CN109252109A - A kind of low-carbon baking hardened steel and its production method - Google Patents
A kind of low-carbon baking hardened steel and its production method Download PDFInfo
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- CN109252109A CN109252109A CN201811219364.3A CN201811219364A CN109252109A CN 109252109 A CN109252109 A CN 109252109A CN 201811219364 A CN201811219364 A CN 201811219364A CN 109252109 A CN109252109 A CN 109252109A
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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
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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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
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
- C21D8/0273—Final recrystallisation annealing
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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
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
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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
- C22C38/10—Ferrous alloys, e.g. steel alloys containing cobalt
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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
- C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
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Abstract
The invention discloses a kind of low-carbon baking hardened steel and its production methods, the ingredient percent of the carbon baking hardened steel is C:0.015-0.021wt%, Mn:0.2-0.3wt%, Si :≤0.03wt%, P:0.02-0.03wt%, S:0.005-0.015wt%, Al:0.03-0.06%wt%, N≤0.003%wt%, Cu:0.002-0.015wt%, B:0.0005-0.001wt%, Co:0.001-0.002wt%, remaining is Fe and inevitable impurity.Solving low-carbon baking hardened steel in the prior art will lead to subsequent flattening process there are longer yield point elongation and is difficult to eliminate, and it is easy to occur elongation strain scar defect in stamping use process, the technical issues of influencing outer plate surfaces quality, the low-carbon baking hardened steel that the production under non-formation state has shorter yield point elongation length is reached, subsequent smooth process difficulty in actual production is reduced, the technical effect for occurring elongation strain trace defect in punching press use process is eliminated.
Description
Technical field
The present invention relates to metal material processing technical field, in particular to a kind of low-carbon baking hardened steel and its producer
Method.
Background technique
Low-carbon baking hardened steel is that a kind of intensity is relatively high (yield strength > 220MPa or more), by stamping
Afterwards, after by baking vanish temperature ageing treatment, the available high quality car steel plate improved to a certain degree of yield strength.Due to low
The characteristic of carbon baking hardened steel, this product can have longer yield point elongation (general > 6%) after heat treatment.
It is difficult to since low-carbon baking hardened steel in the prior art will lead to subsequent flattening process there are longer yield point elongation
It eliminates, and is easy to occur elongation strain scar defect in stamping use process, the technology for influencing outer plate surfaces quality is asked
Topic.
Summary of the invention
The embodiment of the invention provides a kind of low-carbon baking hardened steel and its production methods, low in the prior art to solve
Carbon baking hardened steel will lead to subsequent flattening process there are longer yield point elongation and be difficult to eliminate, and be easy in stamping use
The technical issues of occurring elongation strain scar defect in the process, influencing outer plate surfaces quality has reached raw under non-formation state
The low-carbon baking hardened steel with shorter yield point elongation length is produced, subsequent smooth process difficulty in actual production is reduced, is eliminated
Occurs the technical effect of elongation strain trace defect in punching press use process.
To solve the above-mentioned problems, in a first aspect, the embodiment of the invention provides a kind of carbon baking hardened steel, the carbon dries
The ingredient percent of roasting hardened steel is C:0.015-0.021wt%, Mn:0.2-0.3wt%, Si :≤0.03wt%, P:
0.02-0.03wt%, S:0.005-0.015wt%, Al:0.03-0.06%wt%, N≤0.003%wt%, Cu:0.002-
0.015wt%, B:0.0005-0.001wt%, Co:0.001-0.002wt%, remaining is Fe and inevitable impurity.
Second aspect, the embodiment of the invention provides a kind of production methods of low-carbon baking hardened steel, which comprises
Continuous casting billet is obtained using smelting molten steel；Hot rolling is carried out to the continuous casting billet and obtains strip；After hot rolling, the strip is carried out
It cools down and batches, obtain band coil of strip；The strip is rolled up and carries out cold rolling；After cold rolling, the strip feeding in room temperature is moved back
Continuous annealing is carried out in stove, wherein strip is successively heated to 220 DEG C at the first time, and the second time was heated to 770~
810 DEG C, and the second soaking time is 71~75S, is cooled to 630~650 DEG C through the third time, is cooled to 330 through the 4th time
DEG C, 450 DEG C are heated to through the 5th time, the 6th time was cooled to 430 DEG C, and water cooling to room temperature obtains the carbon baking hardening
Steel, wherein the ingredient percent of the carbon baking hardened steel be C:0.015-0.021wt%, Mn:0.2-0.3wt%,
Si :≤0.03wt%, P:0.02-0.03wt%, S:0.005-0.015wt%, Al:0.03-0.06%wt%, N≤0.003%
Wt%, Cu:0.002-0.015wt%, B:0.0005-0.001wt%, Co:0.001-0.002wt%, remaining is Fe and can not
The impurity avoided.
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 low-carbon baking hardened steel and its production method, the method uses smelting molten steel
Obtain continuous casting billet；Hot rolling is carried out to the continuous casting billet and obtains strip；After hot rolling, the strip is cooled down and is batched,
Obtain band coil of strip；The strip is rolled up and carries out cold rolling；After cold rolling, the strip in room temperature is sent into annealing furnace and is connected
Continuous annealing, wherein strip is successively heated to 220 DEG C at the first time, and the second time was heated to 770~810 DEG C, and second protects
The warm time is 71~75S, is cooled to 630~650 DEG C through the third time, is cooled to 330 DEG C through the 4th time, adds through the 5th time
For heat to 450 DEG C, the 6th time was cooled to 430 DEG C, and water cooling to room temperature obtains the carbon baking hardened steel, wherein the carbon dries
The ingredient percent of roasting hardened steel is C:0.015-0.021wt%, Mn:0.2-0.3wt%, Si :≤0.03wt%, P:
0.02-0.03wt%, S:0.005-0.015wt%, Al:0.03-0.06%wt%, N≤0.003%wt%, Cu:0.002-
0.015wt%, B:0.0005-0.001wt%, Co:0.001-0.002wt%, remaining is Fe and inevitable impurity.Pass through
The content of C, the content of Al and N in control composition, may be implemented subsequent rapid cooling process medium pearlite with disperse state graininess
It is precipitated, while N atom is sufficiently precipitated in the form of AlN compound, in the follow-up process using quick after recrystallization annealing soaking
Cooling then heating and held for some time, realization carbide are sufficiently precipitated with Dispersed precipitate state rapidly again, hence it is evident that are shortened
Low-carbon baking hardened steel yield point elongation length within 3%, draw in punching press use process by elimination under non-formation state
The technical effect of stretching strain trace defect.
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 flow chart of the production method of low-carbon baking hardened steel in this specification embodiment；
Fig. 2 is the microstructure schematic diagram of low-carbon baking hardened steel in this specification embodiment.
Specific embodiment
The embodiment of the invention provides a kind of low-carbon baking hardened steel and its production methods, low in the prior art to solve
Carbon baking hardened steel will lead to subsequent flattening process there are longer yield point elongation and be difficult to eliminate, and be easy in stamping use
The technical issues of occurring elongation strain scar defect in the process, influencing outer plate surfaces quality has reached raw under non-formation state
The low-carbon baking hardened steel with shorter yield point elongation length is produced, subsequent smooth process difficulty in actual production is reduced, is eliminated
Occurs the technical effect of elongation strain trace defect in punching press use process.
Technical solution in the embodiment of the present invention, the method obtain continuous casting billet using smelting molten steel；To the continuous casting billet
It carries out hot rolling and obtains strip；After hot rolling, the strip is cooled down and batched, obtains band coil of strip；To the band coil of strip
Carry out cold rolling；After cold rolling, the strip in room temperature is sent into annealing furnace and carries out continuous annealing, wherein strip successively passes through
220 DEG C are heated at the first time, the second time was heated to 770~810 DEG C, and the second soaking time is 71~75S, through third
Time is cooled to 630~650 DEG C, is cooled to 330 DEG C through the 4th time, is heated to 450 DEG C through the 5th time, cold through the 6th time
But to 430 DEG C, water cooling to room temperature obtains the carbon baking hardened steel, wherein the composition quality percentage of the carbon baking hardened steel
Than for C:0.015-0.021wt%, Mn:0.2-0.3wt%, Si :≤0.03wt%, P:0.02-0.03wt%, S:0.005-
0.015wt%, Al:0.03-0.06%wt%, N≤0.003%wt%, Cu:0.002-0.015wt%, B:0.0005-
0.001wt%, Co:0.001-0.002wt%, remaining is Fe and inevitable impurity.To solve low-carbon in the prior art
Baking hardened steel will lead to subsequent flattening process there are longer yield point elongation and be difficult to eliminate, and be easy to use stamping
The technical issues of occurring elongation strain scar defect in journey, influencing outer plate surfaces quality, has reached and has produced under non-formation state
Low-carbon baking hardened steel with shorter yield point elongation length reduces subsequent smooth process difficulty in actual production, eliminates
Occurs the technical effect of elongation strain trace defect in punching press use process.
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 low-carbon baking hardened steels, referring to FIG. 2, the ingredient of the carbon baking hardened steel
Mass percent is C:0.015-0.021wt%, Mn:0.2-0.3wt%, Si :≤0.03wt%, P:0.02-0.03wt%, S:
0.005-0.015wt%, Al:0.03-0.06%wt%, N≤0.003%wt%, Cu:0.002-0.015wt%, B:
0.0005-0.001wt%, Co:0.001-0.002wt%, remaining is Fe and inevitable impurity.
Further, the mass percent ratio of Al/N is greater than 10 in the ingredient of the carbon baking hardened steel.
Specifically, the ingredient percent of carbon baking hardened steel described in the embodiment of the present application is as follows, wherein C is solid
Molten reinforcing improves yield strength, reduces elongation percentage, and the mass percent of C is 0.015-0.021wt%, and Mn is common solid solution
Yield strength can be improved in intensified element, therefore controlling in 0.2-0.3wt%, Si is deoxidant element, the solution strengthening in steel, control
So that steel is become fragile hereinafter, P is easy in 0.03wt%, influences toughness, control influences the low-temperature flexibility of steel in 0.02-0.03wt%, S,
Control in 0.005-0.015wt%, Al deoxidation must element, while will form AlN and being mingled with, improve intensity, control exists
The N of 0.03-0.06%wt%, N solid solution can improve intensity, and control is in 0.003%wt% hereinafter, the quality of other metallic elements Cu
Percentage is 0.002-0.015wt%, and the mass percent of B is 0.0005-0.001wt%, and the mass percent of Co is
0.001-0.002wt%, remaining is Fe and inevitable impurity.Wherein, C content in the ingredient of continuous casting billet is controlled to exist
Between 0.015%-0.021%, and the content of Al and N in control composition being needed, the mass percent ratio for controlling Al/N is greater than 10,
Its purpose is to realize that subsequent rapid cooling process medium pearlite is precipitated with disperse state graininess, while N atom is with AlN chemical combination
The form of object is sufficiently precipitated, and as can be seen from Figure 2 Carbide Precipitation point is more, is precipitated abundant.It ensure that and give birth in the subsequent process
The low-carbon baking hardened steel of production has yield point elongation shorter under not smooth state.
Preferably, a part of ingredient percent of the carbon baking hardened steel is preferably C:0.016-
0.020wt%, Mn:0.25-0.3wt%, Si :≤0.03wt%, P:0.02-0.03wt%, S:0.005-0.012wt%, Al:
0.03-0.06%wt%, N≤0.025%wt%.Or, a part of ingredient percent of the carbon baking hardened steel can be excellent
It is selected as C:0.015-0.019wt%, Mn:0.25-0.3wt%, Si :≤0.03wt%, P:0.02-0.03wt%, S:0.005-
0.01wt%, Al:0.035-0.06%wt%, N≤0.003%wt%.The carbon baking hardened steel of the ingredient has excellent
Mechanical property, and subsequent smooth process difficulty in actual production is reduced, there is elongation strain in punching press use process in elimination
Trace defect
Embodiment two
The embodiment of the invention provides a kind of production methods of low-carbon baking hardened steel, referring to FIG. 1, the method packet
It includes:
Step 110: continuous casting billet is obtained using smelting molten steel；
Specifically, by set component smelting molten steel and pouring into continuous casting billet in the embodiment of the present application.Wherein, continuous casting billet is
The product that the molten steel that converter is smelt obtains after conticaster is cast.
Step 120: hot rolling being carried out to the continuous casting billet and obtains strip.
Step 130: after hot rolling, the strip being cooled down and batched, obtain band coil of strip.
Further, the heating temperature of the hot rolling is at 1120~1180 DEG C, and finishing temperature is at 890~930 DEG C.Further
, the oiler temperature control batched is at 690~730 DEG C.
Specifically, the heating temperature of setting continuous casting billet carries out hot rolling, wherein hot rolling uses continuous casting steel billet or plate slab
Make raw material, through stepped heating stove heating, after high pressure water dephosphorization enter roughing mill, roughing material through cutting head, tail, enter back into finish rolling
Machine implements computer controlled rolling, batched by section cooling (computer control cooling rate) and coiling machine after finish to gauge, at
For straight hair volume.By straight hair volume after the processing of the finishing lines such as the aligning of cutting head, back-end crop, trimming and multi-pass, smooth, then cutting plate or again
Volume, becomes the products such as hot rolled steel plate, smooth coils of hot-rolled steel, longitudinal sectional band.Hot rolling can destroy the cast sturcture of steel ingot, refine steel
The crystal grain of material, and the defect of microscopic structure is eliminated, to keep steel tissue closely knit, mechanical property is improved.This improvement master
It is embodied in rolling direction, so that steel be made no longer to be ergodicity to a certain extent；The bubble that is formed when casting,
Crackle and loose, can also be under the effect of high moderate pressure by the effect of soldering.The heating temperature of hot rolling is set in the embodiment of the present application
Degree controls finishing temperature at 890~930 DEG C, i.e. finish rolling terminates temperature at 1120~1180 DEG C.After hot rolling, to the band
Steel is cooled down, can be by the way of section cooling, and carries out batching acquisition band coil of strip to strip, wherein oiler temperature control
At 690~730 DEG C.
Step 140: the strip being rolled up and carries out cold rolling.
Further, the cold rolling reduction ratio of the cold rolling is arranged 75%~78%.
Cold rolling is carried out specifically, rolling up to the strip, wherein cold rolling uses coils of hot-rolled steel for raw material, removes through pickling
Carry out cold continuous rolling after oxide skin, finished product is to roll hard volume, the flow harden due to caused by continuous cold deformation make to roll the intensity rolled up firmly,
Hardness rises, tough modeling index declines, and punching performance deteriorates, therefore is only used for the part of simple deformation.General cold continuous rolling plate, cold company
Rolling volume by continuous annealing (CAPL unit) or bell furnace should all make annealing treatment, and eliminate flow harden and rolling stress,
Reach mechanical performance index as defined in standard.Surface quality, appearance, the dimensional accuracy of cold-rolled steel sheet are superior to hot rolled plate.Cold rolling
It is fast with shaping speed, yield is high, and does not damage coating, can be made diversified section form, to adapt to use condition
Needs；And cold rolling can make steel generate very big plastic deformation, to improve the yield point of steel.Certain cold rolling
Lower rate is the driving force of subsequent continuous annealing recrystallization, and determines the amount of Recrystallization nucleation point.Basis in the embodiment of the present application
Different steel strip thickness specifications, the level by the control of cold rolling reduction ratio 75%~78%.
Step 150: after cold rolling, the strip in room temperature being sent into annealing furnace and carries out continuous annealing, wherein strip
It is successively heated to 220 DEG C at the first time, the second time was heated to 770~810 DEG C, and the second soaking time is 71~75S,
630~650 DEG C are cooled to through the third time, is cooled to 330 DEG C through the 4th time, 450 DEG C are heated to through the 5th time, through the 6th
Time is cooled to 430 DEG C, and water cooling to room temperature obtains carbon baking hardened steel, wherein the composition quality hundred of the carbon baking hardened steel
Divide than being C:0.015-0.021wt%, Mn:0.2-0.3wt%, Si :≤0.03wt%, P:0.02-0.03wt%, S:0.005-
0.015wt%, Al:0.03-0.06%wt%, N≤0.003%wt%, Cu:0.002-0.015wt%, B:0.0005-
0.001wt%, Co:0.001-0.002wt%, remaining is Fe and inevitable impurity.
Further, the medium in the annealing furnace is made of hydrogen and nitrogen.
Further, the first time in the continuous annealing be 12~14S, second time be 212~
280S, the third time be 21~25S, the 4th time be 3~4S, the 5th time be 21~23S, the described 6th
Time is 252~255S.
Specifically, the strip in room temperature is sent into continuous annealing furnace and carries out continuous annealing after cold rolling, it is described
The non-oxidizing atmosphere that medium in annealing furnace is made of hydrogen and nitrogen.Wherein, continuous annealing is with respect to for bell-type annealing
, continuous annealing is that strip continues through annealing furnace, the life that annealing furnace is directly batched without sealing, strip without stop
Production mode, and continuous annealing makes deformed grains be re-converted to uniform equi-axed crystal, while eliminating and answering in processing hardening and residual
Power, the heat treatment process of state before the tissue and performance recovery to cold deformation of steel.It is passed through in non-oxidizing atmosphere in annealing furnace
12~14S is heated to 220 DEG C at the first time, is heated to 770~810 DEG C through second 212~280S of time, this process microscopic fibers
It is gradually recrystallized after strip crystal grain is heated, and the second soaking time is 71~75S, this process makes low-carbon baking hardening
The abundant back dissolving of steel carbide is into ferrite matrix.630~650 DEG C are cooled to through 21~25S of third time, through the 4th time 4S
330 DEG C are quickly cooled to, is heated to 450 DEG C through the 5th 21~23S of time, the 6th time 252~255 was cooled to 430 DEG C, in fact
It is sufficiently precipitated in temperature-rise period after the existing rapid super saturated solid solution of carbide and rapid cooling, obtaining carbide microstructure is
It is granular to be uniformly distributed on ferrite crystal grain, extremely so as to shorten low-carbon baking hardened steel yield point elongation length under non-formation state
Within 3%, yield point elongation can be eliminated using lesser smooth amount in subsequent industrial production, reduced in actual production
Subsequent smooth process difficulty, and the ingredient percent of low-carbon baking hardened steel is C:0.015-0.021wt%, Mn:0.2-
0.3wt%, Si :≤0.03wt%, P:0.02-0.03wt%, S:0.005-0.015wt%, Al:0.03-0.06%wt%, N
≤ 0.003%wt%, Cu:0.002-0.015wt%, B:0.0005-0.001wt%, Co:0.001-0.002wt%, remaining is
Fe and inevitable impurity, in 285MPa or more, tensile strength reaches the yield strength of the low-carbon baking hardened steel of the ingredient
To 360MPa or more, elongation percentage is 30% or more.
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 low-carbon baking hardened steel and its production method, the method uses smelting molten steel
Obtain continuous casting billet；The ingredient percent of the continuous casting billet is C:0.015-0.021wt%, Mn:0.2-0.3wt%, Si :≤
0.03wt%, P:0.02-0.03wt%, S:0.005-0.015wt%, Al:0.03-0.06%wt%, N≤0.003%wt%,
Cu:0.002-0.015wt%, B:0.0005-0.001wt%, Co:0.001-0.002wt%, remaining is for Fe and inevitably
Impurity；Hot rolling is carried out to the continuous casting billet and obtains strip；After hot rolling, the strip is cooled down and batched, obtains band
Coil of strip；The strip is rolled up and carries out cold rolling；After cold rolling, the strip in room temperature is sent into annealing furnace and is continuously moved back
Fire, wherein strip is successively heated to 220 DEG C at the first time, and the second time was heated to 770~810 DEG C, and when the second heat preservation
Between be 71~75S, be cooled to 630~650 DEG C through the third time, be cooled to 330 DEG C through the 4th time, be heated to through the 5th time
450 DEG C, the 6th time was cooled to 430 DEG C, and water cooling to room temperature obtains carbon baking hardened steel.Contained by C in control composition
Amount, Al and N content, may be implemented subsequent rapid cooling process medium pearlite with disperse state graininess precipitation, while N atom with
The form of AlN compound is sufficiently precipitated, and is then heated again using being quickly cooled down after recrystallization annealing soaking in the follow-up process
And held for some time, realize that carbide is sufficiently precipitated with Dispersed precipitate state rapidly, hence it is evident that shorten low-carbon under non-formation state
Baking hardened steel yield point elongation length eliminates the technology for occurring elongation strain trace defect in punching press use process within 3%
Effect.
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 (8)
1. a kind of low-carbon baking hardened steel, which is characterized in that the ingredient percent of the carbon baking hardened steel is C:
0.015-0.021wt%, Mn:0.2-0.3wt%, Si :≤0.03wt%, P:0.02-0.03wt%, S:0.005-
0.015wt%, Al:0.03-0.06%wt%, N≤0.003%wt%, Cu:0.002-0.015wt%, B:0.0005-
0.001wt%, Co:0.001-0.002wt%, remaining is Fe and inevitable impurity.
2. the method as described in claim 1, which is characterized in that the quality percentage of Al/N in the ingredient of the carbon baking hardened steel
It is greater than 10 than ratio.
3. a kind of production method of low-carbon baking hardened steel, which is characterized in that the described method includes:
Continuous casting billet is obtained using smelting molten steel；
Hot rolling is carried out to the continuous casting billet and obtains strip；
After hot rolling, the strip is cooled down and batched, obtains band coil of strip；
The strip is rolled up and carries out cold rolling；
After cold rolling, will in room temperature strip be sent into annealing furnace in carries out continuous annealing, wherein strip successively through first when
Between be heated to 220 DEG C, the second time was heated to 770~810 DEG C, and the second soaking time is 71~75S, cold through the third time
But to 630~650 DEG C, 330 DEG C are cooled to through the 4th time, 450 DEG C is heated to through the 5th time, is cooled to through the 6th time
430 DEG C, water cooling to room temperature obtains the carbon baking hardened steel, wherein the ingredient percent of the carbon baking hardened steel is
C:0.015-0.021wt%, Mn:0.2-0.3wt%, Si :≤0.03wt%, P:0.02-0.03wt%, S:0.005-
0.015wt%, Al:0.03-0.06%wt%, N≤0.003%wt%, Cu:0.002-0.015wt%, B:0.0005-
0.001wt%, Co:0.001-0.002wt%, remaining is Fe and inevitable impurity.
4. method as claimed in claim 3, which is characterized in that the heating temperature of the hot rolling is at 1120~1180 DEG C, finish to gauge
Temperature is at 890~930 DEG C.
5. method as claimed in claim 3, which is characterized in that the oiler temperature control batched is at 690~730 DEG C.
6. method as claimed in claim 3, which is characterized in that the cold rolling reduction ratio of the cold rolling is arranged 75%~78%.
7. method as claimed in claim 3, which is characterized in that the medium in the annealing furnace is made of hydrogen and nitrogen.
8. method as claimed in claim 3, which is characterized in that the first time in the continuous annealing is 12~14S,
Second time is 212~280S, and the third time is 21~25S, and the 4th time is 3~4S, when the described 5th
Between be 21~23S, the 6th time be 252~255S.
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN113667895A (en) * | 2021-08-19 | 2021-11-19 | 安钢集团冷轧有限责任公司 | Method for eliminating tensile strain marks of cold-rolled sheet for stamping |
Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5974232A (en) * | 1982-10-20 | 1984-04-26 | Nippon Steel Corp | Production of bake hardenable galvanized steel sheet for ultradeep drawing having extremely outstanding secondary processability |
| CN104561789A (en) * | 2015-01-22 | 2015-04-29 | 首钢总公司 | Ultra-low carbon bake-hardened steel having aging index of lower than 20MPa and production method of steel |
| CN105112776A (en) * | 2015-08-25 | 2015-12-02 | 上海梅山钢铁股份有限公司 | Phosphorus-containing low-carbon cold-rolled hard tin-plated steel plate and production method thereof |
| CN107747033A (en) * | 2017-10-23 | 2018-03-02 | 攀钢集团攀枝花钢铁研究院有限公司 | Baking hardening hot-dip galvanizing sheet steel of excellent shaping and preparation method thereof |
-
2018
- 2018-10-19 CN CN201811219364.3A patent/CN109252109B/en active Active
Patent Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5974232A (en) * | 1982-10-20 | 1984-04-26 | Nippon Steel Corp | Production of bake hardenable galvanized steel sheet for ultradeep drawing having extremely outstanding secondary processability |
| CN104561789A (en) * | 2015-01-22 | 2015-04-29 | 首钢总公司 | Ultra-low carbon bake-hardened steel having aging index of lower than 20MPa and production method of steel |
| CN105112776A (en) * | 2015-08-25 | 2015-12-02 | 上海梅山钢铁股份有限公司 | Phosphorus-containing low-carbon cold-rolled hard tin-plated steel plate and production method thereof |
| CN107747033A (en) * | 2017-10-23 | 2018-03-02 | 攀钢集团攀枝花钢铁研究院有限公司 | Baking hardening hot-dip galvanizing sheet steel of excellent shaping and preparation method thereof |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN113667895A (en) * | 2021-08-19 | 2021-11-19 | 安钢集团冷轧有限责任公司 | Method for eliminating tensile strain marks of cold-rolled sheet for stamping |
| CN113667895B (en) * | 2021-08-19 | 2023-01-20 | 安钢集团冷轧有限责任公司 | Method for eliminating tensile strain marks of cold-rolled sheet for stamping |
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