CN109136762A - A kind of semitrailer welding I beam steel and its production method - Google Patents
A kind of semitrailer welding I beam steel and its production method Download PDFInfo
- Publication number
- CN109136762A CN109136762A CN201811120779.5A CN201811120779A CN109136762A CN 109136762 A CN109136762 A CN 109136762A CN 201811120779 A CN201811120779 A CN 201811120779A CN 109136762 A CN109136762 A CN 109136762A
- Authority
- CN
- China
- Prior art keywords
- welding
- heating
- beam steel
- slab
- temperature
- 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
Links
Classifications
-
- 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
- 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
-
- 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
-
- 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
-
- 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
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- 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
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
-
- 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
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
-
- 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
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel 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
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel 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
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel 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
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Heat Treatment Of Steel (AREA)
Abstract
The invention discloses a kind of semitrailer welding I beam steel and its production methods, the ingredient percent of I-beam steel is C:0.14~0.20wt%, Si:0.10-0.65wt%, Mn:1.1~1.65wt%, Nb:0.02~0.05wt%, Mo:0.3~0.8wt%, V:0.03~0.15wt%, Ti:0.01~0.04wt%, Al:0.01~0.06wt%, Cr:0.3~1.0wt%, Ni:0.5~1.0wt%, B:0.0015~0.0025wt%, P :≤0.02wt%, S :≤0.01wt%, N :≤0.008wt%, remaining is for Fe and inevitably Impurity.With steel intensity rank requirement is unable to reach to solve light-weighted semi-trailer welding I beam in the prior art, and improve the intensity rank of steel, the technical issues of it will cause weld crackings, weld fatigue cracking, semitrailer welding I beam steel is realized with good obdurability, welding performance and low-temperature impact toughness, the technical effect that the lightweight for improving the security performance of vehicle, and being conducive to vehicle develops.
Description
Technical field
The present invention relates to metallurgical technology field, in particular to a kind of semitrailer welding I beam steel and its production method.
Background technique
Commercial vehicle lightweight is under the premise of guaranteeing bus body strength and security performance, and reduction automobile is whole as much as possible
Standby quality increases shipping useful load while raising vehicle dynamic quality, energy-saving, improves shipping and has enough to meet the need ability.In order to suitable
The requirement of automotive light weight technology is answered, some high strength steel iron materials start to be answered in semitrailer welding I-girder rings domain
With.
Since light-weighted semi-trailer welding I beam in the prior art is unable to reach intensity rank requirement with steel, and improve steel
Intensity rank, it will cause weld cracking, weld fatigue cracking the technical issues of.
Summary of the invention
The embodiment of the invention provides a kind of semitrailer welding I beam steel and its production methods, to solve existing skill
Light-weighted semi-trailer welding I beam is unable to reach intensity rank requirement with steel in art, and improves the intensity rank of steel, then can make
At weld cracking, weld fatigue cracking the technical issues of, realize semitrailer welding I beam steel with good obdurability,
The technical effect that the lightweight that welding performance and low-temperature impact toughness improve the security performance of vehicle, and be conducive to vehicle develops.
To solve the above-mentioned problems, in a first aspect, the embodiment of the invention provides a kind of semitrailer welding I beam steel,
The ingredient percent of I-beam steel is C:0.14~0.20wt%, Si:0.10-0.65wt%, Mn:1.1~
1.65wt%, Nb:0.02~0.05wt%, Mo:0.3~0.8wt%, V:0.03~0.15wt%, Ti:0.01~
0.04wt%, Al:0.01~0.06wt%, Cr:0.3~1.0wt%, Ni:0.5~1.0wt%, B:0.0015~
0.0025wt%, P :≤0.02wt%, S :≤0.01wt%, N :≤0.008wt%, remaining is Fe and inevitable impurity.
Preferably, cooling cracks the susceptible index number Pcm≤0.31 of the ingredient of the I-beam steel.
Second aspect, the embodiment of the invention provides a kind of production method of semitrailer welding I beam steel, the sides
Method includes: to obtain slab using smelting molten steel；The slab is heated in heating furnace, the temperature of the slab after heating
It is 1180~1250 DEG C；Roughing and finish rolling are successively carried out to the slab after heating, obtain hot rolled plate；It is right after rolling
The hot rolled plate is using section cooling and batches, and obtains coil of strip；Slow cooling processing is carried out to the coil of strip using burial pit, and slow
Smooth processing is carried out to coil of strip after cold treatment；After smooth processing, uncoiling processing is carried out to coil of strip, obtains roll bending, and to the volume
Plate carries out continuous high frequency induction heating and heat preservation, is quenched to room temperature；After quenching, continuous induction tempering heating and guarantor are carried out to roll bending
Temperature, and carry out air-cooled or air-cooled to room temperature；Crosscutting, acquisition I-beam steel, wherein the I-beam steel is carried out to roll bending
Ingredient percent be C:0.14~0.20wt%, Si:0.10-0.65wt%, Mn:1.1~1.65wt%, Nb:0.02~
0.05wt%, Mo:0.3~0.8wt%, V:0.03~0.15wt%, Ti:0.01~0.04wt%, Al:0.01~
0.06wt%, Cr:0.3~1.0wt%, Ni:0.5~1.0wt%, B:0.0015~0.0025wt%, P :≤0.02wt%, S:
≤ 0.01wt%, N :≤0.008wt%, remaining is Fe and inevitable impurity.
Preferably, the soaking time of the slab is set within the scope of 1~1.5min/mm by by the effective thickness control of slab
It sets.
Preferably, the slab after described pair of heating successively carries out roughing and finish rolling, obtains hot rolled plate, comprising: in institute
Workpiece thickness after stating roughing is 5 times~10 times of the hot rolling plate thickness after the finish rolling；The entry temperature at finishing
It is 1000 DEG C~1050 DEG C, finishing temperature is 830~880 DEG C.
Preferably, the coiling temperature batched is 650 DEG C~750 DEG C, the thickness specification of the coil of strip be 3mm~
10mm。
Preferably, the slow cooling time of the slow cooling processing is greater than 72 hours, and whole cool time is control coil of strip slow cooling temperature
Time lower than 150 DEG C.
Preferably, the heating temperature of the high-frequency induction heating is 900-950 DEG C, and the rate of heat addition is greater than 150 DEG C/S, heat preservation
Time is less than 10min.
Preferably, the quenching uses water quenching.
Preferably, the heating temperature of the tempering heating is 450-650 DEG C, and the rate of heat addition is greater than 150 DEG C/S, soaking time
Less than 20min.
Said one or multiple technical solutions in the embodiment of the present invention at least have following one or more technology effects
Fruit:
The embodiment of the invention provides a kind of vehicle structure hot-strip and manufacturing methods, which comprises uses
Smelting molten steel obtains slab；The slab is heated in heating furnace, after heating the temperature of the slab be 1180~
1250℃；Roughing and finish rolling are successively carried out to the slab after heating, obtain hot rolled plate；After rolling, to the hot rolling
Plate is using section cooling and batches, and obtains coil of strip；Slow cooling processing is carried out to the coil of strip using burial pit, and after slow cooling processing
Smooth processing is carried out to coil of strip；After smooth processing, uncoiling processing is carried out to coil of strip, obtains roll bending, and connect to the roll bending
Continuous high-frequency induction heating and heat preservation, are quenched to room temperature；After quenching, continuous induction tempering heating and heat preservation are carried out to roll bending, gone forward side by side
Row is air-cooled or air-cooled to room temperature；To roll bending carry out it is crosscutting, obtain I-beam steel, wherein the I-beam steel at sub-prime
Amount percentage be C:0.14~0.20wt%, Si:0.10-0.65wt%, Mn:1.1~1.65wt%, Nb:0.02~
0.05wt%, Mo:0.3~0.8wt%, V:0.03~0.15wt%, Ti:0.01~0.04wt%, Al:0.01~
0.06wt%, Cr:0.3~1.0wt%, Ni:0.5~1.0wt%, B:0.0015~0.0025wt%, P :≤0.02wt%, S:
≤ 0.01wt%, N :≤0.008wt%, remaining is Fe and inevitable impurity.By the control to slab heating temperature, protect
The effective thickness for having demonstrate,proved slab is conducive to refine crystal grain；Slab is rolled and carries out cooling and is batched, is conducive to after reinforcing phase transformation
Build up is also beneficial to enhancing precipitating reinforcing effect；And then coil of strip is handled using slow cooling, make the logical volume mechanical property of material
It is more uniform, and so that internal stress is released and is homogenized, so as to improve strip shape quality, be conducive to subsequent heat treatment
The control of plate shape and residual stress；After carrying out smooth and uncoiling processing to coil of strip again, continuous high frequency induction heating is carried out to roll bending
And heat preservation, the rate of heat addition can be improved be conducive to quenching and obtain more tiny martensite and lath of bainite, and is conducive to control
Morphology of carbides in quenching structure；After roll bending quenching, continuous induction tempering heating and heat preservation are carried out to roll bending, improve material
Intensity, be conducive to control material unevenness and guarantee blanking after it is indeformable；It is available thin by the restriction to steel component
Small, uniform tempered structure realizes semitrailer welding I beam steel with good obdurability, welding performance and low temperature punching
Hit the technical effect of toughness.
The above description is only an overview of the technical scheme of the present invention, in order to better understand the technical means of the present invention,
And it can be implemented in accordance with the contents of the specification, and in order to allow above and other objects of the present invention, feature and advantage can
It is clearer and more comprehensible, the followings are specific embodiments of the present invention.
Detailed description of the invention
Fig. 1 is the metallographic structure schematic diagram of this specification embodiment semitrailer welding I beam steel；
Fig. 2 is the flow chart of the production method of semitrailer welding I beam steel in this specification embodiment.
Specific embodiment
The embodiment of the invention provides a kind of semitrailer welding I beam steel and its production methods, to solve existing skill
Light-weighted semi-trailer welding I beam is unable to reach intensity rank requirement with steel in art, and improves the intensity rank of steel, then can make
At weld cracking, weld fatigue cracking the technical issues of, realize semitrailer welding I beam steel with good obdurability,
The technical effect that the lightweight that welding performance and low-temperature impact toughness improve the security performance of vehicle, and be conducive to vehicle develops.
Technical solution in the embodiment of the present invention, the ingredient percent of I-beam steel be C:0.14~
0.20wt%, Si:0.10-0.65wt%, Mn:1.1~1.65wt%, Nb:0.02~0.05wt%, Mo:0.3~0.8wt%,
V:0.03~0.15wt%, Ti:0.01~0.04wt%, Al:0.01~0.06wt%, Cr:0.3~1.0wt%, Ni:0.5~
1.0wt%, B:0.0015~0.0025wt%, P :≤0.02wt%, S :≤0.01wt%, N :≤0.008wt%, remaining is Fe
And inevitable impurity.With steel intensity rank is unable to reach to solve light-weighted semi-trailer welding I beam in the prior art
It is required that and improve steel intensity rank, it will cause weld cracking, weld fatigue cracking the technical issues of, realize semitrailer
Welding I beam has good obdurability, welding performance and low-temperature impact toughness with steel, improves the security performance of vehicle, and
The technical effect developed conducive to the lightweight of vehicle.
In order to make the object, technical scheme and advantages of the embodiment of the invention clearer, below in conjunction with the embodiment of the present invention
In attached drawing, technical scheme in the embodiment of the invention is clearly and completely described, it is clear that described embodiment is
A part of the embodiment of the present invention, instead of all the embodiments.Based on the embodiments of the present invention, those of ordinary skill in the art
Every other embodiment obtained without making creative work, shall fall within the protection scope of the present invention.
Embodiment one
The embodiment of the invention provides a kind of semitrailer welding I beam steel, referring to FIG. 1, the I-beam steel
Ingredient percent be C:0.14~0.20wt%, Si:0.10-0.65wt%, Mn:1.1~1.65wt%, Nb:0.02~
0.05wt%, Mo:0.3~0.8wt%, V:0.03~0.15wt%, Ti:0.01~0.04wt%, Al:0.01~
0.06wt%, Cr:0.3~1.0wt%, Ni:0.5~1.0wt%, B:0.0015~0.0025wt%, P :≤0.02wt%, S:
≤ 0.01wt%, N :≤0.008wt%, remaining is Fe and inevitable impurity.
Further, a part of ingredient percent of I-beam steel is C:0.15~0.20wt%, Mn:
1.2~1.5%wt%, Nb:0.03~0.04wt%, Ti:0.01~0.02wt%, Mo:0.3~0.5wt%, V:0.04~
0.10wt%, Cr:0.5~1.0wt%, B:0.0015~0.0020wt%.
Further, a part of ingredient percent of I-beam steel is C:0.15~0.18wt%, Mn:
1.3~1.6%wt%, Nb:0.02~0.03wt%, Ti:0.02~0.35wt%, Mo:0.45~0.65wt%, V:0.05~
0.12wt%, Cr:0.05~0.08wt%, B:0.0016~0.0022wt%.
Specifically, the I-beam is played a significant role in heat treatment high-strength steel with C in steel, on the one hand pass through addition
C is remarkably improved the intensity of material, but low-temperature impact toughness and solderability to guarantee material, needs to do the upper limit of C content
It clearly limits, the C content that the embodiment of the present application uses is 0.14~0.20wt%.Si is solution strengthening element, but is added excessively high
Si can have a negative impact to the plasticity of material.It is 0.10-0.65wt% that the embodiment of the present application, which adds silicone content,.Mn has solid
Molten invigoration effect, while material harden ability can be improved, it is to improve one of strength of materials important element, but manganese content adds excessively high appearance
It is also easy to produce and is segregated and can reduce toughness of material, deteriorate performance.It is 1.1~1.65wt% that the embodiment of the present application, which adds manganese content,.S and
P element too high levels can adversely affect toughness of material and plasticity.The embodiment of the present application defines that sulfur content should control
Within 0.01wt%, phosphorus content should be controlled within 0.02wt%.Al is deoxidant element, while having certain crystal grain refinement effect
Fruit.The embodiment of the present application defines that aluminium content is 0.01~0.06wt%.Material harden ability, control heat treatment cooling can be improved in Mo
Tissue refines crystal grain, improves material plasticity and intensity.The embodiment of the present application Mo is added to 0.3~0.8wt%, improves tissue
Strengthen performance.The main purpose of Nb is refinement crystal grain, and fine uniform can be obtained using lower finish rolling area rolling temperature in cooperation
Ferrite crystal grain, heat treatment base-material fine microstructures have genetic effect to subsequent heat treatment, are conducive to improve final finished steel plate
Obdurability；On the other hand, the present embodiment uses higher tempering temperature, and Nb has precipitation strength effect simultaneously.This implementation
The Nb content of example addition is 0.02~0.05wt%.The main function of Ti is fixed nitrogen, reduces the N to dissociate in steel by forming TiN,
Improve materials'use performance；In addition, extra Ti in conjunction with C, plays the role of precipitation strength, but the precipitation strength of TiC can be to material
The low-temperature impact toughness of material causes damages, therefore need to control the upper limit of Ti content.The addition of the present embodiment Ti content: 0.01~
0.04wt%.V is the important alloying element designed in the embodiment of the present application, the addition of high V content, the coiling temperature and heat of hot rolling
The tempering temperature of processing considers the precipitation strength and tissue thinning effect of V element.The present embodiment addition 0.03~
The V of 0.15wt% carries out microalloying, cooperates suitable production technology, and a large amount of small and dispersed distributions have been obtained in hot-rolled coil
V precipitate, the precipitate that V is further precipitated during tempering heat treatment greatly improves the strength level of material.This reality
Apply Cr in example is reduced the additive amount of Mn by addition Cr, mitigates center to improve material harden ability and improving strength of materials element
Segregation and banded structure, the content that Cr is added in the present embodiment is 0.3~1.0wt%.Ni is that important hardness of steel and toughness mention
Element is risen, addition Ni can improve welding heat influence area toughness and fatigue behaviour, therefore this implementation while improving strength and toughness
Ni content adds 0.5~1.0wt% in example.The purpose of B is to improve the harden ability of material, improves intensity, but need strict control B's
Additional amount avoids toughness from declining, and B adds 0.0015~0.0025wt% in the embodiment of the present application.N content is excessively high can severe exacerbation
The plasticity and toughness of material, especially for heat treatment high-strength steel, therefore, the embodiment of the present application limits nitrogen content and should be less than
0.008.Surplus other than mentioned component is Fe and inevitable impurity.Preferably, a part of the I-beam steel at
Divide mass percent for C:0.15~0.20wt%, Mn:1.2~1.5%wt%, Nb:0.03~0.04wt%, Ti:0.01~
0.02wt%, Mo:0.3~0.5wt%, V:0.04~0.10wt%, Cr:0.5~1.0wt%, B:0.0015~
0.0020wt%.Or, a part of ingredient percent of I-beam steel is C:0.15~0.18wt%, Mn:1.3~
1.6%wt%, Nb:0.02~0.03wt%, Ti:0.02~0.35wt%, Mo:0.45~0.65wt%, V:0.05~
0.12wt%, Cr:0.05~0.08wt%, B:0.0016~0.0022wt%.The embodiment of the present application uses middle low-carbon alloy
Component system, lower carbon and manganese content make full use of the precipitating reinforcing effect of V, Nb, Ti, at the same add a certain amount of Mo, Cr,
B controls heat-treated sturcture state, obtains tiny, uniform tempered structure, so that material has good obdurability, good
Welding performance and good low-temperature impact toughness, utilize Ni element to improve strength of parent and toughness, it is comprehensive to improve welding point
The structural fatigue performance of mechanical property and crossbeam improves the security performance of vehicle, and the lightweight for being conducive to vehicle develops.
Further, cooling cracks the susceptible index number Pcm≤0.31 of the ingredient of the I-beam steel.
Specifically, the embodiment of the present application by limit I-beam steel ingredient cooling cracks the susceptible index number Pcm≤
0.31, it is ensured that welding cold cracking does not occur in subsequent gas shield welding or submerged arc welding process in the powerful joist steel of superelevation, and improves welding
The comprehensive performance of heat affected area.
Embodiment two
A kind of production method of semitrailer welding I beam steel is present embodiments provided, referring to FIG. 2, the method packet
It includes:
Step 110: slab is obtained using smelting molten steel.
Step 120: the slab being heated in heating furnace, the temperature of the slab is 1180~1250 after heating
℃。
Further, the soaking time of the slab, which is pressed, controls the effective thickness of slab within the scope of 1~1.5min/mm
Setting.
Specifically, the embodiment of the present application obtains slab to smelting molten steel using method of smelting such as converters, by the slab
It heats in heating furnace, the temperature of the slab is 1180~1250 DEG C after heating.The soaking time of the slab is pressed will
The effective thickness control of slab is arranged within the scope of 1~1.5min/mm, is to guarantee using the purpose of higher heating temperature difficult to understand
The compound of Ti, Nb for being formed in family name's body homogenization and alloying element such as slab dissolve more abundant.
Step 130: roughing and finish rolling successively being carried out to the slab after heating, obtain hot rolled plate.
Further, the slab after described pair of heating successively carries out roughing and finish rolling, obtains hot rolled plate, comprising:
Workpiece thickness after the roughing is 5 times~10 times of the hot rolling plate thickness after the finish rolling；The finish rolling entrance temperature
Degree is 1000 DEG C~1050 DEG C, and finishing temperature is 830~880 DEG C.
Specifically, the embodiment of the present application is rolled using two-stage control, the slab after heating is successively carried out thick
It rolls and finish rolling guarantees in 5 times~10 times that the workpiece thickness after the roughing is the hot rolling plate thickness after the finish rolling
With enough austenite Unhydrated cement drafts, can contract while being conducive to refine crystal grain, and increase workpiece thickness
Base length between brachymedial prevents tail temperature from reducing excessive increase mill load to reduce poor into finish rolling head and tail temperature.Finish rolling
Journey need to be 1000 DEG C~1050 DEG C according to finished product thickness specification strict control entry temperature at finishing, and finishing temperature is 830~880
DEG C, it is to obtain the effective ways of fine uniform crystal grain using lower finish rolling area temperature, avoids hot-rolled coil organizational coarseness and band
The appearance of shape tissue.
Step 140: after rolling, the hot rolled plate using section cooling and being batched, obtains coil of strip.
Further, the coiling temperature batched is 650 DEG C~750 DEG C, the thickness specification of the coil of strip be 3mm~
10mm。
Specifically, carrying out section cooling after rolling using leading portion refrigerating mode to the hot rolled plate, being conducive to add
Build up after strong phase transformation, and be conducive to enhance precipitating reinforcing effect, the tiny precipitation product in more ferrites is obtained, from
And effectively improve the strength of materials.Controlling the coiling temperature batched is 650 DEG C~750 DEG C, is mainly in view of the alternate analysis of V, Nb, Ti
Precipitation out and in ferrite, coiling temperature lower limit need strict control to be greater than 620 DEG C, avoid occurring bayesian in hot-rolled coil
Body tissue, to obtain coil of strip, the thickness specification of the coil of strip is 3mm~10mm.
Step 150: slow cooling processing being carried out to the coil of strip using burial pit, and smooth to coil of strip progress after slow cooling processing
Processing.
Further, the slow cooling time of the slow cooling processing is greater than 72 hours, and whole cool time is control coil of strip slow cooling temperature
Degree is lower than 150 DEG C of time.
Specifically, carrying out slow cooling processing, the slow cooling time of the slow cooling processing to the coil of strip after offline using burial pit
Greater than 72 hours, and whole cool time was the time for controlling coil of strip slow cooling temperature and being lower than 150 DEG C.Coil of strip is delayed using burial pit
It is cold, the logical volume mechanical property of material can be made more uniform, and so that internal stress is released and is homogenized, to change
Kind strip shape quality, is conducive to the control of subsequent heat treatment plate shape and residual stress.Smooth place is carried out to coil of strip after slow cooling processing
Reason eliminates wave, need to guarantee that smooth elongation percentage is greater than 1.5%.
Step 160: after smooth processing, uncoiling processing being carried out to coil of strip, obtains roll bending, and the roll bending is carried out continuous high
Frequency induction heating and heat preservation, are quenched to room temperature.
Further, the heating temperature of the high-frequency induction heating is 900-950 DEG C, and the rate of heat addition is greater than 150 DEG C/S, is protected
The warm time is less than 10min.The quenching uses water quenching.
Specifically, carrying out uncoiling processing to coil of strip after smooth processing, roll bending is obtained, and the roll bending is carried out continuous
High-frequency induction heating, the heating temperature of the high-frequency induction heating are 900-950 DEG C, and the rate of heat addition is greater than 150 DEG C/S, using height
The purpose of frequency induction heating be control quenched martensite tissue topography, improve the rate of heat addition be conducive to quenching obtain it is more tiny
Martensite and lath of bainite, and be conducive to control quenching structure in morphology of carbides.Wherein, the heating temperature of the roll bending
When reaching 900-950 DEG C, the roll bending is kept the temperature, soaking time is less than 10min, and the purpose for controlling soaking time is to prevent
The carbide dissolution of V, Ti, Nb in hot-rolled coil, and reduce austenite grain size.Roll bending after heating and thermal insulation is quenched
Processing, using water quenching, target temperature is room temperature, and tiny martensite and bainite structure can be obtained after quenching.
Step 170: after quenching, continuous induction tempering heating and heat preservation being carried out to roll bending, and carry out air-cooled or air-cooled to room
Temperature；
Further, the heating temperature of the tempering heating is 450-650 DEG C, and the rate of heat addition is greater than 150 DEG C/S, when heat preservation
Between be less than 20min.
Specifically, carrying out continuous induction tempering heating to roll bending, the heating temperature of the tempering heating is after quenching
450-650 DEG C, the rate of heat addition is greater than 150 DEG C/S, is to control cementite pattern using the purpose that high-frequency induction quickly heats, together
When be conducive to eliminate steel plate residual stress, be conducive to control material unevenness and guarantee blanking after it is indeformable.Tempering is heated
Roll bending is kept the temperature afterwards, and soaking time is less than 20min, by quickly heat with strict control soaking time, can be obtained tiny disconnected
The cementite of continuous distribution, simultaneously because using higher tempering temperature, V, Nb, Ti existing for solid solution mode will be further in steel
It is precipitated, improves the intensity of material.
Step 180: crosscutting, acquisition I-beam steel, wherein the composition quality hundred of the I-beam steel is carried out to roll bending
Divide ratio for C:0.14~0.20wt%, Si:0.10-0.65wt%, Mn:1.1~1.65wt%, Nb:0.02~0.05wt%,
Mo:0.3~0.8wt%, V:0.03~0.15wt%, Ti:0.01~0.04wt%, Al:0.01~0.06wt%, Cr:0.3~
1.0wt%, Ni:0.5~1.0wt%, B:0.0015~0.0025wt%, P :≤0.02wt%, S :≤0.01wt%, N :≤
0.008wt%, remaining is Fe and inevitable impurity.
Specifically, carry out welding after carrying out laser, plasma or fiery cut blanking to roll bending and I-beam steel is made,
The ingredient percent for controlling I-beam steel is C:0.14~0.20wt%, Si:0.10-0.65wt%, Mn:1.1
~1.65wt%, Nb:0.02~0.05wt%, Mo:0.3~0.8wt%, V:0.03~0.15wt%, Ti:0.01~
0.04wt%, Al:0.01~0.06wt%, Cr:0.3~1.0wt%, Ni:0.5~1.0wt%, B:0.0015~
0.0025wt%, P :≤0.02wt%, S :≤0.01wt%, N :≤0.008wt%, remaining is Fe and inevitable impurity.
Low C, low Mn, high V ingredient mentality of designing in the embodiment of the present application use give full play to the reinforcings such as build up, precipitation strength effect
Fruit, the material yield strength produced are greater than 1100MPa, and tensile strength is greater than 1150MPa, and elongation percentage is greater than 10%, -40 DEG C of punchings
It hits function not crack greater than 27J, 180 ° of clod wash B=35mm/D=4a, material has good welding performance and fatigue behaviour simultaneously.
Embodiment three
A kind of production method of semitrailer welding I beam steel is present embodiments provided, the method is turned using 220 tons
Furnace is smelted, and 2250 hot continuous rolling production lines are rolled, and I-beam is 1500mm with the target width of steel finished product, with a thickness of 3-8mm,
Specific step is as follows for the present embodiment:
Molten steel obtains slab after converter smelting；Smelting process strict control P, S content guarantees slab quality.It smelts
I-beam steel chemical composition is as shown in table 1.Table 1 lists the embodiment of the present application 1100MPa superelevation more than half trailer welding I-shaped
Beam steel chemical composition.
1 1100MPa superelevation more than half trailer welding I beam steel chemical composition of table
Slab is put into heating furnace to heat, the slab after heating is put into milling train and is rolled, obtains hot rolled plate.It is right
Hot rolled plate is cooled down, and carries out section cooling using leading portion refrigerating mode, hot rolled plate after cooling is batched, obtain steel
Volume carries out slow cooling processing using burial pit to the coil of strip, slow cooling soaking time 72 hours, cheats temperature control out at 100 DEG C.It is right
Coil of strip carries out smooth processing after slow cooling, and smooth elongation percentage reaches 1.5%.Uncoiling processing is carried out to the coil of strip, obtains roll bending, it is right
Roll bending carries out continuous high frequency induction heating and heat preservation, then water quenching to room temperature.High-frequency induction tempering is carried out to roll bending after quenching to add
Heat and heat preservation, after be air-cooled to room temperature.Crosscutting, acquisition I-beam steel is carried out to the coil of strip.The specific control of above-mentioned production stage
Parameter processed is as shown in table 2.Table 2 is listed chooses ten groups of component content productions in the ingredient of the I-beam steel of restriction
1100MPa superelevation more than half trailer welding I beam steel processing parameter.
2 1100MPa superelevation more than half trailer welding I beam steel processing parameter of table
Pass through mechanical property such as 3 institute of table for the 1100MPa superelevation more than half trailer welding I beam steel that above-mentioned technique obtains
Show.Table 3 is listed chooses ten groups of component content production 1100MPa superelevation more than half trailers in the ingredient of the I-beam steel of restriction
Welding I beam steel mechanical property parameter.
3 1100MPa superelevation more than half trailer welding I beam steel mechanical property parameter of table
The finished steel plate finally obtained through this embodiment is welded after carrying out laser, plasma or fiery cut blanking
Welding I beam steel is made.The steel plate of the I-beam steel is indeformable after 13 meters and 17.5 meters long crossbeam blanking cutting,
Welding is not cracked, and manufactured automotive frame indices are all satisfied requirement.1100MPa superelevation more than half provided in this embodiment
Trailer welding I beam is welded with steel and is not cracked, and crack sensitivity is low, and welding does not need to preheat, and has good fatigue behaviour
And security performance.1100MPa superelevation more than half trailer welding I beam provided by the embodiments of the present application passes through reasonably optimizing steel with steel
The ratio of middle chemical component gives full play to the strengthening effects such as build up, precipitation strength, has the steel plate finished product finally obtained
Good intensity, toughness, welding performance and strip shape quality.Further, 1100MPa superelevation more than half trailer provided in this embodiment
Welding I beam with steel production method in low C, low Mn, high V, the method that Cr high Ni strengthens in middle Mo, it is stringent to control
The content of P, S in smelting process processed, and controlled rolling and cooling process parameter is rationally set in rolling and heat treatment process, guarantee steel
Board finished product has good structural state, and effectively controls precipitate state, effectively improves the resultant force of beam steel
Performance is learned, the yield strength of beam steel made from the production method reaches 1100MPa or more, while ratio elongation percentage is greater than
10%, and can guarantee that low-temperature impact toughness reaches E step requirement, clod wash D=4a 180 ° wide does not crack.The material of the present embodiment production
Material be obviously improved the intensity rank of crossbeam, be conducive to semitrailer crossbeam material be thinned and vehicle loss of weight, energy it is good full
Sufficient automotive frame loading demands in use and fatigue behaviour requirement.
The technical solution provided in the embodiment of the present application, has at least the following technical effects or advantages:
The embodiment of the invention provides a kind of vehicle structure hot-strip and manufacturing methods, which comprises uses
Smelting molten steel obtains slab；The slab is heated in heating furnace, after heating the temperature of the slab be 1180~
1250℃；Roughing and finish rolling are successively carried out to the slab after heating, obtain hot rolled plate；After rolling, to the hot rolling
Plate is using section cooling and batches, and obtains coil of strip；Slow cooling processing is carried out to the coil of strip using burial pit, and after slow cooling processing
Smooth processing is carried out to coil of strip；After smooth processing, uncoiling processing is carried out to coil of strip, obtains roll bending, and connect to the roll bending
Continuous high-frequency induction heating and heat preservation, are quenched to room temperature；After quenching, continuous induction tempering heating and heat preservation are carried out to roll bending, gone forward side by side
Row is air-cooled or air-cooled to room temperature；To roll bending carry out it is crosscutting, obtain I-beam steel, wherein the I-beam steel at sub-prime
Amount percentage be C:0.14~0.20wt%, Si:0.10-0.65wt%, Mn:1.1~1.65wt%, Nb:0.02~
0.05wt%, Mo:0.3~0.8wt%, V:0.03~0.15wt%, Ti:0.01~0.04wt%, Al:0.01~
0.06wt%, Cr:0.3~1.0wt%, Ni:0.5~1.0wt%, B:0.0015~0.0025wt%, P :≤0.02wt%, S:
≤ 0.01wt%, N :≤0.008wt%, remaining is Fe and inevitable impurity.By the control to slab heating temperature, protect
The effective thickness for having demonstrate,proved slab is conducive to refine crystal grain；Slab is rolled and carries out cooling and is batched, is conducive to after reinforcing phase transformation
Build up is also beneficial to enhancing precipitating reinforcing effect；And then coil of strip is handled using slow cooling, make the logical volume mechanical property of material
It is more uniform, and so that internal stress is released and is homogenized, so as to improve strip shape quality, be conducive to subsequent heat treatment
The control of plate shape and residual stress；After carrying out smooth and uncoiling processing to coil of strip again, continuous high frequency induction heating is carried out to roll bending
And heat preservation, the rate of heat addition can be improved be conducive to quenching and obtain more tiny martensite and lath of bainite, and is conducive to control
Morphology of carbides in quenching structure；After roll bending quenching, continuous induction tempering heating and heat preservation are carried out to roll bending, improve material
Intensity, be conducive to control material unevenness and guarantee blanking after it is indeformable；It is available thin by the restriction to steel component
Small, uniform tempered structure realizes semitrailer welding I beam steel with good obdurability, welding performance and low temperature punching
Hit the technical effect of toughness.
Although preferred embodiments of the present invention have been described, it is created once a person skilled in the art knows basic
Property concept, then additional changes and modifications can be made to these embodiments.So it includes excellent that the following claims are intended to be interpreted as
It selects embodiment and falls into all change and modification of the scope of the invention.
Obviously, those skilled in the art can carry out various modification and variations without departing from this hair to the embodiment of the present invention
The spirit and scope of bright embodiment.In this way, if these modifications and variations of the embodiment of the present invention belong to the claims in the present invention
And its within the scope of equivalent technologies, then the present invention is also intended to include these modifications and variations.
Claims (10)
1. a kind of semitrailer welding I beam steel, which is characterized in that the ingredient percent of I-beam steel is C:
0.14~0.20wt%, Si:0.10-0.65wt%, Mn:1.1~1.65wt%, Nb:0.02~0.05wt%, Mo:0.3~
0.8wt%, V:0.03~0.15wt%, Ti:0.01~0.04wt%, Al:0.01~0.06wt%, Cr:0.3~1.0wt%,
Ni:0.5~1.0wt%, B:0.0015~0.0025wt%, P :≤0.02wt%, S :≤0.01wt%, N :≤0.008wt%,
Remaining is Fe and inevitable impurity.
2. semitrailer welding I beam steel as described in claim 1, which is characterized in that the ingredient of the I-beam steel
Cooling cracks the susceptible index number Pcm≤0.31.
3. a kind of production method of semitrailer welding I beam steel, which is characterized in that the described method includes:
Slab is obtained using smelting molten steel；
The slab is heated in heating furnace, the temperature of the slab is 1180~1250 DEG C after heating；
Roughing and finish rolling are successively carried out to the slab after heating, obtain hot rolled plate；
After rolling, the hot rolled plate using section cooling and is batched, obtains coil of strip；
Slow cooling processing is carried out to the coil of strip using burial pit, and smooth processing is carried out to coil of strip after slow cooling processing；
After smooth processing, to coil of strip carry out uncoiling processing, obtain roll bending, and to the roll bending carry out continuous high frequency induction heating and
Heat preservation, is quenched to room temperature；
After quenching, continuous induction tempering heating and heat preservation are carried out to roll bending, and carry out air-cooled or air-cooled to room temperature；
Crosscutting, acquisition I-beam steel, wherein the ingredient percent of I-beam steel is C:0.14 is carried out to roll bending
~0.20wt%, Si:0.10-0.65wt%, Mn:1.1~1.65wt%, Nb:0.02~0.05wt%, Mo:0.3~
0.8wt%, V:0.03~0.15wt%, Ti:0.01~0.04wt%, Al:0.01~0.06wt%, Cr:0.3~1.0wt%,
Ni:0.5~1.0wt%, B:0.0015~0.0025wt%, P :≤0.02wt%, S :≤0.01wt%, N :≤0.008wt%,
Remaining is Fe and inevitable impurity.
4. method as claimed in claim 3, which is characterized in that the soaking time of the slab is pressed the effective thickness control of slab
System is arranged within the scope of 1~1.5min/mm.
5. method as claimed in claim 3, which is characterized in that the slab after described pair of heating successively carries out roughing and essence
It rolls, obtains hot rolled plate, comprising:
In 5 times~10 times that the workpiece thickness after the roughing is the hot rolling plate thickness after the finish rolling；
The entry temperature at finishing is 1000 DEG C~1050 DEG C, and finishing temperature is 830~880 DEG C.
6. method as claimed in claim 3, which is characterized in that the coiling temperature batched is 650 DEG C~750 DEG C, described
The thickness specification of coil of strip is 3mm~10mm.
7. method as claimed in claim 3, which is characterized in that the slow cooling time of the slow cooling processing is greater than 72 hours, and eventually
Cool time is the time for controlling coil of strip slow cooling temperature and being lower than 150 DEG C.
8. production method as claimed in claim 3, which is characterized in that the heating temperature of the high-frequency induction heating is 900-
950 DEG C, the rate of heat addition is greater than 150 DEG C/S, and soaking time is less than 10min.
9. production method as claimed in claim 3, which is characterized in that the quenching uses water quenching.
10. production method as claimed in claim 3, which is characterized in that the heating temperature of the tempering heating is 450-650
DEG C, the rate of heat addition is greater than 150 DEG C/S, and soaking time is less than 20min.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201811120779.5A CN109136762A (en) | 2018-09-26 | 2018-09-26 | A kind of semitrailer welding I beam steel and its production method |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201811120779.5A CN109136762A (en) | 2018-09-26 | 2018-09-26 | A kind of semitrailer welding I beam steel and its production method |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CN109136762A true CN109136762A (en) | 2019-01-04 |
Family
ID=64812322
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201811120779.5A Pending CN109136762A (en) | 2018-09-26 | 2018-09-26 | A kind of semitrailer welding I beam steel and its production method |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN109136762A (en) |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2020239671A1 (en) * | 2019-05-27 | 2020-12-03 | Salzgitter Flachstahl Gmbh | Method for producing a welded component made of a deformed high-strength steel, and component produced in this manner |
| CN115198165A (en) * | 2022-06-17 | 2022-10-18 | 首钢集团有限公司 | Method for reducing banded structure of 980 MPa-grade cold-rolled high-strength steel |
| CN116334486A (en) * | 2023-03-22 | 2023-06-27 | 包头钢铁（集团）有限责任公司 | High-strength hot-rolled steel strip with excellent low-temperature impact toughness for automobile and manufacturing method thereof |
Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US20020007876A1 (en) * | 2000-04-07 | 2002-01-24 | Kawasaki Steel Corporation | Ferritic stainless steel |
| CN101602078B (en) * | 2009-07-03 | 2010-12-01 | 马景怡 | Method for manufacturing section steel with high strength and high toughness by using hot-rolling steel plate |
| CN105543666A (en) * | 2015-12-30 | 2016-05-04 | 首钢总公司 | Automobile beam steel with 960 MPa yield strength and production method thereof |
-
2018
- 2018-09-26 CN CN201811120779.5A patent/CN109136762A/en active Pending
Patent Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US20020007876A1 (en) * | 2000-04-07 | 2002-01-24 | Kawasaki Steel Corporation | Ferritic stainless steel |
| CN101602078B (en) * | 2009-07-03 | 2010-12-01 | 马景怡 | Method for manufacturing section steel with high strength and high toughness by using hot-rolling steel plate |
| CN105543666A (en) * | 2015-12-30 | 2016-05-04 | 首钢总公司 | Automobile beam steel with 960 MPa yield strength and production method thereof |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2020239671A1 (en) * | 2019-05-27 | 2020-12-03 | Salzgitter Flachstahl Gmbh | Method for producing a welded component made of a deformed high-strength steel, and component produced in this manner |
| CN115198165A (en) * | 2022-06-17 | 2022-10-18 | 首钢集团有限公司 | Method for reducing banded structure of 980 MPa-grade cold-rolled high-strength steel |
| CN116334486A (en) * | 2023-03-22 | 2023-06-27 | 包头钢铁（集团）有限责任公司 | High-strength hot-rolled steel strip with excellent low-temperature impact toughness for automobile and manufacturing method thereof |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN110093552B (en) | High-strength-ductility Q & P steel plate with excellent welding performance and preparation method thereof | |
| EP1808505B1 (en) | Cold rolled high strength thin-gauge steel sheet excellent in elongation and hole expandibility | |
| CN109402499A (en) | A kind of protection steel and its production method | |
| CN111172466B (en) | Plasticity-enhanced cold-rolled dual-phase steel with tensile strength of 590MPa and production method thereof | |
| CN109778062B (en) | Cold-rolled complex phase steel with tensile strength of 1200MPa and preparation method thereof | |
| CN110106322B (en) | High-strength steel for thin engineering machinery and plate shape control method | |
| CN106756612B (en) | A kind of easy laser welding hull plate steel of bainite/martensite/austenite high-ductility and manufacture method | |
| CN110358970B (en) | Welded structure bainite high-strength steel with yield strength of 1100MPa and preparation method thereof | |
| CN105543666B (en) | A kind of yield strength 960MPa beam steels and its production method | |
| CN108998726B (en) | Thick 420 MPa-grade low-yield-ratio low-temperature bridge steel and production method thereof | |
| CN109136762A (en) | A kind of semitrailer welding I beam steel and its production method | |
| CN110747405B (en) | One-thousand-megapascal-grade cold-rolled bainite steel plate suitable for rolling and preparation method thereof | |
| CN115094322A (en) | 80 mm-thick 690 MPa-grade ultrahigh-strength and toughness marine steel plate and preparation method thereof | |
| CN113802060A (en) | Low-cost steel plate for engineering structure and manufacturing method thereof | |
| CN107267859B (en) | A kind of strong armour plate of superelevation and preparation method thereof | |
| KR102209555B1 (en) | Hot rolled and annealed steel sheet having low strength-deviation, formed member, and manufacturing method of therefor | |
| CN114934228B (en) | Hot-formed steel plate and production method thereof | |
| CN115261717B (en) | 1800 MPa-grade high-strength self-toughening steel plate for protection and manufacturing method thereof | |
| KR20120087619A (en) | Hot-rolled steel sheet, method of manufacturing the hot-rolled steel sheet and method of manufacturing oil tubular country goods using the hot-rolled steel sheet | |
| JP2621744B2 (en) | Ultra-high tensile cold rolled steel sheet and method for producing the same | |
| KR101076082B1 (en) | Hot-rolled steel sheet having ultra-high strength, and method for producing the same | |
| CN110117756A (en) | A kind of Cu alloying deep-draw dual phase sheet steel and preparation method thereof | |
| WO2024103499A1 (en) | High-strength steel, zinc-aluminum-magnesium coated steel, automobile part and preparation method | |
| CN115478210B (en) | 1500 MPa-grade high-strength self-toughening protective steel plate and manufacturing method thereof | |
| KR102245228B1 (en) | Steel sheet having excellent uniform elongation and strain hardening rate and method for manufacturing thereof |
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 |
Application publication date: 20190104 |
|
| RJ01 | Rejection of invention patent application after publication |