High Al-content vibration-damping ferritic stainless steel material, and production method

Abstract

A ferritic stainless steel material excellent in vibration damping capability has a composition containing, by mass %, from 0.001 to 0.04% of C, from 0.1 to 2.0% of Si, from 0.1 to 1.0% of Mn, from 0.01 to 0.6% of Ni, from 10.5 to 20.0% of Cr, from 0.5 to 5.0% of Al, from 0.001 to 0.03% of N, from 0 to 0.8% of Nb, from 0 to 0.5% of Ti, from 0 to 0.3% of Cu, from 0 to 0.3% of Mo, from 0 to 0.3% of V, from 0 to 0.3% of Zr, from 0 to 0.6% of Co, from 0 to 0.1% of REM, from 0 to 0.1% of Ca, the balance of Fe and unavoidable impurities, and has ferrite single phase matrix with crystal grains of average crystal grain diameter of from 0.3 to 3.0 mm and a residual magnetic flux density of 45 mT or less.

Claims

1. A vibration-damping ferritic stainless steel material having a chemical composition containing, in terms of percentage by mass, from 0.001 to 0.04% of C, from 0.1 to 2.0% of Si, from 0.1 to 1.0% of Mn, from 0.01 to 0.6% of Ni, from 10.5 to 20.0% of Cr, from 0.5 to 5.0% of Al, from 0.001 to 0.03% of N, from 0 to 0.8% of Nb, from 0 to 0.5% of Ti, from 0 to 0.3% of Cu, from 0 to 0.3% of Mo, from 0 to 0.3% of V, from 0 to 0.3% of Zr, from 0 to 0.6% of Co, from 0 to 0.1% of REM (rare earth element), from 0 to 0.1% of Ca, and the balance of Fe, with unavoidable impurities, having a metal structure containing a ferrite single phase as a matrix and ferrite crystal grains having an average crystal grain diameter of from 0.3 to 3.0 mm, and having a residual magnetic flux density of 45 mT or less.

2. A production method for a vibration-damping ferritic stainless steel material, comprising subjecting a steel material having a chemical composition containing, in terms of percentage by mass, from 0.001 to 0.04% of C, from 0.1 to 2.0% of Si, from 0.1 to 1.0% of Mn, from 0.01 to 0.6% of Ni, from 10.5 to 20.0% of Cr, from 0.5 to 5.0% of Al, from 0.001 to 0.03% of N, from 0 to 0.8% of Nb, from 0 to 0.5% of Ti, from 0 to 0.3% of Cu, from 0 to 0.3% of Mo, from 0 to 0.3% of V, from 0 to 0.3% of Zr, from 0 to 0.6% of Co, from 0 to 0.1% of REM (rare earth element), from 0 to 0.1% of Ca, and the balance of Fe, with unavoidable impurities, to final annealing in a non-oxidative atmosphere under a condition of retaining the steel material in a temperature range of from 900 to 1,250 C. for 10 minutes or more, so as to make an average crystal grain diameter of ferrite crystal grains of from 0.3 to 3.0 mm.

3. The production method for a vibration-damping ferritic stainless steel material according to claim 2, wherein the final annealing is performed in an air atmosphere instead of the non-oxidative atmosphere, and acid cleaning is performed after the final annealing.

4. The production method for a vibration-damping ferritic stainless steel material according to claim 2 or 3, wherein the steel material subjected to the final annealing is a steel material obtained by working a steel sheet material.

Description

BRIEF DESCRIPTION OF DRAWINGS

(1) FIG. 1 is the optical micrograph of the metal structure of Comparative Example No. 1.

(2) FIG. 2 is the optical micrograph of the metal structure of Comparative Example No. 2.

(3) FIG. 3 is the optical micrograph of the metal structure of Comparative Example No. 3.

(4) FIG. 4 is the optical micrograph of the metal structure of Example No. 4 of the invention.

DESCRIPTION OF EMBODIMENTS

(5) Type of Steel Applied

(6) In the invention, in ferritic stainless steel capable of providing a matrix (metal basis material) formed of a ferrite single phase at ordinary temperature, particularly a high Al-content ferritic stainless steel having an Al content of from 0.5 to 5.0% by mass is applied. The combined addition of Cr and a large amount of Al can significantly enhance the level of the vibration damping capability. The mechanism of the enhancement of the vibration damping capability is not yet clarified at the present time.

(7) The contents of the alloy components may be determined within the aforementioned ranges. While P and S are unavoidable impurities, the P content may be allowed up to 0.040%, and the S content may be allowed up to 0.030%.

(8) Examples of the steel types having particularly high heat resistance include the following compositional range (A).

(9) (A) A steel containing, in terms of percentage by mass, from 0.001 to 0.03% of C, from 0.1 to 1.0% of Si, from 0.1 to 1.0% of Mn, from 0.01 to 0.6% of Ni, from 17.5 to 19.0% of Cr, from 2.5 to 4.0% of Al, from 0.001 to 0.03% of N, from 0 to 0.3% of Nb, from 0.1 to 0.3% of Ti, from 0 to 0.3% of Cu, from 0 to 0.3% of Mo, from 0 to 0.3% of V, from 0 to 0.3% of Zr, from 0 to 0.6% of Co, from 0 to 0.1% of REM (rare earth element), from 0 to 0.1% of Ca, and the balance of Fe, with unavoidable impurities.

(10) Metal Structure

(11) In the steel material according to the invention, it is important that the average crystal grain diameter of the ferrite recrystallized grains constituting the matrix (metal basis material) is as extremely large as from 0.3 to 3.0 mm. The average crystal grain diameter is more preferably 0.35 mm or more. A ferromagnetic vibration damping material absorbs vibration energy through migration of magnetic domain walls. The crystal grain boundary becomes a barrier preventing the migration of magnetic domain walls, and therefore it is generally said that a large crystal grain diameter is advantageous for enhancing the vibration damping capability. However, in the case of a ferritic stainless steel material, a good vibration damping capability often cannot be obtained with an average crystal grain diameter of approximately 100 m, and a measure for stably imparting a high vibration damping capability has not been clarified. As a result of various investigations by the inventors, it has been found that the vibration damping capability of the ferritic stainless steel material is enhanced by extremely increasing the average crystal grain diameter thereof to 0.3 mm or more. While the mechanism thereof is not clear at the present time, it is considered that the ferrite recrystallized grains constituting the matrix of the ferritic stainless steel material include grains having large sizes and grains having small sizes mixed with each other, and the small grains among these disadvantageously affect the migration of the magnetic domain walls. It is estimated that the heat treatment is performed to make the average crystal grain diameter as extremely large as 0.3 mm or more, more preferably 0.35 mm or more, so as to grow the recrystallized grains having small sizes to sizes that do not prevent the migration of the magnetic domain walls, resulting in the enhancement of the vibration damping mechanism over the entire steel material.

(12) The average crystal grain diameter can be measured by the optical microscope observation of the cross section according to the intercept method. According to the method described in JIS G0551:2003, a straight line is drawn at an arbitrary position on the image of the optical micrograph, and the number of the intersection points of the straight line and the crystal grain boundaries is counted, from which an average segment length is calculated. The observation is performed for 20 or more in total of straight lines with plural observation view fields. The ferritic stainless steel material having an average crystal grain diameter measured in this method that is 0.3 mm or more exhibits an excellent vibration damping capability. The average crystal grain diameter is more preferably 1.0 mm or more. The steel material having been finished for the working to the shape of the member is subjected to the final annealing described later to grow the crystal grains, and thereby the adverse effect of the coarse crystal grains to the workability can be avoided. The large crystal grains are advantageous from the standpoint of the high temperature creep resistance. However, an excessive increase of the crystal grains may increase the load of the final annealing, which is economically disadvantageous. The average crystal grain diameter suffices to be in a range of 3.0 mm or less, and may be managed to 2.5 mm or less.

(13) Magnetic Characteristics For smoothly performing the migration of the magnetic domain walls, it is also important that the ferrite crystal lattice has a small strain. The extent of the strain in the crystal is reflected to the residual magnetic flux density in the magnetic characteristics. Specifically, assuming materials having the same composition, it can be evaluated that a material having a smaller residual magnetic flux density has a small strain of the crystal lattice. According to the studies by the inventors, a good vibration damping capability can be obtained in a ferritic stainless steel material having a residual magnetic flux density that is 45 mT (450 G) or less at ordinary temperature. The residual magnetic flux density is more preferably 30 mT (300 G) or less. The lower limit thereof is not particularly determined, and is generally 12 mT (120 G) or more.

(14) As other magnetic characteristics, the coercive force is desirably 400 A/m (approximately 5 Oe) or less. The maximum magnetic flux density is desirably 450 mT (4,500 G) or more, and more preferably 520 mT (5,200 G) or more.

(15) Production Method

(16) In the invention, the ferrite recrystallized grains are grown in the final annealing of the ferritic stainless steel material, so as to impart a vibration damping capability thereto.

(17) The process used for providing the steel material for being subjected to the final annealing may be an ordinary production process. For example, a cold rolled annealed acid-cleaned steel sheet or a temper rolling finished steel sheet of a ferritic stainless steel produced by an ordinary method as a raw material is worked into a prescribed member. Examples of the working to the member include various kinds of press work using a mold, bending work, welding work, and the like.

(18) The steel material having been worked into the member is subjected to the final annealing. The material is heated and retained in a temperature range of from 900 to 1,250 C., so as to grow the recrystallized grains to have an average crystal grain diameter of the ferrite crystal grains of from 0.3 to 3.0 mm, and more preferably from 0.35 to 3.0 mm. The retention time in the aforementioned temperature range (i.e., the period of time where the material temperature is in the temperature range) is ensured to be such a period of time that is capable of growing the ferrite crystal grains to the aforementioned average crystal grain diameter, corresponding to the chemical composition and the degree of working of the steel material subjected to the final annealing. However, when the retention time is too short, the enhancement of the vibration damping capability may be insufficient due to shortage in homogenization in some cases. As a result of various investigations, the retention time is preferably ensured to be 10 minutes or more. The retention time is more preferably 50 minutes or more, and further preferably 100 minutes or more. However, a too long retention time is economically disadvantageous. The retention time at the aforementioned temperature may be set in a range of 300 minutes or less, and may also be a range of 200 minutes or less. The appropriate retention temperature and retention time can be comprehended in advance by a preliminary experiment corresponding to the chemical composition and the degree of working of the steel material.

(19) In a cooling step after retaining in the aforementioned temperature range, quenching is preferably avoided to prevent strain in the crystal due to thermal contraction associated with cooling from being introduced. As a result of various investigations, it is effective that the maximum cooling rate of from the maximum attaining temperature, which is in a range of from 900 to 1,250 C., to 200 C. is controlled to 5 C./sec or less. When the cooling rate is too slow, on the other hand, aging precipitation may occur in a temperature range during cooling in some cases, and the precipitated phase may be a factor impairing the migration of the magnetic domain walls through the formation of a strain field in the crystal. Therefore, it is preferred to avoid excessively slow cooling. For example, it is effective that the average cooling rate of from 850 C. to 400 C. is 0.3 C./sec or more.

(20) In view of the above, examples of the more preferred condition for the final annealing taking the cooling rate into consideration include a condition of retaining the steel material in a temperature range of from 900 to 1,250 C. for 10 minutes or more, so as to make an average crystal grain diameter of ferrite crystal grains of from 0.5 to 3.0 mm, and then cooling to a temperature of 200 C. or less at a maximum cooling rate of from a maximum attaining material temperature to 200 C. of 5 C./sec or less and an average cooling rate of from 850 C. to 400 C. of 0.3 C./sec or more.

(21) The final annealing is desirably performed in a non-oxidative atmosphere. Examples thereof include vacuum annealing. In this case, the interior of the furnace is vacuumed to a depressurized state (vacuum atmosphere), for example, of approximately 110.sup.2 Pa or less, and therein, the steel material is heated to and retained in the aforementioned temperature range. In the cooling step, the cooling rate can be controlled, for example, by controlling the introduction amount of an inert gas, and the like. The final annealing may be performed in a reductive atmosphere containing hydrogen. The final annealing may be performed in an air atmosphere, and in this case, a post-treatment, such as acid cleaning, is necessarily performed for removing oxidized scale.

(22) In the case where a flat plate member is to be provided, such a method may be employed that a cold rolled annealed steel sheet in a coil form is directly placed in an annealing furnace and subjected to the final annealing, and then cut into a prescribed dimension.

EXAMPLES

(23) The steels shown in Table 1 were made, from which cold rolled annealed acid-cleaned steel sheets having a sheet thickness of 1.5 mm were obtained according to an ordinary method. Specimens collected from the steel sheets were subjected to final annealing under the conditions shown in Table 2 except for a part of Comparative Examples (Nos. 1 and 3). The method of the final annealing was vacuum annealing, and performed in the following manner. The specimen was placed in a sealable vessel, and in the state where the interior of the vessel was vacuumed to a pressure of approximately 110.sup.2 Pa or less, the specimen was heated and retained at the temperature (i.e., the maximum attaining temperature) shown in Table 2. Thereafter, after decreasing the temperature to 900 C., the specimen was cooled to a temperature of 400 C. or less by introducing argon gas to the vessel up to a pressure of approximately 90 kPa, and then exposed to the air after the temperature reached 200 C. or less. The cooling rate in the final annealing was controlled in such a manner that the maximum cooling rate of from a maximum attaining temperature to 200 C. was 5 C./sec or less, and the average cooling rate of from 850 C. to 400 C. was 0.3 C./sec or more.

(24) The specimens were obtained in the aforementioned manners.

(25) TABLE-US-00001 TABLE 1 Chemical composition (% by mass) Steel C Si Mn Ni Cr Nb Ti Cu Mo Al N Note E 0.010 0.28 1.00 0.17 18.42 0.65 0.15 2.02 0.006 0.010 comparative steel N 0.007 0.33 0.24 0.16 18.17 0.15 0.08 0.06 3.07 0.010 steel for invention

(26) TABLE-US-00002 TABLE 2 Final annealing Temperature Time Class No. Steel Atmosphere ( C.) (min) Comparative 1 E Example Comparative 2 E vacuum 1200 120 Example Comparative 3 N Example Example of 4 N vacuum 1100 60 Invention

(27) The specimens were evaluated as follows.

(28) Measurement of Average Crystal Grain Diameter

(29) The metal structure of the cross section in parallel to the rolling direction and the sheet thickness direction (L cross section) was observed with an optical microscope, and the average crystal grain diameter was measured by the intercept method described previously.

(30) The micrographs of the metal structures of Nos. 1, 2, 3, and 4 are exemplified in FIGS. 1, 2, 3, and 4, respectively.

(31) Magnetism Measurement

(32) A test piece of 250 mm20 mmt (t: sheet thickness, 1.5 mm) with a longitudinal direction directed in the rolling direction was subjected to a magnetism measurement with a direct current magnetism measurement device (B-H Curve Tracer, produced by Riken Denshi Co., Ltd.). The coil used was a solenoidal coil of 62.5 mm in diameter160 mm and 100 turns. The maximum magnetic flux density Bm, the residual magnetic flux density Br, and the coercive force He were obtained from the resulting B-H curve.

(33) Measurement of Loss Factor

(34) A test piece of 250 mm20 mmt (t: sheet thickness, 1.5 mm) with a longitudinal direction directed in the rolling direction was measured for the frequency response function at ordinary temperature by the central exciting method according to JIS K7391:2008, the half value width was read at the position decreased by 3 dB from the resonance peak of the resulting frequency response function, from which the value was calculated according to the expression (1) of JIS K7391:2008, and the average value of the values obtained for at the resonance peaks observed in a range of from 10 to 10,000 Hz was designated as the loss factor of the material.

(35) The results are shown in Table 3.

(36) TABLE-US-00003 TABLE 3 Magnetic characteristics Average Maximum magnetic Residual magnetic Coercive Loss crystal grain flux density flux density force Hc factor Class No. Steel diameter (mm) Bm (mT) Br (mT) (Oe) (A/m) Comparative 1 E 0.025 534.5 30.23 3.414 271.7 0.0008 Example Comparative 2 E 1.52 543.0 25.40 2.802 223.0 0.0023 Example Comparative 3 N 0.050 476.7 49.4 4.670 371.6 0.0006 Example Example of 4 N 0.68 504.5 22.8 1.925 153.2 0.0192 Invention

(37) It is understood that the specimens of Comparative Example No. 2 and Example of Invention No. 4 obtained by performing the final annealing under the aforementioned appropriate condition have a small strain of the crystal lattice since the residual magnetic flux density is small. The average crystal grain diameter thereof is significantly large. For these specimens, enhancement of the loss factor is observed as compared to the specimens not subjected to the final annealing (comparison between No. 1 and No. 2, and comparison between No. 3 and No. 4). Example of Invention No. 4, to which Cr and a large amount of Al are added in combination, exhibits considerably large enhancement of the loss factor as compared to Comparative Example No. 2 having a small Al content.

(38) In Example No. 4, seven resonance peaks were present in a frequency range of from 10 to 10,000 Hz, and assuming that the loss factors at the resonance peaks were .sub.1, .sub.2, . . . , .sub.7 in this order from the low frequency side, the measured values thereof were as follows.

(39) .sub.1=0.0387, .sub.2=0.0209, .sub.3=0.0105, .sub.4=0.0092, .sub.5=0.0087, .sub.6=0.0084, .sub.7=0.0082

(40) The average value of these values is the value of the loss factor 0.0149 shown in Table 2. In the values .sub.1 to .sub.7, the values within the resonance frequency range of from 1,000 to 10,000 Hz are the five values .sub.3 to .sub.7.

(41) Even in the case where Cr and a large amount of Al are added in combination, with the ordinary cold rolled annealed acid-cleaned material as it is, there is no tendency of increasing the vibration damping capability as compared to the steel types having a small Al content (comparison between Comparative Example No. 1 and Comparative Example No. 3). On the other hand, with the final annealing according to the invention performed, a large difference in enhancement of the vibration damping capability occurs, and the effect of the combined addition of Cr and a large amount of Al is manifested (comparison between Comparative Example No. 2 and Example of Invention No. 4). Furthermore, the combined addition of Cr and a large amount of Al provides a significant enhancement of the heat resistance (particularly the high temperature oxidation resistance).