CN106480355A - Pressure vessel hot rolled steel plate and its manufacture method - Google Patents
Pressure vessel hot rolled steel plate and its manufacture method Download PDFInfo
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- CN106480355A CN106480355A CN201510885586.9A CN201510885586A CN106480355A CN 106480355 A CN106480355 A CN 106480355A CN 201510885586 A CN201510885586 A CN 201510885586A CN 106480355 A CN106480355 A CN 106480355A
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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
- 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
-
- 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
- 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
- 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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/005—Ferrite
-
- 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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/009—Pearlite
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- 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)
- Heat Treatment Of Sheet Steel (AREA)
Abstract
The present invention relates to a kind of pressure vessel hot rolled steel plate and its manufacture method.More specifically, the present invention provides a kind of hot rolled steel plate, wherein total with respect to hot rolled steel plate 100 weight %, comprise C：0.1 weight % is to 0.2 weight %, Si：(do not comprise 0 weight %) below 0.5 weight %, Mn：0.5 weight % is to 1.5 weight %, P：(do not comprise 0 weight %) below 0.03 weight %, S：(do not comprise 0 weight %) below 0.015 weight %, Al：(do not comprise 0 weight %) below 0.05 weight %, N：(0 weight % is not comprised) below 0.01 weight %, balance of Fe and other inevitably impurity, described hot rolled steel plate is made up of pearlite and ausferrite microstructure, gross score 100% with respect to described hot rolled steel plate microscopic structure, the volume fraction of described ferritic structure is 75% to 85%, and the equiaxial crystal ratio of described ausferrite microstructure is 0.7 to 1.3.
Description
Technical field
The present invention relates to a kind of pressure vessel hot rolled steel plate and its manufacture method.More specifically, the present invention
It is related to a kind of intensity and the excellent pressure vessel hot rolled steel plate of ductility and its manufacture method.
Background technology
For the pressure vessels such as liquified gas container, based in the burst test of hydraulic pressure after making container
Fracture pressure is extremely important.Therefore, the intensity of the hot rolled steel plate at this moment being used is significant variable.For this reason,
Generally the addition steel impurity content such as C, Si, Mn, Ti, Nb, Mo and V is reduced to minimum High Purity Steel
In, to be used in the hot rolled steel plate making container, there is high intensity.
At present, in order to manufacture high tensile hot rolled steel sheet, Ti, Nb, V, Mo etc. is added to utilize these elements
Precipitation strength manufacturing hot rolled steel plate, or a large amount of add Cr or Mn etc. guaranteeing intensity, or logical
Cross and the steel adding Mn and Cr is carried out by temper annealing (temper annealing) carrys out intensifying impact intensity
And tensile properties.
However, recently because the security legislation such as container explosion accident is strengthened, the safety law after strengthening
Under rule, not only standard is provided with to the fracture pressure in burst test, have also appeared and volume of a container is expanded
The standard of rate.Therefore, in order to meet the security legislation to pressure vessel being reinforced, it is not only steel, just
Even hot rolled steel plate also requires that there is excellent ductility.Its focus of above prior art is only that by base
Close in the solution strengthening of the alloying components such as C, Si, Mn, Cr, Mo and W or based on Ti, Nb, Mo etc.
The precipitation strength of golden composition reaching high intensity, therefore for the extension for guaranteeing volume of a container expansion rate
Property improve be conditional.
In addition, in hot rolling technology, the key factor of impact steel plate material may be exit temperature at finishing
(Final Delivery Temperature, hereinafter referred to as FDT), coiling temperature (Coiling
Temperature, hereinafter referred to as CT) and be to join in runout table (Run Out Table, ROT)
Close the refrigerating mode of coiling temperature (CT).
Particularly, in the period by runout table (ROT), hot rolled steel plate is led to through forcing cooling
Phase transition process, may have last phase (phase).This phase transition process can be subject to temperature and time
Impact, even if therefore having identical exit temperature at finishing (FDT) and coiling temperature (CT), also can
There is because of refrigerating mode not homophase, and then affect material.Conventional hot rolling is carried out continuously after finish to gauge terminates
Cooling is up to coiling temperature, thus cannot form isometry ferrite, there is poor ductility.
Content of the invention
Technical problem
The present invention provides a kind of pressure vessel hot rolled steel plate and its manufacture method.
Technical scheme
According to the hot rolled steel plate of the present invention, wherein total with respect to hot rolled steel plate 100 weight %, C can be comprised：
0.1 weight % is to 0.2 weight %, Si：(do not comprise 0 weight %) below 0.5 weight %, Mn：0.5 weight
Amount % to 1.5 weight %, P：(do not comprise 0 weight %) below 0.03 weight %, S：0.015 weight %
(do not comprise 0 weight %) below, Al：(do not comprise 0 weight %) below 0.05 weight %, N：0.01
(0 weight % is not comprised), balance of Fe and other inevitably impurity below weight %.
Described other inevitably impurity can comprise Cr：(do not comprise 0 weight %) below 0.3 weight %,
Ni：(do not comprise 0 weight %) below 0.3 weight %, Mo：(do not comprise 0 weight %) below 0.2 weight %,
Cu：(0 weight % is not comprised) below 0.1 weight %.
Furthermore, described hot rolled steel plate can be made up of pearlite and ausferrite microstructure, with respect to described heat
The gross score 100% of rolled steel plate microscopic structure, the volume fraction of described ferritic structure can be 75% to 85%,
The volume fraction of described pearlitic structrure can be 15% to 25%.
The equiaxial crystal ratio (aspect ratio) of described ausferrite microstructure can be 0.7 to 1.3.
The yield strength of the hot rolled steel plate according to described feature can be 295MPa to 520MPa, yield strength
The value of × percentage elongation can be more than 11,500 and 17,500.
The present invention additionally provides a kind of hot rolled steel plate manufacture method, it may include following steps：Prepare steel billet,
With respect to 100 total weight %, described steel billet comprises C：0.1 weight % to 0.2 weight %, S i：0.5
(do not comprise 0 weight %) below weight %, Mn：0.5 weight % is to 1.5 weight %, P：0.03 weight %
(do not comprise 0 weight %) below, S：(do not comprise 0 weight %) below 0.015 weight %, Al：0.05
(do not comprise 0 weight %) below weight %, N：(0 weight % is not comprised) below 0.01 weight %, remaining
Measure as Fe and other inevitably impurity；Described steel billet is carried out at 1100 DEG C to 1300 DEG C add again
Heat；Roughing is carried out to the described steel billet heating again；Finish to gauge is carried out to the steel billet of described roughing；To described end
The sheet material rolling is cooled down；And batch the sheet material of described cooling and obtain hot rolled steel plate.
Simply, the step sheet material of described finish to gauge being cooled down, it may include following steps：To described end
The sheet material rolling carries out cooling down for the first time with the speed of 40 DEG C/s to 60 DEG C/s；And it is cold to described first time
But sheet material carries out second cooling with the speed of 1 DEG C/s to 8 DEG C/s.
In addition, described other inevitably impurity can comprise Cr：(0 is not comprised below 0.3 weight %
Weight %), Ni：(do not comprise 0 weight %) below 0.3 weight %, Mo：(do not wrap below 0.2 weight %
Containing 0 weight %), Cu：(0 weight % is not comprised) below 0.1 weight %.
First, in the step that described steel billet is heated at 1100 DEG C to 1300 DEG C again, described steel
Base can be reheated 100 minutes to 400 minutes.Afterwards, it is possible to implement the described steel billet heating again is entered
The step of row roughing.
More specifically, the step carrying out finish to gauge in the steel billet to described roughing, described finish to gauge can be in A1-20℃
To A1Implement within the temperature range of+20 DEG C, described A1As shown in formula (1).
A1=932.1-392.8 [C] -61.9 [Mn]+43.9 [Si]+420.6 [P]+220.0 [Al] -15.5 [Cr
] -15.2 [Ni]+31.5 [Mo] -20 [Cu] --- --- --- --- --- --- ----formula (1)
In formula (1), described [C], [Mn], [Si], [P], [Al], [Cr], [Ni], [Mo]
And [Cu] represents weight % of respective component content.
Step by carrying out finish to gauge to the steel billet of described roughing, the steel billet of described finish to gauge can have size and be
10 μm to 40 μm of austenitic microstructure.
The step that the sheet material of described finish to gauge is cooled down, it may include following steps：Plate to described finish to gauge
Material carries out cooling down for the first time with the speed of 40 DEG C/s to 60 DEG C/s；And the plate to the cooling of described first time
Material carries out second cooling with the speed of 1 DEG C/s to 8 DEG C/s.
More specifically, being carried out for the first time with the speed of 40 DEG C/s to 60 DEG C/s in the sheet material to described finish to gauge
In the step of cooling, the sheet material of described finish to gauge can be cooled to A2- 20 DEG C to A2+ 20 DEG C of temperature range,
Described A2As shown in formula (2).
A2=740.1-35.4 [C] -64.5 [Mn]+29.1 [Si]+16.9 [Cr] -16.9 [Ni] --- --- --- -
- formula (2)
In formula (2), described [C], [Mn], [Si], [Cr] and [Ni] represent respective component content
Weight %.
In the sheet material that described first time is cooled down, second cooling is carried out with the speed of 1 DEG C/s to 8 DEG C/s
In step, the sheet material of described first time cooling can be cooled 1 second to 8 seconds.By to described finish to gauge
The step that cooled down of sheet material, can obtain forming isometry ferrite (polygonal ferrite) knot
The sheet material of structure.
Step by being cooled down to the sheet material of described finish to gauge, can obtain with respect to microscopic structure total score
Number 100% has 75% to 85% isometry ferritic structure and the sheet material of 15% to 25% austenite structure.
Described sheet material can be cooled to by the step obtaining hot rolled steel plate by batching the sheet material of described cooling
A3- 20 DEG C to A3Batch after+20 DEG C of temperature range, described A3As shown in formula (3).
A3=693.4-444.5 [C] -80.5 [Mn] -35.0 [Si] -76.0 [Cr] -35.0 [Ni] -85.7 [Mo]
- formula (3)
In formula (3), described [C], [Mn], [Si], [Cr], [Ni] and [Mo] represent respective composition
Weight % of content.
In the step that the sheet material batching described cooling obtains hot rolled steel plate, described sheet material can be with 40 DEG C/s
Speed to 60 DEG C/s is cooled.
The step obtaining hot rolled steel plate by batching the sheet material of described cooling, can obtain forming pearlite
The hot rolled steel plate of structure.
The hot rolled steel plate manufacture method of the present invention, can also comprise the following steps：Batch the plate of described cooling
Material and obtain hot rolled steel plate；Afterwards, pickling is carried out to obtained hot rolled steel plate.
Described hot rolled steel plate can be made up of pearlite and ausferrite microstructure, with respect to described hot rolled steel plate
The gross score 100% of microscopic structure, the volume fraction of described ferritic structure can be 75% to 85%, pearly-lustre
The volume fraction of body tissue can be 15% to 25%.
The yield strength of described hot rolled steel plate can be 295MPa to 520MPa, the surrender of described hot rolled steel plate
The value of intensity × percentage elongation can be more than 11,500 and less than 17,500.
Beneficial effect
A kind of hot rolled steel plate can be provided according to the present invention, there is the intensity of more than 295MPa, have simultaneously
There is excellent ductility.
Brief description
Fig. 1 illustrates that example and use yield strength, percentage elongation and the yield strength × percentage elongation of comparative example are led
The value going out.
Fig. 2 illustrates the refrigerating mode of the hot rolled steel plate according to example.
Specific embodiment
Referring to the drawings with following embodiments it is possible to be expressly understood advantages of the present invention, feature and realization
These method.However, the present invention can implement it is not limited to public below in a variety of ways
The embodiment opened.The purpose providing following embodiments is, the fully open present invention is so that art
Technical staff has overall and sufficient understanding to content of the invention, and protection scope of the present invention should be with claim
Book is defined.In description, identical reference represents identical element in the whole text.
Therefore, for the technology well known in some embodiments, will no longer be described in detail, with
The present invention is avoided to be explained smudgy.Unless otherwise defined, otherwise in this specification using all arts
The implication of language (including technical term and scientific terminology) is exactly that those skilled in the art is generally understood that
The meaning.In description in the whole text, when certain part " includes (or comprising) " a certain component, unless there are
Especially contrary record, otherwise represents and can also include other components and other components non-excluded.Unless it is another
It is described, otherwise singulative is also intended to including plural form.
According to the hot rolled steel plate of an exemplary embodiment of the present invention, wherein with respect to hot rolled steel plate
100 weight %, can comprise C：0.1 weight % is to 0.2 weight %, Si：(do not comprise below 0.5 weight %
0 weight %), Mn：0.5 weight % is to 1.5 weight %, P：(do not comprise 0 weight %) below 0.03 weight %,
S：(do not comprise 0 weight %) below 0.015 weight %, Al：(0 weight is not comprised below 0.05 weight %
Amount %), N：(0 weight % is not comprised), balance of Fe and other are inevitable below 0.01 weight %
Impurity.
Below, the reasons why composition range limiting the present invention is described.
Carbon (C) plays most economical effective effect in the strengthening of steel.If the content of described C is less than 0.1
Weight %, would not generate enough pearlite it is difficult to guarantee desirable strength.On the contrary, if described C's contains
Amount exceeds 0.2 weight %, will lead to ductility reduction because of undue raising of intensity.Therefore, the content of C
Can be for 0.1 weight % to 0.2 weight %.
Silicon (Si) makes molten steel deoxidization, and has solid solution strengthening effect.If the content of described Si exceeds 0.5
Weight %, will form the red scale that Si causes by surface of steel plate in hot rolling, not only result in steel plate
Surface quality becomes very poor, also can reduce weldability.Therefore although silicon must comprise, but contain
Amount can be for below 0.5 weight %.
Manganese (Mn) is the same with Si to be the effective element of the solution strengthening to steel.One in the present invention is shown
In example property embodiment, more than 0.5 weight % can be comprised, to show described effect.Simply, if described
The content of Mn exceeds 1.5 weight %, will generate non-in mid-depth portion in continuous casting working procedure casting steel billet
The segregation portion of Chang Fada, thus the weldability of final products and mouldability may reduce.Therefore, described
The content of Mn can be for 0.5 weight % to 1.5 weight %.
Phosphorus (P) is impurity element, and when its content exceeds 0.03 weight %, weldability reduces and makes steel
The risk producing fragility can become big.Therefore although must comprise, but content can be 0.03 weight %
Below.
Sulfur (S) is the same with described phosphorus (P) element to be inevitable impurity, may tie with Mn etc.
Close and form non-metallic inclusion.Therefore, the toughness of steel may substantially reduce, so need to try one's best pressing down
The content of sulfur processed.In theory, the content of sulfur is limited to 0 weight % is favourable, but must in manufacturing process
Sulfur so can be contained.Therefore although sulfur is the element that will necessarily contain, but an example according to the present invention
Property embodiment, its content of sulfur (S) element can be for below 0.015 weight %.
Aluminum (Al) is the element adding for deoxidation, can as deoxidizer addition in process for making
With beyond 0.05 weight %.Simply, if addition is excessive, the mouth of pipe (nozzle) will occur in continuous casting
Blocking etc., thus productivity may reduce.Therefore although must comprise, but content can be 0.05
Below weight %.
Nitrogen (N) is the effective element of the hardness to steel, but there is uppity shortcoming.Therefore,
If the content of nitrogen exceeds 0.01 weight %, the risk producing fragility will be increased.Therefore although being necessary
Comprise, but content can be for below 0.01 weight %.
More specifically, can comprise as described other inevitably impurity：Cr：Below 0.3 weight % (no
Comprise 0 weight %), Ni：(do not comprise 0 weight %) below 0.3 weight %, Mo：Below 0.2 weight %
(not comprising 0 weight %), Cu：(0 weight % is not comprised) below 0.1 weight %.Simply, described its
Its impurity is not limited thereto, and can also comprise customary impurities in addition.
More specifically, the effect of chromium (Cr) is to make steel solution strengthening, postpone bainitic transformation in cooling,
To be easily obtained the ferrite of equiax crystal.Simply, if the content of described chromium exceeds 0.3 weight %, will mistake
Divide and postpone ferritic transformation it is impossible to guarantee required ferrite fraction, thus percentage elongation may reduce.
And, chromium is the element inevitably adding in process for making step, and therefore chromium content will not be
0 weight %.
Nickel (Ni) has the raising intensity of base material and the effect of toughness simultaneously.Simply, because nickel is
When expensive element, therefore content exceed 0.3 weight %, not only can reduce economy, also can cause to weld
Property be deteriorated.And, nickel element is the element inevitably adding in process for making step, and therefore nickel contains
Amount will not be 0 weight %.
Molybdenum (Mo) is played and improves yield strength by solution strengthening and impacted by intercrystalline strengthening raising tough
The effect of property.Simply, because molybdenum is expensive element, when therefore content exceeds 0.2%, not only it is manufactured into
This rising, also can cause weldability to be deteriorated.And, molybdenum element is in process for making step inevitably
The element adding, therefore molybdenum content will not be 0 weight %.
Copper (Cu) plays and promotes small precipitate to separate out to improve the effect of intensity.Simply, if copper content
Beyond 0.1 weight %, will result in hot-workability and room temperature processability is deteriorated.And, copper is in refining
The element that steel processing step inevitably adds, therefore copper content will not be 0 weight %.
Additionally, the hot rolled steel plate meeting described composition and compositional range can be by micro- group of pearlite and ferrite
It is configured to, and the gross score 100% with respect to described hot rolled steel plate microscopic structure, described ferritic structure
Volume fraction can be 75% to 85%.Furthermore, with respect to the gross score of described hot rolled steel plate microscopic structure
100%, the volume fraction of described pearlitic structrure can be 15% to 25%.
As it was previously stated, when the fraction of ausferrite microstructure is 75% to 85%, hot rolled steel plate can have
The yield strength of 295MPa to 520MPa.Moreover, the yield strength × elongation of described hot rolled steel plate
The value of rate can be more than 11,500.
Simply, if the fraction of ausferrite microstructure is less than 75%, the second phase comprising pearlite will
Beyond 25%, it is likely to result in percentage elongation and is deteriorated.If conversely, the fraction of ausferrite microstructure exceeds 85%,
Then comprise pearlite second mutually will be lower than 15%, is likely to result in intensity and is deteriorated.Therefore, surrender by force
The value of degree × percentage elongation is less than 11,500, possibly cannot meet an exemplary embodiment of the present invention
Scope.Furthermore, the value of described yield strength × percentage elongation gets over the steel that Gao Yueneng has obtained, but highest can
To be 17, less than 500, only it is not limited to this.
Described yield strength, as the intensity reference value in the tensile test of material, represents and starts plastic deformation
When stress.If more specifically, yield point elongation occurs, can be measured described on the basis of upper yield point
Yield strength, if not having yield point elongation, can be measured by 0.2% residual deformation (off-set) method
Described yield strength.Identical below the definition of the yield strength being previously mentioned in this specification and assay method.
More specifically, described percentage elongation represents the ratio that material extends.More specifically, for the mensure of percentage elongation,
If tensile test piece fracture is it is possible to measure percentage elongation during fracture.And, if tensile test piece does not rupture,
The percentage elongation declining under the intensity of (drop) 80% in the intensity being applied just can be measured.
Tensile test for measuring described yield strength and percentage elongation is to be surveyed using the Z600 of ZWICK company
Force transducer (Load cell) and BTC-EXMULTI.003 type are carried out, and deformation rate speed is
5mm/min.
In addition, the equiaxial crystal ratio (aspect ratio) of described ausferrite microstructure can be 0.7 to 1.3.
Equiaxial crystal ratio (aspect ratio) refers to that horizontal and vertical ratio is aspect ratio, by analyzing steel
EBSD (EBSD) analysis it is known that the equiaxial crystal ratio of described microscopic structure.
More specifically, 10 EBSD detections are carried out in random site with 500 times of multiplying power, to institute's total
According to the basic software Grain Shape Aspect Ratio using TSL OIM Analysis 6.0 software
Software is averaged.
When the aspect ratio of described ausferrite microstructure is 0.7 to 1.3, material anisotropy reduces,
Thus percentage elongation may increase.Especially, might have drawing beneficial to one of liquified gas container manufacturing process
Pull out the drawing of operation.On the contrary, when the aspect ratio of described ausferrite microstructure is less than 0.7 or surpasses
When going out 1.3, drawing is deteriorated, and there is the risk cracking during container formation, even if not producing during drawing
Raw crackle, there is also the risk that the crack resistance of final products is deteriorated.
The hot rolled steel plate manufacture method of another illustrative embodiments according to the present invention, walks including following
Suddenly：Prepare steel billet, with respect to 100 total weight %, described steel billet comprises C：0.1 weight % is to 0.2
Weight %, Si：(do not comprise 0 weight %) below 0.5 weight %, Mn：0.5 weight % to 1.5 weight %,
P：(do not comprise 0 weight %) below 0.03 weight %, S：(do not comprise 0 weight %) below 0.015 weight %,
Al：(do not comprise 0 weight %) below 0.05 weight %, N：(0 weight % is not comprised) below 0.01 weight %,
Balance of Fe and other inevitably impurity；Described steel billet is carried out at 1100 DEG C to 1300 DEG C again
Heating；Roughing is carried out to the described steel billet heating again；Finish to gauge is carried out to the steel billet of described roughing；To described
The sheet material of finish to gauge is cooled down；And batch the sheet material of described cooling and obtain hot rolled steel plate.
Wherein, the step sheet material of described finish to gauge being cooled down, it may include following steps：To described end
The sheet material rolling carries out cooling down for the first time with the speed of 40 DEG C/s to 60 DEG C/s；And it is cold to described first time
But sheet material carries out second cooling with the speed of 1 DEG C/s to 8 DEG C/s.
It is possible, firstly, to preparation steel billet, with respect to 100 total weight %, described steel billet comprises C：0.1 weight
Amount % to 0.2 weight %, Si：(do not comprise 0 weight %) below 0.5 weight %, Mn：0.5 weight % is extremely
1.5 weight %, P：(do not comprise 0 weight %) below 0.03 weight %, S：Below 0.015 weight % (no
Comprise 0 weight %), Al：(do not comprise 0 weight %) below 0.05 weight %, N：0.01 weight % with
Under (do not comprise 0 weight %), balance of Fe and other inevitably impurity.
More specifically, described other inevitably impurity can comprise Cr：(do not wrap below 0.3 weight %
Containing 0 weight %), Ni：(do not comprise 0 weight %) below 0.3 weight %, Mo：Below 0.2 weight % (no
Comprise 0 weight %), Cu：(do not comprise 0 weight %) below 0.1 weight %, but be not limited to this.
The composition of described steel billet and compositional range are identical with the composition of aforesaid hot rolled steel plate and compositional range,
Therefore omit the reasons why limit described composition.
It is then possible to implement the step that described steel billet is heated at 1100 DEG C to 1300 DEG C again.
More specifically, described steel billet can be reheated 100 minutes to 400 minutes.
If as described above, being heated again at a temperature of more than 1100 DEG C it is possible to guarantee the temperature of steel billet
Degree, thus reduce rolling load.Simply, if heated again at too high a temperature, due to Austria
The misgrowth of family name's body crystal grain can occur Local Coarsening it is possible to lead to final microscopic structure roughening.Therefore,
Crystal grain may be uneven.
It is then possible to implement the step that roughing is carried out to the described steel billet heating again.
More specifically, described roughing is the intermediate step before finish to gauge, the roughing mentioned in this manual contains
Justice is all identical.
Thus, it is possible to roughing is carried out to the steel billet heating again so that the steel billet thickness of roughing become described in again
The 10% to 25% of heating steel billet thickness.Simply, roughing final temperature can be fully high temperature, so that
It is able to ensure that follow-up finishing temperature.This is that those skilled in the art in the invention are easy to understand, therefore
Description is omitted.
It is then possible to implement the step that finish to gauge is carried out to the steel billet of described roughing.
Carry out in the step of finish to gauge in the steel billet to described roughing, described finish to gauge can be in A1- 20 DEG C extremely
A1Implement within the temperature range of+20 DEG C.Described A1As shown in following formula (1), by A in this specification1-20℃
To A1+ 20 DEG C of temperature range is defined as finishing temperature.
A1=932.1-392.8 [C] -61.9 [Mn]+43.9 [Si]+420.6 [P]+220.0 [Al] -15.5 [Cr
] -15.2 [Ni]+31.5 [Mo] -20 [Cu] --- --- --- --- --- --- ----formula (1)
In formula (1), described [C], [Mn], [Si], [P], [Al], [Cr], [Ni], [Mo]
And [Cu] represents weight % of respective component content.
Above content shows, in order to be had the hot rolled steel plate of excellent intensity and ductility simultaneously, needs
To control the finishing temperature based on alloying component change using described formula (1).If more specifically, described
Finishing temperature is more than A1+ 20 DEG C, the AUSTENITE GRAIN COARSENING of steel billet will be made, yield strength may drop
Low it is thus possible to the value of desired yield strength × percentage elongation cannot be obtained.And, if described finish to gauge
Temperature is less than A1- 20 DEG C, then due to producing the mixed grain structure that two-phase section rolling causes, ductility may
Reduce, and during hot rolling, rolling load greatly increases, productivity may reduce.Described mixed grain structure is
Refer to the different crystal grain of granularity the tissue deposited.
Therefore, when described temperature range carries out hot rolling finish to gauge, the steel billet of described finish to gauge can be had
Target sizes are 10 μm to 40 μm of fine austenite structure.
It is then possible to implement the step that the sheet material of described finish to gauge is cooled down.Sheet material to described finish to gauge
The step being cooled down, it may include following steps：To the sheet material of described finish to gauge with 40 DEG C/s to 60 DEG C/s
Speed carry out cooling down for the first time；And to described first time cooling sheet material with 1 DEG C/s to 8 DEG C/s's
Speed carries out second cooling.
More specifically, being carried out for the first time with the speed of 40 DEG C/s to 60 DEG C/s in the sheet material to described finish to gauge
In the step of cooling, A can be cooled to2- 20 DEG C to A2+ 20 DEG C of temperature range.Wherein, described A2As
Shown in formula (2), by A in this specification2- 20 DEG C to A2+ 20 DEG C of temperature range is defined as intermediate steps
Temperature.
A2=740.1-35.4 [C] -64.5 [Mn]+29.1 [Si]+16.9 [Cr] -16.9 [Ni] --- --- --- -
- formula (2)
In formula (2), described [C], [Mn], [Si], [Cr] and [Ni] represent respective component content
Weight %.
More specifically, by the sheet material of described finish to gauge is cooled to A2- 20 DEG C to A2+ 20 DEG C of temperature range
First time cooling step, the sheet material of described finish to gauge can be cooled to the speed of 40 DEG C/s to 60 DEG C/s
Described A2- 20 DEG C to A2+ 20 DEG C of temperature range.
Then, the sheet material by cooling down to described first time carries out second with the speed of 1 DEG C/s to 8 DEG C/s
The step of secondary cooling, the sheet material of described first time cooling can be cooled 1 second to 8 seconds.
Above content shows, in order to be had the hot rolled steel plate of excellent intensity and ductility simultaneously, needs
To control the intermediate steps temperature based on alloying component change using described formula (2).
During by conventional continuous coo1ing method to manufacture hot rolled steel plate, due to reaching coiling temperature from finishing temperature
Time very short, so cannot expect to generate sufficient isometry ausferrite microstructure.Therefore, it will
Form acicular ferrite, lead to ductility to be deteriorated.
Controlled by the alloying component according to an exemplary embodiment of the present invention and formula (2)
Intermediate steps temperature range and cooling condition, can promote the ferritic formation of isometry, thus improving extension
Property.Described isometry ferrite refers to the ferrite group that the aspect ratio of ausferrite microstructure is 0.7 to 1.3
Knit, because the formation of described tissue, when isometry ferrite fraction increases, ductility can be improved.
Simply, because described intermediate steps temperature is too high more than A2Although isometry ferrum can be formed when+20 DEG C
Ferritic, but due to ferrite crystal grain growth, yield strength may reduce.On the contrary, intermediate steps
Temperature is less than A2When -20 DEG C, due to the formation of acicular ferrite, ductility may reduce.Therefore,
The value of yield strength × percentage elongation is less than 11,500 it is possible to an exemplary reality of the present invention cannot be met
Apply the scope of mode.
Therefore, by intermediate steps temperature control in described A2- 20 DEG C to A2Carry out within the temperature range of+20 DEG C
During cooling, can obtain forming the sheet material of isometry ferrite structure.And, with respect to the plate of described cooling
The microscopic structure gross score 100% of material, can have 75% to 85% isometry ferritic structure and 15% to 25%
Austenite structure.
Finally, it is possible to implement the step batched the sheet material of described cooling and obtain hot rolled steel plate.More specifically,
Described sheet material can be cooled to by the step obtaining hot rolled steel plate by batching the sheet material of described cooling
A3- 20 DEG C to A3Batch after+20 DEG C of temperature range.Described A3As shown in formula (3), will in this specification
Described A3- 20 DEG C to A3+ 20 DEG C of temperature range is defined as coiling temperature.
A3=693.4-444.5 [C] -80.5 [Mn] -35.0 [Si] -76.0 [Cr] -35.0 [Ni] -85.7 [Mo]
- formula (3)
In formula (3), described [C], [Mn], [Si], [Cr], [Ni] and [Mo] represent respective composition
Weight % of content.
In the step that the sheet material batching described cooling obtains hot rolled steel plate, described sheet material can be with 40 DEG C/s
Speed to 60 DEG C/s is cooled to A3- 20 DEG C to A3Batch after+20 DEG C of temperature range.
Furthermore, described batching can implement 1 minute to 50000 minutes.More specifically, described batching can be real
Apply 1 minute to hundreds of hour.Further, described batching can implement 1 minute to tens hour.
After batching, coiled material temperature close to room temperature when just can carry out subsequent job, therefore as mentioned above may
What needs were longer batches the time.
In order to obtain the hot rolled steel plate with excellent intensity and ductility, as described formula (3) institute
Show the coiling temperature controlling based on alloying component change, to form fine pearlite tissue.
If coiling temperature is more than A3+ 20 DEG C, thick pearlite will be formed, yield strength may be led to
Reduce, it is possible to the value of desired yield strength × percentage elongation cannot be obtained.Contrary, if batching
Temperature is less than A3- 20 DEG C, will result in ductility and be deteriorated.More specifically, coiling temperature is less than A3-20℃
When although forming fine pearlite and improving yield strength, but ductility can be deteriorated it is possible to cannot
Obtain the value of desired yield strength × percentage elongation.Therefore, oiler temperature control is in described temperature range
And when being cooled down, it is possible to obtain form the hot rolled steel plate of pearlitic texture.
Fig. 2 shows the end of the hot rolled steel plate manufacture method according to an exemplary embodiment of the present invention
Temperature change after rolling.
More specifically, to finishing temperature (A1- 20 DEG C to A1+ 20 DEG C), intermediate steps temperature (A2-20℃
To A2+ 20 DEG C) and coiling temperature (A3- 20 DEG C to A3+ 20 DEG C) it is controlled according to alloying component, figure
The rate of cooling equitemperature change of each step is shown in 2.Therefore, aforesaid temperature can be confirmed by Fig. 2
Degree condition and rate of cooling.
In addition, described in being manufactured by the manufacture method according to an exemplary embodiment of the present invention
Hot rolled steel plate, need not carry out subsequent handling and can directly utilize, it is also possible to comprise the following steps：Batch
The sheet material of described cooling and obtain hot rolled steel plate；Afterwards, pickling is carried out to obtained hot rolled steel plate.No
Only such, can also the process such as annealed operation further.
The final hot rolled steel plate being manufactured by methods described can be made up of pearlite and ausferrite microstructure.
And, with respect to the gross score 100% of described hot rolled steel plate microscopic structure, the volume of described ferritic structure
Fraction can be 75% to 85%, and the volume fraction of pearlitic structrure can be 15% to 25%.Now, described ferrum
The equiaxial crystal ratio of ferritic crystal grain can be 0.7 to 1.3.
The yield strength with the hot rolled steel plate of described microscopic structure can be 295MPa to 520MPa.Furthermore,
The combination of the yield strength of described hot rolled steel plate and percentage elongation is that the value of yield strength × percentage elongation can be
More than 11,500.
Below, it is described in detail by embodiment.But, the following example is only intended to illustrate this
Bright, present disclosure is not limited to the following example.
Embodiment
In one embodiment of the invention, manufactured as an example invention steel becomes with the steel billet comparing steel
Divide as shown in Table 1 above.
Then, the steel billet comprising described table 1 composition is heated 200 minutes at 1150 DEG C again.
After roughing is carried out to the described steel billet heating again, the finishing temperature shown in table 2 below
(A1- 20 DEG C to A1+ 20 DEG C) under implement finish to gauge.
The sheet material of described finish to gauge is carried out cooling down for the first time, table 2 below is cooled to the speed of 50 DEG C/s
Shown medium temperature (A2- 20 DEG C to A2+20℃).Reach after described medium temperature with 5 DEG C/s's
Speed carries out second cooling, and cool time is 5 seconds.
The sheet material of described cooling is cooled to the coiling temperature shown in table 2 below with the speed of 50 DEG C/s
(A3- 20 DEG C to A3+ 20 DEG C) after batch, thus obtaining hot rolled steel plate.
[table 2]
[table 3]
Using having the composition of described table 1 and the steel billet of compositional range, described table 2 finishing temperature,
Hot rolled steel plate has been manufactured under the conditions of medium temperature and coiling temperature.Microstructure to final hot rolled steel plate
After tensile property etc. is evaluated, show the result in described table 3.
The tensile strength of described table 3 refers to the maximum load born before Materials Fracture in tensile test
Divided by the value of the former cross section of sample, described tensile strength is in aforesaid mensure yield strength and percentage elongation
Used test a machine and experimental condition under same measure.In addition, yield strength and percentage elongation
Assay method and equipment are as it was previously stated, therefore description is omitted.
More specifically, the comparison steel 1 and 2 of described table 1 and an exemplary embodiment party according to the present invention
The carbon content of formula has differences.More specifically, for the comparison being less than 0.1 weight % using institute's carbonaceous component
The comparative example 1 of steel 1, its solid solution strengthening effect based on carbon is not enough, and therefore pearlite fraction is also non-
Often low, this point be can confirm that by described table 3.Therefore, it is known that surrender is strong as shown in described table 3
The value of degree × percentage elongation is deteriorated.
For using institute's carbonaceous component exceed 0.2 weight % comparison steel 2 comparative example 2 it is known that due to
Pearlitic microstructure excessively generates and causes percentage elongation to be deteriorated.Therefore, it can confirm yield strength × stretch
The value of long rate is also deteriorated.
In addition, the comparison steel 3 and 4 of described table 1 with according to an exemplary embodiment of the present invention
Manganese content has differences.More specifically, be less than the comparison steel 3 of 0.5 weight % for contained manganese composition,
Its solution strengthening based on manganese element is not enough, and therefore pearlite fraction is low, and this point passes through described table 3
Comparative example 3 can confirm that.If pearlite fraction is low, yield strength may reduce it is known that described
In table 3, the value of the yield strength × percentage elongation of comparative example 3 is deteriorated.
For the comparative example 4 of the comparison steel 4 exceeding 1.5 weight % using contained manganese composition, it is by formula (1)
The finishing temperature deriving is too low, therefore can not possibly carry out actual rolling.Cannot obtain as a result, can confirm that
Value to desired yield strength × percentage elongation.
Furthermore, for comparative example 5 it is known that exceeding the finishing temperature scope being derived by formula (1).More specifically
Ground, as described comparative example 5, if exceeding the finishing temperature scope being derived by formula (1), with
Yield strength declines, and the value of yield strength × percentage elongation is deteriorated.
For comparative example 6 and 7 it is known that being exceeded according to this by the intermediate steps temperature range that formula (2) derives
The scope of one illustrative embodiments of invention.
Therefore, for described comparative example 6 and 7 it is known that declining with percentage elongation, yield strength × elongation
The value of rate is deteriorated.
Additionally, for comparative example 8 and 9 it is known that basis is exceeded by the coiling temperature scope that formula (3) derives
The scope of an exemplary embodiment of the present invention.
More specifically, for the comparative example 8 that cannot meet the coiling temperature scope being derived by formula (3), can
Know that intensity is deteriorated, and for comparative example 9, percentage elongation is deteriorated.Therefore, for described comparative example 8 and 9,
Understand that the value of yield strength × percentage elongation is deteriorated.
Comparative example 10 and 11 is the situation being manufactured by manufacturing processes customary, presents from finishing temperature even
Continuous it is cooled to coiling temperature and the situation without intermediate steps temperature.
As a result, described comparative example 10 and 11 cannot meet an exemplary embodiment party according to the present invention
The scope of the ferrite equiaxial crystal ratio of formula is it is known that ductility is deteriorated.And it is known that yield strength × elongation
The value of rate is deteriorated.
Derive conversely, for the compositing range according to an exemplary embodiment of the present invention and by formula
The example 1 to 2 that is all satisfied of hot-rolled condition, can confirm that there is excellent yield strength and elongation
Rate.
Fig. 1 shows by the yield strength of example and comparative example and percentage elongation and yield strength × percentage elongation
The value deriving.
More specifically, square part represents the value of comparative example 1 to 11 in Fig. 1, circular portion represents to be sent out
The value of bright example 1 and 2.Therefore, as shown in figure 1, example 1 and 2 has excellent intensity and extension
Property.More specifically, for described example 1 and 2, the value of yield strength × percentage elongation be 11500 with
On, therefore include in gray area.
Above by reference to accompanying drawing, embodiments of the invention are illustrated, but those skilled in the art can
To understand, in the case of not changing technological thought and essential feature, the present invention can be specifically real with other
The mode of applying is implemented.
Therefore, above-described embodiment is exemplary and nonrestrictive.Protection scope of the present invention should be with
Claims are defined rather than described above, are derived by the implication of claims, scope and such equivalents
Institute's form of having altered or changing, all fall within protection scope of the present invention.
Claims (22)
1. a kind of hot rolled steel plate, wherein total with respect to hot rolled steel plate 100 weight %, comprise C：0.1 weight %
To 0.2 weight %, Si：Do not comprise 0 weight %, Mn below 0.5 weight % and：0.5 weight % to 1.5 weight %,
P：Do not comprise 0 weight %, S below 0.03 weight % and：Do not comprise below 0.015 weight % and 0 weight %,
Al：Do not comprise 0 weight %, N below 0.05 weight % and：Do not comprise 0 weight % below 0.01 weight % and,
Balance of Fe and other inevitably impurity,
Described hot rolled steel plate is made up of pearlite and ausferrite microstructure,
With respect to the gross score 100% of described hot rolled steel plate microscopic structure, the volume fraction of described ferritic structure
For 75% to 85%, and the equiaxial crystal ratio of described ausferrite microstructure is 0.7 to 1.3.
2. hot rolled steel plate according to claim 1, wherein,
Described other inevitably impurity comprises Cr：Do not comprise 0 weight %, Ni below 0.3 weight % and：0.3
Do not comprise 0 weight %, Mo below weight % and：Do not comprise 0 weight %, Cu below 0.2 weight % and：0.1 weight
Measure below % and do not comprise 0 weight %.
3. hot rolled steel plate according to claim 2, wherein,
With respect to the gross score 100% of described hot rolled steel plate microscopic structure, the volume fraction of described pearlitic structrure
For 15% to 25%.
4. hot rolled steel plate according to claim 3, wherein,
The yield strength of described hot rolled steel plate is 295MPa to 520MPa.
5. hot rolled steel plate according to claim 4, wherein,
The value of the yield strength × percentage elongation of described hot rolled steel plate is more than 11,500 and less than 17,500.
6. a kind of hot rolled steel plate manufacture method, comprises the following steps：
Prepare steel billet, with respect to 100 total weight %, described steel billet comprises C：0.1 weight % to 0.2 weight %,
Si：Do not comprise 0 weight %, Mn below 0.5 weight % and：0.5 weight % is to 1.5 weight %, P：0.03 weight
Measure below % and do not comprise 0 weight %, S：Do not comprise 0 weight %, Al below 0.015 weight % and：0.05 weight
Measure below % and do not comprise 0 weight %, N：Do not comprise below 0.01 weight % and 0 weight %, balance of Fe and
Other inevitably impurity；
Described steel billet is heated at 1100 DEG C to 1300 DEG C again；
Roughing is carried out to the described steel billet heating again；
Finish to gauge is carried out to the steel billet of described roughing；
The sheet material of described finish to gauge is cooled down；And
Batch the sheet material of described cooling and obtain hot rolled steel plate,
Wherein, the step sheet material of described finish to gauge being cooled down, comprises the following steps：
The sheet material of described finish to gauge is carried out cooling down for the first time with the speed of 40 DEG C/s to 60 DEG C/s；And to described
The sheet material of cooling carries out second cooling with the speed of 1 DEG C/s to 8 DEG C/s for the first time.
7. hot rolled steel plate manufacture method according to claim 6, wherein,
Described other inevitably impurity comprises Cr：(0 weight %, Ni is not comprised below 0.3 weight %：0.3
Do not comprise 0 weight %, Mo below weight % and：Do not comprise 0 weight %, Cu below 0.2 weight % and：0.1 weight
Measure below % and do not comprise 0 weight %.
8. hot rolled steel plate manufacture method according to claim 7, wherein,
Carry out in the step of finish to gauge in the steel billet to described roughing,
Described finish to gauge is in A1- 20 DEG C to A1Implement within the temperature range of+20 DEG C,
A1=932.1-392.8 [C] -61.9 [Mn]+43.9 [Si]+420.6 [P]+220.0 [Al] -15.5 [Cr] -1
5.2 [Ni]+31.5 [Mo] -20 [Cu] --- --- --- --- --- --- ----formula (1)
In formula (1), described [C], [Mn], [Si], [P], [Al], [Cr], [Ni], [Mo] and [Cu]
Represent weight % of respective component content.
9. hot rolled steel plate manufacture method according to claim 8, it is by entering to the steel billet of described roughing
The step of row finish to gauge, make the steel billet of described finish to gauge have austenitic microstructure that size is 10 μm to 40 μm.
10. hot rolled steel plate manufacture method according to claim 7, wherein,
Carried out in the step cooling down for the first time with the speed of 40 DEG C/s to 60 DEG C/s in the sheet material to described finish to gauge,
The sheet material of described finish to gauge is cooled to A2- 20 DEG C to A2+ 20 DEG C of temperature range,
A2=740.1-35.4 [C] -64.5 [Mn]+29.1 [Si]+16.9 [Cr] -16.9 [Ni] --- --- -- formula (2)
In formula (2), described [C], [Mn], [Si], [Cr] and [Ni] represent weight % of respective component content.
11. hot rolled steel plate manufacture methods according to claim 10, wherein,
The step second cooling being carried out with the speed of 1 DEG C/s to 8 DEG C/s in the sheet material that described first time is cooled down
In, the sheet material of described first time cooling is cooled 1 second to 8 seconds.
12. hot rolled steel plate manufacture methods according to claim 11, it is by the sheet material to described finish to gauge
The step being cooled down is forming isometry ferrite structure.
13. hot rolled steel plate manufacture methods according to claim 12, it is by the sheet material to described finish to gauge
The step being cooled down, makes described sheet material have 75% to 85% isometry with respect to microscopic structure gross score 100%
Ferritic structure and 15% to 25% austenite structure.
14. hot rolled steel plate manufacture methods according to claim 7, its sheet material by batching described cooling
And the step obtaining hot rolled steel plate, described sheet material is cooled to A3- 20 DEG C to A3Roll up after+20 DEG C of temperature range
Take,
A3=693.4-444.5 [C] -80.5 [Mn] -35.0 [Si] -76.0 [Cr] -35.0 [Ni] -85.7 [Mo]-formula
(3)
In formula (3), described [C], [Mn], [Si], [Cr], [Ni] and [Mo] represent respective component content
Weight %.
15. hot rolled steel plate manufacture methods according to claim 14, wherein,
In the step that the sheet material batching described cooling obtains hot rolled steel plate,
Described sheet material is to batch with after the speed cooling of 40 DEG C/s to 60 DEG C/s.
16. hot rolled steel plate manufacture methods according to claim 15, its plate by batching described cooling
Material and the step that obtains hot rolled steel plate more forms pearlitic texture.
17. hot rolled steel plate manufacture methods according to claim 7, wherein,
In the step that described steel billet is heated at 1100 DEG C to 1300 DEG C again,
Described steel billet is reheated 100 minutes to 400 minutes.
18. hot rolled steel plate manufacture methods according to claim 7, further comprising the steps of：
Obtain hot rolled steel plate in the sheet material batching described cooling；
Pickling is carried out to obtained hot rolled steel plate.
The 19. hot rolled steel plate manufacture methods according to any one in claim 6 to 18, wherein,
Described hot rolled steel plate is made up of pearlite and ausferrite microstructure, and micro- with respect to described hot rolled steel plate
The gross score 100% of tissue, the volume fraction of described ferritic structure is 75% to 85%.
The 20. hot rolled steel plate manufacture methods according to any one in claim 6 to 18, wherein,
With respect to the gross score 100% of described hot rolled steel plate microscopic structure, the volume fraction of pearlitic structrure is 15%
To 25%.
The 21. hot rolled steel plate manufacture methods according to any one in claim 6 to 18, wherein,
The yield strength of described hot rolled steel plate is 295MPa to 520MPa.
The 22. hot rolled steel plate manufacture methods according to any one in claim 6 to 18, wherein,
The value of the yield strength × percentage elongation of described hot rolled steel plate is more than 11,500 and less than 17,500.
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| CN111542638A (en) * | 2017-12-26 | 2020-08-14 | Posco公司 | Hot-rolled steel sheet, steel pipe, and component having excellent impact resistance, and method for producing same |
| CN114867884A (en) * | 2019-12-18 | 2022-08-05 | Posco公司 | Steel material for vacuum pipe and method for producing same |
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| KR102296840B1 (en) * | 2019-12-16 | 2021-09-01 | 주식회사 포스코 | High strength steel material having excellent ductility and manufacturing method for the same |
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| JP4018318B2 (en) * | 2000-04-18 | 2007-12-05 | 株式会社神戸製鋼所 | Steel plate manufacturing method with excellent brittle cracking characteristics |
| JP4367091B2 (en) * | 2002-12-20 | 2009-11-18 | Ｊｆｅスチール株式会社 | High-strength hot-rolled steel sheet having excellent fatigue resistance and excellent strength-ductility balance and method for producing the same |
| JP4404004B2 (en) * | 2005-05-11 | 2010-01-27 | 住友金属工業株式会社 | High-tensile hot-rolled steel sheet and manufacturing method thereof |
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| CN1396963A (en) * | 2000-12-01 | 2003-02-12 | Posco公司 | Steel plate to be precipitating TiN+MnS for welded structures, method for manufacturing the same and welded structure using the same |
| JP5454738B2 (en) * | 2011-04-13 | 2014-03-26 | 新日鐵住金株式会社 | Hot rolled steel sheet for gas soft nitriding and method for producing the same |
| JP2014148739A (en) * | 2013-01-10 | 2014-08-21 | Kobe Steel Ltd | Hot rolled steel sheet excellent in cold workability and surface hardness after processing |
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| CN111542638A (en) * | 2017-12-26 | 2020-08-14 | Posco公司 | Hot-rolled steel sheet, steel pipe, and component having excellent impact resistance, and method for producing same |
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| CN114867884B (en) * | 2019-12-18 | 2023-12-22 | Posco公司 | Steel material for vacuum tube and method for producing same |
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