AUSTENITIC, PRECIPITATION HARDENABLE STAINLESS STEEL

Abstract: Austenitic, precipitation hardenable, stainless chro­ mium-nickel-aluminium steel with good cold workability. The steel contains Cr 13-22 % and Ni 5-17 % within the area ABCD on the enclosed diagram, and C up to 0.15 %, Si up to 3.0 %, Mn up to 8.0 %, P up to 0.045 %, S up to 0.040 %, Mo up to 2.0 %, N up to 0.15 %, Al 0.5-2.5 %. In addition the steel can contain one more of the metals Ti, Zr and U up to 2 % with the balance iron and impurities normally occurring in stain­ less steels.

Description: AUSTENITIC, PRECIPITATION HARDENABLE STAINLESS STEEL This invention deals with an austenitic stainless, precipitation hardenable chromium-nickel-aluminium steel with good cold workability. By tempering the martensite obtained by cold working, quenching or in some cases cooling to subzero temperatures, precipitation hardening is obtained. The new alloy can be produced as hot rolled products such as wire rod, bar, strip and plate. Precipitation hardening of stainless steel using aluminium is a well-known technique. These steels can either be given an annealing treatment designed to raise the M temperature so much that martensite is formed on 5 quenching, or they can be annealed at a higher temperature giving an austenitic structure when quenched. In the latter case the steel can be subsequently cold worked, thus transforming the austenite into martensite. After one of these treatments the material can be precipitation hardened. The disadvantage with these steels is that the rate of martensite formation when cold working is extremely high, thus rendering the material difficult to work. The risk of stress cracks, for example, during the wire drawing process is extremely high. The main purpose of the present invention is thus to improve the workability in the cold condition of Cr-Ni-Al steels by lowering the M5 and the Mud30 temperatures sufficiently to ensure that good workability is obtained without at the same time lowering them so far that the austenite is not transformed to martensite when cold worked. Martensite is desirable in the final product since it raises the mechanical strength considerably. Two production heats with the following analyses have been made under production conditions. Table 1 Heat No C Si Mn P S Cr Ni Mo N Al Ti 3423-71 .064 .60 1.30 .021 .014 17.1 8.9 .16 .034 .82 .09 4029-71 .069 .65 1.19 .018 .010 17.2 9.0 .13 .034 1.06 .10 Both heats were melted in a 10-ton high-frequency induction furnace, ingot teemed. and rolled to billets. These were conditioned and rolled to wire rod, 0 6.0 mm for heat 3423-71 and 0 5.6 mm for heat 4029-71. The wire rod was subjected to a normal anneal at 10500C, pickled and inspected before being drawn to wire. As reference material a heat (3226-71) in steel of type 17-7 PH (AISI 631) has been produced by the same method. This is a precipitation hardenable Cr-Ni-Al-steel with the following heat analysis (Table 2). Table 2 Charge C Si Mn P S Cr Ni Mo N Al Ti 3226-71 .073 .74 .74 .013 .006 16.4 7.1 .15 .041 .94 .09 Heats 3423-71 (Table 1) and 3226-71 have been drawn from wire rod, 0 6.0 mm, using single drafts. The tensile strength (Rm), yield strength (Re), and reduction of area (Z) as measured by tensile testing are compared in Figure 1. It is apparent that the yield and tensile strengths increase more slowly for the alloy in the invention (continuous curve) thus causing the drawability, measured as maximum achievable area reduction, to increase from 758 to 92%. Moreover, the ductility measured as reduction of area is higher for the alloy in the invention over the whole range and particularly at large area reductions. It should be noted that stress cracks are completely absent in the material for area reductions as large as 92% compared with 17-7 PH where Åa definite risk of stress crack formation exists at area reductions as low as 45%. The precipitation hardening effect of the alloy in the invention has been tested for two different area reductions and the results are shown below. in Table 3. Table 3 EMI3.1 <tb> <SEP> R <SEP> N/mm2 <SEP> R <SEP> 3 <tb> <SEP> N/mmL <SEP> <tb> <SEP> m <SEP> e <tb> Heat <SEP> Wire <SEP> Area <SEP> Un- <SEP> Tempered <SEP> Un- <SEP> Tempered <tb> No <SEP> dia- <SEP> reduc <tb> No <SEP> meter <SEP> tion <SEP> tempered <SEP> tempered <tb> <SEP> mm <SEP> 8 <SEP> <tb> 3423-71 <SEP> 2.68 <SEP> 80.0 <SEP> 1810 <SEP> 1995 <SEP> 1630 <SEP> 1855 <tb> 4029-71 <SEP> 1.83 <SEP> 89.4 <SEP> 2116 <SEP> 2525 <SEP> 1976 <SEP> 2357 <tb> Tempering treatment: 30 minutes at 4500C. Thus, the tempering treatment gives an increase of yield and tensile strengths of about 200 N/mm2 for heat 3423-71 and about 400 N/mm2 for heat 4029-71. The large difference between these effects can be explained by the fact that wire rod from heat 3421-71 has not been worked sufficiently, i.e. the austenite has not been transformed to martensite insufficient quantities prior to tempering. The alloy in this invention has mainly been developed in order to improve the cold workability of precipitation hardenable stainless Cr-Ni-Al steels. Within the area ABCD in Figure 2 the composition can be set so that annealing in the temperature range 600-950 0C leads to a rise in the M temperature due to carbide precipita S tion. The material can subsequently be cooled to ambient or subzero temperatures in order to obtain a transformation to martensite which can then be tempered. A particularly interesting application is cold heading where tensile strengths as low as 540 - 560 N/mm2 have been measured on material annealed at 10500C. This is true for both heats 3423-71 and 4029-71. The technical result of the invention is that the drawability is considerably improved at the same time as the precipitation hardening effect is retained. It is reasonable to assume that the good weldability can be improved by additions of zirconium and uranium instead of titanium. Since the alloy has an extremely sluggish martensitic transformation in the annealed state the material can be stored and transported outdoors under cold weather conditions without risk of spontaneous martensite formation. Chromium and nickel contents should lie within the area ABCD as shown in Figure 2 where chromium can be partly replaced by molybdenum with up to 2%, and nickel can be partly replaced by manganese according to the formula % Ni = 1/2 (% Mn - 1%). In one, particularly preferred, form of the alloy chromium and nickel should lie within the area ABCD in Figure 2. The alloy according to the invention is annealed within the temperature range 600 - 950 0C, quenched and cooled to below room temperature. The alloy can then be precipitation hardened by tempering. The alloy can also be quenched direct after hot rolling and subsequently cold worked and precipitation hardened by tempering.

Claims: CLAIMS 1. Austenitic, precipitation hardenable, stainless chromium-nickel-aluminium steel with good cold workability and characterized by containing Cr 13 - 22% and Ni 5 - 17% and C up to 0.15%, Si up to 3.0%, Mn up to 8.0%, P up to 0.045%, S up to 0.040%, Mo up to 2.0%, N up to 0.15%, Al 0.5 - 2.5% and preferably one or more of the metals Ti, Zr and U up to 2%, with the balance of iron and impurities normally occurring in stainless steels and the sum of Ni and Mn expressed as Ni' = %Ni + 1/2 (% Mn-1) and the sum of Cr and Mo expressed as Cr' according to the formula Cr' = %Cr + %Mo lies within the area ABCD in the enclosed diagram Figure 2. 2. Steel according to claim 1, characterized by the fact that it contains either Ti up to 0.58 or Zr up to 0.5% or U up to 1%. 3. Steel according to claims 1 and 2, characterized by a chromium content of 22% corresponding to a nickel content between 5.25 and 12.5% and a chromium content of 13% corresponding to a nickel content between 10.15 and 17%. 4. Steel according to claims 1 and 2, characterized by the fact that the chromium content lies between 16.5% and 18.2% and the nickel content between 8.25% and 9.75%.

Inventors: ANGEL, FRANS GUSTAF STEFAN, MALMGREN, NILS GUNNAR EUGEN, SOLLY, BARRY, Malmgren, Nils Gunnar Eugén
Applicants: FAGERSTA AB
Application year: 1980
Main classification: C22C38
IPC codes: C22C38