CN105899702A - Steel material for welding - Google Patents
Steel material for welding Download PDFInfo
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- CN105899702A CN105899702A CN201580003317.3A CN201580003317A CN105899702A CN 105899702 A CN105899702 A CN 105899702A CN 201580003317 A CN201580003317 A CN 201580003317A CN 105899702 A CN105899702 A CN 105899702A
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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
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- C—CHEMISTRY; METALLURGY
- 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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/005—Heat treatment of ferrous alloys containing Mn
-
- 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
-
- 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
- C21D8/0231—Warm 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
- C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
- C21D8/0447—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment
- C21D8/0463—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment following hot rolling
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
-
- 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
- C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
-
- 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
- C21D2211/004—Dispersions; Precipitations
-
- 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
- C21D2211/008—Martensite
Abstract
The purpose of the present invention is to obtain a steel material which has a yield stress of at least 460 MPa, and which exhibits excellent weld-section toughness and joint strength, even in cases when the welding heat input is 200 kJ/cm or more. This steel material is provided with a prescribed component composition, and is configured such that: the mass percentage ratio of Ti to N is at least 2.0, but less than 4.0; the value of A specified in formula (1), namely A=2256*Ti-7716*N+10000*B, is at least 10, but not more than 25, with the caveat that each of the element symbols indicates the amount (in mass%) of each element included in the steel; Ceq specified in formula (2), namely Ceq=C+Mn/6+(Cr+Mo+V)/5+(Cu+Ni)/15, is 0.38-0.43, with the caveat that each of the element symbols indicates the amount (in mass%) of each element included in the steel; and the amount of B dissolved in the steel material is at least 5 ppm by mass.
Description
Technical field
The present invention relates to a kind of various steel structure institutes as the field such as boats and ships, civil construction
Use, yield stress is the steel material for welding of more than 460MPa, particularly relates to a kind of suitable
Close the steel of the weld heat input Large Heat Input Welding more than 200kJ/cm, specifically, relate to
Even and if one is in the case of implementing above-mentioned Large Heat Input Welding, it may have outstanding weldering
Connect the steel of portion's toughness and strength of joint.
Background technology
At the steel structure that the fields such as boats and ships, marine structure, building and steel pipe are used,
The works of desired shape is generally made by solder joints.Therefore, from guaranteeing peace
The angle of full property is set out, it is desirable to these works are except to guarantee the mother metal of used steel
Beyond characteristic, i.e. intensity and toughness, the toughness of weld part also wants outstanding.
In recent years, the steel structure of above-mentioned boats and ships etc. is more and more large-scale so that used
Steel constantly develop to high intensityization and thickeningization.Change along with these, welding procedure
The most use submerged-arc welding, gas shielded arc welding and electroslag welding etc. efficiently and the welding of large-line energy
Method, in the case of utilizing such Large Heat Input Welding to carry out welding procedure, it is also desirable to
The steel that the toughness of weld part is outstanding.
But, it is difficult to the machinery spy making high strength steel, thick steel sheet take into account mother metal seen from many places
Property (particularly low-temperature flexibility) and welding heat affected zone (Heat Affected Zone；Hereinafter,
Be designated as HAZ) the report of both low-temperature flexibilities.
For this report, such as described in patent documentation 1 and patent documentation 2,
Disclose a kind of utilize controlled rolling, control cooling realize taking into account mother metal low-temperature flexibility and
The technology of both low-temperature flexibilities of HAZ.
It follows that HAZ when explanation implements Large Heat Input Welding organizes.In HAZ with
The part that welding metal connects is commonly called " junction surface (bond portion) ".Near junction surface
The particularly fusing point that is exposed in heat affected zone of HAZ near high temperature in, accordingly, there exist
The tendency that coarse grains and toughness are remarkably decreased.On the other hand, slightly away from junction surface
Place, form softened region owing to crystal grain becomes fine grained region, it is strong that this becomes joint
The main cause that degree reduces.
As it has been described above, the toughness that Large Heat Input Welding causes HAZ reduces, for this HAZ
Toughness reduces, and also studied a lot of countermeasure so far.TiN is such as made fine to be dispersed in steel
Suppress the coarsening of austenite crystal or TiN is used as ferritic phase deformed nucleus
Such technology has obtained practical.Additionally, by making the dispersion of the oxide of Ti reach
The technology of the effect of suppression austenite crystal coarsening as described above is the most under development.
But, in the above-mentioned technology using TiN, there are the following problems: owing to accepting
When Large Heat Input Welding, welding heat affected zone is heated to the solution temperature region of TiN,
This make TiN decompose and cause above-mentioned dispersion effect to disappear, or due to TiN decomposition and
The solid solution Ti produced and solid solution N causes the basic organization embrittlement of steel, and these all make sweating heat
The toughness affecting portion significantly reduces.
Additionally, in the technology using Ti oxide, exist and be difficult to make oxide uniformly, carefully
Disperse such problem micro-ly.As the technology of solution problems, such as at patent documentation 3
In disclose following technology: implement the Large Heat Input Welding more than 200kJ/cm to improve
The toughness of welding heat affected zone, the addition to the Ca that the form controlling sulfide is used
Suitably adjust, make CaS crystallize, and precipitate is come as ferritic phase deformed nucleus
It is efficiently used.
Compared with oxide, above-mentioned CaS crystallizes at low temperatures, therefore, it is possible to fine divide
It is dispersed in steel, and, when steel plate cools down, the ferrite transformation such as MnS, TiN, BN
Generate core fine to disperse as core such that it is able to make the group of welding heat affected zone
Knit the Ferrite-Perlite structure being formed as trickle, and be capable of high tenacity.Therefore,
Utilize the technology of patent documentation 3, it is possible to suppress to a certain extent to weld along with large-line energy
The HAZ toughness connect is low.
But, research afterwards finds, for having carried out making the yield stress of steel plate reach
The high intensity of more than 460MPa, and for the addition of the steel of larger amount of C, alloying element,
When carrying out the weld heat input Large Heat Input Welding more than 200kJ/cm, near junction surface
HAZ on will be formed several volume % to be referred to as island-like martensite (following, at this
In bright, be also denoted as MA) hard brittle microstructures, this brittle microstructures stop weld part toughness
Improve further.
I.e., it was found that at the junction surface in such Large Heat Input Welding portion improving high strength steel
Neighbouring HAZ toughness aspect, except austenite crystal coarsening to be suppressed, makes ferritic phase
Beyond deformed nucleus fine dispersion, minimizing solid solution N, there is a need to suppress the life of island-like martensite
Become.
About the technology of the island-like martensite reducing HAZ portion, such as, in patent documentation 4
Disclose following technology: in addition to reducing the content of C, Si and being effective, reduce P's
Content is the most effective for the island-like martensite reducing HAZ portion.
And, in patent documentation 5, by adding Mn energetically and reducing P with doing one's utmost,
It is obtained in that and reduces the island-like martensite of HAZ near junction surface and the outstanding surrender of toughness should
Power is the steel of 460MPa degree.
On the other hand, the HAZ brought along with Large Heat Input Welding about suppression softens
Technology, and the undisclosed content so much as HAZ toughness countermeasure.Above-mentioned patent documentation 3,
Patent documentation any one of 4 and 5 does not describes yet and softens relevant content to HAZ.Permissible
Think and reason for this is that, when carrying out the design of initial high input energy welding steel,
To be able to ensure that strength of joint is as premise.
The content softened accordingly, with respect to suppression HAZ, illustrates published technology.
In these techniques, exist and utilize technology and the utilization of the precipitation strength elements such as Nb, V
The technology of the effect that the quenching property brought by B improves.
Such as in patent documentation 6, while improving C amount, reduce the amount of Si, Mn, and
And by comprising Nb, V, reduce HAZ with this and soften.
On the other hand, in patent documentation 7, in order to the quenching property realizing being brought by B carries
Height, is suppressed containing Ti, B and Nb such empirical formula more than N amount by regulation
HAZ softens.
Additionally, in patent documentation 8, measured by regulation solid solution B, it is achieved brought by B
Quenching property improves, thus suppresses HAZ to soften.
Patent documentation 1: Japanese Laid-Open Patent Publication 57-134518 publication
Patent documentation 2: Japanese Laid-Open Patent Publication 59-83722 publication
Patent documentation 3: No. 3546308 publications of Japanese Patent Publication No.
Patent documentation 4: Japanese Unexamined Patent Publication 2008-163446 publication
Patent documentation 5: Japanese Unexamined Patent Publication 2011-6772 publication
Patent documentation 6: Japanese Laid-Open Patent Publication 60-67622 publication
Patent documentation 7: Japanese Unexamined Patent Publication 2007-177327 publication
Patent documentation 8: No. 4233033 publications of Japanese Patent Publication No.
But, exist especially as it has been described above, the technology described in patent documentation 3 is a kind of improvement
For the steel that yield stress is 390MPa degree implement when Large Heat Input Welding,
The technology of the toughness at junction surface, for improving further for yield strength, such as surrender should
Power: for the large-line energy HAZ toughness of the steel of 460MPa degree and HAZ soften, have
Time can not tackle fully.
Additionally, yield stress is 460MPa degree by the technology described in patent documentation 4
Steel, as object, reduce near junction surface by reducing the content of C, Si and P
The island-like martensite of HAZ, and make ferritic phase deformed nucleus trickle by adding the addition of C a
Ground dispersion, so that it is guaranteed that HAZ toughness, but in the document, HAZ is not softened and carry out
Describe, and, because Ni must be added and probability that existence can cause cost of alloy to improve.
Additionally, yield stress is 460MPa degree by the technology described in patent documentation 5
Steel are as object, by using Mn to reduce island-like martensite energetically, thus inexpensively
Steel needed for ground acquisition, but, it is still as patent documentation 4, not about HAZ
The description softened.
On the other hand, although the technology described in patent documentation 6 have employed raising C amount and makes
By the method for the precipitation strength elements such as Nb, V, HAZ softening is fully processed, but order
People is worried, can form a large amount of island near junction surface on HAZ when Large Heat Input Welding
Shape martensite, so that the toughness of the HAZ near junction surface significantly reduces.
Press down additionally, the technology described in patent documentation 7 and 8 is the quenching property using B
HAZ processed soften technology, patent documentation 7 therein be add substantial amounts of Ti, B and
Premised on N, worrying, there is the problem in terms of manufacturing property, make us load simultaneously
The heart can cause the toughness of HAZ because of solid solution N in the TiN melting range near junction surface
Reduce.
In addition, the technology described in patent documentation 8 is premised on there is not Nb,
Using yield stress: the steel of 460MPa degree, as in the case of object, remain and are difficult to really
Protect the such problem of strength of joint.
Summary of the invention
The present invention develops in view of the foregoing, its object is to provide at a low price
Even if a kind of weld heat input Large Heat Input Welding more than 200kJ/cm that implements, still in weldering
Meet the HAZ toughness side near the hardness of heat affected zone does not reduces, softening resistance and junction surface
Face outstanding, yield stress be the high input energy welding steel material of more than 460MPa.
In order to solve above-mentioned problem, inventors to tissue factor to for yield stress being
The high strength steel of more than 460MPa implements the weld heat input big line more than 200kJ/cm
During energy welding, HAZ toughness near junction surface and HAZ region, softening portion hard
The impact that degree brings studies in detail.Itself found that: about the HAZ near junction surface
Toughness, even if also can produce harmful effect, phase to toughness with the presence of a small amount of island-like martensite
Instead, the hardness in region, softening portion can be improved by producing island-like martensite.
Therefore, inventors are for the island-like martensite at the HAZ suppressed near junction surface
On the basis of generation, the method improving the growing amount of the island-like martensite in region, softening portion is entered
Go research.Itself found that: for the HAZ near junction surface, by C, Si,
P amount suppress relatively low while, by contain energetically Mn make up by C measure reduction cause
Strength of parent decline, it is possible to do not produce as far as possible and the HAZ toughness near junction surface brought not
The island-like martensite of good impact, is effectively improved strength of parent.
It moreover has been found that by Ti, N and the B in region, softening portion is controlled suitably
In the range of and application B raising quenching property effect, it is possible to do not increase near junction surface
The island-like martensite ground of HAZ promotes the formation of the island-like martensite in region, softening portion.
I.e., for B, near the junction surface in the high temperature being exposed near fusing point
In HAZ, be not produced from the generation along with top bainite, growth and away from the shifting of crystal boundary
Dynamic to remain in quenching of the non-transformed austenite between lath of bainite (bainite lath)
Fire performance is not improved, but, at the HAZ that the temperature-rise ratio brought by heat affecting is less
In softened region, B is along with ferrite transformation diffusion and by non-transformed austenite
Occur segregation to make its quenching property improve on crystal boundary, thus exist and promote island-like martensite
The effect formed.
But, HAZ softened region is less because of the temperature-rise ratio brought by heat affecting, institute
Almost not produce the dissolving of precipitate, the amount of the B contributing to quenching property depends on
State during manufacturing process.And, each in the controlled rolling of mother metal manufacturing process and cooling
In the individual stage, B forms nitride sometimes because of the difference of manufacturing condition, in this case, it is impossible to
Play its effect improving quenching property.
Therefore, inventors through the most repeatedly studying, found that: in steel plate manufacture
In operation, the precipitation of B nitride can be limited by the following method as far as possible, and together with upper
The composition optimization stated is together, it is thus achieved that outstanding HAZ characteristic, so far, develops the present invention,
The method is as follows: first, initially after austenite recrystallization temperature region implements rolling,
Accelerate to be cooled to austenite non-recrystallization temperature province, then implement austenite non-recrystallization temperature
The rolling of degree region, afterwards, is again carried out accelerating cooling.
I.e., the primary structure of the present invention is as follows.
1. a steel material for welding, it contains C:0.030 mass %～0.080 mass %, Si:
0.01 mass %～0.10 mass %, Mn:1.80 mass %～2.40 mass %, P:0.010
Below quality %, S:0.0005 mass %～0.0040 mass %, Al:0.005 mass %～
0.100 mass %, Nb:0.003 mass %～0.030 mass %, Ti:0.010 mass %～
0.050 mass %, N:0.0030 mass %～0.0120 mass % and B:0.0005 mass
%～0.0025 mass %, and quality % of Ti and N ratio (Ti/N) is more than 2.0 and not
Foot 4.0, below formula son (1) in regulation A value be less than more than 3 25, following
Formula (2) in the scope that Ceq is 0.38～0.43 of regulation, remaining part is not by Fe and not
The one-tenth that evitable impurity is constituted is grouped into, and yield stress is more than 460MPa and solid solution B
Amount is more than 5 mass ppm, is implementing the line energy of weld heat input: more than 200kJ/cm
During amount welding, the island-like martensite in tissue near the junction surface of heat affected zone is 1vol%
Hereinafter, and heat affected zone region, softening portion tissue in island-like martensite be 5vol%
Above.
A=2256 × Ti-7716 × N+10000 × B ... (1)
Ceq=C+Mn/6+ (Cr+Mo+V)/5+ (Cu+Ni)/15 ... (2)
Wherein, quality % content during each symbol of element represents the steel of each element.
2., according to the steel material for welding described in upper note 1, state in being grouped into thereon, possibly together with
Below V:0.20 mass %, below Cu:0.30 mass %, below Ni:0.30 mass %,
Select in below Cr:0.40 mass % and below Mo:0.40 mass % more than one
Element.
3., according to the steel material for welding described in upper note 1 or upper note 2, state in being grouped into thereon,
Possibly together with from Ca:0.0005 mass %～0.0050 mass %, Mg:0.0005 mass %～
0.0050 mass %, Zr:0.0010 mass %～0.0200 mass %, REM:0.0010 matter
More than one the element selected in amount %～0.0200 mass %.
Invention effect
Use the present invention, it is possible to obtain when implementing Large Heat Input Welding, have concurrently good
Strength of joint and the steel of welding heat affected zone toughness, for by submerged-arc welding, electroslag welding this
The Large Heat Input Welding of sample and the boats and ships that are built into, the quality of large structure improve have bigger
Help.Particularly, if in thickness of slab is more than the steel of 50mm apply the present invention, with
Compare toward the steel in technology, welding strength of joint and welding heat affected zone toughness this
Two aspects, demonstrate more significant superiority.
Detailed description of the invention
It follows that illustrate the present invention.Additionally, in the present invention as the steel of object
Refer to the steel manufactured by hot rolling.
In the present invention, important be control respectively the one-tenth of steel be grouped into, intensity and because of super
In the softened region of the welding heat affected zone crossing the Large Heat Input Welding of 200kJ/cm and formed
Minimum hardness (hereinafter also referred to as the hardness in HAZ region, softening portion).
First, to the island-like martensite of the heat affected zone of the feature of the steel as the present invention
Volume fraction illustrates.
The island-like martensite in tissue near the junction surface of heat affected zone is below 1vol%
In welding heat affected zone (HAZ), it is exposed in high temperature occur Austria by suppression
The generation of the island-like martensite near family name's body coarsening, heat affected zone junction surface, it is possible to
Improve the toughness in Large Heat Input Welding portion.In order to obtain such effect, need to connect above-mentioned
The volume fraction of the island-like martensite near conjunction portion suppresses at below 1vol%.Additionally, it is above-mentioned
The lower limit of the volume fraction of island-like martensite is also not particularly limited, even 0vol% also may be used.
Additionally, refer to start at from junction surface 600 μm near the junction surface of the heat affected zone of the present invention
Within the welding heat affected zone of scope, this tissue be in addition to have above-mentioned island-like martensite with
Outward, based on acicular ferrite, bainite, and comprise ferrite, pearlite known
Tissue.
The island-like martensite in the region, softening portion of heat affected zone is more than 5vol%
The joint welded the steel of yield stress: more than 460MPa and produce needs to reach
More than 570MPa is reached to the tensile strength identical with mother metal, i.e. tensile strength.Here,
Tensile strength as butt joint produce the factor of impact, mainly welding metal intensity,
The hardness etc. in thickness of slab, HAZ region, softening portion, the particularly district of softening portion of heat affected zone
The impact that the tissue in territory brings is bigger.And, yield stress is the steel of more than 460MPa
The tissue of softened region be ferrite and the second phase constitution, as the second phase constitution, it is possible to
By producing the island-like martensite of the volume fraction of more than 5vol%, it is thus achieved that desired joint is strong
Degree.
Additionally, in the present invention, the softened region of heat affected zone refers to distance junction surface
About 10mm, after by the heating that brought by welding, austenitic formation is trickle
The heat affected zone of grain.
Additionally, in the present invention, the region, softening portion of heat affected zone refers to 1mm
Measurement vickers hardness hv (JIS Z 2244 (1998)) in clathrate at equal intervals of left and right,
Centered by the point representing lowest hardness, the point of measurement everywhere nearest for distance center is connected each other
The region got up.
In the present invention, in order to carry out as above institute at the tissue in the region, softening portion to HAZ
While the control stated, it is achieved high intensity, the one-tenth that steel should be had be grouped into make as
Lower regulation.Additionally, below, the % being grouped into about the one-tenth of steel refers to quality %.
C:0.030 mass %～0.080 mass %
C is the element of the intensity for improving steel, needed for as structural steel
Intensity, C needs more than containing 0.030 mass %.On the other hand, if C is more than 0.080
Quality %, easily the MA of the HAZ near generation junction surface, therefore, is set to 0.080 by the upper limit
Quality %.
Si:0.01 mass %～0.10 mass %
Si is the element added as deoxidizer during molten steel, needs to add 0.01 mass
More than %.On the other hand, if it exceeds 0.10 mass %, except the toughness of mother metal reduce with
Outward, near the junction surface of Large Heat Input Welding, HAZ produces MA, is easily caused tough
Property reduce.Then, Si is set in the range of 0.01 mass %～0.10 mass %.
Mn:1.80 mass %～2.40 mass %
Mn is for improving the element of intensity as C, than the alloy being referred to as Mo, V
Element is cheap, and does not promote that the MA of the HAZ near junction surface generates, therefore, at this
Invention is added energetically.And, in order to ensure desirable strength and obtain the effect above,
Need to add more than 1.80 mass %, more preferably add more than 1.90 mass %, the most excellent
More than 2.00 mass % are added in choosing.On the other hand, if the Mn containing excess, damage on the contrary
Toughness of welded zone, needs to add below 2.40 mass %, more preferably add 2.20 mass % with
Under, further preferably add below 2.10 mass %.
Below P:0.010 mass %
P is the one of the element contained as impurity, because it makes steel plate mother metal and HAZ
Toughness reduce, it is advantageous on the basis of in view of economy when founding blank,
Its content is reduced in possible scope.Therefore, P amount is limited in below 0.010 mass %.
Below preferably 0.008 mass %.
S:0.0005 mass %～0.0040 mass %
S be for formed the MnS that plays a role as ferritic nucleation site or
The essential elements of CaS.Therefore, more than 0.0005 mass % is added.But, if excessively
Add, instead result in base metal tenacity and reduce, therefore, the upper limit is set to 0.0040 mass %.
Al:0.005 mass %～0.100 mass %
Al is the element added for the deoxidation of steel, needs containing more than 0.005%.Another
Aspect, if content is more than 0.100 mass %, not only can make the toughness of mother metal decline, and
Also the toughness that can make welding metal declines.Then, Al is set in 0.005 mass %～0.100
In the range of quality %.Preferably 0.010 mass %～the scope of 0.100 mass %.
Nb:0.003 mass %～0.030 mass %
Nb is to guaranteeing that strength of parent, HAZ softening portion hardness and strength of welded joint have
The element of effect.But, in the case of addition is less than 0.003 mass %, the effect above will
Can diminish, if but content is more than 0.030 mass %, it will the HAZ near junction surface
Produce MA and make toughness reduce.Then, Nb is set in 0.003 mass %～0.030
In the range of quality %.
Ti:0.010 mass %～0.050 mass %
Ti can form TiN when solidification and separate out, the austenite of HAZ near suppression junction surface
The coarsening of crystal grain.Additionally, Ti contributes to the height of HAZ becoming ferritic phase change core
While malleablization, guarantee solid solution B by reducing the N to be combined with B, guaranteeing HAZ
Effectively play a role on the basis of softening portion hardness and strength of welded joint.In order to obtain
Obtain such effect, need to add more than 0.010 mass %, preferably add 0.015 mass %
Above.On the other hand, if content is more than 0.050 mass %, the TiN of precipitation will be thick
Change, it is impossible to obtain the effect above.Then, Ti is set in 0.010 mass %～0.050 matter
In the range of amount %.
N:0.0030 mass %～0.0120 mass %
N forms TiN when solidification, contributes to suppressing the austenite of the HAZ near junction surface
The coarsening of crystal grain, meanwhile, N produces BN, this BN and plays as ferritic phase deformed nucleus
Effect makes the tissue granular of the HAZ near junction surface, contributes to the high tenacity of steel.
And, reach requirement in order to ensure such TiN, needing containing N is 0.0030 matter
Amount more than %, preferably comprises more than 0.0050 mass %.More preferably contain 0.0070 mass
More than %.On the other hand, if excessively containing N, in the difference according to weld heat input condition,
And in the region making TiN melt, solid solution N measures increase, the toughness of HAZ is made to reduce on the contrary.
Therefore, the upper limit is set to below 0.0120 mass %.It is preferably set to below 0.0100 mass %.
B:0.0005 mass %～0.0025 mass %
B is the element of the quenching property for improving steel, by reducing the phase alternating temperature of austenite
Degree promotes the generation of the such hard tissue of bainite, martensite, contributes to mother metal steel plate
High intensity.Equally, the ferritic product as soft phase in HAZ softening portion is also suppressed
Raw so that the intensity in HAZ softening portion improves.In order to obtain such effect, need containing
B is more than 0.0005 mass %.On the other hand, if the content of B is more than 0.0025 mass
%, will cause quenching property superfluous, and the toughness instead resulting in mother metal steel plate and HAZ reduces.
Therefore, B is set in the range of 0.0005 mass %～0.0025 mass %.
Solid solution B amount is set to more than 5 mass ppm
In the present invention, the amount of the solid solution B in steel is set to more than 5 mass ppm.At steel
In solid solution B amount less than 5ppm in the case of, when organizing the formation of of HAZ softened region
It is not sufficiently effective that the quenching property making non-transformed austenite improves, it is impossible to obtains and is used for obtaining institute
The island martensite scale of construction of desired hardness.
Quality % ratio (Ti/N) of Ti and N: more than 2.0 and less than 4.0
Ti/N is defined as A value described later, and meanwhile, in the present invention, Ti/N is important
Key element.Ti/N is for junction surface, the TiN fine dispersion situation of HAZ with by solid solution N
The toughness deterioration caused has considerable influence, needs to control aptly.If i.e. Ti/N
It is more than 4.0, does not separates out due to BN and the precipitation such as the boron-carbide of Ti, cause HAZ
Toughness is greatly reduced, if but Ti/N is less than 2.0, the HAZ toughness caused due to solid solution N
Reduce and HAZ BN separate out, it is impossible to guarantee the quenching property of B, thus be difficult to ensure that
Required HAZ softening portion hardness.Therefore, the value of Ti/N is set to more than 2.0 and not enough
4.0.Preferably, the value of Ti/N is more than 2.5 in the scope of less than 3.5.
A value: less than more than 3 25
In formula (1) shown below, the A value of regulation is of paramount importance item in the present invention
One of mesh.When steel are by the thermal process suitable with the heat affected zone of Large Heat Input Welding,
Even if the generation of TiN, BN etc. is reacted not in the case of carrying out with meeting balance theory, for
Solid solution B is made to have given play to the effect improving quenching property, except in terms of Ti, N and B
On the basis of meeting the addition of above-mentioned steel, in addition it is also necessary to A value is more than 3.But,
If A value is more than 25, the quenching property of steel will be superfluous, thus the toughness to HAZ
Produce harmful effect.Therefore, in the present invention, A value is set to less than more than 3 25.Excellent
Elect the scope of 6～15 as.
A=2256 × Ti-7716 × N+10000 × B ... (1)
Wherein, content (quality during each symbol of element (Ti, N, B) represents the steel of each element
%).
Ceq: 0.38～0.43
The high input energy welding steel material of the present invention, due to heat input during welding, causes in system
The effect of the organizational controls such as the TMCP implemented when making mother metal is completely ineffective.Therefore, even if
Welding time heating and cooling under, it is also desirable to take into account intensity and the toughness of welding point, institute
To need carbon equivalent C of the index as quenching propertyeqControl in suitable scope.
In particular, it is desirable to so that carbon equivalent C defined in below formula (2)eqFor
The mode of the scope of 0.38～0.43 controls the composition of each composition.At above-mentioned Ceq less than 0.38
Time, quenching property is not enough, and the hardness in region, softening portion significantly reduces, therefore, it is impossible to really
The intensity of the welding point desired by guarantor.On the other hand, if CeqMore than 0.43, then quench
Performance is superfluous, and the ferritic generation near junction surface is suppressed, and promotes island martensite
Body produces, therefore, it is impossible to guarantee sufficient toughness.Preferably, Ceq0.39～0.42
In the range of.
Ceq=C+Mn/6+ (Cr+Mo+V)/5+ (Cu+Ni)/15 ... (2)
Here, each symbol of element in above-mentioned formula represent respective element (C, Mn,
Cr, Mo, V, Cu, Ni) content (quality %).
In the basis of the above present invention forms, remaining part is exactly that Fe is with inevitable
Impurity.Additionally, as the impurity that can not keep away, as long as such as O is less than 0.0050% with regard to energy
Enough it is allowed to.
In the steel of the present invention, in addition to mentioned component, for the purpose of improving intensity etc.,
Can be containing selected among V, Cu, Ni, Cr and Mo in the range of lower note
Plant above element as optional element.
Below V:0.20 mass %, below Cu:0.30 mass %, Ni:0.30 mass % with
Under, below Cr:0.40 mass % and below Mo:0.40 mass %
V, Cu, Ni, Cr and Mo are the effective elements of the high intensityization to mother metal, for
Obtain this effect, it is preferred that V, Cu and Ni add more than 0.05 mass %, Cr
More than 0.02 mass % is added with Mo.But, if adding any one element in a large number, all
Toughness will be produced harmful effect, also have, Ni is related to cost of alloy to be increased, therefore,
In the case of containing these elements, it is desirable to V is set to below 0.20 mass %, by Cu
It is set to below 0.30 mass %, Ni is set to below 0.30 mass %, Cr and Mo is set
It it is below 0.40 mass %.
And, the steel of the present invention are in addition to mentioned component, it is possible in the range of lower note
Containing more than one elements selected among Ca, Mg, Zr and REM as optional unit
Element.
Ca:0.0005 mass %～0.0050 mass %
Can change to obtain the toughness fixing, that brought of S by dispersal oxide, sulfide
It is apt to effect and contains Ca.In order to obtain the effect above, it is preferred that at least contain 0.0005
Quality %.But, even if addition is more than 0.0050 mass %, the most simply the effect above reaches
To saturated.Then, in the case of containing Ca, be preferably set to 0.0005 mass %～
The scope of 0.0050 mass %.
Mg:0.0005 mass %～0.0050 mass %, Zr:0.0010 mass %～0.0200
Quality %, REM:0.0010 mass %～0.0200 mass %
Any one in Mg, Zr and REM, is all to have dispersal oxide to bring toughness
Improve the element of effect.In order to embody such effect, it is preferred that be 0.0005 containing Mg
It is more than 0.0010 mass % more than quality %, containing Zr and REM.On the other hand, i.e.
Make the Mg of interpolation more than 0.0050 mass %, interpolation Zr and REM more than 0.0200 matter
Amount %, is also that this effect reaches saturated.Then, in the case of containing these elements,
Preferably they are set in above-mentioned scope.
Manufacture method
Preferably, use the welding method that converter or electric furnace etc. are commonly used to having above-mentioned one-tenth
The steel being grouped into is founded, and utilizes continuous casing or ingot casting method etc. to commonly use
Operation forms the slab raw material for manufacturing steel plate.Hereinafter, for the present invention use preferred
Steel plate manufacturing condition illustrate.
Heating-up temperature: 1050 DEG C～1200 DEG C
In order to make the complete solid solution of Nb carbonitride in steel billet, it is preferred that adding steel billet
Hot temperature is set as more than 1050 DEG C.On the other hand, if heating-up temperature is more than 1200 DEG C,
The coarsening of austenite crystal particle diameter will be caused when heating, base metal tenacity is brought bad shadow
Ring, it is therefore preferable that the upper limit to be set to 1200 DEG C.
The rolling in austenite recrystallization temperature region
The austenite crystal that the rolling in austenite recrystallization temperature region has when making heating is certain
The effect of degree granular, it is desirable to minimum more than 1 time rolling, it is preferred that implement accumulation
Reduction ratio more than 20%.As long as the steel of mentioned component scope, austenite recrystallization temperature district
The lower limit temperature in territory the most about 900 DEG C～the scope of 1000 DEG C.
The coldest from austenite recrystallization temperature region to austenite non-recrystallization temperature province
But
This operation is one of of paramount importance project among manufacturing process.As it has been described above,
In HAZ softened region, it is possible to the solid solution B amount making the quenching property of tissue improve is equivalent to
The solid solution B amount being able to ensure that under state when manufacturing steel plate.
Therefore, have the nitride of a large amount of B to separate out when manufacturing steel plate in the case of, there is use
Not enough in the solid solution B guaranteeing quenching property, cause to obtain enough in HAZ softened region
The situation of hardness.
Further, it is desirable in cooling procedure when manufacturing steel plate, produce with the nitride of B
Temperature province suitable, from austenite recrystallization temperature region to austenite non-recrystallization temperature
The rate of cooling in region is the fastest.Generally, this operation is treated as the temperature reduction of hot rolling
The machine time and carry out air cooling, but in the present invention, by enforcement, there is the cooling than air cooling
The acceleration cooling of fireballing rate of cooling, rolls shortening the arrival control as next procedure
While the time of operation processed, it is possible to prevent the solid solution B that the precipitation of the nitride because of B causes
Minimizing.Additionally, this acceleration cooling is particularly from the temperature range of 1000 DEG C to 600 DEG C
Interior enforcement is effective.
In the present invention, in order to the rolling of austenite non-recrystallization temperature province described later after
Cooling distinguish, and then rolling in austenite recrystallization temperature region is implemented
Acceleration cooling be referred to as once cool down.In this once cools down, it is preferred that utilize water-cooled
Accelerate cooling device or remove the oxide skin produced on surface of steel plate in rolling
So-called rust removalling equipments etc., reach the rate of cooling faster than air cooling.Specifically, preferably 3
Rate of cooling more than DEG C/sec.
The rolling of the accumulation reduction ratio more than 40% of austenite non-recrystallization temperature province
The most above-mentioned acceleration cools down, and implements controlled rolling in austenite non-recrystallization temperature province.
In the case of accumulation reduction ratio during this controlled rolling is less, it is difficult to obtain regulation
Base metal tenacity.Therefore, the lower limit of accumulation reduction ratio is set to 40%.Although it is desirable to accumulation pressure
Lower rate is higher, but in industrial aspect, exists about 80% as the situation of the upper limit, excellent
Choosing is 50%～80%.
After the rolling of austenite non-recrystallization temperature province, from Ar3Temperature more than transformation temperature arrives
The cooling twice of the temperature province of less than 550 DEG C
Cooling twice is so that the austenite structure being processed into by controlled rolling is undergone phase transition
For the purpose of cooling.And, in order to make the phase transformation of tissue complete, require cool to 550 DEG C with
Under temperature province, the lower limit preferably having cooled down temperature is 550 DEG C.The cooling of cooling twice
Speed is to need the rate of cooling faster than air cooling, preferably carries out the pressure cooling of more than 5 DEG C/sec.
It is more preferable that carry out the pressure cooling of more than 10 DEG C/sec.Cooling means limits the most especially
Fixed, it is desirable to be the cooling of water-cooled.
Here, the steel temperature of the present invention represents surface temperature and the thickness of slab central part of steel
The mean temperature of temperature.Ar3Transformation temperature is different according to the composition of steel, therefore, it is possible to
Obtain according to following formula simply.Additionally, in following formula, each symbol of element represents each element
Content (quality %) in steel.0 it is expressed as in the case of not containing.
Ar3(DEG C)=910-273C-74Mn-56Ni-16Cr-9Mo-5Cu
Embodiment
After utilizing converter to found out the steel with the composition shown in table 1, utilize casting continuously
Method forms slab, then utilizes the controlled rolling shown in table 2, control cooling condition to produce
The steel plate that 40mm～80mm is thick.Secondary numbering shown in table 2 represents that composition of steel is identical but manufactures
The situation that condition is different.Additionally, once cooling is the water by being arranged on roll mill outlet side
Cool equipment is implemented, it is thus identified that the average cooling rate in cooling is more than 3 DEG C.
[table 1]
[table 2]
Table 2
For utilizing above-mentioned composition and via steel plate out manufactured by manufacturing process, from plate
The tension test sheet of parallel portion 14mm Φ is taken off in the position in thick direction 1/4, based on JIS Z 2241
(1998) regulation implements tension test, and has obtained 0.2% endurance (YS) and tension
Intensity (TS).
Additionally, from the position in thickness of slab direction 1/4, be defined as based on JIS Z 2202 (1998)
Standard, takes off v-notch standard-sized Charpy-type test sheet, and based on JIS Z 2242
(1998) regulation implements impact test, has obtained fracture transition temperature (vTrs).
Here, the desired value of vTrs is less than-60 DEG C.
Additionally, in order to the heat input implementing weld heat input: more than 200kJ/cm is welded
When, the hardness in the region, softening portion of heat affected zone is evaluated, from thickness of slab direction 1/4
The small specimen of 3mm Φ × 10mm is taken off in position, just goes up being heated to be equivalent to transformation temperature
After the temperature of position 900 DEG C, perform carry out between 800 DEG C～500 DEG C 390 seconds cold
But heat treatment.It is that clathrate is measured and processed it performing these with the interval of about 1mm
After the vickers hardness hv (JIS Z 2244 (1998)) of small specimen, will be
Low hardness is as softening portion hardness.The desired value of softening portion hardness is set to more than 160.
Additionally, HAZ is centered by region, softening portion is the point to represent lowest hardness, will apart from
What the heart was nearest measures the region that point is connected with each other.
Additionally, utilize nitric acid ethanol (nital) corrosive liquid pair and above-mentioned HAZ district of softening portion
Corresponding position, territory is etched and has revealed tissue.SEM is used to clap under 1000 times
Take the photograph the macrograph in 3 visuals field, and it is carried out image analysis, obtain the average of MA
Area fraction, then using the average area fraction of this MA as HAZ region, softening portion
MA volume fraction (vo1%).
In order to implement weld heat input: more than 200kJ/cm heat input weld when,
Near the junction surface of heat affected zone, the toughness in portion is evaluated, and takes off width from above-mentioned steel plate:
80mm × length: the test film of 80mm × thickness: 15mm, is then being heated to 1450 DEG C
Afterwards, after carrying out cooling in 390 seconds between 800 DEG C～500 DEG C, take off 2mmV type and cut
Mouth Charpy test sheet, same as above, the impact test temperature of Charpy-type test will be performed
It is set to-40 DEG C, and utilizes three meansigma methodss tested to be evaluated.Desired value is set to-40
DEG C average absorption energy (vE-40DEG C) be more than 50J.Additionally, same as above, right
The area fraction of the MA in the test film cross section after thermal process enforcement is evaluated.
Table 3 shows by upper note order implement the steel after evaluation mother metal characteristic,
The measurement result of the MA volume fraction (vol%) in HAZ characteristic and HAZ.
[table 3]
Table 3
[note 1] underscore represents the content outside the scope of the invention.
According to this table: in the example of secondary numbering A of steel plate composition No.1～12, energy
Enough obtain mother metal and the outstanding characteristic of HAZ.On the other hand, for steel plate composition No.1～
For the steel plate of secondary numbering B of 4, affected by manufacturing condition, the not met present invention's
Key element, mother metal characteristic and HAZ characteristic are poor.No.13～27 is formed at steel plate additionally, understand
In, chemical composition is outside the scope that present invention provide that, therefore, even secondary numbering A,
HAZ characteristic is the poorest.
Claims (3)
1. a steel material for welding, it contains C:0.030 mass %～0.080 mass %, Si:
0.01 mass %～0.10 mass %, Mn:1.80 mass %～2.40 mass %, P:0.010
Below quality %, S:0.0005 mass %～0.0040 mass %, Al:0.005 mass %～
0.100 mass %, Nb:0.003 mass %～0.030 mass %, Ti:0.010 mass %～
0.050 mass %, N:0.0030 mass %～0.0120 mass % and B:0.0005 mass
%～0.0025 mass %, and quality % of Ti and N ratio (Ti/N) is more than 2.0 and not
Foot 4.0, this steel material for welding is characterised by,
Below formula son (1) in regulation A value be less than more than 3 25, following
The scope that Ceq is 0.38～0.43 of regulation in formula (2), remaining part is by Fe and can not
The one-tenth that the impurity avoided is constituted is grouped into, and yield stress is more than 460MPa and solid solution B
Amount is more than 5 mass ppm, is implementing the line energy of weld heat input: more than 200kJ/cm
During amount welding, the island-like martensite in tissue near the junction surface of heat affected zone is 1vol%
Hereinafter, and heat affected zone region, softening portion tissue in island-like martensite be 5vol%
Above,
A=2256 × Ti-7716 × N+10000 × B ... (1)
Ceq=C+Mn/6+ (Cr+Mo+V)/5+ (Cu+Ni)/15 ... (2)
Wherein, quality % content during each symbol of element represents the steel of each element.
Steel material for welding the most according to claim 1, wherein,
In described one-tenth is grouped into, possibly together with below V:0.20 mass %, Cu:0.30
Below quality %, below Ni:0.20 mass %, below Cr:0.40 mass % and Mo:
More than one the element selected in below 0.40 mass %.
Steel material for welding the most according to claim 1 and 2, wherein,
In described one-tenth is grouped into, possibly together with from Ca:0.0005 mass %～0.0050 mass
%, Mg:0.0005 mass %～0.0050 mass %, Zr:0.0010 mass %～0.0200
More than one the unit selected in quality %, REM:0.0010 mass %～0.0200 mass %
Element.
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| PCT/JP2015/001417 WO2015141203A1 (en) | 2014-03-17 | 2015-03-13 | Steel material for welding |
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| CN108676975A (en) * | 2018-06-01 | 2018-10-19 | 马鞍山钢铁股份有限公司 | The heat treatment method of segregation defects in a kind of removal metal welding seam |
| CN110257612A (en) * | 2019-06-17 | 2019-09-20 | 首钢集团有限公司 | A kind of preparation method of low residual stress low alloy high strength steel plate |
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| WO2016060141A1 (en) * | 2014-10-17 | 2016-04-21 | Ｊｆｅスチール株式会社 | Steel for high-energy-input welding |
| CN116171335A (en) * | 2020-09-30 | 2023-05-26 | 杰富意钢铁株式会社 | Steel plate |
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| KR20160117536A (en) | 2016-10-10 |
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| TW201538746A (en) | 2015-10-16 |
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