The invention relates to a high-alloy steel, in particular for producing pipes shaped by means of internal high pressure, having high cold formability, TRIP and/or TWIP properties, a partially or completely austenitic microstructure having at least 5% residual austenite, and having the following chemical composition (in wt %): Cr: 7 to 20; Mn: 2 to 9; Ni: up to 9; C: 0.005 to 0.4; N: 0.002 to 0.3; the remainder being iron including unavoidable, steel-accompanying elements, with optional addition of the following elements (in wt %): Al: 0 to 3; Si: 0 to 2; Mo: 0.01 to 3; Cu: 0.005 to 4; V: 0 to 2; Nb: 0 to 2; Ti: 0 to 2; Sb: 0 to 0.5; B: 0 to 0.5; Co: 0 to 5; W: 0 to 3; Zr: 0 to 2; Ca: 0 to 0.1; P: 0 to 0.6; S: 0 to 0.2. The invention further relates to a method for producing pipes from this steel, said pipes being shaped by means of internal high pressure.

A structural component for an automotive vehicle formed from a single-piece of steel material and having a closed, complex cross-section with increased strength, for example a strength of greater than 650 MPa, and thus improved performance, is provided. The structural component typically has an elongation of greater than 5%. The structural component is formed by expanding a boron-containing steel material, for example heating or hydroforming a tube of the steel material. The boron-containing steel material expands by least 2% during the forming process and thus achieves the closed, complex cross-section, while also achieving the high strength. In addition, the structural component can be formed with zones of varying thickness, strength, hardness, elongation, and/or other varying properties to achieve the desired performance.

A deformation-hardened component is made of galvanized steel by cutting a plate from a steel strip or steel sheet coated with zinc or with a zinc-based alloy and subsequently heating the plate to a deformation temperature above Ac3 for deformation and hardening. The galvanized steel has an at least partially martensitic transformation structure and includes as a chemical composition in wt. % C: 0.10-0.50, Si: 0.01-0.50, Mn: 0.50-2.50, P<0.02, S<0.01, N<0.01, Al: 0.015-0.100, B<0.004, remainder iron, including unavoidable smelting-induced, steel-accompanying elements. The chemical composition further includes at least one element selected from the group consisting of Nb, V, Ti, with a sum of the contents Nb+V+Ti being in a range of 0.01 to 0.20 wt. %. The structure of the steel after deformation-hardening has an average grain size of the former austenite grains of <15 ?m.

A method is disclosed for pressure forming a metal preform including shock annealing of the preform and subsequently preheating the preform prior to pressure forming. Shock annealing may be carried out as differential shock annealing in which different regions of the preform are annealed to different degrees. Preheating may be carried out by differentially preheating, optionally shock preheating, different regions of the preform for preheating at least those regions of the preform which will be subject to elevated expansion during pressure forming. Shock annealing by induction heating can lower energy consumption, reduce processing times and allow for larger expansion of the preform.

A method is disclosed for pressure forming a metal preform including shock annealing of the preform and subsequently preheating the preform prior to pressure forming. Shock annealing may be carried out as differential shock annealing in which different regions of the preform are annealed to different degrees. Preheating may be carried out by differentially preheating, optionally shock preheating, different regions of the preform for preheating at least those regions of the preform which will be subject to elevated expansion during pressure forming. Shock annealing by induction heating can lower energy consumption, reduce processing times and allow for larger expansion of the preform.

A method is disclosed for pressure forming a metal preform including shock annealing of the preform and subsequently preheating the preform prior to pressure forming. Shock annealing may be carried out as differential shock annealing in which different regions of the preform are annealed to different degrees. Preheating may be carried out by differentially preheating, optionally shock preheating, different regions of the preform for preheating at least those regions of the preform which will be subject to elevated expansion during pressure forming. Shock annealing by induction heating can lower energy consumption, reduce processing times and allow for larger expansion of the preform.

A method is disclosed for pressure forming a metal preform including shock annealing of the preform and subsequently preheating the preform prior to pressure forming. Shock annealing may be carried out as differential shock annealing in which different regions of the preform are annealed to different degrees. Preheating may be carried out by differentially preheating, optionally shock preheating, different regions of the preform for preheating at least those regions of the preform which will be subject to elevated expansion during pressure forming. Shock annealing by induction heating can lower energy consumption, reduce processing times and allow for larger expansion of the preform.

Steel material for composite pressure vessel liners that, when used as raw material for manufacturing a composite pressure vessel liner, yields a liner having sufficient strength and a high fatigue limit and enables the manufacture of an inexpensive composite pressure vessel is provided. Steel material for composite pressure vessel liners comprises: a chemical composition containing, in mass %, C: 0.10% to 0.60%, Si: 0.01% to 2.0%, Mn: 0.1% to 5.0%, P: 0.0005% to 0.060%, S: 0.0001% to 0.010%, N: 0.0001% to 0.010%, and Al: 0.01% to 0.06%, with a balance being Fe and incidental impurities; and a metallic microstructure in which a mean grain size of prior austenite grains is 20 m or less, and a total area ratio of martensite and lower bainite is 90% or more.

A high-strength heavy-walled stainless steel seamless tube or pipe exhibiting excellent low-temperature toughness is characterized by having a chemical composition containing Cr: 15.5% to 18.0% and a steel microstructure containing a ferritic phase and a martensitic phase, wherein the maximum value of the areas of the ferrite grains in the steel microstructures in a circumferential direction cross section and an L direction (rolling direction) cross section of the steel tube or pipe is 3,000 m.sup.2 or less and the content of ferrite grains having areas of 800 m.sup.2 or less is 50% or more on an area fraction basis, where, when adjacent ferrite grains are present in the steel microstructure and the crystal misorientation between one ferrite grain and the other ferrite grain is 15 or more, the adjacent grains are assumed to be grains different from each other.

A method of incremental autofrettage is taught herein, whereby the cycle life of a metal liner in a pressure vessel is increased. This method serves to increase the yield strength of the metal liner through sequential work hardening due to repeated autofrettage at increasing pressures. By incrementally increasing the internal pressure used in the autofrettage process, the compressive stresses at an inner surface of the metal liner may be controlled so that post-pressurization buckling does not occur, yet the yield strength of the metal liner is substantially increased. The higher compressive stresses in the metal liner mean that higher Maximum Expected Operating Pressures (MEOPs) may be used without detracting from the cycle life of the metal liner, or alternatively, for lower pressures, a longer metal liner cycle life may be obtained. Either internal or external pressures may be used, generated by a pressure source, or a suitable die.