Fabrication method for stepped forged material

Abstract

Provided is a method for fabricating a stepped forged material that can realize a uniform microscopic structure in both the large diameter flange portion and the small diameter shaft portion. This method for fabricating a stepped forged material comprises the following steps: a step for obtaining a primary forged material in which an austenite stainless steel billet is heated to 1000-1080 C., and, without any further heating, the material is forged by means of reciprocal forging into a round rod having along the entire length thereof a forging ratio of 1.5 or greater; a step for obtaining a secondary forged material, that forms the large diameter flange portion and the small diameter shaft portion, in which without reheating, the small diameter shaft portion is formed by means of reciprocal forging at a temperature where the surface temperature of the primary forged material never falls more than 200 C. lower than the abovementioned material heating temperature and the forging is completed before the surface temperature of the final forged portion falls more than 300 C. lower than the abovementioned heating temperature; and a step for performing a solution heat treatment in which the secondary forged material is heated to 1040-1100 C. for 30 minutes or longer.

Claims

1. A method for producing a stepped forged material, comprising the steps of: obtaining a primary forged material, wherein an austenite stainless steel billet for forging is heated to 1000-1080 C., and, without any further heating, the material is forged into a round rod having a forging ratio of 1.5 or greater along the entire length of the material by means of reciprocal forging of repeating a forging operation in which the material is delivered from one end to the other end in the axial direction with respect to a forging apparatus and thereafter delivered in the opposite direction; obtaining a secondary forged material formed to have a large diameter flange portion and a small diameter shaft portion, wherein without reheating, forging is started at a temperature before a surface temperature of the primary forged material falls more than 200 C. lower than the material heating temperature, and the small diameter shaft portion is formed by means of reciprocal forging of repeating a forging operation in which the primary forged material is delivered from one end in the axial direction to a predetermined position with respect to the forging apparatus and thereafter delivered in the opposite direction, and the forging is completed before a surface temperature of a final forged portion falls more than 300 C. lower than the material heating temperature; and performing a solution heat treatment, wherein the secondary forged material is heated to 1040-1100 C. for 30 minutes or longer.

2. The method for producing a stepped forged material according to claim 1, wherein a forging ratio to obtain the primary forged material is 1.5 to 1.9 and a forging ratio to obtain the small diameter shaft portion of the secondary forged material from the primary forged material is 3.0 or less.

3. The method for producing a stepped forged material according to claim 1, wherein the forging is performed by a radial forging apparatus, wherein forging from four orthogonal directions in the radial direction of a shaft of a forged material is executed simultaneously and the forged material is delivered to the axial direction while rotating the shaft.

4. The method for producing a stepped forged material according to claim 2, wherein the forging is performed by a radial forging apparatus, wherein forging from four orthogonal directions in the radial direction of a shaft of a forged material is executed simultaneously and the forged material is delivered to the axial direction while rotating the shaft.

Description

BRIEF DESCRIPTION OF DRAWINGS

(1) FIG. 1 is a drawing showing an example of a stepped forged material obtained by the method according to the present invention.

(2) FIG. 2 is a microscope structure photograph showing an example of grain size observation of a flange portion of a stepped forged material produced according to the present invention.

(3) FIG. 3 is a microscope structure photograph showing an example of grain size observation of a shaft portion of the stepped forged material produced according to the present invention.

(4) FIG. 4 is a microscope structure photograph showing an example of grain size observation of a flange portion of a stepped forged material produced according to a comparative example.

(5) FIG. 5 is a microscope structure photograph showing an example of grain size observation of a shaft portion of the stepped forged material produced according to a comparative example.

DESCRIPTION OF EMBODIMENTS

(6) As described above, the important feature of the present invention is to apply the step in which heating the flange portion is performed before forging and after that no heating is performed in a forging step, and to find out the forging condition compatible with this step. This feature will be explained in detail hereinafter.

(7) In the present invention, the intended material is austenite stainless steel. Austenite stainless steel is, among G4303 and G3214 of Japanese Industrial Standards for example, alloy with composition classified in austenite and its improved alloy.

(8) These austenite stainless steels are steel with limited low carbon and material with excellent corrosion resistance to be used as many machine parts in the field of aircrafts and nuclear power. Moreover, in the austenite stainless steel, since Cr carbide is deposited due to a small amount of carbon existing in a hot working step, a solution heat treatment for dissolving this to increase corrosion resistance needs to be applied. As the temperature of the solution heat treatment is higher than the recrystallization temperature, recrystallization occurs due to remained strain in the hot working step. Unless sufficient strain remains before the solution heat treatment, the structure becomes coarse and a uniform microscopic structure with excellent strength and toughness cannot be obtained.

(9) The present invention has found out a step of obtaining a uniform microscopic structure in this solution heat treatment that finally determines the structure.

(10) In the present invention, first, a billet for forging is heated to 1000 to 1080 C. and, without any further heating, the material is forged into a round rod having a forging ratio of 1.5 or greater along the entire length of the material by means of reciprocal forging of repeating a forging operation in which this material is delivered from one end toward the other end in the axial direction with respect to a forging apparatus and thereafter delivered in the opposite direction to obtain a primary forged material.

(11) In the present invention, if the heating temperature before the forging exceeds 1080 C., the heating temperature is so high that strain is released, which cannot cause sufficient strain to remain in the large diameter flange portion to be obtained in the forging. Moreover, when the heating temperature before the forging is less than 1000 C., the material cannot be softened sufficiently, so that cracking tends to occur in the forging. Further, grain size of the large diameter portion becomes non-uniform to be a mixed grain structure. Accordingly, in the present invention, the heating temperature is defined as 1000 to 1080 C.

(12) Moreover, in the present invention, when heating is performed during the forging step, strain is not a little released and a microscopic structure cannot be obtained in the solution heat treatment. Consequently, excluding heating in the forging step is a fundamental requirement in the present invention.

(13) Moreover, in the present invention, a forging operation in which the material is delivered from one end toward the other end in the axial direction with respect to the forging apparatus and thereafter delivered in the opposite direction is repeated. By forging with such reciprocal forging, the entire material can be uniformly forged. Thanks to the reciprocal forging, the forging time is shortened than that of a one-way forging, and forging can be performed within a constant temperature range to cause uniform strain to remain.

(14) As to the forging apparatus to be applied to the present invention, a radial forging apparatus is effective, in which forging is executed simultaneously from four orthogonal directions and in the radial direction of a shaft of a forged material, and the forged material is delivered to the axial direction while rotating the shaft. The reason is that the radial forging apparatus can simultaneously apply pressure from the four orthogonal directions and is more excellent than a two surface forging apparatus in forming the round rod shape.

(15) Moreover, in this step of determining the large diameter flange portion in the present invention, a forging ratio of 1.5 or greater is required to cause sufficient strain to remain.

(16) Additionally, excessive forging ratio means sizing up the original material, which is not efficient. As an upper limit of the forging ratio, 1.9 is preferable.

(17) Next, a secondary forged material that is formed to have the large diameter flange portion and the small diameter shaft portion is obtained. In this process, without reheating the obtained primary forged material, forging is started at a temperature before the surface temperature of the primary forged material falls more than 200 C. lower than the abovementioned material heating temperature, and the small diameter shaft portion is formed by means of reciprocal forging of repeating a forging operation in which the primary forged material is delivered from one end in the axial direction toward a predetermined position with respect to the forging apparatus and thereafter delivered in the opposite direction, and the forging is completed before the surface temperature of the final forged portion falls more than 300 C. lower than the abovementioned heating temperature.

(18) In obtaining the secondary forged material, when the forging temperature is lowered to be significantly different from the forging temperature condition for obtaining the primary forged material forming the flange portion, a problem of forging defect due to ductility deterioration occurs. To avoid this, in the present invention, in the step of obtaining the secondary forged material forming the small diameter shaft portion, forging is started at a temperature before the surface temperature of the primary forged material falls more than 200 C. lower than the abovementioned material heating temperature, and the forging is completed before the surface temperature falls more than 300 C. lower than the abovementioned heating temperature.

(19) In the step of obtaining the secondary forged material, the reason why the same reciprocal forging as in the step of obtaining the primary forged material is applied is to cause uniform strain to remain.

(20) Moreover, in the abovementioned step of determining the small diameter shaft portion of the present invention, a forging ratio from an end surface of the round rod material to the predetermined position is preferably 3.0 or less. When the forging ratio becomes too large, defect and cracking, etc. tend to occur. Consequently, in the present invention, a forging ratio from the end surface of the billet to the predetermined position is 3.0 or less.

(21) Additionally, here, a forging ratio refers to a forging ratio from the round rod material.

(22) Next, a solution heat treatment is performed, in which the secondary forged material is heated at 1040 to 1100 C. for 30 minutes or more. As described above, this step of solution heat treatment is an important step to solve Cr carbide and to increase corrosion resistance. If the temperature of the solution heat treatment is low, recrystallization is not sufficiently advanced and miniaturization of crystal grain is difficult. On the other hand, if the temperature of the solution heat treatment is high, crystal grain becomes non-uniform and miniaturization of crystal grain is difficult. The time for the solution heat treatment is required to be 30 minutes or more.

EXAMPLE

(23) The present invention will be explained in more detail with the following example.

(24) A stepped forged material shown in FIG. 1 was produced from a billet for forging made of JIS G3214 SUS316 steel. First, an octagonal forging material of 320 mm1700 mmL was heated to 1050 C., and without any further heating, forging was started in a radial forging apparatus. The used radial forging apparatus included ram cylinders in four directions, which execute forging with a feeding speed of 50 mm for one stroke and a rotation angle of 30.

(25) By repeating a forging operation in which the abovementioned material was delivered from one end to the other end in the axial direction with respect to the radial forging apparatus and thereafter delivered in the opposite direction, the entire length of the abovementioned material was subjected to reciprocal forging with a forging ratio of 1.6 to obtain a primary forged material with the diameter of 260 mm and the length of 2700 mm.

(26) Next, without reheating, a forging was started with the surface temperature of the primary forged material being a temperature shown in Table 1, and by reciprocal forging of repeating a forging operation in which the material is delivered from one end in the axial direction to a three-quarter position in the longitudinal direction with respect to the forging apparatus and thereafter delivered in the opposite direction, a small diameter shaft portion with the diameter of 170 mm and a forging ratio of 2.3 to the primary forged material was formed. At this time, the forging was completed before the surface temperature of the final forged portion became the temperature shown in Table 1 to obtain the secondary forged material according to the present invention.

(27) TABLE-US-00001 TABLE 1 Forging start Forging completion No Temperature ( C.) Temperature ( C.) 1 900 840 2 856 812 3 879 812 4 877 822 5 906 823 6 907 847 7 902 842 8 905 849 9 907 850 10 902 842

(28) Moreover, as a comparative example, after obtaining the primary forged material in the same manner as the present invention, reheating was performed by holding the heating at 1050 C. for 3 hours, and then forging of forming the small diameter shaft portion was started. The subsequent forging condition was the same as in the present invention and the secondary forged material of the comparative example was obtained.

(29) The obtained secondary forged materials according to the present invention and the comparative example were subjected to a solution heat treatment holding at 1050 C. for 120 minutes to obtain stepped forged materials.

(30) FIG. 1 shows a schematic diagram of the obtained stepped forged material. From portion A and portion B shown in FIG. 1, a metal structure observation test piece was respectively obtained. Table 1 shows average grain size numbers of the present invention and the comparative example, and FIGS. 2 to 5 show photographs of representative (the present invention No. 1 and the comparative example) metal structures.

(31) TABLE-US-00002 TABLE 2 A Flange B Shaft portion grain portion grain size number size number The present invention No. 1 4.5 4.5 The present invention No. 2 4.0 4.0 The present invention No. 3 3.5 4.0 The present invention No. 4 4.0 4.0 The present invention No. 5 4.0 4.0 The present invention No. 6 4.0 4.0 The present invention No. 7 4.0 4.0 The present invention No. 8 4.0 4.0 The present invention No. 9 4.0 4.0 The present invention No. 10 4.0 4.0 Comparative example 2.0 3.5

(32) As shown in Table 2, FIGS. 2 and 3, in the present invention, the large diameter flange portion whose structure tends to be coarse had a uniform microscopic structure, and the small diameter shaft portion also had a uniform microscopic structure. Moreover, occurrence of forging defect was not confirmed.

(33) On the other hand, in the comparative example, as shown in Table 2 and FIGS. 4 and 5, the grain size of the flange portion was coarse to be 2.0. Moreover, the grain size of the shaft portion was coarse compared to the present invention and wide variation was confirmed, and accordingly, an inferior structure to the present invention was obtained.

REFERENCE SIGNS LIST

(34) 1 flange portion 2 shaft portion