High strength stainless steel

Abstract: The invention relates to a high silicon containing stainless steel alloy in which the amounts of the alloy elements have been balanced such that the austenite phase remains stable without deformation into martensite also at extended degrees of working. The steel alloy should essentially consist of 0,04-0,25 % C, 2,0-5,0 % Si, 3,5-7,5 % Mn, 16-21 % Cr, 8-11 % Ni, 0,10-0,45 % N, the remainder being iron and normal impurities.

Description: The invention relates to a high strength precipitation hardening non-magnetic stainless Cr-Ni-Mn-Si-N-steel alloy in which the austenite phase is sufficiently stable so that it is not subject of transformation to the ferromagnetic martenite phase even at substantial reduction, for instance by cold rolling of sheet or drawing of wire. The rapid development that occurs within computer and electronics industry has created an increased demand of materials with combination of properties not previously considered or simply achievable such as the combination of high mechanical strength and a non-magnetic structure for materials to be used in spring applications where a material is required that is magnetically inert. For many of these products the manufacture involves various formation sequences. Since it is common knowledge that increased strength also leads to impaired ductility it is an essential advantage if the formation steps can be carried out in as soft condition as possible and required strength can be achieved by a simple heat treatment. Among these high strength stainless steel the non-stable austenitic spring steels, SS 2331 with a typical standard analysis of 17 Cr, 7 Ni, 0,8 Si, 1,2 Mn, 0,1 C and 0,03 N are in a special position due to their combination of high strength and good corrosion properties. The very high strength that is achievable with this type of steel depends from the fact that the (non-magnetic) austenitic structure is transformed during deformation to (ferromagnetic) martensite, a phase that has exceptional hardness. When increasing its amounts of constituents type SS 2343/2353, the tendency for the formation of deformation martensite is reduced but thereby has also the possibility of achieving high strength been reduced. Furthermore, the use of this type of steel leads to high alloying costs for the high amounts of nickel and molybdenum. French patent publication FR-A-2229776 discloses an austenitic stainless steel alloy having a composition of 10-25% chromium, 3-15 % nickel, 6-16 % manganese, 2-7 % silicon, 0,001-0,25 % carbon, 0,001-0,4 % nitrogen, and balance iron except for incidental impurities. Up to 4 % molybdenum, up to 4 % copper, 0,09 % maxiumum phosphorous, up to 0,25 % maximum sulfur and up to 0,50 % maximum selenium may be present. This reference indicates that the alloy contains a "substantially austenitic structure after working". The only exemplary compositions are outside the ranges disclosed and claimed herein. This reference does not disclose that these materials have components that are balanced so as to obtain high strength combined with low magnetic permeability. US Patent 4,337,088 discloses the use in an oilwell stabilizer of two different austenitic stainless steel alloys, Nitronic² 50 and Nitronic 60 (see column 2, lines 4 to 26 for their respective compositions). Nitronic² 50 has a composition outside those claimed herein. In addition, this patent does not disclose that these materials have compositional components which are balanced so as to obtain a stable austenite condition under severe cold working conditions combined with low magnetic permeability as disclosed herein. The invention is defined in claim 1 and preferred embodiments of the invention are defined in claims 2-7. The amounts of the various components, which are very critical, are governed by the demand of the structure which should be single phase austenite showing no presence of ferrite. The austenite phase shall be sufficiently stable so that it is not, to a significant degree, transformed into ferromagnetic martensite during cooling from high temperature annealing or at substantial cold working, typically above 70 % thickness reduction during cold working or a corresponding degree of reduction at wire drawing. At the same time the austenite phase shall during deformation exhibit a substantial cold hardening which means that high mechanical strength can be achieved without presence of a ferromagnetic phase. Important is also the possibility of achieving, in the cold worked condition, a further increase in strength by carrying out a simple heat treatment. In order to achieve these objectives simultaneously the effects of the alloying constituents must be known. Certain of these constituents are ferrite formers whereas others are austenite formers at those temperatures that are relevant at hot working and annealing. Additionally, certain of these constituents will increase the defomation hardening during cold working whereas others decrease the same. The reason for limiting the composition of the steel of the present invention is explained hereunder wherein all amounts are given in terms of weight-%. Carbon is an element which strongly contributes to austenite formation. Carbon also contributes to a stabilization of austenite against martensite transformation and it has consequently a double positive effect in this alloy. Carbon also positively contributes to the work hardenability at cold working. The carbon content should therefore exceed 0,04 %. High carbon amounts however leads to negative effects. The high chromium affinity results in an increased tendency for carbide precipitation with increased carbon content. This also leads to impaired corrosion properties, embrittlement problems, and a destabilazation of the matrix which might lead to local martensite transformation which renders the material being partially ferromagnetic. The maximum content of C is limited to 0,25 % at cold working, preferably below 0,15 %. Si is an important element for the purpose of facilitating the manufacturing process. In addition thereto Si has been found to have a precipitation hardening effect by contributing to the precipitation of γ-phase during heat treatment. The Si content should therefore be at least 2 %. Si is however a ferrite stabilizer which rather drastically tends to increase the tendency for the formation of the ferromagnetic phase of ferrite. High Si amounts additionally promote the tendency of precipitating easily melting intermetallic phases and thereby impairs the hot working. The Si-content should therefore be limited to max 5 % preferably 3,0-5,0 %. Manganese has been found to contribute positively to several properties of the alloy of this invention. Mn stabilizes austenite without simultaneously negatively affecting the work hardening. Mn has the additional important ability of providing solubility of nitrogen, properties described more specifically hereunder, in melted and solid phase. The Mn content should therefore exceed 3,5 %. Mn increases the coefficient of linear expansion and reduces electrical conductivity which could be of disadvantage for applications within electronics and computer areas. High amounts of Mn also reduce corrosion resistance in chloride containing environments. Mn is also much less efficient than nickel as a corrosion reducing element under oxidizing corrosion conditions. The Mn content should therefore not exceed 7,5 %, and should preferably amount to 3,5-5,5 %. Cr is an important alloy element from several aspects. Cr content should be high in order to achieve good corrosion resistance. Cr also increases nitrogen solubility of nitrogen in the melt and in the solid phase and thereby enables increased alloyed presence of nitrogen. Increased Cr content also contributes to stabilized austenite phase towards martensite transformation. The alloy of the present invention can, to advantage as described below be annealed and precipitate high chromium containing nitrides. In order to reduce the tendency for too strong local reductions of Cr-content with non-stabilization and reduction in corrosion resistance the Cr content should exceed 16 %. Since Cr is a ferrite stabilizing element presence of very high Cr contents will lead to the presence of ferromagnetic ferrite. The Cr content should therefore be less than 21 %, preferably less than 19 %. Ni is, next after carbon and nitrogen, the most efficient austenite stabilizing element. Ni also increases austenite stability towards deformation into martensite. Ni is also, in contrast of Mn, known for efficiently contributing to corrosion resistance under oxidizing conditions. Ni is, however, an expensive alloy element at the same time as it has a negative impact on work hardening during cold working. In order to achieve a sufficiently stable non-magnetic structure the Ni-content should exceed 8 %. In order to achieve high strength after cold working the Ni-content should not exceed 11 %, and preferably not exceed 10 %. N is a central alloy element in the present alloy. N is a strong austenite former, it promotes solution hardening and stabilizes the austenite phase strongly towards deformation into martenite. N is also of advantage for the purpose of achieving increased work hardening at cold working and it acts as a precipitation hardening element at heat treatment. Nitrogen can therefore contribute to a further increase of the cold rolled strength. Nitrogen also increases resistance towards nodular corrosion. Chromium nitrides precipitated during heat treatment also appear to be less sensibilizing than corresponding chromium carbides. In order to completely take advantage of its many good properties the N content should not be less than 0,10 %, preferably not less than 0,15 %. When using very high nitrogen contents the solubility of N is exceeded in the melt. The N content should therefore be equal to or less than 0,45 %, and preferably amount to 0,20-0,45 %. The invention will in the following be disclosed by way of results from research carried out whereby further details about structure, work hardening, mechanical properties and magnetic propertieswill be disclosed. Production of the testing materials included melting in a high-frequency induction furnace and casting to ingots at about 1600°C. These ingots were heated to about 1200°C and hot worked by forging the material into bars. The materials were then subject of hot rolling into strips which thereafter were quench annealed and clean pickled. The quench anneal was carried out at about 1080°C and quenching occurred in water. The strips obtained after quench annealing were then cold rolled to various reduction degrees after which test samples were taken out for various tests. In order to avoid variations in temperature and its possible impact on magnetic properties the samples were cooled to room temperature after each cold rolling step. The chemical analysis of the testing materials in weight-% appear from Table 1 below: P,S < 0.030 weight-% is valid for all alloys above. In quench annealed condition samples were taken for control of amounts of ferrite and martensite and for measurement of hardness. The results are disclosed in Table 2. All test alloys fulfill the requirements of being free from ferrite and martensite in quench annealed condition. The annealed hardness corresponds approximately with that of reference materials AISI 304/305. As described above it is very important that materials according to the invention has been subject of substantial word hardening at the cold working steps. Table 3 below shows how increased hardness is obtained with increased deformation degree. All testing alloys appear to have been substantially work hardened compared with reference materials AISI 304/305. The strength of the alloys when subjected to uniaxial tensile testing as function of cold working degree appears from Table 4, where R p 0,05 and R p 0,2 correspond to the load that gives 0,05 % and 0,2 % remaining elongation, and where R m corresponds with the maximum load value in the load-elongation diagram and where A10 corresponds with ultimate elongation. Table 4 shows that with alloys of the invention very high strength levels can be obtained at cold working. AISI 305 appears to show a substantially slower work hardening due to its low contents of dissolved alloy elements, i.e. nitrogen and carbon, combined with rather high nickel content. Spring steel type SS 2331 are often annealed in order to obtain a further improvement of the mechanical properties. This enables a positive impact on several important spring properties such as fatigue strength and relaxation resistance and the possibility of forming the material in a rather soft condition. The higher ductility at lower strength can hereby be used for a more complicated formation of the material. Table 5 shows the effects of such annealing on mechanical properties after 75 % cold reduction. The annealing tests resulted in optimal effect at a temperature of 450°C and 2 h maintenance. The alloys of the present invention have a very good effect after annealing. It is of specific importance to have achieved such a substantial increase in R p 0,05 (> 40 %). This is the value that is best correlated with the elastic limit which is an indication how much a spring can carry a load without plastification. Due to the increased value in R p 0.05 a larger application area for a spring is achieved. It is specifically interesting to notice that there is a modest increase in tensile strength in the materials AISI304 and AISI305. This is an important disadvantage since the tensile strength by experience is the value that is best correlated to the fatigue strength. For a material according to this invention there is the requirement that this material, whilst exhibiting high strength, also has as low magnetic permeability as possible, i.e. close to 1. Table 6 shows the magnetic permeability depending upon field strength for the various alloys after 75 % cold reduction and annealing at 450°C/2 h. Table 6 shows that with alloys of this invention it is possible, by coldworking and precipitation hardening, to achieve a strength exceeding 1800 or even 1900 MPa combined with very low values of the magnetic permeability < 1.05. The reference alloys with compositions outside the scope of this invention and the reference steels AISI304 and AISI305 either appear to be too unstable in austenite, alloys 866, 872 and AISI 304 appear to be non-magnetic at high strength or appear to have an insufficient degree of work hardening, and alloy AISI305 appears to have sufficient mechanical strength that is representative for a good spring material. The effect of silicon as a precipitation hardening element is apparent from alloys 880 and 881 which, except Si, have a corresponding composition. The latter alloy has a high Si content and appears to have, at same reduction degree and heat treatment, about 200 N/mm² higher tensile strength than compared with alloy 880 which has a lower Si content.

Claims: Precipitation hardening stainless steel alloy having high strength and low magnetic permeability characterized in the following analysis by weight: C 0,04-0,25 % Si 2,0-5,0 % Mn 3,5-7,5 % Cr 16-21 % Ni 8-11 % N 0,10-0,45 % the remainder of said composition being iron and normal impurities, the contents of said elements being balanced so that the austenite phase remains stable towards deformation into martensite even at cold working > 70 % area of reduction, said alloy having a Rm-value >1800 MPa and a magnetic permeability of <1.05 as a result of an annealing at 450 °C for 2 h after cold working. The steel of claim 1, characterized in that the Cr-content is 16-19 %. The steel of claim 1, characterized in that the Ni-content is 8-10 %. The steel of claim 1, characterized in that the C-content is 0,04-0,15 %. The steel of claim 1, characterized in that the Si-content is 3,0-5,0 %. The steel of claim 1, characterized in that the N-content is 0,15-0,45 %. The steel of claim 1, characterized in that the Mn-content is 3,5-5,5 %.

Inventors: HOLMBERG HAKAN, HOLMBERG, HAKAN
Applicants: SANDVIK AB, SANDVIK AKTIEBOLAG
Application year: 1991
Main classification: C22C38
IPC codes: C22C38, H01F1