JP3367831B2 - Welding material for high strength ferritic heat resistant steel - Google Patents

Description

Description: BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a heat generator such as a steam generator or a boiler used under high temperature and high pressure, and
The present invention relates to a welding material suitable for welding high-strength ferritic heat-resistant steel used in a high-temperature environment of not less than ° C. 2. Description of the Related Art Austenitic stainless steel, high Cr ferritic steel having a Cr content of 9 to 12%, and 2
-There are low Cr ferritic steel represented by 1 / 4Cr-1Mo steel, carbon steel, and the like (hereinafter, all content of alloy components means wt%), but these are used temperature, pressure, The selection is made according to the usage environment and the like and economics. Among them, high-strength low Cr ferritic steels have been actively researched and developed and put to practical use.
The use of high-strength low-Cr ferritic steel is expected to increase in the future because it is relatively inexpensive. However, the development of welding materials used for these high-strength low-Cr ferritic steels has been delayed, and from the viewpoint of cost reduction, welding materials with better workability are desired. [0003] Accordingly, the present invention provides a welding method in which the weld metal after welding has a high-temperature strength equal to or higher than that of existing high-strength ferritic heat-resistant steel, and the preheating or post-heating treatment can be omitted during welding. An object of the present invention is to provide a welding material for low Cr ferritic heat resistant steel having excellent metal toughness. SUMMARY OF THE INVENTION The present invention relates to a welding material to which a Re element, which has not been used as an additional element in the prior art, is added. S
i: 0.01 to 0.3%, Mn: 0.01 to 0.3%,
P: 0.002 to 0.025%, S: 0.001 to 0.
015%, Cr: 0.8 to 2.5%, Ni: 0.01 to
0.5%, Mo: 0.01 to 0.3%, V: 0.01 to
0.5%, W: 0.1 to 2%, Nb: 0.01 to 0.2
%, Re: 0.03 to 0.5%, Al: 0.003 to
0.05%, B: 0.0001 to 0.01%, N: 0.
003 to 0.03%, the balance being iron and inevitable impurities, and Mo / 3 + W / 2 + Re ≧ 0.5%
And C + Si / 30 + Mn / 20 + Ni / 60 + Cr /
20 + Mo / 15 + V / 10 + W / 7 + Re / 3 + 5x
An object of the present invention is to provide a welding material for a high-temperature strength ferritic heat-resistant steel, which satisfies the relationship of B ≦ 0.45%, which can omit a prognostic heat. The function of each component and the reason for selecting the content will be described below. DESCRIPTION OF THE PREFERRED EMBODIMENTS C combines with Cr, Fe, W, V, and Nb to form carbides and contributes to high-temperature strength, and itself stabilizes the structure as an austenite stabilizing element. . If it is less than 0.03%, the precipitation of carbides is insufficient and the creep rupture strength is low. If it exceeds 0.08%, the carbides are excessively precipitated and the weld metal is remarkably hardened to deteriorate the impact characteristics. In addition, since the welding workability also deteriorates in proportion to the amount of C added, the appropriate content of C is 0.03 to 0.3.
08%. [0006] Si acts as a deoxidizing agent, and if it exceeds 0.3%, toughness is remarkably reduced, and is harmful to strength.
The content of Si is set to 0.01 to 0.3%. [0007] Mn is effective for stabilizing the structure.
If it is less than 01%, a sufficient effect cannot be obtained, and if it exceeds 0.3%, the weld metal is hardened. Therefore, the content of Mn is 0.1.
01 to 0.3%. Both P and S are harmful elements for toughness and workability. Even if the amount of S is extremely small, P and S destabilize the grain boundaries and Cr ₂ O ₃ scale film, and cause reduction in strength and toughness. ,
Even within the above-mentioned allowable range, it is better to be as small as possible. As an inevitable content, P is 0.002 to 0.025.
% And S are set to 0.001 to 0.015%. [0009] Cr is an indispensable element from the viewpoint of the oxidation resistance and high-temperature corrosion resistance of heat-resistant steel. If its content is less than 0.8%, sufficient oxidation resistance and high-temperature corrosion resistance cannot be obtained. On the other hand, 2.
If it exceeds 5%, strength and toughness are rather impaired, which is disadvantageous from the viewpoint of economy. Therefore, the content of Cr is set to 0.8 to 2.5%. Ni is an austenite stabilizing element,
And it contributes to improvement in toughness, but if its content exceeds 0.5%, the high temperature creep strength is impaired. Also, in view of economy, large-scale addition is disadvantageous. Therefore, the content of Ni is 0.0
1% to 0.5%. V combines with C and N to form fine precipitates such as V (C, N). These precipitates greatly contribute to the improvement of the long-term creep strength at high temperatures. However, if the content is less than 0.01%, a sufficient effect cannot be obtained. If the content exceeds 0.5%, the creep strength and toughness are rather deteriorated. Therefore, the appropriate content of V is 0.01 to 0.5%. Mo is effective in improving the creep strength, but if it is less than 0.01%, a sufficient effect cannot be obtained.
%, The intermetallic compound is precipitated at a high temperature to lower the toughness, and also has no effect on the strength. Therefore, it was set to 0.01 to 0.3%. W is effective as a solid solution strengthening element and a fine carbide precipitation strengthening element in improving the creep strength. In particular, the addition of Mo in combination with Mo can further increase the creep strength. If it is less than 0.1%, there is no effect, and if it exceeds 2%, the steel is hardened and the workability of welding is impaired, so the content is made 0.1 to 2%. The addition of Re is a feature of the wire component of the present invention, and has been found to increase the creep strength in proportion to the amount added. This is due to solid solution strengthening, but what is important is that the creep strength further increases even when Mo and W having the same function are added simultaneously. Therefore, it is appropriate to set the content to 0.03 to 0.5% in consideration of economy. As for Mo, W and Re, Mo
/3+W/2+Re≧0.5%. This is because, as a result of investigating the high-temperature strength of weld metals of various chemical components, the strength has a close relationship with the amounts of Mo, W, and Re added, and as shown in the above formula, the same amount of added metal is used. In terms of the amount, Re was found to be three and two times as effective as Mo and W, respectively. Therefore,
In order to maintain high-temperature strength equal to or higher than that of the base material, the above formula is set to 0.1.
It should be 5% or more. Nb, like V, combines with N to form Nb (C,
N) to contribute to creep strength. Particularly at a relatively low temperature of 600 ° C. or lower, a remarkable strength improving effect is exhibited. Also,
There is also an effect of making the structure of the weld metal finer, and an appropriate amount is also effective in improving toughness. If it is less than 0.01%, the above effects cannot be obtained. If it exceeds 0.2%, undissolved Nb
C is increased and creep strength and toughness are impaired. Therefore, N
The b content is suitably from 0.01% to 0.2%. Al is indispensable as a deoxidizing element. When the content is 0.003% or less, there is no effect.
If it exceeds, the Al content is set to 0.003 to 0.05% because the creep strength is impaired. B has the effect of dispersing and stabilizing carbides by adding a very small amount. If it is less than 0.0001%, the effect is small, and if it exceeds 0.01%, processability is impaired. Therefore, the addition of B reduces the content to 0.0001 to 0.01%.
It is better to range. N is necessary for the formation of carbonitrides with V and Nb, and its effect is less than 0.003%. However, if the content exceeds 0.03%, the structure becomes finer and the nitride coarsens, impairing strength and toughness. Therefore, the content of N is set to 0.03% or less, and is set to 0.003 to 0.03%. For C, Cr, Mo, V, W, Re and B, C + Si / 30 + Mn / 20 + Ni / 6
0 + Cr / 20 + Mo / 15 + V / 10 + W / 7 + Re
/3+5×B≦0.45%. This is because, as long as the above formula is satisfied, even if the prognostic heat is omitted, no crack is generated in the weld metal, and it has been found that the welding workability is not adversely affected. If it exceeds 0.45%, cracks occur in the weld metal and workability deteriorates. Example: 20 mm 2.25Cr-0.1Mo with a thickness of 20 mm
-1.6W-V-Nb steel groove as shown in Fig. 1 (thickness t of welded material 1 = 20mm, groove angle θ = 20 °, root gap L = 20mm with backing material 2) And TIG welding was performed using a welding wire having a component composition shown in Table 1 and a wire diameter of 1.6 mm without performing preheating (welding at room temperature) under welding conditions shown in Table 2. At the time of the welding, the welding workability was evaluated. Post heat treatment (stress relief annealing) was omitted from the obtained weld metal, and a creep rupture test piece and a Charpy impact test piece were collected. The creep rupture test was conducted at a test temperature of 650 ° C. and a stress of 70 MPa and 10 MPa.
It was set to 0 MPa. Charpy impact test is 2mm at 0 ° C
An impact test was performed using a V-notch specimen. Table 3 shows the test results. [Table 1] [Table 2] [Table 3] The wires T1 to T9 all satisfied the requirements of the present invention, and the weld metal had a bainite single phase structure. The weld metal welded with the welding material of the present invention has a creep rupture property exceeding the strength of a recently developed high-strength ferritic steel, and also has an impact property of absorbing energy of 150 J or more and heat after preheating. It was confirmed that the welding material had both high strength and toughness even if omitted. In addition, the characteristics when the welding material of the present invention was applied under current general welding conditions were also equivalent to the case where the heat after preheating was omitted. The wires T10 to T19 show a comparative example. 1. Wire T10 is used for ordinary heat-resistant steel.
It is an example of a 25Cr-1Mo-based wire. It was a component outside the scope of the present invention, and without preheating, cracks were observed in the weld metal and the impact characteristics were low. T11-
T19 is also a component outside the scope of the present invention. T11 is M
o / 3 + W / 2 + Re = 0.30%, resulting in poor creep rupture characteristics and poor welding workability. T12, T14, T17, T18 and T1
No. 9 is excellent in creep rupture characteristics, but all are C + S
i / 30 + Mn / 20 + Ni / 60 + Cr / 20 + Mo
/15+V/10+W/7+Re/3+5xB>0.4
The content is 5%, and the generation of cracks and welding workability are poor, and cannot be put to practical use. T13, T15 and T16 have relatively good welding workability, but T13 and T16 have low creep rupture strength, and T15 has the worst impact characteristics. From the above, in the comparative example, the creep rupture characteristics,
It is understood that the welding material does not satisfy all of the impact characteristics and welding workability and cannot be used without heat after preheating. The welding material of the present invention is a conventional 2.25 Cr-
Compared with the welding wire for 1Mo steel, it has significantly increased creep strength at high temperatures, and has excellent properties such as toughness and workability. By using the welding material of the present invention when welding low Cr ferritic heat-resistant steel used for various power generation boilers, chemical pressure vessels, etc., the reliability of the welded joint can be significantly improved, and the heat after preheating can be improved. Can be omitted, and workability is improved.

BRIEF DESCRIPTION OF THE DRAWINGS FIG. 1 is a view showing a groove shape when welding is performed using the welding material of the present invention.

────────────────────────────────────────────────── ─── Continuation of the front page (56) References JP-A-10-6079 (JP, A) JP-A-10-1749 (JP, A) JP-A-9-59746 (JP, A) JP-A 9-59 118953 (JP, A) JP-A-6-306550 (JP, A) JP-A-7-303988 (JP, A) JP-A-5-269590 (JP, A) (58) Fields investigated (Int. ⁷ , DB name) B23K 35/30 C22C 38/00-38/60

Claims (1)

(57) [Claims 1] C: 0.03 to 0.08% by weight,
Si: 0.01 to 0.3%, Mn: 0.01 to 0.3
%, P: 0.002 to 0.025%, S: 0.001 to
0.015%, Cr: 0.8 to 2.5%, Ni: 0.0
1 to 0.5%, Mo: 0.01 to 0.3%, V: 0.0
1 to 0.5%, W: 0.1 to 2%, Nb: 0.01 to
0.2%, Re: 0.03-0.5%, Al: 0.00
3 to 0.05%, B: 0.0001 to 0.01%, N:
0.003 to 0.03%, the balance being iron and unavoidable impurities, and Mo / 3 + W / 2 + Re ≧ 0.
5% and C + Si / 30 + Mn / 20 + Ni / 60 + C
r / 20 + Mo / 15 + V / 10 + W / 7 + Re / 3 +
A welding material for a high-temperature-strength ferritic heat-resistant steel capable of omitting a prognosis heat, wherein the welding material satisfies a relationship of 5 × B ≦ 0.45%.