CN101909810A - Flux cored arc weld metal joint having superior CTOD in low temperature and steel member having the weld metal joint - Google Patents
Flux cored arc weld metal joint having superior CTOD in low temperature and steel member having the weld metal joint Download PDFInfo
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- CN101909810A CN101909810A CN2008801232653A CN200880123265A CN101909810A CN 101909810 A CN101909810 A CN 101909810A CN 2008801232653 A CN2008801232653 A CN 2008801232653A CN 200880123265 A CN200880123265 A CN 200880123265A CN 101909810 A CN101909810 A CN 101909810A
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K35/00—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting
- B23K35/02—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by mechanical features, e.g. shape
- B23K35/0255—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by mechanical features, e.g. shape for use in welding
- B23K35/0261—Rods, electrodes, wires
- B23K35/0266—Rods, electrodes, wires flux-cored
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K35/00—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting
- B23K35/22—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by the composition or nature of the material
- B23K35/24—Selection of soldering or welding materials proper
- B23K35/30—Selection of soldering or welding materials proper with the principal constituent melting at less than 1550 degrees C
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K35/00—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting
- B23K35/22—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by the composition or nature of the material
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K35/00—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting
- B23K35/22—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by the composition or nature of the material
- B23K35/24—Selection of soldering or welding materials proper
- B23K35/30—Selection of soldering or welding materials proper with the principal constituent melting at less than 1550 degrees C
- B23K35/3053—Fe as the principal constituent
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K9/00—Arc welding or cutting
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K9/00—Arc welding or cutting
- B23K9/16—Arc welding or cutting making use of shielding gas
- B23K9/173—Arc welding or cutting making use of shielding gas and of a consumable electrode
-
- 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
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
-
- 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
- C22C38/04—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
- C22C38/06—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
- C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
-
- 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
Abstract
The present invention relates to a weld metal joint subjected to flux cored arc welding (FCAW) used for weld structures, such as ships, buildings, bridges, marine structures, steel pipes, and line pipes, and a steel member having the weld metal joint, and more particularly, to a flux cored arc weld (FCAW) metal joint having excellent CTOD properties at low temperature and a steel member having the FCAW metal joint. A flux cored arc weld metal joint having excellent CTOD properties at low temperature may include, by weight: 0.01 to 0.2% C, 0.1 to 0.5% Si, 1.0 to 3.0% Mn, 0.5 to 3.0% Ni, 0.01 to 0.1% Ti, 0.0010 to 0.01% B, 0.005 to 0.05% Al, 0.003 to 0.006% N, at most 0.03% P, at most 0.03% S, 0.03 to 0.07% O, the FCAW metal joint satisfying a relation of 0.7<=Ti/O<=1.3, 6<=Ti/N<=12, 7<=O/B<=12, and 1.2<=(Ti+4B)/O<=1.9, and the balance of Fe and unavoidable impurities, the FCAW metal joint including a microstructure having acicular ferrite of 85% or more and at least one of the balance of bainite, grain boundary ferrite, and polygonal ferrite. A steel member includes the metal weld joint. According to the invention, there is provided a flux cored arc weld metal joint having a high- strength property and CTOD properties at low temperatures and a steel member having the metal weld joint.
Description
Technical field
The present invention relates to be used for Welding Structure for example ship, building, bridge, marine structure, steel pipe and pipeline carry out the welded metal joints that flux cored wire arc welding meets (FCAW), and steel member with described welded metal joints, more specifically, relate to the steel member that the flux cored wire arc welding that has excellent CTOD performance at low temperatures connects (FCAW) metal joint and has described FCAW metal joint.
Background technology
Recently, because marine structure is built and used to the continuous rise of oil price more and more at cold district.Used steel member requires to have at low temperatures high strength and high CTOD performance.
The CTOD performance of marine structure welding point is to guarantee the very important factor of marine structure stability.
Usually, the flux cored wire arc welding that carries out in marine structure connects the heat input of using the about 7-25kJ/cm of heat input range.
Usually, the weld metal that forms in welding process forms thick column structure in process of setting, and forms coarse-grain circle ferrite and Widmannstatten structure ferrite along the austenite grain boundary in the coarse grain.That is, welded metal joints be in the weld zone CTOD performance descend the most severe part.
Therefore, for guaranteeing welded stability, the fine structure that control welded metal joints is to guarantee the CTOD performance of welded metal joints.For this reason, the technology that the regulation welding material is formed has been proposed.The flat 11-170085 of TOHKEMY discloses the example of described technology.Yet this technology does not relate to the control to fine structure and particle diameter, and is difficult to obtain enough toughness with the welded metal joints that the described welding material of the document is made.
In addition, TOHKEMY 2005-171300 discloses a kind of composition, comprise in weight %, at the most 0.07% C, at the most 0.3% Si, 1.0-2.0% Mn, at the most 0.02% P, at the most Ti and the B of 0.0005-0.005%, the wherein ARM---it is defined as ARM=197-1457C-1140sol.Al+11850N-316 (Pcm-C)---of N, the 0.005-0.02% of sol.Al (solubility Al), the 0.0020-0.01% of 0.1% S, 0.04-0.1% in the scope of 40-80.Yet,, therefore be difficult to guarantee carry out the impact flexibility of the welded metal joints of large-line energy SAW because specified ARM does not comprise qualification to oxygen content in the welded metal joints.
In addition, the flat 10-180488 of TOHKEMY is by comprising in weight %, the slag former of 0.5-3.0%, the C of 0.04-0.2%, the B of Mo, the 0.002-0.015% of Ni, the 0.05-1.0% of Mg, the 0.5-4.0% of Mn, the 0.05-0.3% of 0.1% Si, 1.2-3.5% to be guaranteeing suitable impact flexibility at the most, but do not relate to the content of oxygen and nitrogen.Therefore, be difficult to guarantee the CTOD performance of metal solder.
Summary of the invention
Technical problem
One aspect of the present invention provides the flux cored wire arc welding that has high-intensity performance and have excellent CTOD performance simultaneously at low temperatures to connect metal joint by the transformation of using Ti oxide and solubility B to accelerate the intragranular acicular ferrite, and the steel member with described metal welding joints.
Technical scheme
Hereinafter will describe the present invention.
According to an aspect of the present invention, the invention provides the flux cored wire arc welding that has excellent CTOD performance at low temperatures and connect metal joint, described FCAW metal joint comprises, by weight: the C of 0.01-0.2%, the Si of 0.1-0.5%, the Mn of 1.0-3.0%, the Ni of 0.5-3.0%, the Ti of 0.01-0.1%, the B of 0.0010-0.01%, the Al of 0.005-0.05%, the N of 0.003-0.006%, 0.03% P at the most, 0.03% S at the most, the O of 0.03-0.07%, described FCAW metal joint satisfies 0.≤Ti/O≤1.3,6≤Ti/N≤12, the relation of 7≤O/B≤12 and 1.2≤(Ti+4B)/O≤1.9, and the Fe of surplus and unavoidable impurities, described FCAW metal joint comprise a kind of have 85% or more acicular ferrite and surplus be bainite, at least a microscopic structure in grain boundary ferrite and the polygonal ferrite.
Described FCAW metal joint can comprise that also the element of Zr of W that one or more are selected from the Mo of the Cr of the Cu of the V of the Nb of 0.0001-0.1%, 0.005-0.1%, 0.01-2.0%, 0.05-1.0%, 0.05-1.0%, 0.05-0.5% and 0.005-0.5% is or/and one or more are selected from the element of the REM of the Ca of 0.0005-0.005% and 0.005-0.05%.
The TiO oxide of particle diameter in the scope of 0.01-0.1 μ m (micron) can 1.0 * 10
7/ mm
3Or higher being distributed in the described FCAW metal joint.
According to another aspect of the present invention, the invention provides steel member with described FCAW metal joint.
Beneficial effect
Can provide a kind of and have high-intensity performance by the transformation of using TiO oxide and solubility B to accelerate acicular ferrite in the welded metal joints, the flux cored wire arc welding that has simultaneously excellent CTOD performance at low temperatures connects metal joint, and the steel member with described metal welding joints.
The specific embodiment
To describe the present invention now.
The kind and the size of the oxide that the inventor is to influencing acicular ferrite---known its to guaranteeing that excellent CTOD performance is effective in the welded metal joints---are studied, with exploitation at the welded metal joints that carries out having when flux cored wire arc welding meets (FCAW) with the sweating heat input of 7-30kJ/cm such as high strength and excellent CTOD performance.According to this result of study, the inventor finds that the amount of the grain boundary ferrite in the welded metal joints and the amount of acicular ferrite can change by TiO and solubility B, and also respective change of the CTOD value of described welded metal joints.
Based on this research, in the present invention,
[1] the TiO oxide is used for the FCAW metal.
[2] conversion 85% or more acicular ferrite in the FCAW metal joint, the particle diameter of the oxide in the described metal joint is 0.01-0.1 μ m (micron), quantity is 1.0 * 10
7/ mm
3Or more, thus toughness improved, and
[3] by guaranteeing that TiO and solubility B accelerate the transformation of described acicular ferrite.
Now [1], [2] and [3] are described in detail.
[1] management of TiO oxide
The inventor finds, if keep the ratio between the Ti/O and O/B in the welded metal joints rightly, the TiO oxide of suitable quantity can distribute rightly with alligatoring that stops austenite crystal in the weld metal solidification process and the transformation of accelerating acicular ferrite in the TiO oxide so.
They also find, when the TiO oxide is distributed in the austenite crystal rightly, along with the temperature in the austenite descends, TiO oxide in the austenite plays the effect in the heterogeneous nucleation site of acicular ferrite transformation, thereby forms ferrite at intragranular at grain boundary ferrite before forming on the crystal boundary.Therefore, the CTOD performance of described welded metal joints can significantly be improved.
For this reason, the TiO oxide is meticulous and to distribute equably be very important.In addition, when according to the size of the ratio research TiO oxide of Ti/O and O/B, quantity and distribution, the inventor find when Ti/O in the scope of 0.2-0.5, and the ratio of O/B obtains 1.0 * 10 in the scope of 5-10 the time
7/ mm
3Or more particle diameter is the TiO oxide of 0.01-0.1 μ m (micron).
[2] microscopic structure of welded metal joints
According to the research that the ratio of Ti/O and O/B is carried out size, quantity and the distribution of TiO oxide according to the present invention, confirm when Ti/O in the scope of 0.2-0.5, and the ratio of O/B forms 1.0 * 10 in the scope of 5-10 the time
7/ mm
3Or more particle diameter is the TiO oxide of 0.01-0.1 μ m (micron).
When the TiO oxide was distributed in the weld metal rightly, the transformation meeting of intragranular acicular ferrite was accelerated prior to crystal boundary in the process of cooling welded metal joints, thus described acicular ferrite can reach welded metal joints 85% or more.
[3] effect of solubility boron in the welded metal joints
According to research of the present invention, the oxide in being evenly distributed on welded metal joints, the boron of solid solubility spreads on whole crystal boundary to reduce the energy of crystal boundary.Therefore, thus the diffusion of solubility boron stops the transformation of grain boundary ferrite to accelerate the transformation of intragranular acicular ferrite.That is, solubility boron suppresses the transformation of grain boundary ferrite on crystal boundary and the transformation of quickening intragranular acicular ferrite, and this helps the improvement of the CTOD performance of welded metal joints.
Hereinafter the composition to welded metal joints is described in detail.
[composition]
Carbon (C) content is in the scope of 0.01-0.2%.
Carbon (C) is a kind of important element of guaranteeing weld metal intensity and welding quenching degree.Yet when the content of carbon (C) surpassed 0.2%, solderability significantly descended, and in the welded metal joints cold cracking may take place, and the impact flexibility under the high heat input significantly reduces.
Silicon (Si) content is in the scope of 0.1-0.5%.
When silicone content less than 0.1% the time, deoxidation deficiency, and the flowability of weld metal descends.When silicone content surpassed 0.5%, the transformation of M-A constituent element was accelerated in the weld metal, reduced impact flexibility and influenced welding crack sensibility.
The content of manganese (Mn) is in the scope of 1.0-3.0%.
Mn strengthens deoxidation and intensity, makes the Ti composite oxides accelerate the formation of acicular ferrite thereby be precipitated as MnS around the TiO oxide, to improve the toughness of welded metal joints.
Mn forms substitutional solid solution in matrix, thereby makes described matrix solution strengthening to guarantee intensity and toughness.For this reason, Mn content is preferably 1.0% or more.Yet, when Mn content surpasses 3.0%, disadvantageously form the low-temperature transformation tissue.
The content of titanium (Ti) is in the scope of 0.01-0.1%.
Ti combines with oxygen (O) and forms meticulous Ti oxide and meticulous TiN precipitation.Therefore, Ti is a kind of important element.For forming meticulous TiO oxide and TiN composite precipitation, Ti content is preferably 0.01% or more.Yet, when Ti content surpasses 0.1%, disadvantageously form thick TiO oxide and thick TiN precipitation.
Nickel (Ni) content is in the scope of 0.5-3.0%.
Ni is a kind of element that improves the intensity and the toughness of matrix by the solution strengthening effect.For obtaining these effects, Ni content is preferably 0.5% or higher.Yet when Ni content surpassed 3.0%, quenching degree significantly increased, and the high temperature cracking may take place.
The content of boron (B) is in the scope of 0.0010-0.01%.
B is a kind of element that increases quenching degree.Thereby B content need for 0.0010% or higher make B along cyrystal boundary segregation to suppress the transformation of grain boundary ferrite.Yet when the content of B surpassed 0.01%, the increase that may weld quenching degree unfriendly caused cold cracking and reduces toughness to accelerate martensitic transformation.Therefore, B content is in the scope of 0.0010-0.01%.
The content of nitrogen (N) is in the scope of 0.003-0.006%.
N is a kind of TiN of formation precipitation and the important element that increases the amount of meticulous TiN precipitation.N is to size, spacing and the density of TiN precipitation, and TiN precipitation and oxide form the incidence of composite precipitation, and the high-temperature stability of described precipitation has important function.Therefore, N content is preferably 0.003% or higher.
Yet, when N content surpasses 0.006%, be difficult to realize any further effect, and toughness can descend because of the amount increase of soluble nitrogen in the weld metal.
The content of phosphorus (P) is 0.030% or lower.
P is a kind of impurity element that promotes the high temperature cracking in welding process.Therefore, P content is low more favourable more.For increasing toughness and reducing cracking, P content is preferably 0.03% or lower.
The content of aluminium (Al) is in the scope of 0.005-0.05%.
Al is used as deoxidier and is the essential elements that reduces oxygen content in the weld metal.In addition, Al content be 0.005% or higher so that Al combine with solubility N to form meticulous AlN precipitation.Yet, when Al content surpasses 0.05%, can form thick Al
2O
3Thereby stop increasing the formation of the essential TiO oxide of toughness.Therefore, Al content is preferably 0.05% or lower.
The content of sulphur (S) is restricted to 0.030% or lower.
S is a kind of to forming the essential element of MnS.The content of S is 0.03% or lower to obtain the MnS composite precipitation.When the content of S surpasses 0.03%, thus may form low-melting compound for example FeS cause the high temperature cracking.
The content of oxygen (O) is in the scope of 0.03-0.07%.
O be a kind of when welded metal joints solidifies and Ti reaction form the element of Ti oxide.Described Ti oxide is accelerated the transformation of acicular ferrite in the welded metal joints.When O content was lower than 0.03%, the Ti oxide may not be distributed in the welded metal joints rightly.When O content surpasses 0.07%, can form thick Ti oxide and, influence welded metal joints such as other oxide of FeO.
The ratio of Ti/O is in the scope of 0.7-1.3.
When the ratio of Ti/O was lower than 0.7, growth of control austenite crystal and acicular ferrite changed the TiO oxide deficiency in the required weld metal.In addition, the ratio of contained Ti descends in the TiO oxide, and the TiO oxide can not be as the nucleation site of acicular ferrite, and therefore the phase fraction to the effective acicular ferrite of toughness that improves the heat affected area reduces.When the ratio of Ti/O surpasses 1.3, just can not stop the growth of austenite crystal in the weld metal again.On the contrary, the ratio of alloy compositions descends in the described oxide, and therefore described oxide can not be as the nucleation site of acicular ferrite.
The ratio of Ti/N is in the scope of 6-12.
In the present invention, when the ratio of Ti/N less than 6 the time, the amount of the TiN precipitation that forms in the TiO oxide reduces and therefore effective transformation of acicular ferrite is had adverse effect.When the ratio of Ti/N surpasses 12, can not realize further effect, and the increase of the amount of soluble nitrogen, thereby reduce impact flexibility unfriendly.
The ratio of O/B is in the scope of 7-12.
In the present invention, when the ratio of O/B less than 7 the time, the amount of solubility B---in its cooling procedure after welding along the austenite grain boundary diffusion to stop the transformation of grain boundary ferrite---is not enough.When the ratio of O/B surpasses 12, can not realize further effect, and the amount of soluble nitrogen increases, reduce the toughness of heat affected area unfriendly.
(Ti+4B)/ratio of O is in the scope of 1.2-1.9.
In this embodiment, when the ratio of (Ti+4B)/O less than 1.2 the time, thereby the toughness that the amount of solubility N increases increasing welded metal joints is invalid.When the ratio of (Ti+4B)/O surpasses 1.9, the lazy weight of TiN and BN precipitation.
In the present invention, in order to improve mechanical performance, can in steel, add one or more elements that are selected from Nb, V, Cu, Mo, Cr, W and Zr again with above-mentioned composition.
The content of copper (Cu) is in the scope of 0.1-2.0%.
Cu be a kind of solid solution in matrix to guarantee the element of intensity and toughness by the solution strengthening effect.For this reason, the content of Cu is required to be 0.1% or more.Yet when Cu content surpasses 2.0%, thereby the increase of the quenching degree of welded metal joints reduces toughness and cause the high temperature in the weld metal to ftracture.
In addition, when Cu and Ni add fashionablely together, their total content is lower than 3.5%.When the content of Cu and Ni surpassed 3.5%, quenching degree increased, to such an extent as to toughness and solderability are had detrimental effect.
The content of Nb is in the scope of 0.0001-0.1%.
Nb is a kind of important element that strengthens quenching degree.Although because Nb also reduces Ar under low cooldown rate
3Temperature also enlarges the scope that bainite generates, and therefore needs to use Nb to obtain bainite structure.
Nb content is required to be 0.0001% or more to gain in strength.Yet when Nb content surpassed 0.1%, the formation of M-A constituent element quickening in the welded metal joints in the welding process was so that have adverse effect to the toughness of welded metal joints.
The content of V is in the scope of 0.005-0.1%.
V is that a kind of VN of formation precipitation is to accelerate the element of ferritic transformation.V content is required to be 0.005% or higher.Yet, when V content surpasses 0.1%, can in welded metal joints, form for example carbide of hard phase, to such an extent as to the toughness of welded metal joints is had adverse effect.
The content of chromium (Cr) is in the scope of 0.05-1.0%.
Cr increases quenching degree and intensity.When Cr content less than 0.05% the time, can not obtain required intensity.When Cr content surpasses 1.0%, can cause the toughness of welded metal joints to descend.
The content of molybdenum (Mo) is in the scope of 0.05-1.0%.
Mo also is a kind of element that increases quenching degree and intensity.The content of Mo is required to be 0.05% or higher to obtain required intensity.For hardening welded metal joints and stop disadvantageous low-temperature welding cracking, Mo content is the same with Cr to be 1.0% or lower.
The content of W is in the scope of 0.05-0.5%.
W is a kind of increase elevated temperature strength and to the precipitation-hardening effective elements.Yet when W content was lower than 0.05%, intensity just had increase slightly.When W content surpasses 0.5%, the toughness of welded metal joints had adverse effect.
Zr content is in the scope of 0.005-0.5%.
Because Zr is effective to gaining in strength, so Zr content is preferably 0.005% or higher.When Zr content surpasses 0.5%, the toughness of welded metal joints had adverse effect.
One or both growths that also can add in the present invention, Ca and REM with the inhibition original austenite grains.
Ca and REM are the useful elements that is used for forming at the welding process stable arc and in welded metal joints oxide.In addition, in cooling procedure, Ca and REM suppress the growth of austenite crystal and promote intragranular ferritic transformation, thereby increase the toughness of welded metal joints.For this reason, preferably calcium (Ca) content is 0.0005% or higher, and REM content is 0.005% or higher.Yet when Ca content surpasses 0.005%, and REM surpasses at 0.05% o'clock, can form the large scale oxide, thereby reduce toughness.With regard to REM, one or more among Ce, La, Y and the Hf can be used for realizing above-mentioned effect.
[microscopic structure of welded metal joints]
The microscopic structure of the welded metal joints that forms behind FCAW in the present invention, can comprise acicular ferrite and described acicular ferrite and have 85% or higher phase fraction.Acicular ferrite structure can obtain high strength and low temperature CTOD simultaneously.
Described microscopic structure comprises one or more in bainite, grain boundary ferrite and the polygonal ferrite.
When described microscopic structure comprises the mixture of ferrite and bainite structure, can obtain higher CTOD value, but the intensity step-down of welded metal joints.When described microscopic structure comprised the mixture of martensite and bainite structure, the intensity of welded metal joints uprised, but for example decline of CTOD performance and the increase of low temperature property easy to crack of the mechanical performance of welded metal joints.
[oxide]
The oxide that is present in the welded metal joints has important function to the transformation of the microscopic structure of the welded metal joints that welded.That is, the transformation of microscopic structure is subjected to being distributed in the appreciable impact of kind, size and the quantity of the oxide in the welded metal joints.
Particularly, for the FCAW metal joint, crystal grain is chap in process of setting, and forms tissue such as coarse-grain circle ferrite, Widmannstatten structure ferrite and bainite along crystal boundary, thereby reduces the performance of welded metal joints.
For stoping this situation, it is very important that the TiO oxide is evenly distributed in the welded metal joints with 0.5 μ m (micron) or littler regular spaces.
In addition, the particle diameter of TiO oxide in the scope of 0.01-0.1 μ m (micron) and the critical value of TiO oxide be every 1mm
3In 1.0 * 10
7Individual or more.When described particle diameter during less than 0.01 μ m (micron), the TiO oxide in the FCAW welded metal joints can not promote the transformation of acicular ferrite.In addition, when described particle diameter surpassed 0.1 μ m (micron), the locking action of austenite crystal (inhibition of grain growth) descended, and the thick non-metallic inclusion of TiO oxide conduct, and its CTOD performance to welded metal joints has adverse effect.
In addition, the invention provides steel member with above-mentioned welded metal joints.
In the present invention, except that FCAW, also can use another kind of welding method to make welded metal joints.When the cooldown rate of welded metal joints was high, oxide spread meticulously, obtains microscopic structure thus.Therefore, the large-line energy welding method that needs high cooldown rate.
In addition, for the same reason, just cooling means and Cu-substrate approach also can be used for increasing the cooling velocity of welded metal joints.
Yet even above-mentioned known technology is used for the present invention, therefore these fall within the scope of the present invention in fact also just to modification of the present invention.
Embodiment
Hereinafter describe the present invention by embodiment of the present invention.
Make the welded metal joints of forming shown in table 1 and 2 by FCAW with 7-30kJ/cm or higher welding heat input.
Downcut test specimen and carry out tension test and the CTOD test from the mid portion of welded metal joints, the results are shown in table 3.
Use is according to No. 4 test specimens of KS B 0801 test specimen as tension test, and described tension test is carried out with the ram speed of 10mm/min.
Make the CTOD test specimen according to the BS7448-1 specification, fatigue crack is positioned at the centre of SAW welded metal joints.
Use image analyzer and electron microscope to measure size, the quantity and spacing that the CTOD performance of welded metal joints is had the oxide of material impact according to a counting method.The results are shown in table 3.
Based on 100mm
2Size assess surface to be tested.
By being processed into the CTOD test specimen uses CTOD testing equipment assessment FCAW metal joint-10 ℃ temperature CTOD by the FCAW metal joint that the FCAW method obtains.
Table 1
Table 2
Table 3
As shown in table 3, the quantity of the TiO oxide of welded metal joints constructed in accordance is 3 * 10
8/ mm
3Or more, and the quantity of the TiO oxide of compared steel is 4.3 * 10
6/ mm
3Or still less.When comparing with compared steel, the invention steel has more all even meticulous composite precipitation, and its quantity significantly increases.
Simultaneously, the microscopic structure of invention steel comprises that phase fraction is 85% or more acicular ferrite.
Therefore, according to described FCAW method, the invention steel comprises polygonal ferrite and acicular ferrite at intragranular.Herein, the phase fraction of described acicular ferrite is 85% or more, and when comparing with compared steel, the invention steel has excellent welded metal joints CTOD performance.
Claims (7)
1. a flux cored wire arc welding that has excellent CTOD performance at low temperatures connects metal joint, and described FCAW metal joint comprises, by weight:
The C of 0.01-2%, the Si of 0.1-0.5%, the Mn of 1.0-3.0%, the Ni of 0.5-3.0%, the Ti of 0.01-0.1%, the B of 0.0010-0.01%, the Al of 0.005-0.05%, the N of 0.003-0.006%, 0.03% P at the most, 0.03% S at the most, the O of 0.03-0.07%, described FCAW metal joint satisfies 0.7≤Ti/O≤1.3,6≤Ti/N≤12, the relation of 7≤O/B≤12 and 1.2≤(Ti+4B)/O≤1.9, and the Fe of surplus and unavoidable impurities, described FCAW metal joint comprise a kind of have 85% or more acicular ferrite and surplus be bainite, at least a microscopic structure in grain boundary ferrite and the polygonal ferrite.
2. the FCAW metal joint of claim 1, also comprise be selected from following at least a: the Ca of Zr, the 0.0005-0.005% of W, the 0.005-0.5% of Mo, the 0.05-0.5% of Cr, the 0.05-1.0% of Cu, the 0.05-1.0% of the Nb of 0.0001-0.1%, the V of 0.005-0.1%, 0.01-2.0% and the REM of 0.005-0.05%.
3. claim 1 or 2 FCAW metal joint, wherein particle diameter is that the TiO oxide of 0.01-0.1 μ m (micron) is with 1.0 * 10
7/ mm
3Or be distributed in the described welded metal joints more.
4. the flux cored wire arc welding that has excellent CTOD performance at low temperatures that has claim 1 connects the steel member of metal joint.
5. the steel member of claim 4, wherein said welded metal joints also comprise be selected from following at least a: the Ca of Zr, the 0.0005-0.005% of W, the 0.005-0.5% of Mo, the 0.05-0.5% of Cr, the 0.05-1.0% of Cu, the 0.05-1.0% of the Nb of 0.0001-0.1%, the V of 0.005-0.1%, 0.01-2.0% and the REM of 0.005-0.05%.
6. claim 4 or 5 steel member, wherein particle diameter is that the TiO oxide of 0.01-0.1 μ m (micron) is with 1.0 * 10
7/ mm
3Or be distributed in the described weld metal more.
Applications Claiming Priority (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| KR10-2007-0138045 | 2007-12-26 | ||
| KR1020070138045A KR100910493B1 (en) | 2007-12-26 | 2007-12-26 | Flux Cored Arc Weld Metal Joint Having Superior CTOD in Low Temperature |
| PCT/KR2008/007627 WO2009082162A2 (en) | 2007-12-26 | 2008-12-23 | Flux cored arc weld metal joint having superior ctod in low temperature and steel member having the weld metal joint |
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| Publication Number | Publication Date |
|---|---|
| CN101909810A true CN101909810A (en) | 2010-12-08 |
| CN101909810B CN101909810B (en) | 2013-03-06 |
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| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN2008801232653A Active CN101909810B (en) | 2007-12-26 | 2008-12-23 | Flux cored arc weld metal joint having superior CTOD in low temperature and steel member having the weld metal joint |
Country Status (4)
| Country | Link |
|---|---|
| JP (1) | JP5172970B2 (en) |
| KR (1) | KR100910493B1 (en) |
| CN (1) | CN101909810B (en) |
| WO (1) | WO2009082162A2 (en) |
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2007
- 2007-12-26 KR KR1020070138045A patent/KR100910493B1/en active IP Right Grant
-
2008
- 2008-12-23 WO PCT/KR2008/007627 patent/WO2009082162A2/en active Application Filing
- 2008-12-23 CN CN2008801232653A patent/CN101909810B/en active Active
- 2008-12-23 JP JP2010540572A patent/JP5172970B2/en active Active
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Also Published As
| Publication number | Publication date |
|---|---|
| JP5172970B2 (en) | 2013-03-27 |
| JP2011507707A (en) | 2011-03-10 |
| KR20090070147A (en) | 2009-07-01 |
| WO2009082162A2 (en) | 2009-07-02 |
| KR100910493B1 (en) | 2009-07-31 |
| WO2009082162A3 (en) | 2009-09-24 |
| CN101909810B (en) | 2013-03-06 |
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