JPS5820720B2 - welding wire - Google Patents

Description

DETAILED DESCRIPTION OF THE INVENTION The present invention relates to a structure having a bath contact portion that is resistant to neutron-induced property changes,
Relates to nuclear reactor pressure vessels in which the weld metal of the weld zone exhibits resistance to neutron-induced property changes equal to or greater than that of the base metal.

In particular, the invention relates to a welding wire capable of providing such a weld.

It has been observed that steels of the type currently used as materials for nuclear reactor pressure vessels undergo changes in ductility after prolonged exposure to high-energy (>IMev) neutrons.

As a result, as the pressure vessel deteriorates, it can withstand less stress and requires lengthy equipment start-up and shutdown processes.

This type of long process is completely wasteful.

In some cases, the bath contact, and more particularly the weld metal, rather than the material, such as the steel plate, is the limiting factor in determining the stresses that the furnace can withstand and how many start-up and shut-down steps are required. .

Therefore, it would be advantageous to form a weld metal with a resistance to neutron induced changes equal to or greater than that of the pressure vessel material.

Changes in the toughness of metals are measured by a standard test called the Charpy Notch impact test.

A pendulum shock is applied to the metal sample to be tested, thereby destroying the sample.

The ductility of the samples is determined by the amount of energy absorbed from the pendulum and the non-ductility transition temperature for each sample, which is the temperature at which the shock pendulum absorbs a given energy (30 ft-6s).

This change in temperature due to radiation-induced effects is denoted as ΔNDTT.

It is preferred that the weld metal, when subjected to irradiation, have a ΔNDTT at least as low as the materials being joined by the weld metal.

Unfortunately, in order to observe the ΔNDTT of a material, it is not sufficient to provide a weldment with the same constituent proportions as the material.

Although steel sheets and steel weldments can have the same chemical composition, they are different materials with dissimilar mechanical properties due to differences in metallographic structure.

This phenomenon is similar to the well-known differences between snow and ice, or between diamonds, redwoods, and amorphous carbon.

That is, even if the constituent materials are the same, the structures and properties are different.

Current technology in this field involves special heat treatments of materials for reactor pressure vessels.

It produces a bainite metal composition structure and has special mechanical properties.

This heat treatment generally involves raising the temperature of the material to what is known as the austenitizing range (~1600°F), followed by water quenching.

The rapid cooling during quenching causes the formation of bainite within the material.

In this way, the desired mechanical properties are imparted by the heat treatment.

However, since a large structure is formed by welding the materials, it is not possible to heat treat the weld in the same way as above, since heating the entire structure is prevented.

Localized or regional heat treatment of weldments is carried out mostly to relieve internal stresses and is carried out at temperatures below the austenitizing range, thus preventing structural changes. .

Similar to heat treating materials, locally heat treating a weldment can create undesirable stresses within the structure.

Therefore, it is not common practice to simply select a welding alloy based on the alloy of the materials to be welded.

Generally, different chemical compositions of the weld metal are required to meet strength requirements.

In this respect, m-welding technology differs from basic steelmaking methods.

In view of the advantages of using weld metals that are at least as resistant to neutron radiation as the materials to be welded, over the past 15 years the composition of various welding alloys has been studied to form welding alloys that are resistant to neutron-induced changes. Many experiments have been conducted.

These studies have developed a number of alloys that have the required toughness at least as strong as the material metal.

However, although alloy development is progressing, the general effects of individual elements in alloys have not been studied (e.g., U-P otapovs and J
, R. Hawthorne [Effect of residual elements on the 550'F irradiation response of selected pressure vessel steels and weld metals, NRL Rev.] 6 8 0 3 +
Naval Research Laborato
ry+November 22, 1968) is completely inaccurate, especially regarding the effect of nickel (for example, J, R.

"New Nip Cr t M" by Hawthorne
o Resistance to Irradiation Brittleness of Steel Sheets, Forged Steels and Direct Metals” NRL Report 7573 t Naval Re
5earch Laboratory, September 13, 1973; “Pressure Vessel Technology” Part 3, ASME, 197
4, pp. 231-251).

According to current knowledge, a detailed theory of the relationship between composition and ΔNDTT has not been established, and therefore no predictions are made regarding the desired direct metal composition range.

An object of the present invention is a welding wire that provides a weld metal that exhibits sufficient resistance to neutron-induced changes so that it does not become a limiting factor in nuclear reactor operation.

The weld metal according to the present invention has the following composition at the time of welding (welding composition)
(wt%).

Carbon 0.18 or less Manganese
1.00~2.20 phosphorus
0.015 or less
0.02 or less Silicon 0.5
0 or less Nickel 1.20 or less ROM 2.50 or less Molybdenum 0.30 to 120 Copper
Vanadium below 0.10
0.05 or less iron The residual weld metal must satisfy the following conditions in its welded state.

^/fl≦04 Here, A is the sum of nickel and silicon (by weight) in the direct metal, and D is the sum of manganese, chromium, and molybdenum (by weight).

The features and advantages mentioned above can be appreciated from the accompanying drawings.

The aforementioned alloy composition ratios relate to the composition of the weld metal such that the change in non-ductile transition temperature (ΔNDTT) due to neutron irradiation is lower than or equal to the ΔNDTT of the material steel commonly used in the assembly of nuclear reactor pressure vessels.

Commonly used steel is ASMEA508 class 2. A3
02B and A333B.

When using HY80 (ASMEA543),
The desired effect is achieved with an alloy of the above composition.

The composition of the direct metal of the present invention is a value in a welded state.

As will be recognized by those skilled in the art, the composition of the weld metal at maturity is predicted from the composition of the direct wire and liquid-resistant flux used.

For example, in the submerged arc welding process, the flux shields the liquid-resistant weld metal from the atmosphere, and the welding direct metal produces chemical differences due to the interaction between the molten direct metal and the flux. has almost the same composition as the welding wire (electrode).

Therefore, for submerged arc direct, it is only necessary to adjust the melting of the direct wire according to the details given above.

In the hand arc welding process, a consumable vinegar electrode is used to coat the weld metal with a flux that protects and contains alloying constituents during welding.

The interaction of the flux with the metal electrode forms the desired welded direct alloy.

Therefore, for manual arc welding, and for electroslag direct, where chemical interaction between the molten flux and the metal occurs to produce a deposit-resistant direct alloy, the flux and direct metal are mixed during the welding process. The combination of the two must be tailored to produce an adhesion resistant welding alloy that meets the composition ranges and ratios A/B described herein.

Direct wire melts compatible with the present invention contain pond impurities, but in very small amounts.

This amount of impurities does not affect the fundamental and novel properties of the composition of the present invention.

Therefore, in the claims, "the remainder consists essentially of iron" means that it may contain components that do not substantially affect the basic and novel characteristics of the composition of the present invention, This indicates that commercially available iron can be used in terms of purity.

The significance of the conditions regarding the ratio A/B in the composition according to the present invention can be evaluated by referring to the description regarding the examination of each ratio shown below.

The ranges of each component according to the present invention are the result of research on previously published data regarding the relationship between composition and ΔNDTT.

First, the role of carbon in increasing susceptibility was speculated in the investigation.

Studies on the stability of vacancies in neutron-irradiated metals by Beeler and Beeler (J, R.
Beeler+Jr and M, F, Beeler
[Void Nuclei Attrition and Stabilization: Critical Nuclear Size] Effects of Radiation on the Substructure and Mechanical Properties of Metals and Alloys, ASTM 5TP529, 1973.
289-302), it is shown that carbon forms bonded complexes with vacancies in stereotransition metals.

The configurational energy of such complexes is low, which is very favorable in terms of energy for attachment of free carbon atoms or carbon atoms released from the precipitate by thermal action or neutron bombardment into the vacancies.

The theory behind the present invention is that the presence of these vacancy chains causes irradiation sulfidation and thus high NDTT shifts.

There is a variety of indirect evidence for carbon-vacancy complex hardening mechanisms.

Combustion Engineering/N
uclearRegulatoryComm 1ss
ion / Naval Re5earch Labo
Weld l (J
, R. Hawthorne et al. "Evaluation of commercially available A333-B temporary and post-deposit molds prepared to improve resistance to radiation causation" ASTM ST P 570;
American Society for Test
ing and Materials, Philadelphia, Pasateina, January 1976, Publication TLS-4.
(191), a large NDTT of 175°C was observed compared to the expected shift of 138°C based on copper content.

Before irradiation, this Weld.1 contained numerous carbides that could act as carbon sources for carbon-vacancy complex formation.

Additionally, Weld 1 had a high nickel content.

Sm1th shows that nickel enhances the thermodynamic activity of carbon in iron (R,P.

Sm1th Activity of carbon in iron-nickel alloy at 11000°C Trans, AIMFJ, 1960°2
18, pp. 62-64).

This increased carbon activity also increases the OT potential for vacancy-complex and precipitate formation.

Because the nickel content of weld l and H8STweld 50 is high, and because these factors appear to be directly responsible for the unusually high NDTT softness experienced by the metal, the activity of the carbon (yet an apparent effect of the nickel) may be affected. We evaluated the elements of the song that give the following.

In Sm1th, silicon increases the activity of carbon in iron, but
Manganese has been disclosed to reduce this (R,
P.

[Equilibrium of iron-carbon-silicon and iron-carbon-manganese alloys with methane-hydrogen mixtures at 1000°C,” Journal of the American Chemical Society.
rican Chemical Society)
, Vol. 70, 1948, pp. 2724-2729).

Molybdenum is known to counteract the effect of nickel on the tempering brittleness of steel.
EnergyApplication9a Pers
pectivej ClimaxMolybdenum
Company, = New York, pp. 20-21)
, is also known to inhibit hardening due to irradiation (N., Igata et al., “Role of Alloying Elements on Radiation Hardening in Steels for Pressure Vessels,” Radiation Effects on Basic Structures and Mechanical Properties of Metals and Alloys. Influence of ASTM 5TP529 y American
5ociety for Testing andMa
terials, 1973 + pp. 63-74).

Finally, chromium has been shown to reduce the effect of nickel on radiation sensitivity (L, E, S
teale “Effects of irradiation on reactor constituent materials J 1
August 1, 1973 - January 31, 1974, NRLMe
morandum Report 2752 + Na
valResearch Laboratory, Washington, March 1974, pp. 12 and 20).

Molybdenum and chromium are strong carbide formers;
It is also known that it tends to remove carbon from solid bodies.

Therefore, we decided to study the effects of the various elements mentioned above and divided them into two groups as follows.

A - Negative Effect B - Positive Effect (Anti-A) Nickel Silicon Manganese Molybten Chromate For liquid metal chemical data, sum the weight % values of the elements of group A and the weight % values of the elements of group B. The ratio was determined by dividing by the sum of .

Weld data were also divided into two groups according to copper content to take into account the known influence of copper on irradiation damage.

The correlation between the ratio A/B and the reported effects of NDTT shift and irradiation has been shown to influence the NDTT value.
This was done by normalizing to n/i, IMev.

This was accomplished by plotting the m-metallic NDTT shift theta against neutron action and drawing a straight line through the data representing the trend of INDTT shifted lamp neutron action.

Find the slope of the straight line that represents the trend and average it.

The average slope is 0.43.

Normalization point) 3. OXl 019n /cra, >
I Mev was chosen because much of the data is separated around this effect, so normalizing to this point would reduce potential errors.

The relevant expressions used for normalization are:

, (NDTTn-JNDTT i(,,' ”,)””
t where ΔNDTT = NDTT shift Φt = neutron action letter i - initial value letter n = normalized value The chemical data of the weld metal are shown in Tables 1 and 2 (
high copper content group and low copper content group, respectively).

Details of the heat treatment for the weld metals used are shown in Table 3.

Table 4 shows the data when the weld metal was irradiated, the ratio A/B and the normalized NDTT shift value.

These data are all representative of the known data for irradiation at 288° C. for weld metals available for research.

Data point names are the same as disclosed in the literature.

The numbers given as references in the table correspond to the list of references in Table 5.

Figure 1 shows normalized JNDTT vs. ratio A/B for weld metals in the high copper content group (>0.15 wt.
).

The line drawn in the data in Figure 1 is as the ratio A/B increases. This indicates that ΔNDTTn also increases.

Cheetah Boyne) is below the PS3 and 64 line.

This is due to both rapid cooling from strain relief annealing or short annealing (third
table).

Short-time annealing inhibits carbon diffusion within the weld metal.

The heavy loading nature of carbon diffusion will be discussed later, but it is related to the fact that carbon atoms must be present at specific lattice positions to prevent the formation of vacancy complexes.

CF48 shows the influence of long-term heat treatment on the shift of NDTT.

In addition to containing a high content of nickel and copper, C
The material designated F48 is heat treated for a total of 80 hours.

The trend curve for the ratio A/B can be drawn below CF48 because point) 3N5 (30 hour heat treatment) is considered to be more representative of the heat treatment given to weld metal.

In Fig. 1 (Cu>0.15), the effect of nickel-silicon cannot be ignored.

weld 2 is the lowest ratio A/B and lowest ΔNDTT
n.

Its copper content level is 0.20% by weight whereas points 49 and N44 have lower copper content (019 and 016% by weight respectively) but a higher shift is seen with the ratio A/B. .

Data point E, weld 50 sweld
l and w51 have various copper levels, and when plotted as a function of the ratio A/B, all four points lie close to the normalized shift around 166°C.

Copper level for point E and weld50 is 0
23 weight bearing, weld l is 036 weight bearing, and w51 is within the range of 0.15 to 0.33 weight bearing.

Although data point CF24 contains a lower amount of copper (0,24 weight factor) than weld l, it is observed that the shift also increases with increasing values of the ratio A/B.

Thus, the use of the ratio A/B fully explains the behavior of the weld metal upon irradiation that cannot be explained by copper content alone.

FIG. 2 shows data for low tone group weld metals with copper content below 0.15 dw.

Similar to Figure 1, there are also some data points that are not on the curve of Figure 2.

Most of these points represent weld metal with structures other than ferrite.

Cheetahboine (first used in research by Hawthorne + Fortner and Grant)
N23 (J, R.

Hawthorne “New Reactor Pressure Vessel Steel Receptacle Radiation Resistant Experimental Welding %JWeldingRe
search Supplement, 1970 1
S m1dt and S m1dt and S
reported by Prague (F, A.

Sm1dt, Jr. and J.A., Spragu.
e [Property changes due to impurity-defect interaction in iron and pressure vessel alloys J ASTM ST P 529
+ American Society for Te
Sting and Materials, 1973
.

78-91), and based on this information, the initial Hawth
Pond Acid Liquid Metal (Cheetaboine) N40. from the research of Orne Fortner and Grant. N39°N
41) was also estimated to have a structure other than ferrite.

The biggest exception in Figure 2 is Cheetah Boyne) B.

The weld metal at data point B contains nickel 24ON (J, R, Hawthorne [New Radiation Causal Resistance of Ni Cr Mo Steel Sheets, Forgings and Weldments J NRL Report 7573 r N
aval Research Laboratory+
Washington, September 1973).

When nickel is present in large amounts in the steel, it is an ausanite stabilizer that lowers the austenite to ferrite transformation temperature).

As a result, the structure of the weld metal at point B upon cooling includes ferrite as well as martensite, bainite, or both.

The detailed microstructure of data point B has not been reported.

Point) The difference between ponds in B is the annealing time and strain relief firing.

This is a method of cooling from scratch.

The weld metal with has a short annealing time (6.5 hours) and the strain relief annealing temperature is 31°C in 70 minutes from 613℃.
Fan cooled to 6°C.

Additionally, it inhibits carbon diffusion during strain relief annealing.

The effect of strain relief annealing treatment is data point CF
24. This is demonstrated by referring back to CF48 and 3N5 (FIG. 1).

These points also contained large amounts of nickel and could therefore have had a hybrid composition.

deer. However, the strain relief annealing time is considerably longer than that of B.

CF24 and CF48 are strain annealed for 65 hours, cooled, and then rolled again for 15 hours.

3N5 is annealed in 30 hours (Table 3).

The difference in annealing time is evidence of carbon diffusion effects on the sensitivity to irradiation.

The effect of nickel-silicon on sensitivity to radiation is also evident in FIG.

Data point) PS2 contains the least amount of copper (0.05wt) and has a normalized shift of 208.8°C.

This shift corresponds to point 5, which contains 0.14 weight fractions of copper.
2 and 53 have (ΔNDTTn2125°C
) is significantly higher than

However, the shift is proportional to the cheetah bond ratio A/B.

Point) The ratio A/B for PS2 is 1-07,
The ratio of points 52 and 53 is 0.63.

To demonstrate the separate but additive effects of copper and the ratio A/B on the NDTT shift, reference is made to FIG.

Figure 3 shows the weld metal (Δ
NDTT) versus (ratio A/B).

Cu≦0.05 0.05<Cu≦0.15 Cu>0.15 The curve as a function of the ratio A/B predicts the trend of ΔNDTT, but each trend curve is higher as the residual copper content is higher. It can be seen that the higher the shift value, the higher the shift value.

Thus, the effects of copper and the ratio A/B on the sensitivity of the weld metal to radiation are separate but additive.

Although we have described the relationship between the ratio A/B and ΔNDTT,
This relationship was also applied to the investigation of a range of direct metals whose ΔNDTT is equal to or less than that of pressure vessel steels.

Pressure vessel steels undergo changes in NDTT, which depend on their copper content.

Until recently, copper was treated as an impurity and no strict limits were placed on its amount.

At copper contents of 0.15% and above, the pressure vessel copper is approximately 144%
It has a ΔNDTT of °C.

005 to 0''5, ΔNDTT is about 106°C, and below 0.05%, ΔNDTT is about 78°C.

These ΔNDTT are all 3.0×1019 neutrons/
The effect of d is also remarkable.

Figure 3 shows carbon content below 0.15% and ratio A/
By setting B to 0.4 or less, ΔNDTT is equal to or lower than that of low copper content pressure vessel steel (3, OX 1
78°C) under the action of 0f' neutrons/-.

The composition ranges according to the invention are based on worst case assumptions.

Among the matters of the song is the long heat treatment.

In most cases, the bath weld metal is subjected to a post-weld heat treatment consisting of a short heat treatment at an annealing temperature, followed by a short cooling from this annealing temperature.
will have a lower NDTT shift than that predicted by the trend lines in Figure and Figure 2.

Exposure to this temperature for a short period of time inhibits carbon diffusion through the structure to the desired locations.

Beeler and Beeler, supra, point out that carbon-air complexes in alpha iron (ferrites) have carbon atoms located a finite distance from the vacancy along the <100> line.

In order for carbon atoms to reach these locations, diffusion of carbon through the structure must occur.

(This diffusion is time and temperature dependent).

Therefore, prolonged heat treatment and slow cooling rates after welding promote diffusion.

When irradiation takes place, the carbon atoms are in position to pierce the vacancies.

The activity of a carbon atom is influenced by its closest neighbors, such as silicon, nickel, manganese, etc.

High carbon activity by increasing nickel and silicon promotes radiation hardening and thus the formation of vacancy complexes resulting in high NDTT shifts.

The ferrite structure is the most susceptible to neutron induction, and the ferrite structure directly in the metal has a ratio of A/B.
Assuming that the nickel-silicon effect is applied only to ferritic structure weld metals.

The five data points in Figure 2 below the trend line (N23.N39.N40.N4L B) are direct metals whose structure is martensite, bainite, or a combination of these with ferrite. Related.

In either case, the data points have lower NDTT shifts than predicted by their respective ratios AIB.

Martensite has a body-centered tetragonal structure, and carbon atoms are incorporated into the structure by martensitic transformation.

The formation of bainite results from the nucleation of ferrite by rejected carbides.

The carbide structure formed in ferrite has a very fine grain size.

Before carbon-vacancy complexes are formed in bainite, carbon atoms must be extracted from the carbide by radiation bombardment, and carbon must diffuse into the ferrite.

The influence of structure on the sensitivity of the material to radiation is H
awthorne and 5teele (J, R, Hawthorne
Andori, E.

5teele [Initial Evaluation of Metallurgical Variables as Possible Factors Controlling Radiation Sensitivity of Structural Steel J NRL Report 6420 + Naval Re5earchLab
oratory, Washington, September 1966).

Research on materials HY80 and A35O-LF3.

In their research, they found that hardened and tempered structures, especially tempered martensite, have lower radiation sensitivity than transformation products at higher temperatures, such as ferrite.

For both materials used in this study (HY80 and .

A35O-LF3), the irradiation ΔNDTT is highest when the heat treatment produces equiaxed ferrite.

In addition to the conditions of the ratio A/B, the range of each component must also be in accordance with the above conditions.

The carbon must be maintained below 0.18 gw to minimize the amount of carbon present to suppress irradiation induced defects.

The low carbon content maximizes the ductility or notch strength of the weld joint.

To obtain the desired strength for directly deposited metal, the range of manganese is limited to 1-00 to 220 parts.

Manganese increases strength in ferrite and hardenability in steel alloys.

Furthermore, manganese is limited to a phosphorus content below 0.015 wt. which counteracts the effect that nickel and silicon have in promoting carbon vacancy filling.

This is because researchers have theorized that phosphorus may play a role in increasing the sensitivity of steel to damage caused by irradiation.

The sulfur content is limited to a maximum of 0.02 parts by weight to prevent too many manganese-sulfide inclusions from forming.

Such inclusions cause poor notch ductility, resulting in a high initial (before irradiation) NDTT value.

Nickel has good initial notch ductility (low initial NDTT), although it is detrimental to the sensitivity of the metal to direct irradiation.
value).

The range is limited to 1.20 weight factor or less to allow the user to match the notch ductility of the base material.

At the higher end of this nickel content range, the amounts of manganese, chromium, and molybdenum in the alloy are in the ratio A/
The value must be large enough to keep B below 0.4.

Chromium is a hardening element similar to manganese, although its tendency to form carbides is greater than manganese.

As a result, chromium tends to remove carbon atoms from the solid matrix (chromium carbide formation), thus preventing the carbon atoms from forming bond complexes with radiation-induced defects.

The range is limited to below 250 wt. weight to allow the user to vary the direct metal during adhesion to obtain the required hardness and strength properties.

The range of molybdenum is limited to 030 to L20 by weight so that the liquid resistant metal has the necessary hardness and strength properties when resistant to adhesion.

Molybdenum is a very strong carbide former and has the same effect as chromium in reducing the tendency of carbon to resist irradiation-induced defects.

Copper content is limited to less than 0.10 weight factor as the steel is known to cause high NDTT shifts in weld metals exposed to irradiation.

The low copper content minimizes the susceptibility of the weld metal to neutron induced damage.

Similarly, vanadium is used because researchers believe this element is detrimental to the weld metal's resistance to irradiation.
Limited to under 005 weight.

The ranges and ratios A/B of the various components described above are ΔNDTT comparable to conventionally used types of pressure vessel steel materials.
However, it is preferable to select a range from the above-mentioned ranges that is compatible with the strength and bonding properties suitable for the particular pressure vessel material.

For example, the following materials are preferably in the following composition range:

Composition of weld metal when welding ASMEA533B% plate (weight%) Carbon 0.10 or less Manganese
1.00~1.25 phosphorus
0.015 or less
0402 or less Silicon
0.20~0.30 nickel 0.
10 or less Molybdenum 0.40-060 Copper
Vanadium below 0.10 Iron below 0.05
Composition of weld metal (% by weight) when welding residual A308 class 2 forging material Carbon 0.10 or less Manganese
120~1.50 Phosphorus 0.015 or less Sulfur 002 or less Silicon 0.30~
040 Nickel 050~0.60 Rirom 0.45
~065 Molybdenum 030~045 Copper
Vanadium 0.10 or less Iron 005 or less Composition of weld metal when welding residual ASME543 steel plate (wt%) Carbon Manganese 0.08 or less
1.10~1.30 phosphorus
0015 or less
001 or less Silicon 030~0
,40 Nickel 0.65~080 Rim 1.90
~2.20 Molybdenum 0.90~1.
IO Copper 0.10 or less Vanadium 0.05 or less Iron
Remaining Table 5 (References) 1. J. R. Hawthorne et al. “Effects of anti-irradiation on nuclear reactor constituent materials J NRL Memorandum) 17
53Naval Research Laborato
ry, Washington, February 15, 1967 2, U-Potapovs+ J-R-Hawthor
ne [550℃ of selected pressure vessel steel and direct materials
Effect of residual elements on the irradiation response in JNRL
Report 6803 s Naval Research
Laboratory, Washington, November 1968
March 22, 3, L-E, Steele et al. [Effects of Irradiation on Reactor Constituent Materials J NRL Memo Report 1937° Naval Research Laboratory
, Washington, November 15, 1968 4, J., R-Hawthorne "Demonstration of Improved Radiation Embrittlement Resistance of A333-B Steel Through Control of Selected Residual Elements" Constituent Alloys for Nuclear Reactors Effects of Irradiation on ASTM 5TP484°America
n Society for Testing an
dMaterials+ 1970, pp. 96-127 5, J-R-Hawthorne et al.
33-8 Evaluation of steel sheets and adhesion-resistant metals prepared to improve radiation embrittlement resistance JASTM 5TP570
+ American 5ociety for T
estingand Materials1 Philadelphia, Pasateina, January 1976, Combust
ion Engineering Publication TLS-41
916, L, E, 5teele [Terification of steel for reactor pressure vessels by neutron irradiation
onalAtomic Energy Agency,
Technical report shop 163. 1975, pp. 117-119 7, J. R. Hawthorne “Thickness 12
Dynamic fracture and Charpy rate of inch A333-8 steel plate and yeast-welded metal after irradiation J Nuclear'Eng
ineeringandDesign 17. 197
L 116-l 3'0 page 8, J-R-Beeler, JrtM, F, Bee
ler [Void Nuclei Attrition and Stabilization: Critical Nuclear Size - Effect of Radiation on the Substructure and Mechanical Properties of Metals and Alloys ASTM 5TP529°Amer
ican Society for Testing
and Materials, 1973t 289-3
02 page 9, R-P-8mith [Activity of carbon in iron-nickel alloys at 1000°C J Trans 41
MEs1960, Vol, 218, pp. 62-64 10,
R-P-8mith "Methane-hydrogen mixture, iron-carbon-silicon alloy and iron-carbon-
Equilibrium with Manganese Alloys,” Journal of the American Chemical Society.
f the American Chemical So
ciety+Vo1.70.1948t 2724~2
729 pages) 11, [Application of molybdenum to atomic energy, its prospects J C1imax] V1o1ybdenum Co
mpany1 New York, pp. 20-21 12, N-I gata et al. “The role of various alloying elements on radiation-induced hardening in pressure vessel steels” Effect of radiation on the basic structure and mechanical properties of metals and alloys, ASTM 5TP529° American
Society for Testing and
Materials, 1973, pp. 63-74 13,
Edited by L, E-8teele, “Effects of Irradiation on Reactor Constituent Materials, August 1, 1973 – January 31, 1974 J NRL Memo Report 2752° Naval Re5
EARCH LABORATORY, WASHINGTON, 19
March 1974, pp. 12 and 20 14, J-R, Hawthorne et al. [New Radiation Resistance Experimental Welding Metal for Steel Tanks for Reactor Pressure Vessels.”
W liquid resistant ding Re5search Suppleme
nt, October 1970, pp. 453s-458s 15, F, A, Sm1dtt Jr+ J-A-8
prague “Characteristic changes due to impurity-deficiency interactions in iron and pressure vessel alloys JASTM 5TP5
29゜American 5ociety for T
esting and Materials, 1973
, pp. 78-91 16, J-R-Hawthorn
e “New Ni Cr M.

Radiation oxidation resistance of steel plates, forgings and welded products”NR
L Report 7573 s NavalResearch
, Washington, September 17, 1973, J-R, Haw.
thorne, L, E, 5teele [Initial Evaluation of Metallurgical Variables as Possible Factors Controlling the Radiation Sensitivity of Structural Steels J NRL Report 6420 INaval
Research Laboratory, Washington, September 18, 1966, L-E-8teele et al., “Effects of Irradiation on Reactor Constituent Materials,” Quarterly Revo-) August 1, 1966-1
0/31 J NRL Report 1731°Naval
Research Laboratory, Washington, November 19, 1966, T-R, Mager+ F-0, Thoma
s “Evaluation of Radiation Damage to Pressure Vessel Steel by Linear Elastic Fracture Device J WCAP-7328, West
inhouse E 1 electric corporation
ation, Bitz'9-g, Pasateina, 196
October 20, 9, T-R-Mager et al. “Rochester
Analysis of capsule V from gas and E 1etric
R-E, G 1nnaUnitA1 Reactor Pressure Vessel Radiation Monitoring Program J Westinghouse
Electric Corporation.

Pittsburgh, Pasadena, March 21, 1973, J.
-R-Hawthorne U °Potapov
a [Initial evaluation of the notch ductility behavior of A333 pressure vessel steel by neutron irradiation J NRL Report 67
-72 t Naval Research Labo
ratory, Washington, November 22, 1968, C.E-Childress rASTM
A-533fB Welding Metal and Heavy Sect
ional S steelT technology P
Thickness of logram10. Inch ASTM A-543
Assembly method and data about steel plates, documentary report 3” 0RNL-4313-3, Oak Rid
geNational Laboratory, Oak Ridge Tenet'-1 January 23, 1971, J-S-Perrin et al. [Point Beach Nuclear Reactor Plant Units] AI Pressure Vessel Monitoring Program,
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[Brief explanation of drawings]

Figure 1 is a graph of (ΔNDTT) versus (ratio A, /B) for a weld metal with a copper content of 0.1515% by weight;
Figure 3 shows a graph of (ΔNDTT) versus (ratio A/B) for a weld metal with a copper content of 0.15% by weight, and Figure 3 shows the respective effects of copper content and ratio A/H (ΔNDTT).
T) is a graph of 1 (ratio A/B).

Claims (1)

[Claims] I An m-welding wire used when welding steel materials subject to neutron bombardment selected from ASMEA 533B steel plate, ASMEA 508 class 2 forged steel, and ASMEA 543 steel plate by a submerged arc method, the welding wire comprising carbon 018 Weight under weight, manganese 1°00 to 2
．． 20% by weight phosphorus 0.015% by weight, sulfur 0.
02 weight range, silicon 0.50 weight range, nickel 1.20 weight range, chromium 2.50 weight range, molybdenum 0.30 to 1.20 weight range, copper 0.10 weight range The following is characterized by having a composition in which the weight of vanadium is 5 or less, the remainder is substantially iron, and the ratio of the total weight of nickel and silicon to the total weight of manganese, chromium, and molybdenum is 0.4 or less. and welding wire. 2 The ASMEA533B steel plate that is subjected to neutron bombardment is coated with a vinegar solution using the submerged arc method, and the liquid-resistant wire is made of carbon of 0.090% by weight, 1.130% by weight, 0.008% by weight, and 0.013% by weight. Irium 0
．． 250 weight weight class kkel 0.030 weight weight class rom 0
010 weight class, molybdenum 0.560 weight class 0.0
30% by weight, 0.010% by weight of vanadium, the remainder being substantially iron, and having a composition in which the ratio of the total weight of nickel and silicon to the total weight of manganese, chromium and molybdenum is 0.4 or less. A welding wire according to claim 1. 3 The liquid-resistant wire for applying vinegar solution to ASMEA508 class 2 forged steel subjected to neutron bombardment using the submerged arc method is carbon 0075 weight class gun 1.310 weight class gun 0.012 weight class 0.016 weight class Iron 0300 weight class, Nickel 0560 weight class, Chromium 0.
590 weight weight rib weight class 360 weight ratio, copper 0.05
, O weight class, vanadium 0.010 weight class etc. are substantially iron, and have a composition in which the ratio of the total weight of nickel and silicon to the total weight of manganese, chromium and molybdenum is 0.4 or less A liquid-resistant wire according to claim 1. 4 The welding wire for welding ASMEA543 steel plates subjected to neutron bombardment by the submerged arc method was made of carbon 0.070 wt.
, oos weight class, sulfur 0.006 weight class ion 0.
350 weight weight class Kkel 0.710 weight weight class ROM 20
50 weight class, molybdenum 0960 weight class, copper 0.050
Weight support, vanadium 0050 weight class, the balance consisting essentially of iron, and the ratio of the total weight of nickel and silicon to the total weight of manganese, chromium and molybdenum is 0
．． The welding wire according to claim 1, having a composition of 4 or less.