CN106166652B - The preparation method of Austenitic heat-resistant alloy welding point and the welding point obtained with it - Google Patents
The preparation method of Austenitic heat-resistant alloy welding point and the welding point obtained with it Download PDFInfo
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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
- B23K33/00—Specially-profiled edge portions of workpieces for making soldering or welding connections; Filling the seams formed thereby
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- 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
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- B23K9/16—Arc welding or cutting making use of shielding gas
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Abstract
The preparation method of Austenitic heat-resistant alloy welding point and the welding point obtained with it.A kind of manufacturing method of Austenitic heat-resistant alloy welding point, it will be after the austenite alloy base material welding with regulation chemical composition using welding material, implement heat treatment temperature T (DEG C) after welding, be heat-treated after the welding of heat treatment time t (minute) and T to 500 DEG C of average cooling rate RC (DEG C/h) satisfactions [800≤T≤1250], [0.2 × T+270≤t≤0.6 × T+810] and [RC >=0.05 × T 10] after welding, the welding material has following chemical compositions：C：0.06~0.18%, Si：1.0% or less, Mn：2.0% or less, P：0.03% or less, S：0.01% or less, Ni：40.0~60.0%, Cr：20.0~26.0%, the total of Mo and/or W：6.0~13.0%, Ti：0.05~0.6%, Al：1.5% or less, N：0.18% or less, O：0.01% or less, Co：0~15.0%, Nb：0~0.5%, B：0~0.005%, remainder：Fe and impurity.
Description
Technical field
The present invention relates to the creeps that the high-temperature components such as main steam pipe, high-temperature reheat pipe as boiler for power generation use
Intensity and using when weld part resistance to anti-thread breakage excellent Austenitic heat-resistant alloy welding point manufacturing method and make
The welding point obtained with it.
Background technology
In recent years, from the viewpoint of reducing carrying capacity of environment, for boiler for power generation etc., fortune is promoted in the world
Turn condition high temperature and pressure, for as the requirement of the Austenitic heat-resistant alloy of superheater tube or the materials'use of reheater tube
With superior elevated temperature strength and corrosion resistance.
In addition, in the past for used ferrite system heat resisting steel include the heavy walls such as main steam pipe, reheated steam pipe structure
The various components such as part have studied being applicable in for Austenitic heat-resistant alloy.
Under this technical background, such as is disclosed in patent document 1 and improve the same of elevated temperature strength by efficiently using W
When provide effective B amounts, the Ni based alloy products so as to improve hot-workability.In addition, being disclosed by effective in patent document 2
The Austenitic heat-resistant alloy being improved to creep strength using Cr, Ti and Zr is disclosed containing largely in patent document 3
W and efficiently use Al and Ti, by solution strengthening and the precipitation strength mutually realized using γ ', to which intensity is improved
Ni based heat resistant alloys.
When using these Austenitic heat-resistant alloys as works, usually it is assembled by welding.For using
For the welding point of Austenitic heat-resistant alloy, it is known that easy to produce the various crackles for mainly originating from metallurgy factor.Especially
Be under high temperature environment for a long time use when, leads to the problem of so-called stress relaxation crackle as.Stress relaxation crackle refer to by
The crackle generated during the residual stress relaxation that welding generates.
Disclosed in patent document 4 and efficiently use Mo and W to improve creep strength, and stipulated that impurity element and Ti and
The content of Al, so as to the austenite of crackle for preventing the when of being used for a long time under the resistance to liquation crack and high temperature when welding from generating
It is heat-resisting alloy.According to patent document 4, when using above-mentioned Austenitic heat-resistant alloy, main steam pipe or high temperature reheating are steamed
For the butt joint used in the components such as steam pipe, stress relaxation crackle can be prevented.
And as shown in non-patent literature 1, usual austenite stainless steel or Ni based alloys are without the heat treatment after welding.
However, for austenite stainless steel, in order to improve corrosion resistance and toughness, sometimes in 1000~1150 DEG C of temperature range
It is heat-treated after inside being welded, in addition, in order to remove residual stress, is welded within the temperature range of 800~900 DEG C sometimes
After be heat-treated.
In non-patent literature 2,18Cr-12Ni-Nb series austenites system stainless steel uses for a long time at high temperature in order to prevent
When the crackle that generates, disclose the heat treatment method by following three sections of steps：Welded-joint is heated to 600 DEG C or so simultaneously
It keeps, is then kept again at 1050 DEG C at such a temperature, finally kept at 900 DEG C.
Existing technical literature
Patent document
Patent document 1：No. 4631986 bulletins of Japanese Patent No.
Patent document 2：International Publication No. 2009/154161
Patent document 3：International Publication No. 2010/038826
Patent document 4：Japanese Unexamined Patent Publication 2010-150593 bulletins
Non-patent literature
Non-patent literature 1：Engagement welds that skill Intraoperative (engagement welding technique) Q＆A1000 editorial boards, " engagement welds skill
Intraoperative (engagement welding technique) Q＆A1000 ", in August, 1999, p502-503,653-654
Non-patent literature 2：Interior Mu Huzang, ridge woods like long, Li Lin filial piety, gloomy man, " the 18Cr-12Ni-Nb Steel ying power of setting store by morals
Remove baked I な ま and cut the れ stress of 18Cr-12Ni-Nb steel (removal annealing crack) ", Shi Chuan Island broadcast mill skill Reported and (broadcast on Ishikawa island
Grind skill report), Showa in March, 50, volume 15, No. 2, p209-215
Invention content
Problems to be solved by the invention
In Patent Documents 1 to 3, the problem of the stress relaxation crackle generated when not accounting for using for a long time under high temperature.Such as
It is upper described, disclose the butt joint for being used in the components such as main steam pipe or high-temperature reheat pipe in patent document 4 and
Speech, can prevent the Austenitic heat-resistant alloy of stress relaxation crackle.However, there are variously-shaped and rulers in actual works
Very little weld part.The inventors of the present invention implement detailed investigation, as a result it is found that different and residual according to the shape and size of weld part
The existence of residue stress is different.And according to the shape or size of weld part, even if the technology described in using patent document 4,
It is also possible to the effect that cannot fully obtain preventing stress relaxation crackle.
In addition distinguish, for the Austenitic heat-resistant alloy as object of the present invention, even if merely assigning non-special
In the case of being heat-treated after welding described in sharp document 1 or 2, residual stress can also be relaxed, so as to prevent stress
Relaxation crackle.But according to the condition being heat-treated after welding, the creep strength of welding point is possible to be greatly reduced.
The object of the present invention is to provide the main steam pipes or the high temperature structure such as reheated steam pipe as thermal power generation boiler
The manufacturing method of part uses, creep strength and proof stress relax anti-thread breakage excellent Austenitic heat-resistant alloy welding point and
The welding point obtained using it.
The solution to the problem
The inventors of the present invention weld to solve the above-mentioned problems and to implementing the Austenitic heat-resistant alloy being heat-treated after welding
Connector is studied in detail.And implement creep test for having carried out the welding point of rear heat treatment under various conditions,
As a result known to according to connector and creep strength reduce degree there are a great differences.
In order to investigate this reason, using the welding point before and after progress creep test, structure observation is carried out, for creep
The big situation of strength reduction and small situation, compare the difference of tissue.As a result, being connect for the welding that creep strength is greatly reduced
For head, coarse M is sparsely precipitated before creep test23C6Carbide, and constitute M23C6The Cr contents of carbide are low.Into
And after creep test, M23C6Carbide is significantly roughened.
Fine M23C6The contribution that carbide improves creep strength by being scattered in crystal grain is big.Result, it is believed that high
For a long time in use, due to M under warm environment23C6Carbide is significantly roughened and creep strength is greatly reduced.M23C6Carbide Coarsening
Mechanism can be as described below.
Fine carbide is precipitated in crystal grain if using for a long time under high temperature environment.As a result, after due to welding
It is heat-treated originally in crystal grain there are in the welding point of coarse carbide, two kinds of different carbide of size are mixed in one
It rises.If particle size difference significantly if pass through following processes：The difference of interface energy between particle increases, the difference shape of interface energy
The carbide small at driving force disappears, neighbouring coarse carbide further growth.
And think, as in the main composition amount of element contained in the carbide of precipitate and equilibrium state lower substrate
The difference hour of the amount of element contained, carbide are easy growth.That is, constituting M23C6The Cr contents of carbide are low to become M23C6Carbonization
The main reason for growth of object promotes.
The inventors of the present invention further investigate repeatedly, as a result, it has been found that, M in order to prevent23C6The roughening of carbide, at hot after welding
Manage temperature, after welding heat treatment time and by heat treatment temperature after welding until being easy to generate M23C6Until 500 DEG C of carbide
The various conditions of cooling rate carry out appropriate management and be important.
The present invention proposes that purport is, following Austenitic heat-resistant alloy welding points based on above-mentioned discovery
Manufacturing method and the welding point obtained using it.
(1) a kind of manufacturing method of Austenitic heat-resistant alloy welding point, is welded alloy base material using welding material
After connecing, it is heat-treated after implementing welding under conditions of meeting following (i)~(iii) formulas,
800≤T≤1250···(i)
-0.2×T+270≤t≤-0.6×T+810···(ii)
RC≥0.05×T-10···(iii)
Wherein, the meaning of each symbol in above formula is as described below,
T：Heat treatment temperature after welding, unit are DEG C
t：Heat treatment time after welding, unit are minute
RC：T to 500 DEG C of average cooling rate, unit are DEG C/h
The alloy base material has following chemical compositions：The C based on quality %：0.04~0.12%, Si：1.0% or less,
Mn：2.0% or less, P：0.03% or less, S：0.01% or less, Ni：42.0~48.0%, Cr：20.0~26.0%, W：4.0
~10.0%, Ti：0.05~0.15%, Nb：0.1~0.4%, Al：0.3% or less, B：0.0001~0.01%, N：0.02%
Below, O：0.01% or less, Ca：0~0.05%, Mg：0~0.05%, REM：0~0.1%, Co：0~1.0%, Cu：0~
4.0%, Mo：0~1.0%, V：0~0.5%, remainder：Fe and impurity,
The welding material has following chemical compositions：The C based on quality %：0.06~0.18%, Si：1.0% or less,
Mn：2.0% or less, P：0.03% or less, S：0.01% or less, Ni：40.0~60.0%, Cr：20.0~26.0%, Mo and W
One or both of total：6.0~13.0%, Ti：0.05~0.6%, Al：1.5% or less, N：0.18% or less, O：
0.01% or less, Co：0~15.0%, Nb：0~0.5%, B：0~0.005%, remainder：Fe and impurity.
(2) according to the manufacturing method of the Austenitic heat-resistant alloy welding point described in (1), wherein aforementioned alloy base material
Chemical composition based on quality % containing being selected from
Ca：0.0001~0.05%,
Mg：0.0001~0.05%,
REM：0.0005~0.1%,
Co：0.01~1.0%,
Cu：0.01~4.0%,
Mo：0.01~1.0%,
V：One or more of 0.01~0.5%.
(3) according to the manufacturing method of the Austenitic heat-resistant alloy welding point described in (1) or (2), wherein aforementioned welding
The chemical composition of material contains based on quality % to be selected from
Co：0.01~15.0%,
Nb：0.01~0.5%,
B：One or more of 0.0001~0.005%.
(4) manufacturing method of the Austenitic heat-resistant alloy welding point according to any one of (1)~(3), wherein
The condition being heat-treated after aforementioned welding also meets following (iv) formulas,
RH≥40···(iv)
Wherein, the meaning of the symbol in above formula is as described below,
RH：500 DEG C of average heating speeds to T, unit are DEG C/h.
(5) manufacturing method of the Austenitic heat-resistant alloy welding point according to any one of (1)~(4), wherein
The thickness of aforementioned alloy base material is more than 30mm.
(6) a kind of Austenitic heat-resistant alloy welding point uses the manufacturing method described in any one of (1)~(5)
It obtains.
The effect of invention
Manufacturing method according to the invention, when can stably obtain creep strength and the use when can have both high temperature
The Austenitic heat-resistant alloy welding point that the proof stress of weld part relaxes anti-thread breakage.
Specific implementation mode
Each condition of the present invention is described in detail below.It should be noted that in the following description, about content
" % " is referred to " quality % ".
1. the chemical composition of alloy base material
The each element contained by alloy base material used in the manufacture of the Austenitic heat-resistant alloy welding point of the present invention
Restriction reason it is as described below.
C：0.04~0.12%
C has the function of making stabilization of austenite, and is to form fine carbide and have and improve in applied at elevated temperature
Creep strength effect element.In order to fully obtain this effect, the C content for 0.04% or more is needed.However, C contains
When amount is excessive, carbide becomes thick, and is largely precipitated, therefore so that creep strength is reduced instead.If especially big to containing
The welding point of amount C is heat-treated after implementing welding, then the growth of carbide, creep strength is promoted to significantly reduce.Therefore, C content
It is set as 0.12% or less.C content is preferably 0.05% or more, and more preferably 0.06% or more.In addition, C content is preferably
0.11% hereinafter, more preferably 0.08% or less.
Si：1.0% or less
Si has deoxidation, and the effective element of raising of the corrosion resistance and oxidative resistance when being to high temperature.However,
Excessively containing in the case of Si, the stability of austenite reduces, and leads to the reduction of toughness and creep strength.Therefore, the content of Si
The upper limit is set, is set as 1.0% or less.Si contents are preferably 0.8% hereinafter, more preferably 0.6% or less.
It should be noted that Si contents without especially setting lower limit, however cannot fully be taken off when extreme reduction
The detergency deterioration of oxygen effect, alloy, and the improvement effect of the corrosion resistance and oxidative resistance when also being difficult to obtain high temperature, manufacture
Cost is also sharply increased.Therefore, Si contents are preferably 0.02% or more, and more preferably 0.05% or more.
Mn：2.0% or less
It is the element with deoxidation in the same manner as Mn and Si.In addition, Mn additionally aids the stabilisation of austenite.However,
Lead to embrittlement when Mn content excess, and then also generates the reduction of toughness and creep ductility.Therefore, the upper limit is arranged in Mn contents, if
It is 2.0% or less.Mn contents are preferably 1.8% hereinafter, more preferably 1.5% or less.
It should be noted that Mn contents without especially setting lower limit, however cannot fully be taken off when extreme reduction
The detergency deterioration of oxygen effect, alloy, and be also difficult to obtain stabilization of austenite effect, and then manufacturing cost also substantially rises
It is high.Therefore, Mn contents are preferably 0.02% or more, and more preferably 0.05% or more.
P：0.03% or less
P contains in the alloy as impurity, and in the case of largely containing, hot-workability and weldability significantly reduce, in turn
Creep ductility under high temperature after long-time use also reduces.Therefore, the upper limit is arranged in P content, is set as 0.03% or less.P content
Preferably 0.025% hereinafter, more preferably 0.02% or less.
It should be noted that it is preferred that reduce P content as far as possible, but extreme reduction leads to the increase of manufacturing cost.Cause
This, P content is preferably 0.0005% or more, and more preferably 0.0008% or more.
S：0.01% or less
S and P contains in the alloy similarly as impurity, and in the case of largely containing, hot-workability and weldability are notable
It reduces, and then the creep ductility under high temperature after long-time use also reduces.Therefore, S contents be arranged the upper limit, be set as 0.01% with
Under.S contents are preferably 0.008% hereinafter, more preferably 0.005% or less.
It should be noted that S contents preferably reduce as far as possible, but extreme reduction leads to the increase of manufacturing cost.Cause
This, S contents are preferably 0.0001% or more, and more preferably 0.0002% or more.
Ni：42.0~48.0%
Ni is the effective element for obtaining austenite, and tissue when being for ensuring to use for a long time under high temperature is steady
Necessary element for qualitative.In order to obtain sufficient effect in the range of the Cr contents of the present invention, 42.0% or more is needed
Ni contents.However, Ni is expensive element, cost is caused to increase if a large amount of contain.Therefore the setting upper limit, Ni contents
It is set as 42.0~48.0%.Ni contents are preferably 42.5% or more, and more preferably 43.0% or more.In addition, Ni contents are preferably
47.5% hereinafter, more preferably 47.0% or less.
Cr：20.0~26.0%
Oxidative resistance and corrosion resistance when Cr is in order to ensure high temperature and required element.In addition, Cr also formed it is fine
Carbide and contribute to ensuring for creep strength.In order to obtain said effect in the range of the Ni contents of the present invention, need
20.0% or more Cr contents.However, when Cr contents are more than 26.0%, the stability degradation of austenite when high temperature and cause compacted
The reduction of intensity adjustable.Especially in implementing the present invention being heat-treated after welding for welding point, promote the growth of carbide,
Therefore creep strength significantly reduces.Therefore, Cr contents are set as 20.0~26.0%.Cr contents are preferably 20.5% or more, more excellent
It is selected as 21.0% or more.In addition, Cr contents are preferably 25.5% hereinafter, more preferably 25.0% or less.
W：4.0~10.0%
W is to be solid-solution in matrix, be additionally formed fine intermetallic compound phase and creep strength when to high temperature and stretching
Big element is contributed in the raising of intensity.In order to fully obtain this effect, 4.0% or more W content is needed.But even if mistake
Amount is also saturated containing W, effect, instead so that creep strength reduces.In turn, excessive containing sometimes since W is expensive element
Lead to the increase of cost.Therefore, the upper limit is set, and W content is set as 4.0~10.0%.W content is preferably 4.5% or more, more preferably
It is 5.0% or more.In addition, W content is preferably 9.5% hereinafter, more preferably 9.0% or less.
Ti：0.05~0.15%
Ti is precipitated with fine carbonitride form in crystal grain, creep strength when helping to improve high temperature and is stretched strong
Degree.In order to fully obtain this effect, 0.05% or more Ti contents are needed.However, when Ti content excess, it is a large amount of that carbon nitrogen is precipitated
Compound leads to the reduction of creep ductility and toughness.Therefore, the upper limit is set, and Ti contents are set as 0.05~0.15%.Ti contents are excellent
It is selected as 0.06% or more, more preferably 0.07% or more.In addition, Ti contents are preferably 0.14% hereinafter, more preferably 0.13%
Below.
Nb：0.1~0.4%
Nb and C or N are precipitated in conjunction with and with fine carbide or carbonitride form in crystal grain, when contributing to high temperature
Creep strength improves.In order to fully obtain this effect, 0.1% or more Nb contents are needed.However, when Nb content excess, with
Carbide and carbonitride form are largely precipitated, and lead to the reduction of creep ductility and toughness.Therefore, the upper limit, Nb contents are set
It is set as 0.1~0.4%.Nb contents are preferably 0.12% or more, and more preferably 0.15% or more.In addition, Nb contents are preferably
0.38% hereinafter, more preferably 0.35% or less.
Al：0.3% or less
Al is the element for having deoxidation.But the detergency of alloy significantly deteriorates if Al content is excessive, hot-working
Property and ductility reduction.Therefore the setting upper limit, Al content are set as 0.3% or less.Al content is preferably 0.2% hereinafter, more preferably
It is 0.1% or less.
It should be noted that for Al content without especially setting lower limit, but cannot fully be obtained if extreme reduce
The detergency of deoxidation effect, alloy deteriorates instead, and the improvement effect of the corrosion resistance and oxidative resistance when being difficult to obtain high temperature,
Manufacturing cost is also sharply increased.Therefore, Al content is preferably 0.0005% or more, and more preferably 0.001% or more.
B：0.0001~0.01%
B be for by fine dispersion grain boundary carbide improve creep strength and strengthen crystal boundary in cyrystal boundary segregation and
Say effective element.This effect in order to obtain, B content need to be 0.0001% or more.However, when B content excess, due to weldering
Thermal Cycle in connecing and be largely segregated B in the heat affected area of melting near border and reduce the fusing point of crystal boundary, liquation crack
Sensibility improves.Therefore, the upper limit is set, and B content is set as 0.0001~0.01%.B content is preferably 0.0005% or more, more excellent
It is selected as 0.001% or more.In addition, B content is preferably 0.008% hereinafter, more preferably 0.006% or less.
N：0.02% or less
Although N is for making austenite stablize effective element, excessive to contain sometimes, big in use at high temperature
The fine nitride of amount is precipitated in crystal grain and causes the reduction of creep ductility and toughness.Therefore, the upper limit is arranged in N content, if
It is 0.02% or less.N content is preferably 0.018% hereinafter, more preferably 0.015% or less.
It should be noted that for N content without especially setting lower limit, but be difficult to obtain when extreme reduction so that Austria
The effect that family name's body is stablized, manufacturing cost are also sharply increased.Therefore, N content is preferably 0.0005% or more, more preferably
0.0008% or more.
O：0.01% or less
O (oxygen) contains in the alloy as impurity, and when content excess, hot-workability reduces, and then leads to toughness and prolong
The deterioration of malleability.Therefore, the upper limit is arranged in O content, is set as 0.01% or less.O content is preferably 0.008% hereinafter, more preferably
0.005% or less.
It should be noted that for O content without especially setting lower limit, but extreme reduction leads to the liter of manufacturing cost
It is high.Therefore, O content is preferably 0.0005% or more, and more preferably 0.0008% or more.
The alloy base material used in the manufacture of the Austenitic heat-resistant alloy welding point of the present invention has following chemical groups
At：Containing above-mentioned each element, remainder is made of Fe and impurity.
It should be noted that when " impurity " refers to industrially manufacturing alloy, from the ore, waste material or manufacture as raw material
The mixed ingredient such as environment.
In alloy base material in the present invention, other than above-mentioned element, can also contain selected from Ca, Mg, REM, Co, Cu,
One or more of Mo and V element.
The restriction reason of function and effect and content below for above-mentioned element illustrates.
Ca：0~0.05%
Ca has the function of improving hot-workability.Accordingly it is also possible to contain Ca.However, when Ca content excess, combined with O
And detergency significantly reduces, hot-workability deteriorates instead.When therefore, containing Ca, Ca contents are set as 0.05% or less.Ca contents are excellent
It is selected as 0.03% or less.
It should be noted that wanting in the case of obtaining said effect, Ca contents are preferably 0.0001% or more, more preferably
It is 0.0005% or more.
Mg：0~0.05%
Have the function of improving hot-workability in the same manner as Mg and Ca.Accordingly it is also possible to contain Mg.However, Mg contents are excessive
When, with O in conjunction with and detergency significantly reduce, instead hot-workability deteriorate.When therefore, containing Mg, Mg contents be set as 0.05% with
Under.Mg contents are preferably 0.03% or less.
It should be noted that wanting in the case of obtaining said effect, Mg contents are preferably 0.0001% or more, more preferably
It is 0.0005% or more.
REM：0~0.1%
The affinity of REM and S is strong, has the function of improving hot-workability, and compacted in use when being for high temperature
Become the effective element of raising of ductility.Accordingly it is also possible to contain REM.However, when REM content excess, combined with O, is significantly dropped
Low detergency, instead hot-workability deterioration.When therefore, containing REM, REM contents are set as 0.1% or less.REM contents are preferably
0.06% or less.
It should be noted that wanting in the case of obtaining said effect, REM contents are preferably 0.0005% or more, more excellent
It is selected as 0.001% or more.
It should be noted that " REM " is general name of 17 kinds of elements of total of Sc, Y and lanthanide series, what the content of REM referred to
It is the total content of one or more of REM elements.In addition, for REM, usually contain in norium.
Thus, for example the amount that can also add, make REM in the form of norium reaches above range to contain.
Above-mentioned Ca, Mg and REM improve the effect of hot-workability due to all having, and can only contain therein any
Kind, or can by it is two or more it is compound in the form of contain.By these elements compoundings come to contain total amount sometimes can be 0.2%.
Co：0~1.0%
It is austenite forming element in the same manner as Co and Ni, improves phase stability and contribute to the raising of creep strength.Therefore,
Co can also be contained.However since Co is the extremely expensive element of price, the excess of Co, which contains, causes cost substantially to increase.
When therefore, containing Co, Co contents are set as 1.0% or less.Co contents are preferably 0.8% or less.
It should be noted that wanting in the case of obtaining said effect, Co contents are preferably 0.01% or more, more preferably
0.03% or more.
Cu：0~4.0%
Cu has the function of improving creep strength.That is, being austenite forming element in the same manner as Cu and Ni and Co, improve mutually steady
Raising that is qualitative and contributing to creep strength.Accordingly it is also possible to contain Cu.However, it is excessive containing in the case of Cu, cause heat to add
The reduction of work, thus containing Cu when, Cu contents are set as 4.0% or less.Cu contents are preferably 3.0% or less.
It should be noted that wanting in the case of obtaining said effect, Cu contents are preferably 0.01% or more, more preferably
0.03% or more.
Mo：0~1.0%
Mo has the function of improving creep strength.That is, Mo has creep strength when being solid-solution in matrix and improving high temperature
Effect.Therefore it can also contain Mo.However, excessive containing in the case of Mo, the stability of austenite reduces, and instead results in creep
Strength reduction.When therefore containing Mo, Mo contents are set as 1.0% or less.Mo contents are preferably 0.8% or less.
It should be noted that wanting in the case of obtaining said effect, Mo contents are preferably 0.01% or more, more preferably
0.03% or more.
V：0~0.5%
V has the function of improving creep strength.That is, V and C or N in conjunction with and form fine carbide or carbonitride, have
It is improved the effect of creep strength.Accordingly it is also possible to contain V.However, when excessively containing V, with carbide or carbonitride form
It is a large amount of to be precipitated, lead to the reduction of creep ductility.When therefore, containing V, V content is set as 0.5% or less.V content is preferably
0.4% or less.
It should be noted that wanting in the case of obtaining said effect, V content is preferably 0.01% or more, more preferably
0.02% or more.
Above-mentioned Co, Cu, Mo and V improve the effect of creep strength due to all having, and can only contain therein any
Kind, or by it is two or more it is compound in the form of contain.By these elements compoundings come to contain total amount sometimes can be 6.5%.
2. the chemical composition of welding material
The each element contained by welding material used in the manufacture of the Austenitic heat-resistant alloy welding point of the present invention
Restriction reason it is as described below.
C：0.06~0.18%
C has the function of the stabilization of austenite in the welding metal after to weld, and is to form fine carbonization
Object and have the effect of improve applied at elevated temperature in creep strength element.In turn, by being formed altogether with Cr in being solidified in welding
Brilliant carbide additionally aids the reduction of Solidification Cracking Sensitivity.In order to fully obtain this effect, 0.06% or more C is needed
Content.However, when C content excess, carbide is largely precipitated, therefore makes creep strength and ductility reduction instead.Therefore, C contains
Amount is set as 0.18% or less.C content is preferably 0.07% or more, and more preferably 0.08% or more.In addition, C content is preferably
0.16% hereinafter, more preferably 0.14% or less.
Si：1.0% or less
Si is effective for deoxidation in the manufacture of welding material, and resistance to when being the high temperature to the welding metal after welding
The effective element of raising of corrosion and oxidative resistance.However, excessive containing in the case of Si, the stability of austenite is reduced and is led
Cause the reduction of toughness and creep strength.Therefore, the upper limit is arranged in Si contents, is set as 1.0% or less.Si contents be preferably 0.8% with
Under, more preferably 0.6% or less.
It should be noted that Si contents without especially setting lower limit, however cannot fully be taken off when extreme reduction
The detergency deterioration of oxygen effect, alloy, and the improvement effect of the corrosion resistance and oxidative resistance when also being difficult to obtain high temperature, manufacture
Cost is also sharply increased.Therefore, Si contents are preferably 0.02% or more, and more preferably 0.05% or more.
Mn：2.0% or less
It is in the manufacture of welding material in the same manner as Mn and Si for the effective element of deoxidation.In addition, Mn additionally aids weldering
The stabilisation of the austenite in welding metal after connecing.However, lead to embrittlement when Mn content excess, and then also generate toughness and compacted
Become the reduction of ductility.Therefore, the upper limit is arranged in Mn contents, is set as 2.0% or less.Mn contents are preferably 1.8% hereinafter, more preferably
It is 1.5% or less.
It should be noted that Mn contents without especially setting lower limit, however cannot fully be taken off when extreme reduction
The detergency deterioration of oxygen effect, alloy, and be also difficult to obtain stabilization of austenite effect, and then manufacturing cost also substantially rises
It is high.Therefore, Mn contents are preferably 0.02% or more, and more preferably 0.05% or more.
P：0.03% or less
P contains as impurity in welding material, is the element that Solidification Cracking Sensitivity is improved in welding.In turn, make
The creep ductility of welding metal when high temperature after long-time use reduces.Therefore, P content be arranged the upper limit, be set as 0.03% with
Under.P content is preferably 0.025% hereinafter, more preferably 0.02% or less.
It should be noted that it is preferred that reduce P content as far as possible, but extreme reduction leads to the increase of manufacturing cost.Cause
This, P content is preferably 0.0005% or more, and more preferably 0.0008% or more.
S：0.01% or less
S and P contain similarly as impurity largely contain in welding material in the case of, hot-workability and weldability
Significantly reduce, so S at high temperature for a long time use when lead to embrittlement in column crystal cyrystal boundary segregation in welding metal, improve
Stress relaxation crack sensitivity.Therefore, the upper limit is arranged in S contents, is set as 0.01% or less.S contents be preferably 0.008% hereinafter,
More preferably 0.005% or less.
It should be noted that S contents preferably reduce as far as possible, but extreme reduction leads to the increase of manufacturing cost.Cause
This, S contents are preferably 0.0001% or more, and more preferably 0.0002% or more.
Ni：40.0~60.0%
Ni is for making the effective element of stabilization of austenite in the welding metal after welding, and is for ensuring high temperature
Necessary element for structure stability when lower long-time uses.The Ni contents of this effect in order to obtain, welding material need
To be 40.0% or more.However, Ni is expensive element, even the welding material manufactured on a small scale, if largely containing
Then also result in cost increase.Therefore the setting upper limit, Ni contents are set as 40.0~60.0%.Ni contents be preferably 40.5% with
On, more preferably 41.0% or more.In addition, Ni contents are preferably 59.5% hereinafter, more preferably 59.0% or less.
Cr：20.0~26.0%
Oxidative resistance when Cr is the high temperature for ensuring the welding metal after welding and the effective element of corrosion resistance.Separately
Outside, Cr also forms fine carbide and contributes to ensuring for creep strength.In turn, by being formed altogether with C in being solidified in welding
Brilliant carbide additionally aids the reduction of Solidification Cracking Sensitivity.These effects in order to obtain need 20.0% or more Cr to contain
Amount.However, when Cr contents are more than 26.0%, the stability degradation of austenite when high temperature and the reduction for leading to creep strength.Cause
This, the Cr contents of welding material are set as 20.0~26.0%.Cr contents are preferably 20.5% or more, more preferably 21.0% with
On.In addition, Cr contents are preferably 25.5% hereinafter, more preferably 25.0% or less.
The total of one or both of Mo and W：6.0~13.0%
Mo and W is to be solid-solution in matrix in welding metal or form fine intermetallic compound phase and high to improving
The big element of the contribution of creep strength and tensile strength when warm.In order to fully obtain this effect, one of Mo and W or two
Person, which amounts to, to be needed containing 6.0% or more.However, being saturated excessively containing these elements, effect, it is strong that creep is reduced instead
Degree.In turn, excessive containing the increase for occasionally resulting in cost since Mo and W is expensive element.Therefore, the upper limit is set,
The total content of one or both of Mo and W is set as 6.0~13.0%.Total content is preferably 6.5% or more, more preferably
7.0% or more.In addition, total content is preferably 12.5% hereinafter, more preferably 12.0% or less.
Ti：0.05~0.6%
Ti is precipitated with fine carbonitride form in crystal grain in welding metal, helps to improve creep when high temperature
Intensity and tensile strength.In order to fully obtain this effect, Ti contents need to be 0.05% or more.However, when Ti content excess,
It is a large amount of that carbonitride is precipitated, lead to the reduction of creep ductility and toughness.Therefore, the upper limit is set, and the Ti contents of welding material are set
It is 0.05~0.6%.Ti contents are preferably 0.06% or more, and more preferably 0.07% or more.In addition, Ti contents are preferably
0.58% hereinafter, more preferably 0.55% or less.
Al：1.5% or less
Deoxidation effective element when Al is the manufacture for welding material.In addition, forming fine gold in welding metal
Compound phase between category and the raising for contributing to creep strength.However, when Al content excess, the detergency of alloy is significantly deteriorated and is welded
The hot-workability and ductility reduction of material are connect, therefore manufacturing is deteriorated.And it is formed in welding metal between a large amount of metal
Compound phase significantly improves stress relaxation crack sensitivity when being used for a long time under high temperature.Therefore, the upper limit is set, material is welded
The Al content of material is set as 1.5% or less.Al content is preferably 1.4% hereinafter, more preferably 1.3% or less.
It should be noted that Al content without especially setting lower limit, however cannot fully be taken off when extreme reduction
Oxygen effect, alloy detergency deteriorate instead, and the improvement effect of the corrosion resistance and oxidative resistance when also being difficult to obtain high temperature,
Manufacturing cost is also sharply increased.Therefore, Al content is preferably 0.0005% or more, and more preferably 0.001% or more.
N：0.18% or less
N is to make stabilization of austenite in welding metal, improve creep strength, and being dissolved and help to ensure to stretch strong
The element of degree.However, excessive containing sometimes, a large amount of fine nitride is precipitated in crystal grain and causes compacted in use at high temperature
Become the reduction of ductility and toughness.Therefore, the upper limit is arranged in the N content of welding material, is set as 0.18% or less.N content is preferably
0.16% hereinafter, more preferably 0.14% or less.
It should be noted that for N content without especially setting lower limit, but be difficult to obtain when extreme reduction so that Austria
The effect that family name's body is stablized, manufacturing cost are also sharply increased.Therefore, N content is preferably 0.0005% or more, more preferably
0.0008% or more.
O：0.01% or less
O (oxygen) contains as impurity in welding material, and when content excess, hot-workability reduces, and leads to manufacturing
Deterioration.Therefore, the upper limit is arranged in O content, is set as 0.01% or less.O content is preferably 0.008% hereinafter, more preferably 0.005%
Below.
It should be noted that for O content without especially setting lower limit, but extreme reduction leads to the liter of manufacturing cost
It is high.Therefore, O content is preferably 0.0005% or more, and more preferably 0.0008% or more.
Co：0~15.0%
Make that the austenite structure of welding metal is stable in the same manner as Co and Ni, contribute to the raising of creep strength, therefore
It can contain as needed.However, since Co is the extremely expensive element of price, even welding material, excess contain
Cost is also resulted in substantially to increase.When therefore, containing Co, Co contents are set as 15.0% or less.Co contents be preferably 14.0% with
Under, further preferably 13.0% or less.It should be noted that wanting in the case of obtaining said effect, Co contents are preferably
0.01% or more, more preferably 0.03% or more.
Nb：0~0.5%
Nb and C or N are precipitated in conjunction with and with fine carbide or carbonitride form in crystal grain, when contributing to high temperature
Creep strength improves, therefore can also contain as needed.However, when the content excess of Nb, with carbide and carbonitride shape
Formula is largely precipitated, and leads to the reduction of creep ductility and toughness.When therefore, containing Nb, Nb contents are set as 0.5% or less.Nb contains
Amount preferably 0.48% is hereinafter, more preferably 0.45% or less.It should be noted that want in the case of obtaining said effect,
Nb contents are preferably 0.01% or more, and more preferably 0.03% or more.
B：0~0.005%
B be for the raising of the creep strength of welding metal effectively and for strengthening crystal boundary in cyrystal boundary segregation and
It says effective element, therefore can also contain as needed.However, when B content excess, the Solidification Cracking Sensitivity in welding is aobvious
It writes and increases.When therefore, containing B, B content is set as 0.005% or less.B content is preferably 0.004% hereinafter, more preferably
0.003% or less, it should be noted that want in the case of obtaining said effect, B content is preferably 0.0001% or more, more
Preferably 0.0005% or more.
The welding material used in the manufacture of the Austenitic heat-resistant alloy welding point of the present invention has following chemical groups
At：Containing above-mentioned each element, remainder is made of Fe and impurity.
3. heat treatment condition after welding
The Austenitic heat-resistant alloy welding point of the present invention can be female by aforementioned alloy by using aforementioned welding material
After material welding, it is heat-treated after implementing welding to manufacture.As previously mentioned, it is anti-thread breakage in order to have both creep strength and proof stress relaxation,
It needs to be heat-treated after being welded under conditions of meeting following (i)~(iii) formulas.
Heat treatment temperature T (DEG C) after welding：800≤T≤1250···(i)
As it was noted above, the welding point being thermally treated resulting in after welding is under high temperature environment for a long time in use, in order to subtract
The reduction of light creep strength inhibits the coarse M in heat treatment process after welding23C6The generation of carbide and raising M23C6Carbon
Cr contents in compound are effective.In order to reach these, treatment temperature set will be needed after welding to obtain low.Therefore, butt welding
The rear heat treatment temperature setting upper limit is connect, is set as 1250 DEG C or less.
On the other hand, welding residual stress cannot be made fully to relax if heat treatment temperature is too low after welding, cause to answer
Power relaxation crack sensitivity increases.Therefore, heat treatment temperature is set as 800 DEG C or more after welding.Heat treatment temperature is preferred after welding
It is 850 DEG C or more, more preferably 900 DEG C or more.In addition, heat treatment temperature is preferably 1150 DEG C hereinafter, more preferably after welding
1000 DEG C or less.
Heat treatment time t (minute) after welding：-0.2×T+270≤t≤-0.6×T+810···(ii)
In order to inhibit the coarse M after welding in heat treatment process23C6The generation of carbide, only after regulation welding at heat
It is insufficient to manage temperature, needs to be managed heat treatment time after welding using the relationship with above-mentioned temperature.In order to mitigate
The reduction of creep strength will need after welding heat treatment time to be set to short, is set as [- 0.6 × T+810] (minute) below.Separately
On the one hand, welding residual stress cannot be made fully to relax if heat treatment time is too short after welding, lead to stress relaxation crackle
Sensibility increases.Therefore heat treatment time is set as [- 0.2 × T+270] (minute) or more after welding.
T to 500 DEG C of average cooling rate RC (DEG C/h)：RC≥0.05×T-10···(iii)
It only manages after above-mentioned welding after heat treatment temperature and welding when heat treatment time, cannot completely inhibit after welding at heat
Coarse M during reason23C6The generation of carbide.Due to also generating M when cooling after being heat-treated after welding23C6Carbonization
Object, it is therefore desirable to according to heat treatment temperature management after welding by the temperature to the lower limit of 500 DEG C of average cooling rate.Therefore right
By heat treatment temperature after welding to 500 DEG C average cooling rate be arranged lower limit, be set as [0.05 × T-10] (DEG C/h) with
On.
It should be noted that in the manufacturing method of the Austenitic heat-resistant alloy welding point of the present invention, after aforementioned welding
The condition of heat treatment preferably also meets following (iv) formulas.
500 DEG C of average heating speeds (DEG C/h) to T：RH≥40···(iv)
In the temperature-rise period being heat-treated after welding, if the average heating speed of 500 DEG C of heat treatment temperature T (DEG C) to after welding
RH is less than 40 DEG C/h, then in temperature-rise period, fine carbide, carbonitride and intermetallic are precipitated in crystal grain
Object, when complicated weld part shape, it is possible to stress relaxation crackle is generated during being heat-treated after welding.Cause
This, is arranged lower limit to the average heating speed of 500 DEG C of heat treatment temperatures to after welding, is preferably set to 40 (DEG C/h) or more.
4. other
For the alloy base material and welding material used in the manufacture of the Austenitic heat-resistant alloy welding point of the present invention
Shape or size be not particularly limited.Wherein, it is being more than the alloy of 30mm using thickness that the manufacturing method of the present invention, which is especially,
Effect is played when base material.Therefore, the thickness of alloy base material is preferably greater than 30mm.
More specific description is carried out to the present invention by the following examples, but the present invention is not limited by these embodiments
It is fixed.
[embodiment 1]
It will be melted with the alloy of chemical composition shown in table 1 and make steel ingot.Using above-mentioned steel ingot, pass through hot-forging forming
Afterwards, solution heat treatment when carrying out 1230 DEG C, make respectively thickness 15mm, width 50mm, length 100mm and thickness 32mm,
The alloy sheets of width 150mm, length 200mm.Then, these alloy sheets are split for creep rupture test and stress relaxation respectively
The confirmation of the presence or absence of line.
[table 1]
In turn, after steel ingot being made with the melting of the alloy of chemical composition shown in table 2, pass through hot forging, hot rolling and machinery
Processing makes the welding material of outer diameter 1.2mm.
[table 2]
Creep rupture test follows the steps below.In the alloy of above-mentioned thickness 15mm, width 50mm, length 100mm
The length direction of plate, 30 ° of finished edge angle, root thickness 1mm V grooves after, using above-mentioned welding material, welded by TIG
It connects, multi-layer welding is carried out in groove, make welding point.Then, under the conditions of for obtained welding point shown in table 3
It is heat-treated after implementing welding.Then, by welding point pole creep is acquired in such a way that welding metal forms the center of parallel portion
Destructive test piece, the targeted fractured time of base material alloy sheets is about 1000 hours 700 DEG C, 147MPa under conditions of carry out it is compacted
Become destructive test.
[table 3]
* mean to be unsatisfactory for condition specified in the present invention.
* means to be unsatisfactory for optimum condition specified in the present invention.
-0.2×T+270≤t≤-0.6×T+810···(ii)
RC≥0.05×T-10···(iii)
In addition, the confirmation of the presence or absence of stress relaxation crackle, in order to reproduce the harsh stress shape in complicated weld part shape
State is carried out according to following step.Using the alloy sheets of above-mentioned thickness 32mm, width 150mm, length 200mm, it is based on JIS Z
Then y types weld cracking expreiment method specified in 3158 (1993), the test film made by being machined use above-mentioned
Welding material carries out single layer welding in groove, makes welding point by TIG weld.Then, it is connect for obtained
Head, after being heat-treated after implementing welding under the same conditions with the condition implemented in above-mentioned creep rupture test, 700 DEG C of progress,
500 hours aging strengthening models.For the welding heat affected zone of treated welding point, test film is acquired by each 5 positions.
Then, by the cross section mirror ultrafinish of the test film, after being corroded with chloroazotic acid, optical microphotograph sem observation is carried out under 500 times of multiplying power,
Investigate the presence or absence of crackle.
The result of above-mentioned creep rupture and crackle observation, which summarizes, is shown in table 3.As a result, it will fracture about creep rupture test
The case where time is more than the targeted fractured time of base material alloy sheets is denoted as " ◎ ", will be more than the targeted fractured time of base material alloy sheets
85% the case where be denoted as "○", be in addition to this denoted as "×".In addition, about crackle observation as a result, complete used in observing
For 5, portion test film all without finding that the welding point of crackle is denoted as "○", only one section finds that the welding point of crackle is denoted as
" △ ", is judged as qualification.And more than two test films find that the welding point of crackle is denoted as "×", is judged as unqualified.
As shown in Table 3, after welding heat treatment condition meet present invention provide that test number 1~5,7~20 and
27~45, there is good creep strength, even and harsh weld part shape, also there is excellent proof stress relaxation to split
Line.In addition we know, test number 6 is since the Elevated Temperature Conditions in being heat-treated after welding are less than preferred range, for this
For the harsh weld part shape being applicable in embodiment, although only one section generates stress relaxation crackle, have
The performance that can be allowed.
On the other hand, prescribed limit of the test number 21 due to rear heat treatment temperature less than the present invention, weld part
Residual stress removal is insufficient, and stress relaxation crackle is generated with high-frequencies more than two sections.In addition, test number 22 and 23
Since the retention time in rear heat treatment is less than the lower limit time determined by rear heat treatment temperature, similarly weld part is residual
Residue stress removal is insufficient, for harsh weld part shape applicable in this present embodiment, due to prolonged timeliness heat
Processing generates stress relaxation crackle with high-frequencies more than two sections.
In turn, test number 24 and 25 due to the retention time in rear heat treatment be more than determined by rear heat treatment temperature it is upper
Between in limited time, coarse M is generated in rear heat treatment process23C6Carbide cannot get necessary creep strength.In addition, experiment is compiled
Numbers 26, since the cooling velocity in rear heat treatment is less than the lower limit determined by rear heat treatment temperature, generate in rear heat treatment process
Coarse M23C6Carbide cannot get necessary creep strength.
Industrial availability
Manufacturing method according to the invention, when can stably obtain creep strength and the use when can have both high temperature
The Austenitic heat-resistant alloy welding point that the proof stress of weld part relaxes anti-thread breakage.
Claims (11)
1. a kind of manufacturing method of Austenitic heat-resistant alloy welding point, after alloy base material is welded using welding material,
It is heat-treated after implementing welding under conditions of meeting following (i)~(iii) formulas,
800≤T≤1250···(i)
-0.2×T+270≤t≤-0.6×T+810···(ii)
RC≥0.05×T-10···(iii)
Wherein, the meaning of each symbol in above formula is as described below,
T：Heat treatment temperature after welding, unit are DEG C
t：Heat treatment time after welding, unit are minute
RC：T to 500 DEG C of average cooling rate, unit are DEG C/h
The alloy base material has following chemical compositions：The C based on quality %：0.04~0.12%, Si：1.0% or less, Mn：
2.0% or less, P：0.03% or less, S：0.01% or less, Ni：42.0~48.0%, Cr：20.0~26.0%, W：4.0~
10.0%, Ti：0.05~0.15%, Nb：0.1~0.4%, Al：0.3% or less, B：0.0001~0.01%, N：0.02% with
Under, O：0.01% or less, Ca：0~0.05%, Mg：0~0.05%, REM：0~0.1%, Co：0~1.0%, Cu：0~
4.0%, Mo：0~1.0%, V：0~0.5%, remainder：Fe and impurity,
The welding material has following chemical compositions：The C based on quality %：0.06~0.18%, Si：1.0% or less, Mn：
2.0% or less, P：0.03% or less, S：0.01% or less, Ni：40.0~60.0%, Cr：20.0~26.0%, in Mo and W
The total of one or both：6.0~13.0%, Ti：0.05~0.6%, Al：1.5% or less, N：0.18% or less, O：
0.01% or less, Co：0~15.0%, Nb：0~0.5%, B：0~0.005%, remainder：Fe and impurity.
2. the manufacturing method of Austenitic heat-resistant alloy welding point according to claim 1, wherein the alloy base material
Chemical composition based on quality % containing being selected from
Ca：0.0001~0.05%,
Mg：0.0001~0.05%,
REM：0.0005~0.1%,
Co：0.01~1.0%,
Cu：0.01~4.0%,
Mo：0.01~1.0%,
V：One or more of 0.01~0.5%.
3. the manufacturing method of Austenitic heat-resistant alloy welding point according to claim 1, wherein the welding material
Chemical composition based on quality % containing being selected from
Co：0.01~15.0%,
Nb：0.01~0.5%,
B：One or more of 0.0001~0.005%.
4. the manufacturing method of Austenitic heat-resistant alloy welding point according to claim 2, wherein the welding material
Chemical composition based on quality % containing being selected from
Co：0.01~15.0%,
Nb：0.01~0.5%,
B：One or more of 0.0001~0.005%.
5. the manufacturing method of Austenitic heat-resistant alloy welding point according to claim 1, wherein hot after the welding
The condition of processing also meets following (iv) formulas,
RH≥40···(iv)
Wherein, the meaning of the symbol in above formula is as described below,
RH：500 DEG C of average heating speeds to T, unit are DEG C/h.
6. the manufacturing method of Austenitic heat-resistant alloy welding point according to claim 2, wherein hot after the welding
The condition of processing also meets following (iv) formulas,
RH≥40···(iv)
Wherein, the meaning of the symbol in above formula is as described below,
RH：500 DEG C of average heating speeds to T, unit are DEG C/h.
7. the manufacturing method of Austenitic heat-resistant alloy welding point according to claim 3, wherein hot after the welding
The condition of processing also meets following (iv) formulas,
RH≥40···(iv)
Wherein, the meaning of the symbol in above formula is as described below,
RH：500 DEG C of average heating speeds to T, unit are DEG C/h.
8. the manufacturing method of Austenitic heat-resistant alloy welding point according to claim 4, wherein hot after the welding
The condition of processing also meets following (iv) formulas,
RH≥40···(iv)
Wherein, the meaning of the symbol in above formula is as described below,
RH：500 DEG C of average heating speeds to T, unit are DEG C/h.
9. according to the manufacturing method of Austenitic heat-resistant alloy welding point according to any one of claims 1 to 8, wherein
The thickness of the alloy base material is more than 30mm.
10. a kind of Austenitic heat-resistant alloy welding point uses the manufacturing method described in any one of claim 1~8
It obtains.
11. a kind of Austenitic heat-resistant alloy welding point, is obtained using the manufacturing method described in claim 9.
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| JP7393626B2 (en) * | 2019-09-26 | 2023-12-07 | 日本製鉄株式会社 | Austenitic stainless steel welded fittings |
| CN112935619B (en) * | 2020-12-01 | 2023-04-18 | 四川大西洋焊接材料股份有限公司 | Matched welding rod for welding martensitic steel serving at 630 ℃ for long time and preparation method thereof |
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| JP2001003120A (en) * | 1999-06-18 | 2001-01-09 | Babcock Hitachi Kk | Method for welding heat resistant steel and after-heat treatment thereof |
| CN102686757A (en) * | 2009-12-10 | 2012-09-19 | 住友金属工业株式会社 | Austenitic heat-resistant alloy |
| CN102947047A (en) * | 2010-06-07 | 2013-02-27 | 新日铁住金株式会社 | Welding material for austenitic heat-resistant steel, and welded metal and welded joint each using same |
| CN104014929A (en) * | 2014-06-19 | 2014-09-03 | 西安特种设备检验检测院 | Dissimilar metal welding method for martensite heat-resisting steel and high-temperature nickel base alloy |
| CN104493374A (en) * | 2014-11-19 | 2015-04-08 | 钢铁研究总院 | Austenitic stainless steel welding wire and welding technology thereof |
Also Published As
| Publication number | Publication date |
|---|---|
| CN106166652A (en) | 2016-11-30 |
| JP2016215228A (en) | 2016-12-22 |
| JP6439579B2 (en) | 2018-12-19 |
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