CN110157864A - A kind of 1300MPa grades of low hydrogen-induced delayed cracking sensibility hot forming steel and production method - Google Patents

A kind of 1300MPa grades of low hydrogen-induced delayed cracking sensibility hot forming steel and production method Download PDF

Info

Publication number
CN110157864A
CN110157864A CN201910423899.0A CN201910423899A CN110157864A CN 110157864 A CN110157864 A CN 110157864A CN 201910423899 A CN201910423899 A CN 201910423899A CN 110157864 A CN110157864 A CN 110157864A
Authority
CN
China
Prior art keywords
temperature
steel
hot forming
low hydrogen
forming steel
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Pending
Application number
CN201910423899.0A
Other languages
Chinese (zh)
Inventor
陈勇
葛锐
祝洪川
余立
周少云
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Wuhan Iron and Steel Co Ltd
Original Assignee
Wuhan Iron and Steel Co Ltd
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by Wuhan Iron and Steel Co Ltd filed Critical Wuhan Iron and Steel Co Ltd
Priority to CN201910423899.0A priority Critical patent/CN110157864A/en
Publication of CN110157864A publication Critical patent/CN110157864A/en
Pending legal-status Critical Current

Links

Classifications

    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21C—MANUFACTURE OF METAL SHEETS, WIRE, RODS, TUBES OR PROFILES, OTHERWISE THAN BY ROLLING; AUXILIARY OPERATIONS USED IN CONNECTION WITH METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL
    • B21C37/00—Manufacture of metal sheets, bars, wire, tubes or like semi-manufactured products, not otherwise provided for; Manufacture of tubes of special shape
    • B21C37/02—Manufacture of metal sheets, bars, wire, tubes or like semi-manufactured products, not otherwise provided for; Manufacture of tubes of special shape of sheets
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/26—Methods of annealing
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/74—Methods of treatment in inert gas, controlled atmosphere, vacuum or pulverulent material
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/002—Heat treatment of ferrous alloys containing Cr
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/008—Heat treatment of ferrous alloys containing Si
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/005—Modifying the physical properties by deformation combined with, or followed by, heat treatment of ferrous alloys
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/52—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length
    • C21D9/54—Furnaces for treating strips or wire
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C33/00—Making ferrous alloys
    • C22C33/04—Making ferrous alloys by melting
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese

Abstract

A kind of 1300MPa grades of low hydrogen-induced delayed cracking sensibility hot forming steel, its component and wt% are as follows: C:0.14~0.18%, Si:1.10~1.25%, Mn:2.0~2.4%, P≤O.Ol%, S≤0.008%, A1s:0.065~0.090%, Cr:0.19~0.24%, Ti:0.026~0.035%, Nb:0.026~0.035%, B:0.002~0.005%, N≤0.005%；Production technology: desulfurizing iron and converter smelting；Slab heating；Roughing；Finish rolling；Section cooling；It batches；The cold rolling after conventional cold pickling；Annealing；It is smooth；Through conventional finishing and shearing after under the protective atmosphere of pure nitrogen gas austenitizing；It is hot press-formed；Quenching；It is stand-by after lonneal.The present invention not only yield strength Rp0.2: 850~1000MPa, tensile strength Rm >=1300MPa, elongation percentage A50mmUnder the premise of >=7%, make Hydrogen Embrittlement I≤45%.Body of a motor car weight, and the safety of energy effective protection driver and passenger can not only be mitigated.

Description

A kind of 1300MPa grades of low hydrogen-induced delayed cracking sensibility hot forming steel and production method
Technical field
The present invention relates to a kind of mechanical engineering steel and production method, definitely belong to a kind of automobile hot forming steel and life Production method, and it is suitable for product thickness in 0.8~2mm.
Background technique
With the fast development of automobile industry, the Main way of lightweight and safety as development of automobile industry.It uses Hot forming steel is the current raising maximally efficient measure of Crash Safety Design of Vehicles and light-weighted important channel.Application at present Most is low-carbon Mn-B system steel plate, its tissue becomes uniform martensite after quenching, and intensity reaches 1300MPa grades, applies in A The positions such as column, B column, front and back bumper bar, hinge stiffening plate, door anti-collision joist, middle channel.
However, the Delayed Cracking problem of steel also occurs therewith as intensity improves, becomes and restrict super-high strength steel and apply and hair One significant problem of exhibition.Delayed Cracking is material under the action of static stress, and brittleness occurs suddenly after a certain period of time for process A kind of phenomenon destroyed, it is the result to interact between material-environment-stress.Numerous studies have demonstrated that steel is stagnant It is a kind of form that hydrogen causes Material degradation caused by cracking is the hydrogen in material and material military service environment afterwards, it is especially big to intensity In the super-high strength steel of 1000MPa, hydrogen-induced delayed fracture sensibility is more significant.Delayed Cracking is usually born in material outer Add stress level to occur suddenly when being substantially less than its yield strength, there is unpredictability, often lead to more serious destruction And consequence, therefore super-high strength steel Delayed Cracking has become automotive light weight technology and must solve the problems, such as.
The concrete measure taken both at home and abroad at present is following several.(1) crystal grain is refined, by the way that the members such as Al, Ti, Nb, V are added Element generates the carbonitride of disperse educt to refine original austenite grain, can also improve toughness while improving intensity. (2) cyrystal boundary segregation is reduced, the content of the impurity elements such as phosphorus, sulphur is reduced, crystal boundary binding force is improved, delays sprouting for delayed fracture crackle It is raw, so as to improve the resistance for delayed fracture of high strength steel.(3) resistance to tempering is improved, the strong member of anti-temper softening ability is added Plain such as molybdenum, vanadium, so as to improve steel belt roof bolt temperature, make overall grain-boundary strength in the case where keeping intensity constant It is improved；(4) it improves notch toughness: by adjusting alloying element, the methods of such as adding nickel content, reduces manganese content, it can be with Higher notch toughness is obtained, the generation of delayed fracture is inhibited.(5) hydrogen amount of steel surface intrusion is reduced.(6) make intrusion hydrogen without Suitable micro alloying element V, Ti, Nb etc. is added in evilization, and forming tiny carbonitride can be used as the trap of hydrogen, inhibits hydrogen Diffusion, be uniformly distributed the hydrogen in steel.Lower bainite tissue and appropriate martensite, retained austenite are obtained by isothermal processes Heterogeneous structure, realized using the high intensity and bainite of martensitic structure, the good delayed fracture drag of austenite structure Good resistance for delayed fracture under high-intensitive obtains crystal boundary carbonization by the methods of thermomechanical treatment, magnetic field, induction heat treatment The less fine martensitic structure of object, it is also possible to obtain good resistance for delayed fracture.
Through retrieving: most basic mechanical performances for only focusing on hot forming steel in contemporary literature, and rarely about Research of the delayed fracture to the harmfulness of hot forming steel.
China Patent Publication No. is the document of 101275200A, " a kind of thermal forming martensite steel " is disclosed, to geneva The delayed fracture problem of body steel is more paid close attention to, and proposes that steel suitably can be improved containing a certain amount of austenite in hot forming steel Delayed fracture performance.However the place that comes with some shortcomings in the document.The document is to develop a kind of thin thickness part use first Steel but without carrying out mechanical test using sheet metal specimens, but uses pole sample to carry out tension test, bar samples and plate examination Sample due to different in its cross sectional shape, the stress-strain state being subject to during stretching be it is different, use rodlike examination Sample replace thin plate sample be it is inappropriate, this result has no directive significance to practical application.Secondly, using the rodlike examination of φ 12 Sample substitution thin plate sample carries out mechanical test and shows that these test steel are not rolled sufficiently, and final rolling thickness is not less than 12mm, this differs huge with actual use lamella thickness, it can thus be appreciated that the inventor does not fully realize the operation of rolling to material The influence of mechanical property.Third is that its heating cycle for testing hydrogen induced cracking (HIC) tensile sample is 900-950 DEG C of x30min, and practical The plate heating cycle of forming is 900-950 DEG C of x5min, and the two technique difference is huge, passes through the property for the steel that such method obtains Can there can be larger difference, the result obtained lacks persuasion.
Summary of the invention
The technical problem to be solved by the present invention is existing 1300MPa hot forming steel, hydrogen-induced delayed fracture sensibility compared with Greatly, there is cracking risk when in use, influence the deficiency of service life, one kind is provided and is guaranteeing to use mechanical property are as follows: surrender Intensity Rp0.2: 850~1000MPa, tensile strength Rm >=1300MPa, elongation percentage A50mmUnder the premise of >=7%, keep hydrogen embrittlement quick The hot forming steel and production method of perceptual I≤45%.
Realize the measure of above-mentioned purpose:
A kind of 1300MPa grades of low hydrogen-induced delayed cracking sensibility hot forming steel, component and weight percent content are as follows: C: 0.14~0.18%, Si:1.10~1.25%, Mn:2.0~2.4%, P≤O.Ol%, S≤0.008%, A1s:0.065~ 0.090%, Cr:0.19~0.24%, Ti:0.026~0.035%, Nb:0.026~0.035%, B:0.002~0.005%, N≤0.005%, Yu Wei Fe and inevitable impurity.
Preferably: the weight percent content of Mn is 2.12~2.35%.
Preferably: the weight percent content of Ti is 0.029~0.035%.
Preferably: the weight percent content of Nb is 0.029~0.035%.
Preferably: the weight percent content of A1s is 0.072~0.090%.
A kind of method for producing 1300MPa grades of low hydrogen-induced delayed cracking sensibility hot forming steel, step:
1) desulfurizing iron and converter smelting, control the C of smelting endpoint 0.05~O.06%, P≤0.008%, S≤ 0.002%, N≤0.004%, tapping temperature is at 1700~1780 DEG C；
2) be casting continuously to form base and slab heated: heating and temperature control at 1280~1320 DEG C, heating rate control 350~ 400 DEG C/h；
3) carry out roughing: control roughing outlet temperature is at 1050~1100 DEG C；
4) finish rolling is carried out, controls the finishing temperature of finish rolling at 850~910 DEG C；
5) section cooling is carried out, in the case where cooling velocity is 10~15 DEG C/sec, is cooled to 640~680 DEG C；
6) it is batched, is batched when temperature is down to 630~660 DEG C；
7) cold rolling is carried out after conventional cold pickling, and controls cold rolling total reduction 50~74%；
8) it anneals, annealing temperature is controlled at 750~810 DEG C, and controls temperature drop speed at 5~8 DEG C/sec；
9) progress is smooth, controls smooth elongation percentage 1.1~1.3%；
10) austenitizing, heating and temperature control are carried out under the protective atmosphere of pure nitrogen gas after conventional finishing and shearing It is kept the temperature at 850~900 DEG C, and at this temperature, soaking time was controlled at 5~8 minutes；
11) progress is hot press-formed, and controls heating and come out of the stove to the merging mold time and be no more than 6 minutes, forming temperature control It makes at 780~820 DEG C,
12) it is quenched, controls its cooling velocity at 30~50 DEG C/sec；
13) stand-by after lonneal, tempering temperature is controlled at 200~250 DEG C, and is kept for 10~20 seconds at this temperature Clock.The effect and mechanism of each element and main technique of the present invention
C: carbon is strong solution strengthening element, to being played a decisive role for superhigh intensity, group of the carbon content to final products Knitting form and performance has larger impact, but content is too high, easily formed in the cooling procedure after finish rolling a large amount of pearlite or Bainite, martensite, content is higher, and intensity is higher, so that plasticity be caused to reduce, the blanking before being formed is difficult.So Under the premise of guaranteeing heat treatment reinforcement, carbon content is not easy excessively high.Therefore its content is limited to 0.14~0.18% range.
Si: silicon has stronger solid solution strengthening effect, and the intensity of steel can be improved, meanwhile, silicon can improve the harden ability of steel, have and subtract Few effect of the austenite to volume change when martensite transfor mation, to effectively control the generation of hardening flaw: in lonneal Carbon diffusion can be hindered, the speed of martensite decomposition and carbide agglomeration is delayed, keeps steel hardness decline in tempering slower, Significantly improve steel belt roof bolt stability and intensity.So its content is limited to 1.10~1.25% ranges.
Mn: manganese plays solution strengthening effect, while can remove the FeO in steel, significantly improves the quality of steel.It can also be with sulfide Dystectic MnS is generated, in hot-working, MnS has enough plasticity, and steel is made not generate hot-short phenomenon, mitigates the harmful of sulphur and makees With improving the hot-working character of steel.Manganese can reduce phase driving force, move to right C curve, improve the harden ability of steel, expand γ phase Area, it can reduce the Ms point of steel, therefore can guarantee and obtain martensite under suitable cooling velocity, and can increase retained austenite Stability.So its content is limited to 2.0~2.4% ranges, preferably content is 2.12~2.35%.
Cr: chromium can reduce phase driving force, and the forming core of carbide is grown up when also reducing phase transformation, so improving the through hardening of steel Property.In addition, chromium can improve steel belt roof bolt stability.So its content is limited to 0.19~0.24% range.
B: boron is strong raising harden ability element, and micro boron element, which is added, in steel can significantly improve the harden ability of steel.But It is its content lower than 0.002%, or is higher than 0.005%, it is unobvious to the effect for improving harden ability.So to consider production Its content is limited to 0.002~0.005% range by reality and harden ability effect.
Al: it plays deoxidation in steel, and should ensure that in steel has a certain amount of dissolved aluminum, otherwise cannot play its effect, Suitable aluminium is added in steel simultaneously can eliminate nitrogen in steel, oxygen atom to the adverse effect of performance, and hydrogen can also be reduced by adding Al Diffusion coefficient in steel.Therefore Als content is limited to O.065~0.90% range, preferably content 0.072~ 0.090%.
P: phosphorus is the harmful element in steel, Yi Yinqi center segregation of casting blank.In subsequent hot continuous rolling heating process easily partially Gather crystal boundary, significantly increases the brittleness of steel.The performance of steel is not influenced based on cost consideration and simultaneously, the control of its content is existed 0.01% or less.
S: sulphur is very harmful element.Sulphur in steel often exists with the oxide morphology of manganese, this sulphide inculsion meeting Deteriorate the toughness of steel, and cause the anisotropy of performance, therefore, sulfur content in steel need to be controlled more lower better.Based on to system This considerations of is caused, by sulfur content control in steel below 0.008%.
N: nitrogen can form titanium nitride in the steel for adding titanium, and this second phase being precipitated at high temperature is conducive to strengthen matrix, But nitrogen content, higher than 0.005%, the solubility product of nitrogen and titanium is higher, just will form the coarse nitridation of particle in steel at high temperature Titanium, the serious plasticity and toughness for damaging steel；In addition, higher nitrogen content can be such that micro alloying element needed for stablizing nitrogen contains Amount increases, to increase cost.Therefore by the control of its content below 0.005%.
Ti: titanium is strong C, N compound formation element, and the purpose being added in steel is the N element in fixed steel, but excessive Ti The hardness and strength of martensite after test steel quenches can be reduced in conjunction with C.In addition, the addition of titanium has one to the harden ability of steel Fixed contribution.So its content is limited to 0.026~0.035% range, preferably content is 0.029~0.035%.
Nb: niobium is also strong C, N compound formation element, can play the role of fining austenite grains, be added on a small quantity in steel Niobium can form the carbon of a certain amount of niobium, nitride, so that Austenite Grain Growth is hindered, therefore, quenched martensite Slat dimension is smaller, greatly improves the intensity of steel；In addition the carbon of niobium, nitride are good hydrogen traps, effectively hydrogen can be inhibited to exist Diffusion in steel is conducive to the anti-hydrogen-induced delayed fracture performance for promoting steel.Therefore its content is controlled 0.026~0.035% Between, preferably content is 0.029~0.035%.
Why the present invention controls coiling temperature at 630~660 DEG C, is that Nb, Ti in steel etc. are precipitated due to coiling temperature Object is very crucial, and when batching the Carbonitride Precipitation for being conducive to Nb, Ti in higher temperature, this is conducive to the delayed fracture for promoting steel Performance, and temperature is excessively high, and excessive iron scale can be generated in belt steel surface, is unfavorable for the surface quality of product, thus set It is proper at 630~660 DEG C.
Compared with prior art, the present invention not only yield strength Rp0.2: 850~1000MPa, tensile strength Rm >= 1300MPa, elongation percentage A50mmUnder the premise of >=7%, make Hydrogen Embrittlement I≤45%.It is applied to automobile upper body and gets off Structural member and safety member are made on body, can not only mitigate body of a motor car weight, and be capable of the peace of effective protection driver and passenger Entirely.
Detailed description of the invention
Fig. 1 is metallurgical structure figure of the invention.
Specific embodiment
The present invention is described in detail below:
Table 1 is the chemical component comparative example of various embodiments of the present invention and comparative example；
Table 2 is the main technique production number comparative example of various embodiments of the present invention and comparative example；
Table 3 is the performance test results list of various embodiments of the present invention and comparative example
Various embodiments of the present invention produce according to the following steps:
1) desulfurizing iron and converter smelting, control the C of smelting endpoint 0.05~O.06%, P≤0.008%, S≤ 0.002%, N≤0.004%, tapping temperature is at 1700~1780 DEG C；
2) be casting continuously to form base and slab heated: heating and temperature control at 1280~1320 DEG C, heating rate control 350~ 400 DEG C/h；
3) carry out roughing: control roughing outlet temperature is at 1050~1100 DEG C；
4) finish rolling is carried out, controls the finishing temperature of finish rolling at 850~910 DEG C；
5) section cooling is carried out, in the case where cooling velocity is 10~15 DEG C/sec, is cooled to 640~680 DEG C；
6) it is batched, is batched when temperature is down to 630~660 DEG C；
7) cold rolling is carried out after conventional cold pickling, and controls cold rolling total reduction 50~74%；
8) it anneals, annealing temperature is controlled at 750~810 DEG C, and controls temperature drop speed at 5~8 DEG C/sec；
9) progress is smooth, controls smooth elongation percentage 1.1~1.3%；
10) austenitizing, heating and temperature control are carried out under the protective atmosphere of pure nitrogen gas after conventional finishing and shearing It is kept the temperature at 850~900 DEG C, and at this temperature, soaking time was controlled at 5~8 minutes；
11) progress is hot press-formed, and controls heating and come out of the stove to the merging mold time and be no more than 6 minutes, forming temperature control It makes at 780~820 DEG C,
12) it is quenched, controls its cooling velocity at 30~50 DEG C/sec；
13) stand-by after lonneal, tempering temperature is controlled at 200~250 DEG C, and is kept for 10~20 seconds at this temperature Clock.
Table 1 is the chemical component comparative example (wt%) of various embodiments of the present invention and comparative example
Table 2 is the main technique following table of various embodiments of the present invention and comparative example
Table 3 is the performance test results of various embodiments of the present invention and comparative example
The experiment condition of Hydrogen Embrittlement I: slow tension test, tensile strain rate are carried out in the HCl of 0.1mol/L It is 1.0 × 10-5/ s evaluates anti-hydrogen-induced delayed fracture performance, I by calculating elongation percentage loss (hydrogen embrittlement index I)εIt is worth smaller generation The anti-hydrogen-induced delayed fracture performance of table is better.
Can see case study on implementation 1~8 from the test result of table 3 has preferable performance, and yield strength is in 854MPa Between~998MPa, tensile strength is all larger than 1300MPa, and elongation percentage is up to being all larger than 7%, 2 comparison case tensile strength and in the wrong It takes intensity and properties of product produced by the invention is suitable, but elongation percentage difference is larger, two compared steels are only 6.4% He 6.2%, elongation percentage of the invention is then 8.8~9.2%.
Present embodiment is only the best example, not to the restricted implementation of technical solution of the present invention.

Claims (6)

1. a kind of 1300MPa grades of low hydrogen-induced delayed cracking sensibility hot forming steel, component and weight percent content are as follows: C: 0.14~0.18%, Si:1.10~1.25%, Mn:2.0~2.4%, P≤O.Ol%, S≤0.008%, A1s:0.065~ 0.090%, Cr:0.19~0.24%, Ti:0.026~0.035%, Nb:0.026~0.035%, B:0.002~0.005%, N≤0.005%, Yu Wei Fe and inevitable impurity.
2. a kind of 1300MPa grades of low hydrogen-induced delayed cracking sensibility hot forming steel as described in claim 1, it is characterised in that: The weight percent content of Mn is 2.12~2.35%.
3. a kind of 1300MPa grades of low hydrogen-induced delayed cracking sensibility hot forming steel as described in claim 1, it is characterised in that: The weight percent content of Ti is 0.029~0.035%.
4. a kind of 1300MPa grades of low hydrogen-induced delayed cracking sensibility hot forming steel as described in claim 1, it is characterised in that: The weight percent content of Nb is 0.029~0.035%.
5. a kind of 1300MPa grades of low hydrogen-induced delayed cracking sensibility hot forming steel as described in claim 1, it is characterised in that: The weight percent content of A1s is 0.072~0.090%.
6. a kind of method of 1300MPa grades of low hydrogen-induced delayed cracking sensibility hot forming steel as described in claim 1 is produced, Step:
1) desulfurizing iron and converter smelting, control the C of smelting endpoint 0.05~O.06%, P≤0.008%, S≤0.002% ,
N≤0.004%, tapping temperature is at 1700~1780 DEG C；
2) be casting continuously to form base and heat to slab: at 1280~1320 DEG C, heating rate is controlled 350~400 heating and temperature control DEG C/h；
3) carry out roughing: control roughing outlet temperature is at 1050~1100 DEG C；
4) finish rolling is carried out, controls the finishing temperature of finish rolling at 850~910 DEG C；
5) section cooling is carried out, in the case where cooling velocity is 10~15 DEG C/sec, is cooled to 640~680 DEG C；
6) it is batched, is batched when temperature is down to 630~660 DEG C；
7) cold rolling is carried out after conventional cold pickling, and controls cold rolling total reduction 50~74%；
8) it anneals, annealing temperature is controlled at 750~810 DEG C, and controls temperature drop speed at 5~8 DEG C/sec；
9) progress is smooth, controls smooth elongation percentage 1.1~1.3%；
10) austenitizing is carried out under the protective atmosphere of pure nitrogen gas after conventional finishing and shearing, heating and temperature control is 850 ~900 DEG C, and keep the temperature at this temperature, soaking time was controlled at 5~8 minutes；
11) progress is hot press-formed, and controls heating and come out of the stove to the merging mold time and be no more than 6 minutes, and forming temperature control exists 780~820 DEG C,
12) it is quenched, controls its cooling velocity at 30~50 DEG C/sec；
13) stand-by after lonneal, tempering temperature is controlled at 200~250 DEG C, and is kept for 10~20 seconds at this temperature.
CN201910423899.0A 2019-05-21 2019-05-21 A kind of 1300MPa grades of low hydrogen-induced delayed cracking sensibility hot forming steel and production method Pending CN110157864A (en)

Priority Applications (1)

Application Number Priority Date Filing Date Title
CN201910423899.0A CN110157864A (en) 2019-05-21 2019-05-21 A kind of 1300MPa grades of low hydrogen-induced delayed cracking sensibility hot forming steel and production method

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
CN201910423899.0A CN110157864A (en) 2019-05-21 2019-05-21 A kind of 1300MPa grades of low hydrogen-induced delayed cracking sensibility hot forming steel and production method

Publications (1)

Publication Number Publication Date
CN110157864A true CN110157864A (en) 2019-08-23

Family

ID=67631638

Family Applications (1)

Application Number Title Priority Date Filing Date
CN201910423899.0A Pending CN110157864A (en) 2019-05-21 2019-05-21 A kind of 1300MPa grades of low hydrogen-induced delayed cracking sensibility hot forming steel and production method

Country Status (1)

Country Link
CN (1) CN110157864A (en)

Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN110438314A (en) * 2019-09-05 2019-11-12 首钢集团有限公司 A kind of production method of the steel containing B
CN114921619A (en) * 2022-05-23 2022-08-19 武汉钢铁有限公司 Steelmaking method capable of improving delayed cracking resistance of hot formed steel in CSP production line

Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2004197119A (en) * 2002-12-16 2004-07-15 Jfe Steel Kk Hot-rolled steel sheet superior in uniformity of material quality, hot-dipped steel sheet, and manufacturing method therefor
JP2005325398A (en) * 2004-05-13 2005-11-24 Jfe Bars & Shapes Corp High-strength gear and manufacturing method therefor
CN102181790A (en) * 2011-05-09 2011-09-14 武汉钢铁(集团)公司 Steel with 1,300MPa-level tensile strength for automobile safety piece and production method thereof
CN102747272A (en) * 2012-08-01 2012-10-24 攀枝花贝氏体耐磨管道有限公司 B-P-T steel tube and preparation method thereof
CN103320702A (en) * 2013-06-26 2013-09-25 武汉钢铁(集团)公司 Thermoforming steel with tensile strength of 1,700MPa level and production method thereof
CN109154045A (en) * 2016-05-25 2019-01-04 杰富意钢铁株式会社 Coated steel sheet and its manufacturing method

Patent Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2004197119A (en) * 2002-12-16 2004-07-15 Jfe Steel Kk Hot-rolled steel sheet superior in uniformity of material quality, hot-dipped steel sheet, and manufacturing method therefor
JP2005325398A (en) * 2004-05-13 2005-11-24 Jfe Bars & Shapes Corp High-strength gear and manufacturing method therefor
CN102181790A (en) * 2011-05-09 2011-09-14 武汉钢铁(集团)公司 Steel with 1,300MPa-level tensile strength for automobile safety piece and production method thereof
CN102747272A (en) * 2012-08-01 2012-10-24 攀枝花贝氏体耐磨管道有限公司 B-P-T steel tube and preparation method thereof
CN103320702A (en) * 2013-06-26 2013-09-25 武汉钢铁(集团)公司 Thermoforming steel with tensile strength of 1,700MPa level and production method thereof
CN109154045A (en) * 2016-05-25 2019-01-04 杰富意钢铁株式会社 Coated steel sheet and its manufacturing method

Cited By (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN110438314A (en) * 2019-09-05 2019-11-12 首钢集团有限公司 A kind of production method of the steel containing B
CN110438314B (en) * 2019-09-05 2021-05-25 首钢集团有限公司 Production method of steel containing B
CN114921619A (en) * 2022-05-23 2022-08-19 武汉钢铁有限公司 Steelmaking method capable of improving delayed cracking resistance of hot formed steel in CSP production line
CN114921619B (en) * 2022-05-23 2023-11-03 武汉钢铁有限公司 Steelmaking method capable of improving delayed cracking resistance of hot forming steel in CSP production line

Similar Documents

Publication Publication Date Title
CN110079743A (en) A kind of 1500MPa grades of low hydrogen-induced delayed cracking sensibility hot forming steel and production method
CN104593675A (en) Preparation method of metal material with TWIP (twinning induced plasticity) and TRIP (transformation of retained austenite induced plasticity) effects
EP4159886A1 (en) Ultrahigh-strength dual-phase steel and manufacturing method therefor
CN107012398B (en) A kind of Nb-microalloying TRIP steel and preparation method thereof
EP4317512A1 (en) Low-carbon, low-alloy and high-formability dual-phase steel having tensile strength of greater than or equal to 590 mpa, hot-dip galvanized dual-phase steel, and manufacturing method therefor
EP4261320A1 (en) High-strength and toughness free-cutting non-quenched and tempered round steel and manufacturing method therefor
CN107254635B (en) It is a kind of to exempt from annealed alloy steel wire rod and its production method with excellent drawing property
CN110129673A (en) A kind of 800MPa grades of high strength and ductility Q&P steel plate and preparation method thereof
Zhou et al. Effect of austempering treatment on the microstructure and mechanical properties of 0.4 C–1.5 Si-1.5 Mn TRIP-aided bainitic ferrite steel
CN113234906A (en) Production method for improving performance uniformity of high-strength steel and high-strength steel
CN110157864A (en) A kind of 1300MPa grades of low hydrogen-induced delayed cracking sensibility hot forming steel and production method
CN115181897B (en) 1280 MPa-level low-carbon low-alloy ultra-high strength dual-phase steel and rapid heat treatment manufacturing method
JPH03140411A (en) Improvement of cold working ability of heat treated steel
CN111394658B (en) 980 MPa-grade cold-rolled Q & P steel suitable for conventional continuous annealing production line and manufacturing method thereof
US20220205058A1 (en) A high strength steel product and a process to produce a high strength steel product
CN106086655B (en) A kind of anti-collision hot forming martensite steel for being advantageous to optimize retained austenite
EP4317515A1 (en) Dual-phase steel and hot-dip galvanized dual-phase steel having tensile strength greater than or equal to 980mpa and method for manufacturing same by means of rapid heat treatment
CN109778070A (en) A kind of steel plate and its production method
CN115181886B (en) 980 MPa-level low-carbon low-alloy dual-phase steel and rapid heat treatment manufacturing method
CN113025886B (en) Cold-rolled annealed dual-phase steel with enhanced formability and preparation method thereof
CN111647803B (en) Copper-containing high-strength steel and preparation method thereof
KR100530068B1 (en) Steel strip for the automotive reinforcement parts and method of manufacturing thereof
CN113528974B (en) Steel for protection and preparation method thereof
CN115029630B (en) Thermal forming steel capable of improving 1800MPa grade delayed cracking resistance and production method thereof
CN115181890B (en) 1180 MPa-level low-carbon low-alloy dual-phase steel and rapid heat treatment manufacturing method

Legal Events

Date Code Title Description
PB01 Publication
PB01 Publication
SE01 Entry into force of request for substantive examination
SE01 Entry into force of request for substantive examination
RJ01 Rejection of invention patent application after publication
RJ01 Rejection of invention patent application after publication

Application publication date: 20190823