A METHOD OF MANUFACTURING A CLAD BAR

Abstract: A columnar core member (11) is fitted in a cylindrical outside lay­ er member (12) and the resulting assembly is heated (20), and then the heated assembly is rolled by a rotary mill (4) provided with three or more cone type rolls (1, 2) to integrate the core member (11) and the outside layer member (12). In order to prevent unnecessary substances, such as oxides, from being formed on an interface between the core member and the outside layer member, the assembly is tightly welded at both ends under reduced press­ ure or under vacuum or the assembly is cold drawn, the as­ sembly thus welded or cold drawn is then heated and subsequ­ ently rolled by a rotary mill. Thus, an intermetallic com­ pound layer formed between the core member and the outside layer member can be thinned, whereby improving bond strength.

Description: The present invention relates to a method of manufac­ turing a clad bar comprising an inner layer and an outer layer formed of two kinds of metal. A clad bar comprising a core member and an outer layer member coated on an outside of said core member to utilize mechanical properties of the core member and a corrosion-­ resistance, abrasion-resistance and beautiful external ap­ pearance of the outer layer member has been known. The fol­ lowing methods of manufacturing a clad bar have been known. <1>Japanese Patent Laid-Open No. 141313/1980 This relates to a method in which a core member is fitted in a cylindrical outer layer member, the resulting assembly being subjected to a cold drawing to closely con­ tact the outer layer member to the core member, and then the cold drawn assembly being heated followed by rolling by grooved rolls. With this method, a brittle layer of inter­ metallic compounds is formed at the bonding interface between the core member and the outer layer member, whereby the sufficient bond strength cannot be attained. <2> Japanese Patent Laid-Open No. 160551/1979 This relates to a method in which a core member is fitted in a cylindrical outer layer member, the resulting assembly being subjected to a cold drawing, and then annealed to bring about the diffusion through the boundary surface, whereby carrying out the bond. With this method, since intermetallic compounds formed by the diffusion are brittle and weak, the bond strength is reduced. <3> Japanese Patent Laid-Open No. 110486/1984 This relates to a method in which a core member is fitted in a cylindrical outer member, the resulting assembly being subjected to a cold reduction, a disk formed of the same material as the outer layer member being welded to both end faces of the reduced assembly by the friction welding to seal up a gap between the core member and the outer layer member, and then assembly being heated followed by being subjected to a hot rolling by grooved rolls or hot extru­ sion. With this method, the rolling is alternately carried out in a direction different 90° to each other in the hot rolling by the grooved rolls, so that a portion subjected to the compression in one rolling receives a tensile force in a radial direction in the subsequent rolling, whereby bringing out the separation of the outer layer member from the core member at the bonding interface therebetween. In addition, the hot extrusion does not lead to the attainment of the sufficient bond strength. <4> Japanese Patent Laid-Open No. 103928/1983 This relates to a method in which a core member is fitted in a cylindrical outer layer member, and then merely the outer layer member is reduced by means of a die so that the core member may not be deformed. With this method, since a heating is not applied, a diffusion layer is not formed in the bonding interface between the core member and the outer layer member, that is, the core member and the outer layer member are not integrated with each other. As a result, the bonding strength is reduced. <5> Japanese Patent Publication No. 8188/1979 This relates to a method in which a core member is fitted in an outer layer member, and then both members are simultaneously elongated by the hydrostatic extrusion method to carry out the bond. With this method, not only the bond strength is not sufficient, but also a length of a product capable of manufacturing has an upper limit since it is nec­ essary to increase an elongation rate in the event that a long product is manufactured. In addition, this method is complicated in comparison with the methods <1> to <4>. Besides, in a rolling method using a grooved roll as in the methods <1> and <3>, a sectional shape of the core mem­ ber after rolling becomes quite different from a circular shape, so that a thickness of the outer layer member becomes uneven. Accordingly, disadvantages occur in the exposure of the core member in the subsequent turning process and the like. As described above, with the conventional methods, no sufficient bond strength has been attained. Accordingly, the development of a method of manufacturing a clad bar, to which a superior bond strength is required, has been expect­ ed. A first object of this invention is to provide a method of manufacturing a clad bar capable of attaining the high bond strength by carrying out a hot rolling using a rotary mill. A second object of this invention is to provide a meth­ od of manufacturing a clad bar capable of attaining the still higher bond strength by sealing up a gap between a core member and an outer layer member under reduced pressure or under vacuum in order to prevent the oxidation in an bonding interface resulting from the heating. A third object of this invention is to provide a method of manufacturing a clad bar capable of preventing the oxida­ tion in the bonding interface when heated even in the case where a coefficient of thermal expansion of an outer layer member is larger than that of a core member. A forth object of this invention is to provide a method of manufacturing a clad bar capable of attaining the still higher bond strength by carrying out a cold drawing prior to the heating to eliminate a gap between an outer layer member and a core member. A fifth object of this invention is to provide a method of manufacturing a clad bar capable of making a thickness of an outer layer member uniform. The purport of the present invention consists in that an assembly comprising a core member and an outer layer mem­ ber fitted said core member therein is heated, and then sub­ jected to a rolling by a rotary mill having three or more cone type rolls to bond both members to each other. In order to make the hot rolling progress smooth, both members are fixed at an end of the assembly and in order to prevent the oxidation in the bonding interface when heated, the gap between both members of the assembly is sealed up under reduced pressure or under vacuum. In the case that a coefficient of thermal expansion of the outer layer member is larger than that of the core member, this sealing up process is indispensable. In addition, in order to attain the still higher bond strength, a cold drawing is carried out prior to the hot rolling so as to eliminate the gap between the outer layer member and the core member. The above and further objects and features of the invention will more fully be apparent from the following detailed description with accompanying drawings. Fig. 1 is a sectional view showing an assembly; Fig. 2 is a side view showing the assembly; Fig. 3 is a schematic side view showing a rotary mill used in a method according to the present invention; Fig. 4 is a sectional view of Fig. 3 taken along a line IV-IV thereof; Fig. 5 is a rough side view showing a feed angle β; Fig. 6 is a schematic diagram showing a state of gener­ ating the flaring; Fig. 7 is a sectional view showing a clad bar manufac­ tured by rolling using a grooved roll; Fig. 8 is a graph showing an appearance of bonding of a clad bar manufactured by a method according to the present invention; Fig. 9 is a diagram showing a test method of shear strength; Fig. 10 is a graph showing investigation results of shear strength (a graph showing a relation between a heating temperature and a shear strength of a titanium-clad copper rod); Fig. 11 is a SEM (scanning electron microscope) photo­ graph of a bonding interface between a core member and an outer layer member of a titanium-clad copper rod manufactur­ ed by a method according to the present invention; Fig. 12 is a SEM photograph of a bonding interface be­ tween a core member and an outer layer member of a titanium-­ clad copper rod manufactured by means of a grooved roll; Fig. 13 is a graph showing a relation between a heating temperature and a shear strength of a stainless steel-clad copper rod; Fig. 14 is a schematic side section view of a rotary mill used in a method according to the present invention (taken along a line XIV-XIV of Fig. 15); Fig. 15 is a front view of Fig. 14 taken along a line XV-XV thereof; Fig. 16 is a side view showing a roll; Fig. 17 is a sectional view showing an assembly used in a sixth preferred embodiment; Fig. 18 is a side view of Fig. 17; Fig. 19 is a progress chart of a sixth preferred em­ bodiment; Fig. 20 is a SEM photograph showing a bonding interface between a core member and an outer layer member; Fig. 21 is a graph showing an EPMA (electron probe micro analysis) results; Fig. 22 is an end view showing an assembly used in an eighth preferred embodiment; Fig. 23 is a side section view showing an assembly used in an eighth preferred embodiment; Fig. 24 is a graph showing a shear strength in an eighth preferred embodiment; Fig. 25 is a side section view showing an assembly in another preferred embodiment; and Fig. 26 is a SEM photograph showing a bonding interface in a ninth preferred embodiment. The present invention is fundamentally characterized in that an assembly is elongated in a rotary mill having three or more cone type rolls after heating. The first preferred embodiment, which will be below described, comprises merely these fundamental characteristics, in short, comprises mere­ ly a process in which a core member is fitted in an outer layer member and then the resulting assembly is elongated after heating. As shown in Figs. 1 and 2, an assembly 10 is round rod-­ like and comprises a cylindrical outer layer member 12 put on a periphery of a core member 11 having a circular sec­ tion. This assembly is heated in a heating furnace (not shown) and then transferred in a rotary mill which permits high reduction. Fig. 3 shows the principal parts of a rotary mill 4 used in the present invention, rolls 1 and 2 being shown in a sectional view taken along line III-III of Fig. 4. The rotary mill 4 has three cone type rolls 1, 2, 3 arranged around a pass line, said three rolls 1, 2, 3 being provided with gorged portions 1a, 2a, 3a, respectively, at an outlet side (larger diameter side) end portion of the assembly 10, an inlet side (smaller diameter side) of the assembly 10 forming inlet faces 1b, 2b, 3b having a diameter gradually reduced toward an axial end with the gorged portions as boundaries, an outlet side of the assembly 10 forming outlet faces 1c, 2c, 3c having an inclination smaller than that of the inlet faces 1b, 2b, 3b, and a distance between the out­ let faces 1c, 2c, 3c and the pass line being made equal to that between the gorged portions 1a, 2a, 3a and the pass line. Such cone type rolls 1, 2, 3 are all arranged so that the inlet faces 1b, 2b, 3b thereof may be positioned in an upstream side of a transfer direction of the assembly 10 and intersecting point O (hereinafter referred to as a roll-ar­ ranging centre) of an axis shaft line Y-Y and planes includ­ ing the gorged portions 1a, 2a, 3a may be positioned around the pass line X-X at regular intervals on the same one plane meeting at right angles with the pass line X-X of the assem­ bly 10. And, the axis shaft line Y-Y of each roll 1, 2, 3 is inclined by a cross angle of γ around the roll-arranging centre so that a forward axial end may approach toward the pass line X-X, as shown in Fig. 3, and said forward axial end is inclined by a feed angle of β toward the same one side of a circumferential direction of the assembly 10, as shown in Figs. 4, 5. The rolls, 1, 2, 3 are connected with a driving device (not shown) and are rotated in the same one direction, as shown by an arrow in Fig. 4. The hot assembly 10 threaded among the rolls are moved forward in the axial direction while being rotated on its axis, that is, it is forced to make a spiral progressive movement. The assembly 10 is reduced in outside diameter by a bite portion A of the roll under such high reduction as at a reduction in area of 25 % or more but at most 80 to 90 % while it is forced to make the spiral progressive movement among the rolls so that an outside surface B of rolling por­ tion of the assembly 10 may be formed in a frustum conical shape, as shown in Fig. 3, and then turned into a round clad bar 13 having an appointed outside diameter in the gorged portion and the outlet face. This rolling is not limited to one pass. Two or more passes may be carried out. A method of the present invention will be below de­ scribed more concretely. The assembly 10 is formed by degreasing and cleaning an outside surface of a core member 11 having a circular sec­ tion and an inside surface of a cylindrical outside layer member 12 having an inside diameter nearly equal to an out­ side diameter of the core member 11 to remove oils and the like hindering the diffusion and fitting the core member 11 in the outside layer member 12. The outside layer member 12 is preferably made of a material having a deformation re­ sistance larger than that of the core member 11, if pos­ sible. Subsequently, the assembly 10 is heated to form a dif­ fusion layer on the above described interface, whereby bond­ ing the outside surface of the core member 11 to the inside surface of the outside layer member 12. A heating tempera­ ture is selected at lower than melting points of the core member 11, the outside layer member 12 and the intermetallic compounds thereof. Because if even one of the core member 11 and the outside layer member 12 is molten, its solidifi­ cation leads to the generation of cracks there, whereby re­ ducing the bond strength. In addition, this heating tempe­ rature is selected in view of a quantity of heat generated during the rolling under high reduction. The assembly 10, which was heated in this manner, is elongated by means of a rotary mill 4. The rolling conditions by the rotary mill 4 are select­ ed in dependence upon a diameter, deformation resistance and the like of the assembly 10 but the cross angle γ is se­ lected at 0-15° and the feed angle β is selected at 6-­ 20°. Next, the facilities used and operating conditions are described below. At first, a reason why the rotary mill 4 is used, is described. This is because the bond strength, which has been wanting in the conventional grooved rolling, is in­ creased. In the grooved rolling, a plurality of pairs of grooved rolls having a pressing direction different 90° to each other are provided along the pass line, so that in the rolling by means of a pair of grooved rolls, the assembly 10 exhibits portions restricted by the rolls and portions which are not restricted by the rolls. Provided that in the portions, which are not restricted by the rolls, a strain of the core member 11 in the direc­ tion of elongation due to the rolling is ε z1 , a strain of the core member 11 in a direction vertical to the direction of elongation (in the radial direction) due to the rolling is ε r1 , a strain of the outside layer member 12 in the di­ rection of elongation due to the rolling is ε z2 , and a strain of the outside layer member 12 in the direction verti­ cal to the direction of elongation (in the radial direction) due to the rolling is ε r2 . If the core member 11 and the outside layer member 12 are rolled at the same time, ε z1 >ε z2 holds good in the event that the core member 1 is smaller than the outside layer member 12 in deformation resistance. However, since the volume is constant even though the deformation occurs by the rolling, the following equation hold good. ε z1 + ε o1 + ε r1 = 0 whereby ε o1 represents a strain in a peripheral direction of the core member. ε z2 + ε o2 + ε r2 = 0 whereby ε o2 represents a strain in a peripheral direction of the outside layer member. Provided that ε o1 ≒ ε o2 , ε r1 <ε r2 holds good. T is, the strain of the outside layer member 12 in the direc­ tion vertical to the direction of elongation (in the radial direction) becomes larger than that of the core member 11, whereby generating a radial tensile stress on an interface between the outside layer member 12 and the core member 11. In short, a portion compressed in the rolling by means of a certain pair of grooved roll becomes a non-restricted por­ tion in the rolling by means of a next pair of grooved roll different 90° in pressing direction to receive the above described tensile stress, so that the separation is apt to be generated. In addition, a cross section of the clad bar subjected to the grooved rolling is formed of four projections E ar­ ranged at regular intervals in a peripheral direction of the core member 11 and a wall-thickness of the outside layer member 12 is reduced at such four portions, that is, it be­ comes uneven, as shown in Fig. 7. On the contrary, in the case where the rotary mill is used, as obvious from Figs. 3, 4, 6, the restricted portions and the non-restricted portions are formed on the same one peripheral portions of the assembly but the assembly makes a spiral progress among the rolls, so that the tensile stress is not acted upon the portions which receive the compression pressure. Accordingly, in the case where the rotary mill is used, the tensile stress, which is generated in the above describ­ ed grooved rolling, is not generated. This is advantageous to the bond of the boundary interface. In addition, in the case where the rotary mill is used, a maximum reduction in area of 80-90 % per pass can be attained. And, as a result, a working heat is generated in the assembly 10 heated at the above described low temperature to promote the diffusion. Besides, even though the intermetallic compounds are formed, a thickness of the formed intermetallic compound layer can be reduced by rolling under high reduction, whereby produc­ ing a clad bar 13 superior in bond strength. Furthermore, it is a reason why a rotary mill having three or more cone type rolls is used that internal cracks due to "Mannesmann effect", which are generated in the central portion of a rod to be rolled when an rotary mill having two rolls is used, can be prevented from generating when the rotary mill having three or more rolls used. The above described rolls have a structure supported at both ends. This is because such a structure can lead to an accuracy of size of outside diameter within ±0.1 % but a structure supported at one-end leads to the deterioration of dimensional accuracy of outside diameter to ± 0.7 % on ac­ count of the decrease of mill rigidity and an influence of slip along the interface between both metals of an assembly to be rolled. Accordingly, the structure supported at both ends is preferably used. Next, a cross angle γ is described. U. S. Patent Application No. 508,720, British Patent Application No. 83-17789, Canadian Patent Application No. 431,444 and Australian Patent Application No. 16285/83 re­ late to a method of manufacturing a bar in high efficiency without generating internal cracks, in which a cross type rotary mill having three or more rolls is used. According to the invention of these patent applications, a dimension­ al accuracy of outside diameter is dependent upon a cross angle γ. In the case of γ>0°, the accuracy is ± 0.05 to ±0.1 %. In the case of γ=0°, the accuracy is ± 0.17 %. In the case of γ<0°, the accuracy is ± 0.4 % to ±0.75 %. The similar tendency appears also in the rolling proc­ ess in the present invention but in the case of a clad bar, the degree of change in outside diameter becomes the degree of change in thickness of an outside layer member, so that it is necessary to suppress this degree of change in outside diameter as far as possible in the case where the outside layer member is thin, in the case where the outside layer member is machined by turning in the subsequent process, and the like. Otherwise, the core member is exposed according to circumstances. Accordingly, γ≧0° is selected in the case where the outside layer is thin, in the case where the outside layer member is machined by turning in the subsequent process, and the like. On the other hand, an upper limit of γ is 15° in view of a limit of a design of chocks holding a roll shaft in a structure supported at both ends. Next, a feed angel β is described. A rolling speed v is calculated by the following equation: v = πD×(N/60)×sinβ×η (m/s) wherein D: a diameter of gorged portions (m) N: a rotational frequency of roll (rpm) η: advancing factor (0.7 to 1.5 in dependence upon the surface state of a roll and the like) In view of the oscillation of a rod to be rolled, an upper limit of rotational frequency of a roll is 250 rpm. It is required for attainment of a certain extent of rolling speed to maintain a feed angle β at a certain magnitude. A lower limit of the feed angle β is 6°. On the other hand, a length of a portion, on which the rod to be rolled is brought into contact with the roll is reduced with an increase of the feed angle β and a quantity of the reduced diameter in the spiral movement direction of the rod to be rolled is increase, whereby a slipping phenom­ enon appears on the interface between both metals of the rod (assembly) to be rolled. If the feed angle becomes 20° or more, the dimensional accuracy of outside diameter becomes ± 0.4 % or more. Accordingly, the upper limit of β is preferably selected at 20°. Next, a reason why the reduction in area is preferably selected at 25 % or more is described. In order to obtain a sufficient bond on the interface between the core member and the outside layer member, a higher reduction in area is preferably selected. According to Japanese Industrial Standards (JIS) G3604, a shear strength of 10 kgf/mm² is required for copper (copper alloys) - clad steels. In the case where the core member is copper and the outside layer member is stainless steel, a shear strength of 19.2 kgf/mm² is obtained at a reduction in area of 26.5 %. In addition, in the case where the core member is cop­ per and the outside layer member is titanium, a shear strength of 10.0 kgf/mm² is obtained at a reduction in area of 25 %. A reduction in area of 25 % or more is preferably selected on the basis of the above described actual results. Next, a reason why the outside layer member is prefer­ ably larger than the core member in deformation resistance will be described. If a deformation resistance of the out­ side layer member is smaller than that of the core member, the outside layer member 12a is deformed more greatly than the core member 11 to reduce a wall-thickness thereof. Thus, as shown in Fig. 6, a wall-thickness is reduced, and a peripheral length gets longer, whereby the lengthened por­ tion is jutted out to a gap between rolls to generate the flaring. As a result, a gap C is generated between the core member 11 and the outside layer member 12a, whereby the dif­ fusion layer of both metals, which have been already formed by heating, is separated. In order to prevent this, the outside layer member is preferably larger than the core member in deformation resistance. Next, relations among the reduction in area, heating temperature and shear strength of a bonded portion, and the like will be described below with reference to the preferred embodiments. (First Example) Core member: outside diameter: 49 mm (accuracy: -0.1 to +0.0 mm) material: pure Al (JIS 1070) Outside layer member: outside diameter: 55 mm inside diameter: 49 mm (accuracy: 0.0 to +0.1 mm) material: pure Ti (JIS Grade 2) These core member and outside layer member were produc­ ed by machining and degreasing and then, cleaned. Subseq­ uently, the core member was fitted in the outside layer mem­ ber. The resulting assembly was heated at 400°C, 500°C and 600°C, respectively, for an hour, and the heated assembly was elongated by a rotary mill at a reduction in area of 20%, 30%, 40%, 60% and 80%. In the rotary mill, cross angle (γ): 5°, feed angle (β): 13°, diameter of roll: 120mm, material of roll: SCM440, rotational frequency of roll: 100rpm. Fig. 8 shows an appearance of bonding between the core member and the outside layer member on a cutting plane after cutting clad bars produced at various heating temperature and reductions in area by means of a shearing machine. The heating temperature (°C) is taken on an abscissa and the reduction in area (%) is taken on an ordinate. ○ shows a good appearance while x shows a bad appearance. As under­ stood from Fig. 8, if the reduction in area is 30 % or more, a titanium-clad aluminium bar exhibiting a good bond strength can be manufactured. In addition, the bonding interface was observed by a scanning electron microscope (SEM), and electron probe micro analysis (EPMA) and an ultrasonic test to find no separa­ tion, oxide nor defect. A titanium-clad aluminium bar was manufactured by the grooved rolling for comparison. The assembly, which was produced in the same manner as the above described, was heat­ ed at 600°C and then continuously rolled form an outside di­ ameter of 55 mm to that of 30 mm after six passes (an aver­ age reduction in area per pass was 18 %). Such a clad bar manufactured by the grooved rolling exhibited the separation of the outside layer member from the core member on the cut­ ting plane after cutting by a shearing machine as visually observed. In addition, the separation was found at several places by observation of a SEM. (Second Example) <1> Core member: pure Cu [tough pitch copper (JIS C 1100)] Outside layer member: pure Ti (JIS Grade 2) <2> Core member: pure Cu [tough pitch copper (JIS C 1100)] Outside layer member: Ti-6Al-4V The assemblies were produced from the above described com­ binations of core member and outside layer member in the same manner as in First Example and heated at 600°C, 700°C and 800°C, respectively, for an hour. Subsequently, the heated assembly was elongated by means of a rotary mill in the same manner as in First Example. In addition, as for titanium/copper assembly <1>, a part of assembly was reduced in outside diameter by 2 mm by means of a die and then sub­ jected to a hot elongating. That is, two kinds of clad bar comprising the core member and the outside layer member dif­ ferent in material and one kind of clad bar different in manufacturing method, ie., three kinds of clad bar were manufactured. Second Example is different from First Example in addition of the drawing by means of a die. In order to investigate the bond strength of the manu­ factured clad bar, every two test pieces having a portion of an appointed length h from one end side of a test piece hav­ ing an appointed length left as it was and the other end side formed in the form of column having an outside diameter smaller than that of the core member, as shown in Fig. 9, were prepared for each clad bar to be investigated. The pressure was given from the other end side under the condi­ tion that the outside layer member portion of one end side of the test piece was engaged with an edge portion of a cir­ cular opening portion having a diameter slightly larger than an outside diameter of the core member to measure a load P at which the core member and the outside layer member were fractured. The measured value was put in the following equation (2) to obtain a shear strength. Shear strength = P/(π·D·h) ···(2) wherein D: outside diameter of the core member Fig. 10 collectively shows the investigation results of shear strength of clad bars manufactured at various heating temperatures and reductions in area. The heating tempera­ ture (°C) was taken on an abscissa and the share strength (kgf/mm²) was taken on an ordinate. As for three kinds of clad bar different in material and manufacturing method clad bars manufactured at the same one heating temperature and reduction in area, they showed a nearly same shear strength, so that an average value was shown for them. Referring to Fig. 10, ▪ marks, Δ marks, ▴ marks, ○ marks and  marks represent a reduction in area of 20 %, 30 %, 40 %, 60 % and 80 %, respectively. As understood from Fig. 10, it is nec­ essary for attainment of a shear strength of 10 kgf/mm² to select the reduction in area of 30 % or more. In addition, the bonding interface was observed by a SEM, EPMA and ultrasonic test to find no separation, oxide nor defect. Titanium/copper assembly produced in the same manner as in First Example was heated at 800°C and then subjected to the grooved rolling for comparison. The measured value of shear strength of the manufactured clad bar amounted to 6.5 kgf/mm² which was lower than the reference value. Fig. 11 is a photograph of a bonding interface of a clad bar manufactured according to the present invention at a reduction in area of 80 % taken by means of a SEM while Fig. 12 is a photograph of a bonding interface of a clad bar manufactured by the grooved rolling for comparison taken by means of a SEM likewise. As understood from both these photographs, cracks were found on an interface between the diffusion layer and the copper side and the existence of the separation in the clad bar was confirmed in the case of the Comparative Example. On the contrary, no separation was found in the case according to the present invention. (Third Example) Core member: pure Cu [tough pitch copper (JIS C 1100)] Outside layer member: stainless steel (JIS SUS304) An assembly comprising the core member and the outside layer member was manufactured in the same manner as in First Example and heated at 900°C, 950°C and 1,000°C, respective­ ly, for an hour. Then, the heated assembly was elongated by means of a rotary mill in the same manner as in First Exam­ ple. In addition, a part of the manufactured assemblies was drawn by means of a die in outside diameter by 2 mm and then elongated in the same manner as above described. And, every two test pieces as shown in Fig. 9 were prepared from each of the manufactured clad bars and measured on the shear strength. Fig. 13 is a graph collectively showing the measurement results of shear strength of the clad bars manufactured at various heating temperatures and reductions in area. The heating temperature (°C) was taken on an abscissa and the shear strength (kgf/mm²) was taken on an ordinate. As for two kinds of clad bar different in manufacturing method com­ posite bodies manufactured by the same heating temperature and reduction in area, they showed a nearly same value of shear strength, so that an average value was shown for them. Marks in Fig. 13 represent the same reductions in area as in Example 2. As understood from Fig. 13, if 10 kgf/mm² is used as a minimum reference of shear strength similarly as in Example 2, the shear strength of the reference value or more can be obtained by selecting the reduction in area at 30 % or more. The satisfactory shear strength, in short, the satisfactory bond strength, can be attained. In addition, there was nothing unusual as for the bonding interface, too. Besides, although the assembly comprising two kinds of metal put one on the other was heated as it was and then subjected to the elongation by means of a rotary mill or the assembly was subjected to a cold drawing and then heated followed by subjecting to the elongating in the rotary mill in the above description, an assembly comprising two kinds of metal and an intermediate layer put therebetween may be heated and then subjected to the elongating in the rotary mill. (Fourth Example) In this Example an outside layer member and a core mem­ ber are joined together and restricted at one end of the as­ sembly comprising the outside member and the core mem­ ber by means of mechanical or metallurgical means not so as to relatively move and then at least the outside layer mem­ ber is heated and a wall-thickness of the outside layer mem­ ber is reduced from one end side of the assembly to bond the outside layer member on the core member. The detailed description will be given below. As shown in Fig. 14, an assembly 10 is a stepped col­ umnar member and comprises a nearly columnar core member 11 provided with a skidproof restrictive member 11a having one end portion of slightly larger diameter and cylindrical out­ side layer member 12 having a length shorter than that of the core member 11 put on the core member 11 so as to be en­ gaged with the restrictive member 11a, and heated by means of a high-frequency heating coil 20 and then transferred in a longitudinal direction (a direction shown by a white ar­ row) toward a rotary mill 4. The rotary mill 4 is provided with three rolls 1, 2, 3 having a hump arranged around a pass line, said rolls 1, 2, 3 each having a diameter gradually increasing from an inlet side toward an outlet side, and with inlet faces 1b, 2b, 3b and the subsequent outlet faces 1c, 2c, 3c provided with hump portions 1d, 2d, 3d having a large face angle, outlet reeling portions and relief portions. The rolls 1, 2, 3 have a cross angle γ and a feed an­ gle β respectively, as shown in Figs. 14, 16. The rolls 1, 2, 3 are connected with a driving device (not shown) and ro­ tated in the same one direction, as shown by an arrow in Fig. 2. The hot assembly 10 rolled in among these rolls is transferred in a longitudinal direction with being rotated on the pass line, that is, it is forced to make a spiral progressive movement. The assembly 10 is reduced in outside diameter of the outside layer member 12 by the inlet inclined portions 1b, 2b, 3b and the roll hump portions 1d, 2d, 3d at, for exam­ ple, a maximum reduction in area of 80 to 90 % while it is forced to make the spiral progressive movement among the rolls so that the outside layer member 12 may be formed in a stepped frustum conical shape, as shown in Fig. 14, and then turned into a clad bar 13 having an appointed outside diame­ ter at the outlet faces 1c, 2c, 3c. This Example will be below described in more detail. The core member 11 is columnar and provided with the restrictive member 11a having a slightly larger diameter at one end portion thereof. The outside layer member 12 is cy­ lindrical having an inside diameter equal to an outside dia­ meter of the core member 11 or slightly larger than the out­ side diameter of the core member 11. An outside surface of the core member 11 and an inside surface of the outside lay­ er member 12 are degreased and cleaned and then, the core member 11 is put in the inside of the outside layer member 12 so as to be engaged with the restrictive member 11a to obtain the assembly 10. The above described cleaning aims at the formation of a diffusion through the boundary surface between the core mem­ ber 11 and the outside layer member 12 during the rolling. The interface must be maintained clean so that the diffusion may not be hindered even during the heating and rolling. Subsequently, the assembly 10 is passed through the high-frequency heating coil 20. A frequency of the high-­ frequency heating coil 20 is set so as to heat merely the outside layer member 12 of the assembly 10. Accordingly, merely the outside layer member 12 is heated here and then the assembly 10 is rolled in among the rolls 1, 2, 3, where­ by particularly a wall-thickness of the outside layer member is reduced. In this Example, since the rolls 1, 2, 3 having hump portion are used, the flaring can be prevented even though the deformation resistance of the outside layer mem­ ber 12 is small. In addition, the outside layer member 12 receiving a reduction is prevented from sliding relatively to the core member by means of the restrictive member 11a, so that the outside layer member is elongated, whereby the core member is bonded with the outside layer member. Thus, the core member 11 can be bonded with the outside layer member 12 all over the length thereof by suitably sel­ ecting a length of the core member 11, a length of the out­ side layer member 12 and a reduction in area of the outside layer member 12. Besides, the diffusion layer formed between the core member 11 and the outside layer member 12 by heating is thinned by rolling. Further, the outside layer member 12 is elongated to cover a portion of the core member 11 which has been naked and portions of the outside layer member 12 elon­ gated by the rolls 1, 2, 3 are diffused on the interface of the core member to form a thin diffusion layer, whereby bonding the outside layer member to the core member. Accor­ dingly, the manufactured clad bar 13 exhibits a high bond strength all over the length thereof. The concrete example will be described below. Core member: pure Ti (JIS Grade 2) outside diameter: 20 mm, length: 2750 mm Outside layer member: pure Al (JIS 1070) outside diameter: 32 mm, wall-thickness: 5.75 mm, length: 800 mm The core member and the outside layer member were de­ greased and cleaned and then the core member was fitted in the outside layer member to obtain an assembly. The outside layer member of the resulting assembly was heated at 500°C and then subjected to the rolling by means of an Assel mill type rotary mill provided with rolls made of SCM440 under the conditions that a cross angle (γ): 5°, a feed angle (β): 10°, a maximum diameter of rolls in the hump: 120 mm, a face angle of an inlet inclined portion: 3°, a face angle of roll hump portion: 20°, and a rotational frequency of roll: 60 rpm to manufacture a clad bar having an outside diameter of 24 mm. And, the manufactured clad bar was investigated on the bonding interface. It was found from the investigation re­ sults by an electron prove micro analysis (EPMA) that no oxide exists on the bonding interface. Furthermore, it was found from the investigation results by a scanning electron microscope (SEM) that no separation is found on the bonding interface and the diffusion layer is 1 micron thick. In ad­ dition, it was investigated whether separations are formed on the bonding interface obtained by cutting using a shear­ ing machine or not, and no separation was found. (Fifth Example) This Example was carried out in the same manner as in Fourth Example. Core member: pure Cu (JIS C 1100) outside diameter: 21.5 mm, length: 3100 mm Outside layer member: Pure Ti (JIS Grade 2) outside diameter: 32 mm, wall-thickness: 5 mm, length: 800 mm Both members of the assembly were simultaneously heated at 750°C and then subjected to the rolling under the same conditions as in Fourth Example to manufacture a clad bar having an outside diameter of 21 mm. A reduction in area of the outside layer member and the core member was 78.3 % and 16.3 %, respectively. The shear strength and bonding interface of the manu­ factured clad bar were investigated. The shear strength was 21.3 kgf/mm² which met the reference value of the shear strength of 10 kgf/mm² according to JIS G3604. In addition, on the bonding interface, no oxide was found as investigated by an EPMA and no separation was found as investigated by a SEM. The diffusion layer was 1.3 microns thick. (Sixth Example) This Example aims to increase the bond strength by carrying out the cold drawing prior to the rolling. Referring to Fig. 17, which is a front sectional view showing an assembly 10, and Fig. 18, which is a side view showing the assembly 10, the assembly 10 comprises a core member 11 made of copper having a circular section, a Ni foil 13 wound around the periphery of the core member 11 and a cylindrical outside layer member 12 made of stainless steel put on the Ni foil 13 by drawing. The resulting round rod-like assembly 10 is heated in a heating furnace (not shown) and then transferred in a rotary mill. Fig. 19 is a process chart showing this example. At first, as shown in Fig. 19(a), a peripheral surface of a copper rod having a circular section is subjected to, for example, a turning to remove scales and then degrease and cleaned with acetone and the like to form the core member 11, while, as shown in Fig. 19(b), an inside circumferential surface of a cylindrical stainless steel pipe is subjected to the pickling and then degreased and cleaned in the same manner as for the core member 11 to form the outside layer member 12. The Ni foil 13 of, for example, about 40 microns thick is wound around the peripheral surface of said core member 11, as shown in Fig. 19(c), and the core member 11 surround­ ed by the Ni foil 13 is put in an inside of the outside lay­ er member 12 and then subjected to the cold drawing, as shown in Fig. 19(d), to form the round rod-like assembly 10 as shown in Fig. 19(e). It is a reason why said Ni foil 13 is wound that if copper is diffused into stainless steel, when the core mem­ ber 11 and the outside layer member 12 are heated and rolled at high temperature with bringing into contact to each other, cracks are generated in stainless steel of the out­ side layer member. Accordingly, in this Example, easily diffusible Ni is put between both members so that copper may not be diffused into stainless steel, and is a diffusion layer is formed between the core member 11 and the Ni foil 13 as well as the outside layer member 12 and the Ni foil 13 to improve the bonding and the bond strength at the same time. In addition, Ni may be plated on the inside surface of the outside layer member 12 of the peripheral surface of the core member 11 in place of winding the Ni foil 13 around the core member 11. Said assembly 10 is formed so that no gap may exist at the interface between the core member 11 and the Ni foil 13 as well as the outside layer member 12 and the Ni foil 13. In short, the assembly 10 is formed so that no oxide may be generated on the interface between the core member 11 and Ni foil 13 and the interface between the outside layer member 12 and the Ni foil 13 when heated. Subsequently, the assembly 10 is heated at, for exam­ ple, 1,020°C in the heating furnace. This heating tempera­ ture is limited to temperature lower than 1,030 to 1,040°C at which the lowest melting-point core member 11 beings to melt. Since stainless steel is apt to be broken at low tem­ perature comparatively high temperature of 1,030°C or less is preferably selected in view of the workability of stain­ less steel. This heating leads to the formation of the diffusion layer on both interfaces during the rolling and the improve­ ment in bonding and bond strength. And, the heated assembly 10 is subjected to the rolling by said rotary mill. Thus, a stainless steel-clad copper bar 14 having integrity of bonding and high bond strength as shown in Fig. 19(f) can be manufactured in a high productivity. This Example is concretely described. An inside surface and an outside surface of a stainless steel pipe (JIS SUS 301S) having an inside diameter of 66 mm and an outside diameter of 76.3 mm were subjected to the pickling and then degreased and cleaned with acetone. In addition, a copper rod (oxygen-free copper) was machined in a finishing accuracy of 1.6 microns Ra as prescribed in JIS B 0601 to make an outside diameter 62 mm and then degreased and cleaned with acetone. Subsequently, a Ni foil of 40 microns thick was wound around the periphery of the copper rod and the copper rod surrounded by the Ni foil was insert­ ed into said stainless steel pipe. The resulting assembly was subjected to the cold drawing to reduce the outside dia­ meter until 70 mm. The drawn assembly was heated at 1,020°C and then subjected to the elongating until the outside dia­ meter thereof becomes 60 mm, 50 mm, 40 mm and 35 mm. The rolling conditions were as follows: A cross angle (γ): 5°, a feed angle (β): 13°, a di­ ameter of roll: 180 mm, a material of roll: SCM440, and a rotational frequency of roll: 100 rpm. The results of the measurement of shear strength by the method shown in Fig. 9 are shown in the following Table. In every case, the shear strength of 10 kgf/mm² or more can be attained. In addition, in order to investigate the bonding inter­ face of said clad bar, the observation by a scanning elec­ tron microscope (SEM), the observation by an electron probe micro analysis (EPMA) and the ultrasonic test were carried out. Then, no separation and oxide were confirmed, as shown in Fig. 20, from the observation by a SEM. In addition, the concentration of Ni, Cr, Fe and Cu to be measured was changed in the direction of thickness in the vicinity of both interfaces, as shown in Fig. 21, according to the ob­ servation by an EPMA. It can be understood from the above observation that each element is sufficiently diffused and an excellent bond is attained. Besides, it was found from the results of the ultrasonic test that no defect, such as the generation of cracks, existed on the interface. (Seventh Example) In this Example the assembly is subjected to cold draw­ ing in the same manner as in Sixth Example and then both end faces of the assembly are tightly closed up by the fusion welding. In the event that a thermal expansion coefficient of an outside layer member is larger than the of a core member, clearance is generated between the core member and the outside layer member and the interface is oxidized according to circumstances but the oxidation can be prevent­ ed by tightly closing up both end faces of the assembly, whereby attaining a high bond strength. Core member: carbon steel (C: 0.06%) Outside layer member: stainless steel (JIS SUS304) The core member was subjected to the polishing process and then degreased and cleaned. An inside circumferential surface of the outside layer member was degreased and cleaned and then the core member was inserted into the outside layer member. Subsequently, the resulting assembly was subjected to the cold drawing to make an outside diameter 57 mm. Subsequently, the core member and the outside layer member are welded together at both end faces of the assembly by the shield metal arc welding to close up the interface between the core member and the outside layer member tight­ ly. Then, the assembly is heated at 1,100°C and subjected to the elongation by the rotary mill. Rolling conditions were selected as follows: cross angle (γ): 3° feed angle (β): 15° rotational frequency of roll: 100 rpm reduction in area: 79.2% (57 mm⊘ → 26 mm⊘) The shear strength was measured by a method as shown in Fig. 9 with the results as shown below. <1> 34.4 kgf/mm², <2> 35.2 kgf/mm² In addition, a thickness of the outside layer member was measured at 8 points in a circumferential direction with the results as shown in the following Table. As obvious from these results, a nearly uniform distribution of wall-­ thickness was attained. In addition, an outside diameter was 26 ± 0.02 mm in both cases <1> and <2>. In addition, it was found from the investigation by the ultrasonic test that no separation existed on the interface. (Eighth Example) This Example is characterized by a method of tightly closing up both end faces of the assembly. Core member: pure Ti (JIS Grade 2) outside diameter: 54.6 mm, length: 800 mm Outside layer member: pure Ni (Ni: 99.6 %) outside diameter: 60.3 mm, wall-thickness: 2.8 mm, and length: 806 mm Fig. 22 is a front view showing an assembly 10, and Fig. 23 is a side view showing the assembly 10. An inside circumferential surface of the outside layer member and a peripheral surface of the core member are de­ greased and cleaned, and then the core member is fitted in the outside layer member to form an assembly. The resulting assembly is provided with a disc-like cap 15 made of Ni en­ gaged with both end faces thereof by means of suitable means and the cap 15 is welded to the outside layer member 12 by the electron beam welding method under vacuum or under re­ duced pressures. It is a reason why such the cap 15 is used that Ti can not be welded to Ni. The degree of vacuum was selected at 5×10⁻¹, 1×10⁻¹, 3×10⁻², 3×10⁻³ and 3×10⁻⁴ Torr, respectively. After tightly closing up the assembly, the assembly was heated at 800°C and then subjected to the elongating by the rotary mill. The rolling conditions were selected as follows: cross angle (γ): 3° feed angle (β): 13° diameter of roll: 117 mm rotational frequency of roll: 80 rpm reduction in area: 88.5 % (60.3 mm⊘→20.5 mm⊘) The shear strength of the resulting clad bar was mea­ sured by the method as shown in Fig. 9 with the results shown in Fig. 24. In the event that the degree of vacuum is 1×10⁻¹ Torr or more, the shear strength is remarkably reduced. Accordingly, the degree of vacuum of preferably 1×10⁻¹ Torr or less should be selected in the welding. If the degree of vacuum of 1×10⁻¹ Torr or less is used, the shear strength of the resulting clad bar can meet the reference value of the shear strength of titanium-clad steel of 14 kgf/mm² prescribed in JIS G 3603. In addition, the outside layer member 12 may be formed in a cylinder having a bottom, as shown in Fig. 25, and the core member 11 is inserted into the outside layer member 12, and then an opened portion of the cylinder may be covered with the cap 13 followed by welding in vacuum chamber by the electron beam welding method. (Ninth Example) In this Example, the same method as in Eighth Example is used. The size of the core member and the outside layer member is same as in Eighth Example. The materials are shown in the following Table. The degree of vacuum was selected at 3 × 10⁻³ Torr. The shear strength is shown in the following Table as measured by the method shown in Fig. 9. That is, the shear strength is 20 kgf/mm² or more in every sample. A clad bar, which is obtained in the above described manner, was cold drawn by means of a die until a outside diameter of 3 mm. Fig. 26 is a photograph of the final clad wire taken by SEM. No separation and oxide were observed at all. In addition, it is necessary to remove scales from the outside surface prior to the cold drawing. As this invention may be embodied in several forms without departing from the spirit of essential characteris­ tics thereof, the present embodiment is therefore illustra­ tive and not restrictive, since the scope of the invention is defined by the appended claims rather than by the de­ scription preceding them, and all changes that fall within the meets and bounds of the claims, or equivalence of such meets and bounds thereof are therefore intended to be em­ braced by the claims.

Claims: 1. A method of manufacturing a clad bar, in which a columnar core member is fitted in a cylindrical outside layer member to bond them to each other, characterised by comprising; a step of heating an assembly obtained by fitting the core member in the outside layer member; and a step of elongating the heated assembly by a rotary mill having three or more cone type rolls to finish the assembly to a desired size. 2. A method of manufacturing a clad bar as set forth in Claim 1, in which the heating temperature is selected at temperature lower than melting points of the core member, the outside layer member and intermetallic compounds thereof. 3. A method of manufacturing a clad bar as set forth in Claim 1, in which said rotary mill is provided with rolls having a structure supported at both ends, a cross angle being set at 0-15°, and a feed angle being set at 6-20°. 4. A method of manufacturing a clad bar as set forth in Claim 1, in which the core member is fixedly mounted on the outside layer member at one end thereof prior to the elongating. 5. A method of manufacturing a clad bar as set forth in Claim 4, in which the core member is longer than the outside layer member, the assembly comprising the core member and the outside layer member being trued up and fixedly mounted at one end prior to the elongating, and the assembly being introduced into the rotary mill from said one end side. 6. A method of manufacturing a clad bar as set forth in Claim 5, in which the outside layer member is preferentially heated to make the deformation resistance thereof smaller than that of the core member and then the assembly is introduced into the rotary mill. 7. A method of manufacturing a clad bar, in which a columnar core member is fitted in a cylindrical outside layer member to bond them to each other, characterised by comprising; a step of tightly closing up a gap at each end of the assembly comprising the core member and the outside layer member under reduced pressure or under vacuum; a step of heating the closed up assembly; and a step of elongating the heated assembly by a rotary mill having three or more cone type rolls to finish the assembly to a desired size. 8. A method of manufacturing a clad bar as set forth in Claim 7, in which the heating temperature is selected at temperature lower than heating points of the core member, the outside layer member and intermetallic compounds thereof. 9. A method of manufacturing a clad bar as set forth in Claim 7, in which said rotary mill is provided with rolls having a structure supported at both ends, a cross angle being set at 0-15°, and a feed angle being set at 6-20°. 10. A method of manufacturing a clad bar as set forth in Claim 7, in which said hermetical closure is carried out by the electron beam welding method. 11. A method of manufacturing a clad bar as set forth in Claim 7, in which a gap is tightly closed up by welding a putting plate to end faces of the assembly comprising the core member and the outside layer member. 12. A method of manufacturing a clad bar as set forth in Claim 11, in which said core member is made of titanium or titanium alloys and the outside layer member is made of nickel or nickel alloys. 13. A method of manufacturing a clad bar, in which a columnar core member is fitted in a cylindrical outside layer member to bond them to each other, characterised by comprising; a step of cold drawing an assembly comprising the core member and the outside layer member; a step of heating the cold drawing assembly; and a step of elongating the heated assembly by a rotary mill provided with three or more cone type rolls to finish the assembly to a desired size. 14. A method of manufacturing a clad bar as set forth in Claim 13, in which said core member is made of copper and the outside layer member is made of stainless steel. 15. A method of manufacturing a clad bar as set forth in Claim 13, in which nickel is interposed between the core member and the outside layer member. 16. A method of manufacturing a clad bar as set forth in Claim 13, in which the heating temperature is selected at temperature lower than melting points of the core member, the outside layer member and intermetallic compounds thereof. 17. A method of manufacturing a clad bar as set forth in Claim 13, in which said rotary mill is provided with rolls having a structure supported at both ends, a cross angle being set at 0-15°, and a feed angle being set at 6-20°. 18. A method of manufacturing a clad bar, in which a columnar core member is fitted in a cylindrical outside layer member to bond them to each other, characterised by comprising; a step of cold drawing an assembly comprising the core member and the outside layer member; a step of tightly closing up the cold drawn assembly at each end thereof; a step of heating the tightly closed assembly; and a step of elongating the heated assembly by a rotary mill provided with three or more cone type rolls. 19. A method of manufacturing a clad bar as set forth in Claim 18, in which said core member is made of carbon steel or low-alloy steel and the outside layer member is made of stainless steel. 20. A method of manufacturing a clad bar as set forth in Claim 18, in which heating temperature is selected at temperature lower than melting points of the core member, the outside layer and intermetallic compounds thereof. 21. A method of manufacturing a clad bar as set forth in Claim 18, in which said rotary mill is provided with rolls having a structure supported at both ends, a cross angle being set at 0-15°, and a feed angle being set at 6-20°. 22. A method of manufacturing a clad bar as set forth in any of Claims 1, 7, 13 and 18 in which a reduction rate in said elongating is selected at 25% or more/pass. 23. A method of manufacturing a clad bar as set forth in any of Claims 1, 7, 13 and 18 in which a deformation resistance of the outside layer member is larger than that of the core member. 24. A method of manufacturing a clad bar as set forth in any of claim 1, 7, 13 and 18, in which a thermal expansion coefficient of the outside layer member is larger than that of the core member.

Inventors: HAYASHI, CHIHIROÂCENTRAL RESEARCH LAB. SUMITOMO, NAKASUJI, KAZUYUKIÂCENTRAL RESEARCH LAB. SUMITOMO, Hayashi, Chihiro§Central Research Lab. Sumitomo, Nakasuji, Kazuyuki§Central Research Lab. Sumitomo
Applicants: SUMITOMO METAL INDUSTRIES, LTD.
Application year: 1987
Main classification: B21B1
IPC codes: B21B1, B21C37