CN102876983B - Production process for 82B wire rod used for high strength prestressed steel wire and wire rod thereof - Google Patents

Production process for 82B wire rod used for high strength prestressed steel wire and wire rod thereof Download PDF

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CN102876983B
CN102876983B CN201210372518.9A CN201210372518A CN102876983B CN 102876983 B CN102876983 B CN 102876983B CN 201210372518 A CN201210372518 A CN 201210372518A CN 102876983 B CN102876983 B CN 102876983B
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wire rod
temperature
wire
prestressed steel
strength prestressed
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CN201210372518.9A
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CN102876983A (en
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李义长
易良刚
张颖刚
蒲勇
赵如龙
蒋世川
黄生权
彭可雕
万朝明
李琨
王洪利
樊毅
刘志军
李荣华
杨旭
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攀钢集团成都钢钒有限公司
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Abstract

The invention relates to a production process for an 82B wire rod used for a high strength prestressed steel wire and a wire rod thereof. The production process achieves objects of refining grains, improving the metallographic structure and obtaining high sorbite rate, improves strength and plasticity of the 82B wire rod used for the high strength prestressed steel wire and realizes an object of optimizing a metallographic structure and mechanical properties of the 82B wire rod used for the high strength prestressed steel wire, by optimally designing chemical components of the 82B wire rod used for the high strength prestressed steel wire, adjusting heating procedures of a heating furnace before rolling, and employing controlled rolling and controlled cooling techniques. The high power quality and mechanical properties of the 82B wire rod with a nominal diameter of 6.5 mm used for the high strength prestressed steel wire reach the national standard of the hot rolling wire rod used for the prestressed steel wire and steel strand, and meet production requirement of downstream users.

Description

Production technique and the wire rod thereof of 82B wire rod for a kind of high-strength prestressed steel wire
Technical field
The invention belongs to field of metallurgy, relate to a kind of production technique of wire rod, more particularly, relate to the production technique of a kind of high-strength prestressed steel wire 82B wire rod and the wire rod obtaining according to this production technique.
Background technology
High-strength prestressed steel wire is intensity rank product high, with high content of technology in Constructional Steel, is widely used in large high-speed railway, highway, bridge, roof truss, crane girder, Highrise buildings, tie industry etc.Due to the singularity of compressor wire working conditions and Working environment, its quality is had to 3 basic demands, material is even, and poker characteristic is good; With a collection of product must intensity in a rank.Correspondingly also require the purity of steel of production preload tension wire material products wire rod high, composition is even, surface quality good, organize sorbite rate high and even; Stable performance.And intensity is higher, the requirement of steel, metallographic structure and surface quality etc. to wire rod used is higher.High-carbon steel wire rod is the preferred raw materials of producing compressor wire, is characterized in high-carbon, high strength, and requires there is good combination of strength and toughness, to meet the needs of user to steel cold drawing performance.
China's compressor wire is that sorbitic rate is not high and inhomogeneous, mechanical property is not high by the subject matter of gren rod at present, and this is the principal element of restriction China compressor wire development.Therefore, exploitation high-strength prestressed steel wire becomes one of emphasis of wire rod research and development with gren rod.
Summary of the invention
For the deficiencies in the prior art, one of object of the present invention is to solve the one or more problems that exist in above-mentioned prior art.
The object of the present invention is to provide a kind of can crystal grain thinning, improve metallographic structure, obtain high sorbite rate to reach the production technique of the high-strength prestressed steel wire 82B wire rod that improves the mechanical property such as intensity and plasticity of high-strength prestressed steel wire 82B wire rod and optimize the object of its metallographic structure and according to wire rod that this production technique was obtained.
To achieve these goals, an aspect of of the present present invention provides a kind of high-strength prestressed steel wire 82B production technique of wire rod, described production technique comprises following operation: raw material is prepared, smelting molten steel, continuous casting becomes base, add hot continuously cast material, temperature-controlled rolling becomes wire rod, the rolling of weaving silk, control cooling, aftertreatment also obtains wire rod finished product, wherein, by weight percentage, described wire rod finished product comprises following chemical composition: C:0.80~0.85%, Si:0.15~0.30%, Mn:0.70~0.90%, P≤0.025%, S≤0.025%, Cr:0.15~0.30%, Ni≤0.10%, Cu≤0.05%, V:0.02~0.05%, Als≤0.02%, and the Fe of surplus and inevitable impurity, in the described step that adds hot continuously cast material, controlling preheating section temperature and be 700~760 ℃, warm up time is 35~50 minutes, heating zone temperature is that 960~1000 ℃, heat-up time are 35~50 minutes, soaking zone temperature is that 990~1030 ℃, soaking time are 30~40min, and to control furnace atmosphere be weak reducing atmosphere, become in the step of wire rod at described temperature-controlled rolling, controlling start rolling temperature is 950~990 ℃, in the step of the described rolling of weaving silk, controlling laying temperature is 860~880 ℃, in the cooling step of described control, adopt that stelmor control cold line coils to roll rear control cooling, the cooling rate that controlling board twists in before pearlitic transformation is 9.5~10.5 ℃/s, pearlitic transformation temperature is controlled at 640~690 ℃, after phase transformation, cooling rate is 1.5~2.5 ℃/s, make cooling after, wire rod surface temperature before aftertreatment is less than or equal to 300 ℃.
An embodiment of the production technique of 82B wire rod for high-strength prestressed steel wire according to the present invention, described temperature-controlled rolling becomes the step of wire rod to comprise to make continuously cast bloom to form successively the step of wire rod by roughing unit, intermediate mill, pre-finishing mill group, pre-finishing mill group, finishing train and reducing sizing mill group, wherein, the temperature that control wire rod enters finishing train entrance is 850~880 ℃, and the temperature that control wire rod enters reducing sizing mill group entrance is 850~880 ℃.
An embodiment of the production technique of 82B wire rod for high-strength prestressed steel wire according to the present invention, by weight percentage, contains 0.20~0.24% Cr, 0.020~0.025% V in described wire rod finished product.
An embodiment of the production technique of 82B wire rod for high-strength prestressed steel wire according to the present invention, the nominal diameter of described wire rod finished product is 6.5mm.
An embodiment of the production technique of 82B wire rod for high-strength prestressed steel wire according to the present invention, the local total decarburized layer degree of depth in one side of described wire rod finished product is not more than 1.5% of wire rod finished product nominal diameter.
An embodiment of the production technique of 82B wire rod for high-strength prestressed steel wire according to the present invention, is mainly nodular troostite in the metallographic structure of described wire rod finished product, and sorbitic content is no less than 90%.
An embodiment of the production technique of 82B wire rod for high-strength prestressed steel wire according to the present invention, the real tensile strength R of described wire rod finished product m>=1200MPa, elongation A>=11%, relative reduction in area Z>=30%.
Another aspect of the present invention provides a kind of high-strength prestressed steel wire 82B wire rod, and described wire rod is made by the production technique of 82B wire rod according to above-mentioned high-strength prestressed steel wire.
The present invention compared with prior art, use the equipment advantage of high line unit, by high-strength prestressed steel wire is designed, adjusts process furnace heating cycle, employing controlled rolling, the control cooling technology before rolling by the optimization of Chemical Composition of 82B wire rod, crystal grain thinning, improve metallographic structure, obtain high sorbite rate, the intensity and the plasticity that have improved high-strength prestressed steel wire 82B wire rod, reach and optimize the metallographic structure of high-strength prestressed steel wire 82B wire rod, the object of mechanical property.
Accompanying drawing explanation
Fig. 1 is the micro test metallographic structure schematic diagram of the sample one of high-strength prestressed steel wire 82B wire rod in the embodiment of the present invention.
Fig. 2 is the micro test metallographic structure schematic diagram of the sample two of high-strength prestressed steel wire 82B wire rod in the embodiment of the present invention.
Fig. 3 is the micro test metallographic structure schematic diagram of the sample three of high-strength prestressed steel wire 82B wire rod in the embodiment of the present invention.
Embodiment
Hereinafter, describe the production technique of high-strength prestressed steel wire of the present invention 82B wire rod and the wire rod obtaining according to this production technique in detail in connection with exemplary embodiment.Wherein, unless otherwise noted, related per-cent is all weight percentage.
Exemplary embodiment according to high-strength prestressed steel wire according to the present invention by the production technique of 82B wire rod, described production technique comprises following operation: raw material preparation, smelting molten steel, continuous casting become base, add hot continuously cast material, temperature-controlled rolling becomes wire rod, the rolling of weaving silk, control cooling, aftertreatment and obtain wire rod finished product.Wherein, by weight percentage, described wire rod finished product comprises following chemical composition: C:0.80~0.85%, Si:0.15~0.30%, Mn:0.70~0.90%, P≤0.025%, S≤0.025%, Cr:0.15~0.30%, Ni≤0.10%, Cu≤0.05%, V:0.02~0.05%, Als≤0.02%, and the Fe of surplus and inevitable impurity; In the described step that adds hot continuously cast material, controlling preheating section temperature and be 700~760 ℃, warm up time is 35~50 minutes, heating zone temperature is that 960~1000 ℃, heat-up time are 35~50 minutes, soaking zone temperature is that 990~1030 ℃, soaking time are 30~40min, and to control furnace atmosphere be weak reducing atmosphere; Become in the step of wire rod at described temperature-controlled rolling, controlling start rolling temperature is 950~990 ℃; In the step of the described rolling of weaving silk, controlling laying temperature is 860~880 ℃; In the cooling step of described control, adopt that stelmor control cold line coils to roll rear control cooling, the cooling rate that controlling board twists in before pearlitic transformation is 9.5~10.5 ℃/s, pearlitic transformation temperature is controlled at 640~690 ℃, after phase transformation, cooling rate is 1.5~2.5 ℃/s, make cooling after, wire rod surface temperature before aftertreatment is less than or equal to 300 ℃.
In the present embodiment, by to the optimization of Chemical Composition design of 82B wire rod for high-strength prestressed steel wire, adjust process furnace heating cycle before rolling, adopt controlled rolling, control the improvement such as cooling technology, effectively reach crystal grain thinning, improve metallographic structure, obtain the object of high sorbite rate, improved the mechanical property of high-strength prestressed steel wire 82B wire rod.
According to the present invention, by weight percentage, wire rod finished product comprises following chemical composition: C:0.80~0.85%, Si:0.15~0.30%, Mn:0.70~0.90%, P≤0.025%, S≤0.025%, Cr:0.15~0.30%, Ni≤0.10%, Cu≤0.05%, V:0.02~0.05%, Als≤0.02%, and the Fe of surplus and inevitable impurity.Because high-strength prestressed steel wire belongs to hypereutectoid steel with 82B wire rod, if need not reduce plasticity in improving the intensity of hypereutectoid steel, by adding appropriate micro alloying element, to adjust rolling technology be the most effective solution up to now again.Research to microalloy element shows: Cr unit have the effect that reduces Cooling Austenite Transformation temperature, and the pearlite interlaminar spacing that can reduce hypereutectoid steel improves the intensity of steel, reduces γ → Fe 3the velocity of transformation of C alleviating suppresses proeutectoid cementite and separates out, improves the drawing property, crystal grain thinning of steel and improve plasticity; V element has the effect of crystal grain thinning, and trace V (< 0.1%) element can improve intensity and the plasticity of high carbon steel.Therefore, the present invention carries out microalloying by adding trace alloying element Cr and V, reaches the object of Optimal performance.Preferably, in wire rod finished product, contain 0.20~0.24% Cr, 0.020~0.025% V.
According to the present invention, in the step that adds hot continuously cast material, controlling preheating section temperature and be 700~760 ℃, warm up time is 35~50 minutes, heating zone temperature is that 960~990 ℃, heat-up time are 35~50 minutes, soaking zone temperature is that 990~1030 ℃, soaking time are 30~40min, and control furnace atmosphere is weak reducing atmosphere, finally make the top and bottom temperature difference, the total length temperature difference of continuously cast bloom all be no more than 30 ℃.Because the present invention has added micro alloying element in wire rod, in order to allow the abundant solid solution of micro alloying element in austenite, play the object of crystal grain thinning, raising sorbite rate, raising intensity and plasticity, avoid that scaling loss is excessive and original austenite grains is thick simultaneously, the present invention has suitably reduced the Heating temperature of preheating section, heating zone, proper extension this heat-up time of two periods, and suitably improved the Heating temperature of soaking zone.
Appropriate heating zone temperature, heat-up time and soaking zone temperature, soaking time can be given full play to the effect of micro alloying element and billet quality do not caused to damage, if the temperature of heating zone, soaking zone is low or heat-up time is short, micro alloying element fully solid solution in austenite so that its precipitation strength and Grain refinement bring into play not out; If the temperature height of heating zone, soaking zone or grown heat-up time, affect billet quality by increasing the scaling loss of blank, cause its intensity of thick reduction and the plasticity and toughness of original austenite grains.Guarantee the temperature of heating zone and soaking zone, need appropriate design preheating section temperature and warm up time, if the temperature of preheating section is low or heat-up time short will make ensuing heating zone temperature not or steel billet internal and external temperature inequality, if the temperature height of preheating section increase by increasing blank internal stress the probability that crack defect produces, affect production efficiency if grown reduction steel rolling rhythm the heat-up time of preheating section.
Because surface decarburization is the normal defect occurring of high carbon steel, in order to reduce decarburization, in many group heating-furnaces, data analysis draws and adopts weak reducing atmosphere can effectively control decarburization.Because normally used continuous casting billet heating stove is walking beam furnace, and walking beam furnace is steel billet head end and tail end switch type " flame ", so there is the temperature difference in continuously cast bloom, in order to improve the poker characteristic homogeneity of finished product, must guarantee that the continuously cast bloom top and bottom temperature difference, the total length temperature difference are no more than 30 ℃.According to the present invention, become in the step of wire rod at temperature-controlled rolling, controlling start rolling temperature is 950~990 ℃, so, controlled combinations granularity, can reduce roll wear on the other hand on the one hand.If excess Temperature can make original grain thick, reduce product intensity; If the too low meeting of temperature increases the weight of milling train wearing and tearing, increase production cost.
According to the present invention, above-mentioned temperature-controlled rolling becomes the step of wire rod specifically to comprise to make continuously cast bloom to form successively the step of wire rod by roughing unit, intermediate mill, pre-finishing mill group, finishing train and reducing sizing mill group, wherein, the temperature that control wire rod enters finishing train entrance is 850~880 ℃, and the temperature that control wire rod enters reducing sizing mill group entrance is 850~880 ℃.Temperature control is rolled like this, and controlled combinations granularity, can reduce roll wear on the other hand on the one hand.If excess Temperature can make coarse grains, reduce product intensity; If the too low meeting of temperature increases the weight of milling train wearing and tearing, greatly increase production cost; In addition, wire rod will guarantee that in too high or too low for temperature being all difficult to of reducing sizing mill group entrance laying temperature is in claimed range.
According to the present invention, in the step of rolling of weaving silk, controlling laying temperature is 860~880 ℃; In the cooling step of control, adopt that stelmor control cold line coils to roll rear control cooling, the cooling rate that controlling board twists in before pearlitic transformation is 9.5~10.5 ℃/s, pearlitic transformation temperature is controlled at 640~690 ℃, after phase transformation, cooling rate is 1.5~2.5 ℃/s, cooling after, wire rod surface temperature before aftertreatment is less than or equal to 300 ℃.Rolling the cooling object of rear control is after high temperature rolling, to control the phase transition process of rolled piece, thereby controls steel structural state, and then improves comprehensive mechanical property and the use properties of wire rod.Laying temperature is too low can reduce stabilization of austenite, easily separates out pro-eutectoid phase, is the 82B hypereutectoid steel of cementite for pro-eutectoid mutually, and this will increase its drawing fragility affects wire rod use properties; The too high one side of laying temperature can make the coarse grains of steel reduce its mechanical property, and also can increase on the other hand wire rod surface decarburization affects follow-up use.If the cooling rate before pearlitic transformation is on the low side, can not Quick winding cross pro-eutectoid and form mutually district, will generate the pro-eutectoid phase that affects the follow-up use of wire rod; If the cooling rate before pearlitic transformation is too fast, can be difficult to control follow-up transformation temperature and causes generation to affect the even abnormal structure such as martensite, bainite of troostite of the follow-up drawing of wire rod.Pearlitic transformation excess Temperature can increase perlite sheet spacing reduce sorbite percentage, the too low meeting of pearlitic transformation temperature make perlite sheet spacing meticulous and form troostite, this all will affect the follow-up drawing property of wire rod.Therefore, must determine rational laying temperature and coordinate suitable cooling control after rolling technique, just can obtain the tissue needing.
An embodiment at high-strength prestressed steel wire of the present invention by the production technique of 82B wire rod, the nominal diameter of wire rod finished product is 6.5mm.And, one side total decarburized layer degree of depth of the wire rod finished product that high-strength prestressed steel wire obtains by the production technique of 82B wire rod is according to an exemplary embodiment of the present invention not more than 1.5% of wire rod finished product nominal diameter, and wherein total decarburized layer comprises ferrite and transition layer; In the metallographic structure of wire rod finished product, be mainly nodular troostite, sorbitic content is no less than 85%, and does not allow the existence of cementite network and quenching structure (martensite and troostite region); The tensile strength R of the hot rolling sample of wire rod finished product m>=1210MPa, elongation A>=9%, relative reduction in area Z>=25%, the tensile strength R of the sample of wire rod finished product timeliness after 15 days m>=1200MPa, elongation A>=11%, relative reduction in area Z>=30%.
High-strength prestressed steel wire according to the present invention is to adopt the production technique of above-mentioned high-strength prestressed steel wire 82B wire rod to make with 82B wire rod.In an embodiment at high-strength prestressed steel wire of the present invention with 82B wire rod, the nominal diameter of wire rod is 6.5mm; The local total decarburized layer degree of depth in one side of wire rod is not more than 1.5% of wire rod finished product nominal diameter; In the metallographic structure of wire rod finished product, be mainly nodular troostite, sorbitic content is no less than 85%; The tensile strength R of the hot rolling sample of wire rod m>=1210MPa, elongation A>=9%, relative reduction in area Z>=25%, the tensile strength R of the sample of wire rod timeliness after 15 days m>=1200MPa, elongation A>=11%, relative reduction in area Z>=32%.
Particularly, high-strength prestressed steel wire according to the present invention can comprise the following steps by the exemplary embodiment of the production technique of 82B wire rod:
Raw material preparation, smelting molten steel, continuous casting become base, add hot continuously cast material, temperature-controlled rolling becomes wire rod, the rolling of weaving silk, control cooling, aftertreatment and obtain wire rod finished product.
Specifically comprise raw material (blast-melted) → 50 ton converter → LF stove → continuous casting → steel billet check → (reconditioning) → process furnace charging roller material loading → steel billet enter six rolling → 1# flying shear crops of come out of the stove → high-pressure water descaling → roughing of stove → walking-beam furnace heating → furnace delivery table steel billet → in roll six rolling → 2# flying shear crops, tail → in roll two rollings → pre-four rollings of finish rolling (comprising vertical kink) → 1#, 2# water cooling box is cooling → 3# flying shear crop → Horizontal loose sleeve → BGV6 frame finish rolling → 3#, 4# water cooling box is cooling → and TMB1+TMB2 subtracts fixed diameter rolling → 5# water tank cooling → (pinch roll) → Laying head → loose volume is air-cooled → and collection furls collection → extension volume → PF hook-type fortune machine and transports → check on the quality, sampling, wipe out end to end → compress the bundling → extension label of weighing → unload volume → warehouse-in → finished product to transport.
Wherein, high-strength prestressed steel wire is as shown in table 1 with the optimization of Chemical Composition design of 82B wire rod.
The chemical composition of 82B wire rod for table 1 high-strength prestressed steel wire
??C ??Si ??Mn ??P ??S ??As
??0.80~0.85 ??0.15~0.30 ??0.70~0.90 ??≤0.025 ??≤0.025 ??≤0.020
??Cr ??Ni ??Cu ??V ??Mo ??Alt
??0.15~0.30 ??≤0.10 ??≤0.05 ??0.02~0.05 ??≤0.03 ??≤0.02
??Sn ??N ??O ??H
??≤0.010 ??≤0.0070 ??≤0.0020 ??≤0.00020
Continuously cast bloom heating condition optimal control in process furnace is as shown in table 2.
The heating condition of table 2 continuously cast bloom
Air-fuel ratio is 0.75~0.82, and furnace atmosphere is week reduction, and the top and bottom temperature difference of continuously cast bloom, the total length temperature difference all should be no more than 30 ℃.Wherein, the composition of weak reducing atmosphere is as shown in table 3.
The gas content of table 3 weak reducing atmosphere
When controlled rolling, to enter the temperature of finishing train entrance be 850~880 ℃ to wire rod, and the temperature that enters reducing sizing mill group entrance is 850-880 ℃; Laying temperature is 860-880 ℃.
Controlling cooling employing stelmor control cold line carries out, the control of stelmor roller-way speed is as shown in table 4, the control of stelmor fan delivery is as shown in table 5, realizing the cooling rate that controlling board twists in before pearlitic transformation is 9.5~10.5 ℃/s, pearlitic transformation temperature is controlled at 640~690 ℃, after phase transformation, cooling rate is 1.5~2.5 ℃/s, and makes surface temperature≤300 ℃ of cooling rear wire rod.
Table 4 stelmor roller-way speed
Roller-way section 1 section 2 sections 3 sections 4 sections 5 sections 6 sections 7 sections
Roller-way speed (m/s) ??0.62 ??0.62 ??0.65 ??0.68 ??0.71 ??0.75 ??0.79
Roller-way section 8 sections 9 sections 10 sections 11 sections 12 sections 13 sections
Roller-way speed (m/s) ??0.83 ??0.87 ??0.91 ??0.96 ??0.96 ??0.96
Table 5 stelmor fan delivery
Blower fan numbering ??1# ??2# ??3# ??4# ??5# ??6# ??7# ??8# ??9# ??10# ??11# ??12#
Air quantity (HZ) ??41 ??41 ??39 ??39 ??38 ??38 ??38 ??38 ??30 ??30 ??30 ??30
The mechanical performance index that the present embodiment will reach is as shown in table 6.
Table 6 mechanical performance index
The local total decarburized layer degree of depth in one side of the wire rod that the present embodiment obtains should be not more than 1.5% of wire rod nominal diameter, and metallographic structure is mainly nodular troostite, wherein sorbite is no less than 90%, does not allow the existence in cementite network and quenching structure (martensite and troostite region).
Enumerating concrete example is below further elaborated exemplary embodiment of the present invention.Example is only for the present invention is described, and not limits by any way the present invention.
In example below, 82B wire rod 3 stoves for the high-strength prestressed steel wire that it is 6.5mm that nominal diameter has been manufactured experimently in production, called after sample one, sample two and sample three respectively, its concrete production technique is strictly undertaken by the production technique of 82B wire rod by above-mentioned high-strength prestressed steel wire, the finished product of the each sample of gained through check after indices as shown in table 7, table 8, table 9 and Fig. 1 to Fig. 3.
The chemical composition of 82B wire rod for the high-strength prestressed steel wire of table 7 Φ 6.5mm
As shown in Table 7, the high-strength prestressed steel wire of 3 stove of trial-production is by the chemical composition of 82B wire rod all in scope of design value, and sample one is 0.20~0.24% to the Cr element in sample three, and V element is 0.024~0.025%.
The mechanical property of 82B wire rod for the high-strength prestressed steel wire of table 8 Φ 6.5mm
As shown in Table 8, the high-strength prestressed steel wire of the Φ 6.5mm of trial-production has all reached internally controlling requirement value by sample one to the mechanical property of sample three of 82B wire rod, has realized the combination of high-strength high-plasticity, good mechanical performance.
The micro test interpretation of result of 82B wire rod for the high-strength prestressed steel wire of table 9 Φ 6.5mm
Can be found out by table 9, Fig. 1 to Fig. 3, the high power quality of the high-strength prestressed steel wire 82B wire rod of the Φ 6.5mm that high-strength prestressed steel wire according to the present invention is produced by the production technique of 82B wire rod is fine, the national standard that has reached compressor wire and steel strand gren rod, also meets user's service requirements.
In sum, the present invention is designed (carrying out Cr, V microalloying), adjusts process furnace heating cycle, is optimized cooling controlling and rolling controlling process by optimization of Chemical Composition, has realized the combination of high-carbon steel wire rod high strength and high-ductility.The high power quality of the high-strength prestressed steel wire 82B wire rod of the Φ 6.5mm that trial-production is produced and mechanical property are all better than the national standard requirement of compressor wire and steel strand gren rod, meet the production requirement of downstream user.
Although described the present invention in conjunction with exemplary embodiment above, those of ordinary skills should be clear, in the case of not departing from the spirit and scope of claim, can carry out various modifications to above-described embodiment.

Claims (6)

1. a production technique for 82B wire rod for high-strength prestressed steel wire, is characterized in that, described production technique comprises following operation:
Raw material preparation, smelting molten steel, continuous casting become base, add hot continuously cast material, temperature-controlled rolling becomes wire rod, the rolling of weaving silk, control cooling, aftertreatment and obtain wire rod finished product,
Wherein, by weight percentage, described wire rod finished product comprises following chemical composition: C:0.80~0.85%, Si:0.15~0.30%, Mn:0.70~0.90%, P≤0.025%, S≤0.025%, Cr:0.20~0.24%, Ni≤0.10%, Cu≤0.05%, V:0.020~0.025%, Als≤0.020%, and the Fe of surplus and inevitable impurity;
In the described step that adds hot continuously cast material, controlling preheating section temperature and be 700~760 ℃, warm up time is 35~50 minutes, heating zone temperature is that 960~1000 ℃, heat-up time are 35~50 minutes, soaking zone temperature is that 990~1030 ℃, soaking time are 30~40min, and to control furnace atmosphere be weak reducing atmosphere;
Become in the step of wire rod at described temperature-controlled rolling, controlling start rolling temperature is 950~990 ℃;
In the step of the described rolling of weaving silk, controlling laying temperature is 860~880 ℃;
In the cooling step of described control, adopt that stelmor control cold line coils to roll rear control cooling, the cooling rate that controlling board twists in before pearlitic transformation is 9.5~10.5 ℃/s, pearlitic transformation temperature is controlled at 640~690 ℃, after phase transformation, cooling rate is 1.5~2.5 ℃/s, make cooling after, wire rod surface temperature before aftertreatment is less than or equal to 300 ℃.
2. the production technique of 82B wire rod for high-strength prestressed steel wire according to claim 1, it is characterized in that, described temperature-controlled rolling becomes the step of wire rod to comprise to make continuously cast bloom to form successively the step of wire rod by roughing unit, intermediate mill, pre-finishing mill group, finishing train and reducing sizing mill group, wherein, the temperature that control wire rod enters finishing train entrance is 850~880 ℃, and the temperature that control wire rod enters reducing sizing mill group entrance is 850~880 ℃.
3. the production technique of 82B wire rod for high-strength prestressed steel wire according to claim 1, is characterized in that, the nominal diameter of described wire rod finished product is 6.5mm.
4. the production technique of 82B wire rod for high-strength prestressed steel wire according to claim 1, is characterized in that, the local total decarburized layer degree of depth in one side of described wire rod finished product is not more than 1.5% of wire rod finished product nominal diameter.
5. the production technique of 82B wire rod for high-strength prestressed steel wire according to claim 1, is characterized in that, in the metallographic structure of described wire rod finished product, be mainly nodular troostite, sorbitic content is no less than 90%.
6. the production technique of 82B wire rod for high-strength prestressed steel wire according to claim 1, is characterized in that the actual measurement tensile strength R of described wire rod finished product m>=1200MPa, elongation A>=11%, relative reduction in area Z>=30%.
CN201210372518.9A 2012-09-29 2012-09-29 Production process for 82B wire rod used for high strength prestressed steel wire and wire rod thereof CN102876983B (en)

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