CN107138876A - A kind of low nickel cupric type T/P92 steel wldings of high temperature creep-resisting - Google Patents
A kind of low nickel cupric type T/P92 steel wldings of high temperature creep-resisting Download PDFInfo
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- CN107138876A CN107138876A CN201710527074.4A CN201710527074A CN107138876A CN 107138876 A CN107138876 A CN 107138876A CN 201710527074 A CN201710527074 A CN 201710527074A CN 107138876 A CN107138876 A CN 107138876A
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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
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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
- B23K35/22—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
- B23K35/308—Fe as the principal constituent with Cr as next major constituent
- B23K35/3086—Fe as the principal constituent with Cr as next major constituent containing Ni or Mn
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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
- B23K2103/00—Materials to be soldered, welded or cut
- B23K2103/02—Iron or ferrous alloys
- B23K2103/04—Steel or steel alloys
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Abstract
The present invention provides a kind of low nickel cupric type T/P92 steel wldings of high temperature creep-resisting, it is characterised in that：Including component C, Mn, Si, Cr, Ni, W, Mo, Nb, V, N, B, Al, Ti, S, P, Fe and Cu, copper content in wlding（wt.%）For：0.8‑1.5.Wlding of the present invention adds copper, reduces nickel element content, is not added with noble element cobalt, reduces material cost, its deposited metal is while ferrite formation is suppressed, it is to avoid AC1That puts significantly reduces, and its ambient temperature mechanical properties meets or exceeds T/P92 steel wldings that are existing nickelic or adding cobalt；Wlding of the present invention has an excellent Properties of High Temperature Creep, its deposited metal it is long when the stress rupture life-span closest to P92 steel average value.
Description
Technical field
The invention belongs to technical field of heat-resistant steel, and in particular to a kind of ultra supercritical coal-fired unit high temperature creep-resisting T/
P92 steel welding materials.
Background technology
T/P92 steel is that a certain amount of wolfram element, appropriate reduction molybdenum element content are added on the basis of T/P91 steel, and is added
Plus a kind of novel martensitic heat resisting steel obtained from micro boron element, it is widely used in extra-supercritical unit main steam pipe, header
Deng posted sides pipeline, and the heating surface tube such as superheater, reheater, its casting material (C92) is also used for manufacture cylinder and valve.
The main method of welding T/P92 steel is for manual electric arc welding (SMAW), submerged-arc welding (SAW) and argon tungsten-arc welding (GATW) etc. at present,
The welding materials such as packing material, i.e. welding rod and welding wire need to be added during welding.
Compared with T/P91 steel, more High-Temperature Strengthening elemental tungsten is added in T/P92 steel, its wlding deposited metal or weldering
It is sewn in process of setting and easily forms δ-ferrite, it reduces the impact flexibility and high temperature creep strength of material.It is therefore prevented that deposition
It is the matter of utmost importance for needing to solve during T/P92 steel welding material is designed that δ-ferrite is formed in metal or weld seam.At present, T/ is suppressed
P92 steel wldings deposited metal formation δ-ferritic composition design method has 2 kinds, and a kind of method is to improve the manganese in deposited metal
The MTS616 series welding rods and welding wire of the content of element and nickel element, such as Bole welding group (the gloomy welding of the former base of a fruit), Britain are graceful thorough
The welding rods of Chromet 92 and 9CrWV welding wires of special welding material company etc.；Another method adds mother metal institute in deposited metal
Without cobalt element, the welding rods of ALCROMOCORD 92 and the welding wires of ALCROMO WF 92 such as Switzerland's Olympic health, day Benshen's steel
CR-12S welding rods and US-12CRSD welding wires etc..The drawbacks of former composition design method, is that manganese, nickel are expansion austenite phase
P-block element p, the A of deposited metal can be significantly reduced by improving their contentC1Point, austenite is re-formed in post weld heat treatment
Risk, the upper limit content for limiting Mn+Ni of having to for this, causes deposited metal still to have δ-ferrite residual.Contain in addition, improving nickel
Croop property is adversely affected when amount is long to the high temperature of material.Though latter composition design method is to deposited metal AC1The influence of point
Very little, but cobalt is expensive, adds wlding cost.It is therefore desirable to provide a kind of deposited metal that can both suppress to form δ-iron
Ferritic, while having deposited metal A againC1The point T/P92 steel welding material specials that high, Properties of High Temperature Creep is excellent and cost is low.
The content of the invention
The problem of existing for prior art, the technical scheme that the present invention uses for solution problems of the prior art
It is as follows：
A kind of low nickel cupric type T/P92 steel wldings of high temperature creep-resisting, it is characterised in that：The wlding include following component C,
Mn, Si, Cr, Ni, W, Mo, Nb, V, N, B, Al, Ti, S, P, Fe and Cu.
Copper content (wt.%) is in the wlding：0.8-1.5.
The content (wt.%) of each component is in the wlding：C 0.07-0.12、Mn 0.30-0.60、Si≤0.40、Cr
8.50-9.50、Ni≤0.40、W 1.50-2.00、Mo 0.30-0.60、Cu 0.8-1.5、Nb 0.04-0.07、V 0.15-
0.25th, N 0.03-0.07, B 0.001-0.005, Al≤0.03, Ti≤0.01, S≤0.01, P≤0.02, surplus are Fe.
The technical scheme is that by calculating deposited metal chromium equivalent and optics Metallographic Analysis of Semi, the δ that is inhibited-
Ferrite forms required minimum copper content；Calculated by Material Thermodynamics and dilatometry quantitative study copper content is to deposition gold
Belong to AC1The influence of point；Influence by high-temerature creep destructive test research copper content to deposited metal croop property, and pass through electricity
Copper particle distribution and size in the micro-analysis laboratory facilities research deposited metal creep sample such as mirror, grasp copper in T/P92
High-Temperature Strengthening mechanism in steel, it is determined that the copper content scope of reinforcing best results.The result of study of 3 aspects of summary, really
Determine the copper content scope of cupric type T/P92 steel wlding deposited metals, and the austenizer such as manganese and nickel content is carried out corresponding
Adjustment.
The high temperature creep-resisting of the present invention considers following factor with the composition characteristic of T/P92 steel welding material deposited metals：
Carbon：C is austenite stabilizer element, can be with stable tempering martensitic microstructure, and forms carbide raising
Creep strength.When C content is less than 0.07%, weld seam easily forms δ-ferrite, and carbide quantity is few, to creep strength not
Profit.But C content is too high, increase welding crack sensibility, therefore the present invention C content scope control in 0.07-0.12%.
Manganese and nickel：Mn is austenite stabilizer element, is conducive to suppressing δ-ferrite, while Mn has deoxidation desulfuration,
The intensity and toughness of weld seam can be increased.But Mn too high levels, hence it is evident that the A of reduction weld seamC1Point, causes weld seam in highest postwelding heat
Austenite is re-formed under treatment temperature, Mn contents significantly reduce creep strength more than 1.5% in addition.Ni is also austenitic formation
Element, has positive role, therefore can improve the impact flexibility of weld seam to suppressing δ-ferrite formation and stable martensitic structure.For
The new 9%Cr refractory steel weld seam formation δ-ferrite such as suppression T/P91, T/P92, European BS EN standards define highest Ni
Content is 0.8%, or even 1.0%, hence it is evident that higher than the Ni upper content limits value (0.4%) of T/P91, T/P92 steel.But, improve Ni
Content significantly reduces AC1Point, causes weld seam to re-form austenite under highest post weld heat treatment temperature, in addition, there is research table
It is bright, when the Ni contents in high chromium refractory steel are more than 0.4%, accelerate M during long-term creep23C6The roughening of type carbide and Z
The formation of phase, reduces croop property.Consider, the present invention is by the control of Mn contents in 0.30-1.0%, and the control of Ni contents exists
Within 0.40%, and Mn+Ni total content is controlled below 1.0%, than states such as current MTS616, Chromet 92 and 9CrWV
The Ni contents of outer trade mark T/P92 steel wlding deposited metal and Mn+Ni total content reduction by 50% or so.
Silicon：Si is a kind of important deoxidier, and can improve the antioxygenic property of weld seam.Appropriate low Si contents are favourable
In the toughness for improving weld metal, 0.30%, the present invention need to be less than according to the Si contents of some technical standard order weld seams of the U.S.
Si contents control in 0.1%-0.40%, the Si upper content limits (0.5%) than P92 steel are lower.
Chromium：Cr is to ensure anti-steam oxidation and the most important element of heat erosion.With the increase of Cr contents, the anti-steaming of weld seam
Vapour corrosive nature is better.But, Cr is ferrite former, during its too high levels, and δ-ferrite, reduction will be produced in weld seam
The impact flexibility and creep strength of weld seam.Therefore, Cr contents of the invention are controlled in 8.5-9.5%.
Tungsten and molybdenum：W and Mo are ferrite former, are unfavorable for preventing weld seam formation δ-ferrite, but they are T/
Most important solution strengthening element in P92 steel, and the stability of carbide can be improved and indirect invigoration effect is played.To ensure
The high temperature creep strength of weld seam, W and Mo content ranges of the invention are suitable with T/P92 steel, respectively 1.5-2.0% and 0.3-
0.6%.
Copper：Plus Cu is the main innovation point of the present invention, because T/P92 steel and existing T/P92 steel welding material deposition gold
Cu is free of in category.Cu main function has：Cu is austenite former, can suppress to form δ-ferrite in weld seam, in addition,
The experimental study of inventor shows that the T/P92 steel weld seam of cupric is after experience post weld heat treatment, and the Cu of as-welded lower solid solution is with ε-Cu
Particle is separated out, and it is and higher in the number density of lath circle in lath and lath circle dispersed distribution, as shown in Figure 1.Therefore,
With M23C6Type carbide is the same, and it can prevent the migration of sub boundary during long-term creep and improve creep strength, such as Fig. 2
It is shown.The determination of Cu content ranges need to consider to suppress ferrite formation, give full play to the effect of its High-Temperature Strengthening and avoid AC1Point
Substantially reduce this 3 factors.The present invention is related such that its content range：The ferrite content determined according to chromium equivalent thought
Computational methods (refer to Chinese patent ZL201210192206.X), and on ferrite Forming ability is suppressed, Cu is suitable with Co, about
1.5 times of Mn, about the 60% of Ni, that is, keep identical to suppress often to add 1% Cu in ferrite effect, weld seam, can reduce
1.5% Mn, or reduce by 0.6% Ni.For the influence of High-Temperature Strengthening, when Cu contents are less than 0.5%, Cu elements are substantially
In the base, seldom, precipitation strength effect is little for the ε-Cu quantity of precipitation for solid solution；Experimental study shows, when Cu contents exceed
When 1.5%, ε-Cu assemble roughening (Fig. 3 and Fig. 4) during long-term creep, not only weaken reinforcing effect, and reduction is lasting
Plasticity.On Cu contents to AC1The influence of point, though Cu reduces A to expand austenite phase p-block element pC1Point, but Patent No.
ZL201210131877.5 patent shows that Cu reduces AC1The amplitude of point is less than Mn and Ni, in addition, calculation of thermodynamics and actual measurement are tied
Fruit shows, when Cu contents are more than 0.7%, continues to increase Cu contents, to AC1Point has little to no effect, as shown in Figure 5-Figure 7.It is comprehensive
The copper addition for considering above-mentioned 3 factors is closed, it is final to determine that copper content scope of the invention is：0.8-1.5%.
Niobium：Nb is carbide, and it forms the MX type Second Phase Precipitation things of small and dispersed with C, N, and it is in height
It is highly stable under temperature, so as to improve the high temperature creep strength of weld seam.When its content is less than 0.04%, object amount is separated out few, it is impossible to
The reinforcing effect of abundance is obtained, studies have found that Nb contents are high, the impact flexibility of weld seam is reduced.Therefore, the present invention contains Nb
Amount control is in 0.04%-0.07%, and the upper limit is 0.09% more slightly lower than T/P92 steel.
Vanadium：V is carbide, and it forms small and dispersed, stable MX type Second Phase Precipitation things with C, N, carries
The high temperature creep strength of high weld seam.Its influence to welding seam toughness is smaller, in order to ensure the Properties of High Temperature Creep of weld seam, this hair
Bright V content is suitable with T/P92 steel, controls in 0.15%-0.25%.
Nitrogen：N, into the MX type Second Phase Precipitation things of small and dispersed, significantly improves the high temperature creep strength of weld seam with Nb, V-arrangement.
Its influence to welding seam toughness is smaller, in order to ensure the Properties of High Temperature Creep of weld seam, N content and T/P92 steel phases of the invention
When control is in 0.04%-0.07%.
Boron：B is boundary-strengthening element, can improve the high temperature creep strength of weld seam, but boron easily burns in welding process
Damage.In order to ensure the Properties of High Temperature Creep of weld seam, B content of the invention is controlled in 0.001%-0.005%, slightly below T/
The higher limit (0.006%) of P92 steel.
Aluminium：Al is added in wlding as deoxidier, and the Al content remained in weld seam is too high, reduces the lasting of weld seam
Plasticity.In addition, Al is easily preferentially combined with N so that the N of solid solution is approximately zero in weld seam, it is impossible to form precipitation strength effect, drop
The high temperature creep strength of low weld seam.Therefore, the Al content of the present invention is controlled below 0.03%.
Titanium：Ti is a kind of extremely strong carbide former, influence Nb, V and C, N combination, while can be formed once
TiN, is unfavorable for playing precipitation enhancement.Therefore, Ti contents of the invention are controlled below 0.01%.
Sulphur and phosphorus：S and P are inevitably impurity element, the crackle tendency of their increase weld seams, and reduce in weld seam
The creep rupture plasticity of weld seam.Therefore, the present invention controls S and P content within 0.01% and 0.02% respectively.
The invention has the advantages that：
(1) wlding of the present invention adds copper, reduces nickel element content, is not added with noble element cobalt, reduces material cost, its
Deposited metal is while ferrite formation is suppressed, it is to avoid AC1That puts significantly reduces, and its ambient temperature mechanical properties reaches or surpassed
Cross T/P92 steel wldings that are existing nickelic or adding cobalt；
(2) wlding of the present invention has an excellent Properties of High Temperature Creep, its deposited metal it is long when the stress rupture life-span most
Close to the average value of P92 steel.
Brief description of the drawings
Precipitated phase of Fig. 1 wlding deposited metals of the present invention after 760 DEG C × 4h tempering；
Precipitated phase of Fig. 2 wlding embodiments of the present invention after 650 DEG C/100Ma/4897.1h duration runnings；
Precipitated phase of T/P92 wlding deposited metals of the Fig. 3 containing 1.69%Cu after 760 DEG C × 4h tempering；
Precipitation of T/P92 wlding deposited metals of the Fig. 4 containing 1.69%Cu after 650 DEG C/100Ma/3896.5h duration runnings
Phase；
Fig. 5 is copper content to P92 weld seams AC1The thermodynamics calculation results of point influence；
Fig. 6 wlding embodiment deposited metal A of the present inventionC1The dilatometry measured result of point；
Fig. 7 wlding comparative example deposited metal A of the present inventionC1The dilatometry measured result of point；
Fig. 8 is microscopic structure (SMAW) of the wlding deposited metal of the present invention after 760 DEG C × 4h tempering；
The comparison of Fig. 9 wlding embodiments of the present invention and comparative example in the 650 DEG C/100Ma stress rupture times；
Embodiment
Below by embodiment, and with reference to accompanying drawing, technical scheme is described in further detail, such as Fig. 1-
Shown in 9：
Found out by accompanying drawing 1, wlding deposited metal of the present invention is after 760 DEG C × 4h tempering, except precipitation on martensite lath circle
M23C6Type carbonization beyond the region of objective existence, also separates out relatively fine ε-Cu particles.
Found out by accompanying drawing 2, wlding deposited metal of the present invention is after 650 DEG C/100Ma/4897.1h creeps, martensite lath
ε-Cu particles in boundary are highly stable, do not significantly build up and grow up.
Found out by accompanying drawing 3 and accompanying drawing 4, when the Cu contents in T/P92 weld seams are more than 1.5%, weld metal 760 DEG C ×
Though ε-Cu the particles separated out on martensite lath circle after 4h tempering are relatively fine, persistently tried in 650 DEG C/100Ma/3896.5h
Occurs obvious agglomeration after testing.
Found out by accompanying drawing 5, when Cu contents are more than 0.7%, continue to increase Cu contents, to AC1Point has little to no effect.
Found out by accompanying drawing 6, the A of wlding weld metal of the present inventionC1Point is 809 DEG C, (760 DEG C) high compared with post weld heat treatment temperature
Go out 49 DEG C, meet post weld heat treatment temperature and compare AC1The requirement of low more than 20-30 DEG C of point, surplus is larger.
Found out by accompanying drawing 7, the A of the wlding weld metal containing 1.69%CuC1Point is 805 DEG C, with the weld seam containing 0.86Cu%
Metal AC1Less, experiment is confirmed when Cu contents are more than 0.7% point difference, continues to increase Cu contents, to T/P92 weld metals
AC1Point has little to no effect.
Found out by accompanying drawing 8, wlding weld metal of the present invention is tempering lath martensitic structure, without ferrite.
Found out by accompanying drawing 9, T/P92 steel wlding weld metal (1#) of the present invention is most long in 650 DEG C/100Ma creep rupture life,
More than the average value of T/P92 steel creep rupture lives, hence it is evident that higher than it is existing nickelic or add cobalt T/P92 steel wlding weld metals (5#-
7#)。
And the creep rupture life of the T/P92 wldings deposited metal (4#) containing 1.69%Cu reduces compared with 1#, illustrate when Cu contents surpass
When crossing the upper limit of the present invention (1.5%), the adverse effect to enduring quality is larger.
According to the deposited metal of the material component proportion design wlding in technical solution of the present invention after 760 DEG C × 4h tempering
Tissue signature and performance：
(1) weld seam is deep drawing martensitic structure, without ferrite；
(2) weld seam AC1Point >=805 DEG C；
(3) room-temperature mechanical property of weld seam：Rp0.2(σ0.2) >=550MPa, Rm(σb)≥680MPa,A(δ0.5) >=18, KV2
>=47J, meets GB/T5118-2012 standards and ASME SFA-5.5-2015 standards to T/P92 steel wlding deposited metal room temperature power
Learn the requirement of performance：Rp0.2(σ0.2) >=530MPa, Rm(σb)≥620MPa,A(δ0.5) >=15 or 17% (GB/T5118 standard gauges
It is set to 15%, ASME standards to be defined as 17%)；
(4) enduring quality：Creep rupture life >=4500h under 650 DEG C/100MPa.
According to the composition range of the present invention, by taking welding rod as an example, multigroup has been done to low nickel cupric type T/P92 steel wldings of the invention
Embodiment, copper is added by coating or core wire.The copper content scope of comparative example 1 exceedes the upper limit (1.5%) of the present invention, is
In order to illustrate the influence of the too high properties of weld of copper content.In order to contrast, in same weld technique (preheating 200-250 DEG C, electric current
130-180A, voltage 24-30V, interlayer temperature≤350 DEG C) and post weld heat treatment technique (760 DEG C × 4h) under the conditions of, with current 3
Plant typical case's T/P92 steel electrodes --- Thyssen MTS616 welding rods (improving manganese element and nickel element content), day Benshen's steel CR-
The welding rods of ALCROMOCORD 92 (plus cobalt element) of 12S welding rods (plus cobalt element), Olympic health, have carried out the ratio of deposited metal performance
Compared with.Table 1 lists the chemical composition of 7 kinds of T/P92 steel electrode deposited metals.
The embodiment of table 1 and the chemical composition of comparative example deposited metal (wt%)
The properties test result of the embodiment of the present invention is as shown in table 2- tables 3.Found out by table 2, welding rod deposition of the present invention
The room-temperature mechanical property of metal is suitable with MTS616 welding rod deposited metals, and room temperature impact toughness is less than CR-12S welding rods deposition gold
Category, but mechanical properties and impact flexibility are integrally better than the welding rod deposited metals of ALCROMOCORD 92.As seen from Table 3, this hair
Ballistic work of the bright welding rod deposited metal after Long-term Aging and the welding rod deposited metal of MTS616, CR-12S and ALCROMOCORD 92
Quite.As seen from Table 4, in terms of high temperature creep-resisting is with the most important performance indications of wlding, the length of welding rod deposited metal of the present invention
When enduring quality be significantly better than CR-12S welding rod deposited metals, also superior to the welding rod deposited metal of MTS616, ALCROMOCORD 92,
Its life-span of creep rupture under 650 DEG C/100MPa has exceeded the P92 steel life-span of creep rupture average values that ECCC in 2005 is announced
(4735h).The copper content scope of comparative example 1 exceedes the upper limit of the present invention, and its creep rupture life has declined compared with embodiment.
The room-temperature mechanical property of the embodiment of table 2 and comparative example
The room temperature impact work((J) of the embodiment of table 3 and comparative example after 650 DEG C
The stress rupture time (h) of the embodiment of table 4 and comparative example under 650 DEG C of different stress
In summary, high temperature creep-resisting P92 wldings of the present invention taken with low cost copper substitute nickel element or
The alloy compositions design of expensive cobalt element, in the room-temperature mechanical property and the premise of long-time aging ballistic work for ensureing deposited metal
Under, improve deposited metal it is long when enduring quality this most important performance indications, have the advantages that cost performance is high.
Protection scope of the present invention is not limited to the above embodiments, it is clear that those skilled in the art can be to this hair
It is bright to carry out various changes and deform without departing from scope and spirit of the present invention.If these are changed and deformation belongs to power of the present invention
In the range of profit requirement and its equivalent technologies, then including the intent of the present invention is also changed and deformed comprising these.
Claims (3)
1. a kind of low nickel cupric type T/P92 steel wldings of high temperature creep-resisting, it is characterised in that：The wlding include following component C,
Mn, Si, Cr, Ni, W, Mo, Nb, V, N, B, Al, Ti, S, P, Fe and Cu.
2. a kind of low nickel cupric type T/P92 steel wldings of high temperature creep-resisting as claimed in claim 1, it is characterised in that：It is described
Copper content (wt.%) is in wlding：0.8-1.5.
3. a kind of low nickel cupric type T/P92 steel wldings of high temperature creep-resisting as claimed in claim 1, it is characterised in that：It is described
The content (wt.%) of each component is in wlding：C 0.07-0.12、Mn 0.30-0.60、Si≤0.40、Cr 8.50-9.50、Ni
≤0.40、W 1.50-2.00、Mo 0.30-0.60、Cu 0.8-1.5、Nb 0.04-0.07、V 0.15-0.25、N 0.03-
0.07th, B 0.001-0.005, Al≤0.03, Ti≤0.01, S≤0.01, P≤0.02, surplus are Fe.
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| CN201710527074.4A CN107138876B (en) | 2017-06-30 | 2017-06-30 | High-temperature creep resistant low-nickel copper-containing T/P92 steel welding material |
| PCT/CN2018/097698 WO2019001587A1 (en) | 2017-06-30 | 2018-07-28 | Low-nickel copper-containing type t/p92 steel weld material for combating high temperature creep |
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| CN201710527074.4A CN107138876B (en) | 2017-06-30 | 2017-06-30 | High-temperature creep resistant low-nickel copper-containing T/P92 steel welding material |
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Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2019001587A1 (en) * | 2017-06-30 | 2019-01-03 | 武汉大学 | Low-nickel copper-containing type t/p92 steel weld material for combating high temperature creep |
| CN110000490A (en) * | 2019-05-17 | 2019-07-12 | 中国电建集团上海能源装备有限公司 | A kind of T/P92 heat resistant steel electrode and preparation method thereof |
| CN110142530A (en) * | 2019-06-18 | 2019-08-20 | 清河县联盛焊接材料有限公司 | A kind of welding rod suitable for various steels welding, purposes and preparation method thereof |
| CN112536545A (en) * | 2019-09-20 | 2021-03-23 | 林肯环球股份有限公司 | High chromium creep resistant weld metal for arc welding of thick walled steel members |
| CN112536544A (en) * | 2019-09-20 | 2021-03-23 | 林肯环球股份有限公司 | High chromium creep resistant weld metal for arc welding of thin wall steel members |
| CN112935620A (en) * | 2021-01-14 | 2021-06-11 | 上海欣冈贸易有限公司 | Metal composition for welding |
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| WO2019001587A1 (en) * | 2017-06-30 | 2019-01-03 | 武汉大学 | Low-nickel copper-containing type t/p92 steel weld material for combating high temperature creep |
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| CN112536544A (en) * | 2019-09-20 | 2021-03-23 | 林肯环球股份有限公司 | High chromium creep resistant weld metal for arc welding of thin wall steel members |
| CN112935620A (en) * | 2021-01-14 | 2021-06-11 | 上海欣冈贸易有限公司 | Metal composition for welding |
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| WO2019001587A1 (en) | 2019-01-03 |
| CN107138876B (en) | 2022-05-24 |
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