CN111843284B - Welding wire for 9Cr-3W-3Co martensite heat-resistant steel and application of welding wire in GTAW welding process - Google Patents
Welding wire for 9Cr-3W-3Co martensite heat-resistant steel and application of welding wire in GTAW welding process 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
- 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
Abstract
The invention provides a welding wire for 9Cr-3W-3Co martensite heat-resistant steel and application thereof in a GTAW welding process. The welding wire comprises the following chemical components in percentage by mass: c: 0.05 to 0.12%, Si: 0.50% or less, Mn: 1.0% or less, P: 0.01% or less, S:0.008% or less, Ni: 0.20% or less, Cr: 8.50-9.50%, W: 2.50-3.0%, Co: 2.50-3.50%, Nb: 0.03-0.07%, V: 0.15-0.25%, N: 0.03 to 0.07%, B: 0.004% or less, Cu: 0.10% or less, Ti: 0.01% or less, Al: less than 0.03%, and the balance Fe and inevitable impurities. A of GTAW weld metal of the welding wireC1High point, high weld impact toughness and excellent high-temperature creep rupture strength.
Description
Technical Field
The invention belongs to the technical field of welding materials, and particularly relates to a welding wire for 9Cr-3W-3Co martensite heat-resistant steel and application thereof in a GTAW welding process.
Background
The 9Cr-3W-3Co martensite heat-resistant steel is an ideal material for building an ultra-supercritical thermal power generating unit with steam temperature parameters of more than 625 ℃, commercial grades of G115 steel developed in China and T/P93 steel developed in Japan are available, and the creep rupture strength of the steel is improved by 20-50% compared with that of T/P92 steel. The main difference between the G115 steel and the T/P93 steel is that the former steel is added with about 1% of Cu element. In the process of building a high-parameter ultra-supercritical thermal power generating unit, a large number of welding joints of the steel exist, so that the technological property and the normal-temperature mechanical property of the joints are required to meet the requirements, and particularly the matched welding material with excellent high-temperature creep resistance is required. Argon tungsten-arc welding (GATW) has the advantages of good protection effect, single-side welding and double-side forming, stable welding quality and the like, is a common welding method for ultra-supercritical power station equipment, and is used for backing welding and all-position filling welding of small-diameter pipes. In recent years, the narrow gap GTAW method has begun to be used for welding large-diameter martensitic heat-resistant steel pipes.
At present, some components of argon arc welding wires for G115 steel are disclosed, such as argon arc welding solid welding wires for G115 heat-resistant steel with the patent publication number CN106914712A, heat-resistant steel solid welding wires for 650 ℃ ultra-supercritical thermal power generating units with the patent publication number CN108127291A, TIG (tungsten inert gas) containing welding wires for steel for steam temperature ultra-supercritical thermal power generating units with the patent publication number CN106425157A, and a preparation method thereof. The argon arc welding wires disclosed in the patent documents adopt the same Cu-containing component design as that of G115 steel, so that A of a welding seam is causedC1The point is low, and the high-temperature tempering treatment temperature after welding is reduced. In order to avoid the formation of new austenite during the post-weld heat treatment, the post-weld heat treatment time has to be extended, which greatly reduces the production efficiency. CN108838579A patent publication No. Bright welding wire for ultra-supercritical coal-fired power station heat-resistant steelAlthough the welding wire does not contain Cu, the welding seam obtains higher impact toughness, but the content of C element is too high, the welding crack sensitivity is increased, and in addition, the content of W element is obviously lower than that of the base material, so that the high-temperature creep endurance strength is reduced. In addition, the above patent documents mostly adopt high B and low N composition design, limited by the welding metallurgy process, and these welding wires are difficult to obtain a high B and low N composition combined weld under the conventional GTAW welding process, which not only has great waste of B element, but also may increase the microscopic defect sensitivity of the weld, and is not favorable for the high temperature creep strength of the weld.
Disclosure of Invention
The invention aims to provide a welding wire for 9Cr-3W-3Co martensite heat-resistant steel and application thereof in a GTAW welding process, the content of alloy elements of the welding wire is reduced compared with that of the existing welding wire, and A of a welding seam is reducedC1The spot is improved, the formability is good, the defect sensitivity is low, the weld impact toughness is high, the high-temperature creep endurance strength is excellent, and 9Cr-3W-3Co martensite heat-resistant steel such as G115, P93 and the like can be welded under the conventional GTAW process.
In order to solve the technical problems, the invention provides the following technical scheme:
the welding wire for the 9Cr-3W-3Co martensite heat-resistant steel comprises the following chemical components in percentage by mass: c: 0.05 to 0.12%, Si: 0.50% or less, Mn: 1.0% or less, P: 0.01% or less, S: 0.008% or less, Ni: 0.20% or less, Cr: 8.50-9.50%, W: 2.50-3.0%, Co: 2.50-3.50%, Nb: 0.03-0.07%, V: 0.15-0.25%, N: 0.03 to 0.07%, B: 0.004% or less, Cu: 0.10% or less, Ti: 0.01% or less, Al: less than 0.03%, and the balance Fe and inevitable impurities.
Further, the content of C in the welding wire is as follows: 0.06-0.10%.
Further, the content of Si in the welding wire is as follows: 0.15 to 0.35 percent.
Further, the content of Mn in the welding wire is as follows: 0.40 to 1.0%.
Further, Ni in the welding wire is less than 0.10%.
Further, the content of N in the welding wire is as follows: 0.03 to 0.06 percent.
Further, the content of B in the welding wire is as follows: 0.001 to 0.003%.
Further, the content of Al in the welding wire is as follows: less than 0.015%.
The application of the welding wire for the 9Cr-3W-3Co martensite heat-resistant steel in the GTAW welding process is provided.
Further, the GTAW welding process of the welding wire is a manual GTAW process or a hot wire automatic GTAW process, wherein:
the manual GTAW process conditions are as follows: the diameter of a welding wire is 2.4mm, the preheating temperature is 150-; postweld heat treatment process: 760 and 780 ℃ heat preservation time is 1.5-4 h;
the hot wire automatic GTAW process conditions are as follows: the diameter of the welding wire is 1.0mm, the preheating temperature is 150-; postweld heat treatment process: keeping the temperature for 1.5-4h at 760-780 ℃.
The reasons for the action of each element and the range thereof of the steel according to the present invention will be explained below. Unless otherwise specified,% of chemical composition means mass%.
C：0.05～0.12％
C forms carbide in the weld and improves creep strength. The C content is too low, the carbide content is reduced, and the creep strength is not improved. However, the C content is too high, which obviously increases the crack sensitivity of the welding seam, so the C content of the invention is controlled within the range of 0.05-0.12%. Preferably 0.06-0.10%.
Si: less than 0.50%
Si is an important deoxidizer, and the proper Si content is favorable for improving the toughness of weld metal, improving the weld forming and improving the oxidation resistance of the weld. However, too much addition results in creep embrittlement and a reduction in toughness. The Si content of the invention is controlled to be less than 0.50%, preferably 0.15-0.35%.
Mn: 1.0% or less
Mn is an austenite stabilizing element, is beneficial to inhibiting the formation of delta-ferrite, has the deoxidizing and desulfurizing effects and can improve the strength and the toughness of a welding seam. However, the Mn content is too high, and A of the weld is reducedC1And spot, causing the weld to reform austenite at the post-weld heat treatment temperature. Therefore, the Mn content is at most 1.0%. In order to ensure the deoxidation effect, the preferable range is 0.40 to 1.0%.
P: less than 0.01%
P is an unavoidable impurity element in the weld which increases the crack tendency of the weld and reduces the creep rupture ductility of the weld. Therefore, the P content is controlled within 0.01 percent.
S: less than 0.008%
S is an inevitable impurity element in the weld which increases the crack tendency of the weld and reduces the creep rupture ductility of the weld. Therefore, the S content is controlled within 0.008 percent.
Ni: less than 0.20%
Ni is an austenite forming element, and is advantageous for inhibiting the formation of delta-ferrite and improving the impact toughness of the weld. However, Ni extraction significantly reduced AC1This results in weld re-forming austenite at the post-weld heat treatment temperature, which in turn reduces impact toughness and is detrimental to high temperature creep strength. The Ni content of the invention is controlled below 0.20 percent, even below 0.10 percent.
Cr：8.50～9.50％
Cr is the most important element to ensure resistance to steam oxidation and hot corrosion. The steam corrosion resistance of the weld is better as the Cr content is increased. However, Cr is a ferrite-forming element, and if the content thereof is too high, δ -ferrite is generated in the weld, and the impact toughness and creep strength of the weld are reduced. Therefore, the Cr content of the invention is controlled to be 8.50-9.50%.
W：2.50～3.0％
W is the most important strengthening element, and on one hand, the creep strength is improved in the welding seam through solid solution strengthening, and on the other hand, the creep strength can be improved by forming a precipitation phase or improving the stability of other precipitation phases. However, if the content is too high, the formation of δ -ferrite is promoted, the tendency to age embrittlement increases, and the impact toughness of the weld is lowered. Therefore, the W content of the invention is controlled to be 2.50-3.0%.
Co：2.50～3.50％
The main function of Co is to inhibit the formation of delta-ferrite and improve the impact toughness of the weld. In addition, Co contributes to improvement of high-temperature creep rupture strength. Considering that Co is a noble metal element, the Co is controlled to be 2.50-3.50%.
Nb：0.03～0.07％
Nb is an important precipitation strengthening element, and forms a dispersed MX-type precipitate with C, N and the like, which is very stable at high temperature and improves the high-temperature creep strength of the weld. When the content is less than 0.02%, the amount of precipitates is small and a sufficient strengthening effect cannot be obtained. However, if the Nb content is too high, the impact toughness of the weld is reduced. Therefore, the content of Nb is controlled to be 0.03-0.07 percent.
V：0.15～0.25％
V is an important precipitation strengthening element, and forms MX type second phase precipitates which are dispersed with C, N, particularly VN with a remarkable strengthening effect, so that the high-temperature creep strength of the welding seam is obviously improved. However, the V content is too high, which promotes the formation of delta-ferrite. Therefore, the content of V is controlled to be 0.15-0.25%.
N：0.03～0.07％
N is a strong austenite forming element and can suppress the formation of delta-ferrite. In addition, the high-temperature creep strength of the weld joint is obviously improved by forming a dispersed MX-type precipitate with Nb and V. Therefore, the content of N is controlled to be 0.03-0.07%, preferably 0.03-0.06%.
B: less than 0.004%
B is a grain boundary strengthening element and can improve the high-temperature creep strength of a welding seam, but B is easy to burn in the welding process. In addition, too high a B content increases the crack sensitivity of the weld. Therefore, the content of B is controlled within 0.004%, preferably 0.001-0.003%.
Cu: less than 0.10%
Although Cu has the functions of inhibiting ferrite formation and strengthening certain precipitates, the Cu obviously reduces the Ac1 point, so that the weld joint is reformed into austenite at the postweld heat treatment temperature, and the impact toughness of the weld joint is reduced. Therefore, the Cu content of the present invention is controlled to 0.10% or less.
Ti: less than 0.01%
Ti is a very strong carbonitride forming element, affects the combination of Nb, V and C, N, and simultaneously forms primary TiN, which is not beneficial to playing the role of precipitation strengthening. Therefore, the Ti content in the present invention is controlled to 0.01% or less.
Al: less than 0.03%
Al is added as a deoxidizer in the welding material, so that the content of residual Al in the welding line is too high, and the lasting plasticity of the welding line is reduced. In addition, Al is easy to be preferentially combined with N, so that the N dissolved in the welding seam is approximately zero, the precipitation strengthening effect cannot be formed, and the high-temperature creep strength of the welding seam is reduced. Therefore, the Al content of the present invention is controlled to 0.03% or less, preferably 0.015% or less.
The welding wire of the invention welds the joint structure characteristics and the mechanical properties of 9Cr-3W-3Co martensite heat-resistant steel by a GTAW welding process:
(1) the weld is a tempered martensite structure without delta-ferrite.
(2) Weld AC1The point is more than or equal to 800 ℃.
(3) Under the condition of 760 multiplied by 1.5h postweld heat treatment, the 20 ℃ impact energy KV of the welding line2Not less than 80J; under the condition of 770 multiplied by 1.5h postweld heat treatment, the 20 ℃ impact energy KV of the welding line2≥150J。
(4) Room temperature tensile strength R of jointm≥700MPa。
(5) The joint is at 650 ℃/104The creep rupture strength under h is synchronously improved by more than 20-50% compared with the T/P92 steel joint.
Compared with the prior art, the invention has the following advantages:
1. the invention obtains the welding wire suitable for welding 9Cr-3W-3Co martensite heat-resistant steel by adjusting and optimizing the contents of Cu, Ni, B, N and other elements and strictly controlling the contents of Al, Ti and other impurity elements, wherein the contents of Cu and Ni are controlled at a low level, so that the welding seam is improvedAC1The welding material cost is reduced; the N content is properly increased, so that the smelting difficulty of the welding wire is reduced, the high-temperature creep resistance of the welding line is improved, and the high-temperature creep endurance strength of the joint is synchronously and obviously improved compared with that of a T/P92 steel joint.
2. The content of alloy elements of the welding wire is reduced compared with the existing welding wire, and the A of a welding lineC1The point is improved, the formability is good, the defect sensitivity is low, the post-welding heat treatment process window is wide, the impact toughness of a welding seam is high, the high-temperature creep endurance strength of the welded 9Cr-3W-3Co steel joint is synchronously improved by 20-50% compared with that of a T/P92 steel joint, the cost is low, and 9Cr-3W-3Co martensite heat-resistant steel such as G115 and P93 can be welded under the conventional GTAW process.
Drawings
FIG. 1 is a photomicrograph of a weld joint made with the wire of example 1 of the present invention.
FIG. 2 shows the microstructure of a weld of a welding head of a welding wire according to example 1 of the present invention.
FIG. 3 is a permanent strength curve of a welding joint of the welding wire of example 1 of the present invention.
Detailed Description
The technical scheme of the invention is further described in detail by the following embodiments and the accompanying drawings:
according to the component range of the welding wire, a plurality of groups of examples are carried out on the welding wire, comparative examples are given, and the specific chemical components and the mass percentage of each component of the examples and the comparative examples are shown in the table 1.
TABLE 1 chemical composition (wt%) of welding wire of examples 1-3 and comparative examples 1-2
A deposited metal phase change point test sample of the welding wire is prepared by overlaying by a hot wire automatic GTAW method, and the process conditions are as follows: diameter of welding wire 1.0mm, preheating temperature150 ℃, the interlayer temperature is 150-. Testing of weld metals by thermal expansion method AC1The results are shown in Table 2. As can be seen, the A weld beads obtained by the welding wires of examples 1 to 3 by controlling the Cu and Ni contents at low levelsC1The dots are significantly improved compared to comparative example 2.
TABLE 2 phase Change Point of weld obtained by welding wires of examples 1-3 and comparative example 2
| Point of transformation | Example 1 | Example 2 | Example 3 | Comparative example 2 |
| AC1/℃ | 804 | 808 | 806 | 778 |
Welding wires (the diameter is 2.4mm) of examples 1-3 and comparative example 1 are used for respectively welding G115 small-caliber pipes with the specification of phi 45 multiplied by 8mm, the welding position is vertically fixed (2G), the welding method is a manual GTAW process, the groove is V-shaped, the angle is 70 degrees, and the welding process parameters are shown in a table 3.
TABLE 3 Manual GTAW welding Process parameters for examples 1-3 welding wire
After welding, the steel plate is kept warm and slowly cooled to room temperature, and then high-temperature tempering heat treatment is carried out at 760 ℃ for 1.5h, or 760 ℃ for 4h, or 770 ℃ for 1.5 h.
FIG. 1 is a photomicrograph of the weld joint of the wire of example 1 showing: the welding wire of the embodiment 1 has good welding seam forming and no defects such as cracks, air holes, inclusions and the like under the conventional GTAW welding process, which shows that the welding wire has low defect sensitivity.
FIG. 2 is a microstructure of a weld of a welding head of the welding wire of example 1, showing: the weld of the welding wire of the embodiment 1 under the conventional GTAW process is a tempered lath martensite structure, and delta-ferrite does not appear.
The room temperature tensile and flexural properties of the joints of the wires of examples 1-3 were evaluated according to the DL/T868 weld procedure and are shown in Table 4. It can be seen that the room temperature tensile and bending properties of the joint both meet the requirements.
TABLE 4 Normal temperature tensile and flexural Properties of joints of welding wires of examples 1 to 3
Note: the postweld heat treatment conditions are 760 ℃ multiplied by 1.5 h.
The weld joints of the example 1 and comparative example 1 wires were subjected to room temperature impact testing, and the results are shown in Table 5. It can be seen that the impact energy of the weld of the example is significantly higher than that of the weld of the comparative example 1 at 760 ℃ for 4 h. In addition, the impact work of the weld of example 1 at 780 ℃ for 0.5h exceeded 180J, indicating that example 1 is due to the increase in AC1The welding line with excellent impact toughness can be obtained at a higher heat treatment temperature and in a shorter heat treatment time, and the production efficiency is improved.
TABLE 5 room temperature impact properties of the weld joint portions of the welding wires of example 1 and comparative example 1
Note: 1) the size of an impact sample is 5 multiplied by 10 multiplied by 55mm, and the test data is converted into the value of 10 multiplied by 55mm of a standard sample;
2) the values in parentheses are mean values.
The weld joint to which the wire of example 1 was welded was subjected to a 650 ℃ creep rupture strength test and the results are shown in Table 6. It can be seen that the fracture site is at the base material under high stress conditions, and the fracture site is transferred from the base material to the HAZ under low stress conditions. This indicates that neither in the high stress or low stress regions the joint failure location is in the weld. FIG. 3 is a graph showing the endurance strength of a joint welded by the welding wire of example 1, in which it can be seen that the weld wire of the present invention is used to weld a joint of G115 steel having an extrapolation of 650 ℃/10 in comparison with base materials of both G115 steel and T/P92 steel4The h endurance strength is synchronously improved by about 50 percent compared with the T/P92 steel joint, which shows that the creep endurance strength of the welding seam obtained by the welding wire is equivalent to that of the base metal.
TABLE 6 high temperature creep rupture strength test results at 650 ℃ for joints obtained with the example 1 welding wire
According to the invention, the contents of Cu, Ni, B, N and other elements are adjusted and optimized, and the contents of Al, Ti and other impurity elements are strictly controlled, so that the 9Cr-3W-3Co martensitic heat-resistant steel welding wire is obtained. The content of alloy elements of the welding wire is reduced compared with the existing welding wire, and A of GTAW welding lineC1The point is improved, the formability is good, the defect sensitivity is low, the post-welding heat treatment process window is wide, the impact toughness of the welding seam is high, and the high-temperature creep endurance strength of the welded 9Cr-3W-3Co steel joint is synchronously improved by 20-50% compared with that of a T/P92 steel joint.
It is apparent that the above embodiments are only examples for clearly illustrating and do not limit the embodiments. Other variations and modifications will be apparent to persons skilled in the art in light of the above description. And are neither required nor exhaustive of all embodiments. And obvious variations or modifications are therefore intended to be included within the scope of the invention as claimed.
Claims (9)
1. The 9Cr-3W-3Co martensite heat-resistant steel welding wire is characterized by comprising the following chemical components in percentage by mass: c: 0.05 to 0.12%, Si: 0.50% or less, Mn: 1.0% or less, P: 0.01% or less, S: 0.008% or less, Ni: 0.20% or less, Cr: 8.50-9.50%, W: 2.50-3.0%, Co: 2.50-3.50%, Nb: 0.03-0.07%, V: 0.15-0.25%, N: 0.03 to 0.07%, B: 0.0015-0.004%, Cu: 0.10% or less, Ti: 0.01% or less, Al: less than 0.03%, and the balance Fe and inevitable impurities.
2. The welding wire as defined in claim 1, wherein the C content in the welding wire is: 0.06-0.10%.
3. The welding wire of claim 1, wherein the Si content in the welding wire is: 0.15 to 0.35 percent.
4. The welding wire as defined in claim 1, wherein the Mn content in the welding wire is: 0.40 to 1.0%.
5. The welding wire of claim 1, wherein the Ni content in the welding wire is: less than 0.10%.
6. The welding wire as defined in claim 1, wherein the content of N in the welding wire is: 0.03 to 0.06 percent.
7. The welding wire as defined in claim 1, wherein the heat-resistant steel has an Al content of: less than 0.015%.
8. Use of a welding wire for 9Cr-3W-3Co martensitic heat resistant steel according to any one of claims 1 to 7 in a GTAW welding process.
9. The use of claim 8, wherein the GTAW welding process of the welding wire is a manual GTAW process or a hot wire automatic GTAW process, wherein:
the manual GTAW process conditions are as follows: the diameter of a welding wire is 2.4mm, the preheating temperature is 150-; postweld heat treatment process: 760 and 780 ℃ heat preservation time is 1.5-4 h;
the hot wire automatic GTAW process conditions are as follows: the diameter of the welding wire is 1.0mm, the preheating temperature is 150-; postweld heat treatment process: keeping the temperature for 1.5-4h at 760-780 ℃.
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| CN114161027B (en) * | 2022-01-07 | 2022-12-30 | 北京科技大学 | Welding wire for 630 ℃ ultra-supercritical G115 heat-resistant steel, preparation method and GTAW using method |
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| EP3037205B1 (en) * | 2014-12-25 | 2018-06-27 | Kabushiki Kaisha Kobe Seiko Sho (Kobe Steel, Ltd.) | Wire for gas shield arc welding |
| CN106425157A (en) * | 2016-10-28 | 2017-02-22 | 四川大西洋焊接材料股份有限公司 | TIG welding wire of steel for steam temperature ultra supercritical thermal power generating unit and preparation method thereof |
| CN106670738B (en) * | 2016-11-14 | 2019-08-02 | 上海锅炉厂有限公司 | The welding procedure of boiler tubing G115 steel |
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| CN109048119B (en) * | 2018-08-30 | 2022-02-11 | 天津重型装备工程研究有限公司 | Solid welding wire for 650 ℃ ultra-supercritical thermal power turbine steel casting |
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