JP2012012636A - Titanium alloy excellent in intergranular corrosion resistance - Google Patents

Abstract

PROBLEM TO BE SOLVED: To provide a titanium alloy that may minimize the proceeding of intergranular corrosion even in specific environments where the intergranular corrosion may easily proceed.SOLUTION: The titanium alloy contains 0.35-0.55% of Ni, 0.01-0.02% of Pd, 0.02-0.04% of Ru, and 0.1-0.2% of Cr, respectively, and the balance is composed of titanium and inevitable impurities. In the titanium alloy, Ni-rich phases, each of which is a phase (other than a titanium α phase) locally containing Ni in a content of 10 times or more the average Ni content, are aligned along a rolling direction to form a row, and a plurality of the rows are aligned in parallel in a width direction.

Description

  The present invention relates to a titanium alloy having excellent corrosion resistance under a special environment, particularly excellent intergranular corrosion resistance.

  Titanium is known to exhibit excellent corrosion resistance in various chloride solutions including seawater and in oxidizing acids such as nitric acid. However, when exposed to high-temperature and high-concentration conditions in a non-oxidizing environment such as hydrochloric acid or sulfuric acid, the excellent corrosion resistance may not be exhibited.

  From the viewpoint of improving the corrosion resistance under the environment as described above, a Ti—Pd alloy (JIS H 4650 11-13, ASTM Gr. 7, Gr. 11) has been used conventionally.

  Recently, in order to make up for the disadvantage that the Ti—Pd alloy is expensive, a corrosion-resistant titanium alloy with a reduced content of Pd, which is an expensive platinum group element, less expensive Ru, Ni, Cr, etc. In addition, corrosion resistant titanium alloys in which a part of Pd is replaced with (hereinafter, these titanium alloys may be referred to as “low cost version corrosion resistant titanium alloys”) have been developed (for example, Patent Documents 1 to 3).

  Among the above-mentioned low price version corrosion resistant titanium alloys, JIS 14 type, 15 type (JIS H4650), ASTM Gr. 33, Gr. Ti-0.4Ni-0.015Pd-0.025Ru-0.14Cr alloy (nominal composition: hereinafter referred to as "Ti-Ni-Pd-Ru-Cr alloy") Is also known).

  It is also known that the mechanism of developing corrosion resistance in a new low-priced corrosion resistant titanium alloy (Ti-Ni-Pd-Ru-Cr alloy) is different from that of existing low-priced corrosion resistant titanium alloys (for example, non-patent literature). 1). That is, the new low cost version corrosion resistant titanium alloy contains Cr that was not contained in the existing low price version corrosion resistant titanium alloy. Then, in the initial state where the alloy is exposed to a corrosive environment, Cr elutes selectively, so that Pd and Ru, which are platinum group elements having a lower content than the existing low cost version corrosion resistant titanium alloys, are concentrated on the surface. Will do. As a result, even with a small amount of platinum group elements, excellent corrosion resistance is exhibited.

Japanese Patent Publication No. 4-57735 JP-A 61-127844 Japanese Patent Laid-Open No. 4-308051

“Iron and Steel”, vol. 80, no. 4 (1994), P353-358

  Ti—Ni—Pd—Ru—Cr alloys as described above are inexpensive and exhibit excellent corrosion resistance, and thus have been widely used in the chemical industry, seawater heat exchanger fields, and the like. It was. However, Ti-Ni-Pd-Ru-Cr alloys, such as those based on the assumption that Ti-Ni-Pd-Ru-Cr alloys are replaced every few years under certain special circumstances. In a severe environment that cannot be maintained, or in an environment where the anode current flows through the Ti-Ni-Pd-Ru-Cr alloy in parts attached around the electrode of the electrolysis tank, the corrosion mode is May exhibit intergranular corrosion.

  Corrosion-resistant titanium alloys are inherently excellent in intergranular corrosion resistance, and even when pure titanium is used, intergranular corrosion does not occur so much. There are things to do. This intergranular corrosion may cause rapid destruction of the apparatus with respect to general corrosion, which is a normal corrosion form, and is a corrosion form that is disliked by users. Therefore, the actual situation is that a Ti—Ni—Pd—Ru—Cr-based alloy capable of reducing the progress of intergranular corrosion as much as possible even in the above-described corrosive environment is desired.

  The present invention has been made paying attention to the circumstances as described above, and an object thereof is to provide a titanium alloy capable of reducing the progress as much as possible even in a special environment in which intergranular corrosion is likely to proceed. There is.

  The titanium alloy of the present invention capable of achieving the above object is Ni: 0.35 to 0.55% (meaning of mass%, the same applies hereinafter), Pd: 0.01 to 0.02%, Ru: 0.0. A titanium alloy containing 02 to 0.04%, Cr: 0.1 to 0.2%, with the balance being titanium and inevitable impurities, and locally containing Ni that is 10 times or more of the average Ni content When the phases (except for the titanium α phase) that are contained in the material are Ni-rich phases, the Ni-rich phases form a row that exists along the rolling direction, and a large number of rows are formed in the width direction. It has a gist in that.

The titanium alloy of the present invention has Ni: 0.35-0.55%, Pd: 0.01-0.02%, Ru: 0.02-0.04%, Cr: 0.1-0.2% Each of which is a titanium alloy consisting of titanium and unavoidable impurities, and a phase containing locally Ni that is 10 times or more of the average Ni content (excluding the titanium α-phase). This phase also has a gist in that the Ni-rich phase contains Ti ₂ Ni.

  Moreover, each titanium alloy of the said invention is obtained by performing the final annealing after rolling in the range of temperature: 600-725 degreeC.

According to the present invention, the final firing conditions after rolling of the Ti—Ni—Pd—Ru—Cr alloy are appropriately controlled, and (1) a row in which the Ni-rich phase in the titanium alloy exists along the rolling direction is provided. In addition, the structure is such that a large number of rows are formed in the width direction, or (2) the Ni-rich phase is mainly composed of Ti ₂ Ni. The titanium alloy can be excellent in intergranular corrosion resistance, and such a titanium alloy is extremely useful as a material for an apparatus or the like used in an environment where intergranular corrosion is likely to occur.

It is a drawing substitute photograph which shows the EPMA mapping result of Ni of the L direction cross-sectional structure in the titanium alloy which changed final annealing temperature. It is a drawing-substitution scanning micrograph showing the corrosion form of a titanium alloy with the final annealing temperature changed. It is a drawing-substitution scanning photomicrograph showing another example of the corrosion form of the titanium alloy with the final annealing temperature changed. It is a drawing substitute photograph which shows the EPMA mapping result of Ni and Cr of the L direction cross-sectional structure in the titanium alloy which changed the final annealing temperature variously. It is a drawing substitute photograph which shows the result of the secondary electron image (SEM image) and mapping of a test piece. It is a drawing substitute photograph which shows the example of the result observed with the transmission electron microscope (TEM) of the test piece.

  The Ti—Ni—Pd—Ru—Cr alloy used in the present invention is used as a raw material for various chemical industry equipment and heat exchangers, but its form is a hot rolled plate or a cold rolled plate. Will be applied. These rolled sheets are made into products after final annealing. The titanium annealing method may be vacuum annealing in the laboratory (vacuum atmosphere or annealing in an atmosphere replaced with Ar after evacuation → no pickling thereafter), but industrially emphasizes productivity. Therefore, continuous annealing and pickling are performed in an air atmosphere. And when implementing this final annealing, it is common that the temperature (final annealing temperature) is performed by comparatively high temperature about 750-800 degreeC from a viewpoint of obtaining the outstanding moldability.

  In order to improve the intergranular corrosion resistance in the Ti—Ni—Pd—Ru—Cr alloy, the present inventor has studied from various angles. As a result, it was ascertained that in the case where the final annealing was performed at a temperature in the range of 600 to 725 ° C., the structure of the titanium alloy showed a peculiar aspect.

That is, in a titanium alloy that has been subjected to final annealing in the above temperature range, a phase that locally contains Ni that is 10 times or more of the average Ni content (excluding the titanium α phase) is a Ni-rich phase. In this case, this Ni-rich phase forms (1) a structure in which Ni-rich phases exist along the rolling direction and a structure form in which a large number of these rows are arranged in the width direction, or (2) the Ni-rich phase It was found that the structure was such that it contained Ti ₂ Ni. And, in the titanium alloy having these microstructures, it has been found that excellent intergranular corrosion resistance can be exhibited even in a special corrosive environment where conventional intergranular corrosion has occurred. completed.

  Among the microstructure forms of the titanium alloy of the present invention, the Ni-rich phase forms a row in the rolling direction, and the structure shape in which this row is formed in a row in the width direction is a cross section in the rolling direction ( It can be confirmed by mapping with an EPMA (Electron Probe microanalyzer) of the L direction cross section.

Further, the “Ni-rich phase” is a phase that locally contains Ni that is 10 times or more of the average Ni content (excluding the titanium α phase), or contains Ti ₂ Ni. Such a structure can be confirmed by observation with a transmission electron microscope (TEM), analysis of the crystal structure by electron beam diffraction, or the like.

  FIG. 1 shows the EPMA mapping results of the L-direction cross-sectional structure of JIS type 14 cold rolled sheet (Ti-0.4Ni-0.015Pd-0.025Ru-0.14Cr alloy) with various final annealing temperatures. (For other conditions, see Examples below). In FIG. 1, the whitish portion indicates the presence of the Ni-rich phase. As is apparent from this result, it can be seen that when the final annealing temperatures are 650 ° C. and 725 ° C., a large number of Ni-rich phase rows are formed in the width direction.

  On the other hand, in the rolled sheet having a final annealing temperature of 750 ° C., there is a region in which the Ni-rich phases are slightly connected in a row, but in the case of a cold-rolled material having a final annealing temperature of 650 ° C. and 725 ° C. It turns out that there are not many. Moreover, in the case of a cold-rolled material having final annealing temperatures of 800 ° C. and 830 ° C., it can be seen that the Ni-rich phase array is almost broken.

  The titanium alloy of the present invention is manufactured with a final annealing temperature of 725 ° C. or lower, whereby the above-described microstructure is obtained and the intergranular corrosion resistance is improved, but the final annealing temperature is less than 600 ° C. Then, the intergranular corrosion resistance is good, but since the progress of recrystallization becomes insufficient and the minimum required formability cannot be obtained, the lower limit of the final annealing temperature is preferably 600 ° C. . Incidentally, the atmosphere at the time of this final annealing is usually an atmospheric atmosphere, but it is needless to say that it may be a vacuum atmosphere or an atmosphere substituted with Ar after evacuation.

  In the case of continuous annealing (and pickling) in an air atmosphere, the time for performing the final annealing (time to be exposed to the annealing temperature) is about 1 to 10 minutes. In the case of vacuum annealing, it takes about 1 to 8 hours to achieve uniform heating of the entire coil.

  The chemical component composition in the titanium alloy of the present invention basically follows the official standard values, and on the premise of such chemical component composition, the structure is controlled. The reason for setting the range is as follows.

[Ni: 0.35-0.55%]
Ni is a relatively inexpensive element compared to Pd. Even if the content of Pd is reduced by containing 0.35% or more, the corrosion resistance of titanium alloy (in a non-oxidizing environment and at a high temperature). -An element effective for imparting corrosion resistance in a high concentration atmosphere. However, when the content exceeds 0.55%, workability deteriorates. A preferable lower limit of the Ni content is 0.40% or more (more preferably 0.45% or more) from the viewpoint of corrosion resistance.

[Pd: 0.01 to 0.02%]
It is a noble metal element for improving the basic corrosion resistance of Pd titanium alloy, and is contained in a relatively small amount due to the synergistic effect of other elements. In order to exert such effects, it is necessary to contain 0.01% or more of Pd. However, if the Pd content becomes excessive and exceeds 0.02%, the material cost increases, which is not preferable. The preferable lower limit of the Pd content is 0.012% or more (more preferably 0.015% or more) from the viewpoint of corrosion resistance.

[Ru: 0.02-0.04%]
Ru, like Ni, is an element that is relatively inexpensive compared to Pd, and by containing 0.02% or more, even if the Pd content is reduced, the corrosion resistance of titanium alloys (in a non-oxidizing environment) And an element effective for imparting corrosion resistance in a high temperature / high concentration atmosphere. However, if the content exceeds 0.04%, the material cost increases, which is not preferable. The minimum with preferable Ru content is 0.025% or more (more preferably 0.03% or more) from a corrosion-resistant viewpoint.

[Cr: 0.1-0.2%]
Cr is an element that contributes to the improvement of the corrosion resistance and crevice corrosion resistance of the titanium alloy without adversely affecting the workability, and is an element that further improves the corrosion resistance of the titanium alloy in combination with the above elements. In order to exert such effects, Cr needs to be contained in an amount of 0.1% or more. However, if the content is excessive, the workability deteriorates, so it should be 0.2% or less. The minimum with preferable Cr content is 0.12% or more (more preferably 0.15% or more) from a viewpoint of corrosion resistance.

  In the titanium alloy of the present invention, other than the above components (remainder) is composed of titanium and inevitable impurities. The above “inevitable impurities” are impurity elements inevitably contained in the raw material sponge titanium, and typically include oxygen, iron, carbon, nitrogen, hydrogen, chromium, nickel, etc., and the manufacturing process. In addition, elements that may be incorporated into the product, such as hydrogen, are also included in the inevitable impurities.

  In order to adjust the strength level of the titanium alloy, the amount of oxygen, iron, nitrogen, carbon, chromium, nickel, etc. may be intentionally adjusted. Here, it is included in the range of inevitable impurities. The content ranges of these inevitable impurities are generally as follows. However, the titanium alloy of the present invention positively contains a predetermined amount of chromium (Cr) and nickel (Ni) among these impurities, and the content thereof also takes into account the following inevitable impurity amounts. Total amount.

Oxygen: 100 to 3000 ppm (meaning “mass ppm”, the same shall apply hereinafter)
Iron: 100-3000ppm Nitrogen: Maximum 500ppm
Carbon: Maximum 800ppm Hydrogen: Maximum 150ppm
Chromium: 10-300ppm
Nickel: 10-300ppm

  The reason why the intergranular corrosion resistance is improved by adopting the above-described structure in the titanium alloy of the present invention has not been fully clarified, but is the main additive element of this titanium alloy. It was considered that the coexistence of Ni and Cr had some influence on the intergranular corrosion resistance.

  It is known that the normal corrosion generation principle of titanium alloys is the following reaction. That is, on the free surface of titanium, the anodic reaction (reaction in which the metal is eluted) represented by the following formula (1) and the cathodic reaction represented by the following formula (2) (when dissolved oxygen is present, the reduction reaction of dissolved oxygen) In an acidic solution, a reduction reaction of hydrogen ions) occurs simultaneously (entire corrosion).

Ti → Ti ³⁺ + 3e ⁻ (1)
O ₂ + 2H ₂ O + 4e ⁻ → 4OH ⁻ (2)

On the other hand, even when there is a gap structure, the anode reaction and the cathode reaction occur simultaneously at the inside and outside of the gap at the beginning. However, since the dissolved oxygen or hydrogen ions are not easily supplied from outside the gap, There is a difference in oxidant concentration inside and outside. For this reason, an oxidant concentration cell is formed inside and outside the gap, and the anode reaction takes place inside the gap and the cathode reaction takes place outside the gap. In the gap, the H ⁺ concentration increases due to the anode reaction, and the pH decreases. Further, since an electrical neutral condition is satisfied with respect to H ⁺ , an anion such as Cl ⁻ migrates from outside the gap, resulting in a highly concentrated hydrochloric acid solution. This prevents the passive state from being maintained, leading to active dissolution, that is, crevice corrosion.

  As described above, the overall corrosion and crevice corrosion of titanium alloys involve anodic and cathodic reactions, but the corrosion principle of intergranular corrosion is that of intergranular segregation of impurities and alloy elements. Conceivable. In the titanium alloy of the present invention, it is presumed that the Ni-rich phase remains in the special form as described above by annealing at a relatively low temperature, and segregation to the grain boundary is prevented.

  EXAMPLES Hereinafter, the present invention will be described more specifically with reference to examples. However, the present invention is not limited by the following examples, but may be appropriately modified within a range that can meet the purpose described above and below. Of course, it is possible to implement them, and they are all included in the technical scope of the present invention.

[Example 1]
A commercially available Ti—Ni—Pd—Ru—Cr alloy, that is, a JIS 14 type cold-rolled annealed plate (Ti-0.4Ni-0.015Pd-0.025Ru-0.14Cr alloy) was used, and the reduction ratio was: Perform 40% cold rolling, thickness is 1.1mm, subdivide the plate into necessary amount, and simulate the continuous annealing / pickling process in the following atmospheric annealing (final annealing) → salt immersion → pickling treatment To prepare a corrosion test piece.

[Atmospheric annealing]
Temperature: 670 ° C, 700 ° C, 725 ° C, 750 ° C, 775 ° C, 800 ° C, 830 ° C
Salt immersion: immersion for 1 minute in a commercial titanium descaling salt heated to about 500 ° C. (trade name: manufactured by Nihon Parkerizing Co., Ltd .: “Colline DGS”) Pickling: about 0.1 mm in thickness with nitric hydrofluoric acid Pickling

  The obtained corrosion test piece was subjected to a corrosion test under the following conditions to investigate its corrosion resistance. This test condition simulates a harsh use environment in which the Ti—Ni—Pd—Ru—Cr alloy targeted in the present invention cannot maintain a passive state.

[Corrosion test conditions]
It was immersed in a boiling 10% aqueous hydrochloric acid solution for 24 hours, and the annual corrosion rate (mm / year) was calculated based on the area of the specimen before the test and the mass change before and after the test. The results (relationship between final annealing temperature and corrosion rate) are shown in Table 1 below.

  Moreover, the test piece surface after a test was observed with the scanning microscope (SEM), and the presence or absence of intergranular corrosion was also investigated. The corrosion forms are shown in FIGS. 2 and 3 (drawing substitute photos). 2 (a) has an annealing temperature of 670 ° C., FIG. 2 (b) has an annealing temperature of 700 ° C., FIG. 2 (c) has an annealing temperature of 725 ° C., and FIG. An annealing temperature is 750 ° C., FIG. 3B is an annealing temperature of 775 ° C., FIG. 3C is an annealing temperature of 800 ° C., FIG. 3D is an annealing temperature of 830 ° C., Respectively.

  From these results, it is clear that the corrosion rate does not change so much depending on the final annealing temperature, but there is a large change in the corrosion form. That is, in the case where the final annealing temperature is 725 ° C. or lower, the corrosion form is mainly proceeding to the overall corrosion [FIGS. 2 (a) to (c)], whereas the final annealing temperature is 750 ° C. or higher. Then it can be seen that intergranular corrosion is in progress. Therefore, it can be seen that by setting the final annealing temperature to 725 ° C. or lower, the progress of intergranular corrosion can be effectively prevented. In this example, the lower limit of the final annealing temperature was 670 ° C., but it was confirmed that no intergranular corrosion occurred even at a temperature lower than this temperature.

  FIG. 4 shows the result of EPMA mapping for Ni and Cr in the cross section (L direction cross section) of the test piece used in the corrosion test (Ni at an annealing temperature of 650 to 830 ° C.). (See also FIG. 1 for mapping). As is apparent from this result, in the titanium alloy containing Ni and Cr, Ni and Cr are distributed in a coexisting state. However, in the case where the annealing temperature is 750 ° C. or higher, Ni and Cr coexist. It can be seen that the state (Ni and Cr having the same distribution state) occurs remarkably. That is, this coexistence state was considered to have an adverse effect on intergranular corrosion.

[Example 2]
FIG. 5 (drawing substitute photograph) shows the secondary electron image (SEM image) and the mapping result of the corrosion test piece (having a final annealing temperature of 700 ° C.) produced in the same manner as in Example 1. The position of the white precipitation seen in the SEM image and the portion where the concentration of Ni, Cr, Fe is high are almost the same, and the concentration difference between the base material portion (α phase) and the precipitation portion is particularly clear with respect to Ni. It can be said that the precipitation part is a Ni-rich phase. On the other hand, it can be seen that Pd and Ru are distributed almost uniformly.

Accordingly, FIG. 6 (drawing substitute photograph) shows an example of a 14 μm square visual field in which the above-mentioned test piece was observed again with a transmission electron microscope (TEM). The precipitates of 0.2 μm or more in the TEM image are surrounded by circles (◯), and if this is spot spectroscopic analyzed in TEM, the Ni content can be measured. 6A shows a case where the Ni-rich phase is Ti ₂ Ni, and FIG. 6B shows a case where the Ni-rich phase is a β phase.

  In the example shown in FIG. 6, since the ingot used as a sample is 0.49% on the top side and 0.43% on the bottom side, the average Ni content of the base material is 0.46%. It was.

  And since the content of Ni is known from the spot analysis, it can be determined from the result whether or not the precipitate is a Ni-rich phase (in the present invention, the average Ni content of the base material is 10 times or more. “Ni-rich phase”). However, from the mapping result, it is estimated that most of the precipitates are Ni-rich phase.

Furthermore, an electron beam can be applied to each of the precipitates at this time, and the crystal structure of the precipitate can be analyzed by electron beam diffraction. As a result, it can be determined whether the precipitate is Ti ₂ Ni or β phase. . An example of the analysis result of the Ni-rich phase is also shown in FIG.

When the final annealing temperature (in the atmosphere) was variously changed for the above test piece (however, it was carried out at 650 ° C., 700 ° C., 725 ° C., 750 ° C., 800 ° C., 830 ° C.), the form of the precipitate (Ti ₂ Ni Or β phase). The results are shown in Table 2 below.

As apparent from the results, the final annealing temperature is 650 ° C., 700 ° C., at 725 ° C., although Ti ₂ Ni is detected, and the other 750 ° C., 800 ° C., 830 ° C. In the Ti ₂ Ni detection It can be seen that only the β phase is detected. Considering the results of Table 1 together, it can be seen that the intergranular corrosion can be suppressed when the Ni-rich phase contains Ti ₂ Ni.

Claims (3)

  Ni: 0.35-0.55% (meaning of mass%, the same applies hereinafter), Pd: 0.01-0.02%, Ru: 0.02-0.04%, Cr: 0.1-0. A titanium alloy containing 2% of each, the balance being titanium and inevitable impurities, and a phase locally containing Ni that is 10 times or more of the average Ni content (excluding the titanium α phase) When the Ni-rich phase is formed, the Ni-rich phase forms a row that exists along the rolling direction, and is excellent in intergranular corrosion resistance, characterized in that the row is formed in a row in the width direction. Titanium alloy. Ni: 0.35-0.55%, Pd: 0.01-0.02%, Ru: 0.02-0.04%, Cr: 0.1-0.2%, respectively, the balance being titanium And a titanium alloy composed of unavoidable impurities, wherein a phase locally containing Ni of 10 times or more of the average Ni content (excluding the titanium α phase) is a Ni-rich phase. A titanium alloy excellent in intergranular corrosion resistance, characterized in that the rich phase contains Ti ₂ Ni.   The titanium alloy according to claim 1 or 2, which is obtained by performing final annealing after rolling at a temperature in a range of 600 to 725 ° C.