TW202024346A - Titanium alloy wire rod and method for manufacturing titanium alloy wire rod - Google Patents

Abstract

A titanium alloy wire rod including an [alpha] phase and a [beta] phase, the metallographic structure in an outer circumferential region extending from the surface toward the center of gravity to a depth of 3% of the wire diameter being an isometric structure having [alpha] crystal grains in which the average crystal grain size thereof is 10.0 [mu]m or less in a cross section perpendicular to the longitudinal direction, and the metallographic structure in an internal region including the center of gravity and extending to a position at 20% of the wire diameter from the center of gravity to the surface being an acicular structure in a cross section perpendicular to the longitudinal direction.

Description

Titanium alloy wire and manufacturing method of titanium alloy wire

The invention relates to a titanium alloy wire and a method for manufacturing the titanium alloy wire.

Titanium is a lightweight and high-strength material that has excellent specific strength and excellent corrosion resistance. It is used in various applications such as aircraft, chemical plants, building exterior materials, decorations, and consumer goods. In particular, α+β type titanium alloys such as Ti-6Al-4V, Ti-6Al-6V-2Sn, Ti-6Al-2Sn-4Zr-2Mo, etc. have excellent mechanical properties such as specific strength, ductility, toughness, and heat resistance. Among the alloys, it continues to be frequently used.

In Patent Document 1, for the purpose of obtaining a titanium alloy with stable fatigue strength with little variation and high hot workability, an α+β type titanium alloy is proposed, which is composed of: 0.5% or more and less than 1.4 % Fe, 4.4% or more and less than 5.5% Al, and the remainder is titanium and impurities.

Prior art literature Patent literature Patent Document 1: Japanese Patent Application Publication No. 7-70676

Problems to be solved by the invention Ti-6Al-4V, Ti-5Al-1Fe and other high-strength titanium alloy wires used in aircraft fasteners (bolts, nuts, etc.) or automobile valves must have better fatigue strength and creep strength, and require more Further improve.

The present invention was made in view of the above problems. The object of the present invention is to provide a titanium alloy wire with excellent fatigue strength and creep strength, and a method for manufacturing titanium alloy wire that can be industrially and stably manufactured.

Means to solve the problem The inventors of the present invention have conducted incisive research to solve the above-mentioned problems, and as a result, they focused on the characteristics of the needle-like structure and the equiaxed structure of the titanium alloy wire and its location. Needle-like structure has excellent creep characteristics, while equiaxed structure has excellent fatigue characteristics. And found that a titanium alloy wire rod, by arranging the acicular structure and the equiaxed structure in a predetermined position, the fatigue strength and creep strength coexist at an excellent level at the same time. In addition, it has been discovered that the processing heat generated during the manufacture of a titanium alloy wire can be used as a method of arranging a predetermined acicular structure and an equiaxed structure, and further studies have been carried out. As a result, the present invention has been completed.

The gist of the present invention completed based on the above knowledge is as follows. [1] A titanium alloy wire containing α phase and β phase; The titanium alloy wire has the following chemical composition: In terms of mass %, Al: 0% or more and 7.0% or less, V: 0% or more and 6.0% or less, Mo: 0% or more and 7.0% or less, Cr: 0% or more and 7.0% or less, Zr: 0% or more and 5.0% or less, Sn: 0% or more and 3.0% or less, Si: 0% or more and 0.50% or less, Cu: 0% or more and 1.8% or less, Nb: 0% or more and 1.0% or less, Mn: 0% or more and 1.0% or less, Ni: 0% or more and 1.0% or less, S: 0% or more and 0.20% or less, REM: 0% or more and 0.20% or less, Fe: 0% or more and 2.10% or less, N: 0% or more and 0.050% or less, O: 0% or more and 0.250% or less, C: 0% or more and 0.100% or less and Remaining part: Ti and impurities, and The content of Al, Mo, V, Nb, Fe, Cr, Ni and Mn satisfies the following formula (1); In a cross section perpendicular to the length direction, in the outer peripheral region from the surface to the center of gravity to a depth of 3% of the wire diameter, the metal structure is an equiaxed structure with α grains with an average crystal grain size of 10 μm or less; and In the aforementioned cross section perpendicular to the longitudinal direction, the metal structure is a needle-like structure in the inner region including the center of gravity from the center of gravity to the surface to the position of 20% of the wire diameter. -4.00≦[Mo]+0.67[V]+0.28[Nb]+2.9[Fe]+1.6[Cr]+1.1[Ni]+1.6[Mn]-[Al]≦6.00　・・・(1) In addition, in the formula (1), the description of [element symbol] indicates the content (mass %) of the corresponding element symbol, and 0 is substituted for the element symbol that is not contained. [2] For example, the titanium alloy wire of [1], which contains in mass%: Al: 4.5% or more and 6.5% or less and Fe: 0.50% or more and 2.10% or less. [3] For example, the titanium alloy wire of [1], which contains in mass%: Al: 2.0% or more and 7.0% or less and V: 1.5% or more and 6.0% or less. [4] For example, the titanium alloy wire of [1], which contains in mass%: Al: 5.0% or more and 7.0% or less, Mo: 1.0% or more and 7.0% or less, Zr: 3.0% or more and 5.0% or less and Sn: 1.0% or more and 3.0% or less. [5] The titanium alloy wire rod of any one of [1] to [4], wherein in the cross section perpendicular to the length direction, the average aspect ratio of the α grains in the outer peripheral region is 1.0 or more and less than 3.0, The average aspect ratio of the alpha grains in the inner region is 5.0 or more. [6] For example, the titanium alloy wire rod of [5], wherein in the aforementioned cross section perpendicular to the length direction, the area of the region including the center of gravity with the average aspect ratio of the α grains of 5.0 or more is 40% or more relative to the cross-sectional area . [7] The titanium alloy wire rod of any one of [1] to [6], wherein the average crystal grain size of the α crystal grains in the outer peripheral region is 5.0 μm or less. [8] For example, the titanium alloy wire rod of any one of [1] to [7] has a wire diameter of 2.0 mm or more and 20.0 mm or less. [9] A method for manufacturing titanium alloy wire rod, which has the following steps: The step of heating the titanium alloy blank to a temperature above (β transformation point -200)°C; and The aforementioned titanium alloy is processed according to the total shrinkage rate of 90.0% or more, the average shrinkage rate of each pass in more than 1 pass from at least the final pass is 10.0% or more, and the wire drawing speed is 5.0m/sec or more. The steps of the blank. [10] For example, the titanium alloy wire manufacturing method of [9] further has a step of heat treatment in a temperature range above (β transformation point -300)°C and (β transformation point-50)°C.

Invention effect According to the present invention, it is possible to provide a titanium alloy wire rod with excellent fatigue strength and creep strength, and a method for manufacturing a titanium alloy wire rod capable of industrially and stably manufacturing a titanium alloy wire rod.

Hereinafter, the preferred embodiments of the present invention will be described in detail with reference to the drawings. ＜1. Titanium alloy wire＞ First, the titanium alloy wire of this embodiment will be described.

(1.1　Metal structure) First, the metallic structure of the titanium alloy wire of this embodiment will be explained. The titanium alloy wire of this embodiment is composed of an α+β type titanium alloy having the chemical composition described below, and has a two-phase structure at room temperature. The two-phase structure is mainly composed of the α phase and contains a small amount of β in the α phase. phase. Here, the "main body" of the α phase means that the area ratio of the α phase is 70% or more. The area ratio of β phase is about 2% to 30%. In addition, it is difficult to measure the area ratio of the β phase in the titanium alloy wire material of the respective embodiments of the present invention, and the allowable measurement error is ±5%. With regard to the titanium alloy wire rod of this embodiment, the metal structure has an average crystal grain size of 10 μm or less in the outer peripheral area from the surface to the center of gravity to the position of 3% of the wire diameter in a cross section perpendicular to the longitudinal direction. The equiaxed structure of the equiaxed α grains, and in the cross section perpendicular to the length direction, from the center of gravity to the surface to the position of 20% of the wire diameter, the metal structure has Needle-like structure of acicular α grains.

As shown in Figure 1, the equiaxed structure of the α+β titanium alloy is an aggregate structure of equiaxed α grains a, and there is a fine β phase in the grain boundaries between the α grains a and the grains. b. The acicular structure is a metallic structure of the α-phase formed by cooling the original β-phase titanium at a high temperature and growing from the grain boundary to the acicular shape. As shown in Figure 2, the needle-like structure of the α+β-type titanium alloy has the following structure: old β grains grow from the grain boundary position to needle-shaped needle-shaped α (indicated by symbol c in Figure 2) and needle-shaped β (Indicated by symbol e in FIG. 2) It is a layered structure. As mentioned above, the equiaxed structure and the needle-like structure can be distinguished by observing the metal structure.

The titanium alloy wire material of this embodiment has an excellent fatigue strength and creep strength by arranging the acicular structure and the equiaxed structure at a predetermined position. If specified, in titanium alloys, the needle-like structure has excellent creep characteristics and the equiaxed structure has excellent fatigue characteristics. However, the starting point of fatigue failure occurs near the surface (outer circumference) of the titanium alloy wire. Therefore, the inventors thought of disposing a fine equiaxed structure near the surface layer of the titanium alloy wire to increase fatigue strength, and disposing a needle-like structure with excellent creep strength near the center of gravity of the titanium alloy wire to ensure creep The strength is excellent enough.

In addition, the inventors of the present invention focused on the average aspect ratio and average crystal grain size of α grains in the outer peripheral region of the titanium alloy wire as an indicator of the fine equiaxed structure near the surface layer. Within the range, that is, a region in which a fine equiaxed structure is formed in the outer peripheral area (equiaxial structure area), the fatigue strength of the titanium alloy wire is improved. In addition, the inventors of the present invention focused on the average aspect ratio of α grains in the region including the center of gravity as an indicator of the acicular structure in the inner region including the center of gravity, and found that it becomes a certain value or more. , That is, because the area including the center of gravity is formed with needle-like structure (needle-like structure area), the creep strength of the titanium alloy wire is improved. Through the above, the creep strength and fatigue strength of the titanium alloy wire can be improved simultaneously.

In addition, the present inventors have also discovered that the titanium alloy wire material having the metal structure as described above can be manufactured by the method of manufacturing the titanium alloy wire material of the present embodiment which will be detailed later, and finally completed the present invention. Hereinafter, the metal structure of the titanium alloy wire rod of this embodiment will be specifically described.

Fig. 3 is an explanatory diagram schematically showing an example of the titanium alloy wire 1 of the present embodiment. In addition, the size of each area shown in the figure is appropriately enlarged and reduced for ease of explanation, instead of showing the actual size of each area.

In addition, the cross-sectional shape of the titanium alloy wire of the present invention can be any shape, and the following description assumes that the titanium alloy wire 1 of the present embodiment has a circular cross section in a cross section perpendicular to the longitudinal direction L. In addition, the cross section in the figure is a cross section perpendicular to the longitudinal direction L of the titanium alloy wire rod 1.

In this specification, as shown in FIG. 3, the outer peripheral area 2 is defined as the following area: in the cross section of the titanium alloy wire 1 perpendicular to the longitudinal direction L, from the outer peripheral surface 3 toward the center of gravity G to correspond to the wire diameter R The area up to 3% depth d. In addition, there may be cases where an oxide film or the like adheres to the outer peripheral surface 3 of the titanium alloy wire rod 1, and the thickness of such an adherent is not included in the outer peripheral surface that is the starting point for the measurement of the depth d of the outer peripheral region 2.

In addition, in this specification, as shown in FIG. 3, the inner region 4 is defined as the following region: in the cross section of the titanium alloy wire 1 perpendicular to the longitudinal direction L, from the center of gravity G to the outer peripheral surface 3 to the wire diameter R The area including the center of gravity G up to 20% of the position. In this specification, the center of gravity G in the cross section perpendicular to the longitudinal direction L of the titanium alloy wire 1 is defined as the so-called " Geometric center". In this embodiment, the cross section of the titanium alloy wire rod 1 perpendicular to the longitudinal direction L forms a circle, and therefore, the center of gravity G shown in FIG. 3 is the center of the circular cross section.

Furthermore, in this embodiment, the cross section of the titanium alloy wire rod 1 perpendicular to the longitudinal direction L forms a circle, so the wire diameter R can be defined as the diameter of the circular cross section. In addition, when the cross section of the titanium alloy wire 1 is non-circular, such as an elliptical shape, the wire diameter R can be defined as the average value of the long diameter and the short diameter in the elliptical cross section.

The titanium alloy wire rod 1 of the present embodiment has a cross section perpendicular to the longitudinal direction L of the titanium alloy wire rod 1, from the outer peripheral surface 3 of the titanium alloy wire rod 1 to the center of gravity G to a depth equivalent to 3% of the wire diameter R In the outer peripheral region 2 up to d, the metal structure exhibits an equiaxed structure having equiaxed α grains. When the metal structure of the outer peripheral region 2 is an equiaxed structure, in addition to the increased ductility in the outer peripheral region 2 of the titanium alloy wire rod 1, the surface properties are also good, and defects that become the starting point of fatigue failure in the surface are reduced. Thereby, it is possible to prevent breakage when the titanium alloy wire rod 1 is manufactured, and also to improve the fatigue characteristics. In contrast, if the metal structure of the outer peripheral region 2 of the titanium alloy wire rod 1 becomes an acicular structure, the ductility decreases, and as a result, the fatigue strength of the titanium alloy wire rod 1 cannot be improved.

The average aspect ratio of the α grains in the outer peripheral region 2 may be 1.0 or more and less than 3.0. In order to obtain more excellent fatigue strength, the upper limit is preferably 2.5, and more preferably 2.0. In addition, the average aspect ratio of α crystal grains is theoretically "1" when the metal structure of the outer peripheral region 2 is a complete equiaxed structure. Therefore, the lower limit of the average aspect ratio of α grains in the outer peripheral region 2 is 1.0.

In addition, in this embodiment, the average crystal grain size of the α crystal grains in the outer peripheral region is 10.0 μm or less. As a result, the metal structure of the outer peripheral area becomes finer, and it also complements the equiaxialization of α grains, so that the surface roughness is reduced, and the defects that are the starting point of fatigue failure in the surface are reduced. As a result, the fatigue strength of the titanium alloy wire is reduced. Will improve. On the other hand, if the average crystal grain size of the α crystal grains in the outer peripheral region is larger than 10.0 μm, the surface roughness increases, and the titanium alloy wire rod cannot have excellent fatigue strength.

The average crystal grain size of the α crystal grains in the outer peripheral region may be 10.0 μm or less. In order to further increase the fatigue strength of the titanium alloy wire, it is preferably 5.0 μm or less, more preferably 3.0 μm or less. In addition, the lower limit of the average crystal grain size of the α crystal grains in the outer peripheral region can be set to, for example, 1.0 μm. If it is less than this value, it will be difficult to make and it may cost more.

Next, in the present embodiment, in the cross section of the titanium alloy wire rod 1 perpendicular to the longitudinal direction L, the inner region including the center of gravity from the center of gravity G of the titanium alloy wire rod 1 to the position of 20% of the wire diameter In 4, the metal structure shows an acicular structure with acicular α grains. When the metal structure in the inner region 4 is an acicular structure, the creep strength of the titanium alloy wire will increase. In contrast, when the metallic structure of the inner region 4 in the titanium alloy wire rod 1 does not fully grow into an acicular structure, the creep strength of the titanium alloy wire rod 1 is insufficient. Creeping is the following phenomenon: the dislocation introduced into the metal structure due to deformation is restored by the diffusion of atoms, so that the material softens and the deformation proceeds. Therefore, the rate of recovery (the diffusion rate of atoms) affects the creep. The α/β interface formed by the needle-like structure is highly integrated, and the diffusion rate of atoms is slow, so the needle-like structure is said to have excellent creep strength. By making the metal structure into an acicular structure in the inner region 4 containing the center of gravity G of the titanium alloy wire 1, the creep strength can be improved.

In the inner region 4 including the center of gravity G from the center of gravity G of the titanium alloy wire 1 to the surface to the position of 20% of the wire diameter, the average aspect ratio of the α grains should be 5.0 or more. The variable strength is preferably 6.0 or more, more preferably 7.0 or more. In the internal region 4 including the center of gravity G, the upper limit of the average aspect ratio of the α crystal grains is not particularly limited, and can be set to 20.0 or less based on actual performance.

In addition, in the present embodiment, in the cross-section perpendicular to the longitudinal direction L of the titanium alloy wire rod 1, the average aspect ratio of the α crystal grains is 5.0 or more and the region including the center of gravity G (including the center of gravity G and having the needle-shaped α The area ratio of the acicular structure region of the crystal grains may be, for example, 20% or more with respect to the area of the cross-section perpendicular to the longitudinal direction L of the titanium alloy wire 1. From the viewpoint of further improving the creep strength, the area ratio of the acicular structure region is preferably 40% or more, preferably 50%, relative to the area of the cross-section perpendicular to the length direction L of the titanium alloy wire 1 the above.

From the viewpoint of making the metal structure into an equiaxed structure in the outer peripheral region, in the cross section perpendicular to the longitudinal direction L of the titanium alloy wire rod 1, the region including the center of gravity G where the average aspect ratio of the α grains is 5.0 or more The area ratio (acicular structure region with needle-shaped α crystal grains including the center of gravity G) is preferably 90% or less with respect to the area of the cross section perpendicular to the longitudinal direction L of the titanium alloy wire 1 Less than 80%. In addition, between the outer peripheral area 2 formed by the equiaxed tissue shown in FIG. 1 and the needle-shaped tissue area including the center of gravity G, it is ideal to continuously change from the equiaxed structure to the needle-shaped structure, which is a mixture of these tissues. The organization does not matter.

In the cross section perpendicular to the longitudinal direction L of the titanium alloy wire rod 1, the average crystal grain size and the average aspect ratio of α crystal grains can be calculated by the following method. First, after mirror-polishing a cross section of the titanium alloy wire rod 1 perpendicular to the longitudinal direction L, it is etched with a mixed aqueous solution of hydrofluoric acid and nitric acid. The average crystal grain size and the average aspect ratio can be determined by observing the optical micrograph of the surface. The average crystal grain size can be measured by the linear method (according to JIS G 0551). In the outer peripheral area 2 from the outer peripheral surface 3 of the titanium alloy wire rod 1 toward the center of gravity G to a depth d equivalent to 3% of the wire diameter R, an optical microscope photograph is taken at a magnification of, for example, 500 times, and the obtained photograph is drawn vertically and horizontally. For each of the 5 lines, calculate the average crystal grain size by using the number of grain boundaries that cross the line for each line, and calculate it based on the arithmetic mean of the average crystal grain size of a total of 10 lines. The average aspect ratio can be calculated as follows: in the outer circumferential area 2 from the outer circumferential surface 3 of the titanium alloy wire 1 toward the center of gravity G to a depth d equivalent to 3% of the wire diameter, and in the outer circumferential area 2 from the center of gravity G to the surface 3 In the inner region 4 including the center of gravity G up to 20% of the wire diameter R, an optical microscope photograph is taken at a magnification of, for example, 500 times, and the long axis and the short axis of the obtained photograph are measured for 50 arbitrary crystal grains, and taken as Calculate the average of the values obtained by dividing the long axis by the short axis. Here, as shown in Figure 4, the "long axis 11" refers to the line connecting any two points on the grain boundary 10 (contour) of the α phase, the one with the longest length, and the "short axis 12" is aligned with the long axis 11 Among the lines that are perpendicular to any two points on the crystal boundary 10 (contour), the one with the longest length.

Here, the average aspect ratio of α crystal grains was measured when the cross section of the titanium alloy wire 1 perpendicular to the longitudinal direction L was measured, and when the cross section of the titanium alloy wire 1 parallel to the longitudinal direction was measured. At the time of measurement, it can be considered that it will become the same value. However, when the measurement is performed in the cross section parallel to the longitudinal direction L of the titanium alloy wire rod 1, it may be difficult to distinguish the structure having α grains elongated by rolling and the needle-like α grains. organization. Therefore, it is calculated using the value measured in the cross section perpendicular to the longitudinal direction L of the titanium alloy wire 1. In addition, in terms of a structure having α grains elongated by rolling, when the measurement is performed in a cross section perpendicular to the longitudinal direction L of the titanium alloy wire 1 and the length of the titanium alloy wire 1 When the measurement is performed in a cross section in which the direction L is parallel, it can be considered that the value of the aspect ratio of the α crystal grains is different. Specifically, when measuring a structure having α grains elongated by rolling, when measured in a cross section parallel to the longitudinal direction L of the titanium alloy wire rod 1, it was observed that the aspect ratio was large (for example, it became 5.0 or more) In contrast to this, when measured in a cross section perpendicular to the longitudinal direction L of the titanium alloy wire rod 1, α crystal grains with a small aspect ratio (for example, about 1.0 to 3.0) were observed. Therefore, by measuring the average aspect ratio of the α grains in the cross section perpendicular to the length direction L of the titanium alloy wire rod 1, it is possible to distinguish between the α grains elongated by rolling and the needle-shaped α grains. Grains. In addition, when calculating the average crystal grain size and the average aspect ratio of the α crystal grains, it is estimated that the α crystal grains having the same orientation are arranged with the fine needle-like β phase interposed therebetween. Since EBSD is difficult to detect small β phases, it may be difficult to perform analysis by EBSD.

Strictly speaking, the center of gravity G is in the cross section perpendicular to the length direction L of the titanium alloy wire 1 and exists in the form of "dots". Therefore, when observing the average aspect ratio of α grains in the inner region 4 of the titanium alloy wire 1 including the center of gravity G, the observation of α is for the region from the center of gravity G to the outer peripheral surface 3 to 20% of the wire diameter R. The aspect ratio of the grains can be calculated by averaging the observed aspect ratios. The metal structure of the titanium alloy wire of this embodiment has been described above.

(1.2　Chemical composition) Next, the chemical composition of the titanium alloy wire of this embodiment will be explained. The chemical composition of the titanium alloy wire of this embodiment is not particularly limited as long as it can be formed into a two-phase structure of α phase and β phase at the temperature environment during use or room temperature. For example, JIS H 4600 and JIS H 4650 can be used. The described various compositions of α+β type titanium alloys. Alternatively, it may contain the elements described below. In addition, including the following description, unless otherwise specified in this manual, if the content is expressed by "%", the "%" represents mass %.

Al: 0% or more and 7.0% or less Aluminum (Al) is an element that dissolves in the α phase to strengthen the α phase. Although the α+β titanium alloy wire may not contain Al, in order to obtain this effect, it may contain 2.0% or more, preferably 2.5% or more of Al. On the other hand, if the Al content is too large, depending on the chemical composition, α ₂ phase (Ti ₃ Al) may be precipitated and the ductility may decrease, and the amount of α phase may increase and the hot workability may decrease. The Al content is 7.0% or less, preferably 6.5% or less.

V: 0% or more and 6.0% or less Vanadium (V) stabilizes the β phase and improves hot formability and heat treatment properties. Although the α+β type titanium alloy wire may not contain V, in order to obtain this effect, it may contain 1.5% or more, preferably 2.0% or more. On the other hand, if the V content is too large, depending on the chemical composition, the volume ratio of the β phase may increase, and the strength of the α+β titanium alloy wire may decrease. Therefore, the V content can be set to 6.0% or less, preferably It is 5.5% or less.

Mo: 0% or more and 7.0% or less Molybdenum (Mo) also stabilizes the β phase and improves hot formability and heat treatment properties. Although the α+β type titanium alloy wire may not contain Mo, in order to obtain this effect, it may contain 1.0% or more, preferably 1.5% or more of Mo. On the other hand, if the Mo content is too large, depending on the chemical composition, the volume ratio of the β phase may increase, and the strength of the α+β titanium alloy wire may decrease. Therefore, the Mo content can be set to 7.0% or less, and it is better to set it. Less than 6.0%.

Cr: 0% or more and 7.0% or less Chromium (Cr) also stabilizes the β phase and improves hot formability and heat treatment properties. Although the α+β titanium alloy wire may not contain Cr, in order to obtain this effect, it may contain 2.0% or more, preferably 3.0% or more of Cr. On the other hand, if the Cr content is too large, depending on the chemical composition, the volume ratio of the β phase may increase, and the strength of the α+β titanium alloy wire may decrease. Therefore, the Cr content can be set to 7.0% or less. Less than 6.0%.

Zr: 0% or more and 5.0% or less Zirconium (Zr) is an element that strengthens both the α phase and the β phase. Although the α+β titanium alloy wire may not contain Zr, in order to obtain this effect, it may contain 1.5% or more, preferably 2.0% or more of Zr. On the other hand, if the Zr content is too large, depending on the chemical composition, the precipitation of the α ₂ phase (Ti ₃ Al) may be promoted and the ductility may be reduced. Therefore, the Zr content can be set to 5.0% or less, preferably 4.5 %the following.

Sn: 0% or more and 3.0% or less Tin (Sn) is an element that strengthens both the α phase and the β phase. Although the α+β type titanium alloy wire may not contain Sn, in order to obtain this effect, it may contain 1.0% or more, preferably 1.5% or more of Sn. On the other hand, if the Sn content is too large, depending on the chemical composition, the precipitation of the α ₂ phase (Ti ₃ Al) may be promoted and the ductility may be reduced. Therefore, the Sn content can be set to 3.0% or less, preferably 2.5 %the following.

Si: 0% or more and 0.50% or less Silicon (Si) improves heat resistance. Although the α+β type titanium alloy wire may not contain Si, in order to obtain this effect, it may contain 0.04% or more, preferably 0.07% or more of Si. On the other hand, if the Si content is too large, depending on the chemical composition, the creep strength may decrease due to the precipitation of silicides. Therefore, the Si content can be set to 0.50% or less, preferably 0.35% or less .

Cu: 0% or more and 1.8% or less Copper (Cu) stabilizes the β phase, and also solid-dissolves in the α phase to strengthen the α phase. Although the α+β titanium alloy wire may not contain Cu, in order to obtain this effect, it may contain 0.4% or more, preferably 0.8% or more of Cu. On the other hand, if the Cu content is too high, depending on the chemical composition, the fatigue strength may be reduced due to Ti ₂ Cu precipitation. Therefore, the Cu content can be set to 1.8% or less, preferably 1.5% or less.

Nb: 0% or more and 1.0% or less Niobium (Nb) improves oxidation resistance. Although the α+β type titanium alloy wire may not contain Nb, in order to obtain this effect, it may also contain 0.1% or more, preferably 0.2% or more of Nb. On the other hand, if the Nb content is too large, depending on the chemical composition, the volume ratio of the β phase may increase, and the strength of the α+β titanium alloy wire may decrease. Therefore, the Nb content can be set to 1.0% or less, preferably Less than 0.8%.

Mn: 0% or more and 1.0% or less Manganese (Mn) also stabilizes the β phase and improves hot formability and heat treatment properties. Although the α+β titanium alloy wire material may not contain Mn, in order to obtain this effect, it may contain Mn in an amount of 0.1% or more, preferably 0.2% or more. On the other hand, if the Mn content is too high, depending on the chemical composition, the volume ratio of the β phase may increase, and the strength of the α+β titanium alloy wire may decrease. Therefore, the Mn content can be set to 1.0% or less, and it is better to set Less than 0.8%.

Ni: 0% or more and 1.0% or less Nickel (Ni) also stabilizes the β phase and improves hot formability and heat treatment properties. Although the α+β titanium alloy wire may not contain Ni, in order to obtain this effect, it may contain 0.1% or more, preferably 0.2% or more of Ni. On the other hand, if the Ni content is too large, depending on the chemical composition, the volume ratio of the β phase may increase, and the strength of the α+β titanium alloy wire may decrease. Therefore, the Ni content can be set to 1.0% or less, preferably Less than 0.8%.

S: 0% or more and 0.20% or less Sulfur (S) improves machinability. Although the α+β type titanium alloy wire may not contain S, in order to obtain this effect, it may contain 0.01% or more, preferably 0.03% or more. On the other hand, if the S content is too large, depending on the chemical composition, the thermoformability may be reduced due to the formation of inclusions, so the S content can be set to 0.20% or less, preferably 0.10% or less.

REM: 0% or more and 0.20% or less Rare earth elements (REM) are contained together with S to improve machinability. Although the α+β titanium alloy wire may not contain REM, in order to obtain this effect, it may contain 0.01% or more, preferably 0.03% or more of REM. On the other hand, if the REM content is too large, depending on the chemical composition, the thermoformability may be reduced due to the formation of inclusions. Therefore, the REM content can be set to 0.20% or less, preferably 0.10% or less.

Here, as REM, specifically, the following elements can be cited, and one of them can be contained alone or two or more of them can be contained in combination: scandium (Sc), yttrium (Y), lanthanum (La), cerium ( Ce), dysprosium (Pr), neodymium (Nd), samarium (Pm), samarium (Sm), europium (Eu), samarium (Gd), turbidium (Tb), dysprosium (Dy), 鈥 (Ho), erbium ( Er), 銩 (Tm), ytterbium (Yb) and lutetium (Lu). When two or more rare earth elements are contained, mixtures or compounds of rare earth elements such as mixed rare earth elements (rare earth metal alloys) and neodymium alloys (alloys composed of Nd and Pr) before separation and refining can be used. . In addition, when two or more rare earth elements are contained, the above-mentioned REM amount refers to the total amount of all rare earth elements.

Fe: 0% or more and 2.10% or less Iron (Fe) is an element that strengthens the β phase. Although the α+β-type titanium alloy wire may not contain Fe, in order to obtain this effect, it may contain 0.50% or more, preferably 0.70% or more of Fe. On the other hand, if the Fe content is too high, depending on the chemical composition, Fe segregation may cause a decrease in manufacturability, or the precipitation of intermetallic compounds (TiFe) may cause a decrease in toughness and ductility. Therefore, the Fe content can be set to 2.10%. Below, it is preferably set to 1.50% or less.

N: 0% or more and 0.050% or less Nitrogen (N) is an element that dissolves in the α phase to strengthen the α phase. Although the α+β-type titanium alloy wire may not contain N, in order to obtain this effect, it may contain 0.002% or more, preferably 0.005% or more. On the other hand, if the N content is too large, depending on the chemical composition, low-density inclusions (TiN) may be formed and become the starting point of fatigue failure. Therefore, the N content can be set to 0.050% or less, preferably 0.030% the following.

O: 0% or more and 0.250% or less Oxygen (O) is an element that dissolves in the α phase to strengthen the α phase. Although the α+β titanium alloy wire may not contain O, in order to obtain this effect, it may contain O in an amount of 0.050% or more, preferably 0.100% or more. On the other hand, if the O content is too large, depending on the chemical composition, the α phase may increase excessively and cause the ductility to decrease. Therefore, the O content can be set to 0.250% or less, preferably 0.200% or less.

C: 0% or more and 0.100% or less Carbon (C) will dissolve in the α phase to strengthen the α phase, and by containing it with S, the machinability will be improved. Although the α+β type titanium alloy wire may not contain C, in order to obtain this effect, it may contain 0.005% or more, preferably 0.010% or more. On the other hand, if the C content is too large, depending on the chemical composition, the carbide may increase excessively and cause the hot formability to decrease. Therefore, the C content can be set to 0.100% or less, preferably 0.080% or less.

The remaining part of the chemical composition of the titanium alloy wire of this embodiment may be titanium (Ti) and impurities. Impurities refer to components mixed in due to raw materials or other factors during the industrial production of titanium alloy wires, and are permitted within a range that does not adversely affect the titanium alloy wires of this embodiment. The impurity can include, for example: hydrogen (H), tantalum (Ta), cobalt (Co), tungsten (W), palladium (Pd), boron (B), chlorine (Cl), sodium (Na), magnesium (Mg) ), calcium (Ca), etc. When the aforementioned H, Ta, Co, Pd, W, B, Cl, Na, Mg, and Ca are contained as impurities, the content thereof is, for example, 0.05% or less each and 0.10% or less in total.

Mo equivalent In the chemical composition of the titanium alloy wire of this embodiment, the contents of Al, Mo, V, Nb, Fe, Cr, Ni, and Mn more satisfy the following formula (1). -4.00≦[Mo]+0.67[V]+0.28[Nb]+2.9[Fe]+1.6[Cr]+1.1[Ni]+1.6[Mn]-[Al]≦6.00　・・・(1) In addition, in the formula (1), the description of [element symbol] indicates the content (mass %) of the corresponding element symbol, and 0 is substituted for the element symbol that is not contained.

A=[Mo]+0.67[V]+0.28[Nb]+2.9[Fe]+1.6[Cr]+1.1[Ni]+1.6[Mn]-[Al]

Here, the Mo equivalent A expressed on the right side of the above formula (1) is used to combine the elements described in the formula that can stabilize the β phase (β stabilizing elements) Mo, V, Nb, Fe, Cr, Ni, and The degree of stabilization of β phase caused by Mn is digitized. At this time, based on the degree of stabilization of the β phase by Mo, the degree of stabilization of the β phase by the β stabilizing elements other than Mo is relative to the positive coefficient. On the other hand, since Al is an element (α stabilizing element) that dissolves in the α phase to strengthen the α phase, in the Mo equivalent A, the correlation coefficient of Al becomes a negative value.

[Range of Mo equivalent A: -4.00≦A≦6.00] The titanium alloy wire of this embodiment contains at least one element selected from the group consisting of Mo, V, Nb, Fe, Cr, Ni, and Mn, so that the Mo equivalent A represented by the above formula (1) is The value is in the range from -4.00 to 6.00. When the value of the Mo equivalent A is less than -4.00, the β phase becomes too small, it is difficult to form a needle-like structure, and the creep characteristics are not improved. The lower limit of Mo equivalent A is preferably -3.50, preferably -3.00. On the other hand, when the value of Mo equivalent A is greater than 6.00, the needle-like α phase cannot be formed from the β phase during cooling, and the inside becomes a β single-phase structure, and the creep characteristics are not improved. The upper limit of Mo equivalent A is preferably 5.00, preferably 4.00. The titanium alloy wire with the above chemical composition will become an α+β titanium alloy wire with α phase and β phase.

More specifically, the titanium alloy wire may also contain: Al: 4.5% or more and 6.5% or less, preferably 4.8% or more or 6.2% or less, Fe: 0.50% or more and 2.10% or less, preferably 0.70% or more or 1.50% or less. Also, it may be the following: N: 0% or more and 0.050% or less, preferably 0.002% or more or 0.030% or less, O: 0% or more and 0.250% or less, preferably 0.100% or more or 0.200% or less, C: 0% or more and 0.100% or less, preferably 0.001% or more or 0.080% or less.

The titanium alloy wire rod with the above chemical composition becomes an α+β type titanium alloy wire rod with α phase and β phase, and has stable fatigue strength with little variation and high hot workability. In addition, the titanium alloy wire rod with the above chemical composition can be exemplified by Super-TiX 51AF (Ti-5Al-1Fe, manufactured by Nippon Steel Corporation).

Alternatively, the titanium alloy wire may also contain: Al: 2.0% or more and 7.0% or less, preferably 2.5% or more or 6.5% or less, V: 1.5% or more and 6.0% or less, preferably 2.0% or more or 5.5% or less. Also, it may be the following: Fe: 0% or more and 0.50% or less, preferably 0.03% or more or 0.30% or less, N: 0% or more and 0.050% or less, preferably 0.002% or more or 0.030% or less, O: 0% or more and 0.250% or less, preferably 0.100% or more or 0.200% or less.

The titanium alloy wire rod with the above chemical composition will also become an α+β type titanium alloy wire rod containing α phase and β phase, and has stable and uneven fatigue strength and high hot workability. In addition, titanium alloy wires with the above chemical composition can be exemplified by Ti-3Al-2.5V, Ti-6Al-4V, SSAT-35 (Ti-3Al-5V, manufactured by Nippon Steel Corporation) and the like.

In addition, titanium alloy wire may also contain: Al: 5.0% or more and 7.0% or less, preferably 5.5% or more or 6.5% or less, Mo: 1.0% or more and 7.0% or less, preferably 1.8% or more or 6.5% or less, Zr: 3.0% or more and 5.0% or less, preferably 3.6% or more or 4.4% or less, Sn: 1.0% or more and 3.0% or less, preferably 1.75% or more or 2.25% or less. Also, it may be the following: Si: 0% or more and 0.50% or less, preferably 0.06% or more or 0.10% or less, Fe: 0% or more and 0.50% or less, preferably 0.03% or more or 0.10% or less, N: 0% or more and 0.050% or less, preferably 0.002% or more or 0.030% or less, O: 0% or more and 0.250% or less, preferably 0.100% or more or 0.200% or less.

The titanium alloy wire rod with the above chemical composition becomes an α+β type titanium alloy wire rod containing α phase and β phase, and has particularly excellent creep characteristics. In addition, titanium alloy wires with the above chemical composition can be exemplified by Ti-6Al-2Sn-4Zr-2Mo-0.08Si, Ti-6Al-2Sn-4Zr-6Mo, etc. The chemical composition of the titanium alloy wire of the present embodiment has been described above.

(1.3　Wire diameter and shape) The wire diameter R of the titanium alloy wire rod 1 of the present embodiment is not particularly limited, and it can be set to, for example, 2 mm or more and 20 mm or less. By making the wire diameter R of the titanium alloy wire 1 2 mm or more, a needle-like structure with needle-like α crystal grains can be formed in the inner region 4 including the center of gravity G, and a fine-grained structure can be formed more reliably in the outer peripheral region 2 The fine equiaxed structure of equiaxed α grains can more reliably achieve excellent fatigue strength and creep strength at the same time. In addition, by making the wire diameter R of the titanium alloy wire 1 20mm or less, wire drawing at high speed can be carried out, and the central part of the rod wire is stable and easy to process and generate heat, which makes it easy to be inside the center of gravity. Area 4 acquires needle-like tissue. The lower limit of the wire diameter R of the titanium alloy wire 1 of this embodiment is preferably 3 mm, and the upper limit of the wire diameter R is preferably 15 mm.

In addition, the shape (cross-sectional shape) of the titanium alloy wire of the present embodiment is not limited to that shown in the figure, and may be a polygonal shape such as an ellipse and a square in addition to a circular shape.

Regarding the embodiment described above, in the cross section of the titanium alloy wire rod 1 perpendicular to the longitudinal direction L, the metallic structure of the outer peripheral region 2 is fine equiaxed with equiaxed α grains having an average crystal grain size of 10 μm or less In addition, the metal structure of the inner region 4 including the center of gravity G is an acicular structure having acicular α crystal grains, so that the fatigue strength and creep strength of the titanium alloy wire are excellent at the same time.

The titanium alloy wire of the present embodiment described above has excellent creep strength and fatigue strength in addition to the excellent properties, corrosion resistance, and specific strength derived from the α+β type titanium alloy. Therefore, the titanium alloy wire of the present embodiment can be used for any purpose, and can be suitably used for fasteners (fixtures) such as bolts and nuts, valves, and the like. The titanium alloy wire of this embodiment is particularly suitable as a material for fasteners or valves of transportation equipment, such as airplanes and automobiles. The titanium alloy wire of this embodiment described above can be manufactured by any method, and it can also be manufactured by the manufacturing method of the titanium alloy wire of this embodiment described below, for example.

<2. Manufacturing method of titanium alloy wire> Next, the manufacturing method of the titanium alloy wire rod of this embodiment is demonstrated. The manufacturing method of the titanium alloy wire of this embodiment has the following steps: the step of heating the titanium alloy blank to a temperature above (β transformation point -200)°C (heating step); and the total shrinkage rate is 90% or more, At least from the final pass, the average shrinkage rate per pass in more than one pass is 10% or more, and the drawing speed is 5 m/sec or more to process the α+β titanium alloy blank (processing step). Hereinafter, each step is explained.

(2.1　Prepare titanium alloy blank) First, before the above steps, prepare titanium alloy blanks. Titanium alloy blanks can use those with the above-mentioned chemical composition, and can use those made by known methods. For example, titanium alloy blanks can be obtained by making an ingot from sponge titanium using a vacuum arc melting method, and hot forging it at the temperature of the β single-phase zone. In addition, for titanium alloy blanks, pre-treatments such as cleaning treatment and pickling can also be performed as needed.

In addition, the wire diameter of the titanium alloy blank can be appropriately selected depending on the predetermined reduction in the processing step and the predetermined wire diameter of the titanium alloy wire.

(2.2　 heating step) In this step, the titanium alloy blank is heated to a temperature above (β transformation point -200)°C. Thereby, the deformation resistance is reduced, and it becomes easier to maintain the temperature near the center of gravity of the titanium alloy blank above the β transformation point in the processing steps described later, and the growth of the acicular structure near the center of gravity of the titanium alloy blank can be promoted. As a result, in the processing steps described later, the average aspect ratio of α grains in the vicinity of the center of gravity (inner region) can be made 5.0 or more. In contrast, when the heating temperature in this step is lower than (β transformation point -200)°C, the deformation resistance becomes too large, or sometimes the temperature near the center of gravity of the titanium alloy blank cannot be maintained at β in the later processing steps. Above the metamorphic point, the needle-like structure cannot be fully grown near the center of gravity of the titanium alloy blank, and as a result, the average aspect ratio of the α grains near the center of gravity (inner area) cannot be increased sufficiently.

The heating temperature in this step only needs to be above (β transformation point-200)°C, and from the viewpoint of deformation resistance, it is preferably above (β transformation point-150)°C and at (β transformation point-125) )°C or higher is better. The upper limit of the heating temperature in this step is not particularly limited, but from the viewpoint of the reduction in yield due to the formation of scale, the heating temperature is preferably (β transformation point + 100) ℃ or less, preferably (β transformation point) Point +50) ℃ below.

In addition, the "β transformation point" in this specification refers to the end temperature of β transformation of the titanium alloy when it is heated. The titanium alloy wire of this embodiment and the titanium alloy blank used as its raw material are in the α+β two-phase region where α phase and β phase exist at room temperature or in the use environment, and the β transformation start temperature is at the aforementioned room temperature or Below the temperature of the operating environment. The β transformation temperature T can be obtained from the state diagram. The state diagram can be obtained by, for example, the CALPHAD (Computer Coupling of Phase Diagrams and Thermochemistry) method. For this, the integrated thermodynamic calculation system Thermo-Calc and the predetermined database (TI3) of Thermo-Calc Software AB can be used.

(2.3　Processing steps) In this step, the wire drawing of the titanium alloy blank is carried out by sequentially passing through a plurality of rolling passes, which is the so-called wire drawing processing step.

This processing step is not carried out by reversible rolling, but by tandem rolling. The tandem rolling system is as follows: the rolled material is continuously passed through a plurality of rolling passes arranged in a line, and the rolling passes are rolled sequentially in one direction in each rolling pass. By using tandem rolling to produce titanium alloy wire, the total shrinkage rate can be more than 90%, and the average shrinkage rate per pass in more than one pass from at least the final pass can be over 10%. And the wire drawing speed is above 5m/sec to process titanium alloy blanks.

Here, with reference to the drawings (a diagram showing a cross section perpendicular to the longitudinal direction), the process of manufacturing the titanium alloy wire of the present embodiment through the processing steps will be described. Figures 5(a) to 5(e) schematically show the process of manufacturing the titanium alloy wire of this embodiment in sequence.

First, since it has been heated to a temperature above (β transformation point -200)°C in the aforementioned heating step, the metal structure becomes an α+β structure with β phase as the main phase, or β single phase. Here, the case of the β single-phase structure composed only of β crystal grains 20 as shown in FIG. 5(a) will be described. Then, in the early stage of processing, as shown in Figure 5(b), when the temperature is reduced and the β phase is transformed into the α phase, needle-like α crystal grains 21 are formed, forming a structure composed of α and β phases. Needle-like tissue. In addition, the needle-like structure is a structure in which needle-like α and needle-like β that grow into needles are arranged in layers.

Next, in the middle of the processing step, the needle-shaped α crystal grains 21 are split due to processing, and the crystal grains grow to form equiaxed α crystal grains 22 as shown in FIG. 5(c). In the middle of the processing step, since the wire drawing speed (strain speed) is still small and the processing heat generation is small, the temperature near the center of gravity will not be higher than the β transformation point (it becomes a high temperature until the β single-phase region). Therefore, an α+β type equiaxed structure in which equiaxed α crystal grains 22 and equiaxed β crystal grains are mixed is formed.

Next, in the later stage of the processing step, the wire drawing speed increases, and heat is generated by processing, and the temperature rises to a temperature above the β transformation point near the center of gravity. Therefore, as shown in FIG. 5(d), the α phase is transformed into the β phase in the inner region including the center of gravity, and a β single-phase structure composed of only β crystal grains 23 is formed. In addition, in general, titanium alloys have a large deformation resistance, and heat generation during the rolling step and the wire drawing step is relatively large. In particular, in the later stage of the processing step, since the average shrinkage ratio and the wire drawing speed become relatively large, the processing heat generation increases when passing through the rolling pass. In addition, in the inner region of the titanium alloy blank, for example, near the center of gravity, less heat is generated and dissipated for processing, so the temperature of this region rises and becomes above the β transformation point.

On the other hand, the outer peripheral area can sufficiently dissipate heat from the outer peripheral surface even at the later stage of the processing step, and by processing at a relatively low temperature, the metal structure can be refined and equiaxed. Therefore, the α crystal grains 24 in the outer peripheral region become fine equiaxed crystal grains with an average crystal grain size of 10 μm or less. In addition, since the metal structure of the outer peripheral region is sufficiently refined and equiaxed as described above, the occurrence of defects on the outer peripheral surface can be suppressed, and the occurrence of defects such as breakage during manufacturing can be suppressed.

Then, at the end of the processing step, the titanium alloy billet will be cooled to the vicinity of the center of gravity. Therefore, as shown in Figure 5(e), the needle-like α crystals are formed when the temperature is reduced and the transformation from the β phase to the α phase occurs. The granule 25 forms a needle-like structure in the inner region including the center of gravity. In this way, the titanium alloy wire rod of this embodiment is manufactured. In a cross section perpendicular to the longitudinal direction, the metal structure in the outer peripheral region is a fine equiaxed structure 24, and the metal structure in the inner region is a needle-like structure 25.

In addition, by including a processing step, the total shrinkage rate in this step is 90% or more, the average shrinkage rate per pass is 10% or more in at least the final pass, and the drawing line The titanium alloy blank is processed at a speed of 5 m/sec or more to manufacture the titanium alloy wire of this embodiment. That is, in a cross section perpendicular to the longitudinal direction L, in the outer peripheral region 2 from the surface 3 toward the center of gravity G to a depth d corresponding to 3% of the wire diameter, the metal structure has an average crystal grain size of 10 μm The following is the equiaxed structure of equiaxed α grains, and in the inner region 4 including the center of gravity G from the center of gravity G to the surface 3 to the position of 20% of the wire diameter, the metallic structure becomes needles with acicular α grains状 Organization. In a cross section perpendicular to the longitudinal direction L, the average aspect ratio of the α grains in the outer peripheral region 2 is 1.0 or more and less than 3.0, and the average aspect ratio of the α grains in the inner region 4 is 5.0 or more.

In addition, the wire drawing speed in one or more passes from at least the final pass explained above is much higher than the wire drawing speed (about 0.2~2.0m/sec) used in the manufacture of titanium alloy wire in the past. The inventors of the present invention found that by deliberately using the above-mentioned wire drawing speed and the above-mentioned average shrinkage ratio to generate greater processing heat generation, the metal structure of the above-mentioned titanium alloy wire of this embodiment can be obtained.

As described above, in this embodiment, the average reduction rate per pass is 10% or more among one or more passes from at least the final pass. In this way, sufficient processing heat can be generated in at least one pass from the final pass. In contrast, if the average shrinkage ratio is less than 10%, sufficient processing heat cannot be generated, the temperature of the internal region 4 including the center of gravity G cannot be made high enough, and the β phase cannot grow sufficiently.

In at least one pass from the final pass, the average shrinkage rate of each pass only needs to be more than 10%, and in order to generate greater processing heat to make β single-phase structure, so that the subsequent cooling The formation of needle-like structure is preferably above 15%, more preferably above 20%. In addition, in at least one or more passes from the final pass, the upper limit of the average shrinkage rate per pass is not particularly limited. From the viewpoint of the load on the equipment, the average shrinkage rate is preferably 45% Below, it is preferably 35% or less.

In at least one pass from the final pass, the drawing speed is 5m/sec or more. As a result, in at least one or more passes from the final pass, the amount of heat dissipation can be reduced, and the heat generated by processing heat will be accumulated in the inner region 4 including the center of gravity G, and as a result, the temperature of the inner region 4 can be increased. Become high enough. On the other hand, in one or more passes from at least the final pass, when the wire drawing speed is less than 5m/sec, the heat dissipation becomes large. As a result, the heat energy generated by the processing heat cannot be stored in the inner region 4 including the center of gravity G. The temperature of the inner region 4 cannot be made high enough. Therefore, it does not become a β single-phase structure, and it becomes difficult to form an acicular structure during subsequent cooling.

In at least one or more passes from the final pass, the drawing speed should be at least 5m/sec. In order to fully grow the β phase to form needle-like structure during subsequent cooling, it is preferably at least 10m/sec. , It is better to be above 20m/sec. In addition, in at least one or more passes from the final pass, the upper limit of the wire drawing speed is not particularly limited. From the viewpoint of the stability of operation and the load on the equipment, the wire drawing speed is preferably 75m/sec. Hereinafter, it is preferably 50 m/sec or less.

In addition, the total shrinkage rate of the titanium alloy blank processed in this step is more than 90%. As a result, as described above, the metal structure of the outer peripheral region 2 is equiaxed and refined. On the other hand, if the total shrinkage ratio of the titanium alloy blank is less than 90%, the equiaxialization and miniaturization of the metal structure of the outer peripheral region 2 are insufficient. Alternatively, even if the metal structure of the outer peripheral region 2 is equiaxed, the α crystal grains are not sufficiently refined and have a larger grain size.

The above-mentioned total area reduction ratio may be 90% or more, and in order to more reliably equiaxial and refine the metal structure of the outer peripheral region 2, it is preferably 95% or more, and more preferably 99% or more.

In addition, the reduction ratio per pass refers to the reduction rate of the area after the 1 pass relative to the cross-sectional area before the 1 pass, and the total reduction ratio refers to the titanium alloy blank after processing in this step The reduction rate of the cross-sectional area relative to the cross-sectional area before processing.

In addition, the slit shape of the roller used in this step is not particularly limited as long as the above-mentioned drawing speed and surface shrinkage ratio can be achieved, and well-known slit shapes such as true circle, ellipse, and square shape can be used.

In addition, the number of passes through the roller (number of passes) in this step is not particularly limited, as long as it is 5 or more times to enable the implementation of this step. In addition, it is advisable to perform more than 10 passes to achieve a reduction rate of more than 90%.

Through the above steps, the titanium alloy wire of the present embodiment can be industrially and stably manufactured. In addition, for the obtained titanium alloy wire rod, the following heat treatment and post-treatment may be performed as needed.

(2.4　 heat treatment step) For the titanium alloy blanks (titanium alloy wires) obtained through the above steps, heat treatment (annealing treatment) can also be performed in a temperature range above (β transformation point-300) ℃ and (β transformation point-50) ℃ ). Thereby, the strain generated in the above processing steps can be removed, and the fatigue strength of the obtained titanium alloy wire can be further improved.

In this treatment, the heat treatment temperature is above (β transformation point -300)°C. Thereby, the strain generated in the processing step can be sufficiently removed. The heat treatment temperature is preferably above (β transformation point-250)°C, preferably above (β transformation point-200)°C.

In addition, in this treatment, the heat treatment temperature is (β transformation point-50)°C or lower. Thereby, a hybrid (bimodal) structure of equiaxed structure and needle-like structure is generated in the outer peripheral region 2, and the fatigue characteristics can be prevented from being reduced. The heat treatment temperature is preferably (β transformation point -100)°C or lower.

In addition, the heat treatment time is not particularly limited and can be appropriately selected, and it may be, for example, 1 minute or more and 120 minutes or less, preferably 2 minutes or more or 60 minutes or less.

In addition, the gas environment during the heat treatment is not particularly limited, and may be air, vacuum, or inert gas (argon gas, etc.). As long as it is not a gas environment that particularly promotes chemical reactions such as oxidation, it can be treated later by descaling.

(2.5　 post-processing) The post-treatment may include removing the oxide film by pickling or cutting, or cleaning treatment, etc., which may be appropriately applied as necessary. In the above, the manufacturing method of the titanium alloy wire of this embodiment has been demonstrated.

Example Hereinafter, examples are shown and embodiments of the present invention are specifically described. In addition, the examples shown below are only examples of conditions of the present invention, and the present invention is not limited to the following examples.

1. 　Manufacturing of titanium alloy wire First, an ingot with the chemical composition in Table 1 is produced by the vacuum arc melting method, and hot forged at the temperature of the β single-phase zone to obtain a titanium round rod, which has alloy types A to O Composition and predetermined diameter (wire diameter 22mm~180mm). In addition, in each titanium round bar, components other than the composition described in Table 1 are titanium and impurities. In addition, the alloy types A to M are all α+β-type titanium alloys that can be formed at room temperature or in a use environment with a two-phase structure of α phase and β phase. The alloy type N is an α+β type titanium alloy with almost no β phase at room temperature, and the alloy type O is a semi-stable β type titanium alloy whose transformation start temperature of Asada loose iron is below room temperature. Alloy types A to M are examples that satisfy the composition range specified in claim 1. Alloy types A to A4 are examples that satisfy the composition range specified in claim 2. Alloy types B~B5 are examples that satisfy the composition range specified in claim 3. Alloy types C~C9 are examples that satisfy the composition range specified in claim 4.

[Table 1]

Next, after heating each titanium round bar obtained (heating step), a wire drawing process (processing step) was performed using a roller. And, if necessary, a heat treatment step (heat treatment step) is performed. The heat treatment is performed in a 100% argon atmosphere for 10 minutes. Thus, the titanium alloy wire rods of various examples were obtained. Listed in Table 2, Table 3 and Table 4: the heating temperature (℃) in the heating step, the average shrinkage rate (%) of each pass in more than one pass in the processing step from at least the final pass, and the Linear speed (m/sec), total shrinkage in processing steps (%), presence or absence of heat treatment steps, and heat treatment temperature (°C).

[Table 2]

[table 3]

[Table 4]

2. 　Analysis and Evaluation For each titanium alloy wire, the following items were analyzed and evaluated.

2.1 　 Observation of metal structure (microstructure) Regarding the titanium alloy wire rod of each example, the cross-section perpendicular to the longitudinal direction was observed as follows, and for each area of the cross-section, whether the metal structure was an equiaxed structure or an acicular structure was investigated. In addition, the average crystal grain size and average aspect ratio of the α crystal grains were measured and calculated, and the area ratio of the region where the average aspect ratio of the α crystal grains was 5.0 or more with respect to the above-mentioned cross section was determined. First, with respect to the titanium alloy wire rod of each example, after mirror-polishing a cross section perpendicular to the longitudinal direction, it was etched with a mixture of hydrofluoric acid and nitric acid. The average crystal grain size and average aspect ratio are measured by observing the optical micrograph of the surface. The average crystal grain size was measured by the linear method based on JIS G 0551. Specifically, based on an optical microscope photograph taken at a magnification of 500 times, five lines are drawn vertically and horizontally, and the average crystal grain size is calculated by using the number of grain boundaries that cross the line for each line. Calculate the arithmetic average of the average crystal grain size of 10 bars. The average aspect ratio is an optical microscope photograph taken at a magnification of 500 times. The long axis and the short axis are measured for 50 arbitrary crystal grains, and the long axis is divided by the short axis as the arithmetic average of the value. Figure out. Here, the "long axis" refers to the line connecting any two points on the grain boundary (contour) of the α phase, the one with the longest length, and the "short axis" is orthogonal to the long axis and connected to the crystal boundary (contour) Of any two-point line, the one with the longest length.

2.2 Fatigue strength The fatigue strength is a rotating bending fatigue test based on JIS Z 2274:1978, and the maximum stress when there is no fracture until 10 ⁷ times is the fatigue strength.

2.3　 creep strength Creep strength is a creep test based on JIS Z 2271:2010. Specifically, the creep test was carried out for 100 hours in an environment of 400°C, and the minimum stress that reached 0.2% strain at this time was used as the creep strength.

2.4 Evaluation For the same alloy type, in order to compare with the titanium alloy wire obtained by the manufacturing method equivalent to the conventional manufacturing method, in the examples of alloy types A to O shown in Table 2 (all comparative examples), one of the processing steps At least from the final pass, the average shrinkage rate (%) of each pass in more than one pass is 16%, and the drawing speed (m/sec) is set to 2.0m/sec (less than 5m/sec). For the titanium alloy wire rods illustrated in Table 2, the metal structures of the outer and inner regions are equiaxed. On the other hand, in the invention examples 1 to 31 of alloy types A to M shown in Table 3, the average shrinkage rate (%) per pass in more than one pass is 16% from at least the final pass in the processing steps. , The drawing speed (m/sec) is 25m/sec. The titanium alloy wire rods of invention examples 1 to 31 shown in Table 3, the metal structure of the outer peripheral area becomes an equiaxed structure with equiaxed α phase as the parent phase and fine β phase in its grain boundaries and grains. The metallic structure of the region becomes a needle-like structure in which the acicular α phase and β phase are arranged in layers. In addition, in Comparative Examples 1 and 2 of alloy types N and O shown in Table 3, the average reduction rate (%) per pass in one or more passes from at least the final pass in the other processing steps is 16%. The drawing speed (m/sec) is 25m/sec. However, the Mo equivalent (Moeq) of Comparative Example 1 is less than -4.0. In Comparative Example 1, the metal structure of the outer peripheral region becomes the equiaxed structure of the α single phase, and the equiaxed structure of the α single phase is based on the α phase composed of equiaxed α grains, and there is almost no β Phase (there is a very small amount of β phase), the metal structure in the inner region becomes a kind of α phase with relatively small aspect ratio α crystal grains as the parent phase, and there is almost no β phase (the β phase is very small ) Of the organization. In more detail, the internal region of Comparative Example 1 has a structure in which the equiaxed β phase is finely dispersed in the massive α phase. In addition, the Mo equivalent (Moeq) of Comparative Example 2 was greater than 6.0. In Comparative Example 2, the metal structure in the outer peripheral region and the metal structure in the inner region both become the β single-phase equiaxed structure composed of equiaxed β grains. In addition, in Table 3, since the metal structure of the inner region of Comparative Examples 1 and 2 and the metal structure of the outer region of Comparative Example 2 are different from the equiaxed structure of the present invention, " ^* " is added to distinguish.

In Table 2 and Table 3, the fatigue strength is compared and evaluated for the alloy types A to O. Based on the fatigue strength of the examples of alloy types A to O shown in Table 2, the evaluation was performed using the following stages A to C. In addition, when the fatigue strength is equal to or higher than the reference fatigue strength, that is, the evaluations of A and B are passed.

A: Compared with the reference fatigue strength, it has increased by more than 10 MPa. B: Compared with the reference fatigue strength, there is a variation in the range of -10 MPa or more and less than 10 MPa. C: Compared with the reference fatigue strength, it is reduced by more than 10MPa and below 20MPa.

In addition, in Table 2 and Table 3, the creep strength (creep stress) was compared and evaluated for the examples of alloy types A to O. Based on the creep strength of the examples of alloy types A to O shown in Table 2, evaluations were made using the following stages A to C. In addition, when the intensity of creep change is increased compared with the reference creep intensity, that is, the evaluation of A and B is passed.

A: Compared with the reference creep strength, it has increased by more than 20MPa. B: Compared with the reference creep strength, it is improved by 10 MPa or more and less than 20 MPa. C: Compared with the reference creep strength, there is a variation in the range of -10 MPa or more and less than 10 MPa.

Regarding the alloy types A~O shown in Table 1, the titanium alloy wire rod obtained by the manufacturing method equivalent to the conventional manufacturing method is listed in Table 2: The metal structure of the peripheral region, the average aspect ratio of the α grains, The average crystal grain size, the metallic structure of the inner region, the average aspect ratio of the α grains, the area ratio of the acicular structure region, and the fatigue strength and creep strength that are the evaluation criteria. In addition, Table 3 lists the metal structure, the average aspect ratio of α grains, and the average crystallinity of the outer peripheral regions of Inventive Examples 1 to 31 (Alloy Types A to M) and Comparative Examples 1 and 2 (Alloy Types N and O) The grain size, the metal structure of the internal area, the average aspect ratio of the α grains, the area ratio of the acicular structure area, the fatigue strength and the evaluation result of the evaluation object, and the creep strength and the evaluation result of the evaluation object. In Invention Examples 1 to 31, the fatigue strength was evaluated as either A or B, and it was equal to or higher than the reference fatigue strength. In addition, in Inventive Examples 1 to 31, the evaluation of creep strength is either A or B, which is improved compared to the reference creep strength. On the other hand, the creep strength of Comparative Examples 1 and 2 was not sufficiently improved.

Next, in Table 4, the fatigue strength and creep strength are compared and evaluated for alloy types A, B, and C. The heating steps and processing steps of Inventive Examples 32 to 54 meet the present invention, while the metal structure of the outer peripheral region of the titanium alloy wire rods of Inventive Examples 32 to 54 becomes an equiaxed α phase as the parent phase and its grain boundaries and grains There is a fine β-phase equiaxed structure, and the metallic structure in the inner region becomes a needle-like α-phase and β-phase arranged in a layered needle-like structure. On the other hand, any of the heating steps or processing steps of Comparative Examples 3-10 is outside the scope of the present invention, and any of the following titanium alloy wires of Comparative Examples 3-10 falls outside the scope of the present invention: The metallic structure of the region, the average aspect ratio of α crystal grains, the average crystal grain size of α crystal grains, or the metallic structure of the internal zone, the average aspect ratio of α crystal grains. In addition, the wire diameters of Inventive Examples 32 to 54 are 1.5 mm to 22.0 mm. In addition, invention examples 32 to 50, 52, and 53 are examples that satisfy the wire diameters of 2.0 mm to 20.0 mm specified in claim 8.

Invention examples 32 to 48 and invention examples 51 to 54 are based on the fatigue strength and creep strength of the alloy type A in Table 2, and the invention example 49 is based on the fatigue strength and creep strength of the alloy type B in Table 2. Inventive example 50 is based on the fatigue strength and creep strength of the alloy type C example in Table 2, and evaluated using the stages A to C in the same way as above.

As shown in Table 4, the titanium alloy wires of Invention Examples 32 to 54 have both excellent fatigue strength and creep strength. In particular, in the titanium alloy wire rods of Inventive Examples 32 to 54, good results were obtained with respect to the creep strength system relative to the comparative example as a reference. In contrast, the titanium alloy wire rods of Comparative Examples 3 to 10 were unable to achieve excellent fatigue strength and creep strength at the same time.

In Comparative Example 3, the total shrinkage ratio is less than 90.0%, so the outer peripheral area becomes a structure that has not been equiaxed (not equiaxed), and the structure is changed to a certain degree in the aspect ratio and crystal grain size of the α grains. There is a small amount of fine β phase in the large α phase. In addition, in Comparative Example 3, the wire drawing speed is less than 5.0m/sec and the processing heat generation is small. Therefore, the internal region becomes a kind of α phase composed of equiaxed α crystal grains as the parent phase, and the β phase is finely dispersed in the α phase. The isometric organization. In Comparative Example 4, the average shrinkage rate of 1 or more passes from at least the final pass is less than 10.0%, and the processing heat generation is small, so the inner and outer areas are both a kind of equiaxed α grains The formed α phase is the parent phase and a small amount of β phase is finely dispersed in an equiaxed structure. In Comparative Example 5, the total shrinkage ratio is less than 90.0%, so the outer peripheral area becomes a structure that has not yet been equiaxed (not equiaxed), and the structure is a structure where the aspect ratio of the alpha grains has increased to some extent. There is a small amount of fine β phase in the phase, and the inner area becomes a needle-like α phase and β phase arranged in a layered needle-like structure. In Comparative Example 6, the wire drawing speed is less than 5.0m/sec and the processing heat generation is small. Therefore, both the inner region and the outer peripheral region become a kind of α phase composed of equiaxed α crystal grains as the parent phase, and the α phase is finely dispersed There is a small amount of isometric structure of β phase. In Comparative Example 7, the total shrinkage ratio is less than 90.0%, so the outer peripheral area becomes an equiaxed structure with the α phase composed of coarse equiaxed α grains as the parent phase and a small amount of β phase dispersed in the α phase. The area becomes a needle-like α-phase and β-phase arranged in a layered needle-like structure. In Comparative Example 8, due to the low heating temperature, both the inner region and the outer peripheral region have an equiaxed structure in which the α phase composed of equiaxed α crystal grains is used as the parent phase and a small amount of β phase is finely dispersed in the α phase. In Comparative Example 9, the total area reduction ratio is less than 90.0%, so the outer peripheral region becomes a structure that has not been equiaxed (not equiaxed), and the structure is changed to a certain degree in the aspect ratio and crystal grain size of the α grains. There is a small amount of fine β phase in the larger α phase, and the inner region becomes a needle-shaped α phase and β phase arranged in a layered needle-like structure. In Comparative Example 10, the total shrinkage ratio is less than 90.0%, so the outer peripheral area becomes a structure that has not been equiaxed (not equiaxed), and this structure is a small amount in the α phase whose aspect ratio has increased to some extent. The β phase is fine, and the inner region becomes a needle-like α phase and β phase arranged in a layered needle-like structure.

The titanium alloy wires of Invention Examples 32, 33, 36, 39-41, 45-52 in which the area ratio of the needle-like structure region including the center of gravity is greater than 40%, are particularly excellent in creep strength. In addition, the titanium alloy wires of Invention Examples 32 to 35, 39, 40, 42 to 44, 47 to 50, 53, and 54 in which the average particle size of the α grains in the outer peripheral region are 5.0 μm or less have excellent fatigue strength.

The preferred embodiments of the present invention have been described in detail above, but the present invention is not limited by these examples. Obviously, anyone with a general knowledge in the technical field of the present invention can think about various changes or amendments within the scope of the technical ideas described in the scope of the patent application, and know that these also belong to the present invention. The scope of technology.

1: Titanium alloy wire 2: Peripheral area 3: outer peripheral surface 4: Internal area 10: Grain boundary of α phase 11: Long axis 12: short axis 20,23: β grains 21: Needle-like alpha grains 22: Equiaxial alpha grains 24: Equiaxed fine α grains (fine equiaxed structure) 25: Needle-like alpha grains (needle-like structure) a: α grain b: β phase c: needle-shaped α d: equivalent to 3% depth e: Needle β G: Center of gravity L: length direction R: wire diameter T: β metamorphosis temperature

Fig. 1 is an explanatory diagram schematically showing an isometric organization. Fig. 2 is an explanatory diagram schematically showing a needle-like structure. Fig. 3 is a perspective cross-sectional view schematically showing a titanium alloy wire according to an embodiment of the present invention. Fig. 4 is an explanatory diagram schematically showing the state of specifying the major axis and the minor axis. 5(a) to 5(e) are explanatory diagrams schematically showing the process of manufacturing the titanium alloy wire of this embodiment in order.

Claims (10)

A titanium alloy wire containing α phase and β phase; The titanium alloy wire has the following chemical composition: In terms of mass %, Al: 0% or more and 7.0% or less, V: 0% or more and 6.0% or less, Mo: 0% or more and 7.0% or less, Cr: 0% or more and 7.0% or less, Zr: 0% or more and 5.0% or less, Sn: 0% or more and 3.0% or less, Si: 0% or more and 0.50% or less, Cu: 0% or more and 1.8% or less, Nb: 0% or more and 1.0% or less, Mn: 0% or more and 1.0% or less, Ni: 0% or more and 1.0% or less, S: 0% or more and 0.20% or less, REM: 0% or more and 0.20% or less, Fe: 0% or more and 2.10% or less, N: 0% or more and 0.050% or less, O: 0% or more and 0.250% or less, C: 0% or more and 0.100% or less and Remaining part: Ti and impurities, and The content of Al, Mo, V, Nb, Fe, Cr, Ni and Mn satisfies the following formula (1); In a cross section perpendicular to the length direction, in the outer peripheral area from the surface to the center of gravity to a depth of 3% of the wire diameter, the metal structure is an equiaxed structure with α grains with an average crystal grain size of 10 μm or less; and In the aforementioned cross-section perpendicular to the length direction, the metal structure is needle-like structure in the inner region including the center of gravity from the center of gravity to the surface to the position of 20% of the wire diameter; -4.00≦[Mo]+0.67[V]+0.28[Nb]+2.9[Fe]+1.6[Cr]+1.1[Ni]+1.6[Mn]-[Al]≦6.00　・・・(1) In addition, in the formula (1), the description of [element symbol] indicates the content (mass %) of the corresponding element symbol, and 0 is substituted for the element symbol that is not contained. For example, the titanium alloy wire of claim 1, which in mass% contains: Al: 4.5% or more and 6.5% or less and Fe: 0.50% or more and 2.10% or less. For example, the titanium alloy wire of claim 1, which in mass% contains: Al: 2.0% or more and 7.0% or less and V: 1.5% or more and 6.0% or less. For example, the titanium alloy wire of claim 1, which in mass% contains: Al: 5.0% or more and 7.0% or less, Mo: 1.0% or more and 7.0% or less, Zr: 3.0% or more and 5.0% or less and Sn: 1.0% or more and 3.0% or less. The titanium alloy wire rod of any one of claims 1 to 4, wherein in the cross section perpendicular to the length direction, the average aspect ratio of the α grains in the outer peripheral region is 1.0 or more and less than 3.0, and the inner region The average aspect ratio of the α grains is 5.0 or more. The titanium alloy wire of claim 5, wherein in the aforementioned cross section perpendicular to the length direction, the area of the region including the center of gravity with the average aspect ratio of the α grains of 5.0 or more is 40% or more relative to the cross-sectional area . The titanium alloy wire rod according to any one of claims 1 to 6, wherein the average crystal grain size of the α crystal grains in the outer peripheral region is 5.0 μm or less. For example, the titanium alloy wire of any one of claims 1 to 7, the wire diameter is 2.0 mm or more and 20.0 mm or less. A method for manufacturing titanium alloy wire rod, which has the following steps: The step of heating the titanium alloy blank to a temperature above (β transformation point -200)°C; and The aforementioned titanium alloy is processed according to the total shrinkage rate of 90.0% or more, the average shrinkage rate of each pass in more than 1 pass from at least the final pass is 10.0% or more, and the wire drawing speed is 5.0m/sec or more. The steps of the blank. For example, the method for manufacturing a titanium alloy wire of claim 9 further has a step of heat treatment in a temperature range of (β transformation point-300)°C or higher and (β transformation point-50)°C or lower.

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