05-20 | Nisshin Steel Co., Ltd. | Ferritic and martensitic stainless steels excellent in machinability |
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- 2008-05-23 CN CN2008100379169A patent/CN101586209B/en active Active
Patent Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1282381A (en) * | 1997-12-19 | 2001-01-31 | 埃克森美孚上游研究公司 | Ultra-high strength steels with excellent cryogenic temp. toughness |
| US20040096351A1 (en) * | 2000-06-14 | 2004-05-20 | Nisshin Steel Co., Ltd. | Ferritic and martensitic stainless steels excellent in machinability |
Non-Patent Citations (2)
| Title |
|---|
| JP特开2003-105485A 2003.04.09 |
| JP特开2003-231941A 2003.08.19 |
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