CN104805354A - Boracic deep low temperature hot rolling H-section steel and preparation method thereof - Google Patents
Boracic deep low temperature hot rolling H-section steel and preparation method thereof Download PDFInfo
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Abstract
The invention discloses a boracic deep low temperature hot rolling H-section steel and a preparation method thereof. The specification range of the H-section steel is in a small specification of below H300*300*10*15, and the H-section steel has the performance requirements that the longitudinal low-temperature impact of wing plates at the temperature of -50 to -70 DEG C is greater than or equal to 80J, the transverse low-temperature impact of the wing plates at the temperature of -20 DEG C is greater than or equal to 70J, the longitudinal low-temperature impact of web plates at the temperature of -50 to -70 DEG C is greater than or equal to 100J, and the performance of the steel is higher than that of the national standard GB/T1591-2008 low-medium high-strength structure E-level steel that the low-temperature impact is greater than or equal to 34J at -40 DEG C. In order to guarantee deep low temperature impact toughness, the low temperature impact toughness is guaranteed by adopting the cooperation of low carbon, low silicon, high manganese and vanadium boron. The H-section steel comprises the following chemical components in percentage by weight: 0.06% to 0.15% of C, 0.15% to 0.25% of Si, 1.0% to 1.50% of Mn, smaller than or equal to 0.010% of P, smaller than or equal to 0.010% of S, 0.070% to 0.10% of V, 0.005% to 0.02% of B, greater than or equal to 0.025% of Alt, smaller than or equal to 2.0*10<-4> of [H], smaller than or equal to 20*10<-4> of [O], smaller than or equal to 60*10<-4> of [N] and the balance of Fe. The production technology comprises the steps of furnace revolving, LF refining, VD vacuum, matrix blank continuous casting, H-section steel rolling and straightening.
Description
Technical field
The present invention relates to metallurgical technology field, particularly relate to one and adopt rectangular bloom production boracic deep hypothermia hot rolled H-shaped and preparation method thereof.
Background technology
NORTHWEST CHINA, the Northeast's winter temperature are cold, and the requirement of structural steel On Impact Toughness needs to reach about-50 DEG C; In addition offshore platform construction, polar region exploitation, etc. in Special use and outlet Russia etc. national requirements is hot rolled H-shaped meets-50 DEG C to-70 DEG C impelling strength technical requirementss.S275NL, S355NL, S420N, S460NL continuous request-50 DEG C ballistic work >=27J that such as European standard EN10025-3 produces; Day marks the grades of steel such as SLA325, SLA365 and requires-55 DEG C of ballistic works, С 345, С 345 К, С 375 grade of steel requirements-70 DEG C of ballistic work >=29J that Russia mark Г О С Т 27772-88 produces.
The technique means of hot rolled H-shaped guarantee low-temperature impact toughness mainly contains two kinds of approach: one realizes refined crystalline strengthening by controlled rolling and controlled cooling in rolling process, reaches the object ensureing low-temperature impact toughness; Another kind ensures that the alloying constituent such as nickel, molybdenum of low-temperature impact toughness reaches low-temperature impact toughness high object by adding.All there is obvious deficiency in these two kinds of approach, controlled rolling and controlled cooling Fabricating Technology of Fine-grained Strengthening is very difficult to control aborning, require high, temperature to control to be difficult to realize to milling train and qualification rate lower, simultaneously large on rhythm of production impact, be not suitable for continuous batch to produce, after adopting the shaped steel welding after controlled rolling and controlled cooling Fabricating Technology of Fine-grained Strengthening in addition, weld seam is low relative to matrix hardness; The second approach adds a large amount of nickel, molybdenum alloy low-temperature impact toughness is significantly reduced, but due to nickel molybdenum cost too high, economic production is difficult to realize.Seek produce a kind of stablize lower than-40 DEG C to-60 DEG C low-temperature impact toughness and also the H profile steel of low production cost extremely important, and there is great economy and social benefit, perfect to Chinese H profile steel product, has Great significance by big steel country to iron and steel transformation of making the country prosperous to China.
What require that deep hypothermia impelling strength requires at present is hot rolled H-shapedly generally low-alloy high-tensile structural steel, wherein more extensive with Q345 level applications.Q345 rank C, D, E level steel require to have good low-temperature flexibility, and GB/T1591-2008 requires Q345E steel longitudinally-40 DEG C >=34J.At present, steel over-all properties, particularly low-temperature impact toughness are improved to the technique that Q345 rank low-alloy high-tensile structural steel mainly takes niobium, vanadium, titanium microalloying and controlled rolling and controlled cooling to combine.Its strengthening mechanism is precipitation strength and refined crystalline strengthening, and the latter is also useful to toughness.In the actual industrial production process of Q345 rank H profile steel, through niobium, vanadium, titanium after single or combination microalloying and cooling controlling and rolling controlling process, lower than-40 DEG C, ballistic works fluctuation is comparatively large and qualification rate is not high.
" a kind of have favorable low-temperature impact toughness add boron H profile steel and preparation method thereof " microalloy adopts the composite evacuated induction furnace of Nb-B to smelt, " a kind of boracic vanadium low-temperature impact toughness excellent hot rolled H-shaped and preparation method thereof " microalloy adopts V-B compound, and this patent is applied to Hot Metal in Beam Blank and produces-40 DEG C >=34J Low Temperature Hot Rolling H profile steel.From composition, strictly control B content adds the upper limit to this patent is 0.002%, what in actual industrial production, data show B element too much adds the ductility and the impact that directly affect steel, and when B content is added beyond 0.003%, ductility and impact property obviously decline." a kind of boracic vanadium low-temperature impact toughness excellent hot rolled H-shaped and preparation method thereof " is high-carbon, boron add-on is more, does not control aluminium, and gas controls not strict." a kind of boracic vanadium low-temperature impact toughness excellent hot rolled H-shaped and preparation method thereof " controls the low temperature finish to gauge technique of difficulty for adopting.
Summary of the invention
The present invention relates to a kind of boracic deep hypothermia hot rolled H-shaped and preparation method thereof, comprise smelting technology and rolling technology, its object is to provide a kind of micro-alloyed hot-rolled H profile steel and production technique thereof, product appropriate design composition of the present invention, interpolation trace alloying element V, B, and make its mechanical property reach deep hypothermia impact requirement by optimized production process method, can produce with the easiest, efficient method and manufacture again, reduce production cost.
To achieve these objectives, a kind of boracic deep hypothermia of the present invention is hot rolled H-shaped, described H profile steel chemical composition and content weight percent thereof are: C 0.06 ~ 0.15%, Si 0.15 ~ 0.25%, Mn 1.0 ~ 1.50%, P≤0.010%, S≤0.010%, V0.070 ~ 0.10%, B 0.005 ~ 0.02%, Alt>=0.025%, [H]≤2.0 × 10 in steel
-4, [O]≤20 × 10
-4, [N]≤60 × 10
-4all the other are Fe, and production technique is converter, LF refining, VD vacuum, rectangular billet caster, casting billet surface cleaning, Rolling With Universal Mill H profile steel and aligning.
The preferred technical scheme of the present invention is: its chemical composition and weight percent are: C 0.13%, Si 0.20%, Mn 1.25%, P0.008%, S0.005%, N0.0050%, V0.07%, B 0.01%, Alt>=0.025%, [H]≤2.0 × 10 in steel
-4, [O]≤20 × 10
-4, all the other are Fe.
Production method of the present invention is: during smelting, converter terminal control C (weight percent %) >=0.06, P < 0.01 controls tapping temperature and is greater than 1640 DEG C; Adopt silicomanganese and Fe-al-mn Deoxidizing, have aluminium final deoxygenation; Tapping pushing off the slag, pushing off the slag unsuccessfully must be skimmed; Refining white slag operates; Refining adds vanadium iron and ferro-boron latter stage, after adding vanadium iron weak stir 3 minutes after add ferro-boron; Dark vacuum time >=the 15min of VD, dark vacuum tightness≤0.1KPa, soft blow time >=15min.After VD, molten steel composition target value for (weight percent %) is: C 0.13, Si 0.20, Mn 1.25, P0.008, S0.005, N0.0050, V0.07, B 0.01, Alt >=0.025, all the other are Fe and inevitable impurity.Continuous casting liquidus temperature: TL=1515 DEG C; Molten steel overheat Δ T≤20 DEG C; Permanent pulling rate is adopted to operate, pulling rate 0.59-0.66m/min.Steel billet stacking slow cooling after casting.Cut strand 100mm-300mm thickness and carry out low-power sulphur print inspection.Steelworks ensures that steel billet is sent to Steel Mill without after surface quality and internal soundness.Steel Mill again carries out visual inspection before strand enters process furnace, have scab, crackle, the steel billet that sticks up skin choose.Furnace temp is 1250 DEG C ~ 1280 DEG C; Be weak reducing atmosphere in process furnace, steel billet enters roughing mill advance horizontal high voltage water dephosphorization (before namely entering BD1 frame), rolling start rolling temperature 1180 DEG C ~ 1220 DEG C, CCS frame (universal mill) carries out 8 passes, temperature 880 DEG C ~ 930 DEG C before Rolling With Universal Mill speed >=4m/s, CCS finishing rolling mill.
Technical requirement: casting billet surface without scabbing, crackle, stick up skin, sand holes, be mingled with, the defect such as pore; Non-metallic inclusion (level) A≤2.0, B≤1.5, C≤2.0, D≤2.0, Ds≤2.0; Grain fineness number is not less than 8 grades, and crystal grain inequality degree, in three level ranges, is organized as perlite+ferrite; Yield strength >=350MPa, tensile strength is 500MPa ~ 550MPa, unit elongation A% >=30, low-temperature impact-70 DEG C >=34.J
Rectangular bloom of the present invention produces the low temperature resistant H profile steel of low-alloy high-strength, and it is characterized in that the web of H profile steel and wing plate have excellent mechanical property, performance is higher than standard GB/T/T1591-2008.This H profile steel tensile strength 500MPa ~ 550MPa, yield strength >=350MPa, unit elongation >=30%,-40 DEG C of impact >=100J, wing plate is-50 DEG C to-70 DEG C low-temperature impact >=80J longitudinally, and horizontal low-temperature impact-20 DEG C >=70J of wing plate, web is-50 DEG C to 70 DEG C low-temperature impact >=100J longitudinally.
Advantage of the present invention is:
1. the present invention is by adding V, B microalloying, adopts low silicon, low-sulfur, low-phosphorous Composition Design, improves the over-all properties of H profile steel, and production technique is simple, is beneficial to popularization;
2. in the present invention, V adds separately fashionable formation VC in micro-alloyed steel, and belong to mesophase spherule, its chemical formula can at VC, V
4c
3between change.When general low nitrogen content, the solubleness of VC in γ-Fe is more much higher than NbC, below 900 DEG C, and V (C, N) can be dissolved in completely in γ-Fe, therefore the Main Function of vanadium is the alternate precipitation in γ-α transition process and the precipitation strength in ferrite.The strengthening and toughening mechanism of of Vanadium Microalloyed Plate Steels mainly contains refined crystalline strengthening, precipitation strength and solution strengthening;
3. before the present invention can realize last passage machine of universal mill finish to gauge, temperature carries out H profile steel high-temperature final rolling in 910 DEG C-950 DEG C, and the operation of rolling does not carry out controlled cooling model, and carry out delivery with As rolled and use, steel have good welding property;
4. suppress phosphorus, sulphur at the segregation of crystal boundary and the grain boundary fracture that causes adding on a small quantity of micronutrient boron, significantly improve low-temperature flexibility, this is because boron inhibits phosphorus, sulphur can improve to the reduction of crystal boundary and boron self result that Grain-boundary Junctions makes a concerted effort;
5. boron adds in steel can increase outside the hardening capacity of steel, found that trace B element also existed microstructure coarsening and reduces intensity in soft steel in the last few years in a large amount of industrial production, improve the effect of unit elongation and low-temperature impact toughness, that can reduce steel on the contrary when boron add-on is too much in steel prolongs plasticity.Therefore the advantage that the present invention gives prominence to is the content strictly controlling steel boron, to reaching optimum strong plasticity coupling;
6. present invention achieves the industrial production that rectangular bloom produces small dimension H profile steel deep hypothermia.
Below in conjunction with accompanying drawing, the invention will be further described.
Accompanying drawing explanation
Fig. 1 a wing plate-40 DEG C impacts sample, grain fineness number 9.5 grades;
Fig. 1 b web-40 DEG C impacts sample, grain fineness number 11 grades;
Fig. 1 c wing plate-50 DEG C of impact specimens, grain fineness number 9.5 grades;
Fig. 1 d wing plate-70 DEG C of impact specimens, grain fineness number 9.5 grades;
Fig. 2 a wing plate is-40 DEG C of impact fracture macro morphologies longitudinally;
Fig. 2 b-40 DEG C of impact fracture formation of crack is cleavage feature;
Fig. 2 c-40 DEG C of impact fracture expansion area is cleavage feature;
Fig. 3 a wing plate is-70 DEG C of impact fracture macro morphologies longitudinally;
Fig. 3 b-70 DEG C of impact fracture formation of crack is cleavage feature;
Fig. 3 c-70 DEG C of impact fracture expansion area is cleavage feature;
Fig. 4 a wing plate 0 DEG C of transverse impact fracture apperance;
There is longitudinal band clearly in Fig. 4 b 0 DEG C of transverse impact fracture face;
MnS inclusion on Fig. 4 c 0 DEG C of transverse impact longitudinal band;
Embodiment
Below in conjunction with embodiment, to above-mentioned being described in more detail with other technical characteristic and advantage of the present invention.
Embodiment 1:
The chemical component weight per-cent of steel is: C 0.13%, Si 0.20%, Mn 1.25%, P0.005%, S0.005%, N 0.0050%, V0.07%, B 0.01%, Alt 0.028%, all the other are Fe, and production method comprises 100t converter, external refining, VD vacuum, continuous casting, heating, universal rolling successively.The parameter of each step is: adopt 100t converter smelting, it is 1650 DEG C that converter terminal C 0.06%, P 0.02%, S 0.04% controls converter terminal tapping temperature; Slag charge is joined and alloy addition comprises: lime 360 kilograms, 400 kilograms, ferromanganese, ferrosilicon 100 kilograms, silicomanganese 240 kilograms, vanadium iron 70 kilograms, aluminum steel 152 kilograms during external refining; LF temperature in place 1523 DEG C, LF offs normal temperature 1640 DEG C, heat-up time 50min, LF refining time 63 minutes; Wherein LF molten steel composition weight percent in place is C0.11%, Si0.06%, Mn1.02%, P0.02%, S0.03%, Al0.04%; LF molten steel composition weight percent of offing normal is C0.15%, Si0.19%, Mn1.39%, P0.01%, S0.01%, Al0.03%, V0.08%, B0.0012%; Temperature 1623 DEG C before VD, dark vacuum time 13min, temperature 1584 DEG C after dark vacuum processing time 20min, VD, feeds silicon-calcium wire 150m and makes inclusion modification, and soft blow time 15min ensures that inclusion fully floats; Teeming temperature 1575 DEG C during continuous casting, continuous casting superheating temperature controls at 20 DEG C, and pulling rate is 0.48m/min.Steel billet stacking slow cooling after casting; Finished product composition by weight percent is: C 0.13%, Si 0.20%, Mn 1.25%, P0.005%, S0.005%, V0.07%, B 0.01%, Alt 0.028%, [O] 0.00128, [N] 0.00323, [H] 0.0001.Steelworks ensures that steel billet is sent to Steel Mill without after surface quality and internal soundness; The strand that rectangular bloom is of a size of 280mm × 325mm by Steel Mill again carries out visual inspection before entering process furnace, have scab, crackle, the steel billet that sticks up skin choose; Furnace temp is 1250 DEG C; 2 hours heat-up times, be weak reducing atmosphere in soaking 40min process furnace, steel billet enters roughing mill advance horizontal high voltage water dephosphorization (before namely entering BD1 frame), rolling start rolling temperature 1200 DEG C, soaking zone temperature 1266 DEG C, the first heating zone temperature 1232 DEG C, the second heating zone temperature 1103 DEG C, cogging temperature 1130 DEG C before BD1, BD1 amounts to 7 passages, and CCS amounts to 3 passages, rolling specs H244 × 175 × 11 × 7, finishing temperature 918 DEG C, temperature on cooling table 725 DEG C.
Longitudinally and laterally sample from H profile steel wing plate respectively, then carry out mechanical property, metallographic structure analysis from the longitudinal sampling of web.According to the regulation of GB/T1591-2008 ratio in ancient name for China (V-type) impact experiment, when thickness of steel product is less than 12mm, should adopt 10mm × 7.5mm × 55mm or 10mm × 5mm × 55mm small size sample, shock absorption energy is be not less than prescribed value 75% or 50%.Be cooled to black steel state less than about 500 DEG C after rolling to sample first, to place after 10 days (timeliness) again sub-sampling carry out mechanics performance determining.Under this technique, product mechanical property is in table 1, Charpy impact value in table 2, inclusion and fabric analysis in table 3,
Table 1 mechanical properties value
| Sample position | Numbering | Rel | Rm | A％ |
| Wing plate longitudinally | 69 | 367 | 519 | 32.5 |
| Wing plate longitudinally | 69 | 360 | 524 | 33.5 |
| Web longitudinally | 069 | 409 | 531 | 31.5 |
| Web longitudinally | 069 | 410 | 527 | 31.0 |
Table 2 Charpy impact value
Table 3 inclusion and tissue
Above-described embodiment is only be described the preferred embodiment of the present invention; not scope of the present invention is limited; under not departing from the present invention and designing the prerequisite of spirit; the various distortion that those of ordinary skill in the art make technical scheme of the present invention and improvement, all should fall in protection domain that claims of the present invention determines.
Claims (5)
1. a boracic deep hypothermia is hot rolled H-shaped, it is characterized in that chemical composition and the weight percent content thereof of described H profile steel are: C 0.06 ~ 0.15%, Si 0.15 ~ 0.25%, Mn 1.0 ~ 1.50%, P≤0.010%, S≤0.010%, V0.070 ~ 0.10%, B 0.005 ~ 0.02%, Alt>=0.025%, [H]≤2.0 × 10
-4, [O]≤20 × 10
-4, [N]≤60 × 10
-4, all the other are Fe.
2. boracic deep hypothermia according to claim 1 is hot rolled H-shaped, it is characterized in that: described H profile steel specification limit is below H300*300*10*15, its wing plate is-50 DEG C to-70 DEG C low-temperature impact >=80J longitudinally, horizontal low-temperature impact-20 DEG C >=70J of wing plate, web is-50 DEG C to-70 DEG C low-temperature impact >=100J longitudinally.
3. prepare the method that boracic deep hypothermia as claimed in claim 1 or 2 is hot rolled H-shaped, it is characterized in that comprising the following steps: hot metal pretreatment, 100t converter, external refining, VD vacuum, rectangular billet caster, heating, BD cogging, CCS universal rolling.
4. the preparation method that boracic deep hypothermia according to claim 3 is hot rolled H-shaped, is characterized in that the parameter of each step is: weight percent >=0.06% of converter terminal control C during smelting, the weight percent < 0.01% of P; Control tapping temperature and be greater than 1640 DEG C; Slag charge is joined and alloy addition comprises lime, ferromanganese, ferrosilicon, silicomanganese, vanadium iron, aluminum steel during external refining; Adopt silicomanganese and Fe-al-mn Deoxidizing, have aluminium final deoxygenation; Tapping pushing off the slag, pushing off the slag unsuccessfully must be skimmed; Refining white slag operates; Refining adds vanadium iron and ferro-boron latter stage, after adding vanadium iron weak stir 3 minutes after add ferro-boron; Dark vacuum time >=the 15min of VD, dark vacuum tightness≤0.1KPa, soft blow time >=15min; Continuous casting liquidus temperature: TL=1515 DEG C; Molten steel overheat Δ T≤20 DEG C; Permanent pulling rate is adopted to operate, pulling rate 0.4-0.65m/min; Cut strand 100mm-300mm thickness and carry out low-power sulphur print inspection; Furnace temp is 1100 DEG C ~ 1250 DEG C; 1 ~ 2 hour heat-up time, be weak reducing atmosphere in soaking 40min process furnace, the first heating zone temperature 1100 DEG C ~ 1250 DEG C, the second heating zone temperature 1100 DEG C ~ 1250 DEG C, be weak reducing atmosphere in process furnace, strand enters the dephosphorization of roughing mill advance horizontal high voltage water; , rolling start rolling temperature 1100 DEG C ~ 1200 DEG C, CCS universal mill carries out 7-9 passes, temperature 880 DEG C ~ 930 DEG C before Rolling With Universal Mill speed >=4m/s, CCS finishing rolling mill.
5. the preparation method that boracic deep hypothermia according to claim 4 is hot rolled H-shaped, it is characterized in that: molten steel composition target value is weight percentage as C 0.13% after described VD vacuum step, Si 0.20%, Mn 1.25%, P0.008%, S0.005%, N0.0050%, V0.07%, B 0.01%, Alt >=0.025%, all the other are Fe.
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Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN107299283A (en) * | 2017-05-27 | 2017-10-27 | 内蒙古包钢钢联股份有限公司 | Depth low temperature resistant hot rolled H-shaped and its production technology |
| CN110468344A (en) * | 2019-09-23 | 2019-11-19 | 包头钢铁（集团）有限责任公司 | A kind of boron low-cost high-strength of vanadium containing niobium is hot rolled H-shaped and preparation method thereof |
| CN110468336A (en) * | 2019-09-23 | 2019-11-19 | 包头钢铁（集团）有限责任公司 | A kind of low strain dynamic aging sensitivity steel for welded structures and its preparation process |
| CN110468337A (en) * | 2019-09-23 | 2019-11-19 | 包头钢铁（集团）有限责任公司 | A kind of low-cost high-strength of boron containing niobium is hot rolled H-shaped and preparation method thereof |
| CN110484822A (en) * | 2019-09-23 | 2019-11-22 | 包头钢铁（集团）有限责任公司 | A kind of high-strength thick hot-rolling H-shaped piling bar and preparation method thereof |
| CN115261705A (en) * | 2022-06-27 | 2022-11-01 | 包头职业技术学院 | Preparation method of high-strength high-toughness wear-resistant anti-fatigue steel guide plate |
Citations (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1164875A (en) * | 1995-08-31 | 1997-11-12 | 川崎制铁株式会社 | Hot-rolled steel sheet and process for producing the same |
| CN101812632A (en) * | 2009-11-03 | 2010-08-25 | 莱芜钢铁股份有限公司 | -40 to -60DEG C low-temperature impact toughness hot rolled H-shaped steel and preparation method thereof |
| CN102618781A (en) * | 2012-03-30 | 2012-08-01 | 莱芜钢铁集团有限公司 | Hot-rolled H-steel for low temperature-resistance structure and preparation method for hot-rolled H-steel |
| CN103276310A (en) * | 2013-05-31 | 2013-09-04 | 内蒙古包钢钢联股份有限公司 | Rare-earth-containing H-shaped steel with low-temperature toughness and production method thereof |
| CN103820706A (en) * | 2013-12-12 | 2014-05-28 | 山西新泰钢铁有限公司 | Hot-rolling H-shaped steel containing and vanadium boride and having excellent low-temperature impacttoughness and preparation method of hot-rolling H-shaped steel |
| JP5574059B2 (en) * | 2011-12-15 | 2014-08-20 | 新日鐵住金株式会社 | High-strength H-section steel with excellent low-temperature toughness and method for producing the same |
| CN104411846A (en) * | 2012-06-28 | 2015-03-11 | 杰富意钢铁株式会社 | High carbon steel pipe having excellent cold workability, machinability, and quenching properties, and method for manufacturing same |
-
2015
- 2015-04-30 CN CN201510216747.5A patent/CN104805354A/en active Pending
Patent Citations (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1164875A (en) * | 1995-08-31 | 1997-11-12 | 川崎制铁株式会社 | Hot-rolled steel sheet and process for producing the same |
| CN101812632A (en) * | 2009-11-03 | 2010-08-25 | 莱芜钢铁股份有限公司 | -40 to -60DEG C low-temperature impact toughness hot rolled H-shaped steel and preparation method thereof |
| JP5574059B2 (en) * | 2011-12-15 | 2014-08-20 | 新日鐵住金株式会社 | High-strength H-section steel with excellent low-temperature toughness and method for producing the same |
| CN102618781A (en) * | 2012-03-30 | 2012-08-01 | 莱芜钢铁集团有限公司 | Hot-rolled H-steel for low temperature-resistance structure and preparation method for hot-rolled H-steel |
| CN104411846A (en) * | 2012-06-28 | 2015-03-11 | 杰富意钢铁株式会社 | High carbon steel pipe having excellent cold workability, machinability, and quenching properties, and method for manufacturing same |
| CN103276310A (en) * | 2013-05-31 | 2013-09-04 | 内蒙古包钢钢联股份有限公司 | Rare-earth-containing H-shaped steel with low-temperature toughness and production method thereof |
| CN103820706A (en) * | 2013-12-12 | 2014-05-28 | 山西新泰钢铁有限公司 | Hot-rolling H-shaped steel containing and vanadium boride and having excellent low-temperature impacttoughness and preparation method of hot-rolling H-shaped steel |
Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN107299283A (en) * | 2017-05-27 | 2017-10-27 | 内蒙古包钢钢联股份有限公司 | Depth low temperature resistant hot rolled H-shaped and its production technology |
| CN110468344A (en) * | 2019-09-23 | 2019-11-19 | 包头钢铁（集团）有限责任公司 | A kind of boron low-cost high-strength of vanadium containing niobium is hot rolled H-shaped and preparation method thereof |
| CN110468336A (en) * | 2019-09-23 | 2019-11-19 | 包头钢铁（集团）有限责任公司 | A kind of low strain dynamic aging sensitivity steel for welded structures and its preparation process |
| CN110468337A (en) * | 2019-09-23 | 2019-11-19 | 包头钢铁（集团）有限责任公司 | A kind of low-cost high-strength of boron containing niobium is hot rolled H-shaped and preparation method thereof |
| CN110484822A (en) * | 2019-09-23 | 2019-11-22 | 包头钢铁（集团）有限责任公司 | A kind of high-strength thick hot-rolling H-shaped piling bar and preparation method thereof |
| CN115261705A (en) * | 2022-06-27 | 2022-11-01 | 包头职业技术学院 | Preparation method of high-strength high-toughness wear-resistant anti-fatigue steel guide plate |
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