CN105899702B - Steel material for welding - Google Patents
Steel material for welding Download PDFInfo
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- CN105899702B CN105899702B CN201580003317.3A CN201580003317A CN105899702B CN 105899702 B CN105899702 B CN 105899702B CN 201580003317 A CN201580003317 A CN 201580003317A CN 105899702 B CN105899702 B CN 105899702B
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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
- 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
- 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
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/12—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
It is an object of the invention to obtain also to have outstanding toughness of welded zone and strength of joint in the case that weld heat input is more than 200kJ/cm, and yield stress is more than 460MPa steel.There is the steel of the present invention defined composition to form, moreover, Ti and N quality % ratios are set to more than 2.0 and are set to less than more than 10 25 less than 4.0, by A values specified in lower note formula (1), Ceq specified in lower note formula (2) is set to 0.38~0.43, the solid solution B amounts in steel are set to more than 5 mass ppm.7716 × N+10000 of A=2256 × Ti × B ... (1) Ceq=C+Mn/6+ (Cr+Mo+V)/5+ (Cu+Ni)/15 ... (2) wherein, each element symbol represent each element steel in content (quality %).
Description
Technical field
The present invention relates to used in a kind of various steel structures as fields such as ship, civil construction, yield stress
Exceed 200kJ/cm Large Heat Input Welding for more than 460MPa steel material for welding, more particularly to a kind of suitable weld heat input
Steel, specifically, be related to one kind in the case of above-mentioned Large Heat Input Welding is implemented, it may have outstanding welding
The steel of portion's toughness and strength of joint.
Background technology
In steel structure used in the fields such as ship, marine structure, building and steel pipe, generally pass through solder joints
The works of desired shape is made.Therefore, from the angle for ensuring security, it is desirable to which these works are except true
Beyond the mother metal characteristic of steel used in guarantor, i.e. intensity and toughness, the toughness of weld part is also outstanding.
In recent years, the steel structure of above-mentioned ship etc. is more and more large-scale so that used steel are constantly to high-strength
Degreeization and thickeningization development.Along with these changes, welding procedure is also using submerged-arc welding, gas shielded arc welding and electroslag welding etc.
Efficient and large-line energy welding method, in the case where the Large Heat Input Welding as carries out welding procedure, it is also desirable to
The outstanding steel of the toughness of weld part.
However, (particularly low temperature is tough for the visible mechanical property for being difficult to make high strength steel, thick steel sheet take into account mother metal in many places
Property) and welding heat affected zone (Heat Affected Zone；Hereinafter, be designated as HAZ) low-temperature flexibility both report.
For this report, such as described in patent document 1 and patent document 2, open one kind is rolled using control
System, control cooling take into account the low-temperature flexibility of mother metal and the technology both HAZ low-temperature flexibility to realize.
Next, HAZ when explanation implements Large Heat Input Welding is organized.The part to connect with welding metal in HAZ
Commonly known as " junction surface (bond portions) ".HAZ near junction surface is exposed to being particularly near fusing point in heat affected zone
In high temperature, accordingly, there exist the tendency that coarse grains and toughness are remarkably decreased.On the other hand, on the ground slightly away from junction surface
Side, softened region is formed because crystal grain is changed into fine grained region, and this turns into the main reason for strength of joint reduces.
As described above, Large Heat Input Welding causes HAZ toughness to reduce, reduce for the HAZ toughness, also studied so far
Many countermeasures.Such as TiN is set fine to be dispersed in steel to suppress the coarsening of austenite crystal or using TiN as ferrite
Phase deformed nucleus is practical to use such technology to obtain.In addition, by making Ti oxide disperse to reach as above-mentioned
The technology of such effect for suppressing austenite crystal coarsening is also under development.
However, in the above-mentioned technology using TiN, there are the following problems：Due to when Large Heat Input Welding is received, welding
The solution temperature region that heat affected zone is heated to TiN is connect, this causes TiN to decompose and causes above-mentioned dispersion effect to disappear, or
Due to TiN decomposition, caused solid solution Ti and solid solution N causes the basic organization embrittlement of steel, and these all cause welding heat affected zone
Toughness significantly reduce.
In addition, in the technology using Ti oxides, exist and be difficult to make oxide uniformly, fine disperse such ask
Topic.As the technology for solving problems, such as Patent Document 3 discloses following technology：Exceed to improve to implement
The toughness of the welding heat affected zone of 200kJ/cm Large Heat Input Welding, the addition to controlling Ca used in the form of sulfide
Amount is suitably adjusted, and crystallizes CaS, and is efficiently used using precipitate as ferritic phase deformed nucleus.
Compared with oxide, above-mentioned CaS is crystallized at low temperature, therefore, it is possible to fine be dispersed in steel, moreover, in steel
When plate cools down, the ferrite transformation such as MnS, TiN, BN generation core can fine be disperseed as core, so as to make weldering
Organizing the formation of as trickle Ferrite-Perlite structure for heat affected zone is connect, and high tenacity can be realized.Therefore, utilize
The technology of patent document 3, the HAZ toughness that can suppress to come along with Large Heat Input Welding to a certain extent are low.
But research afterwards is found, for the high intensity for having carried out making the yield stress of steel plate reach more than 460MPa
Change, and for the addition of the steel of larger amount of C, alloying element, when the large-line energy for carrying out weld heat input and exceeding 200kJ/cm
During welding, several volume % will be formed on the HAZ near junction surface is referred to as island-like martensite (below, in the present invention
In, be also denoted as MA) hard brittle microstructures, the brittle microstructures prevent weld part toughness further improve.
I.e., it was found that the HAZ toughness sides near the junction surface in the Large Heat Input Welding portion of such improvement high strength steel
Face, except austenite crystal coarsening to be suppressed, make ferritic phase deformed nucleus fine dispersion, reduce solid solution N in addition to, there is a need to
Suppress the generation of island-like martensite.
On the technology for the island-like martensite for reducing HAZ portions, for example, Patent Document 4 discloses following technology：Except
Beyond the content for reducing C, Si is effective, the content for reducing P is also very effective for the island-like martensite for reducing HAZ portions.
Moreover, in patent document 5, by energetically adding Mn and strongly reducing P, it can obtain and reduce junction surface
The outstanding yield stress of neighbouring HAZ island-like martensite and toughness is the steel of 460MPa degree.
On the other hand, on the technology for the HAZ softenings for suppressing to bring along with Large Heat Input Welding, picture is not disclosed
The so much content of HAZ toughness countermeasures.Any one of above-mentioned patent document 3,4 and 5 patent document does not describe soft with HAZ yet
Change related content.It is considered that reason for this is that, when the design of initial high input energy welding steel is carried out, with energy
Enough ensure strength of joint as premise.
Accordingly, with respect to the content for suppressing HAZ softenings, published technology is illustrated.
In these techniques, the quenching property brought using the technology and utilization of the precipitation strength element such as Nb, V by B be present
The technology of the effect of raising.
Such as in patent document 6, Si, Mn amount are reduced while C amounts are improved, and by comprising Nb, V, with this
To reduce HAZ softenings.
On the other hand, in patent document 7, in order to realize that the quenching property brought by B improves, contained by regulation than N
Empirical formula as amount more Ti, B and Nb softens to suppress HAZ.
In addition, in patent document 8, by providing to be dissolved B amounts, realize that the quenching property brought by B improves, so as to suppress
HAZ softens.
Patent document 1：Japanese Unexamined Patent Application 57-134518 publications
Patent document 2：Japanese Unexamined Patent Application 59-83722 publications
Patent document 3：No. 3546308 publications of Japanese Patent Publication No.
Patent document 4：Japanese Unexamined Patent Publication 2008-163446 publications
Patent document 5：Japanese Unexamined Patent Publication 2011-6772 publications
Patent document 6：Japanese Unexamined Patent Application 60-67622 publications
Patent document 7：Japanese Unexamined Patent Publication 2007-177327 publications
Patent document 8：No. 4233033 publications of Japanese Patent Publication No.
However, as described above, the technology described in patent document 3 is a kind of improves especially is being for yield stress
The steel of 390MPa degree implement the technology of when Large Heat Input Welding, junction surface toughness, for for yield strength
Further improve, such as yield stress：For large-line energy HAZ toughness and the HAZ softening of the steel of 460MPa degree, sometimes not
Can fully it tackle.
In addition, the technology described in patent document 4 is using the steel that yield stress is 460MPa degree as object, pass through
C, Si and P content are reduced to reduce the island-like martensite of the HAZ near junction surface, and makes iron by adding appropriate Ca
Ferritic phase deformed nucleus fine disperses, so that it is guaranteed that HAZ toughness, but in the document, HAZ softenings are not described, moreover,
There is a possibility that cost of alloy can be caused to improve because Ni must be added.
In addition, the technology described in patent document 5 is using the steel that yield stress is 460MPa degree as object, pass through
Energetically reduce island-like martensite using Mn, so as to inexpensively obtaining required steel, still, its still with patent document 4
Equally, the not description as described in HAZ softenings.
On the other hand, although the technology described in patent document 6, which employs, improves C amounts and using the precipitation strengths such as Nb, V member
The method of element is fully handled HAZ softenings, but troubling, can be near junction surface in Large Heat Input Welding
A large amount of island-like martensites are formed on HAZ, so that the toughness of the HAZ near junction surface significantly reduces.
In addition, the technology described in patent document 7 and 8 is to suppress the technology of HAZ softenings using B quenching property, its
In patent document 7 be premised on adding substantial amounts of Ti, B and N, it is worrying to be, asking in terms of manufacturing property be present
Topic, while worrying because being dissolved N HAZ toughness can be caused to reduce in the TiN melting ranges near junction surface.
In addition, the technology described in patent document 8 is premised in the absence of Nb, with yield stress：460MPa
In the case that the steel of degree are as object, remain and be difficult to ensure that the problem of strength of joint is such.
The content of the invention
The present invention develops in view of the foregoing, even if implementing weldering its object is to inexpensively provide one kind
Wiring energy exceed 200kJ/cm Large Heat Input Welding, still welding heat affected zone hardness do not reduce, softening resistance and
The high input energy welding steel material outstanding in terms of HAZ toughness near junction surface, yield stress is more than 460MPa.
In order to solve above-mentioned problem, inventors are to tissue factor to being the high-strength of more than 460MPa for yield stress
Degree steel implement when weld heat input exceedes 200kJ/cm Large Heat Input Welding, HAZ toughness and HAZ near junction surface
The influence that the hardness in most softening portion region is brought is studied in detail.Its result is found：It is tough on the HAZ near junction surface
Property, can also harmful effect be produced to toughness, even if with the presence of a small amount of island-like martensite on the contrary, by producing island martensite physical efficiency
The enough hardness for improving most softening portion region.
Therefore, inventors are directed on the basis of caused by the island-like martensite for suppressing the HAZ near junction surface, are improved
The method of the most growing amount of the island-like martensite in softening portion region is studied.Its result is found：Near junction surface
For HAZ, while suppressing relatively low by C, Si, P amount, made up by energetically containing Mn female as caused by reducing C amounts
Material intensity declines, and can not produce as far as possible and carry out dysgenic island-like martensite to the HAZ malleable bands near junction surface, effectively
Improve strength of parent.
It moreover has been found that by the way that Ti, N and B in most softening portion region are controlled into carrying in suitable scope and using B
High quenching property effect, the island horse that junction surface nearby promotes most softening portion region HAZ island-like martensite can not be increased
The formation of family name's body.
I.e., for B, in the HAZ near junction surface in the high temperature near fusing point, it is not produced from adjoint
Top bainite generation, growth and away from crystal boundary movement so that remain in lath of bainite (bainite lath) it
Between the quenching property of non-transformed austenite be not improved, but, in the less HAZ of temperature-rise ratio brought by heat affecting
In softened region, B spreads along with ferrite transformation and makes it by the way that segregation occurs on the crystal boundary of non-transformed austenite
Quenching property improves, thus the effect for the formation for promoting island-like martensite be present.
But HAZ softened region does not almost produce precipitate because the temperature-rise ratio brought by heat affecting is smaller
Dissolving, state when contributing to the B of quenching property amount to depend on manufacturing process.Moreover, in mother metal manufacturing process
Controlled rolling and each stage of cooling, B is because the difference of manufacturing condition forms nitride sometimes, in this case, can not play
It improves the effect of quenching property.
Therefore, as a result inventors have found by further studying repeatedly：In steel plate manufacturing process, by with lower section
Method can limit the precipitation of B nitride as far as possible, and be optimized together with above-mentioned composition, obtain outstanding HAZ characteristic, extremely
This, develops the present invention, and this method is as follows：First, after initially implementing rolling in austenite recrystallization temperature region, accelerate
Austenite non-recrystallization temperature province is cooled to, then implements the rolling of austenite non-recrystallization temperature province, and then secondary implementation
Accelerate cooling.
I.e., primary structure of the invention is as follows.
1. a kind of steel material for welding, it contains C：Mass %, Si of 0.030 mass %~0.080：0.01 mass %~0.10
Quality %, Mn：Mass %, P of 1.80 mass %~2.40：Below 0.010 mass %, S：The matter of 0.0005 mass %~0.0040
Measure %, Al：Mass %, Nb of 0.005 mass %~0.100：Mass %, Ti of 0.003 mass %~0.030：0.010 mass %~
0.050 mass %, N：0.0030 mass %~0.0120 mass % and B：The mass % of 0.0005 mass %~0.0025, and
Ti and N quality % ratios (Ti/N) are more than 2.0 and less than 4.0, A values specified in following formula (1) for more than 3 25 with
Under, Ceq specified in following formula (2) be 0.38~0.43 scope, remaining part is by Fe and inevitable impurity structure
Into composition composition, it is more than 5 mass ppm that yield stress, which is more than 460MPa and is dissolved B amounts, is implementing sealing wire energy
Amount：During more than 200kJ/cm heat input welding, the island-like martensite in tissue near the junction surface of heat affected zone is
Below 1vol%, and the island-like martensite in the tissue in the most softening portion region of heat affected zone is more than 5vol%.
A=2256 × Ti-7716 × N+10000 × B ... (1)
Ceq=C+Mn/6+ (Cr+Mo+V)/5+ (Cu+Ni)/15 ... (2)
Wherein, quality % contents in the steel of each element symbol expression each element.
2. according to the steel material for welding described in upper note 1, in its mentioned component composition, also contain from V：0.20 mass % with
Under, Cu：Below 0.30 mass %, Ni：Below 0.30 mass %, Cr：Below 0.40 mass % and Mo：Below 0.40 mass %
More than one element of middle selection.
3. according to the steel material for welding described in the upper note of note 1 or upper 2, in its mentioned component composition, also contain from Ca：
Mass %, Mg of 0.0005 mass %~0.0050：Mass %, Zr of 0.0005 mass %~0.0050：0.0010 mass %~
0.0200 mass %, REM：More than one the element selected in the mass % of 0.0010 mass %~0.0200.
Invention effect
Using the present invention, it can obtain and when implementing Large Heat Input Welding, have good strength of joint and sweating heat concurrently
The steel of influence portion toughness, for by Large Heat Input Welding as submerged-arc welding, electroslag welding and the ship, the large-scale knot that are built into
The quality of structure thing, which improves, larger help.Particularly, if using the present invention in steel of the thickness of slab more than 50mm, with conventional skill
Steel in art are compared, and in the strength of joint of welding and the toughness these two aspects of welding heat affected zone, are shown more significant excellent
More property.
Embodiment
Next, illustrate the present invention.In addition, the steel as object are referred to by hot rolling system in the present invention
The steel created.
In the present invention, important is composition composition, intensity and the big line because exceeding 200kJ/cm for controlling respectively steel
Minimum hardness in the softened region for the welding heat affected zone that energy is welded and formed is (hereinafter also referred to as HAZ most areas of softening portion
The hardness in domain).
First, the volume fraction of the island-like martensite of the heat affected zone of the feature as steel of the invention is said
It is bright.
The island-like martensite in tissue near the junction surface of heat affected zone is below 1vol%
In welding heat affected zone (HAZ), austenite coarsening, heat affecting occurs by suppressing to be exposed in high temperature
The generation of island-like martensite near the junction surface in portion, it is possible to increase the toughness in Large Heat Input Welding portion.It is such in order to obtain
Effect is, it is necessary to which the volume fraction of the island-like martensite near above-mentioned junction surface is suppressed in below 1vol%.In addition, above-mentioned island
The lower limit of the volume fraction of martensite is simultaneously not particularly limited, even 0vol% also may be used.In addition, the heat affected zone of the present invention
Junction surface nearby refers to starting at the welding heat affected zone of the scope within 600 μm from junction surface, and the tissue is except with upper
State beyond island-like martensite, based on acicular ferrite, bainite, and the known tissue comprising ferrite, pearlite.
The island-like martensite in the most softening portion region of heat affected zone is more than 5vol%
To yield stress：More than 460MPa steel are welded and caused joint needs to reach to resist with mother metal identical
Tensile strength, i.e. tensile strength reach more than 570MPa.Herein, the factor being had an impact as the tensile strength of butt joint, it is main
If the most softening portion region of the intensity of welding metal, thickness of slab, the HAZ most hardness in softening portion region etc., particularly heat affected zone
Taeniae telarum come have a great influence.Moreover, the tissue that yield stress is the softened region of more than 460MPa steel is ferrite
With the second phase constitution, as the second phase constitution, can be obtained by the island-like martensite for the volume fraction for producing more than 5vol%
Desired strength of joint.
In addition, in the present invention, the softened region of heat affected zone refer to it is apart from junction surface 10mm or so, by by
After the heating that welded bands are come, austenitic formation is the heat affected zone of fine particle.
In addition, in the present invention, the most softening portion region of heat affected zone is referred to 1mm or so being in grid at equal intervals
Shape measurement vickers hardness hv (JIS Z 2244 (1998)), centered on the point for representing lowest hardness, distance center is nearest
The region that measurement point links up each other everywhere.
In the present invention, it is real in order to while the tissue in the most softening portion region to HAZ is controlled as described above
Existing high intensity, the composition composition that should have to steel formulate the following rules.In addition, following, the composition on steel forms
% refer to quality %.
C：The mass % of 0.030 mass %~0.080
C is the element for improving the intensity of steel, in order to ensure as the intensity needed for structural steel, C needs to contain
More than 0.030 mass %.On the other hand, if MAs of the C more than 0.080 mass %, the easily HAZ near generation junction surface, because
This, 0.080 mass % is set to by the upper limit.
Si：The mass % of 0.01 mass %~0.10
The element that deoxidier when Si is as molten steel is added is, it is necessary to add more than 0.01 mass %.On the other hand,
If it exceeds 0.10 mass %, in addition to the toughness of mother metal reduces, HAZ is produced near the junction surface that Large Heat Input Welding forms
Raw MA, easily causes toughness to reduce.Then, Si is set in the range of the mass % of 0.01 mass %~0.10.
Mn：The mass % of 1.80 mass %~2.40
Mn is the element for being used to improve intensity as C, and the alloying element than being referred to as Mo, V is cheap, and does not promote to connect
The MA generations of HAZ near conjunction portion, therefore, are energetically added in the present invention.Moreover, in order to ensure required intensity and obtain
The effect above is more preferably added more than 1.90 mass %, it is necessary to add more than 1.80 mass %, further preferably adds 2.00 matter
Measure more than %.On the other hand, if the Mn containing excess, toughness of welded zone is damaged on the contrary, it is necessary to add below 2.40 mass %,
More preferably add below 2.20 mass %, further preferably add below 2.10 mass %.
P：Below 0.010 mass %
P is as impurity and one kind of element for containing, excellent because it makes the reduction of steel plate mother metal and HAZ toughness
Being selected on the basis of economy during in view of founding blank, reducing its content within the bounds of possibility.Therefore, P amounts are limited
Below 0.010 mass %.Preferably below 0.008 mass %.
S：The mass % of 0.0005 mass %~0.0040
S is for forming the MnS or CaS essential elements that are played a role as ferritic nucleation site.Therefore,
Add more than 0.0005 mass %.However, if excessively addition, instead results in base metal tenacity reduction, therefore, the upper limit is set to
0.0040 mass %.
Al：The mass % of 0.005 mass %~0.100
Al be for the deoxidation of steel and the element that adds, it is necessary to contain more than 0.005%.On the other hand, if content surpasses
0.100 mass % is crossed, the toughness of mother metal can not only declined, and can decline the toughness of welding metal.Then, Al is set
It is scheduled in the range of the mass % of 0.005 mass %~0.100.The mass % of preferably 0.010 mass %~0.100 scope.
Nb：The mass % of 0.003 mass %~0.030
Nb is to ensuring strength of parent, HAZ most softening portion hardness and the effective element of strength of welded joint.But
In the case that addition is less than 0.003 mass %, the effect above will diminish, but if content is more than 0.030 mass %, it will
HAZ near junction surface produces MA and reduces toughness.Then, Nb is set in the mass %'s of 0.003 mass %~0.030
In the range of.
Ti：The mass % of 0.010 mass %~0.050
Ti can form TiN in solidification and separate out, and suppress the coarsening of HAZ austenite crystal near junction surface.In addition,
Ti is ensured while HAZ high tenacity is contributed to as ferritic phase change core by reducing the N to be combined with B
B is dissolved, is effectively played a role on the basis of HAZ most softening portion hardness and strength of welded joint is ensured.In order to obtain this
The effect of sample is preferably added more than 0.015 mass %, it is necessary to add more than 0.010 mass %.On the other hand, if content surpasses
Cross 0.050 mass %, the TiN of precipitation will coarsening, the effect above can not be obtained.Then, Ti is set in 0.010 mass %
In the range of~0.050 mass %.
N：The mass % of 0.0030 mass %~0.0120
N forms TiN in solidification, helps to suppress the coarsening of the austenite crystal of the HAZ near junction surface, meanwhile, N
BN is produced, the BN plays a role as ferritic phase deformed nucleus causes the tissue granular of the HAZ near junction surface, contributes to steel
The high tenacity of material.Moreover, in order to ensure such TiN reaches requirement, it is necessary to be more than 0.0030 mass % containing N,
Preferably comprise more than 0.0050 mass %.More preferably contain more than 0.0070 mass %.On the other hand, if excessively containing N,
In the difference according to weld heat input condition, and in the region for melting TiN, solid solution N amounts increase, and make HAZ toughness on the contrary
Reduce.Therefore, the upper limit is set to below 0.0120 mass %.It is preferably set to below 0.0100 mass %.
B：The mass % of 0.0005 mass %~0.0025
B is the element for improving the quenching property of steel, promotes bainite, horse by reducing the phase transition temperature of austenite
The generation of hard tissue as family name's body, contribute to the high intensity of mother metal steel plate.Equally, the conduct in HAZ softenings portion is also suppressed
The ferritic generation of soft phase so that the intensity in HAZ softenings portion improves.In order to obtain such effect, it is necessary to be containing B
More than 0.0005 mass %.On the other hand, if B content will cause quenching property superfluous, on the contrary more than 0.0025 mass %
Cause the reduction of mother metal steel plate and HAZ toughness.Therefore, B is set in the range of the mass % of 0.0005 mass %~0.0025.
Solid solution B amounts are set to more than 5 mass ppm
In the present invention, the solid solution B amounts in steel are set to more than 5 mass ppm.Solid solution B amounts in steel are less than 5ppm
In the case of, HAZ softened region make when organizing the formation of non-transformed austenite quenching property improve it is not sufficiently effective, can not
Obtain the island martensite scale of construction for obtaining desired hardness.
Ti and N quality % ratios (Ti/N)：More than 2.0 and less than 4.0
Ti/N is defined as A values described later, meanwhile, in the present invention, Ti/N is important key element.Ti/N is for HAZ's
Junction surface, TiN fine dispersion situation and the toughness deterioration as caused by solid solution N have considerable influence, it is necessary to suitably be controlled
System.If i.e., Ti/N be more than 4.0, due to BN is not separated out and Ti boron-carbide etc. separate out, cause HAZ toughness significantly to drop
Low, but if Ti/N is less than 2.0, the reduction of the HAZ toughness caused by being dissolved N and HAZ BN are separated out, and can not ensure quenching for B
Fiery performance, so as to be difficult to ensure that required HAZ most softening portion hardness.Therefore, Ti/N value is set to more than 2.0 and less than 4.0.
Preferably, Ti/N value is more than 2.5 in less than 3.5 scope.
A values：Less than more than 3 25
It is one of project mostly important in the present invention in A values specified in formula (1) as shown below.Steel by
When the thermal process suitable with the heat affected zone of Large Heat Input Welding, even if TiN, BN etc. generation reaction are not meeting balance reason
In the case of being carried out by ground, in order that solid solution B has given play to the effect for improving quenching property, except meeting in terms of Ti, N and B
On the basis of the addition of above-mentioned steel, it is also necessary to which A values are more than 3.But if A values more than 25, the quenching property of steel
Will be superfluous, so as to produce harmful effect to HAZ toughness.Therefore, in the present invention, A values are set to less than more than 3 25.It is excellent
Elect 6~15 scope as.
A=2256 × Ti-7716 × N+10000 × B ... (1)
Wherein, content (quality %) in the steel of each element symbol (Ti, N, B) expression each element.
Ceq：0.38~0.43
Heat input when the high input energy welding steel material of the present invention is due to welding, causes what is implemented when manufacturing mother metal
The effect of the organizational controls such as TMCP is completely ineffective.Therefore, under the heating and cooling when welding, it is also desirable to take into account welding and connect
The intensity and toughness of head, so needing as the carbon equivalent C of the index of quenching propertyeqControl is in appropriate scope.
In particular, it is desirable to so that carbon equivalent C defined in following formula (2)eqFor the side of 0.38~0.43 scope
Formula controls the composition of each composition.When above-mentioned Ceq is less than 0.38, quenching property deficiency, the hardness in most softening portion region significantly drops
It is low, therefore, it is impossible to ensure the intensity of desired welding point.On the other hand, if CeqMore than 0.43, then quenching property mistake
Surplus, the ferritic generation near junction surface is suppressed, and promotes island-like martensite to produce, therefore, it is impossible to ensure sufficiently
Toughness.Preferably, CeqIn the range of 0.39~0.42.
Ceq=C+Mn/6+ (Cr+Mo+V)/5+ (Cu+Ni)/15 ... (2)
Herein, each element symbol in above-mentioned formula represents the content of respective element (C, Mn, Cr, Mo, V, Cu, Ni)
(quality %).
In basis composition of the invention more than, remaining part is exactly Fe and inevitable impurity.In addition, as not
The impurity that can be kept away, as long as such as O is that less than 0.0050% can just be allowed to.
,, can be in the scope of lower note for the purpose of improving intensity etc. in addition to mentioned component in the steel of the present invention
Interior more than one elements selected among V, Cu, Ni, Cr and Mo that contain are as optional element.
V：Below 0.20 mass %, Cu：Below 0.30 mass %, Ni：Below 0.30 mass %, Cr：0.40 mass % with
Lower and Mo：Below 0.40 mass %
V, Cu, Ni, Cr and Mo are the effective elements of high intensity to mother metal, in order to obtain the effect, it is preferred that
V, Cu and Ni additions more than 0.05 mass %, Cr and Mo additions more than 0.02 mass %.But if largely add any
Element, will all harmful effect be produced to toughness, also had, Ni is related to cost of alloy increase, therefore, is containing these elements
In the case of, it is desirable to V is set to below 0.20 mass %, Cu is set to below 0.30 mass %, Ni is set to 0.30 mass % with
Under, Cr and Mo be set to below 0.40 mass %.
Moreover, the present invention steel in addition to mentioned component, can in the range of lower note contain from Ca, Mg, Zr with
And more than one elements selected among REM are as optional element.
Ca：The mass % of 0.0005 mass %~0.0050
Ca can be contained for the toughness improvement for obtaining S fixation, being brought by dispersal oxide, sulfide.For
Acquisition the effect above, it is preferred that at least containing 0.0005 mass %.But even if addition more than 0.0050 mass %,
Also it is that the effect above reaches saturation.Then, in the case of containing Ca, be preferably set to 0.0005 mass %~
0.0050 mass % scope.
Mg：Mass %, Zr of 0.0005 mass %~0.0050：Mass %, REM of 0.0010 mass %~0.0200：
The mass % of 0.0010 mass %~0.0200
Any of Mg, Zr and REM, it is the element that there is dispersal oxide to bring toughness improvement.In order to
Effect as embodiment, it is preferred that containing Mg be 0.0010 mass % more than 0.0005 mass %, containing Zr and REM with
On.On the other hand, though addition Mg more than 0.0050 mass %, addition Zr and REM more than 0.0200 mass %, be also
The effect reaches saturation.Then, in the case of containing these elements, they are preferably set in above range.
Manufacture method
Preferably, the welding method commonly used using converter or electric furnace etc. with the steel that mentioned component forms to melting
System, and the process commonly used using continuous casing or ingot casting method etc. forms the slab raw material for manufacturing steel plate.Hereinafter,
The preferable steel plate manufacturing condition used for the present invention illustrates.
Heating-up temperature：1050 DEG C~1200 DEG C
In order that the Nb carbonitrides in steel billet are dissolved completely, it is preferred that the heating-up temperature of steel billet is set as into 1050
More than 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 in heating,
Harmful effect is brought to base metal tenacity, it is therefore preferable that the upper limit is set into 1200 DEG C.
The rolling in austenite recrystallization temperature region
The rolling in austenite recrystallization temperature region has the effect of the austenite crystal granular to a certain degree when making heating
Fruit, it is desirable to roll for minimum more than 1 time, it is preferred that implement accumulation reduction ratio more than 20%.As long as mentioned component scope
Steel, the lower limit temperature in austenite recrystallization temperature region are about just 900 DEG C~1000 DEG C of scope.
From austenite recrystallization temperature region to the once cooling of austenite non-recrystallization temperature province
This process is one of mostly important project among manufacturing process.As described above, in HAZ softened region, energy
Enough make the solid solution B amounts that the quenching property of tissue improves equivalent to the solid solution B amounts being able to ensure that in the state of when manufacturing steel plate.
Therefore, in the case of the nitride precipitation for having a large amount of B when manufacturing steel plate, for ensuring that quenching property is consolidated
Molten B deficiencies, lead to not the situation that enough hardness is obtained in HAZ softened region.
Further, it is desirable in cooling procedure when manufacturing steel plate, with B nitride caused by temperature province it is suitable, from
The cooling velocity of austenite recrystallization temperature region to austenite non-recrystallization temperature province is as fast as possible.Generally, the process is made
Air cooling is carried out for the temperature reduction stand-by time of hot rolling, but in the present invention, pass through and implement the cooling with than air cooling
The acceleration cooling of fireballing cooling velocity, while shortening to up to time as the controlled rolling process of next procedure,
B reduction can be prevented from being dissolved caused by the precipitation of B nitride.In addition, the acceleration cooling particularly from 1000 DEG C to
It is effective to implement within the temperature range of 600 DEG C.
In the present invention, in order to which the cooling after the rolling with austenite non-recrystallization temperature province described later is distinguished,
And then the acceleration cooling that the rolling in austenite recrystallization temperature region is implemented referred to as once is cooled down.Once cooled down at this
In, it is preferred that accelerate cooling device or the removing caused oxide skin on surface of steel plate in rolling using water cooling
So-called rust removalling equipment etc., reach the cooling velocity faster than air cooling.Specifically, preferably more than 3 DEG C/sec of cooling velocity.
The rolling of the accumulation reduction ratio more than 40% of austenite non-recrystallization temperature province
Then above-mentioned acceleration cooling, implements controlled rolling in austenite non-recrystallization temperature province.In the controlled rolling
In the case of accumulation reduction ratio in journey is less, it is difficult to base metal tenacity as defined in acquisition.Therefore, the lower limit for accumulating reduction ratio is set
For 40%.It is higher although it is desirable to accumulate reduction ratio, but in industrial aspect, there is a situation where using 80% or so as the upper limit, it is excellent
Choosing is 50%~80%.
After the rolling of austenite non-recrystallization temperature province, from Ar3More than transformation temperature temperature is to less than 550 DEG C of temperature
The secondary cooling in region
Secondary cooling is the cooling so that for the purpose of being undergone phase transition by controlled rolling and the austenite structure being processed into.And
And in order that the phase transformation of tissue is completed, it is necessary to be cooled to less than 550 DEG C of temperature province, the lower limit of temperature is completed in preferably cooling
For 550 DEG C.The cooling velocity of secondary cooling is to need the cooling velocity faster than air cooling, and it is cold preferably to carry out more than 5 DEG C/sec of pressure
But.It is more preferable that carry out more than 10 DEG C/sec of pressure cooling.Cooling means is simultaneously not particularly limited, it is desirable to is the cold of water cooling
But.
Herein, steel temperature of the invention represents the average temperature of the surface temperature of steel and the temperature of thickness of slab central part
Degree.Ar3Transformation temperature is different according to the composition of steel, therefore, it is possible to simply be obtained according to following formula.In addition, in following formula, respectively
Content (quality %) in the steel of symbol of element expression each element.0 is expressed as in the case of not containing.
Ar3(DEG C)=910-273C-74Mn-56Ni-16Cr-9Mo-5Cu
Embodiment
After the steel with the composition shown in table 1 is founded out using converter, slab, Ran Houli are formed using continuous casting process
The thick steel plates of 40mm~80mm are produced with the controlled rolling shown in table 2, control cooling condition.Secondary numbering shown in table 2 represents
The situation that composition of steel is identical but manufacturing condition is different.In addition, once cooling is set by being arranged on the water cooling of roll mill outlet side
It is standby to implement, 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 the steel plate manufactured by manufacturing process out, from the position in thickness of slab direction 1/4
Parallel portion 14mm Φ tension test sheet is removed, the regulation based on JIS Z 2241 (1998) implements tension test, and obtains
0.2% endurance (YS) and tensile strength (TS).
In addition, from the position in thickness of slab direction 1/4, it is defined based on JIS Z 2202 (1998) regulations, removes v-notch standard
The Charpy-type test piece of size, and the regulation based on JIS Z 2242 (1998) implements impact test, has obtained fracture and has turned
Temperature (vTrs).
Herein, vTrs desired value is less than -60 DEG C.
In addition, in order to implementing weld heat input：It is when more than 200kJ/cm heat input welding, heat affected zone
The hardness in most softening portion region is evaluated, and 3mm Φ × 10mm small specimen is removed from the position of thickness of slab direction 1/4, is being added
After hot 900 DEG C of the temperature to equivalent to the just upper position of transformation temperature, perform and carry out cooling down for 390 seconds between 800 DEG C~500 DEG C
Heat treatment.It is hard with the Vickers of small specimen of 1mm or so the interval in clathrate measurement after these processing are performed
HV (JIS Z 2244 (1998)) is spent, using wherein minimum hardness as most softening portion hardness.The most desired value of softening portion hardness
It is set to more than 160.In addition, HAZ most softening portion regions are centered on the point for representing lowest hardness, by the nearest survey of distance center
The region that amount point is connected with each other.
In addition, carried out using nitric acid alcohol (nital) the corrosive liquid pair position corresponding with above-mentioned HAZ most softening portion regions
Etch and revealed tissue.The macrograph in 3 visuals field is shot under 1000 times using SEM, and image analysis is carried out to it,
MA average area fraction is obtained, then the MA volume fractions using the average area fraction of the MA as HAZ most softening portion regions
(vo1%).
In order to implementing weld heat input：When more than 200kJ/cm heat input welding, heat affected zone engagement
The toughness in portion is evaluated near portion, and width is removed from above-mentioned steel plate：80mm × length：80mm × thickness：15mm experiment
Piece, then after being heated to 1450 DEG C, after cooling in 390 seconds is carried out between 800 DEG C~500 DEG C, remove 2mmV type otch
Charpy test piece, it is same as above, the impact test temperature for performing Charpy-type test is set to -40 DEG C, and utilize three
The average value of experiment is evaluated.Desired value is set to the average absorption energy (vE at -40 DEG C-40DEG C) it is more than 50J.In addition, with
Above-mentioned the same, the MA in the test film section after implementing to thermal process area fraction is evaluated.
Shown in table 3 in mother metal characteristic, HAZ characteristic and HAZ that the steel after evaluation are implemented by upper note order
MA volume fractions (vol%) measurement result.
[table 3]
Table 3
[note 1] underscore represents the content outside the scope of the invention.
It can be seen from the table：In the secondary numbering A of steel plate composition No.1~12 example, mother metal and HAZ can be obtained
Outstanding characteristic.On the other hand, for the secondary numbering B of steel plate composition No.1~4 steel plate, by the shadow of manufacturing condition
Ring, do not meet the key element of the present invention, mother metal characteristic and HAZ characteristic are poor.In addition, understand in steel plate forms No.13~27, chemistry
Composition present invention provide that scope outside, therefore, even secondary numbering A, HAZ characteristic are also poor.
Claims (3)
1. a kind of steel material for welding, it contains C：Mass %, Si of 0.030 mass %~0.080：The matter of 0.01 mass %~0.10
Measure %, Mn：Mass %, P of 1.80 mass %~2.40：Below 0.010 mass %, S：The matter of 0.0005 mass %~0.0040
Measure %, Al：Mass %, Nb of 0.005 mass %~0.100：Mass %, Ti of 0.003 mass %~0.030：0.010 mass %~
0.050 mass %, N：0.0030 mass %~0.0120 mass % and B：The mass % of 0.0005 mass %~0.0025, and
Ti and N quality % ratios (Ti/N) are more than 2.0 and less than 4.0, and the steel material for welding is characterised by,
It is less than more than 3 25, is 0.38 in Ceq specified in following formula (2) in A value specified in following formula (1)
~0.43 scope, the composition that remaining part is made up of Fe and inevitable impurity form, yield stress be more than 460MPa simultaneously
And solid solution B amounts are more than 5 mass ppm, are implementing weld heat input：During more than 200kJ/cm heat input welding, heat affecting
The island-like martensite in tissue near the junction surface in portion is below 1vol%, and the group in the most softening portion region of heat affected zone
The island-like martensite knitted is more than 5vol%,
A=2256 × Ti-7716 × N+10000 × B ... (1)
Ceq=C+Mn/6+ (Cr+Mo+V)/5+ (Cu+Ni)/15 ... (2)
Wherein, quality % contents in the steel of each element symbol expression each element.
2. steel material for welding according to claim 1, wherein,
In composition composition, also contain from V：Below 0.20 mass %, Cu：Below 0.30 mass %, Ni：0.20 mass %
Below, Cr：Below 0.40 mass % and Mo：More than one element of the middle selections of below 0.40 mass %.
3. steel material for welding according to claim 1 or 2, wherein,
In composition composition, also contain from Ca：Mass %, Mg of 0.0005 mass %~0.0050：0.0005 mass %~
0.0050 mass %, Zr：Mass %, REM of 0.0010 mass %~0.0200：Selected in the mass % of 0.0010 mass %~0.0200
More than one the element selected.
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| CN108676975B (en) * | 2018-06-01 | 2020-02-07 | 马鞍山钢铁股份有限公司 | Heat treatment method for removing segregation defects in 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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| CN103334053A (en) * | 2009-02-06 | 2013-10-02 | 杰富意钢铁株式会社 | High-strength steel tube for low-temperature use with superior buckling resistance and toughness in weld heat-affected areas, and manufacturing method for same |
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| JPS5983722A (en) | 1982-11-05 | 1984-05-15 | Kawasaki Steel Corp | Preparation of low carbon equivalent unnormalized high tensile steel plate |
| JPS6067622A (en) | 1983-09-21 | 1985-04-18 | Kobe Steel Ltd | Preparation of low carbon equivalent steel for large heat input welding reduced in welding joint softening |
| JP3546308B2 (en) | 2001-03-05 | 2004-07-28 | Ｊｆｅスチール株式会社 | Large heat input welding steel |
| JP4233033B2 (en) | 2003-11-06 | 2009-03-04 | 株式会社神戸製鋼所 | A thick steel plate with excellent toughness and strength in the heat affected zone. |
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| JP5076658B2 (en) | 2006-12-06 | 2012-11-21 | Ｊｆｅスチール株式会社 | Steel material for large heat input welding |
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| JP5842314B2 (en) * | 2009-09-16 | 2016-01-13 | Ｊｆｅスチール株式会社 | High heat input welding steel |
| JP5772620B2 (en) * | 2011-01-18 | 2015-09-02 | Ｊｆｅスチール株式会社 | Tapered plate manufacturing method |
| JP5824434B2 (en) * | 2011-11-14 | 2015-11-25 | 株式会社神戸製鋼所 | Thick steel plate with excellent toughness in weld heat affected zone |
| JP5949682B2 (en) * | 2012-07-03 | 2016-07-13 | Ｊｆｅスチール株式会社 | Manufacturing method of steel plate for high heat input welding with excellent brittle crack propagation stop properties |
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