CN102268615B - Engineering steel material with excellent core low-temperature impact toughness and lamellar tearing resisting performance and production method thereof - Google Patents

Engineering steel material with excellent core low-temperature impact toughness and lamellar tearing resisting performance and production method thereof Download PDF

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CN102268615B
CN102268615B CN201110186999XA CN201110186999A CN102268615B CN 102268615 B CN102268615 B CN 102268615B CN 201110186999X A CN201110186999X A CN 201110186999XA CN 201110186999 A CN201110186999 A CN 201110186999A CN 102268615 B CN102268615 B CN 102268615B
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CN102268615A (en
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廖卫团
温志红
何矿年
李桦
杨太阳
刘年富
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Shaoguan Iron And Steel Group Co Ltd Guandong Prov
SGIS Songshan Co Ltd
Shaogang Songshan Co Ltd Guangdong
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Shaoguan Iron And Steel Group Co Ltd Guandong Prov
Shaogang Songshan Co Ltd Guangdong
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Abstract

The invention relates to a production method of an engineering steel material with excellent core low-temperature impact toughness and lamellar tearing resisting performance. The engineering steel material comprises the following main components in percentage by weight: 0.030-0.010 percent of carbon, 1.20-1.60 percent of manganese, 0.10-0.35 percent of silicon, 0.015-0.03 percent of niobium, 0.005-0.020 percent of titanium, 0.020-0.040 percent of total aluminum, and not less than 0.10 percent of calcium/total aluminum; the engineering steel material also comprises the following residual components in percentage by weight: not more than 0.006 percent of nitrogen, not more than 0.004 percent of oxygen, not more than 0.015 of phosphorus, not more than 0.006 percent of sulfur, not more than 0.04 percent of arsenic, not more than 0.03 percent of stannum and not more than 0.02 percent of antimony; and except the main components and the residual components, the balance is ferrum. According to the engineering steel material and the production method provided by the invention, without adding nickel, vanadium and other expensive alloying elements and without adopting offline quenching and tempering treatment and other expensive equipment, the steel material with the yield strength of not less than 420 Megapascal and the excellent core toughness and lamellar tearing resisting performance can be obtained by only adopting a niobium and titanium micro-alloyed low carbon-manganese-niobium-titanium component system and fitting with an online quenching and tempering process.

Description

The production method of the engineering steels of the good and anti-lamellar tearing of heart section low-temperature impact toughness
Technical field
The present invention relates to a kind of metallurgical steel, more particularly, the present invention relates to a kind of engineering steels and production technique thereof of low C-Mn-Nb-Ti composition system.
Background technology
Along with China's Industrial Economic Development, high grade of steel high-performance steel grade is required progressively to improve, thereby the development and the exploitation that have driven domestic high-performance steel enter a brand-new stage.Wherein, bridge structure, Highrise buildings, ocean platform and hull structure etc. adopt other Hi-Stren steel of yield strength 420MPa level usually; And because the application scenario of said structure requires steel plate to bear certain stress at thickness direction, the impact of heart section and anti-layer state such as steel plate are torn ability, just easily cause structure deteriorate, therefore, these harsh engineering-environments have proposed requirements at the higher level to steel plate thickness performance uniformity, anti-lamellar tearing performance: require to guarantee that yield strength 420MPa rank thick steel plates has performance uniformity and the anti-lamellar tearing performance of good thickness direction.
Since blank bring center segregation and center porosity eliminate in follow-up being difficult in rolling, add the ununiformity of the rolling and process of cooling tissue of thick dimension board, cause steel plate thickness directional performance lack of homogeneity, especially the impact of heart section is difficult to reach requirement.When the lamellar tearing of steel plate welds exactly or steel construction when meeting with stresses, the process that matrix metal ftractures and expands along inclusion under the effect of thickness direction (Z-direction) stress, therefore, steel inclusion quantity and inclusion morphology are large to the lamellar tearing performance impact.
And for reaching the thickness directional properties homogeneity, prior art except adding Nb, Ti, is also added other multiple alloying elements aspect microalloying, process aspect, and existing three kinds of main production:
The one, adopt the off-line hardening and tempering process, and add a large amount of alloying elements such as Ni, Cr etc.Such as " Wide and Thick Slab " 2010 the 4th interim disclosed " developments of high strength steel plate for ship building NVD (E) 420 steel plates " documents, wherein just add the elements such as V, Cr, Ni, B, and adopt the off-line hardening and tempering process to scheme to reach performance requriements.
The 2nd, adopt normalizing process to satisfy the thickness directional properties homogeneity, for example:
Publication number is the production method that the Chinese patent file of CN101921953A discloses a kind of anti-corrosion and high strength ultra-thick steel plates, this technology is except adding Nb, Ti, also add the alloying elements such as Cu, Ni, V, this technical products center toughness improves, be used for satisfying yield strength 355MPa rank steel grade, yield strength reaches 420-445MPa among the embodiment, but as yield strength 420MPa rank steel grade, the intensity surplus only is 0-25MPa, and production process has subtle change just may cause intensity not conform to; And because it adopts the Heating temperature of normalizing process high, the steel plate reaustenitizing obtains ferrite and adds the tissue that perlite is the master after the cooling, need on the intensity to add the requirement that more alloying element just can reach 420MPa, so production cost is high.
And for example publication number is engineering steel and the production method thereof that the Chinese patent file of CN101643885 discloses a kind of anti-lamellar tearing excellent property, it is for reaching yield strength 420MPa rank, add Cr, Ni alloying element, and adopt normalizing heat treatment method to improve the thickness direction homogeneity of structure, carry out the anti-lamellar tearing performance of inclusion modification processing improvement by adding Zr.Because the molten point of Zr is high, its adding has increased the difficulty of producing, and improves production cost.
The 3rd, high cleanliness steel technology is in conjunction with TMCP technique, but be Plate Steel and the manufacture method that the Chinese patent file of CN1804093 discloses a kind of Large Heat Input Welding such as publication number, this technology is by the B-Mg microalloying, and the molten steel RE-treated is with cleaning molten steel and make inclusion modification.And RE-treated often causes the again pollution of molten steel because of its content and the evenly difficult control of performance.And do not relate to heart section impact property and anti-lamellar tearing ability in this technology.
As fully visible: thus conventional art has carried out following effort for the high degree of uniformity of realizing 420MPa intensity rank microcosmic point crystal grain reaches good thickness center toughness and anti-lamellar tearing performance:
The alloying aspect, various process using are added micro alloying element in a large number, except Nb, Ti, also add Cu, Ni, Cr, V, B etc., the result has increased steel-making cost, and the interpolation of a large amount of microalloy elements affects the billet surface quality, joins such as adding of Cu and causes the steel plate crackle; The affiliation that adds of Ni causes iron scale to be difficult to remove, and when containing Ni in the steel, if oxidation occurs, the part that Ni concentrates will be protruding, and interface shape is rough and uneven in surface, and the separability of squama is worsened.
Process aspect perhaps adopts complicated Clean Steel technology, such as RE-treated, Zr processing etc., but is difficult to realize; Perhaps adopt normalizing thermal treatment, but for organizing the loss of strength that changes after the compensation normalizing thermal treatment, need to add a large amount of microalloy elements; Perhaps adopt the off-line hardening and tempering process, but because the off-line modifier treatment need to be equipped with the expensive device such as quenching press, increased and reheated and the two procedures of quenching, corresponding production cycle and the production cost of having increased, and can't produce for the steel mill that is not equipped with the off-line tempering product line.And this had both restricted the development and progress of vast steel production enterprise, also was unfavorable for the research and development of 420MPa intensity rank steel.
Summary of the invention
Above-mentioned shortcoming for prior art, the objective of the invention is to provide the production method of the engineering steels of the good and anti-lamellar tearing of a kind of heart section low-temperature impact toughness, it has following advantage: the low C-Mn-Nb-Ti composition system that only adopts Nb, Ti microalloying, cooperate press quenching to add tempering process, and needn't add the expensive alloy element such as Ni, V, needn't adopt the expensive device such as off-line modifier treatment, just can obtain the steel of yield strength 〉=420Mpa, good center toughness and anti-lamellar tearing performance.
For this reason, one of technical solution of the present invention is the engineering steels of the good and anti-lamellar tearing of a kind of heart section low-temperature impact toughness, it comprises the principal constituent of following weight percent (wt%): C:0.030~0.10, Mn:1.20~1.60, Si:0.10~0.35, Nb:0.015~0.03, Ti:0.005~0.020, Alt:0.020~0.040, and Ca/Alt 〉=0.10, Fe: be the surplus outside above-mentioned principal constituent and the following remaining composition; It also comprises the remaining composition of following weight percent (wt%): N≤0.006, O≤0.004, P≤0.015, S≤0.006, As≤0.04, Sn≤0.03, Sb≤0.02.
Tradition guarantees that the center toughness steel grade is owing to its steel billet material reason, as producing other steel of high-intensity high-tenacity level, must add the expensive alloy element such as Cr, Ni, V, or adopt little B to process, adopt normalizing or off-line hardening and tempering process on the technique, normalizing process easily causes intensity can not reach requirement, and the off-line hardening and tempering process need possess the expensive equipments such as quenching press, and complex procedures, and present technology does not reach the correlation technique of heart section impelling strength relevant for yield strength 420MPa rank.
Disadvantage for traditional material, the inventor is on the basis of great many of experiments, be based on the equipment of common iron and steel metallurgy enterprise, by the purity of suitable raising steel and the Control and Inclusion Removal technology of characteristic, exploitation has made the steel that the present invention has the low-carbon bainite tissue;
The chemical composition of steel of the present invention, its prescription main principle is low-carbon (LC), Nb, Ti microalloying.Each coherent element carries out the composition proportion adjustment according to following principle:
Carbon is the strengthening element of traditional steel, but it is extremely harmful to toughness and weldability.Carbon content has good weldability less than 0.1% the time.And along with the development of the technology such as microalloying and controlled rolling and controlled cooling, so that carbon content can also keep it than high-strong toughness when reducing.But when carbon content in steel<0.01%, owing to the Precipitation of the minimizing of interstitial carbon and Nb, C, N reduces the crystal boundary that weakened, make the heat affected zone Grain-Boundary Phase to embrittlement.From over-all properties, the carbon content scope fixes on 0.03%~0.10%.
Silicon mainly plays solution strengthening effect, adds silicon in the steelmaking process as reductive agent and reductor; The silicone content increase can make hardness and the strength increase of steel, but plasticity and toughness descend and the welding property of reduction steel.The present invention controls its scope 0.10~0.35%.
Manganese mainly plays solution strengthening.In the situation that carbon content is identical, along with the increase of manganese content, strength increase, manganese be the effect of landing low transformation temperature also, helps grain refining, so manganese is indispensable element.But the manganese too high levels can make toughness drop, causes Banded Structure of Steel Plate serious, strengthens anisotropy, and the present invention controls its scope 1.20~1.60%.
The easy generation MnS of being combined with manganese of sulphur is mingled with, and affects the low-temperature impact toughness of steel; Phosphorus is the element that easily causes segregation in steel, and it also can worsen welding property, significantly reduces the low-temperature impact toughness of steel, improves ductile-brittle transition temperature.Therefore, P, S element should be removed as far as possible.
And owing to As, Sn, Sb element their electronegativity factor and size factor, so that they are very easily at Grain Boundary Segregation, reduce crystal boundary force of cohesion.Be that the work of rupture of steel reduces on the impact of macro property, impelling strength obviously reduces.Therefore, should give suitably controlling especially to its content.
Niobium is to obtain one of the most effective micro alloying element of good controlled rolling effect.Usually after containing the niobium steel and being heated to 1200 ℃, soaking 2hr, but in the steel niobium solid solution in austenite.This solid solution niobium can hinder Austenite Grain Growth in heat-processed, at carbon, the nitride of rolling middle meeting Precipitation niobium on dislocation, subgrain boundary, crystal boundary, hinder Austenite Dynamic Recrystallization, and crystal grain thinning improves intensity, improves steel plate toughness.
The effect of titanium mainly is that its undissolved carbon, nitride particles are distributed on the austenite grain boundary, fix nitrogen in the steel with little titanium in the steel, owing to the TiN that forms indissoluble has eliminated the free nitrogen in the steel, thereby improve the toughness of steel, TiN can hinder Austenite Grain Growth in the heat-processed of steel before hot-work.Improve the solid solubility of niobium under the austenitic state, further bring into play crystal grain thinning and the precipitation strength effect of niobium.In addition, trace amount of titanium can prevent from coarse-grain occurring at welded heat affecting zone, guarantees that steel have high tenacity at welded heat affecting zone.The add-on of titanium is too much, can form the disadvantageous TiC of toughness.Therefore, titanium content is controlled at 0.005-0.020% in the actual production.
The effect of calcium mainly is the sex change for inclusion.Molten steel is carried out ladle calcium process, can promote to form the calcium-aluminate that is easy to float, reduce Al 2O 3The formation of inclusion, and can avoid generating the MnS of dendritic crystal state, but give birth to glomerate CaS, thus reduce inclusion to the impact of the anti-lamellar tearing performance of steel plate.
Under the smelting system of back, cooperation that press quenching adds tempering process, as indicated in embodiment of the invention actual measurement parameter, the present invention fills a prescription and can produce the steel of yield strength 〉=other high strength of 420MPa level, good center toughness and anti-lamellar tearing performance; Be fit to be applied on the harsh ocean platform of engineering-environment, hull structure and the high building structure.
Be the stable processing technique of the low-temperature impact toughness that further improves engineering steels and crack arrest characteristic, stable operation steel, engineering steels of the present invention comprises following concrete improvement:
In the described engineering steels principal constituent, the weight percent of Ca (wt%) is: 0.002~0.005.
For further improving the structure composition index performance of engineering steels, engineering steels of the present invention comprises following concrete improvement:
Described engineering steels reaches following technical indicator: yield strength ReH 〉=420MPa, tensile strength Rm 〉=520MPa, the V-type Impact energy Ak v of thickness heart section 〉=100 joules (J) in the time of-60 ℃, Z-direction tensile property 〉=50%.
Correspondingly, another technical solution of the present invention is the production method of the engineering steels of the good and anti-lamellar tearing of a kind of as mentioned above heart section low-temperature impact toughness, and it comprises the steps:
A, converter smelting: control enters converter molten iron S≤0.005%, the pushing off the slag of keeping under strict control of tapping;
B, ladle furnace LF refining: carry out refining to going out the converter molten iron, make LF stove molten steel;
C, vacuum degassing furnace RH refining: carry out vacuum outgas to going out LF stove molten steel, total argon blowing time 〉=30 minutes, evacuated pressure≤1kPa, vacuumize hold-time 〉=15min, feeding CaSi line or FeCa alloy wire in ladle, vacuum outgas is carried out to going out LF stove molten steel in Ca/Alt 〉=0.10 in the control steel, make refined molten steel, in ladle, feed CaSi line or FeCa alloy wire by molten steel 700-800g/t ratio per ton;
D, continuous casting: adopt the refined molten steel continuous casting, make the thick strand of 250mm, then more than the cooling in heap 48hr; Casting process adopts light soft reduction process, and the draft on the fan-shaped section unit length is controlled at 1-3.5mm/m;
E, strand heating: strand behind the cooling in heap is heated, and the whole time of heating is pressed slab thickness timing rate 〉=8min/cm control, wherein, 1150-1280 ℃ of heating zone control temperature, 1230-1250 ℃ of soaking zone control temperature:
F, controlled rolling: carry out roughing, finish rolling to heating rear strand, wherein, roughing: the single pass draft in control roughing speed 1.5~2.5m/s, 980~1100 ℃ of temperature, rear 2 roads greater than 15%, roughing total deformation rate 〉=60%; Finish rolling: control finish rolling speed 1.5~6m/s, start rolling temperature 820-940 ℃, finishing temperature 770-820 ℃, reduction in pass are 4-30%, and the finish rolling total deformation rate is 50~75%, makes the finish rolling plate;
G, press quenching: the finish rolling plate is carried out water-cooled, and the control speed of cooling is 5 ℃/s-25 ℃/s, and the quenching final temperature is 350-550 ℃, makes the quenching plate;
H, temper: the quenching plate is carried out temper, 620 ± 10 ℃ of tempering temperatures, tempering time (min) is controlled to be 3HD+10 by quenching panel thickness HD (mm), makes described engineering steels finished product after quality inspection, and the steel product maximum ga(u)ge is 60mm.
Step I, namely to the tempering plate align, more than the cooling in heap 24hr.
Engineering steels production method of the present invention is on the improvement basis of steel billet proportioning of the present invention and quality, give full play to the tooling device of suiting measures to local conditions at the replenishing of parameter and operating aspect, cooperation, guarantee effect, with comparatively simple and crude condition, easy steps comparatively, realize obtaining the purpose of the steel of yield strength 〉=420Mpa, good center toughness and anti-lamellar tearing performance.
For further improving the over-all properties of high-performance engineering steel, engineering steels of the present invention comprises the improvement of following concrete technology parameter aspect:
Among the described step C, evacuated pressure is controlled to be 0.02-0.2kPa, and vacuumizing the hold-time is 15-20min, behind feeding CaSi line or FeCa alloy wire, also comprises the operation of soft blow 〉=5 minute.
Among the described step D, also comprise the loose and segregation≤B1 level of control strand, thick strand cooling in heap is 48-60hr..
In the described step e, the whole time of heating is controlled at 8-10min/cm by slab thickness.
In the described step F, the last 2-3 percentage pass reduction of finish rolling is as the criterion to guarantee plate shape.
The invention will be further described below in conjunction with specific embodiment.
Embodiment
In chemical composition scope of the present invention, (wt%) is as shown in table 1 to determine embodiment 1,2,3 chemical compositions, wherein all controlling Fe is 97.7~98.6, N≤0.006,0≤0.004, As≤0.04, Sn≤0.03, Sb≤0.02, embodiment 1,2,3 metallurgy and foundry steps and control parameter are as shown in table 2, embodiment 1,2,3 main roughing, finish rolling, press quenching step and control parameter are as shown in table 3, and the 420MPa strength steel sheet finished steel mechanical property that makes is as shown in table 4.The typical gold phase constitution that obtains is acicular ferrite+granular bainite+a small amount of granular ferrite.
Contrast 1 is " Wide and Thick Slab " magazine the 4th phase in 2010 13 to 17 pages of disclosed " developments of high strength steel plate for ship building NVD (E) 420 steel plates " documents in the table 1,2,3, and contrast 2 is the CN101643885 patent document for publication number.
Table 1 steel proportioning chemical composition (wt%)
Table 2 metallurgy and foundry system
Table 3 press quenching adds the tempering process characteristic parameter
Table 4 performance situation
By upper table 4 performance perameter as seen: the surplus of the yield strength of engineering steels of the present invention is enough abundant, and steel plate all reaches good in center toughness, anti-lamellar tearing performance and related fields performance index.

Claims (5)

1. the production method of the engineering steels of the good and anti-lamellar tearing of a heart section low-temperature impact toughness, described engineering steels, it comprises the principal constituent of following weight percent (wt%): C:0.030~0.10, Mn:1.20~1.60, Si:0.10~0.35, Nb:0.015~0.03, Ti:0.005~0.020, Alt:0.020~0.040, the weight percent of Ca (wt%) is: 0.002~0.005, and Ca/Alt 〉=0.10, Fe: be the surplus outside above-mentioned principal constituent and the following remaining composition; It also comprises the remaining composition of following weight percent (wt%): N≤0.006, O≤0.004, P≤0.015, S≤0.006, As≤0.04, Sn≤0.03, Sb≤0.02;
Its production method comprises the steps:
A, converter smelting: control enters converter molten iron S≤0.005%, the pushing off the slag of keeping under strict control of tapping;
B, ladle furnace LF refining: carry out refining to going out the converter molten iron, make LF stove molten steel;
C, vacuum degassing furnace RH refining: carry out vacuum outgas to going out LF stove molten steel, total argon blowing time 〉=30 minutes, evacuated pressure≤1kPa, vacuumize hold-time 〉=15min, feeding CaSi line or FeCa alloy wire in ladle, vacuum outgas is carried out to going out LF stove molten steel in Ca/Alt 〉=0.10 in the control steel, make refined molten steel, in ladle, feed CaSi line or FeCa alloy wire by molten steel 700-800g/t ratio per ton;
D, continuous casting: adopt the refined molten steel continuous casting, make the thick strand of 250mm, then more than the cooling in heap 48hr; Casting process adopts light soft reduction process, and the draft on the fan-shaped section unit length is controlled at 1-3.5mm/m;
E, strand heating: strand behind the cooling in heap is heated, and the whole time of heating is pressed slab thickness timing rate 〉=8min/cm control, wherein, and 1150-1280 ℃ of heating zone control temperature, 1230-1250 ℃ of soaking zone control temperature;
F, controlled rolling: carry out roughing, finish rolling to heating rear strand, wherein, roughing: the single pass draft in control roughing speed 1.5~2.5m/s, 980~1100 ℃ of temperature, rear 2 roads greater than 15%, roughing total deformation rate 〉=60%; Finish rolling: control finish rolling speed 1.5~6m/s, start rolling temperature 820-940 ℃, finishing temperature 770-820 ℃, reduction in pass are 4-30%, and the finish rolling total deformation rate is 50~75%, makes the finish rolling plate;
G, press quenching: the finish rolling plate is carried out water-cooled, and the control speed of cooling is 5 ℃/s-25 ℃/s, and the quenching final temperature is 350-550 ℃, makes the quenching plate;
H, temper: the quenching plate is carried out temper, 620 ± 10 ℃ of tempering temperatures, tempering time in min is controlled to be 3HD+10 by the quenching panel thickness HD in mm, makes described engineering steels finished product after quality inspection, and the steel product maximum ga(u)ge is 60mm;
Described production method also comprise step I, namely to the tempering plate align, more than the cooling in heap 24hr;
Described engineering steels reaches following technical indicator: yield strength ReH 〉=420MPa, tensile strength Rm 〉=520MPa, the V-type Impact energy Ak v of thickness heart section 〉=100 joules (J) in the time of-60 ℃, Z-direction tensile property 〉=50%.
2. the production method of the engineering steels of the good and anti-lamellar tearing of the heart as claimed in claim 1 section low-temperature impact toughness, it is characterized in that: among the described step C, evacuated pressure is controlled to be 0.02-0.2kPa, vacuumizing the hold-time is 15-20min, behind feeding CaSi line or FeCa alloy wire, also comprise the operation of soft blow 〉=5 minute.
3. the production method of the engineering steels of the good and anti-lamellar tearing of the heart as claimed in claim 1 section low-temperature impact toughness, it is characterized in that: among the described step D, also comprise the loose and segregation≤B1 level of control strand, thick strand cooling in heap is 48-60hr.
4. the production method of the engineering steels of the good and anti-lamellar tearing of the heart as claimed in claim 1 section low-temperature impact toughness, it is characterized in that: in the described step e, the whole time of heating is controlled at 8-10min/cm by slab thickness.
5. the production method of the engineering steels of the good and anti-lamellar tearing of the heart as claimed in claim 1 section low-temperature impact toughness, it is characterized in that: in the described step F, the last 2-3 percentage pass reduction of finish rolling is as the criterion to guarantee plate shape.
CN201110186999XA 2011-07-05 2011-07-05 Engineering steel material with excellent core low-temperature impact toughness and lamellar tearing resisting performance and production method thereof Active CN102268615B (en)

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