CN110079743A - A kind of 1500MPa grades of low hydrogen-induced delayed cracking sensibility hot forming steel and production method - Google Patents
A kind of 1500MPa grades of low hydrogen-induced delayed cracking sensibility hot forming steel and production method Download PDFInfo
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- CN110079743A CN110079743A CN201910423900.XA CN201910423900A CN110079743A CN 110079743 A CN110079743 A CN 110079743A CN 201910423900 A CN201910423900 A CN 201910423900A CN 110079743 A CN110079743 A CN 110079743A
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- 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
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
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- 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
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0226—Hot rolling
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- 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
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
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- 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
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- 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
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- 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
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- 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
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- 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
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- 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 1500MPa grades of low hydrogen-induced delayed cracking sensibility hot forming steel, its component and wt% are as follows: C:0.18~0.22%, Si:1.20~1.45%, 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:0.050~0.085%, 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 RpO.2In 900~1100MPa, tensile strength Rm >=1500MPa, elongation percentage A50mmUnder >=8%, 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
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.
Most basic mechanical performances for only focusing on hot forming steel in contemporary literature, and rarely about delayed fracture
Research 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 1500MPa 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 RpO.2: 900~1100MPa, tensile strength Rm >=1500MPa, elongation percentage A50mmUnder >=8%, make Hydrogen Embrittlement I≤
45% hot forming steel and production method.
Realize the measure of above-mentioned purpose:
A kind of 1500MPa grades of low hydrogen-induced delayed cracking sensibility hot forming steel, component and weight percent content are as follows: C:
0.18~0.22%, Si:1.20~1.45%, 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:0.050~0.085%, B:0.002~0.005%,
N≤0.005%, Yu Wei Fe and inevitable impurity.
Preferably: the weight percent content of Mn is 2.15~2.35%.
Preferably: the weight percent content of Ti is 0.026~0.031%.
Preferably: the weight percent content of Nb is 0.063~0.085%.
Preferably: the weight percent content of A1s is 0.072~0.090%.
A kind of method for producing 1500MPa 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 1200~1250 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) smart bundle is carried out, controls the finishing temperature of finish rolling at 840~880 DEG C；
5) section cooling is carried out, in the case where cooling velocity is 15~20 DEG C/sec, is cooled to (620~660 DEG C)；
6) it is batched, is batched when temperature is 580~620 DEG C near；；
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 0.18~0.20% 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 1.20~1.45% 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 2.15~2.35%.
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.
Als: 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, and Ti can generate TiN in conjunction with the N in steel can reduce the toughness of steel, content needs to be controlled.So will
Its content is limited to 0.026~0.035% range, and preferably content is 0.026~0.031%.
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, to hinder Austenite Grain Growth, play the role of refining crystal grain, because
This, quenched martensite lath size is smaller, greatly improves the intensity of steel；In addition the carbon of niobium, nitride are good hydrogen
Trap can effectively inhibit diffusion of the hydrogen in steel, be conducive to the anti-hydrogen-induced delayed fracture performance for promoting steel.Therefore its content is controlled
System is between 0.050~0.085%, and preferably content is 0.063~0.085%.
Why the present invention controls coiling temperature at 580~620 DEG C, is that Nb, Ti in steel etc. are precipitated due to coiling temperature
Object is very crucial, the Carbonitride Precipitation of Nb, Ti can be promoted to grow up when batching in higher temperature, and precipitation is more abundant, but analyses
Particle can be coarse out, is unfavorable for promoting the delayed fracture performance of steel；And the too low precipitation of temperature can be insufficient, is also unfavorable for being promoted and prolong
Slow cracking performance, thus be set in 580~620 DEG C it is proper.
Compared with prior art, the present invention not only yield strength RpO.2: 900~1100MPa, tensile strength Rm >=
1500MPa, elongation percentage A50mm>=8%, and Hydrogen Embrittlement I≤45%, it is applied to make on automobile upper body and lower body
Structural member and safety member can not only mitigate body of a motor car weight, and be capable of the safety of effective protection driver and passenger.
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:0.05 of smelting endpoint~O.06%, and 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 1200~1250 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) smart bundle is carried out, controls the finishing temperature of finish rolling at 840~880 DEG C；
5) section cooling is carried out, in the case where cooling velocity is 15~20 DEG C/sec, is cooled to (620~660 DEG C)；
6) it is batched, oiler temperature control is at 580~620 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
Hydrogen Embrittlement IHEExperiment condition: in the HCl of 0.1mol/L carry out the slow tension test of SSRT, elongation strain
Rate is 1.0 × 10-5/ s evaluates anti-hydrogen-induced delayed fracture performance, I by calculating elongation percentage loss (hydrogen embrittlement index I)εValue is got over
It is small that represent anti-hydrogen-induced delayed fracture performance better.
From the interpretation of result of table 3, can see case study on implementation 1~8 from the test result of table 3 has preferable performance,
Yield strength is between 912MPa~1100MPa, and tensile strength is all larger than 1500MPa, and up to being all larger than 8%, 2 compare elongation percentage
Case tensile strength and the properties of product of yield strength and this method production are suitable, but elongation percentage difference is larger, two comparisons
Steel is only 6.3% and 6.1%,
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 1500MPa grades of low hydrogen-induced delayed cracking sensibility hot forming steel, component and weight percent content are as follows: C:
0.18~0.22%, Si:1.20~1.45%, 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:0.050~0.085%, B:0.002~0.005%,
N≤0.005%, Yu Wei Fe and inevitable impurity.
2. a kind of 1500MPa 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 2.15~2.35%.
3. a kind of 1500MPa 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 0.026~0.031%.
4. a kind of 1500MPa 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 0.063~0.085%.
5. a kind of 1500MPa 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 1500MPa 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 1200~1250 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) smart bundle is carried out, controls the finishing temperature of finish rolling at 840~880 DEG C；
5) section cooling is carried out, in the case where cooling velocity is 15~20 DEG C/sec, is cooled to 620~660 DEG C；
6) it is batched, is batched when temperature is 580~620 DEG C near；
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.
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Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN111748736A (en) * | 2020-06-24 | 2020-10-09 | 武汉钢铁有限公司 | 1800 MPa-grade low-hydrogen delayed cracking sensitive hot forming steel and production method thereof |
| CN113528947A (en) * | 2021-06-21 | 2021-10-22 | 武汉钢铁有限公司 | Steel for high-plasticity-toughness automobile structural part with tensile strength of 1500MPa produced by CSP and production method |
| CN114807780A (en) * | 2022-04-27 | 2022-07-29 | 鞍钢股份有限公司 | 600 MPa-grade steel for automobile axle housing for hot stamping and production method thereof |
| 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 |
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| CN114807780A (en) * | 2022-04-27 | 2022-07-29 | 鞍钢股份有限公司 | 600 MPa-grade steel for automobile axle housing for hot stamping and production method thereof |
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| 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 |
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