CN113832414A - High-performance YP1100 MPa-level steel plate and manufacturing method thereof - Google Patents
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Abstract
A high-performance YP1100 MPa-level steel plate and a manufacturing method thereof are disclosed, wherein the steel plate component adopts a component system of high-C-extremely-low-Si-low-Mn- (Ti + Nb + B + Ca) microalloy steel as a basis, the acid-soluble Als content in the steel is properly increased, and Als/[ (% N) -0.292 (% Ti)]Not less than 22.5, controlling (% C) x CEV x (% Si) not less than 0.0213, and controlling (DI x T) not less than 415Quenching)/TTempering≤905、5.70≤[H×Au]/[(％C)×DI]Not more than 14.80, Ca treatment, Ca/S ratio of 1.00-3.00, (% Ca) × (% S)0.18)≤2.5×10‑3And the metallurgical technology control means are adopted, so that the microstructure of the finished steel plate is fine low-carbon lath martensite, the average grain size is below 20 mu m, the quenched and tempered steel plate with excellent strength-toughness/strong plasticity matching and YP1000MPa grade is obtained, and the problem of excessive quenching of the surface layer of the quenched and tempered steel plate with extremely high strength is solved.
Description
Technical Field
The invention relates to a quenched and tempered steel plate and a manufacturing technology thereof, in particular to a high-performance YP1100 MPa-level steel plate and a manufacturing method thereof.
Background
As is well known, low carbon (high strength) low alloy steel is one of the most important engineering structural materials, and is widely used in petroleum and gas pipelines, offshore platforms, shipbuilding, bridge structures, boiler vessels, building structures, automobile industry, railway transportation and machinery manufacturing. The properties of low carbon (high strength) low alloy steels depend on their chemical composition and manufacturing process, where strength, toughness, plasticity, weldability and the match between them are the most important properties of low carbon (high strength) low alloy steels, which ultimately depend on the microstructure state of the finished steel. With the continuous forward development of metallurgical technology, people put forward higher requirements on the toughness, plasticity and weldability of the ultrahigh-strength steel, namely that the steel plate has the brittle fracture resistance and plasticity instability fracture resistance under the condition of low temperature (minus 40 ℃), and simultaneously the fracture elongation and the uniform elongation reach the level of the steel plate with the tensile strength of 900 MPa. And under the conditions of relatively low alloy content, particularly precious metal content and relatively low manufacturing cost, the comprehensive mechanical property and the service performance of the steel plate are greatly improved, the alloy consumption of steel is reduced, the cost is saved, the self weight, the stability and the safety of the steel member are reduced due to ultrahigh strength and light weight, and more importantly, the cold and hot workability and the safety and the reliability in the service process of the steel member are further improved.
At present, research for developing a new generation of high-performance steel materials is highly advanced within the scope of Japan and Korean, and better microstructure matching, ultrafine metallographic microstructure and substructure (dislocation configuration, pack, block, variable) fine structure and phase angle control are obtained through alloy combination design optimization, control of a sub-microstructure fine structure and innovative manufacturing process technology, so that the ultra-thick high-strength steel plate obtains more excellent matching of strong plasticity and plastic toughness, particularly core impact toughness, weldability and environmental brittleness resistance (hydrogen induced delayed fracture resistance).
The existing high-strength steel plate with the tensile strength of more than or equal to 950MPa is mainly produced by an off-line hardening and tempering process (RQ + T), but the thickness of the steel plate is less than or equal to 60mm, the steel plate can also be produced by an on-line hardening and tempering process (namely DQ + T), and in order to obtain ultrahigh strength, the steel plate must have enough high hardenability and quenchingHardness, i.e. hardenability index DI ≥ 3.50 × finished steel sheet thickness [ DI ═ 0.311C1/2(1+0.64Si) × (1+4.10Mn) × (1+0.27Cu) × (1+0.52Ni) × (1+2.33Cr) × (1+3.14Mo) × 25.4(mm) to ensure sufficiently high strength, excellent low-temperature toughness, and uniformity of microstructure and properties in the plate thickness direction of the steel plate; therefore, a large amount of alloy elements such as C, Cr, Mo, Ni, Cu, V and the like are inevitably added into the steel, and particularly, a large amount of noble metal elements such as Cu, Ni, Mo, V and the like are added, so that the alloy cost of the steel plate is high, the carbon equivalent and the cold crack sensitivity index of the steel plate are high, and the weldability of the steel plate is seriously influenced. In addition, the surface layer (sub) of the high-carbon and high-alloy steel plate is easy to be over-quenched to form a coarse martensite structure, so that the low-temperature toughness, elongation and environmental brittleness resistance of the surface layer (near) of the steel plate are seriously deteriorated [ 1986 in power and civil engineering (japanese), vol.201, P33; iron と stainless steel 1986, Vol.72, S612; iron と stainless steel 1986, Vol.72, S614; iron と stainless steel 1985, Vol.71, S1523; iron と stainless steel 1986, Vol.72, S615; iron と stainless steel 1986, Vol.73, S1398; 1988, Vol.20, P233; 1986 in research on iron manufacture (Japanese), Vol.322, P99; CAMP-ISIJ Japanese 1989, Vol.3, P207; 1990 in NKK handbook (japanese), vol.133, P37; 1994, Vol.249, P1; 1995, Sumitomo metals (Japanese), Vol.47, P1; the Western was thought to be at , 191-192, 2008, P162.
The low elongation and low-temperature toughness are not only adverse to the cold and hot processability of the steel plate, but also have great influence on the fatigue resistance, stress concentration sensitivity resistance, crack resistance and structural stability of the steel plate; when the composite material is used on fatigue heavy-load structures such as pressure steel pipes, steel branch pipes and volute casings, thermal power turbogenerators, ocean oil production platform structures, engineering machinery, coal mine machinery and heavy loading vehicles in hydroelectric engineering, great potential safety hazards exist; therefore, when the large-scale fatigue heavy-duty steel structure adopts ultrahigh-strength steel, the 1000 MPa-grade high-strength steel is generally expected to have excellent strength and toughness, strong plasticity matching and weldability, and the elongation is ensured to be more than 14% so as to ensure the processability and the fatigue resistance of the steel plate. A great deal of prior patents and technical documents only explain how to realize the strength and low-temperature toughness of a base steel plate, improve the welding performance of the steel plate, and obtain an excellent welding heat affected zone HAZ low-temperature toughness, and do not relate to how to improve the tensile strength of the steel plate and simultaneously improve the tensile elongation and the uniformity of mechanical properties in the thickness direction of the steel plate, and further do not point out how to prevent the over-quenching of the surface (sub) layer of the steel plate [ Japanese patents Sho 63-93845, Sho 63-79921, Sho 60-258410, Sho 4-285119, Sho 4-308035, Hei 3-264614, Hei 2-250917, Hei 4-143246, US Patent Patent5798004, European Patent EP 0288054A2, Shi memorial technical lecture 159 and P79-P80 ].
Chinese patent ZL201010227961.8 discloses 960 MPa-grade quenched and tempered steel plate with excellent toughness and plasticity and a manufacturing method thereof, although the comprehensive mechanical property of the steel plate also reaches a higher level: the tensile strength is more than or equal to 980MPa, the yield strength is more than or equal to 890MPa, and the Charpy transverse impact energy (single value) at the temperature of-60 ℃ is more than or equal to 47J, but the maximum thickness of the produced steel plate by the steel plate manufacturing technology can only reach 80 mm.
The HT960 steel plate with excellent ductility and toughness and the manufacturing method thereof disclosed by the Chinese patent ZL201110071217.8 are produced by adopting a TMCP + offline tempering process, the quenching potential of alloy elements is fully exerted, the alloy content, the manufacturing period and the manufacturing cost of the steel plate are greatly reduced, the comprehensive mechanical property and the weldability of the steel plate are also improved to a large extent, but the production thickness of the steel plate is limited, the maximum thickness can only reach 70mm, and the steel plate with a thicker specification can not be produced.
The product mechanism and the manufacturing process of the steel plate with the yield strength of more than or equal to 1100MPa are not researched and developed systematically, and the batch commercial production is not realized.
Disclosure of Invention
The invention aims to provide a high-performance YP1100 MPa-level steel plate and a manufacturing method thereof, which can realize that the steel plate obtains extremely high strength, excellent low-temperature toughness and fracture elongation, has excellent toughness and ductility matching and good weldability, and has the tensile strength of more than or equal to 1200MPa, the yield strength of more than or equal to 1100MPa and the fracture elongationδ5The charpy transverse impact energy (single value) at 40 ℃ is more than or equal to 12 percent, and the welding performance is excellent (the preheating temperature is less than or equal to 200 ℃ and the welding heat input of 30kJ/cm-50kJ/cm can be borne); the invention successfully solves the mutual contradiction between the strength and the plasticity, the strength and the low-temperature toughness, the strength and the weldability of the martensite steel with extremely high strength, and eliminates the problem of over quenching of the surface (sub) surface layer of the steel plate under the condition of higher C content to cause the low plasticity and the toughness of the surface of the steel plate; the method solves the problem of excessive quenching of the surface layer of the extremely-high-strength quenched and tempered steel plate, and is particularly suitable for manufacturing important equipment such as engineering machinery, port machinery, coal mine machinery, heavy trucks, large special loading vehicles and the like.
In order to achieve the purpose, the technical scheme of the invention is as follows:
the invention adopts a component system of high-C-extremely-low Si-low Mn- (Ti + Nb + B + Ca) microalloyed steel as a basis, properly improves the content of acid-soluble Als in the steel and Als/[ (% N) -0.292 (% Ti)]Not less than 22.5, controlling (% C) x CEV x (% Si) not less than 0.0213, and controlling (DI x T) not less than 415Quenching)/TTempering≤905、5.70≤[H× Au]/[(％C)×DI]Not more than 14.80, Ca treatment, Ca/S ratio of 1.00-3.00, (% Ca) × (% S)0.18)≤2.5×10-3And the metallurgical technology control means are adopted, so that the microstructure of the finished steel plate is fine low-carbon lath martensite, the average grain size is below 20 mu m, the quenched and tempered steel plate with excellent strength-toughness/strong plasticity matching and YP1000MPa grade is obtained, and the problem of excessive quenching of the surface layer of the quenched and tempered steel plate with extremely high strength is solved.
Specifically, the high-performance YP1100 MPa-level steel plate comprises the following components in percentage by weight:
C：0.16％～0.20％，
Si：≤0.20％，
Mn：0.60％～1.00％，
P：≤0.013％，
S：≤0.0030％，
Cu：0.15％～0.40％，
Ni：1.10％～1.50％，
Cr：0.60％～1.00％，
Mo：0.35％～0.60％，
Nb：0.010％～0.030％，
Ti：0.006％～0.015％，
Als：0.030％～0.065％，
B：0.0008％～0.0016％，
N：≤0.0050％，
O：≤0.0030％，
Ca：0.0010％～0.0035％，
the balance of Fe and inevitable impurities; and the content of the elements must satisfy the following relation at the same time:
(％Als)/[(％N)-0.292(％Ti)]≥22.5；
(% C). times.CEV.times. (% Si). ltoreq. 0.0213 wherein:
CEV is the carbon equivalent of IIW,
CEV＝(％C)+(％Mn)/6+[(％Cu)+(％Ni)]/15+[(％Cr)+(％Mo)+(％V)]/15；
5.70≤[H×Au]/[(％C)×DI]≤14.80；
415≤(DI×Tquenching)/TTempering≤905；
Wherein:
DI is the index of hardenability in mm,
DI＝0.367C0.5(1+0.7Si)(1+3.33Mn)(1+0.35Cu)(1+0.36Ni)(1+2.16Cr)(1+3
Mo)(1+1.75V)(1+1.77Al)×25.4；
au is an austenite stabilization index, and the unit is,
Au＝2.54+40.53(％C+％N)+0.43(％Cu+％Ni+％Mn)-0.22(％Al)-2.64 (％P+％S)-1.26(％Cr+％Mo)-(％Si)；
h is the thickness of the steel plate, and the unit is mm;
TquenchingIs the quenching temperature, and the unit is;
TtemperingIs the quenching temperature, and the unit is;
ca treatment, the ratio of Ca/S is between 1.00 and 3.00, (% Ca) × (% S)0.18)≤2.5×10－3。
The microstructure of the quenched and tempered steel plate is fine low-carbon lath martensite, and the average grain size of the steel plate is below 20 mu m.
The tensile strength of the steel plate is more than or equal to 1200MPa, the yield strength is more than or equal to 1100MPa, and the fracture elongation rate delta5More than or equal to 12 percent and less than or equal to 47J of Charpy transverse impact energy (single value) at 40 ℃.
In the composition design of the steel plate of the invention:
c is the most effective hardening element, can effectively improve the hardness of the quenched steel plate and is the most effective alloy element for improving the quenched and tempered steel plate, so that C is of great importance for controlling the content range of C in the extremely high-strength quenched and tempered steel plate; the proper increase of the C content in the steel can not only greatly reduce the consumption of other alloy elements, but also more importantly, when the C content in the steel is lower than a critical value, the strength of the steel plate can not be effectively improved by adding more other alloy elements, which is particularly important for YP1100 MPa-grade quenched and tempered steel plates. As is well known, C has a great influence on the strength, low-temperature toughness, elongation and weldability of the wrought steel plate, and from the viewpoint of improving the intrinsic ductility and weldability of the ultra-high steel plate, it is desirable that the C content in the steel is controlled to be appropriately low; but from the aspects of hardenability, obdurability/strong plasticity matching, weldability, microstructure control and alloy cost control of the steel plate, the C content is not easy to be controlled to be too low, and particularly, the reasonable range of the C content of the YP1100MPa quenched and tempered steel plate is 0.16-0.20 percent.
Si promotes molten steel deoxidation and can improve the strength of a steel plate, but the deoxidation effect of Si is not great in molten steel deoxidized by Al; although Si can improve the strength of the quenched and tempered steel plate, Si reduces the martensite phase transformation critical cooling speed, promotes martensite phase transformation, inhibits the segmentation effect of lower bainite phase transformation on prior austenite crystal grains, coarsens packet crystal cluster size and blocks lath grain boundaries to be small-angled, seriously damages the low-temperature toughness, crack arrest characteristics, elongation and weldability of the quenched and tempered steel plate (especially an extremely high-strength quenched and tempered steel plate), particularly under the condition of large heat input welding, Si not only promotes the formation of M-A islands, but also forms the larger M-A islands, which are not uniformly distributed, and seriously damages the toughness of a welding Heat Affected Zone (HAZ), so that the Si content in the steel is controlled to be as low as possible, and considering the economy and operability of a steel-making process, the Si content is controlled to be less than or equal to 0.20%.
Mn, the most important alloying element, improves the strength of the steel sheet, expands the austenite phase region, and reduces Ar in the steel3The point temperature is increased, the position difference between the block plate structures is increased, the plastic toughness of the quenched and tempered steel plate is improved, and the low-temperature phase transformation structure martensite is promoted to form, so that the strength of the quenched and tempered steel plate is improved; however, Mn is easy to segregate in the molten steel solidification process, particularly under the condition of high C content and carbon equivalent, when the Mn content is high, not only is casting operation difficult to be caused, but also conjugate segregation phenomenon is easy to occur with elements such as C, P, S, Mo, Cr and the like, so that segregation and looseness of the central part of a casting blank are aggravated, and abnormal brittle and hard tissues are easy to form in the subsequent manufacturing and welding processes due to serious casting blank central region segregation, so that the low-temperature toughness of the quenched and tempered steel plate is low, and cracks appear on a welding joint; in addition, when the carbon equivalent is high, particularly both the carbon equivalent and the carbon equivalent are high, Mn increases the hardenability and hardenability of martensite, coarsens the size of martensite crystal clusters (namely packet size), causes over-quenching of the steel plate surface (the surface has extremely low toughness and is easy to generate environmental brittleness), promotes the formation of large martensite laths in a welding heat affected zone, and deteriorates the toughness and crack resistance and crack arrest characteristics of a welded joint; therefore, the appropriate range of the Mn content for the YP1100 MPa-grade quenched and tempered steel sheet is 0.60 to 1.00%.
P has great damage effect on the mechanical properties of the steel plate as harmful impurities in the steel, particularly on the low-temperature impact toughness, elongation, weldability and SR performance of a welded joint, and the lower the requirement is, the better the theoretical requirement is; however, considering steel-making workability and steel-making cost, P content of YP1100 MPa-grade quenched and tempered steel plate which requires low cost, excellent weldability, -40 ℃ toughness and excellent toughness/strong plasticity matching needs to be controlled to be less than or equal to 0.013%.
S has a great damage effect on the low-temperature toughness of a steel plate as harmful inclusions in steel, more importantly, the S is combined with Mn in the steel (particularly when the content of C, Mn is high), MnS inclusions are easily formed, the plasticity of MnS enables MnS to extend along the rolling direction in the hot rolling process to form MnS inclusion bands along the rolling direction, the low-temperature impact toughness, the elongation, the Z-direction performance and the weldability of the steel plate are seriously damaged, and meanwhile, the S is also a main element generating hot brittleness in the hot rolling process, and the lower the theoretical requirement is; however, considering the steel-making operability, steel-making cost and logistics smooth principle, the S content of the YP1100 MPa-grade quenched and tempered steel plate which requires low cost, excellent weldability, toughness at-40 ℃ and excellent toughness/plasticity matching needs to be controlled to be less than or equal to 0.0030 percent.
Cu is an austenite stabilizing element, and Ar can be reduced by adding Cu3The point temperature improves the hardenability of the steel plate and the atmospheric corrosion resistance of the steel plate; however, the addition amount of Cu is too much and is higher than 0.40%, so that the problems of copper brittleness, surface cracking of a casting blank and internal cracking are easily caused, and the SR performance of the welding joint of the steel plate with extremely high strength is particularly deteriorated; in the case of the YP1100 MPa-grade quenched and tempered steel sheet, the Cu addition amount is too small, less than 0.15%, and the above-described effect is small; therefore, the Cu content is preferably controlled between 0.15 percent and 0.40 percent; besides, the composite addition of Cu and Ni can reduce the copper brittleness of copper-containing steel and reduce intergranular cracking in the hot rolling process, and more importantly, both Cu and Ni are austenite stabilizing elements, and the composite addition of Cu and Ni can greatly reduce Ar3The driving force of austenite phase transformation to ferrite is improved, the structural size of the martensite packet is refined, the growth of the martensite laths in each direction is promoted, the direction difference between the martensite blocks and between the phase transformation variant is increased, and the resistance of cracks passing through the martensite blocks and the martensite laths is increased, so that the low-temperature toughness of the ultrahigh-strength steel plate is improved.
The addition of Ni has the following effects:
1) the low-temperature P-N force (crystal lattice friction force) of dislocation in the BCC (body centered cubic) crystal is reduced, the dislocation cross slip is promoted, and the low-temperature intrinsic toughness of a martensite/bainite structure of the BCC crystal structure is improved;
2) ni increases the orientation difference between the martensite/bainite block and the phase change variant, and improves the resistance of the crack to pass through the martensite/bainite block and the martensite/bainite lath;
3) ni as austenite stabilizing element to reduce Ar3Point temperature, and the structural size of martensite packet is refined, so that Ni has the function of simultaneously improving the strength, elongation and low-temperature toughness of the quenched and tempered steel plate, and is an indispensable toughening element of the extremely-high-strength quenched and tempered steel plate;
4) the addition of Ni in the steel can also reduce the copper brittleness of the copper-containing steel, reduce intergranular cracking in the hot rolling process and improve the atmospheric corrosion resistance of the steel plate.
Therefore, theoretically, the higher the Ni content in the steel is in a certain range, the better the Ni content is, but Ni is a precious alloy element, and the manufacturing cost is increased sharply due to the fact that a large amount of Ni is added; for YP1100 MPa-grade quenched and tempered steel plates, considering the balance of performance and manufacturing cost, the steel must have certain Ni content so as to ensure that the quenched and tempered steel plate with extremely high strength has enough hardenability and simultaneously ensure that the toughness/strong plasticity of the steel plate is matched and the low-temperature toughness is excellent; therefore, the reasonable range of the Ni content is 1.10-1.50%.
Cr is used as a weak carbide forming element, and the addition of Cr not only improves the hardenability of the steel plate and promotes the formation of martensite, but also has the functions of strongly increasing the meta-position difference of martensite laths (namely phase-change variants) and increasing the resistance of cracks passing through a martensite block structure, and has the functions of strongly improving the ductility and toughness and the crack resistance of the steel plate while improving the strength of the steel plate; however, when the amount of Cr added is too large, weldability of the steel sheet, particularly toughness after weld joint annealing treatment (i.e., after SR), is seriously impaired; but for YP1100 MPa-grade quenched and tempered steel plates, a certain Cr content is required to ensure that the steel plates have enough hardenability; therefore, the reasonable range of the Cr content is 0.60 to 1.00 percent.
The addition of Mo can greatly improve the hardenability of the steel plate, promote the formation of martensite, improve the tempering characteristic and tempering process window of the steel plate, and improve the matching of the strength, toughness and plasticity of the tempered steel plate; but Mo is used as a strong carbide forming element, so that the martensite formation is promoted, the size of martensite packets is increased, the formation of small-angle grain boundaries among martensite block laths is promoted, the resistance of cracks passing through a martensite block structure is reduced, and in addition, the Mo promotes the over-quenching of the surface (sub) surface layer of the ultrahigh-strength steel; therefore, Mo greatly improves the strength of the steel plate, reduces the low-temperature toughness and the elongation of the extremely-high-strength quenched and tempered steel plate and induces the over-quenching of the surface (sub) surface layer of the steel plate; when the Mo is excessively added (particularly, the content of C, Mn is high), the elongation, weldability and SR performance of a welded joint of the steel plate are seriously damaged, and the SR brittleness and production cost of the steel plate are increased; however, in the case of the YP1100 MPa-grade quenched and tempered steel sheet, a certain Mo content is required to ensure sufficient hardenability and temper softening resistance of the steel sheet. Therefore, the phase change strengthening effect of Mo and the influence on the low-temperature toughness, the elongation and the weldability of the base steel plate are comprehensively considered, and therefore, the reasonable range of the Mo content is 0.35-0.60%.
The purpose of adding trace Nb element into the steel is to perform non-recrystallization controlled rolling, refine the microstructure of the steel plate, in particular refine grains of the surface (sub) layer of the steel plate, reduce the hardenability of the surface (sub) layer of the ultra-high strength steel plate, inhibit the excessive quenching of the surface (sub) layer of the ultra-high strength steel plate and improve the matching of the low-temperature toughness and the obdurability/strong plasticity of the YP1100 MPa-level quenched and tempered steel plate; when the addition amount of Nb is less than 0.010 percent, the effect of controlling rolling and refining grains cannot be effectively exerted; when the addition amount of Nb exceeds 0.030 percent, the formation of upper bainite (Bu) and the secondary precipitation embrittlement action of Nb (C, N) are easily induced in the welding process, and the low-temperature toughness and the crack resistance and crack arrest characteristics of a welding Heat Affected Zone (HAZ) are seriously damaged; therefore, the appropriate range of the Nb content is 0.010-0.030%, the best rolling control effect is obtained, the toughness/strength and plasticity matching of the YP1100 MPa-grade quenched and tempered steel plate is realized, the surface (sub) surface layer is inhibited from being over quenched, and the toughness of HAZ (heat-resistant alloy) in welding and multi-pass welding is not damaged.
The Ti content is between 0.006 and 0.015 percent, the excessive growth of austenite grains in the processes of heating, rolling and quenching and tempering heat treatment of a plate blank is inhibited, the low-temperature toughness of the steel plate is improved, and more importantly, the growth of HAZ grains in the welding process is inhibited, and the HAZ toughness is improved; in addition, Ti has the function of fixing N, eliminates free N in steel and ensures that B element exists in a solid solution B form; however, when the Ti content exceeds 0.015%, excess Ti precipitates as TiC coherent on martensite laths and at the grain boundaries under the condition of high acid-soluble aluminum content, and the microstructure of the steel sheet is seriously embrittled.
Als in steel can fix free [ N ] in steel]Removal of weld Heat Affected Zone (HAZ) free [ N ]]Besides improving the low-temperature toughness of the welded HAZ, it is more important to ensure that the steel has certain solid solution [ B ]]Improving the hardenability of the steel plate; therefore, the lower limit of Als is controlled to be 0.030%; however, excessive addition of Als to the steel not only causes castingCasting is difficult (clogging of the nozzle) and a large amount of dispersed needle-like Al is formed in the steel2O3Inclusions impair the integrity of the steel sheet, low-temperature toughness and weldability, and therefore the upper limit of Als is controlled to 0.065%, and therefore, the preferable range of the Als content is 0.030% to 0.065%.
The content of B is controlled between 0.0008 percent and 0.0016 percent, thereby ensuring the hardenability of the steel plate and not damaging the weldability, HAZ toughness and surface quality of the plate blank.
In order to ensure the existence of solid solution [ B ] in the steel plate and prevent a great amount of coarse AlN from precipitating along the prior austenite grain boundary and damaging the transverse impact toughness and plasticity of the steel plate, the content of N in the steel is less than or equal to 0.0050 percent.
In order to ensure the low-temperature toughness and the plastic toughness of the YP not less than 1100 MPa-grade quenched and tempered steel plate, the inclusion in the steel must be reduced, wherein the aluminum oxide inclusion harm is the largest, and therefore, the O content in the steel is not more than 0.0030 percent.
Ca treatment is carried out on the steel, on one hand, the molten steel can be further purified, and on the other hand, the sulfide in the steel is denatured to be nondeformable, stable and fine spherical sulfide, the hot brittleness of S is inhibited, the low-temperature toughness, the elongation and the Z-direction performance of the steel plate are improved, and the anisotropy and the weldability of the toughness of the steel plate are improved; in addition, Ca treatment is adopted, so that the pouring of the high-acid-content molten aluminum is improved; the addition amount of Ca depends on the content of S in steel, the addition amount of Ca is too low, and the treatment effect is not great; the Ca is added in an excessive amount, the formed Ca (O, S) size is too large, the brittleness is increased, the Ca can be used as a fracture crack starting point, the low-temperature toughness and the elongation of the steel and the weldability of a steel plate are reduced, and meanwhile, the purity of the steel and the pollution to molten steel are reduced. The Ca content is generally controlled in terms of ESSP (wt% Ca) [1-1.24 (wt% O) ]/1.25 (wt% S), where ESSP is a sulfide inclusion shape control index, and preferably ranges from 0.80 to 4.00, and therefore, a suitable range of the Ca content is 0.0010% to 0.0035%.
The following are specifically controlled in the composition design of the invention:
(% Als)/[ (% N) -0.292 (% Ti) ] > 22.5, eliminating steel mid and weld heat affected zone free [ N ]:
1) ensuring that the steel contains enough solid solution [ B ], keeping the steel plate to have enough hardenability and stable hardenability, and realizing the strength, low-temperature toughness and toughness/plasticity matching of the YP1100 MPa-grade quenched and tempered steel plate;
2) the content of free [ N ] in a welding heat affected zone is reduced, and the low-temperature toughness and the crack resistance and crack resistance of the welding heat affected zone are improved (a martensite structure is extremely sensitive to the free [ N ], and the embrittlement effect of the free [ N ] on the martensite structure is more than that of a bainite structure and more than that of a ferrite and pearlite structure).
(％C)×CEV×(％Si)≤0.0213：
1) The martensite phase transformation critical cooling speed is increased, the martensite packet crystal group size and the phase difference between variants are refined, the frequency of a large-angle crystal boundary of a martensite lath interface is increased, the resistance of a crack penetrating through a block substructure is increased, the toughness/strong plasticity matching of the martensite quenched and tempered steel is improved, and the low-temperature toughness, crack resistance and crack arrest characteristics of the martensite steel are improved;
2) the formation of massive M-A islands is inhibited, the size and the number of the M-A islands are reduced, and the crack resistance and the crack arrest characteristics and the environmental brittleness resistance of the martensitic steel are improved;
3) the excessive quenching of the surface of the martensitic steel is inhibited, and the ductility, toughness and environmental brittleness resistance of the surface of the martensitic steel are improved;
4) the degree of conjugate segregation in the solidification process of the molten steel with high carbon and high alloy content is reduced, the integrity and homogeneity of the internal quality of the steel plate are improved, and the UT qualification rate and low-temperature toughness of the steel plate are improved;
this is one of the key core technologies of the present invention.
5.70≤[H×Au]/[(％C)×DI]≤14.80：
1) The martensite steel refines the size of the packet crystal group, improves the frequency of a large-angle grain boundary of a martensite lath (namely a variable) interface, improves the resistance of a crack penetrating through the packet crystal group interface and a block substructure, improves the toughness/strong plasticity matching of the martensite quenched and tempered steel, and improves the low-temperature toughness and crack resistance and crack arrest characteristics of the martensite steel;
2) the optimal matching of the hardenability and the hardenability of the martensitic steel and the thickness of the steel plate is realized, so that the martensitic steel has extremely high strength, excellent low-temperature toughness and fracture elongation, and simultaneously, the steel plate also has excellent obdurability/plastic toughness matching and good weldability, thereby successfully solving the mutual contradiction between the strength and plasticity, the strength and the low-temperature toughness (crack resistance and crack arrest characteristic), the strength and the weldability of the martensitic steel and the sensitivity to environmental brittleness, and eliminating the sensitivity of the low plasticity, the toughness and the environmental brittleness of the surface of the steel plate caused by the over-quenching of the surface (sub) layer of the steel plate under the condition of high C content;
this is one of the key core technologies of the present invention.
415≤(DI×TQuenching)/TTemperingNot more than 905: the matching of the thickness and the hardenability of the steel plate with the quenching and tempering heat treatment process is realized; the martensite steel has extremely high strength, excellent low-temperature toughness and fracture elongation, and simultaneously the steel plate has excellent toughness/ductility matching.
Ca treatment, the ratio of Ca/S is 1.00-3.00, and ((% Ca) × (% S)0.18)≤2.5×10－3: the low-temperature toughness, the toughness/strong plasticity matching and the weldability of the YP-grade quenched and tempered steel plate with the pressure of more than or equal to 1100MPa are improved, and the environmental brittleness (particularly delayed hydrogen-induced cracking at the central part of the plate thickness) of the YP-grade quenched and tempered steel plate with the pressure of more than or equal to 1100MPa is inhibited.
The invention relates to a method for manufacturing a high-performance YP1100 MPa-level steel plate, which comprises the following steps:
1) smelting and casting
Smelting and casting the components into a plate blank, wherein the pouring temperature of a tundish is 1515-1545 ℃, the pulling speed is 0.8-1.2 m/min, and the fluctuation of the liquid level of a crystallizer is less than or equal to 5 mm;
2) rolling of
The first stage is recrystallization rolling, and the heating temperature of the plate blank is controlled between 1130 ℃ and 1180 ℃; the rolling pass reduction rate is more than or equal to 5 percent, and the final rolling temperature is more than or equal to 960 ℃;
rolling in the second stage by using non-recrystallization control, wherein the rolling start temperature of controlled rolling is less than or equal to 850 ℃, the rolling reduction of the average rolling pass is more than or equal to 8 percent, the cumulative rolling reduction is more than or equal to 50 percent, and the final rolling temperature is 750-770 ℃;
3) cooling and heat preservation
After rolling is finished, carrying out stack cooling for at least 24 hours, and then naturally cooling to room temperature;
4) thermal treatment, quenching and tempering process, namely quenching and tempering process
Quenching, wherein the quenching temperature is 880-930 ℃, the quenching holding time is more than or equal to 15min, and the quenching holding time is the heat preservation time for starting timing when the central temperature of the steel plate reaches the quenching target temperature;
tempering, wherein the tempering temperature of the steel plate is 220-300 ℃, and the tempering retention time is more than or equal to 45 min; and the tempering retention time is the heat preservation time when the central temperature of the steel plate reaches the tempering target temperature and the steel plate is naturally air-cooled to the room temperature after the tempering.
In the manufacturing method of the present invention:
according to the component system of the steel and the requirements of the strength, the plasticity and the low-temperature toughness of the steel plate, the design scheme of the manufacturing process is as follows: continuous casting is adopted, the pouring temperature of a tundish is controlled to be 1515-1545 ℃, the pulling speed is controlled to be 0.8-1.2 m/min, and the fluctuation of the liquid level of a crystallizer is less than or equal to 5 mm.
The first stage rolling is recrystallization rolling, in order to ensure that Nb is completely dissolved in solution in the heating and rolling processes, the heating temperature of the plate blank is controlled between 1130 ℃ and 1180 ℃, the pass reduction rate is more than or equal to 5 percent, and the final rolling temperature is more than or equal to 960 ℃.
In the second stage, rolling is controlled by a non-recrystallization region, the rolling start temperature is controlled to be less than or equal to 850 ℃, the rolling average pass reduction rate is greater than or equal to 8%, the cumulative reduction rate is greater than or equal to 50%, the final rolling temperature is 750-770 ℃, and steel plate grains before heat treatment are refined and adjusted, so that a foundation is laid for finally obtaining a fine and uniform martensite structure.
After rolling, the steel plate is cooled in heaps for at least 24 hours, UT flaw detection is carried out, and then natural air cooling is carried out to the room temperature.
The heat treatment process adopts an off-line (quenching and tempering) process, namely a quenching and tempering process to produce the steel plate according to the hardenability indexes DI and Ac of the steel plate3And (3) adjusting the quenching temperature of the steel plate according to the point temperature and the thickness to realize the matching between the hardenability of the steel plate and the quenching temperature and obtain a fine and uniform low-carbon martensite structure so as to obtain all performance requirements of the steel plate, wherein the quenching temperature is 880-930 ℃, the quenching holding time is not less than 15min, and the quenching holding time is the heat preservation time for starting timing when the central temperature of the steel plate reaches the quenching target temperature.
According to the steel plate hardenability index DI and the steel plate thickness, the steel plate tempering temperature is adjusted to realize the matching between the steel plate hardenability and the tempering temperature and ensure that the steel plate obtains excellent strength and toughness/strong plasticity matching; the tempering temperature (plate temperature) of the steel plate is 220-300 ℃, the tempering retention time is more than or equal to 45min, and the tempering retention time is the heat preservation time when the central temperature of the steel plate reaches the tempering target temperature; and naturally cooling the steel plate to room temperature after tempering.
The invention has the beneficial effects that:
the invention designs the components, utilizes the alloy element combination and Ni in the ultra-high strength steel plate, adopts the controlled rolling, rapid quenching and ultra-low temperature tempering heat treatment process in the manufacturing process, fully exerts the hardenability effect of C and the hardenability effect of B, realizes that the cheap alloy Mn and Cr partially replace the precious alloys Ni, Mo, V and the like, greatly reduces the total alloy consumption of the steel plate, obtains the quenched and tempered steel plate with relatively low cost and YP1100MPa grade, has excellent matching of low temperature toughness and obdurability of the steel plate, successfully solves the mutual contradiction between the strength and plasticity of martensitic steel, the strength and low temperature toughness (crack resistance and crack arrest property), the strength and weldability and environmental brittleness sensitivity, eliminates the problems of low plasticity, toughness and environmental brittleness of the surface of the steel plate caused by over quenching of the surface layer (sub) of the steel plate under the condition of higher C content, the safety and stability of the large heavy steel structure are improved; the good weldability saves the manufacturing cost of the ultrahigh-strength steel plate member of the user, shortens the manufacturing time of the steel member of the user and creates great value for the user, so the steel plate is a product with high added value and environmental protection.
The invention adopts low-cost alloy combination design (alloy design technical means such as high carbon, high Cr, low Mn, low Mo, proper addition of Cu and Ni for alloying, Nb + Ti + Ca microalloying treatment and the like), and the manufacturing process adopts special controlled rolling and quenching and tempering processes, thereby not only fully playing the potential of hardenability and hardenability of alloy elements, but also effectively refining steel plate packets (crystal clusters), increasing the large-angle grain boundary density between martensite laths (varients), effectively refining martensite substructures, and having relatively less content (particularly Mo element and the like) under the content of precious alloys; the method not only further reduces the manufacturing cost, but also improves the weldability of the steel plate, and particularly for extremely high-strength quenched and tempered steel plates, the welding cold crack sensitivity is greatly reduced, the welding preheating, the post-heating temperature are reduced, the proper welding heat input range is wider, and the processing and manufacturing cost of a user is correspondingly reduced.
Drawings
FIG. 1 is a photograph of the microstructure (1/4 thickness) of the steel of example 4 of the present invention.
Detailed Description
The invention is further illustrated by the following examples and figures.
The composition examples of the steel of the present invention are shown in Table 1, the manufacturing process of the steel of the present invention are shown in tables 2 to 4, and Table 5 shows the properties of the steel sheet.
As can be seen from the microstructure in FIG. 1, the microstructure of the steel sheet is fine low-carbon tempered martensite, and the average grain size of the steel sheet is below 20 μm.
The YP1100 MPa-level quenched and tempered steel plate is mainly suitable for manufacturing important equipment such as engineering machinery, mining machinery, port machinery, coal mine machinery, heavy trucks, large special loading vehicles and the like, is a key material for important national economic construction, and is a strategic base material for realizing the strong country of the national 2025 manufacturing industry; more importantly, the YP1100 MPa-grade quenched and tempered steel plate can be used for national defense and military projects and is limited by western countries, and is required to be used for specified equipment manufacturing projects.
Claims (6)
1. A high-performance YP1100 MPa-level steel plate comprises the following components in percentage by weight:
C：0.16％～0.20％，
Si：≤0.20％，
Mn：0.60％～1.00％，
P：≤0.013％，
S：≤0.0030％，
Cu：0.15％～0.40％，
Ni：1.10％～1.50％，
Cr：0.60％～1.00％，
Mo：0.35％～0.60％，
Nb：0.010％～0.030％，
Ti：0.006％～0.015％，
Als：0.030％～0.065％，
B：0.0008％～0.0016％，
N：≤0.0050％，
O：≤0.0030％，
Ca：0.0010％～0.0035％，
the balance of Fe and inevitable impurities; and the content of the elements must satisfy the following relation at the same time:
(％Als)/[(％N)-0.292(％Ti)]≥22.5；
(% C). times.CEV.times. (% Si). ltoreq. 0.0213 wherein:
CEV is the carbon equivalent of IIW,
CEV＝(％C)+(％Mn)/6+[(％Cu)+(％Ni)]/15+[(％Cr)+(％Mo)+(％V)]/15；
5.70≤[H×Au]/[(％C)×DI]≤14.80；
415≤(DI×Tquenching)/TTempering≤905；
Wherein:
DI is the index of hardenability in mm,
DI＝0.367C0.5(1+0.7Si)(1+3.33Mn)(1+0.35Cu)(1+0.36Ni)(1+2.16Cr)(1+3Mo)(1+1.75V)(1+1.77Al)×25.4；
au is an austenite stabilization index, and the unit is,
Au＝2.54+40.53(％C+％N)+0.43(％Cu+％Ni+％Mn)-0.22(％Al)-2.64(％P+％S)-1.26(％Cr+％Mo)-(％Si)；
h is the thickness of the steel plate, and the unit is mm;
TquenchingIs the quenching temperature, and the unit is;
TtemperingIs the quenching temperature, and the unit is;
ca treatment, the ratio of Ca/S is 1.00-3.00, and ((% Ca) × (% S)0.18)≤2.5×10－3。
2. The high-performance YP1100MPa grade steel sheet according to claim 1, wherein the microstructure of the steel sheet is fine low carbon lath martensite, and the average grain size of the steel sheet is 20 μm or less.
3. The high-performance YP1100 MPa-grade steel sheet according to claim 1 or 2, characterized in that it has a tensile strength of 1200MPa or more, a yield strength of 1100MPa or more, and an elongation at break δ5More than or equal to 12 percent and less than or equal to 47J of Charpy transverse impact energy (single value) at 40 ℃.
4. The method for producing a high-performance YP1100 MPa-grade steel sheet according to claim 1, 2 or 3, comprising the steps of:
1) smelting and casting
Smelting and casting the slab according to the components of claim 1, wherein the pouring temperature of the tundish is 1515-1545 ℃, the casting speed is 0.8-1.2 m/min, and the fluctuation of the liquid level of the crystallizer is less than or equal to 5 mm;
2) rolling of
The first stage is recrystallization rolling, and the heating temperature of the plate blank is controlled between 1130 ℃ and 1180 ℃; the rolling pass reduction rate is more than or equal to 5 percent, and the final rolling temperature is more than or equal to 960 ℃;
rolling in the second stage by using non-recrystallization control, wherein the rolling start temperature of controlled rolling is less than or equal to 850 ℃, the rolling average pass reduction rate is more than or equal to 8 percent, the cumulative reduction rate is more than or equal to 50 percent, and the final rolling temperature is 750-770 ℃;
3) cooling and heat preservation
After rolling is finished, carrying out stack cooling for at least 24 hours, and then naturally cooling to room temperature;
4) thermal treatment, quenching and tempering process, namely quenching and tempering process
Quenching, wherein the quenching temperature is 880-930 ℃, the quenching holding time is more than or equal to 15min, and the quenching holding time is the heat preservation time for starting timing when the central temperature of the steel plate reaches the quenching target temperature;
tempering, wherein the tempering temperature of the steel plate is 220-300 ℃, the tempering retention time is more than or equal to 45min, and the tempering retention time is the heat preservation time when the central temperature of the steel plate reaches the tempering target temperature; and naturally cooling the steel plate to room temperature after tempering.
5. The method for producing a high-performance YP1100 MPa-grade steel sheet according to claim 4, wherein the microstructure of the steel sheet is fine low-carbon lath martensite, and the average grain size of the steel sheet is 20 μm or less.
6. The method for producing a high-performance YP1100 MPa-grade steel sheet according to claim 4 or 5, wherein the steel sheet has a tensile strength of 1200MPa or more, a yield strength of 1100MPa or more, and an elongation at break δ5More than or equal to 12 percent and less than or equal to 47J of Charpy transverse impact energy (single value) at 40 ℃.
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| CN102747303A (en) * | 2012-06-29 | 2012-10-24 | 宝山钢铁股份有限公司 | High-strength steel sheet with yield strength of 1100MPa and manufacturing method thereof |
| CN104513936A (en) * | 2014-12-19 | 2015-04-15 | 宝山钢铁股份有限公司 | Hardened and tempered high-strength steel with yield strength of 1100MPa and production method thereof |
| CN108559917A (en) * | 2018-06-04 | 2018-09-21 | 南京钢铁股份有限公司 | A kind of yield strength 1100MPa grades of Ultra-fine Grained high strength steel plates and its manufacturing method |
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| CN102747303A (en) * | 2012-06-29 | 2012-10-24 | 宝山钢铁股份有限公司 | High-strength steel sheet with yield strength of 1100MPa and manufacturing method thereof |
| CN104513936A (en) * | 2014-12-19 | 2015-04-15 | 宝山钢铁股份有限公司 | Hardened and tempered high-strength steel with yield strength of 1100MPa and production method thereof |
| CN108559917A (en) * | 2018-06-04 | 2018-09-21 | 南京钢铁股份有限公司 | A kind of yield strength 1100MPa grades of Ultra-fine Grained high strength steel plates and its manufacturing method |
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