WORK HARDENED STAINLESS STEEL FOR SPRINGS

Abstract: Invention patent of metastable austenitic cold deformed "work hardened stainless steel for springs", with 17.0 to 19.0 % Cr, 8.0 to 10.0 % Ni, up to 0.03 % C, 0.006 to 0.16 % N, up to 1.0 % Si, 1.0 to 2.0 % Mn, up to 0.8 % Mo, up to 0.045 % P, up to 0.030 % S and the rest mainly of iron (Fe) and inevitable residuals, being the alloy especially appropriated for spring manufacture that need good resistance to corrosion, having the steel after the cold deformation, high mechanical properties and better resistance to corrosion than UNS S30200 steel, even when submitted to heat treatment of tempering, being the steel appropriated to use as wire rod, bars, wires, sheets and strip forms.

Description: DESCRIPTION WORK HARDENED STAINLESS STEEL FOR SPRINGS. Technical Field The current invention is referred to an improved stainless steel obtained by cold deformation, such as wire drawing and rolling. ' As a result the steel presents a structure consisted of martensite and austenite with high resistance to corrosion. Such properties fit its main application field in the spring manufacture. Background Art The springs, at most, are submitted to load cycle, what requires, therefore, good fatigue resistance. A succession of factors affects this resistance but it is the superficial quality without any doubt that most regulate the springs performance submitted to fatigue requests. The presence of superficial irregularities favour the nucleation of fatigue cracks. Nevertheles, the resistance to fatigue is not guaranteed just by avoiding these defects, because the superficial defects can be formed during the spring use. one of the most prejudicial superficial defect created during the spring use is corrosion. So, when the design conditions demand and the costs permit, it should be used the stainless steel in the spring manufacture. The stainless steel for spring were developed in order to turn possible its aplication to springs, pursuing mainly increase its mechanical strength, very low in the solubilized condition. Compositions that allow by hardening mechanisms, strength levels that overflow 2000 MPa in some alloys and gauge were developed. The stainless steel presents, also one useful property, that is the capacity to be cold worked, what eases the manufacturing process as rolling and drawing. Stainless steel, that forms martensite during cold deformation, are called metastable. They present high strength after cold deformation, as occurs during wires drawing, so they are the main stainless steels used in spring manufacture. The strength is the result of a microstructure consisting of hardened martensite and austenite, having the carbon as the main hardening element. However, the metastable austenitic stainless steel, of the current technical state, most used in spring manufacture, UNS S30200 steel, with up to 0,15% of C, 17,0 to 19,0% Cr, 8,0 to 10,0% Ni, up to 0,75% Si, up to 2,0% Mn, up to 0.045% P and up to 0,030% S, does not present enough resistance to intergranular and pitting corrosion. Besides, due to the high carbon, normally over 0,08%, these steels must be heat treated in cycle known as solubilization, with higher temperatures and longer periods than other stainless steels. So, work with UNS S30200 steel involves more cares and higher costs. Also, the standard stainless steel for springs presents problems in durability when used in applications that require high resistance to corrosion. In the spring manufacturing process, an tempering heat treatment is normally carried out in order to increase the spring strength and durability. Depending on the temperature used the chromium carbide precipitation can occurs, what reduces the resistance to corrosion. The current invention solves these problems. Disclosure of invention The target of this invention is obtain a cold deformed stainless steel for spring manufacture, with microstructure consisted of martensite and austenite mixed up, with better resistance to intergranular and pitting corrosion and that does not involve special cares for solution heat treatment. Specifically, the current invention presents metastable stainless steel for spring manufacture, that after cold deformation, have microstructre consisting of austenite and martensite. This steel have 17,0 to 19,0% Cr, 8,0 to 10,0% Ni, 0,06 to 0.16% N, up to 0,03% C, up to 1,0% Si, 1,0 to 2,0% Mn, up to 0.80% Mo, up to 0,075% P and up to 0,030% S, the rest is iron and inevitable impurity. The stainless steel according to the current invention presents high strength after cold deformation and high resistance to intergranular and pitting corrosion. Besides, the solution heat treatment of this steel does not involve special cares, and can be eventually eliminated. The chemical composition range of the new steel must have hardening properties similar to UNS S30200, where the high resistance is a result of the martensite formation during the cold deformation when drawing or rolling occurs and the hardening by carbon. The martensite level created depends on the alloy stability degree, that is chemical composition function. One of the equations that rules this dependence is the following : Md (30/50) (=C) = 497 - 462 | (%C) + (%N) | - 9,2 (%Si) - - 8,1 (%Mn) - 13,7 (%Cr) - 20 (%Ni) - - 18,8 (%Mθ) where Md (30/50) is temperature, in Celsius (centigrade) degree that occurs the formation of 30% of martensite, after 50% of cold deformation. A typical composition of UNS S30200 steel, used by experts consists on 0,10% C, 0,40% Si, 1,70% Mn, 17,5% Cr, 8,3% Ni, 0,03% N and 0,4% Mo. Using the equations before will result Md (30/50) equal to 6,34°C . The alloy of this current invention must have the same content of the Cr, Ni, Si, Mn and Mo elements present in UNS S30200. Supposing a carbon content equal to 0,02% (the demanded specification is up to 0,03%) and calculating the Md (30/50) for the new alloy we will obtain: Md (30/50) = 57,16 - 462 (%N) . For the new alloy to have an equivalent martensite value, after cold deformation, to UNS S30200, its Md (30/50) must be the same, what involves a desirable typical content of 0.11% nitrogen. In relation to hardening effect, the nitrogen is at least as efficient as carbon, because the nitrogen interactions with the dislocations are much stronger than obtained with carbon. The reason for current stainless steel chemical composition specification are described following. Cr: 17,0% to 19,0% - Chromium is the essencial element to promote the resistance to corrosion through a superficial protector layer formation turning stainless the steel, being these the normally contents used. Ni: 8,0% to 10,0% - Nickel is the element that provides stability to austenite and resistance to corrosion. Its content should be balanced with chromium content to guarantee a start microstructure completely austenitic after the solution heat treatment or the rolling. Besides, the composition range must be stablished in order to occur the martensite formation after cold deformation. C: up to 0,03% - Carbon is a gamagenic element that is dissolved when its concentration is low. However, when the C content increases, the M23C6 carbide type can precipitate in grain boundaries, consuming chromium that is useful to intergranular corrosion resistance. In the current invention the limit of this element, at most 0,03%, will be compensated as we will see below, by the nitrogen content. N: 0,06% to 0,16% - Nitrogen is the most critical element of the current invention and is particularly important to obtain simultaneously the mechanical properties necessary to stainless steel spring manufacture with improved resistance to corrosion. The nitrogen works as a stabilizer of austenitic phase and as a hardner. During the cold deformation, the nitrogen hardens the formed martensite, assuring a high work hardening behaviour. This element increase the resistance to pitting corrosion and delays the kinetics of M23C6 precipitation, increasing, therefore, the resistance to intergranular corrosion. After the heat treatment of the hardened material, by cold drawing or rolling, the nitrogen creates atmospheres in the vicinity of dislocations, raising still more the steel strength. The effect can not be obtained in nitrogen content below 0,06%, on the other hand it can not be over 0,16% because the Md (30/50) value reaches values that damage the alloy metastability and as a result the mechanical property levels reached. Si: up to 1,0% - Silicon is a deoxidizing element and its presence is related with the steel manufacturing process. Mn: 1,0% to 2,0% - manganese is a gamagenic element and help to assure a completely austenitic structure after solution heat treatment. The manganese is also used in steel deoxidation. Besides, P, S and other residual elements inevitably mixed up in the steel manufacturing process should be lowest levels as possible. The alloy, as described, can be manufactured as rolling or forged products by standard or special process such as, powder metallurgy or continuous casting wire rod, bars, wires sheets and strips. Following, the steel properties of the current invention will be described and compared with the used UNS S30200 steel. EXAMPLE: In table 1 we have displayed the comparison of alloys that were casted and rolled to 8 millimeter diameter wire rod and solubilized. The materials were cold deformed by wire drawing up to 3,0 millimeter diameter wire, and in each reduction samples were took off. In Table 2 the work hardening behaviour of the two steels are displayed. The new steel presents a sufficient metastability to reach high levels of strength necessary to spring application. In spite of strength values of the current invention are below the values obtained for the UNS S30200, we get in the example, the minumum levels required by the standards that establish the spring manufacture from drawn wires. Even though, the spring during its manufacturing are submitted to a tempering heat treatment in temperatures around 400°C. The Table 3 displays that the new steel presents in the final condition more hardening than the UNS S30200 steel, showing the effective action of nitrogen as hardening element. The mechanical properties of the start material, solubilized wire rod with 8,0 millimeter diameter, are showed in Table 4. The alloy in the current invention have greater yield strength and the same ductility of the UNS S30200 steel. There is no difference in the tensile strength. Some pitting corrosion tests were made in the solubilized material and in the wire with 82% of deformation. The test was realized according to ASTM G48 rule, mass loss in a ferric chloride solution after 72h. The results are displayed in Table 5. It is clear that the new steel is superior to UNS S30200 in terms of resistance to pitting corrosion, keeping the benefit also in the work hardened condition. The results confirm the strong effect of the nitrogen in the resistance to pitting corrosion. The tests of intergranular corrosion were also conducted in the solubilized material, in the wire with 82% of deformation and in the wire after treatment at 400°C during 40 minutes. The test was realized according to ASTM A 262-C rule, mass loss in boiling nitric acid. The results are displayed in Table 6. In all conditions, the steel of the invention was superior to UNS S30200 steel. The difference was greater after the treatment at 400°C during 40 minutes, due to precipitation of carbide in grain boundaries in the UNS S30200 steel. One must pay attention here for the fact that in the current example , the UNS S30200 steel was solubilized (1060°C during 3h) . One fault in the UNS S30200 steel solution heat treament reduces its resistance to intergranular corrosion. Even in the as rolled condition, the wire rod of the current invention did not present intergranular corrosion. To evaluate the life in fatigue, springs were manufactured from drawn wires of 1,0 mm diameter. The manufacturing process was realized in the same conditions normaly used for UNS S30200 steel. The springs made with the two steels were tested in compression , with load varying from 287 N to 988 N, according to DIN 2089 standard. The steel of current invention showed a life in fatigue, up to breakage, of 120.000 cycles against 80.000 cycle of UNS S30200 steel. It will be obvious to experts that the principles of the invention here released in relation to its specific example, will hold many other changes and aplications. It is also desirable that when analysing the amplitude of the append claims, they are not limited to specific example of the invention here described. Following will be presented the Tables mentioned in EXAMPLE described before. TABLE 1 CHEM ICAL COMPOS ITION I N WE IGHT PORCENTAGEN ftLLQY Cr Ni Hn Si H C UP Cu P S UNS S3020G 18,1 8 ,72 1,42 0,60 0,0*1 COS ft.03 0,1 0,027 0,014 Steel of the invention 17.45 8,21 1,88 ft i c . , iy 0.01 0,3= 0=18 O. ' OJ 0.024 TABLE 2 WORK HARDEN ING BEHAV IOUR Tensile Strenoth (BPai Reouction (%1 35 59 68 75 80 82 Steel of the 575 935 1190 1345 1455 1595 1640 1755 invention UNS S3C200 600 940 1210 1400 1580 1690 1780 1820 TABLE 3 WIRE HARDEN ING AFTER ANNEALING fiate-rial Condition HaronessfHVl j Steei of the 82% όeforae 463 invention 822 cieforfiBd ÷ *00*C x 40 sin 547 UNS S30200 825 deforied 485 82A tieforBed + 40C*C x 40 tin 517 TABLE 4 MECHANICAL PROPERTIES OF THE SOLUBILIZED WIRE ROD TEST TEMPERATURE 25 β C AND t- 0,001 s~ A Steel of the invention UNS S30200 YIELD STRENGTH 0,22 (HPa) TENSILE STRENBTH (HPa) ELONGATION 5d (X) Reduction in area (2! TABLE 5 PITTING CORROSJON TESTS RESULTS - ASTM G4B Haterial Condition Hass Loss (JΠ/CB 2 ) Steel of the solubilized 24,06 invention 82S defcrned 44,03 UNS S30200 solubilized 46,15 822 deforβed 56,38 TABLE 6 INTERGRANULAR CORROSION TESTS RESULTS - ASTM A262-C Haterial Condition Hass Loss (uα/cs a ) Steel of the invention UNS S30200

Claims: WORK HARDENED STAINLESS STEEL FOR SPRINGS CLAIMS 1. "WORK HARDENED STAINLESS STEEL FOR SPRINGS", presenting a structure consisting of martensite and austenite, with high mechanical properties, characterized by the fact that the referred steel presents a high resistance to corrosion after cold deformation, consisting essentially of the following component in weight percentage: 17,0 ≤ Cr < 19,0; 8,0 ≤ Ni ^ 10,0; 0 < C < 0,03; 0,06 N < 0,16; 0 < Si 1,0; 1,0 ^ Mn < 2,0; 0 < Mo ≤ 0,8; 0 < P .$ 0,045; 0 < s ^ 0,030; being the rest of Iron (Fe) and inevitable residuals. 2. "WORK HARDENED STAINLESS STEEL FOR SPRINGS", according to claim 1, characterized by the realization of a heat treatment of tempering in the spring in order to increase the mechanical properties.

Inventors: BARBOSA CELSO ANTONIO, TESSLER MARCELO BLASBALG, BARBOSA, CELSO, ANTONIO, TESSLER, MARCELO, BLASBALG
Applicants: ACOS VILLARES SA, ACOS VILLARES S/A
Application year: 1993
Main classification: C22C38
IPC codes: C21D9, C22C38