Disclosed in the present disclosure is an ultrahigh-strength dual-phase steel. The matrix structure of the ultrahigh-strength dual-phase steel is ferrite and martensite, wherein the ferrite and the martensite are evenly distributed in an island shape. The ultrahigh-strength dual-phase steel contains the following chemical elements in percentage by mass: 0.12-0.2% of C, 0.5-1.0% of Si, 2.5-3.0% of Mn, 0.02-0.05% of Al, 0.02-0.05% of Nb, 0.02-0.05% of Ti, and 0.001-0.003% of B. Further disclosed in the present disclosure is a manufacturing method for the ultrahigh-strength dual-phase steel, comprising the steps of smelting and continuous casting, hot rolling, cold rolling, annealing, tempering, and leveling. The ultrahigh-strength dual-phase steel in the present disclosure has not only good mechanical properties but also excellent delayed cracking resistance and low initial hydrogen content, and can be suitable for manufacturing of vehicle safety structural parts.

Disclosed in the present disclosure is an ultrahigh-strength dual-phase steel. The matrix structure of the ultrahigh-strength dual-phase steel is ferrite and martensite, wherein the ferrite and the martensite are evenly distributed in an island shape. The ultrahigh-strength dual-phase steel contains the following chemical elements in percentage by mass: 0.12-0.2% of C, 0.5-1.0% of Si, 2.5-3.0% of Mn, 0.02-0.05% of Al, 0.02-0.05% of Nb, 0.02-0.05% of Ti, and 0.001-0.003% of B. Further disclosed in the present disclosure is a manufacturing method for the ultrahigh-strength dual-phase steel, comprising the steps of smelting and continuous casting, hot rolling, cold rolling, annealing, tempering, and leveling. The ultrahigh-strength dual-phase steel in the present disclosure has not only good mechanical properties but also excellent delayed cracking resistance and low initial hydrogen content, and can be suitable for manufacturing of vehicle safety structural parts.

The disclosure relates to the field of metal ion capture, more particularly of selective capture of nickel Ni(II) ions, by a polymeric compound based on a polymer selected from styrenic polymers and chloropolymers. In the polymeric compound, at least one portion of the monomer units of the polymer is functionalised by the ligand, the ligand including at least one chemical group selected from the glyoxime groups.

The glyoxime groups have a strong affinity for the Ni(II) ions, as well as an excellent selectivity vis-à-vis metal ions of chemical properties similar to Ni(II) ions. This ligand thus allows a selective complexation of the Ni(II) ions by the polymeric compound, including in solutions of low concentrations of Ni(II) ions.

The polymeric compound according to at least one embodiment of the disclosure is particularly intended for capturing the Ni(II) ions during the electrogalvanising methods as well as for recycling material comprising nickel.

The disclosure relates to the field of metal ion capture, more particularly of selective capture of nickel Ni(II) ions, by a polymeric compound based on a polymer selected from styrenic polymers and chloropolymers. In the polymeric compound, at least one portion of the monomer units of the polymer is functionalised by the ligand, the ligand including at least one chemical group selected from the glyoxime groups.

The glyoxime groups have a strong affinity for the Ni(II) ions, as well as an excellent selectivity vis-à-vis metal ions of chemical properties similar to Ni(II) ions. This ligand thus allows a selective complexation of the Ni(II) ions by the polymeric compound, including in solutions of low concentrations of Ni(II) ions.

The polymeric compound according to at least one embodiment of the disclosure is particularly intended for capturing the Ni(II) ions during the electrogalvanising methods as well as for recycling material comprising nickel.

A surface-treated copper foil includes a treated surface, where the peak extreme height (Sxp) of the treating surface is 0.4 to 3.0 μm. When the surface-treated copper foil is heated at a temperature of 200° C. for 1 hour, the ratio of the integrated intensity of diffraction peak of (111) plane to the sum of the integrated intensities of diffraction peaks of (111) plane, (200) plane, and (220) plane of the treating surface is at least 60%.

A steel sheet including a chemical composition satisfying an equivalent carbon content of 0.60% or more and less than 0.85%, and a steel microstructure with an area fraction of ferrite: less than 40%, tempered martensite and bainite: 40% or more in total, retained austenite: 3% to 15%, and ferrite, tempered martensite, bainite, and retained austenite: 93% or more in total. A 90-degree bending at a curvature radius/thickness ratio of 4.2 in a rolling (L) direction with respect to an axis extending in a width (C) direction causes a change of 0.40 or more in (a grain size in a thickness direction)/(a grain size in a direction perpendicular to the thickness) of the tempered martensite in an L cross section in a 0- to 50-μm region from a surface of the steel sheet on a compression side. The steel sheet has a tensile strength of 980 MPa or more.

A steel sheet including a chemical composition satisfying an equivalent carbon content of 0.60% or more and less than 0.85%, and a steel microstructure with an area fraction of ferrite: less than 40%, tempered martensite and bainite: 40% or more in total, retained austenite: 3% to 15%, and ferrite, tempered martensite, bainite, and retained austenite: 93% or more in total. A 90-degree bending at a curvature radius/thickness ratio of 4.2 in a rolling (L) direction with respect to an axis extending in a width (C) direction causes a change of 0.40 or more in (a grain size in a thickness direction)/(a grain size in a direction perpendicular to the thickness) of the tempered martensite in an L cross section in a 0- to 50-μm region from a surface of the steel sheet on a compression side. The steel sheet has a tensile strength of 980 MPa or more.

The invention relates to the use of a Q&P steel for production of a formed component (2) for high-wear applications, wherein the Q&P steel has a hardness of at least 230 HB, especially at least 300 HB, preferably at least 370 HB, and a bending angle α of at least 60°, especially at least 75°, preferably at least 85°, determined to VDA238-100, and/or a bending ratio of r/t<2.5, especially r/t<2.0, preferably r/t<1.5, where t corresponds to the material thickness of the steel and r to the (inner) bending radius of the steel.

The invention relates to the use of a Q&P steel for production of a formed component (2) for high-wear applications, wherein the Q&P steel has a hardness of at least 230 HB, especially at least 300 HB, preferably at least 370 HB, and a bending angle α of at least 60°, especially at least 75°, preferably at least 85°, determined to VDA238-100, and/or a bending ratio of r/t<2.5, especially r/t<2.0, preferably r/t<1.5, where t corresponds to the material thickness of the steel and r to the (inner) bending radius of the steel.

A surface-treated copper foil including a treating surface, where the root mean square height (Sq) of the treating surface is in a range of 0.20 to 1.50 μm and the texture aspect ratio (Str) of the treating surface is not greater than 0.65. When the surface-treated copper foil is heated at a temperature of 200° C. for 1 hour, the ratio of the integrated intensity of (111) peak to the sum of the integrated intensities of (111) peak, (200) peak, and (220) peak of the treating surface is at least 60%.