CN109868342A - A method of carbon equivalent high steel plate welding heat influence area toughness is improved using rare earth - Google Patents
A method of carbon equivalent high steel plate welding heat influence area toughness is improved using rare earth Download PDFInfo
- Publication number
- CN109868342A CN109868342A CN201910245642.0A CN201910245642A CN109868342A CN 109868342 A CN109868342 A CN 109868342A CN 201910245642 A CN201910245642 A CN 201910245642A CN 109868342 A CN109868342 A CN 109868342A
- Authority
- CN
- China
- Prior art keywords
- steel plate
- steel
- rare
- earth
- molten steel
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Granted
Links
Classifications
-
- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
- Y02P10/00—Technologies related to metal processing
- Y02P10/20—Recycling
Landscapes
- Treatment Of Steel In Its Molten State (AREA)
- Heat Treatment Of Steel (AREA)
Abstract
The present invention relates to a kind of methods for improving carbon equivalent high steel plate welding heat influence area toughness using rare earth, belong to welding high-strength steel sheet technical field.The method successively includes converter smelting step, LF refining step, RH refinement step, continuous casting step, hot-rolled step and heat treatment step, by the way that a certain amount of Rare-Earth Ce alloy is added into molten steel in the RH refining process, it is re inclusion by the field trash in rare earth modified molten steel, make to generate tiny newborn re inclusion in molten steel simultaneously, and controls the Dispersed precipitate of re inclusion.The field trash containing Rare-Earth Ce of newly-generated small and dispersed distribution and by rare earth modified original field trash in molten steel, heat affected area original austenite grain in welding process is inhibited to grow up, the bainite transformation of welding heat affected zone has also been postponed in the addition of rare earth simultaneously, the formation for inhibiting upper bainite, so that the toughness of carbon equivalent high thick plates heat affected area be greatly improved.
Description
Technical field
The invention belongs to weld to use high-strength steel sheet technical field, and in particular to a kind of to improve carbon equivalent high steel using rare earth
The method of plate welding heat influence area toughness.
Background technique
Steel for engineering machinery, building element steel enlarged and high stratification demand for development steel plate have higher intensity,
There is good welding performance simultaneously.But as the raising of armor plate strength, welding performance significantly reduce, weld crack is sensitive
Property increase.Especially for carbon equivalent high slab, with the raising of weld heat input, the original austenite grain of welding heat affected zone
Size dramatically increases, and forms coarse grain heat affect zone, postwelding heat affected area upper bainite tissue easily generated, hence it is evident that reduces sweating heat shadow
Ring the toughness in area.
In order to improve thick plates heat affected area performance, last century the nineties Japanese scholars first proposed " oxide
The concept of metallurgy ", i.e., inclusion particle controllable by tiny, Dispersed precipitate, ingredient using the size generated in steelmaking process
To change the tissue and grain size of steel, to make steel that there is good welding performance.Studies at home and abroad show that using thin in steel
Small, Dispersed precipitate field trash acts not only as pinning particle pinning austenite grain boundary during Thermal Cycle, inhibits
Original austenite grain is grown up, and be can be used as forming core core and promoted Intragranular Acicular Ferrite transformation, so that it is defeated to increase substantially big heat
Enter the toughness of welding heat affected zone.
(golden swamp high noon, middle island be bright, this Itou Kentaro of ridge, Jin Guyan: entering thermosol greatly and connects with high by Japan Patent JP5116890
Power steel-product manufacturing method, JP5116890,1976.5.28.) propose to add a certain amount of Ti in the ingredient design of steel
And N, Austenite Grain Growth during Thermal Cycle is on the one hand prevented using TiN particle, on the other hand promotes needle-shaped iron element
The generation of body, to effectively inhibit the reduction of welding heat influence area toughness.However, with the increase of thermal weld stress, weld seam
The peak temperature of heat affected area will be more than 1400 DEG C near melt run, and TiN particle at this temperature dissolves roughening, to lose
The effect for inhibiting original austenite grain to grow up.
On this basis, researchers explore using the oxide particle with high-temperature stability as pinning crystal boundary and rush
Into the core of Intragranular Acicular Ferrite forming core.Japan Patent JP517300, which has been invented, improves the weldering of steel large-line energy using titanyl compound
The method for connecing performance.Titanyl compound particle can be used as ferritic forming core core, and formed has high inclination-angle crystal grain each other
Acicular ferrite structure, improve the toughness of welding heat affected zone.But titanium-containing oxide is mixed in molten steel and is easy aggregation length
Greatly, bulky grain can reduce the toughness of steel containing titanium inclusion, or even become formation of crack.
In recent years, researchers developed the skill that welding heat influence area toughness is improved using different type particle in steel in succession
Art.If what Japan Patent JP3378433 and Japan Patent JP3476999 was developed utilizes MgO particle, patent CN102191429B is opened
Hair by molten steel casting process add Mg alloy, utilize the MgO or MgO-Ti generated in steel2O3Duplex impurity inhibits welding
Heat affected area Austenite Grain Growth promotes its Intragranular Acicular Ferrite to grow, improves the Large Heat Input Welding performance of slab.Patent
CN101476018B discloses one kind by adding Ca element in steel, is allowed to form nanoscale CaO or the CaS matter of small and dispersed
Point, and depend on MnS and form round or polygon particle, the forming core matter of the more intragranular acicular ferrite of forming quantity thereon
Point, effectively pin austenite grain boundary, refinement crystal grain, improves the toughness of welding heat affected zone coarse grain zone.Patent CN103695776B
By rationally being controlled Ti/N ratio in steel, and the Ca/Al ratio of the micron field trash for diameter more than or equal to 1 μm,
The surface density of surface density, length-width ratio, sub-micron field trash of the diameter less than 1 μm is rationally controlled, these field trash tables are utilized
Face promotes the growth of Intragranular Acicular Ferrite, or austenite grain during Large Heat Input Welding is inhibited to grow up, and improves thick steel plate
Large Heat Input Welding performance.The announcements such as CN1946862B, CN101476018B, CN103695777B, CN104404369A
Technology is by the constituent contents such as Ti, Al, Mg, Ca, Zr in control steel, and then the ingredient that is mingled with of control oxide and quantity.These
Field trash promotes the growth of Intragranular Acicular Ferrite, inhibits austenite grain during Large Heat Input Welding to grow up, so as to improve thickness
The Large Heat Input Welding performance of steel plate.The common ground of these technologies is to promote intragranular acicular ferrite using microinclusions particle
Generation, while inhibiting growing up for original austenite grain during Large Heat Input Welding.But it is pressed from both sides containing Ti and type oxide containing Ca
Miscellaneous that agglomeration is easy in molten steel, particle size is mostly several microns, and even more greatly, above-mentioned technology is not to its size Control
It is described.In addition, the high heat-input for carbon equivalent high steel plate welds, in addition to original austenite grain is anxious during Thermal Cycle
Outside play is grown up, heat affected area will not generate ferritic structure in postwelding cooling procedure, and be also easy to produce a large amount of upper bainite tissues.Needle
To this kind of steel grade, need that heat affected area upper bainite tissue can be inhibited simultaneously while inhibiting original austenite grain to grow up
Generation.
Summary of the invention
The object of the present invention is to provide it is a kind of using rare earth improve carbon equivalent high steel plate welding heat influence area toughness method,
Plate thickness is 20~60mm, base material tensile strength >=750MPa.This method is suitable for engineering machinery, bridge, skyscraper, large-scale stone
Large Heat Input Welding high-strength steel sheet used in oil tank manufacture can in the range of weld heat input >=50kJ/cm
Effectively improve welding heat influence area toughness.
According to the first aspect of the invention, a kind of utilization rare earth raising carbon equivalent high steel plate welding heat influence area toughness is provided
Method.The method successively includes converter smelting step, ladle refining furnace (Ladle refining furnace, LF) refining
Step, RH refinement step, continuous casting step, hot-rolled step and heat treatment step, the method pass through in LF refining step and RH essence
Refining step controls oxygen, calcium and the sulfur content in molten steel, and rare earth alloy is added in RH refinement step, thus in molten steel
In the distribution of newly-generated small and dispersed field trash containing Rare-Earth Ce and by rare earth modified original field trash, to inhibit to weld
Heat affected area original austenite grain is grown up in journey, while postponing the bainite transformation of welding heat affected zone, inhibits upper bainite
It is formed, so that the toughness of carbon equivalent high thick plates heat affected area be greatly improved.
RH method is vacuum circulation degassing method, is Rule iron company, West Germany (Ruhrstahl) and extra large Lars company
(Heraeus) in nineteen fifty-seven joint development, therefore with the name of the initial of two CompanyNames.
Further, it the described method comprises the following steps:
1) converter smelting step: iron water amount is 4:1~6:1 with clean steel scrap ratio, enters furnace molten iron temperature 1350~1400
DEG C, lime, dolomite slag making is added in S mass percent≤0.04% in molten iron, and oxygen blast is smelted；
2) LF refining step: station makes white slag desulfurization, and final slag composition control is CaO/SiO2=4.5:1~7.0:1, tapping
Oxygen mass percent be 0.0020~0.0060%, 1590~1620 DEG C of molten steel temperature；
3) RH refinement step: RH arrives at a station 1580~1610 DEG C of molten steel temperature, is added after 10~20min of RH application of vacuum dilute
Native Ce alloy, total vacuum processing time > 20min, break it is empty after the control of oxygen mass percent 0.0010~0.0050%, bottom later
The soft stirring of Argon is no less than 5min；
4) continuous casting step: in 1.0~1.2m/min, cast temperature is controlled at 1530~1550 DEG C casting speed control, and thickness is made
Degree is the continuous casting steel billet of 200~300mm；
5) hot-rolled step: 1180~1220 DEG C of first stage start rolling temperature, second stage is once to 900~930 DEG C of temperature, eventually
840~870 DEG C of temperature are rolled, by the Rolled From Continuous Casting Slab at 20~60mm steel plate；
6) heat treatment step: to the steel plate carry out modifier treatment, 910~950 DEG C of quenching and preserving heat temperature, soaking time >
8min, it is 580~640 DEG C of tempering temperature, air-cooled after tempering.
Further, the control of converter aim carbon is lower than 0.06% in step 1), makes steel 1610~1650 DEG C of outlet temperature.
Further, Al deoxidation, molten steel Al mass percent 0.020~0.050% is added in step 1) after converter tapping.
Further, Ce mass percent is 0.0015%~0.0040% in the molten steel in step 3).
Further, calcium mass percent < 0.0010% in molten steel in step 3), to avoid raw during liquid steel refining
At the calcium-aluminate of package re inclusion.Sulphur mass percent < 0.0015% in molten steel is dilute to avoid package is generated in steel
The sulfide of native field trash.
Further, Al deoxidation is used before Rare-Earth Ce alloy is added in step 3), before control plus Rare-Earth Ce alloy in molten steel
Oxygen mass percent between 0.0020%~0.0060%.
According to the second aspect of the invention, a kind of steel plate is provided, the steel plate is according to described using dilute in terms of any of the above
The method that soil improves carbon equivalent high steel plate welding heat influence area toughness, which is smelted, to be made, and the chemical composition of the steel plate is according to quality hundred
Divide to compare and is calculated as C 0.06~0.15%, Si 0.1~0.4%, Mn 1.0~2.0%, P≤0.02%, Nb 0.03~0.06%,
0.1~0.4.Mo of V 0.05~0.09%, Cr 0.05~0.15%, Ti 0.010~0.025%, remaining is iron and can not keep away
The impurity element exempted from, Rare-Earth Ce mass percent 0.0015~0.0040%.Steel plate carbon equivalent CeqAre as follows: 0.4%~0.7%, Ceq
=C+Mn/6+ (Cr+Mo+V)/5+ (Ni+Cu)/15.
Further, one of Ce-Al-O, Ce-O-S and Ca-Ce-O-S re inclusion or two is contained in the steel plate
Kind, the mass percent of the chemical composition of Al, Ce, Ca, S and O is 2% < Al < 40%, 20% < Ce < 70% in field trash,
2% < Ca < 15%, 10% < S < 40%, 2% < O < 20%, number density >=150/mm2, and 80% or more rare earth presss from both sides
Sundries size is less than 1 micron.These submicron order field trashes are easy Dispersed precipitate in the soft whipping process of RH, are conducive to field trash
The increase of quantity, while such inclusion melting point is high, thermal stability is good, it will not be molten Peak temperature reaches 1400 DEG C
Solution is in austenite.
Further, the steel plate mother metal tensile strength >=750MPa is 50~100kJ/cm condition in thermal weld stress
Under, welding heat affected zone impact flexibility >=110J.
Beneficial effects of the present invention:
For carbon equivalent high high-strength steel, the present invention makes steel using suitable oxygen and crucial micronutrient levels control technology
Middle formation containing Rare-Earth Ce field trash of the size less than 1 micron, and the ingredient and quantity of these field trashes are rationally controlled, utilize these
The pinning original austenite crystal prevention in the welding process of field trash inhibits original austenite grain to grow up (roughening).Meanwhile using in steel
The rare earth of solid solution inhibits the generation of welding heat affected zone upper bainite tissue.Hot shadow when to which high heat-input welding greatly improved
Ring the performance in area.According to the steel plate that the present invention smelts, base material tensile strength >=750MPa is 50~100kJ/ in thermal weld stress
Under the conditions of cm, welding heat affected zone impact flexibility >=110J.
Detailed description of the invention
In order to more clearly explain the embodiment of the invention or the technical proposal in the existing technology, to embodiment or will show below
There is attached drawing needed in technical description to be briefly described, it should be apparent that, the accompanying drawings in the following description is only this
Some embodiments of invention for those of ordinary skill in the art without creative efforts, can be with
The structure shown according to these attached drawings obtains other attached drawings.
Fig. 1 shows a kind of method for improving carbon equivalent high steel plate welding heat influence area toughness using rare earth according to the present invention
Flow chart；
Fig. 2 shows welding heat affected zone microscopic structures according to an embodiment of the invention；
Fig. 3 shows the welding heat affected zone microscopic structure of a comparative example according to the present invention；
Fig. 4 is shown according to an embodiment of the present invention with comparative example about original austenite grain average-size comparison diagram.
Specific embodiment:
Below with reference to embodiment, the present invention will be further described.
The invention discloses a kind of methods for improving carbon equivalent high steel plate welding heat influence area toughness using rare earth.Wherein,
External refining uses LF+ vacuum outgas/RH process route, and rare earth alloy is added in RH refining process, thus new in molten steel
Generate the field trash containing Rare-Earth Ce of small and dispersed distribution and by rare earth modified original field trash.These field trashes inhibit welding
Heat affected area original austenite grain is grown up in the process, while the bainite turn of welding heat affected zone has also been postponed in the addition of rare earth
Become, inhibits the formation of upper bainite, so that the toughness of carbon equivalent high thick plates heat affected area be greatly improved.
The impact flexibility of thick steel plate welding heat affected zone under the conditions of raising Large Heat Input Welding is carried out the study found that rare earth
Field trash can inhibit welding process Austenite Grain Growth, so that it is welding heat affected to improve steel plate with pinning original austenite crystal prevention
The impact flexibility in area.Present invention determine that the ingredient of these re inclusion particles, size and number.The components utilising of field trash
Field emission scanning electron microscope (FE-SEM/EDS) is analyzed, and after sample surfaces are ground and polished, utilizes FE-SEM/
EDS is observed and is analyzed to field trash, and the average composition of each specimen holder sundries is that field trash of choosing any for 50 divides
Analyse the average value of result.Utilize the number density of full-automatic inclusion analysis system (INCA) statistical analysis field trash.
As shown in Figure 1, according to the present invention a kind of carbon equivalent high steel plate welding heat influence area toughness is improved using rare earth
Method is as follows:
Converter smelting step → LF refining step → RH refinement step → continuous casting step → hot-rolled step → heat treatment step.
Specifically:
Step 101: pneumatic steelmaking iron water amount is 4~6 with clean steel scrap ratio, enters 1350~1400 DEG C of furnace molten iron temperature,
S≤0.04% in molten iron, is added lime, dolomite slag making, and oxygen blast is smelted.The control of converter terminal carbon is lower than 0.06%, and steel-making is eventually
Al deoxidation, molten steel Al mass percent 0.020~0.050% is added in 1610~1650 DEG C of temperature of point after tapping.
Step 102:LF refining station makes white slag desulfurization, and final slag composition control is CaO/SiO2=4.5~7.0, oxygen of tapping
Mass percent be 0.0020~0.0060%, sulphur mass percent < 0.0015%, 1590~1620 DEG C of molten steel temperature.
Step 103:RH refining: RH arrives at a station 1580~1610 DEG C of molten steel temperature, is added after 10~20min of RH application of vacuum
Rare earth alloy, total vacuum processing time > 20min, the control of oxygen mass percent is 0.0010~0.0050% after breaking sky, later
The soft stirring of BOTTOM ARGON BLOWING is no less than 5min.
Its calcium mass percent of the alloy strict control of LF and RH refining addition, LF and RH refining are forbidden to feed Ca line, be guaranteed
Whole molten steel Ca mass percent < 0.0010%.When Ca mass percent is greater than 0.0010%, it is easy to generate calcium-aluminate, this
A little calcium-aluminates can wrap up rare earth oxide and be mingled with, this effect that will be unfavorable for playing rare earth oxide and be mixed in steel.
Step 104: in 1.0~1.2m/min, cast temperature is controlled at 1530~1550 DEG C for pulling speed of continuous casting control, and thickness is made
Degree is the continuous casting steel billet of 200~300mm.
Step 105: hot rolling: 1180~1220 DEG C of first stage start rolling temperature, the two-stage is whole once to 900~930 DEG C of temperature
840~870 DEG C of temperature are rolled, by above-mentioned Rolled From Continuous Casting Slab at 20~60mm steel plate.
Step 106: heat treatment: steel plate progress modifier treatment after hot rolling, 910~950 DEG C of quenching and preserving heat temperature, soaking time
> 8min, it is 580~640 DEG C of tempering temperature, air-cooled after tempering.
Fig. 2 shows welding heat affected zone microscopic structures according to an embodiment of the invention；Fig. 3 shows according to the present invention one
The welding heat affected zone microscopic structure of a comparative example；Fig. 4 is shown according to an embodiment of the present invention with comparative example about former Ovshinsky
Body average grain size comparison diagram.
Table 1 is the chemical component (mass%) and steel plate Rare-Earth Ce mass percent of the embodiment of the present invention and comparative example
Comparing result.
1 embodiment and comparative example chemical component of table
Identified chemical component is controlled according to the present invention in embodiment, and controls Rare-Earth Ce mass percent in steel
It is 0.0025%, makes re inclusion ratio 80% or more of the size less than 1 micron, number density >=150/mm2, and
80% or more re inclusion size is less than 1 micron.Content of rare earth is not up to this patent requirement in the steel of comparative example 1 and 2, therefore
Type, the size and number density of steel plate field trash cannot reach requirement of the invention.
Table 2 is the embodiment of the present invention and comparative example base material performance and welding heat influence area toughness comparing result.
2 embodiment and comparative example base material performance of table and welding heat influence area toughness
The strength of parent of embodiment and comparative example does not have notable difference it can be seen from 2 data of table, and it is strong can to meet tension
Degree >=750MPa requirement.After the welding of the heat input of 25~100kJ/cm, the welding heat affected zone ballistic work of embodiment 1 is obvious
Higher than comparative example 1, especially heat input be 50kJ/cm when, 1 heat affected area ballistic work of embodiment is than 1 heat affected area of comparative example
Toughness is averagely higher by 84.5J.
At the same time, identified chemical component is controlled according to the present invention in embodiment 1, and controls Rare-Earth Ce in steel
Mass percent is 0.0025%.With the increase of thermal weld stress, it is 75kJ/ that Upper Bainite Transformation, which appears in thermal weld stress,
cm.And in comparative example 1 upper bainite produce present thermal weld stress be 50kJ/cm when.Compare comparative example 1, upper shellfish in embodiment 1
What family name's body tissue occurred is delayed by.
As shown in Figure 4, after the welding of the heat input of 25~100kJ/cm, the welding heat affected zone original austenite of embodiment 1
Average grain size is smaller.This shows that appropriate Rare-Earth Ce is added in steel can inhibit welding process Central Plains AUSTENITE GRAIN COARSENING, main
To pass through following two approach: the Ce segregation being dissolved in one side steel reduces crystal boundary energy, another aspect small and dispersed in crystal boundary
Field trash containing Rare-Earth Ce can with anchoring crystal boundary, inhibit original austenite grain grow up.
In conclusion being directed to carbon equivalent high high-strength steel, the present invention is using suitable oxygen and crucial micronutrient levels control
Technology makes to be formed in steel by the way that appropriate Rare-Earth Ce and suitable refining, continuous casting, hot rolling and heat treatment process are added into steel
Tiny, disperse field trash containing Rare-Earth Ce, and reasonably control the ingredient and quantity of these field trashes.Rare-Earth Ce is added in steel,
The small sized re inclusion anchoring original austenite crystal prevention of one side shape inhibits original austenite grain to grow up, while being dissolved
Ce inhibits the generation of upper bainite tissue in welding process, to greatly improved the weldability of carbon equivalent high high strength steel plate
Energy.The thickness specification of steel plate manufactured by the present invention is 20~60mm, and base material tensile strength >=750MPa is in thermal weld stress
Under the conditions of 50~100kJ/cm, welding heat affected zone impact flexibility >=110J.
The technology of the present invention can be used for the system of the carbon equivalent highs high-strength plank such as engineering machinery, bridge, building, pressure vessel
It makes, for improving the welding performance of steel plate.
Claims (10)
1. a kind of method for improving carbon equivalent high steel plate welding heat influence area toughness using rare earth, which is characterized in that the method
It is described successively including converter smelting step, LF refining step, RH refinement step, continuous casting step, hot-rolled step and heat treatment step
Method by being controlled in the content of LF refining step and RH refinement step to oxygen, calcium and sulfide linkage microelement in molten steel,
And Rare-Earth Ce alloy is added in RH refinement step, the field trash containing Rare-Earth Ce that thus newly-generated small and dispersed is distributed in molten steel
And by rare earth modified original field trash.
2. the method according to claim 1, wherein the described method comprises the following steps:
1) converter smelting step: iron water amount is 4:1~6:1 with clean steel scrap ratio, enters 1350~1400 DEG C of furnace molten iron temperature, iron
Sulfur content≤0.04% in water, is added lime, dolomite slag making, and oxygen blast is smelted；
2) LF refining step: station makes white slag desulfurization, and final slag composition control is CaO/SiO2=4.5:1~7.0:1, tapping oxygen contain
Amount be 0.0020~0.0060%, sulfur content < 0.0015%, 1590~1620 DEG C of molten steel temperature；
3) RH refinement step: RH arrives at a station 1580~1610 DEG C of molten steel temperature, and Rare-Earth Ce is added after 10~20min of RH application of vacuum
Alloy, total vacuum processing time > 20min, break it is empty after Control for Oxygen Content 0.0010~0.0050%, the soft stirring of BOTTOM ARGON BLOWING later
No less than 5min；
4) continuous casting step: in 1.0~1.2m/min, cast temperature is controlled at 1530~1550 DEG C casting speed control, be made with a thickness of
The continuous casting steel billet of 200~300mm；
5) hot-rolled step: 1180~1220 DEG C of first stage start rolling temperature, second stage is once to 900~930 DEG C of temperature, finish to gauge temperature
840~870 DEG C of degree, by the Rolled From Continuous Casting Slab at 20~60mm steel plate；
6) heat treatment step: to the steel plate carry out modifier treatment, 910~950 DEG C of quenching and preserving heat temperature, soaking time > 8min,
It is 580~640 DEG C of tempering temperature, air-cooled after tempering.
3. according to the method described in claim 2, it is characterized in that, converter aim carbon controls the refining lower than 0.06% in step 1)
1610~1650 DEG C of steel outlet temperature.
4. according to the method described in claim 2, it is characterized in that, Al deoxidation is added in step 1) after converter tapping, in molten steel
Al content 0.020~0.050%.
5. according to the method described in claim 2, it is characterized in that, in molten steel in step 3) Ce content be 0.0015%~
0.0040%.
6. according to the method described in claim 2, it is characterized in that, Ca content < 0.0010% in molten steel in step 3).
7. according to the method described in claim 2, it is characterized in that, step 3) in be added Rare-Earth Ce alloy before use Al deoxidation,
Oxygen content before control plus Rare-Earth Ce alloy in molten steel is between 0.0020%~0.0060%.
8. a kind of steel plate, which is characterized in that the steel plate is used and mentioned according to claim 1 to described in any one of 7 using rare earth
The method of high carbon equivalent high steel plate welding heat influence area toughness, which is smelted, to be made, and the chemical composition of the steel plate is according to mass percent
It is calculated as C:0.06~0.15%, Si:0.1~0.4%, Mn:1.0~2.0%, P≤0.02%, Nb:0.03~0.06%, V:
0.05~0.09%, Cr:0.1~0.4, Mo:0.05~0.15%, Ti:0.010~0.025%, remaining is for iron and unavoidably
Impurity element, Rare-Earth Ce content 0.0015~0.0040%.
9. steel plate according to claim 8, which is characterized in that contain Ce-Al-O, Ce-O-S and Ca-Ce- in the steel plate
One or both of O-S re inclusion, the mass percent of the chemical composition of Al, Ce, Ca, S and O is 2% in field trash
< Al < 40%, 20% < Ce < 70%, 2% < Ca < 15%, 10% < S < 40%, 2% < O < 20%, number density >=
150/mm2, and 80% or more re inclusion size is less than 1 micron.
10. steel plate according to claim 8, which is characterized in that the steel plate mother metal tensile strength >=750MPa is being welded
Under the conditions of heat input is 50~100kJ/cm, welding heat affected zone impact flexibility >=110J.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201910245642.0A CN109868342B (en) | 2019-03-28 | 2019-03-28 | Method for improving toughness of high-carbon-equivalent steel plate welding heat affected zone by using rare earth |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201910245642.0A CN109868342B (en) | 2019-03-28 | 2019-03-28 | Method for improving toughness of high-carbon-equivalent steel plate welding heat affected zone by using rare earth |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN109868342A true CN109868342A (en) | 2019-06-11 |
| CN109868342B CN109868342B (en) | 2020-02-07 |
Family
ID=66921603
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201910245642.0A Active CN109868342B (en) | 2019-03-28 | 2019-03-28 | Method for improving toughness of high-carbon-equivalent steel plate welding heat affected zone by using rare earth |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN109868342B (en) |
Cited By (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN110484811A (en) * | 2019-09-10 | 2019-11-22 | 中国科学院金属研究所 | A kind of ultra-clean rare earth steel and inclusion conditioning control method |
| CN111411197A (en) * | 2020-04-30 | 2020-07-14 | 包头钢铁（集团）有限责任公司 | Rare earth treated refined ultra-low carbon IF steel casting-rolling overall process Al2O3Method for inclusion |
| CN111534663A (en) * | 2020-05-11 | 2020-08-14 | 包头钢铁（集团）有限责任公司 | Method for refining grain size of ultra-low carbon IF steel in casting and rolling whole process by rare earth treatment |
| CN111809018A (en) * | 2020-06-17 | 2020-10-23 | 包头钢铁（集团）有限责任公司 | Method for improving hydrogen cracking resistance and hydrogen sulfide corrosion resistance of steel blank for 16MnHIC flange |
| CN111893240A (en) * | 2020-07-28 | 2020-11-06 | 北京科技大学 | Method for improving welding performance of Nb and Ti microalloyed steel by using rare earth |
| CN112143955A (en) * | 2020-08-14 | 2020-12-29 | 包头钢铁（集团）有限责任公司 | REMOM method for improving impact toughness of S355ML flange steel |
| CN112626423A (en) * | 2020-12-15 | 2021-04-09 | 包头钢铁（集团）有限责任公司 | Production process for improving welding performance of rare earth high-strength steel |
| CN114635085A (en) * | 2022-03-10 | 2022-06-17 | 包头钢铁（集团）有限责任公司 | Pure C-Si-Mn series high-cleanliness rare earth wind power steel and smelting method thereof |
Citations (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP4105989B2 (en) * | 2003-07-14 | 2008-06-25 | 新日本製鐵株式会社 | High strength welded structural steel excellent in both base metal toughness and weld zone HAZ toughness and method for producing the same |
| CN102251175A (en) * | 2010-05-20 | 2011-11-23 | 株式会社神户制钢所 | Thick steel plate |
| CN103602894A (en) * | 2013-11-12 | 2014-02-26 | 内蒙古包钢钢联股份有限公司 | High-toughness high-strength steel plate and manufacturing method thereof |
| CN103695776A (en) * | 2013-12-20 | 2014-04-02 | 宝山钢铁股份有限公司 | Thick steel plate with low carbon equivalent and excellent welding heat affected zone toughness and manufacturing method of same |
| CN104630655A (en) * | 2014-11-28 | 2015-05-20 | 武汉钢铁(集团)公司 | Extra-thick steel plate having excellent balance between strength and toughness and used for welded structure and production process thereof |
| CN105624553A (en) * | 2015-12-31 | 2016-06-01 | 江西理工大学 | High-strength steel plate with improved low-temperature impact toughness and manufacturing method thereof |
-
2019
- 2019-03-28 CN CN201910245642.0A patent/CN109868342B/en active Active
Patent Citations (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP4105989B2 (en) * | 2003-07-14 | 2008-06-25 | 新日本製鐵株式会社 | High strength welded structural steel excellent in both base metal toughness and weld zone HAZ toughness and method for producing the same |
| CN102251175A (en) * | 2010-05-20 | 2011-11-23 | 株式会社神户制钢所 | Thick steel plate |
| CN103602894A (en) * | 2013-11-12 | 2014-02-26 | 内蒙古包钢钢联股份有限公司 | High-toughness high-strength steel plate and manufacturing method thereof |
| CN103695776A (en) * | 2013-12-20 | 2014-04-02 | 宝山钢铁股份有限公司 | Thick steel plate with low carbon equivalent and excellent welding heat affected zone toughness and manufacturing method of same |
| CN104630655A (en) * | 2014-11-28 | 2015-05-20 | 武汉钢铁(集团)公司 | Extra-thick steel plate having excellent balance between strength and toughness and used for welded structure and production process thereof |
| CN105624553A (en) * | 2015-12-31 | 2016-06-01 | 江西理工大学 | High-strength steel plate with improved low-temperature impact toughness and manufacturing method thereof |
Cited By (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN110484811A (en) * | 2019-09-10 | 2019-11-22 | 中国科学院金属研究所 | A kind of ultra-clean rare earth steel and inclusion conditioning control method |
| CN111411197A (en) * | 2020-04-30 | 2020-07-14 | 包头钢铁（集团）有限责任公司 | Rare earth treated refined ultra-low carbon IF steel casting-rolling overall process Al2O3Method for inclusion |
| CN111534663A (en) * | 2020-05-11 | 2020-08-14 | 包头钢铁（集团）有限责任公司 | Method for refining grain size of ultra-low carbon IF steel in casting and rolling whole process by rare earth treatment |
| CN111809018A (en) * | 2020-06-17 | 2020-10-23 | 包头钢铁（集团）有限责任公司 | Method for improving hydrogen cracking resistance and hydrogen sulfide corrosion resistance of steel blank for 16MnHIC flange |
| CN111893240A (en) * | 2020-07-28 | 2020-11-06 | 北京科技大学 | Method for improving welding performance of Nb and Ti microalloyed steel by using rare earth |
| CN112143955A (en) * | 2020-08-14 | 2020-12-29 | 包头钢铁（集团）有限责任公司 | REMOM method for improving impact toughness of S355ML flange steel |
| CN112626423A (en) * | 2020-12-15 | 2021-04-09 | 包头钢铁（集团）有限责任公司 | Production process for improving welding performance of rare earth high-strength steel |
| CN114635085A (en) * | 2022-03-10 | 2022-06-17 | 包头钢铁（集团）有限责任公司 | Pure C-Si-Mn series high-cleanliness rare earth wind power steel and smelting method thereof |
Also Published As
| Publication number | Publication date |
|---|---|
| CN109868342B (en) | 2020-02-07 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN109868342A (en) | A method of carbon equivalent high steel plate welding heat influence area toughness is improved using rare earth | |
| CN109930070A (en) | A method of low-carbon-equivalent steel plate welding heat influence area toughness is improved using rare earth | |
| CN105256095B (en) | A kind of smelting process of the steel plate of high heat-input welding heat affected zone excellent performance | |
| CN109082591B (en) | 125ksi hydrogen sulfide stress corrosion resistant high-strength oil casing steel and preparation process thereof | |
| CN110952037B (en) | 400MPa hot-rolled refractory steel bar and manufacturing method thereof | |
| CN110184531A (en) | The tank plate and its manufacturing method of a kind of thick easily welding center portion excellent in low temperature toughness of 40-60mm | |
| JP5833767B2 (en) | Smelting method of high aluminum low silicon ultra pure ferritic stainless steel | |
| CN107236905B (en) | 600MPa grade high-strength low yield strength ratio structural steel and irons and its manufacturing method | |
| CN106086641B (en) | A kind of super-huge petroleum storage tank high-strength steel of hydrogen sulfide corrosion resistant and its manufacture method | |
| CN109385576A (en) | A kind of inexpensive X65 pipe line steel and its manufacturing method based on magnesium processing | |
| CN110343954A (en) | A kind of connection rod of automobile engine steel and its manufacturing method | |
| CN107964624A (en) | A kind of yield strength 500MPa level structure steel and preparation method thereof | |
| CN110144522B (en) | Oxide fine-grain type twisted steel and production process thereof | |
| CN109402321A (en) | The control method that oxide is mingled in a kind of ultra-low-carbon steel | |
| CN108823346A (en) | A kind of method of low cost production second level flaw detection Q345R medium plate | |
| WO2022022040A1 (en) | Low temperature-resistant hot-rolled h-type steel for 355mpa marine engineering and preparation method therefor | |
| CN105861775A (en) | Smelting process for ultra-low phosphorus steel with high nickel content | |
| CN109402510A (en) | A kind of resistance to anti-H that extremely trembles with fear2S corrodes welded tube hot rolled strip and its manufacturing method | |
| CN102191429B (en) | Method for improving high heat input welding performance of thick steel plates | |
| WO2023000479A1 (en) | Hot-rolled, low-temperature-resistant, h-shaped steel with grade of yield strength of 420 mpa, and preparation method therefor | |
| CN110117694A (en) | The magnesium adding technology method of the automatic steel containing magnesium | |
| CN108893683A (en) | A kind of sulfur resistive pipe line steel and its production method | |
| CN105714193A (en) | Oxide-enhanced high heat input welding steel plate | |
| CN109881095A (en) | A kind of B grades of acid-resistant pipeline steel plate and smelting process | |
| CN108677084A (en) | A kind of low production method for being mingled with clean steel |
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 | ||
| GR01 | Patent grant | ||
| GR01 | Patent grant |