JPH0730423B2 - Energizing roll alloy for electric plating - Google Patents

Description

TECHNICAL FIELD The present invention relates to an alloy roll for electroplating having excellent corrosion wear resistance.

[Conventional technology]

The current-carrying roll used for electroplating such as continuous electrogalvanizing is, as shown in FIG. 5, a roll body (sleeve).
At both ends of (10), roll end (20,2
0) is fitted. The steel sheet to be plated comes into contact with the surface of the roll body (10), is held by a backup roll, and travels in the plating solution.

The body portion (10) of the current-carrying roll is corroded by the plating solution, which is a strongly acidic corrosive plate, under a current-carrying condition. The corrosion is not a simple corrosion but an electric corrosion having a correlation with the amount of electric current, and the amount of corrosion increases as the amount of electric current increases. Further, the roll body (10) is subjected to mechanical wear due to friction with the steel sheet to be plated which comes into contact with the surface of the roll body (10) and passes through the plating solution. The body portion of the current-carrying roll has a surface roughness (irregularities / scratches) due to corrosive wear in which the current-carrying corrosion and mechanical wear are superposed. The corrosive wear on the surface of the roll body is liable to be concentrated particularly on a portion of the steel sheet to be plated having a high current density and a portion of the backup roll having the highest contact surface pressure.

When the surface of the body of the current-carrying roll is roughened due to corrosion and wear, the flaws are transferred to the plated surface of the steel sheet to be plated, which causes deterioration of the plating quality. Therefore, it is necessary that the roll body has both resistance to electrical corrosion and resistance to mechanical wear and is resistant to corrosive wear. Conventionally, SUS316, which is an austenitic stainless steel, and "Hastelloy C" and "Hastelloy C-276", which are Ni-Cr-Mo Ni-based alloys, have been used as the body material.

[Problems to be solved by the invention]

In recent years, the electroplating conditions have been changed from the conventional 10 to 15KA to 40 to 50KA due to demands for plating quality and productivity improvement.
In addition, the plating solution used has a high acidity and a plating solution with a pH of 1 to 2 and a strong acidity is used.
The speed tends to increase to 200 m / min.

In response to the severer plating conditions, the current-carrying rolls using SUS 316 austenitic stainless steel as the roll body member are
The resistance to galvanic corrosion in the plating solution is insufficient, and the surface height is as low as Hs22, so the resistance to mechanical wear is also insufficient. On the other hand, "Hastelloy C" and "Hastelloy C-
The current-carrying roll, which has a roll body made of 276 ", has a low pH.
It has very good resistance to galvanic corrosion against galvanizing solution, and its surface height is relatively high at Hs25 to 28, but it cannot fully cope with the recent high-speed rolling conditions. In particular, there is a problem in wear resistance when it comes into contact with a hard plated steel sheet such as a high-strength steel sheet (Hs: 25 to 35).

For this reason, in the conventional energizing roll, the surface of the body portion is likely to become rough due to corrosion wear in a short period of time, and the body surface must be re-polished frequently (for example, in a cycle of 1 to 2 weeks).
A great deal of labor and cost are required for the roll replacement and the re-polishing process.

The present invention provides an electric current roll alloy having improved corrosion and wear resistance to solve the above problems.

[Means and Actions for Solving Problems]

The current-carrying roll alloy for electroplating of the present invention focuses on the thermal age hardening characteristics of the 50Cr-50Ni-based alloy, and by devising its component composition, it has a high hardness of Hs40 or higher and greatly increases the resistance to mechanical wear. , Has a high degree of galvanic corrosion resistance comparable to conventional "Hastelloy" materials.

The current-carrying roll alloy of the present invention has Cr: 40 to 55%, Mo: 2 to 10%, V: 2% or less, Fe: 10% or less, S:
i: 1% or less, Mn: 1% or less, N: 0.2% or less, C: 0.1% or less,
The balance consists essentially of Ni, and if desired, a portion of Ni may be
It has a chemical component composition substituted with one or more elements selected from 0.5 to 2% Nb, 0.5 to 3% Ta, 0.1 to 1% Ti, and 0.1 to 1% Al.

Current-carrying roll alloy of the present invention, due to its thermal age hardening characteristics, a high hardness of Hs40 or more is imparted, and against mechanical wear,
It exhibits much higher resistance than conventional "Hastelloy" alloys.
Also, its galvanic corrosion resistance is comparable to that of "Hastelloy" alloys. The combination of mechanical abrasion resistance and electro-corrosion resistance makes it possible to obtain a strong acidity of about pH 1, high current,
It exhibits highly stable corrosion and wear resistance under the plating conditions for high-speed rolling.

The reasons for limiting the components of the current-carrying roll alloy of the present invention are as follows.

Cr: 40 to 55% Cr is in the as-cast structure of the alloy of the present invention, in the γ-Ni matrix, in a state of being precipitated as an α-Cr phase, and when the aging heat treatment is applied, the α-Cr phase is further matrix It precipitates in and hardens the alloy. Fig. 1 shows the Cr content and aging heat treatment (however, 70
The relationship of hardness (Hs) of the alloy after 0 ° C x 50Hr) is shown. As shown in the figure, if the Cr content is less than 40%, the age hardening ability is insufficient, so the Cr content is set to 40% or more. Although the hardenability increases with the increase of Cr content, if it exceeds 55%, the brittleness of the alloy becomes remarkable, so 55% is made the upper limit.

Mo: 2-10% Mo exhibits a remarkable effect in improving the corrosion resistance of the 50Cr-50Ni thermal aged alloy. Fig. 2 shows the relationship between the amount of Mo added when 50Mo is added to the 50Cr-50Ni alloy and the corrosion resistance after thermal aging treatment (700 ° C x 50hr). The vertical axis of the figure represents the corrosion rate (g / m ² h) in the boiling 5% sulfuric acid corrosion test (immersion time: 24 hours).
As shown in the figure, by adding 2% or more of Mo,
It can be seen that the corrosion resistance is remarkably enhanced. However, if it is added in a large amount, an intermetallic compound such as NixMoy is generated and the alloy remarkably becomes brittle, so the upper limit is 10%.

V: 2% or less When the cooling rate after solidification in the casting process is slow (about 50 ° C./min or less), the alloy of the present invention is secondary from the α-Cr phase precipitated along macro grain boundaries. -Ni-Mo as a mechanical precipitation phase
The ternary or Cr-Ni-Mo-Nb quaternary α-type solid solution is easily formed. This α-type solid solution has an Hv of about 600, which is extremely hard and brittle, so the cooling rate is slow and the macrograin coarsened portion is
Intergranular cracking occurs due to tensile stress generated on the outer surface during the solidification process during casting or the subsequent heavy-duty mechanical processing.

V has the effect of suppressing the formation of the α-type solid solution. That is, when V is added, a refinement phenomenon of the α-Cr phase appears, and due to the phenomenon, α tends to precipitate along the grain boundaries.
-Cr phase coupling is blocked. As a result, 2 from the α-Cr phase
Generation of the α-type solid solution that is subsequently generated is suppressed. The effect of preventing grain boundary cracking by suppressing the precipitation of the α-type solid solution is V
It can be obtained by adding a trace amount of. The effect increases as the amount of addition increases, but the effect is almost saturated with the addition of 2%. Further, if added over that amount, precipitation of carbides such as VC and the resulting embrittlement occur, so the upper limit should be 2%. It is preferably 0.4 to 0.7%.

Fe: 10% or less Fe is not an element necessary for the alloy of the present invention, but up to 10% can be mixed. It is economically advantageous that a relatively large amount of mixed Fe is allowed. However, if the mixed amount becomes too large, the corrosion resistance deteriorates, and the σ phase (Fe-Cr) precipitates during the thermal aging treatment, which causes the deterioration of the material, so the upper limit is 10%.

Si: 1% or less Si is effective as a deoxidizer, but the addition amount is 1
% Is sufficient. On the other hand, if it exceeds 1%, the ductility and weldability after thermal aging are significantly deteriorated.

Mn: 1% or less Mn is also effective as a deoxidizing agent like Si, but the amount added for that purpose need not exceed 1%. Addition of more than 1% causes the formation of non-metallic inclusions such as MnS and the resulting reduction in ductility.

In the alloy of the present invention, if desired, a part of Ni may be Nb, Ta, Al, Ti.
It is substituted with one or more elements selected from

Nb: 0.5 to 2% Nb increases the ductility of the alloy by combining with C and N and fixing these elements. Since the presence of N greatly affects the ductility, fixing N as Nb has a great effect of improving the ductility of the thermal aging material. In addition, Nb combines with C existing in the crystal grain boundaries and stabilizes it, thereby showing an effect of preventing hot cracking during welding and suppressing deterioration of corrosion resistance of the weld heat affected zone. These effects are Nb
It is secured by adding 0.5% or more, but if it exceeds 2%, the effect is almost saturated. In addition, excessive nitride is generated and ductility deteriorates. Therefore, it is 0.5 to 2%.

Ta: 0.5-3% Ta has the same action as Nb, and by fixing C and N, the ductility and weldability of the alloy are enhanced. In order to obtain this effect, addition of at least 0.5% is required. However, it is not necessary to add more than 3%, and if more is added, ductility is impaired by the formation of nitrides, so the upper limit is 3%.

Ti: 0.1 to 1% Ti is a strong deoxidizing element, and its deoxidizing action has the effect of improving the ductility of the alloy. Therefore, the required amount of addition is 0.1% or more. However, if excessively added, the ductility rather deteriorates due to the formation of nitrides and carbides, so the upper limit is 1%.

Al: 0.1 to 1% Al is a strong deoxidizing element similar to Ti, and has the effect of improving the ductility of the alloy. For this purpose, it is necessary to add at least 0.1%, but if it is added excessively, an intermetallic compound such as Ni ₃ Al will be generated, which will adversely affect the ductility and the like, so the upper limit is 1%.

C: 0.1% or less C is an element harmful to the corrosion resistance, so it is desirable that the content be small. Particularly, in the alloy of the present invention, when the amount of C exceeds 0.1%, the additional elements such as V and Nb are easily precipitated as carbides, the effectiveness of these additional elements is diminished, and the ductility of the alloy is reduced. descend. Therefore, the C content is 0.1% or less.

N: 0.2% or less N is an unavoidable impurity mixed due to the N absorption phenomenon of Cr in the atmosphere in the alloy melting process. 0.2% of N mixed
If it exceeds 0.2%, the lamellar structure remarkably appears, and the ductility and weldability of the alloy deteriorate, so the upper limit is 0.2%.

Ni: The balance Ni is a basic component of the alloy of the present invention together with Cr.

Ni forms a dense passivation film on the alloy surface and suppresses the corrosion dissolution rate in the plating solution, which is a strongly acidic corrosive solution. It also complements the brittle nature of Cr and imparts good ductility.

FIG. 3 shows the relationship between the aging temperature of the alloy of the present invention and the hardness after aging (however: aging time: 50 hr), and FIG. 4 shows the relationship between the aging time of the alloy of the present invention and the hardness after aging (however, aging). (Temperature: 700 ℃)
Is shown. The composition of the sample material is Cr: 45.4%, Mo: 2.
7%, V: 0.6%, Si: 0.3%, Mn: 0.01%, Fe: 0.3%, C: 0.0
1%, N: 0.11%, balance: Ni. As shown in the figure, excellent thermal aging effect is achieved by aging temperature: 650-800 ℃, aging time: Approximately 30 hours or more, especially aging temperature: 7
It can be seen that the best result is obtained at around 00 ° C and aging time: about 50 hours or more.

When the body (sleeve) of the current-carrying roll is manufactured from the alloy of the present invention, the entire thickness of the body may be formed from the alloy of the present invention, but the wear resistance of the roll body and the galvanic corrosion resistance of the plating solution Since the property is a problem relating to the outer surface of the roll body, by applying the alloy of the present invention only to the surface layer portion and using other appropriate inexpensive material such as carbon steel for the inner layer portion, the structure shown in FIG. Surface layer (11) and inner layer (1
The sleeve (10) having a two-layer structure with 2) is preferable.

As an example of a process for producing an energizing roll having a sleeve having a two-layer structure as a roll body, a hollow cylindrical body to be the surface layer (11) of the sleeve is first centrifugally cast using the alloy of the present invention to After subjecting the cylindrical body to primary rough machining, thermal aging treatment is performed, and then secondary machining is performed. By shrink-fitting this into an inner layer member (12), which is a hollow cylinder made of another material separately provided, a sleeve (1
0) is obtained. The roll ends (20) (20) are shrink-fitted into the openings at both ends of the sleeve (10), and the body ends are pinned (30) or welded to reinforce the strength, thereby completing the intended energizing roll.

[Example] A thermal aging treatment material (700 ° C x 50Hr) of each match having the chemical composition shown in Table 1 was subjected to an electrical corrosion test, a mechanical wear test and a solidification cracking test, and is shown in the right column of the table. I got the result.

In the table, sample numbers (No.) 1 to 12 are invention examples, and No. 101 to 111 are comparative examples. Among the comparative examples, No. 101 is a “Hastelloy C” equivalent material, No. 102 is a SUS 316 stainless steel equivalent material (all using rolled plate materials), and Nos. 103 to 111 are alloys of the present invention. This is an example in which the content of any of the elements (underlined in the table) deviates from the definition of the present invention, although the composition is similar.

[I] Electrical Corrosion Test Simulating actual use conditions of an electrical roll, a test piece [area under test: 1 under test in a strongly acidic corrosion plate [23 g / H ₂ SO ₄ , liquid temperature 55 ° C.]
cm ² ] as the cathode, and a pulse current of 1 A is applied between the anode and the anode (Pt), and the corrosion weight loss of the test piece after 24 hours is measured.

[II] Abrasion test A rotating wheel [SGP 100A (carbon steel), rotation speed 40RPM] was used as a mating material, and a test piece [15 × 20 × 10, mm] was pressed against this with a load of 2 kg, and at the contact part Plating solution 〔23g / H ₂ SO ₄ ,
150 g / ZnSO ₄ .7H ₂ O, 100 g / Na ₂ SO ₄ ] is sprayed to make a wet environment, and the wear amount (mg) of the test piece after 7 days (168 Hr) has elapsed is measured.

[III] Solidification cracking test Preheat the surface of the metal plate to 150-200 ℃ and apply TI to the surface.
Remelting is caused by arc discharge by G welding machine. At this time, the arc current is controlled to a voltage of 15 to 17 v and a current of 130 to 140 A. After remelting for 10 seconds, the surface is covered with asbestos etc. and gradually cooled. After cooling, the surface is polished and the processed surface is inspected for color cracks. This test evaluates castability, and in the table, "○" in the "Castability" column indicates no cracking,
“X” indicates that there is a crack.

As shown in Table 1, the alloy of the present invention is more mechanical than the conventional materials "Hastelloy C" (No. 101) and SUS 316 (No. 102) under the condition of contact with a plating solution. Wear is extremely small. Regarding the corrosion resistance as well, it can be seen that the alloy of the present invention greatly surpasses the conventional SUS 316 material (No. 102) and has galvanic corrosion resistance comparable to "Hastelloy C" (No. 101).

On the other hand, Comparative Examples Nos. 103 to 111 have a composition similar to that of the alloy of the present invention, but lack any element or have an excess or deficiency in the content thereof, and therefore have resistance to galvanic corrosion or wear. Poor or poor castability. For example,
No. 103 with insufficient Cr content has low hardness and poor wear resistance. No. 104 containing excessive Cr has good electrical corrosion resistance and wear resistance, but lacks ductility, and therefore cracks occur during casting. No. 105, which does not contain Mo, has no problem in wear resistance and castability, but has significantly poor electrical corrosion resistance. On the other hand, if Mo is excessively included, the alloy becomes brittle, and as seen in No. 106, solidification cracking cannot be avoided. No. 107 is an example containing an excessive amount of Fe, and although the wear resistance is good, the ductility is poor, so solidification cracking occurs. In addition, the amount of galvanic corrosion tends to increase. No. 108, which contains an excessive amount of C, has good wear resistance, but has significant electrical corrosion and solidification cracking due to insufficient ductility. When Nb is excessively included (No. 10
9), when Ta is contained excessively (No.110) and when V is contained excessively (No.111), there is no problem in galvanic corrosion and wear resistance, but avoiding solidification cracking due to lack of ductility I can't.

[Effects of the Invention] Since the alloy of the present invention is excellent in electrical corrosion resistance and wear resistance against a strongly acidic corrosive liquid, the electrical current roll constituted by using the alloy of the present invention as the roll body member is under continuous electroplating operation. There is little corrosion and wear, and the occurrence of flaws and abrasions during surface polishing by grinding stone grinding to remove the plated metal adhering to the body surface is also slight, maintaining a smooth and beautiful surface property for a long time. Therefore, the frequency of roll replacement is reduced, the re-polishing cost of the roll is reduced, stable continuous plating operation can be maintained, and the effect of stabilizing and improving the quality of plated products can be obtained.

[Brief description of drawings]

Fig. 1 is a graph showing the relationship between Cr content and hardness, and Fig. 2 is
Graph showing the relationship between Mo content and corrosion rate, Fig. 3, Fig. 4
Figure is a graph showing the relationship between aging treatment conditions, post-aging and hardness,
FIG. 5 is a partially sectional front view showing an example of an energizing roll. 10: Roll body (sleeve), 20: Roll end.

Claims (2)

[Claims] 1. Cr: 40 to 55%, Mo: 2 to 10, V: 2% or less, Si: 1
% Or less, Mn: 1% or less, Fe: 10% or less, C: 0.1% or less, N: 0.
An electroplating roll alloy for electroplating with excellent corrosion and wear resistance consisting of 2% or less and the balance consisting essentially of Ni. 2. Cr: 40-55%, Mo: 2-10%, V: 2% or less, S
i: 1% or less, Mn: 1% or less, Fe: 10% or less, C: 0.1% or less,
N: 0.2% or less, Nb: 0.5-2%, Ta: 0.5-3%, Ti:
An electroplating roll alloy for electroplating, which has excellent corrosion resistance and wear resistance and is composed of one or more selected from 0.1 to 1% and Al: 0.1 to 1%, and the balance being substantially Ni.